TW202237546A - Glass with unique fracture behavior for vehicle windshield - Google Patents

Abstract

Disclosed herein are embodiments of a borosilicate glass composition as may be useful for windshield and other applications in particular due to unique fracture behavior.

Description

Glass with unique fracture behavior for vehicle windshields

This case petitions U.S. Application No. 63/123,863 filed December 10, 2020, U.S. Application No. 63/183,292 filed May 3, 2021, U.S. Application No. 63/183,271 filed May 3, 2021, and U.S. Application No. 17/363,266, filed June 30, 2021, each of which is hereby incorporated by reference in its entirety.

The present disclosure relates to glass compositions and glass articles made therefrom, and more particularly to borosilicate glass compositions capable of fusion formation at relatively large thicknesses and glass articles made therefrom.

Glass is used in windows due to its optical clarity and durability. Automotive and architectural windows may comprise a single glass interlayer, or a laminate comprising two glass interlayers with an interlayer of polymeric material interposed therebetween. Particularly for automotive applications, there is a trend to use laminates to improve fuel economy and/or crash performance. Certain laminate designs may utilize a thicker outer glass interlayer as well as a thinner inner glass interlayer. A thicker glass interlayer may be, for example, soda lime glass, which is susceptible to thermal shock and is prone to cracking after being struck by, for example, rocks or other debris thrown from the road. Accordingly, there is a need for improved glass for use in thicker outer glass interlayers in laminates.

According to aspects, embodiments of the present disclosure relate to a borosilicate glass composition. Unless otherwise stated, the glass compositions disclosed herein are described in terms of molar percentages (mole %) analyzed on an oxide basis. In one or more embodiments, the borosilicate glass composition includes at least 74 mol % SiO ₂ , at least 10 mol % B ₂ O ₃ , and has SiO ₂ , B ₂ O ₃ , and Al The sum of ₂ O ₃ is at least 90 mole % of Al ₂ O ₃ . In one or more embodiments, the borosilicate glass composition has a liquidus viscosity greater than 500 kP. In one or more embodiments, the borosilicate glass composition has a temperature of 1725° C. or less at a viscosity of the borosilicate glass composition of 200P.

According to another aspect, the disclosed embodiments relate to a glass interlayer. The glass interlayer has a first major surface and a second major surface opposite the first major surface. Glass interlayers are made from one or more embodiments of the borosilicate glass compositions described herein.

According to yet another aspect, embodiments of the present disclosure relate to a laminate. The laminate includes a first glass interlayer according to one or more embodiments of the glass interlayer described herein. The laminate also includes a second glass interlayer and an interlayer bonding the first glass interlayer to the second glass interlayer.

According to yet another aspect, embodiments of the present disclosure relate to automotive glazing. Automotive glazing is produced from laminates according to the aforementioned laminates.

According to another aspect, embodiments of the present disclosure relate to a vehicle. A vehicle includes a body defining an interior of the vehicle and at least one opening, and said automotive glazing disposed in the at least one opening. In the vehicle, the second glass interlayer is arranged to face the interior of the vehicle, while the first glass interlayer faces the exterior of the vehicle. In one or more embodiments, the first glass interlayer is arranged to face the interior of the vehicle, while the second glass interlayer faces the exterior of the vehicle.

According to yet another aspect, embodiments of the present disclosure relate to a method of forming a glass interlayer. The glass interlayer has a first major surface and a second major surface. In the method, a groove in the isopipe is flooded with at least two streams of a borosilicate glass composition having a liquidus viscosity greater than 500 kP and a borosilicate glass composition having a liquidus viscosity greater than 500 kP and The temperature at the viscosity of 200P is less than 1725°C. In one or more embodiments, the borosilicate glass composition includes at least 74 mol % SiO ₂ and at least 10 mol % B ₂ O ₃ . Additionally, in one or more embodiments, the composition includes a combined amount of SiO ₂ , B ₂ O ₃ , and Al ₂ O ₃ of at least 90 mole percent. In one or more embodiments of the method, at least two streams of borosilicate glass composition are fused at the root of the isopipe to form between the first major surface and the second major surface with at least 2mm thick glass interlayer.

According to yet another aspect, embodiments of the present disclosure relate to a glass interlayer. The glass interlayer has a first major surface and a second major surface opposite the first major surface. The glass interlayer is made of borosilicate glass composition. When the glass interlayer is subjected to a quasi-static 2kgf indentation load with a Vickers tip, the glass interlayer exhibits annular cracks and a plurality of radial cracks, and each radial crack in the plurality of radial cracks is bounded by an annular crack.

According to yet another aspect, embodiments of the present disclosure relate to a glass laminate. The glass laminate includes a first glass interlayer, a second glass interlayer, and an interlayer. The first glass interlayer has a first major surface and a second major surface opposite the first major surface. The first glass interlayer is made of borosilicate glass composition. The second glass interlayer has a third major surface and a fourth major surface opposite the third major surface. The interlayer bonds the second major surface of the first glass interlayer to the third major surface of the second glass interlayer. Borosilicate glass compositions comprising at least 74 mole percent SiO ₂ , at least 10 mole percent B ₂ O ₃ , and having a sum of SiO ₂ , B ₂ O ₃ , and Al ₂ O ₃ of at least 90 mole % amount of Al ₂ O ₃ .

According to yet another embodiment, embodiments of the present disclosure relate to a system including a sensor and a glass laminate. The glass laminate includes a first glass interlayer having a first major surface and a second major surface opposite the first major surface. The first glass interlayer is made of borosilicate glass composition. The glass laminate includes a second glass interlayer having a third major surface and a fourth major surface opposite the third major surface. The interlayer bonds the second major surface of the first glass interlayer to the third major surface of the second glass interlayer. Borosilicate glass compositions comprising at least 74 mole percent SiO ₂ , at least 10 mole percent B ₂ O ₃ , and having a sum of SiO ₂ , B ₂ O ₃ , and Al ₂ O ₃ of at least 90 mole % amount of Al ₂ O ₃ . The sensor is configured to receive, transmit, or receive and transmit a signal through the glass stack, with the signal having a peak wavelength in the range of 400nm to 750nm or in the range of 1500nm or greater.

According to another aspect, embodiments of the disclosure relate to a glass laminate. The glass laminate includes a first glass interlayer having a first major surface and a second major surface opposite the first major surface. The first glass interlayer is a borosilicate glass composition formed by fusion. The glass laminate also includes a second glass interlayer having a third major surface and a fourth major surface opposite the third major surface. Additionally, the glass laminate includes an interlayer that bonds the second major surface of the first glass interlayer to the third major surface of the second glass interlayer. The transmission of ultraviolet light having a wavelength in the range of 300-380 nm through the glass laminate is 75% or less. The transmittance of light in the visible spectrum through the glass laminate is 73% or more, while the total solar transmittance through the glass laminate is 61% or less.

According to another aspect, embodiments of the present disclosure relate to a glass composition comprising SiO ₂ in an amount ranging from about 72 mol % to about 80 mol %, about 2.5 mol % to about 5 mol % % of Al ₂ O ₃ , and B ₂ O ₃ in an amount of about 11.5 mol % to about 14.5 mol %. The glass composition has a liquidus viscosity greater than 500 kP, and the temperature of the glass composition is 1725° C. or less at the viscosity of the borosilicate glass composition of 200 P.

According to another aspect, embodiments of the present disclosure relate to a glass composition comprising about 74-80 mole % SiO ₂ , 2.5-5 mole % Al ₂ O ₃ , 11.5 mol% to 14.5 mol% B2O3, 4.5 mol% to ₈ mol% Na2O, _0.5 mol% to ₃ mol% K2O, 0.5 mol% to _2.5 mol% % MgO, and 0 mol% to 4 mol% CaO.

Additional features and advantages will be described in the subsequent detailed descriptions, and those skilled in the art can partially understand the additional features and advantages based on the description, or by practicing the text herein (including the subsequent detailed descriptions, patent claims) , and accompanying drawings) to understand additional features and advantages.

It is to be understood that both the foregoing general description and the following detailed description are exemplary only, and are intended to provide an overview or framework for understanding the nature and character of what is claimed.

Reference will now be made in detail to various embodiments and examples illustrated in the accompanying drawings. Embodiments of the present disclosure relate to a borosilicate glass composition capable of being fused or fused to form a glass interlayer having a thickness of at least 2 mm, more specifically at least 3 mm, at least 3.3 mm, or at least 3.8 mm . In embodiments, the borosilicate glass composition includes at least 74 mole % SiO ₂ , at least 10 mole % B ₂ O ₃ , and at least some Al ₂ O ₃ , and in embodiments SiO ₂ , The total amount of B ₂ O ₃ , and Al ₂ O ₃ is at least 90 mole percent. The borosilicate glass compositions described herein exhibit a liquidus viscosity of at least 500 kilopoise (kP) and a temperature (T _200P ) of 1725° C. or less at a viscosity of 200 poise (P).

Additionally, embodiments of the borosilicate glass compositions disclosed herein are particularly useful in laminates for automotive glazing applications. In one or more embodiments, borosilicate glass compositions serve as outer interlayers in such laminates. Compared to conventional automotive glazing that includes soda-lime glass interlayers, glass interlayers made from the disclosed borosilicate glass compositions densify during deformation, helping to prevent damage that tends to compromise the strength of the glass interlayers. Formation (initiation) or propagation (propagation) of radial or intermediate cracks. In addition, the borosilicate glass compositions disclosed herein are more resistant to thermal shock than soda-lime glass, which also helps prevent crack initiation and propagation. These performance advantages may be useful when the borosilicate glass composition is used as an inner glass interlayer or an outer glass interlayer in a glass laminate. In some cases, these performance advantages are particularly useful when borosilicate glass compositions are used as the outer glass interlayer in laminates. These and other aspects and advantages of the disclosed borosilicate glass compositions and articles formed therefrom are more fully described below. The embodiments discussed herein are presented by way of illustration and not limitation.

Embodiments of borosilicate glass compositions are described herein with respect to the vehicle 100 shown in FIG. 1 . The vehicle 100 includes a body 110 defining an interior and at least one opening 120 communicating with the interior. The vehicle 100 further includes an automotive glazing 130 (ie, a window) disposed in the opening 120 . The automotive glazing comprises at least one interlayer of the borosilicate glass composition described herein. The automotive glazing 130 may form at least one of side lights, a windshield, a rear window, a window, and a sunroof in the vehicle 100 . In some embodiments, the automotive glass window 130 can form an internal partition (not shown) inside the vehicle, or can be arranged on the outer surface of the vehicle 100, and form the engine body cover, headlight cover, tail light cover, door panel Cover, or pillar cover. As used herein, vehicle (the example illustrated in FIG. 1 ) includes automobiles, rail vehicles, locomotives, boats, boats, as well as airplanes, helicopters, drones, spacecraft, and the like. Additionally, although the present disclosure is framed in vehicles, borosilicate glass compositions may be used in other contexts (eg, architectural glazing or bulletproof glazing applications).

As shown in FIG. 2, in an embodiment, an automotive glazing 130 includes at least one glass interlayer 200 comprising, consisting of, or consisting essentially of an embodiment of the borosilicate glass composition described herein. its composition. In one or more embodiments, the automotive glazing 130 includes only a single glass interlayer 200 (ie, a single glass interlayer is sometimes referred to in the industry as a single piece). As shown in FIG. 2 , the glass interlayer 200 has a first major surface 202 and a second major surface 204 . The first major surface 202 is opposite to the second major surface 204 . The secondary surface 206 extends around the periphery of the glass interlayer 200 and connects the first major surface 202 and the second major surface 204 .

A first thickness 210 is defined between the first major surface 202 and the second major surface 204 . In an embodiment, the first thickness 210 is at least 0.5 mm, at least 1 mm, at least 2 mm, at least 3 mm, at least 3.3 mm, or at least 3.8 mm. In one or more embodiments, the first thickness ranges from about 0.1mm to about 6mm, 0.2mm to about 6mm, 0.3mm to about 6mm, 0.4mm to about 6mm, 0.5mm to about 6mm, 0.6mm to about 6mm, 0.7mm to about 6mm, 0.8mm to about 6mm, 0.9mm to about 6mm, 1mm to about 6mm, 1.1mm to about 6mm, 1.2mm to about 6mm, 1.3mm to about 6mm, 1.4mm to about 6mm , 1.5mm to about 6mm, 1.6mm to about 6mm, about 1.8mm to about 6mm, about 2mm to about 6mm, about 2.2mm to about 6mm, about 2.4mm to about 6mm, about 2.6mm to about 6mm, about 2.8mm to about 6mm, about 3mm to about 6mm, about 3.1mm to about 6mm, about 3.2mm to about 6mm, about 3.3mm to about 6mm, about 3.4mm to about 6mm, about 3.5mm to about 6mm, about 3.6mm to about 6mm, about 3.7mm to about 6mm, about 3.8mm to about 6mm, about 3.9mm to about 6mm, about 4mm to about 6mm, about 4.2mm to about 6mm, about 4.4mm to about 6mm, about 4.5mm to about 6mm, About 4.6mm to about 6mm, about 4.8mm to about 6mm, about 5mm to about 6mm, about 5.2mm to about 6mm, about 5.4mm to about 6mm, about 5.5mm to about 6mm, about 5.6mm to about 6mm, about 5.8 mm to about 6mm, about 1.6mm to about 5.8mm, about 1.6mm to about 5.6mm, about 1.6mm to about 5.5mm, about 1.6mm to about 5.4mm, about 1.6mm to about 5.2mm, about 1.6mm to about 5mm, about 1.6mm to about 4.8mm, about 1.6mm to about 4.6mm, about 1.6mm to about 4.4mm, about 1.6mm to about 4.2mm, about 1.6mm to about 4mm, about 1.6mm to about 3.9mm, about 1.6mm to about 3.8mm, about 1.6mm to about 3.7mm, about 1.6mm to about 3.6mm, about 1.6mm to about 3.5mm, about 1.6mm to about 3.4mm, about 1.6mm to about 3.3mm, about 1.6mm to about 3.2mm, about 1.6mm to about 3.1mm, about 1.6mm to about 3mm, about 1.6mm to about 2.8mm, about 1.6mm to about 2.6mm, about 1.6mm to about 2.4mm, about 1.6mm to about 2.2 mm, about 1.6mm to about 2mm, about 1.6mm to about 1.8mm, about 3mm to about 5mm, or about 3mm to about 4mm. In other embodiments, the glass interlayer may be thinner than 2mm or thicker than 6mm.

In some embodiments, the glass interlayer can have a curvature (eg, a circular geometry or a tubular shape (eg, where the first major surface is the exterior of the tube and the second major surface is the interior surface of the tube)). In some embodiments, the perimeter of the glass interlayer is generally straight, while in other embodiments, the perimeter is complex. The first major surface may have apertures, slots, holes, bumps, dimples, or other geometric shapes.

As will be discussed more fully below, in one or more embodiments, glass interlayer 200 is a fusion formed borosilicate glass composition having a liquidus viscosity of at least 500 kP and 1725° C. or less T _200P .

FIG. 3 illustrates an embodiment of an automotive glazing 130 , wherein the automotive glazing 130 is a laminated structure 300 including the glass interlayer 200 of FIG. 2 as a first glass interlayer 310 . As noted above, glass interlayer 200 may comprise, consist of, or consist essentially of embodiments of the borosilicate glass compositions described herein. In the embodiment shown in FIG. 3 , the first glass interlayer 310 is bonded to the second glass interlayer 320 via an interlayer 330 . More specifically, the second glass interlayer 320 has a third main surface 332 and a fourth main surface 334 . The third main surface 332 is easily opposite to the fourth main surface 334 . The secondary surface 336 extends around the periphery of the second glass interlayer 320 and connects the third main surface 332 and the fourth main surface 334 .

A second thickness 340 is defined between the third major surface 332 and the fourth major surface 334 . In an embodiment, the second thickness 340 is less than the first thickness 210 of the first glass interlayer 310 . In an embodiment, the second glass thickness is 2 mm or less. In an embodiment, the total glass thickness (i.e., first thickness 210 plus second thickness 340) is 8mm or less, 7mm or less, 6.5mm or less, 6mm or less, 5.5mm or less Less, or 5mm or less. In an embodiment, the lower limit for total glass thickness is about 2 mm.

In an embodiment, the glass composition of the second glass interlayer 320 is different from the borosilicate glass composition of the first glass interlayer 310 . In an embodiment, the second glass composition comprises a soda lime silicate composition, an aluminosilicate glass composition, an alkali aluminosilicate glass composition, an alkali-containing borosilicate glass composition, an alkali aluminum Phosphosilicate glass composition, or alkali metal aluminoborosilicate glass composition.

Furthermore, in an embodiment, the first glass interlayer 310 and/or the second glass interlayer 320 may be strengthened. For example, the first glass interlayer 310 and/or the second glass interlayer 320 may be thermally strengthened, chemically strengthened, and/or mechanically strengthened. More specifically, in an embodiment, the first glass interlayer 310 and/or the second glass interlayer 320 are chemically strengthened by ion exchange processing. In one or more embodiments, the first glass interlayer 310 and/or the second glass interlayer 320 are mechanically strengthened by exploiting the mismatch in coefficient of thermal expansion between portions of the interlayer to create regions of compressive stress and exhibit tension. Central area of stress. In some embodiments, the first glass interlayer 310 and/or the second glass interlayer 320 may be thermally strengthened by heating the glass interlayer to a temperature above the glass transition point followed by rapid quenching. In some embodiments, various combinations of chemical strengthening, mechanical strengthening, and thermal strengthening may be used to strengthen the second glass interlayer 320 . In one or more embodiments, the second glass interlayer 320 is strengthened while the first glass interlayer 310 is unstrengthened (but may optionally be annealed), while exhibiting a surface compressive stress of less than about 3 MPa, Or about 2.5 MPa or less, 2 MPa or less, 1.5 MPa or less, 1 MPa or less, or about 0.5 MPa or less.

In one or more embodiments, the interlayer 330 bonds the second major surface 204 of the first glass interlayer 310 to the third major surface 332 of the second glass interlayer 320 . In an embodiment, the intermediate layer 330 comprises a polymer (eg, polyvinyl butyral (PVB), acoustic PVB (APVB), ionomer, vinyl acetate (EVA), thermoplastic polyurethane (TPU), polyester (PE ), polyethylene terephthalate (PET), and the like). The thickness of the intermediate layer may range from about 0.5 mm to about 2.5 mm (more specifically, from about 0.7 mm to about 1.5 mm). In other embodiments, the thickness may be less than 0.5mm or more than 2.5mm. Furthermore, in an embodiment, the intermediate layer 330 may include multiple polymer layers or films to provide various functions for the laminated structure 300 . For example, the middle layer 330 may combine at least one of display features, solar insulation, sound insulation, antenna, anti-glare processing, or anti-reflection processing. In certain embodiments, the intermediate layer 330 is modified to provide ultraviolet (UV) absorption, infrared (IR) absorption, IR reflection, acoustic control/damping, adhesion promotion, and coloration. The intermediate layer 330 may be modified by suitable additives (eg, dyes, pigments, dopants, etc.) to impart desired properties.

In one or more embodiments, the first glass interlayer 310 or the second glass interlayer 320 may be provided with a functional or decorative coating in addition to or instead of the functional or decorative film of the intermediate layer 330 . In an embodiment, the coating is at least one of an infrared reflective (IRR) coating, a glass frit, an anti-reflective coating, or a pigment coating. In an exemplary embodiment of the IRR, the second major surface 204 of the first glass interlayer 310 or the second major surface of the second glass interlayer 320 is coated with an infrared reflective film (and optionally one or more layers of a transparent dielectric film). Three major surfaces 332 . In an embodiment, the infrared reflective film includes a conductive metal (eg, silver, gold, or copper) that reduces the transmission of heat through the coated interlayers 310 , 320 . In embodiments, optional dielectric films may be used to anti-reflect against infrared reflective films and to control other properties and characteristics of the coating (eg, color and durability). In an embodiment, the dielectric film includes one or more oxides of zinc, tin, indium, bismuth, and titanium, among others. In an exemplary embodiment, the IRR coating includes one or two silver layers, each sandwiched between two transparent dielectric films. In an embodiment, the IRR coating is applied using, for example, physical or chemical vapor deposition or via a laminate.

In an embodiment, one or both of the first glass interlayer 310 and the second glass interlayer 320 includes a glass frit. In an embodiment, the glass frit is applied to, for example, the second major surface 204 of the first glass interlayer 310, the third major surface 332 of the second glass interlayer 320, and/or the fourth major surface 334 of the second glass interlayer 320 . In an embodiment, the glass frit provides an enhanced bonding surface for an adhesive (eg, interlayer 330 ) or an adhesive that bonds the glass window 130 to the bonding surface defining the opening 120 in the vehicle body 110 . Additionally, in an embodiment, the glass frit provides a decorative border for the glazing 130 . In addition, in an embodiment, a glass frit may also be used in addition to the above-mentioned IRR coating. In an embodiment, the glass frit is an enamelled glass frit. In other embodiments, the glass frit is designed to be ion exchangeable. That is, the glass frit may be applied to the ion-exchangeable glass prior to ion-exchange processing. This glass frit is configured to allow the exchange of ions between the glass and the processing bath. In an embodiment, the glass frit system is Bi-Si-B alkali system, Zn-based Bi system, Bi-Zn system, Bi system, Si-Zn-B-Ti system without Bi or low Bi, Si-Bi -Zn-B-base system, and/or Si-Bi-Ti-B-Zn-base system, etc. An example of an ion-exchangeable glass frit including a colorant comprises 45.11 mol% _Bi2O3 , 20.61 mol% _SiO2 , 13.56 mol% _Cr2O3 , 5.11 mol% _CuO , 3.48 mol _% Mole % of MnO, 3.07 mole % of ZnO, 2.35 mole % of B ₂ O ₃ , 1.68 mole % of TiO ₂ , 1.60 mole % of Na ₂ O, 1.50 mole % of Li ₂ O, 0.91 mole % mol% K ₂ O, 0.51 mol% Al ₂ O ₃ , 0.15 mol% P ₂ O ₅ , 0.079 mol% SO ₃ , 0.076 mol% BaO, 0.062 mol% ZrO ₂ , 0.060 mol % Fe ₂ O ₃ , 0.044 mol % MoO ₃ , 0.048 mol % CaO, 0.018 mol % Nb ₂ O ₅ , 0.006 mol % Cl, and 0.012 mol % SrO. Examples of ion-exchangeable glass frits are disclosed in U.S. Pat. August 19, 2009), both of which are incorporated herein by reference in their entirety.

In an embodiment, the second glass interlayer 320 may be provided using a colorant coating composed of ink (eg, organic ink). In an embodiment particularly suitable for such a colorant coating, the colorant coating is applied to either the third major surface 332 of the second glass interlayer 320 or the fourth major surface 334 of the second glass interlayer 320 relative to the first major surface 334 of the second glass interlayer 320. A glass interlayer 310 and a second glass interlayer 320 are cold formed. Advantageously, this colorant coating can be applied to the second glass interlayer 320 while the second glass interlayer 320 is in a planar configuration, and then the second glass interlayer 320 can be cold formed into a curved configuration without disrupting the colorant coating. Cloth (e.g., organic ink-coated). In an embodiment, the colorant coating comprises at least one pigment, at least one mineral filler, and a binder comprising alkoxysilane functional isocyanurate or alkoxysilane functional biuret. An example of such a colorant application is described in European Patent No. 2617690B1, which is hereby incorporated by reference in its entirety. Other suitable colorant coatings and methods of applying colorant coatings are described in U.S. Publication No. 2020/0171800A1 (Application No. 16/613,010, filed November 12, 2019) and U.S. Patent No. 9,724,727 (Application No. , filed Feb. 10, 2015), both of which are hereby incorporated by reference in their entirety.

In an embodiment, the coating is an anti-reflective coating. In a particular embodiment, an antireflective coating is applied to the fourth major surface 334 of the second glass interlayer 320 . In an embodiment, the antireflective coating includes multiple layers of low and high index materials or low, medium, and high index materials. For example, in an embodiment, the antireflective coating includes two to twelve layers of alternating low and high index materials (eg, silicon dioxide (low index) and niobium oxide (high index)). In another exemplary embodiment, the antireflective coating includes three to twelve layers of repeating low, medium, and high index materials (e.g., silicon dioxide (low index), alumina (medium index ), and niobium (high refractive index)). In yet other embodiments, the low-index material in the stack may be an ultra-low-index material (eg, magnesium fluoride or porous silicon dioxide). In general, antireflective coatings with more layers in the stack perform better at higher angles of incidence than antireflective coatings with fewer layers in the stack. For example, an antireflective coating stack with four layers has a better performance (less reflection) than an antireflective coating stack with two layers at angles of incidence eg greater than 60°. Furthermore, in embodiments, antireflective coating stacks with ultra-low index materials perform better (less reflective) compared to antireflective coating stacks with low index materials. Other antireflective coatings known in the art may also be suitable for laminate 300 .

In an embodiment, the glass interlayer 200 or laminate 300 exhibits at least one curvature comprising a radius of curvature along at least a first axis in the range of 300 mm to about 10 m. In an embodiment, the glass interlayer 200 or laminate 300 exhibits at least one curvature comprising a curvature in the range of 300 mm to about 10 m along a second axis transverse (specifically perpendicular) to the first axis radius. In other embodiments, the glass interlayer exhibits a curvature, but with a radius of curvature of less than 300 μm or greater than 10 m. In some embodiments, the curvature system is complex and varied.

In an embodiment, curvature is introduced into each glass interlayer 310 , 320 of the glass interlayer 200 or glass laminate 300 through heat treatment. The heat treatment may include a sagging process that uses gravity to shape the glass interlayer 200 or the glass interlayers 310, 320 when heated. In the relaxation step, a glass interlayer (eg, glass interlayer 200 ) is placed on a mold with an open interior, heated in a furnace (eg, a box furnace or an annealer), and allowed to gradually relax under the influence of gravity. Drape into the open interior of the mould. In one or more embodiments, the heat treatment may include a press process using a mold to shape the glass interlayer 200 or the glass interlayers 310 , 320 after or while heating. In some embodiments, two glass interlayers (eg, glass interlayers 310, 320) are formed together in a "pair forming" process. In such a process, one glass interlayer is placed on top of another glass interlayer to form a stack (which may also include an intermediate release layer) that is placed on a mold. In an embodiment, to facilitate the pair forming process, the pair forming temperature (temperature at ¹⁰¹¹ Poise) of the glass interlayers 310, 320 as the inner glass interlayer and/or thinner glass interlayer is higher than that of the outer glass interlayer and/or Thicker glass interlayers 310,320.

In one or more embodiments, the mold may have an open interior for sag handling. Both the stack and the mold are heated by placing them in a furnace, and the stack is gradually heated to the bending or sagging temperature of the glass interlayer. During this process, the interlayers are formed together into a curved shape. Advantageously, at least some of the borosilicate glass compositions of the present disclosure have viscosity profiles at a viscosity of 10 ¹¹ poise that are similar to conventional float-forming borosilicate glass compositions, allowing the use of existing equipment and techniques to The glass interlayer 200 or glass interlayers 310, 320 are formed.

According to an exemplary embodiment, the heating time and temperature are selected to achieve the desired degree of curvature and final shape. Subsequently, the glass interlayer or interlayers of glass are removed from the furnace and allowed to cool. For glass interlayers formed in pairs, the two glass interlayers are separated, reassembled with an interlayer (e.g., interlayer 330) between the glass interlayers, and heated, for example, under vacuum to seal the glass interlayer and interlayer together , to form a stack.

In one or more embodiments, only one glass interlayer is bent using heat (e.g., by a sagging process or a pressing process), while the other glass interlayer is bent using a cold forming process by pressing the glass interlayer to be bent Formed to conform to a glass interlayer that has been bent at a temperature less than the softening temperature of the glass composition, more specifically at a temperature of 200°C or less, 100°C or less, 50°C or less, or at room temperature . The pressure to cold form a glass interlayer relative to another glass interlayer can be provided by, for example, vacuum, mechanical pressing, or one or more clamps. The cold-formed glass interlayer can be held in conformity with the curved glass interlayer via an interlayer and/or mechanically clamped or coupled thereto.

FIG. 4 illustrates an exemplary embodiment of a curved glass laminate 400 . As can be seen from FIG. 4 , the second major surface 204 of the first glass interlayer 310 has a first depth of curvature 410 defined as the maximum depth from the plane of the second major surface 204 (dashed line). In embodiments where the second glass interlayer 320 is curved, the fourth major surface 334 of the second glass interlayer 320 has a second depth of curvature 420 defined as distance from the plane of the fourth major surface 334 (dashed line). maximum depth.

In an embodiment, one or both of the first depth of curvature 410 and the second depth of curvature 420 is about 2 mm or greater. The depth of curvature can be defined as the maximum distance of a surface from the normal distance of a plane defined by points on the perimeter of the surface. For example, one or both of the first depth of curvature 410 and the second depth of curvature 420 may range from about 2 mm to about 30 mm. In an embodiment, the first depth of curvature 410 and the second depth of curvature 420 are substantially equal to each other. In one or more embodiments, the first depth of curvature 410 is within 10% of the second depth of curvature 420 , more particularly within 5% of the second depth of curvature 420 . To illustrate, the second depth of curvature 420 is about 15 mm, while the first depth of curvature 410 ranges from about 13.5 mm to about 16.5 mm (or within 10% of the second sag depth 420 ).

In one or more embodiments, the first curved glass interlayer 310 and the second curved glass interlayer 330 comprise A shape deviation of ±5 mm or less between the first curved glass interlayer 310 and the second curved glass interlayer 320 . In one or more embodiments, the shape deviation is measured between the second major surface 204 and the third major surface 332 or between the first major surface 202 and the fourth major surface 334 . In one or more embodiments, the shape deviation between the first glass interlayer 310 and the second glass interlayer 320 is about ±4 mm or less, about ±3 mm or less, about ±2 mm or less, about ±2 mm or less, about ±1mm or less, about ±0.8mm or less, about ±0.6mm or less, about ±0.5mm or less, about ±0.4mm or less, about ±0.3mm or less, about ±0.2mm or less, or about ±0.1 mm or less. As used herein, shape deviations apply to stacked glass interlayers (that is, without intervening layers), and refer to either the second major surface 204 and the third major surface 332 or the first major surface 202 and the fourth major surface 334 respectively. The maximum deviation of the desired curvature between the coordination positions of .

In one or more embodiments, one or both of first major surface 202 and fourth major surface 334 exhibit minimal optical distortion. For example, one or both of first major surface 202 and fourth major surface 334 exhibit less than about 400 milli-diopters, less than about 300 millidiopters, less than about 250 millidiopters, or less than about 200 millidiopters. A suitable optical distortion detector is supplied by ISRA VISIION AG, Darmstadt, Germany under the trade name SCREENSCAN-Faultfinder. In one or more embodiments, one or both of first major surface 202 and fourth major surface 334 exhibit about 190 millidiopters or less, about 180 millidiopters or less, about 170 millidiopters or less less, about 160 milli-diopters or less, about 150 milli-diopters or less, about 140 milli-diopters or less, about 130 milli-diopters or less, about 120 milli-diopters or less, about 110 milli-diopters or less, About 100 milli-Diopters or less, about 90 milli-Diopters or less, about 80 milli-Diopters or less, about 70 milli-Diopters or less, about 60 milli-Diopters or less, or about 50 milli-Diopters or less. Optical distortion as used herein refers to the maximum optical distortion measured on the respective surface.

The reduction in optical distortion of glass interlayer 200 or glass interlayers 310, 320 is believed to be related to the borosilicate glass compositions disclosed herein and the fusion-forming process possible with the disclosed borosilicate glass compositions. As far as the forming process is concerned, conventional float glass techniques for forming borosilicate glass compositions involve floating molten glass on liquid tin, when floating on tin the glass naturally has a thickness of 6 mm or more. To create the lower thickness, the glass is stretched or stretched while floating, which creates a change in thickness across the surface of the glass known as a stretch line and creates internal stresses. Both stretched line segments and internal stresses can cause optical distortion. Such stretch lines and internal stresses are substantially avoided by fusing to form borosilicate glass compositions according to the present disclosure. In addition, the outer surfaces of the glass interlayer 200 or the glass interlayers 310, 320 are not in contact with any structure during fusion formation, which also reduces optical distortion. Regarding composition, the borosilicate glass disclosed herein allows fusion formation of glass interlayer 200 or glass interlayers 310 , 320 by providing a liquidus viscosity of at least 500 kP and a T _200P of 1725° C. or less. In addition, borosilicate glass compositions according to the present disclosure are also believed to reduce refractive index variation across the surfaces of glass interlayer 200 or glass interlayers 310, 320 compared to conventionally used soda lime silicate glass compositions. . It is also known that a change in the refractive index causes optical distortion, and thus a reduction in the change in the refractive index is expected to reduce the optical distortion.

In one or more embodiments, the first major surface or the second major surface of the first curved glass interlayer exhibits lower film tensile stress. Membrane tensile stress occurs during the cooling of the bent interlayer and laminate. As the glass cools, the major and edge surfaces (orthogonal to the major surfaces) may experience surface compression that is counteracted by the central region exhibiting tensile stress. In some cases, this stress can create problems around the perimeter where edge cooling effects create stress and the bending tool establishes a stress-producing thermal gradient. The low CTE associated with embodiments of the presently disclosed borosilicate glass compositions minimizes adverse residual stresses that may arise during the annealing process of thermal formation. This stress is proportional to the CTE, and thus by reducing the CTE of the borosilicate glass composition, the residual stress is also reduced.

Bending or shaping can introduce additional surface tension near the edges and bring the central stretched region close to the glass surface. Thus, the film tensile stress is the tensile stress measured near the edge (eg, about 10 to 25 mm from the edge surface). In one or more embodiments, the film tensile stress at the first major surface or the second major surface of the dioxane curved glass interlayer is less than about 7 MPa as measured by a surface strain gauge according to ASTM C1279 (MPa). Examples of such surface strain gauges are edge strain gauges or VRPs (both commercially available from Strainoptic Technologies). In one or more embodiments, the film tensile stress at the first major surface or the second major surface of the first curved glass interlayer is about 6 MPa or less, about 5 MPa or less, about 4 MPa or less , or about 3MPa or less. In one or more embodiments, the lower limit of film tensile stress is about 0.01 MPa or about 0.1 MPa. In other embodiments, the film tensile stress is negligible (eg, about 0). Stress systems described herein are designated as compression or tension, where the magnitude of such stress is given as an absolute value.

In one or more embodiments, the laminate 300, 400 may have a thickness of 10 mm or less, 9 mm or less, 8 mm or less, 7 mm or less, or 6 mm or less, wherein the thickness includes The sum of the thicknesses of the first glass interlayer 310 , the second glass interlayer 320 , and the intermediate layer 330 . In various embodiments, the laminate 300, 400 may have a thickness in the range of about 1.8 mm to about 10 mm, or in the range of about 1.8 mm to about 9 mm, or in the range of about 1.8 mm to about 8 mm, Or in the range of about 1.8mm to about 7mm, or in the range of about 1.8mm to about 6mm, or in the range of 1.8mm to about 5mm, or in the range of 2.1mm to about 10mm, or in the range of about 2.1 mm to about 9mm, or about 2.1mm to about 8mm, or about 2.1mm to about 7mm, or about 2.1mm to about 6mm, or about 2.1mm to about In the range of about 5mm, or in the range of about 2.4mm to about 10mm, or in the range of about 2.4mm to about 9mm, or in the range of about 2.4mm to about 8mm, or in the range of about 2.4mm to about 7mm In the range of, or in the range of about 2.4mm to about 6mm, or in the range of about 2.4mm to about 5mm, or in the range of about 3.4mm to about 10mm, or in the range of about 3.4mm to about 9mm In, or in the range of about 3.4mm to about 8mm, or in the range of about 3.4mm to about 7mm, or in the range of about 3.4mm to about 6mm, or in the range of about 3.4mm to about 5mm. In other embodiments, the laminate thickness may be less than 1.8 mm or greater than 10 mm.

In one or more embodiments, compared to the first curved glass interlayer (or the first glass interlayer used to form the first curved glass interlayer), the second curved glass interlayer (or used to form the second curved glass interlayer The second glass interlayer) is relatively thin. In other words, the thickness of the first curved glass interlayer (or the first glass interlayer used to form the first curved glass interlayer) is greater than the thickness of the second curved glass interlayer (or the second glass interlayer used to form the second curved glass interlayer). In one or more embodiments, the first thickness (or the thickness of the first glass interlayer used to form the first curved glass interlayer) is more than twice the second thickness. In one or more embodiments, the first thickness (or the thickness of the first glass interlayer used to form the first curved glass interlayer) ranges from about 1.5 times to about 10 times the second thickness (eg, about 1.75 times to about 10 times, about 2 times to about 10 times, about 2.25 times to about 10 times, about 2.5 times to about 10 times, about 2.75 times to about 10 times, about 3 times to about 10 times, about 3.25 times to about 10 times, about 3.5 times to about 10 times, about 3.75 times to about 10 times, about 4 times to about 10 times, about 1.5 times to about 9 times, about 1.5 times to about 8 times, about 1.5 times to about 7.5 times, about 1.5 times to about 7 times, about 1.5 times to about 6.5 times, about 1.5 times to about 6 times, about 1.5 times to about 5.5 times, about 1.5 times to about 5 times, about 1.5 times to about 4.5 times , about 1.5 times to about 4 times, about 1.5 times to about 3.5 times, about 2 times to about 7 times, about 2.5 times to about 6 times, about 3 times to about 6 times). In other embodiments, the interlayers may have other sizes (eg, the second interlayer is thicker than the first interlayer, or has the same thickness).

In one or more embodiments, the second thickness (or the thickness of the second glass interlayer used to form the second curved glass interlayer) is less than 2.0 mm (eg, 1.95 mm or less, 1.9 mm or less , 1.85mm or less, 1.8mm or less, 1.75mm or less, 1.7mm or less, 1.65mm or less, 1.6mm or less, 1.55mm or less, 1.5mm or less, 1.45 mm or less, 1.4mm or less, 1.35mm or less, 1.3mm or less, 1.25mm or less, 1.2mm or less, 1.15mm or less, 1.1mm or less, 1.05mm or less Less, 1mm or less, 0.95mm or less, 0.9mm or less, 0.85mm or less, 0.8mm or less, 0.75mm or less, 0.7mm or less, 0.65mm or less, 0.6mm or less, 0.55mm or less, 0.5mm or less, 0.45mm or less, 0.4mm or less, 0.35mm or less, 0.3mm or less, 0.25mm or less, 0.2mm or less, 0.15 mm or less, or about 0.1 mm or less). The lower limit of the thickness may be 0.1 mm, 0.2 mm, or 0.3 mm. In some embodiments, the second thickness (or the thickness of the second glass interlayer used to form the second curved glass interlayer) ranges from about 0.1 mm to less than about 2.0 mm, about 0.1 mm to about 1.9 mm, about 0.1mm to about 1.8mm, about 0.1mm to about 1.7mm, about 0.1mm to about 1.6mm, about 0.1mm to about 1.5mm, about 0.1mm to about 1.4mm, about 0.1mm to about 1.3mm, about 0.1mm to about 1.2 mm, about 0.1 mm to about 1.1 mm, about 0.1 mm to about 1 mm, about 0.1 mm to about 0.9 mm, about 0.1 mm to about 0.8 mm, about 0.1 mm to about 0.7 mm, about 0.2 mm to less than About 2.0mm, about 0.3mm to less than about 2.0mm, about 0.4mm to less than about 2.0mm, about 0.5mm to less than about 2.0mm, about 0.6mm to less than about 2.0mm, about 0.7mm to less than About 2.0 mm, about 0.8 mm to less than about 2.0 mm, about 0.9 mm to less than about 2.0 mm, or about 1.0 mm to about 2.0 mm. In other embodiments, the second layer may be thicker than 2.0 mm or thinner than 0.1 mm (eg, less than 700 μm, 500 μm, 300 μm, 200 μm, 100 μm, 80 μm, 40 μm, and/or at least 10 μm).

In some embodiments, the first thickness (or the thickness of the first glass interlayer used to form the first curved glass interlayer) is about 2.0 mm or greater. In such an embodiment, the first thickness (or the thickness of the first glass interlayer used to form the first curved glass interlayer) is the same as the second thickness (or the thickness of the second glass interlayer used to form the second curved glass interlayer) different from each other. For example, the first thickness (or the thickness of the first glass interlayer used to form the first curved glass interlayer) is about 2.0 mm or greater, about 2.1 mm or greater, about 2.2 mm or greater, about 2.3 mm or more, about 2.4mm or more, about 2.5mm or more, about 2.6mm or more, about 2.7mm or more, about 2.8mm or more, about 2.9mm or more, about 3.0mm or larger, about 3.1mm or larger, about 3.2mm or larger, about 3.3mm or larger, 3.4mm or larger, 3.5mm or larger, 3.6mm or larger, 3.7mm or larger, 3.8 mm or greater, 3.9mm or greater, 4mm or greater, 4.2mm or greater, 4.4mm or greater, 4.6mm or greater, 4.8mm or greater, 5mm or greater, 5.2mm or greater , 5.4mm or greater, 5.6mm or greater, 5.8mm or greater, or 6mm or greater. In some embodiments, the first thickness (or the thickness of the first glass interlayer used to form the first curved glass interlayer) ranges from about 2.0 mm to about 6 mm, about 2.1 mm to about 6 mm, about 2.2 mm to about 6mm, about 2.3mm to about 6mm, about 2.4mm to about 6mm, about 2.5mm to about 6mm, about 2.6mm to about 6mm, about 2.8mm to about 6mm, about 3mm to about 6mm, about 3.2mm to about 6mm, About 3.4mm to about 6mm, about 3.6mm to about 6mm, about 3.8mm to about 6mm, about 4mm to about 6mm, about 2.0mm to about 5.8mm, about 2.0mm to about 5.6mm, about 2.0mm to about 5.5mm , about 2.0mm to about 5.4mm, about 2.0mm to about 5.2mm, about 2.0mm to about 5mm, about 2.0mm to about 4.8mm, about 2.0mm to about 4.6mm, about 2.0mm to about 4.4mm, about 2.0 mm to about 4.2mm, about 2.0mm to about 4mm, about 2.0mm to about t3.8mm, about 2.0mm to about 3.6mm, about 2.0mm to about 3.4mm, about 2.0mm to about 3.2mm, or about 2.0mm to about 3mm. In other embodiments, the first interlayer may be thicker than 10.0 mm or thinner than 2.0 mm (e.g., less than 1.5 mm, 1.0 mm, 700 μm, 500 μm, 300 μm, 200 μm, 100 μm, 80 μm, 40 μm, and/or at least 10 μm).

In one or more specific examples, the first thickness (or the thickness of the first glass interlayer used to form the first curved glass interlayer) is about 2.0 mm to about 3.5 mm, and the second thickness (or the thickness used to form the first curved glass interlayer) is about 2.0 mm to about 3.5 mm. The thickness of the second glass interlayer of the two curved glass interlayers) ranges from about 0.1 mm to less than about 2.0 mm. In an embodiment, the ratio of the first thickness to the total glass thickness is at least 0.7, or at least 0.75, or at least 0.8, or at least 0.85, or at least 0.9.

In one or more embodiments, the laminate 300, 400 is substantially free of visual distortion as measured by ASTM C1652/C1652M. In specific embodiments, the laminate, the first curved glass interlayer, and/or the second curved glass interlayer are substantially free of wrinkles or distortions that are visually detectable by the naked eye, according to ASTM C1652/C1652M.

In one or more embodiments, as measured by a surface stress meter (e.g., a surface stress meter (“FSM”) commercially available under the trade designation FSM-6000 from Orihara Industrial Co., Ltd. (Japan)), The first major surface 202 or the second major surface 204 includes a surface compressive stress of less than 3 MPa. In some embodiments, as described herein, the first curved glass interlayer is not strengthened (but may optionally be annealed), and exhibits a surface compressive stress of less than about 3 MPa, or about 2.5 MPa or less, 2 MPa or less, 1.5 MPa or less, 1 MPa or less, or about 0.5 MPa or less. In some embodiments, such surface compressive stress ranges exist on both the first major surface and the second major surface.

In one or more embodiments, the first and second glass interlayers used to form the first curved glass interlayer and the second curved glass interlayer are prior to being formed in pairs to form the first curved glass interlayer and the second curved glass interlayer The system is substantially planar. In some cases, one or both of the first and second glass interlayers used to form the first and second curved interlayers may have a 3D or 2.5D shape without exhibiting a desired depth of curvature , and will eventually form during the pair forming process and be present in the resulting laminate. Additionally or alternatively, for aesthetic and/or functional reasons, the first curved glass interlayer (or the first glass interlayer used to form the first curved glass interlayer) is separated from the second curved glass interlayer (or the first glass interlayer used to form the second curved The thickness of one or both of the glass interlayers (a second glass interlayer) may be constant along one or more dimensions, or may vary along one or more of their dimensions. For example, a first curved glass interlayer (or the first glass interlayer used to form the first curved glass interlayer) is more closely aligned with a second curved glass interlayer (or the first glass interlayer used to form the second curved glass interlayer) than a more central region of the glass interlayer. The edges of one or both of the interlayer's second glass interlayer) can be thicker.

The lengths of the first curved glass interlayer (or the first glass interlayer used to form the first curved glass interlayer) and the second curved glass interlayer (or the second glass interlayer used to form the second curved glass interlayer) (eg, surface ( For example, the longest centerline segment of the first major surface), width (e.g., the longest dimension of the surface orthogonal to the length), and thickness (e.g., the dimension of the interlayer orthogonal to the length and width) dimensions can also be determined according to the product application or use varies. In one or more embodiments, the first curved glass interlayer (or the first glass interlayer used to form the first curved glass interlayer) includes a first length and a first width (the first thickness is related to the first length and the first width). a width orthogonal), and the second curved glass interlayer (or the second glass interlayer used to form the second curved glass interlayer) includes a second length and a second width orthogonal to the second length (the second thickness is the same as the first The second length and the second width are orthogonal). In one or more embodiments, either or both of the first length and the first width are about 0.25 meters (m) or greater. For example, the first length and/or the second length may range from about 1 m to about 3 m, from about 1.2 m to about 3 m, from about 1.4 m to about 3 m, from about 1.5 m to about 3 m, from about 1.6 m to about 3 m , about 1.8m to about 3m, about 2m to about 3m, about 1m to about 2.8m, about 1m to about 2.8m, about 1m to about 2.8m, about 1m to about 2.8m, about 1m to about 2.6m, about 1m to about 2.5m, about 1m to about 2.4m, about 1m to about 2.2m, about 1m to about 2m, about 1m to about 1.8m, about 1m to about 1.6m, about 1m to about 1.5m, about 1.2m to about 1.8m, or about 1.4mm to about 1.6m. In some embodiments, the surface dimension from perimeter to perimeter through the centroid of a respective surface (e.g., first surface, second surface, monolithic major surface, interlayer surface) is at least 1 mm, at least 1 cm, at least 10 cm, At least 1 m, and/or no more than 10 m, whereby breaks involved may not result in failure of the respective interlayer. In other embodiments, the interlayer can have other sizes.

For example, the first width and/or the second width may range from about 0.5 m to about 2 m, from about 0.6 m to about 2 m, from about 0.8 m to about 2 m, from about 1 m to about 2 m, from about 1.2 m to about 2 m , about 1.4m to about 2m, about 1.5m to about 2m, about 0.5m to about 1.8m, about 0.5m to about 1.6m, about 0.5m to about 1.5m, about 0.5m to about 1.4m, about 0.5m to about 1.2 m, about 0.5 m to about 1 m, about 0.5 m to about 0.8 m, about 0.75 m to about 1.5 mm, about 0.75 m to about 1.25 m, or about 0.8 m to about 1.2 m. In other embodiments, the interlayer can have other sizes.

In one or more embodiments, the second length is within 5% (e.g., about 5% or less, about 4% or less, about 3% or less, or about 2% of the first length) of the first length or less). For example, if the first length is 1.5 m, the second length may range from about 1.425 m to about 1.575 m and still be within 5% of the first length. In one or more embodiments, the second width is within 5% of the first width (e.g., about 5% or less, about 4% or less, about 3% or less, or about 2% or less). For example, if the first width is 1 m, the second width may range from about 1.05 m to about 0.95 m and still be within 5% of the first width.

Having described the glass interlayer, its laminate structure, and its use, borosilicate glass compositions are now described in more detail. In an embodiment, the borosilicate glass composition includes at least 74 mol % SiO ₂ , at least 10 mol % B ₂ O ₃ , and at least some Al ₂ O ₃ . In certain embodiments, the borosilicate glass composition includes at least 0.03 mol % iron oxide (eg, Fe ₂ O ₃ or FeO). In more particular embodiments, SiO ₂ , Al ₂ O ₃ , and B ₂ O ₃ constitute at least 90 mole percent of the borosilicate glass composition. In addition, the borosilicate glass composition has a liquidus viscosity of at least 500 kilopoise (kP) and a temperature (T _200P ) at which the viscosity is 200 poise (P) of 1725° C. or less.

In an embodiment, the borosilicate glass composition includes SiO in an amount in the range of at least about ₇₂ molar % (more specifically about 72 molar % to about 80 molar %, especially 74 molar % % to 80 mol%). For example, borosilicate glass compositions include SiO in amounts ranging from about ₇₂ mol % to about 85 mol %, about 73 mol % to about 85 mol %, about 74 mol % % to about 85 mol%, about 75 mol% to about 85 mol%, about 76 mol% to about 85 mol%, about 77 mol% to about 85 mol%, about 78 mol% to About 85 molar %, about 79 molar % to about 85 molar %, about 80 molar % to about 85 molar %, about 81 molar % to about 85 molar %, about 82 molar % to about 85 Mole %, about 83 Mole % to about 85 Mole %, about 84 Mole % to about 85 Mole %, about 74 Mole % to about 84 Mole %, about 74 Mole % to about 84 Mole % %, about 74 mol% to about 83 mol%, about 74 mol% to about 82 mol%, about 74 mol% to about 81 mol%, about 74 mol% to about 80 mol%, about 74 mol% to about 79 mol%, about 74 mol% to about 78 mol%, about 74 mol% to about 77 mol%, about 74 mol% to about 76 mol%, and therebetween All ranges and subranges of . In other embodiments, the glass may have less than 74 mol % SiO ₂ .

In an embodiment, the borosilicate glass composition includes B ₂ O ₃ in an amount ranging from about 10 mol % to about 16 mol % (more specifically, about 11.5 mol % to about 14.5 mol % %). In various embodiments, the borosilicate glass composition includes B2O3 in an amount ranging from about ₁₀ mol% to about ₁₆ mol%, about 11 mol% to about 16 mol%, About 12 mol% to about 16 mol%, about 13 mol% to about 16 mol%, about 14 mol% to about 16 mol%, about 15 mol% to about 16 mol%, about 11 Mole % to about 15 Mole %, about 11 Mole % to about 14 Mole %, about 11 Mole % to about 13 Mole %, about 11 Mole % to about 12 Mole %, about 12 Mole % % to about 13 mol%, about 12 mol% to about 14 mol%, about 14 mol% to about 15 mol%, and all ranges and subranges therebetween. In other embodiments, the glass may have less than 10 mol % B ₂ O ₃ or more than 16 mol % B ₂ O ₃ .

In an embodiment, the borosilicate glass composition includes Al ₂ O ₃ in an amount ranging from about 2 mol % to about 6 mol % (more specifically, about 2.5 mol % to about 5 mol % %). In various embodiments, the borosilicate glass composition includes _Al2O3 in an amount ranging from about ₂ mol% to about 6 mol%, about 3 mol% to about 6 mol%, From about 4 mol% to about 6 mol%, from about 5 mol% to about 6 mol%, from about 3 mol% to about 5 mol%, from about 3 mol% to about 4 mol%, about 4 Mole % to about 5 Mole %, or all ranges or subranges therebetween. Advantageously, _Al2O3 present in these amounts helps to prevent phase separation _of borosilicate glass compositions. In other embodiments, the glass may have less than 2 mol % Al ₂ O ₃ or more than 6 mol % Al ₂ O ₃ .

In an embodiment, the borosilicate glass composition comprises Na ₂ O in an amount ranging from about 3 mol % to about 8 mol % (more specifically, about 4.5 mol % to about 8 mol % ). In various embodiments, the borosilicate glass composition includes Na ₂ O in an amount ranging from about 3 mol % to about 8 mol %, about 4 mol % to about 8 mol %, about 5 mol% to about 8 mol%, about 6 mol% to about 8 mol%, about 7 mol% to about 8 mol%, about 3 mol% to about 7 mol%, about 4 mol% mol% to about 7 mol%, about 5 mol% to about 7 mol%, about 6 mol% to about 7 mol%, about 4 mol% to about 6 mol%, about 5 mol% to About 6 mole %, or any ranges and subranges therebetween. In other embodiments, the glass may have less than ₃ mol% Na2O or more than ₈ mol% Na2O.

In an embodiment, the borosilicate glass composition includes K ₂ O in an amount ranging from about 0.5 mol % to about 5 mol % (more specifically, about 0.5 mol % to about 3 mol % ). In various embodiments, the borosilicate glass composition includes K ₂ O in an amount ranging from about 0.5 mol % to about 5 mol %, about 0.6 mol % to about 5 mol %, about 0.7 mol% to about 5 mol%, about 0.8 mol% to about 5 mol%, about 0.9 mol% to about 5 mol%, about 1 mol% to about 5 mol%, about 2 mol% mol% to about 5 mol%, about 3 mol% to about 5 mol%, about 4 mol% to about 5 mol%, about 2 mol% to about 4 mol%, 3 mol% to 4 mole %, or any ranges and subranges therebetween. In other embodiments, the glass may have less than 0.8 mol% K2O or greater _{than 5} mol% K2O.

_The presence of Na2O and K2O has an effect _on the liquidus viscosity. Thus, in an embodiment, at least one of Na2O or _K2O is present in an amount of at least ₄ mol%. In an embodiment, the combined amount of Na ₂ O and K ₂ O is present in an amount of at least 5.5 mol % when other alkaline earth oxides (eg, CaO or MgO) are present in an amount of at least 1.5 mol %. _In other embodiments, the combined amount of Na2O and K2O is present in an amount of at least ₈ mole percent, regardless of alkaline earth metal oxides. _In some cases, it is believed that K2O and _Na2O tend to lower the liquidus temperature, thereby increasing the viscosity of the liquid. Furthermore, K ₂ O and Na ₂ O tend to increase the liquidus viscosity in combination with B ₂ O ₃ and Al ₂ O ₃ .

_In an embodiment, the ratio of _K2O to Na2O is from about 0.1 to about 0.75. _In embodiments, the ratio of _K2O to Na2O is about 0.15 to about 0.75, about 0.20 to about 0.75, about 0.25 to about 0.75, about 0.30 to about 0.75, about 0.35 to about 0.75, about 0.40 to about 0.75, about 0.45 to about 0.75, about 0.50 to about 0.75, about 0.55 to about 0.75, about 0.60 to about 0.75, about 0.65 to about 0.75, about 0.70 to about 0.75, about 0.1 to about 0.70, about 0.1 to about 0.65, About 0.1 to about 0.60, about 0.1 to about 0.55, about 0.1 to about 0.50, about 0.1 to about 0.45, about 0.1 to about 0.40, about 0.1 to about 0.35, about 0.1 to about 0.30, about 0.1 to about 0.25, about 0.1 to about 0.20, or about 0.1 to about 0.15.

In an embodiment, the borosilicate glass composition contains P ₂ O ₅ in an amount ranging from 0 mol % to about 4 mol %, from about 1 mol % to about 4 mol %, from about 2 mol % mol% to about 4 mol%, about 3 mol% to about 4 mol%, about 1 mol% to about 3 mol%, about 2 mol% to about 3 mol%, about 1 mol% % to about 2 mole %, or any ranges and subranges therebetween. P ₂ O ₅ tends to reduce the density of borosilicate glass compositions, which may lead to increased densification during deformation as described below. _In addition, _P2O5 is expected to increase the liquidus viscosity.

In an embodiment, the borosilicate glass composition includes CaO in an amount ranging from 0 mol% to about 5 mol%, 0 mol% to about 4 mol%, 0 mol% to about 3 mol%, 0 mol% to about 2 mol%, 0 mol% to about 1 mol%, about 1 mol% to about 5 mol%, about 2 mol% to about 5 mol% , about 3 mol% to about 5 mol%, about 4 mol% to about 5 mol%, about 2 mol% to about 4 mol%, about 2 mol% to about 3 mol%, about 3 mol% to about 4 mol%, and all ranges and subranges therebetween.

In an embodiment, the borosilicate glass composition includes MgO in an amount ranging from 0 mol % to about 5 mol % (more specifically, 0.5 mol % to 2.5 mol %). In various embodiments, the borosilicate glass composition includes MgO in an amount ranging from 0 mol % to about 5 mol %, 0 mol % to about 4 mol %, 0 mol % to About 3 mol%, 0 mol% to about 2 mol%, about 0 mol% to about 1 mol%, about 1 mol% to about 5 mol%, about 2 mol% to about 5 mol% mol%, about 3 mol% to about 5 mol%, about 4 mol% to about 5 mol%, about 2 mol% to about 4 mol%, about 2 mol% to about 3 mol% , about 3 mole % to about 4 mole %, and all ranges and subranges therebetween.

In an embodiment, the total amount of CaO and MgO is up to 5 mol%. In an embodiment, the total amount of CaO and MgO is at least 1.5 mol%, wherein the combined amount of K2O and Na2O is less _{than 7} mol%. Alkaline earth oxides (eg, CaO and MgO) tend to lower the liquidus temperature and increase the liquidus viscosity.

In embodiments, the borosilicate glass composition includes SnO ₂ in an amount up to about 0.25 mol%. In an embodiment, the borosilicate glass composition comprises _SnO in an amount ranging from 0 mol % to about 0.25 mol %, from about 0.05 mol % to about 0.25 mol %, from about 0.10 mol % % to about 0.25 mol%, about 0.15 mol% to about 0.25 mol%, about 0.20 mol% to about 0.25 mol%, about 0.05 mol% to about 0.20 mol%, about 0.05 mol% to about 0.15 mol%, about 0.05 mol% to about 0.10 mol%, about 0.10 mol% to about 0.15 mol%, about 0.10 mol% to about 0.20 mol%, about 0.15 mol% to about 0.20 Mole %, or all ranges and subranges therebetween. In some embodiments, another clarifying agent (eg, polyvalent or other oxygen absorbers including antimony, arsenic, iron, cerium, and the like) may be used in place of _SnO2 .

In an embodiment, the borosilicate glass composition includes one or more iron compounds (eg, iron(III) oxide (Fe ₂ O ₃ ) or iron(II) oxide (FeO; for example, iron oxalate (C ₂ FeO ₄ ) source)), more specifically to absorb infrared radiation from sunlight. In an embodiment, the borosilicate glass composition includes the iron compound in an amount up to about 0.50 mole percent (more specifically, about 0.20 to about 0.40 mole percent). In an embodiment, the borosilicate glass composition includes the iron compound in an amount ranging from about 0.03 mol % to about 0.50 mol %, about 0.10 mol % to about 0.50 mol %, about 0.15 mol % mol% to about 0.50 mol%, about 0.20 mol% to about 0.50 mol%, about 0.25 mol% to about 0.50 mol%, about 0.30 mol% to about 0.50 mol%, about 0.35 mol% to about 0.50 mol%, about 0.40 mol% to about 0.50 mol%, about 0.45 mol% to about 0.50 mol%, or any range or subrange therebetween. In other embodiments, other modifiers (eg, TiO ₂ ) may be used in addition to or instead of iron compounds to reduce UV radiation transmission. In an embodiment, TiO ₂ may be provided in an amount of about 0.04 mol % to about 0.12 mol %.

In an embodiment, the glass composition (or glass article formed therefrom) exhibits a liquidus viscosity of at least 500 kP (kP) and up to 50,000 kP. Advantageously, glass compositions having a liquidus viscosity greater than 1000 kP are less susceptible to pocket warping during fusion stretching. As used herein, the term "liquidus viscosity" refers to the viscosity of a molten glass at the liquidus temperature, where the term "liquidus temperature" refers to the temperature at which crystallization first occurs as the molten glass cools from the melting temperature ( Or the temperature at which the last crystal melts as the temperature increases from room temperature).

The borosilicate glass compositions described herein having a liquidus viscosity of at least 500 kP can be fusion formed at a thickness of at least 2 mm, at least 3 mm, at least 3.3 mm, or at least 3.8 mm. In some embodiments, the fusion-formed glass interlayer is substantially free of stretch lines typical of float-formed glass articles. The liquidus viscosity is determined by the following method. First, measure the liquidus temperature of the glass according to ASTM C829-81 (2015) titled "Standard Practice for Measurement of Liquidus Temperature of Glass by the Gradient Furnace Method". Next, measure the viscosity of the glass at the liquidus temperature according to ASTM C965-96 (2012) titled "Standard Practice for Measuring Viscosity of Glass Above the Softening Point".

In an embodiment, the borosilicate glass composition exhibits a strain point temperature ranging from about 480°C to about 560°C, from about 490°C to about 560°C, from about 500°C to about 560°C, from about 510°C to About 560°C, about 520°C to about 560°C, about 530°C to about 560°C, about 540°C to about 560°C, about 550°C to about 560°C, about 480°C to about 550°C, about 480°C to about 540°C °C, about 480°C to about 530°C, about 480°C to about 520°C, about 480°C to about 510°C, about 480°C to about 500°C, or any range or subrange therebetween. In the examples, the strain point temperature was determined using the beam bending viscosity method of ASTM C598-93 (2013). In the examples, the strain point is defined as the temperature at which the viscosity is 10 ^14.68 poise.

In an embodiment, the borosilicate glass composition exhibits an annealing temperature ranging from about 520°C to about 590°C, from about 530°C to about 590°C, from about 540°C to about 590°C, from about 550°C to About 590°C, about 560°C to about 590°C, about 570°C to about 590°C, about 580°C to about 590°C, about 520°C to about 580°C, about 520°C to about 570°C, about 520°C to about 560°C °C, about 520°C to about 550°C, about 520°C to about 540°C, about 520°C to about 530°C, or any range or subrange therebetween. The annealing point was determined using the beam bending viscosity method of ASTM C598-93 (2013). In the examples, the annealing point is defined as the temperature at which the viscosity is 10 ^13.18 poise.

In the examples, glass compositions exhibit a viscosity of about 200P (T _200P ) as measured by Fulcher fitting to high temperature viscosity (HTV) data (i.e., all temperature measurements from 100 kP to 100 Poise) in the temperature range up to 1725°C. For example, the range of T _200P exhibited by the glass composition may be about 1500°C to about 1725°C, about 1525°C to about 1725°C, about 1550°C to about 1725°C, about 1575°C to about 1725°C, about 1600°C °C to about 1725°C, about 1625°C to about 1725°C, about 1650°C to about 1725°C, about 1675°C to about 1725°C, about 1700°C to about 1725°C, about 1500°C to about 1700°C, about 1500°C to About 1675°C, about 1500°C to about 1650°C, about 1500°C to about 1625°C, about 1500°C to about 1600°C, about 1500°C to about 1575°C, about 1500°C to about 1550°C, about 1500°C to about 1525°C °C, or any range or subrange therebetween.

In one or more embodiments, the glass composition or glass article formed therefrom exhibits a density of less than 2.4 g/cm ³ at 20°C. In an embodiment, the density at 20°C is 2.39 g/cm ³ or less, 2.38 g/cm ³ or less, 2.37 g/cm ³ or less, 2.36 g/cm ³ or less, 2.35 g/ ^cm3 or less, 2.34g/ ^cm3 or less, 2.33g/ ^cm3 or less, 2.32g/ ^cm3 or less, 2.31g/ ^cm3 or less, 2.30g/ ^cm3 or Less, 2.29g/ ^cm3 or less, 2.28g/ ^cm3 or less, 2.27g/ ^cm3 or less, 2.26g/ ^cm3 or less, 2.25g/ ^cm3 or less, 2.24g /cm ³ or less, 2.23 g/cm ³ or less, 2.22 g/cm ³ or less, 2.21 g/cm ³ or less, or 2.20 g/cm ³ or less. In the examples, density was determined using the buoyancy method of ASTM C693-93 (2013). Advantageously, a density below 2.4 g/ ^cm3 is less than that of soda lime glass, which is commonly used in automotive glazing laminates.

As noted above, borosilicate glass compositions according to the present disclosure are capable of fusion formation. The resulting glass interlayer can be described as fusion formed. FIG. 7 illustrates an exemplary embodiment of an apparatus 700 for fusing to form a glass interlayer of a borosilicate glass composition. The fusion forming apparatus 700 includes an isopipe 702 defined by a groove 704 , a first forming surface 706 , and a second forming surface 708 . The first formed surface 706 and the second formed surface 708 are angled inwardly below the trench 704 and at the root 710 of the isopipe 702 . The borosilicate glass composition 712 of the present disclosure is provided in a molten state to the trench 704, and the borosilicate glass composition 712 overflows the trench 704 to form two streams and flow down through the forming surfaces 706, 708 . The streams of molten glass meet at root 710 to form glass interlayer 714, which cools and is cut from the flowing streams.

In an embodiment, the bond forming apparatus 700 includes a second isopipe 716 having a second groove 718 , a third forming surface 720 , and a fourth forming surface 722 . Glass composition 724 having the same or different composition as borosilicate glass composition 712 is supplied to second tank 718 in a molten state and overflows out of second tank 718 . Molten glass composition 724 flows downward through third and fourth forming surfaces 720 , 722 , and is directed outward around borosilicate glass composition 712 . In this manner, the glass composition 724 flows downwardly through the first and second forming surfaces 706 , 708 outside the flow of the borosilicate glass composition 712 . At the root 710 of the isopipe 702, the combination of the flow of borosilicate glass composition 712 and the flow of glass composition 724 creates a glass interlayer 714 with cladding layers 726a, 726b. Such cladding may mechanically strengthen the glass based on residual stresses created by the different coefficients of thermal expansion between the compositions 712, 724, or the cladding may be chemically strengthenable (eg, through ion exchange processing). The cladding layers 726a, 726b may also provide other characteristics (eg, specific optical properties) to the glass interlayer 714 formed in this manner.

An advantage of the fusion forming method is that, as the two streams of glass flowing over the channel are fused together, neither of the outer surfaces of the resulting glass article comes into contact with any part of the apparatus. Therefore, the surface properties of the fusion drawn glass article are not affected by this contact. In an embodiment, the fused formed borosilicate glass composition of the present disclosure exhibits an optical distortion of no greater than 75 millidiopters as measured by an optical distortion detector using a transmission optics device according to ASTM 1561. Conventional borosilicate glass compositions having a liquidus viscosity of less than 500 kP and a T _200P temperature of greater than 1725° C. cannot be fused at thicknesses of 2 mm or greater using the fusion stretching process, which conventional Borosilicate glass compositions are generally formed using a floatation process.

example

The following table provides various examples of fusion-formable borosilicate glass compositions. Table 1, composition and properties of examples 1-6 1 2 3 4 5 6 SiO ₂ 75.35 76.72 76.14 75.18 77.19 76.36 Al ₂ O ₃ 3.54 3.54 3.54 4.07 4.04 4.07 B _2O3 12.21 10.75 11.31 12.01 9.84 10.86 Na _{2 O} 4.60 4.67 4.68 4.61 4.70 4.57 K _2O 2.13 2.18 2.18 2.93 3.05 2.94 MgO 0.99 0.99 0.99 0.02 0.02 0.02 CaO 1.03 1.02 1.02 1.05 1.03 1.03 _SnO2 0.14 0.13 0.13 0.13 0.13 0.14 Density (g/cm ³ ) 2.307 2.308 2.308 2.316 2.335 2.324 Strain point (°C) 512.6 518.6 516.7 515.2 528.0 520.7 LTCTE (ppm/℃) 5.1 5.24 5.1 5.58 5.55 5.56 HTCTE (ppm/°C) 25.44 25.26 24.79 24.52 24.6 24.58 Young's modulus (GPa) 66.6 67.7 67.1 66.7 69.2 67.7 Poisson's ratio 0.198 0.194 0.196 0.200 0.194 0.197 Fulchers A -1.531 -1.342 -1.536 -1.163 -1.159 -1.152 Fulchers B 5661.3 5468.2 5817.5 4739.4 4858.6 4848.7 Fulchers T ₀ 140.9 182.3 142.8 227.7 232.4 224.8 200P temperature (°C) 1618 1683 1659 1596 1637 1629 35kP temperature (°C) 1073 1111 1100 1058 1084 1076 200kP temperature (°C) 970 1005 994 961 985 976 Liquidus viscosity (kP) 947 672 1578 3779 2892 4013 Mutually Cristobalite Cristobalite Cristobalite Cristobalite Cristobalite Cristobalite

Examples 1-6 are exemplary glass compositions according to one or more embodiments of the present disclosure. It can be seen from Table 1 that the liquidus viscosity of these glass compositions is much higher than 500 kP required for fusing to form glass compositions. Furthermore, the T _200P of these glasses is much lower than 1725°C. Furthermore, advantageously, these glasses have a density below 2.4 g/cm ³ . Conventional laminates utilize a thicker outer laminate of soda lime glass (with a density above 2.4 g/cm ³ ). Thus, not only are the mechanical properties enhanced, as described below, the disclosed fusion-formable borosilicate glass compositions rely on less than 2.4 g/cm ³ (more specifically 2.35 g/cm ³ or less) of their density while providing weight savings (and thus enhanced fuel efficiency). The low temperature coefficient of thermal expansion (LTCTE), obtained by measuring the expansion of the glass between temperatures of 0°C and 300°C, also enhances the thermal properties of the resulting glass interlayer. In an embodiment, the LTCTE is 5.6 ppm/°C or less (more specifically 5.3 ppm/°C or less, and specifically 5.1 ppm/°C or less). In addition to the properties just discussed, Table 1 also includes information related to strain point temperature, annealing point temperature, high temperature CTE (HTCTE), Young's modulus, and Poisson's ratio.

Table 2 below provides additional exemplary compositions according to the present disclosure. Table 2, composition and properties of examples 7-9 and comparative examples 10 and 11 7 8 9 CE10 CE11 SiO ₂ 76.75 75.93 76.38 76.10 76.25 Al ₂ O ₃ 3.57 3.53 3.56 3.53 3.52 B _2O3 11.18 11.61 12.26 8.47 11.49 Na _{2 O} 6.35 4.59 4.87 6.50 8.73 K _2O 2.04 2.13 1.01 2.15 0.00 MgO 0.00 0.03 1.81 0.06 0.00 CaO 0.01 2.05 0 3.08 0.01 _SnO2 0.11 0.11 0.11 0.11 0.00 Density (g/cm ³ ) 2.328 2.32 2.273 2.385 2.332 Strain point (°C) 518.6 525.8 506.2 543 526.6 Annealing point (°C) 564 571.4 552.9 585.4 569.7 LTCTE (ppm/℃) 5.6 5.15 4.58 6.09 -- Young's modulus (GPa) 68.7 68.3 63.1 74.1 -- Poisson's ratio 0.192 0.192 0.196 0.194 -- Fulchers A -1.121 -0.974 -1.682 -1.272 -1.023 Fulchers B 4505.1 4545.6 6535.2 4696.1 4178.6 Fulchers T ₀ 255.8 251.8 69 240.1 279.4 200P temperature (°C) 1572 1640 1710 1555 1536 35kP temperature (°C) 1051 1076 1119 1048 1030 200kP temperature (°C) 957 976 1005 955 940 Liquidus viscosity (kP) 582 855 1365 308 180 Mutually Cristobalite Cristobalite Cristobalite Cristobalite Cristobalite

Likewise, as can be seen from Table 2, Examples 7-9 of the disclosed fusion-formable borosilicate glass compositions exhibit desirable properties for fusion formation at thicknesses greater than 2 mm. In addition, the properties of borosilicate glass compositions are superior to those of soda lime glass (eg, density and LTCTE). However, as can be seen from Comparative Examples 10 and 11, compositions other than the composition disclosed herein do not have properties required for fusion formation at a relatively large thickness for fusion formation properties. Comparative Example 10 has a lower B2O3 content _of 8.47 mol _% , so that the total amount _{of SiO2} , B2O3, and _Al2O3 is less _than 90 mol%, while Comparative Example ₁₁ does not contain _K2 O or MgO with little CaO tends to increase the liquidus viscosity as described above. However, as discussed later, some embodiments may be used in windshields or other articles (eg, due to fracture behavior, whether or not the respective constituents are fusion-formable).

Table 3 below provides further exemplary compositions of borosilicate glass compositions according to the present disclosure. Table 3, the compositions of examples 12-14 and 18 and comparative examples 15-17 12 13 14 CE15 CE16 CE17 18 SiO ₂ 76.34 76.06 76.15 76.19 76.23 76.09 74.89 Al ₂ O ₃ 3.56 3.54 3.54 3.55 3.55 3.54 3.50 B _2O3 11.80 12.43 12.89 13.35 13.73 14.28 13.60 Na _{2 O} 4.29 4.15 3.85 3.55 3.33 3.12 5.22 K _2O 1.96 1.95 1.80 1.65 1.58 1.51 0.92 MgO 0.95 0.86 0.82 0.77 0.71 0.66 1.76 CaO 0.99 0.90 0.86 0.82 0.76 0.70 -- _SnO2 0.10 0.10 0.10 0.10 0.10 0.10 0.11 Density (g/cm ³ ) 2.298 2.285 2.271 2.259 2.246 2.234 2.273 Strain point (°C) 512.7 511.1 506.6 499.8 499 492 504 Annealing point (°C) 558.7 558.2 554.9 549.7 549.2 543.5 546 LTCTE (ppm/°C) 4.8 4.6 4.5 4.4 4.3 4.1 4.6 Young's modulus (GPa) 65.9 64.6 63.0 61.4 60.2 58.8 -- Poisson's ratio 0.196 0.2 0.2 0.201 0.202 0.203 -- Fulchers A -1.504 -1.647 -1.835 -1.719 -2.093 -1.727 -1.697 Fulchers B 5948 6341.6 7018.7 6898.6 7963.1 7172.3 6442.7 Fulchers T ₀ 111.3 89.1 21.2 33 -55.1 13.3 73.7 T _200P (°C) 1676 1695 1718 1749 1757 1794 1685 T _35kP (°C) 1097 1113 1121 1134 1145 1157 1106 T _200kP (°C) 987 1002 1005 1016 1022 1034 994 Liquidus viscosity (kP) 1021 1197 1752 4569 Mutually Cristobalite Cristobalite Cristobalite Cristobalite

Borosilicate glass composition Examples 12-14 and 18 in Table 3 have the liquid viscosity and T _200P temperature required for fusion formation, and the use of the disclosed borosilicate glass composition as an automotive glazing laminate The density of the outer interlayer and the favorable properties of LTCTE. Furthermore, it can be seen that these examples show that increasing the amount _of B2O3 has a density _- lowering effect. Each of Examples 12-17 had a density of less than 2.3 g/cm ³ , and certain examples had a density of 2.250 g/cm ³ or less. Comparative Examples 15-17 exhibit a T _200P temperature higher than 1725°C. Compared to Examples 12-14 and 18, Comparative Examples 15-17 had too little alkali metal oxide and too little alkali metal and alkaline earth oxide (also known as alkaline earth metal oxide) (for example, for the some fusion-forming properties), but as discussed below, for other embodiments (e.g., windshields and other articles with loop cracks including transverse and radial cracks from Vickers indenters), there may be sufficient Alkali and alkaline earth metal oxides. More specifically, each of Examples 12-14 and 15 included at least 5.5 mol % Na2O ₊ K2O and a total of at least 7.0 mol % Na2O ₊ K2O ₊ MgO ₊ CaO. Based on the examples in Tables 1-3, it is believed that embodiments of the present disclosure will exhibit the T _200P and liquidus viscosity required for fusion formation, wherein the total amount of Na2O ₊ K2O ₊ MgO+CaO is at least 7.0 Mo mol%, especially in the case of at least 5.5 mol% Na ₂ O+K ₂ O and at least 1.5 mol% MgO+CaO. It is further believed that embodiments of the present disclosure will exhibit the T _200P and liquidus viscosity required for fusion formation in which the Na ₂ O+K ₂ O system is at least 8 mol%, regardless of the amounts of MgO and CaO.

Table 4 provides additional exemplary compositions of the disclosed borosilicate glass compositions in which iron compounds (e.g., iron(II) oxide or iron(III) oxide) are further added to absorb sunlight, more specifically infrared (IR ) radiation), which leads to an increase in the temperature inside the vehicle. Thus, by providing IR absorption, automotive glazing comprising laminates with an outer interlayer of the disclosed borosilicate glass composition can provide additional fuel by reducing the heat build-up in the vehicle and the burden on the air cooling system efficiency and comfort. Table 4 provides exemplary borosilicate glass compositions of Table 4, wherein the amount of iron (Fe ₂ O ₃ ) was increased from 0 mol% to 0.44 mol%, and one composition (Example 25) mainly contained oxide Iron(II) (FeO) was used as the main iron compound. In Example 25, iron(II) oxide was provided by using iron oxalate (C ₂ FeO ₄ ) as the batch material source. The carbon system of iron oxalate leaves in the form of carbon dioxide (CO ₂ ), leaving mainly iron(II) oxide and some iron(III) oxide in the glass. Table 4, composition and optical properties of examples 19-25 3 19 20 twenty one twenty two twenty three twenty four 25 SiO ₂ 76.14 76.00 76.16 76.06 76.04 76.22 75.93 75.68 Al ₂ O ₃ 3.54 3.53 3.54 3.53 3.54 3.55 3.52 3.51 B ₂ O ₃ 11.31 11.58 11.41 11.26 11.34 11.25 11.29 12.55 Na ₂ O 4.68 4.58 4.52 4.65 4.57 4.45 4.57 4.2 K ₂ O 2.18 2.11 2.12 2.18 2.11 2.07 2.14 2.05 MgO 0.99 0.98 0.97 0.97 0.98 0.98 0.98 0.85 CaO 1.02 1.01 1.03 1.03 1.03 1.02 1.03 0.9 Fe ₂ O ₃ /FeO -- 0.07 0.15 0.22 0.28 0.37 0.44 0.16 _SnO2 0.13 0.11 0.11 0.11 0.11 0.10 0.10 0.1 Refractive index at 633nm 1.4855 1.4855 1.4855 1.4855 1.4855 1.4855 -- 1.484

Tables 5 and 6 below provide the transmittance data for the borosilicate glass compositions of Table 4 for glass interlayers having a thickness of 3.3 mm and 2.1 mm, respectively. In an embodiment, the addition of iron compounds is used to reduce visible light (ie, about 400 nm to about 750 nm), total solar transmittance, and UV transmittance for a given composition of the borosilicate glass composition. All transmittance values are measured at normal incidence. Example 3 had a visible light transmission (T _VIS ) of 92.4% and a total solar transmission (TTS) of 92.0% measured according to ISO 13837A (A/2°). By increasing the increment of Fe ₂ O ₃ , T _VIS and TTS gradually decreased. As shown in Table 4, the addition of 0.07 mol% (or 0.19 wt%) _Fe2O3 decreased T _VIS by about ₃ %, while TTS decreased by about 6%. The addition of 0.37 mol% (or 0.92 wt% _{) Fe2O3} decreased T _VIS by about 44%, while TTS decreased by about 33%. According to ISO 13837, the minimum requirement for T _VIS for glazing of road vehicles is 73%. Figure 8 provides a graph of the transmittance for Examples 3, 19-24. It can be seen that the addition _{of Fe2O3} reduces the overall measured transmission and produces a significant drop in measured transmission between about 750nm and 1500nm (corresponding to the near infrared spectrum). In an embodiment, the TTS measured according to ISO 13837A (A/2°) of an automotive glazing comprising a laminate 300, 400 comprising at least one glass interlayer comprising a fusion-formable borosilicate glass composition of the present disclosure Line of 61% or less, and/or T _VIS line of at least 73%. In such embodiments, the inventors believe interlayers and other glass interlayers have minimal effect on T _VIS (e.g., up to about a 0.5% reduction) based on previous experience in making such glazing and laminates, and would Further decrease the TTS by eg 3-5%. This is especially true in the case of the fusion-formable borosilicate glass interlayer of the present disclosure as the thicker outer interlayer of the laminate glazing. Table 5, Transmittance properties based on iron content of 3.3MM glasses glass composition Source of Fe Fe grade (wt%) UV cut-off wavelength (nm) T _UV (300-380nm) (%) T _VIS (%) TTS (%) 3 Oxide 0 <300 85.7 92.4 92.0 19 Oxide 0.19 320 59.2 89.3 85.7 20 Oxide 0.37 335 39.1 83.6 80.1 twenty one Oxide 0.55 345 26.7 75.7 74.2 twenty two Oxide 0.70 350 17.6 67.6 69.4 twenty three Oxide 0.92 365 6.1 48.8 59.2 twenty four Oxide 1.1 -- -- 44.2 56.3 25 Oxalate 0.40 330 42.2 79.6 73.8

It can also be seen from Table 5 that increasing the iron content increases the UV cut-off wavelength (that is, the wavelength at which the UV transmittance is below 10%) and reduces the total UV transmittance in the range of 300-380nm, in addition to reducing T _VIS and TTS. In Example 3, the glass composition contained no iron content. The UV cut-off wavelength is lower than 300nm, and the UV transmittance is 85.7%. As the Fe content increased from 0 wt% (or 0 mol%) to 0.92 wt% (or 0.37 mol%), the UV cut-off wavelength increased to 365 nm, while T _UV decreased to 6.1%. In addition to the T _VIS and TTS requirements noted above, embodiments of laminates 300, 400 that include at least one glass interlayer having a fusion-forming borosilicate glass composition disclosed herein have a T of less than 75%. _UV . Advantageously, reducing UV transmittance in the laminate can help reduce yellowing of the polymer interlayer. Figure 10 shows a plot of T _VIS , T _UV , and TTS for Examples 3, 19-23, and 25 as a function of iron content for a single glass interlayer based on the data contained in Table 5.

Table 6 provides the transmittance data for glass interlayers of the same compositions included in Table 5 (except Example 24, which was not included). However, the thickness of the glass interlayer dropped from 3.3mm to 2.1mm. It can be seen from Table 6 that the decrease in interlayer thickness results in a slight decrease in the UV cutoff wavelength, while each of T _UV , T _VIS , and TTS increases more than the thicker 3.3 mm interlayer of Table 5. However, Table 6 still shows that T _UV , T _VIS , and TTS still gradually decrease with the increase of iron content. 11 shows a graph of T _VIS , T _UV , and TTS as a function of iron content for a single glass interlayer based on the data contained in Table 6. FIG. It can also be seen from Tables 5 and 6 that iron(II) oxide from the iron oxalate supplied to the batch provides similar or better levels of UV and solar radiation than iron(III) oxide when considered on a weight percent basis. Radiation absorption. Table 6. Transmittance properties based on iron content of 2.1MM glasses glass composition Source of Fe Fe grade (wt%) UV cut-off wavelength (nm) T _UV (300-380nm) (%) T _VIS (%) TTS (%) 3 Oxide 0 <300 86.7 92.4 92.2 19 Oxide 0.19 315 67.5 90.5 88.0 20 Oxide 0.37 330 49.7 86.7 84.2 twenty one Oxide 0.55 335 37.8 81.5 80.0 twenty two Oxide 0.70 340 28.1 75.8 76.4 twenty three Oxide 0.92 355 13.5 61.5 68.4 25 Oxalate 0.40 320 53.5 84.1 79.6

Figures 12 and 13 illustrate plots of TTS and T _VIS for the glass compositions included in Tables 5 and 6. As shown in Figures 12 and 13, a quadratic relationship is defined as the iron content increases as the plot points move from upper right to lower left. In Figure 12, the relationship between T _VIS and TTS is given by the equation TTS=0.0097(T _VIS ) ² −0.6609(T _VIS )+68.688. In Figure 13, the relationship between T _VIS and TTS is given by the equation TTS=0.014(T _VIS ) ² −1.4278(T _VIS )+103.47. It is believed that using iron oxalate as the source material for the iron compound of the borosilicate glass can shift the curve to the right while increasing T _VIS for the same level of TTS.

In an embodiment, the stacks 300, 400 described herein may be used in a system 800 that also includes a sensor 810 as shown in FIG. 9 . More specifically, the previous discussion indicated that the laminates 300, 400 transmit electromagnetic radiation in the visible spectrum, and as shown in Figure 8, the laminates also substantially transmit electromagnetic radiation at wavelengths greater than 1500 nm (e.g., short-wave infrared) . Signals carried on electromagnetic radiation within these ranges may be transmitted through the laminate 300,400. FIG. 9 shows the sensor 810 receiving an input signal 820 and sending an output signal 830 through the stack 300 , 400 . For example, in one or more embodiments, the laminate 300 , 400 is included in the vehicle 100 as the glazing 130 as shown in FIG. 1 . In such an embodiment, the sensor 810 is disposed inside the vehicle 100 . In this way, the signals 820 , 830 can be sent or received by the vehicle 100 . In one or more embodiments, the signals 820, 830 have peak wavelengths in the visible (about 400 nm to about 750 nm) or short-wave infrared spectrum (1500 nm or greater). In embodiments, these signals facilitate autonomous or semi-autonomous driving of vehicles, open road pricing, telecommunications, traffic monitoring and control, and vehicle-to-vehicle communication, among other possibilities. An example of a sensor 810 that may be utilized in system 800 is a LIDAR that utilizes either or both visible light or shortwave infrared radiation. In embodiments that include an IRR coated stack 300, 400, the IRR coating may be ablated from the interlayer applied in the area where the sensor 810 is configured to receive and transmit signals through the stack 300, 400 Lose.

As noted above, borosilicate glass compositions of the present disclosure have surprisingly improved deformation properties compared to conventional soda lime glass compositions and even conventional borosilicate glass compositions. More specifically, the inventors have discovered that glass interlayers formed from the borosilicate glass compositions disclosed herein surprisingly and unexpectedly densify after deformation, which can limit damage caused by, for example, rocks and other flying objects from roads. Radial crack propagation produced by the fragments.

Figures 5A to 5C are diagrams for the borosilicate glass composition shown herein (Figure 5A), the conventional soda lime silicate glass composition (Figure 5B), and the conventional borosilicate The glass composition (Fig. 5C) was formed from cracks created by quasi-static indentation using a Vickers indentation tip using 2 kilogram force (kgf). It is believed that the quasi-static indentation test using a Vickers tip provides a good indication of the windshield's performance when the outer surface of the windshield is struck by flying debris (eg rocks).

In this test, the more conventional borosilicate glass composition includes 83.60 mol % SiO ₂ , 1.20 mol % Al ₂ O ₃ , 11.60 mol % B ₂ O ₃ in terms of formability , 3.00 mol% Na ₂ O, and 0.70 mol% K ₂ O. The density of this conventional borosilicate glass composition is 2.23g/cm ³ , the strain point is 518°C, the annealing point is 560°C, the LTCTE is 3.25pm/°C, and the Young's modulus is 64GPa. and Poisson's ratio is 0.2. Thus, conventional borosilicate glass compositions include less Al ₂ O ₃ , less total alkali content (especially K ₂ O) than embodiments of the borosilicate glass compositions of the present disclosure. , and less total alkaline earth content. Such conventional borosilicate glass compositions can be used in environments where a low coefficient of thermal expansion (eg, 3.3 ppm/°C or less) is desired. Alkali and alkaline earth oxides tend to increase the coefficient of thermal expansion. Here, a slight increase in the coefficient of thermal expansion to about 5-6 ppm/°C is balanced against the ability to fuse to form borosilicate glass compositions of the present disclosure by increasing the liquidus viscosity and decreasing the T _200P temperature. Furthermore, as will be discussed below, the disclosed borosilicate glass compositions have a surprising and unexpected effect on the fracture properties of glass interlayers made from borosilicate glass compositions.

As can be seen in Figures 5A-5C, each glass composition exhibits radial cracks 510 extending outward from the point where the Vickers indentation tip is pressed into the respective interlayer. However, as shown in FIG. 5A, the glass interlayer of the borosilicate glass composition of the present disclosure exhibits the formation of an annular crack 520 that confines the radial crack 510 and prevents its further growth. More specifically, the radial crack 510 will not continue to extend radially because the radial crack 510 is likely (e.g., more likely, statistically more likely, at least 51% likely, at least 60% likely, at least 80% of sample sizes that may exceed 100) are stopped without crossing (eg, being interrupted) the annular crack 520 . Advantageously, by limiting the propagation of the radial cracks 510, the impact on the overall strength of the glass interlayer (which would degrade the strength) is reduced.

The graphs in Figures 5B and 5C show the morphology of the line segment cross-sections of the cracks shown in the micrographs of Figures 5B and 5C. As can be seen from Figure 5B, the radial crack 510 has a valley 530 at the center of the figure, where the depth below the surface is the deepest. For the soda lime silicate glass of FIG. 5B , the structure of the glass provides a relatively reduced free volume, and the fractured glass network undergoes shear under vigorous contact, resulting in surface packing up to peak 540 . Consequently, the surface around the radial crack 510 is raised, as shown in the photomicrograph of FIG. 5B.

For the conventional borosilicate glass composition of Figure 5C, there is a relatively higher free volume than soda lime silicate glass and a highly connected network in the glass structure that densifies preferentially under sharp contact. Radial crack 510 still includes a central valley 530 at the center of the plot, but due to densification of the structure (shown by arrow 550) that would preserve volume, there is no substantial peak at the edge of radial crack 510, resulting in Higher hoop stress producing clusters of hoop cracks shown in the photomicrograph of Fig. 5C.

Returning to Figure 5A, a comparison between the conventional borosilicate glass composition of Figure 5C and the borosilicate glass composition of the present disclosure can be seen. In the graph of Figure 5A, the annular rupture stress system is shown as a function of distance from the contact circle of the indenter. For a conventional borosilicate glass composition (indicated by curve 560), the hoop stress decreases with increasing distance from the contact circle, which places the greatest hoop rupture stress at the periphery of the contact circle. However, stress field analysis of the cracks in Figures 5A and 5C for borosilicate glass compositions of the present disclosure shows that the maximum annular fracture stress (indicated by the asterisk 570) is surprisingly and unexpectedly related to the contact circle The perimeters are separated by a distance. For borosilicate glass compositions of the present disclosure, the strength-limiting centerline and radial cracks 510 are contained within annular cracks 520 by forming rings at a distance moved away from the crack boundaries.

Although the Vickers indentation test considers quasi-static loading (that is, the load is applied slowly so that the inertial effects of the load are negligible), the Vickers dart drop test also found Behaves the same as conventional float borosilicate glass and outperforms soda lime silicate glass when subjected to dynamic loads. In the Vickers dart drop test, a dart with a Vickers indentation tip (136°) and a weight of 8.6g is dropped from increasing heights (50mm increments) until a visible crack forms in the glass interlayer ( That is, cracks with a length of at least 10 mm). Soda lime silicate glass has an average height of visible crack formation of less than 600mm. The borosilicate glass of the present disclosure has an average height before visible crack formation (specifically greater than 650 mm) of over 600 mm, which is about the same as expected for conventional borosilicate glass compositions. It is believed that the dart drop test provides an indication of the contact rate and force required for radial crack formation in borosilicate glass compositions of the present disclosure to exceed the ability of the glass to densify to form annular cracks.

As noted above, the borosilicate glass compositions of the present disclosure form glass interlayers that are more resistant to thermal shock than soda lime silicate glass. The effect of thermal shock load is shown in Fig. 6A and Fig. 6B. More specifically, samples of fusion-formed glass compositions of the present disclosure (FIG. 6A) and soda-lime glass (FIG. 6B) were indented using a Vickers indenter at 2 kgf, as described above with respect to FIGS. 5A and discussed in Figure 5B. Then, heat the sample up to 150°C, and while the sample is still hot, drop a drop of water (25°C ± 5°C) onto the indentation site. As shown in Figure 6B, soda-lime-silicate glass cracks propagate easily during this thermal shock event. In contrast, cracks in fusion-formed borosilicate glass compositions remain confined within annular crack boundaries, as shown in Figure 6A. One reason for the resistance to thermal shock is the annular crack boundary that prevents radial crack propagation. Another reason for resistance to thermal shock is that the LTCTE of the borosilicate glass composition formed by fusion is significantly lower than that of soda calcium silicate (the borosilicate glass composition that can be fused is 5.6ppm/℃ or less, The sodium calcium silicate system is 8.0ppm/℃).

It is not to be considered that any method described herein must be constructed to perform its steps in a particular order, unless expressly stated otherwise. Thus, where a method claim does not actually recite the order of its steps or does not specify in the claim or description that the steps are to be limited to a particular order, no particular order is to be inferred. Furthermore, the article "a" as used herein is intended to include one or more parts or elements and is not intended to be construed as meaning only one.

Those of ordinary skill in the art will appreciate that various modifications and changes can be made without departing from the spirit or scope of the disclosed embodiments. Since those of ordinary skill in the art can conceive modified combinations, subcombinations and variations of the disclosed embodiments comprising the spirit and substance of the embodiments, the disclosed embodiments should be construed to be included within the scope of the appended claims and their equivalents. Everything within the category of things.

According to an exemplary embodiment and to facilitate the above disclosed information, a vehicle windshield or other article may include a first interlayer (eg, outer interlayer, glass sheet; see, eg, first glass interlayer 310 of FIG. 3 ), a second an interlayer (e.g., outer interlayer, glass sheet; see, e.g., second glass interlayer 320), and an interlayer (see, e.g., interlayer 330), the first interlayer comprising a first major surface (e.g., outer surface, forward facing surface) and a second major surface opposite the first major surface, the second interlayer includes a third major surface and a fourth major surface opposite the third major surface, an intermediate layer coupling the second major surface of the first interlayer to the second interlayer the third major surface of . In contemplated embodiments, any of the first, second, third, and/or fourth surfaces may utilize functional layers (e.g., UV-reflective layers, hydrophobic layers, adhesion-promoting layers, etc.) as described above, for example. ) to coat.

In some embodiments, the second interlayer is tempered soda lime glass. In other embodiments, the second interlayer is ion-exchanged aluminoborosilicate glass. In yet other embodiments, the second interlayer system is glass-ceramic. In some embodiments, the intermediate layer includes a polymer (eg, polyvinyl butyral).

Referring to Tables 1-3, the low temperature thermal expansion coefficient of the composition disclosed herein may range from greater than 4.4ppm/°C to less than 6.09ppm/°C (for example, from 4.5ppm/°C to 6ppm/°C, to 5.8ppm/°C, and/or to 5.6ppm/°C). As previously mentioned, LTCTE is obtained by measuring the expansion of glass at temperatures between 0°C and 300°C (eg, by thermomechanical analysis as described by ASTM test method E831 (Ref. 4)). In other contemplated embodiments, the glasses with unique fracture behavior disclosed herein may not have the viscosity for fusion formation, where the glasses may have less or higher LTCTE. In some embodiments, compositions disclosed herein have an LTCTE of less than 8.7 ppm/°C (possibly associated with soda lime glass) and/or greater than 3.25 ppm/°C (possibly associated with lower CTE borosilicates) couplet). Therefore, it may be counterintuitive that the thermal shock resistance of the glasses disclosed herein may be lower than that of some lower CTE borosilicates. However, applicants have found that higher CTEs (eg, greater than 3.25 ppm/°C) will result in higher surface compression after thermal reformation. The disadvantages associated with lower thermal shock resistance can be offset by the unique fracture mechanics of glass disclosed herein, discussed further below. It turns out that the glasses disclosed herein are more heat resistant than soda calcium by having LTCTE below 8.7 ppm/°C, and may also have improved blunt impact performance compared to other borosilicates.

In some embodiments, the first interlayer has a thickness of at least 200 μm and no more than 1 cm, and/or the thicknesses described above (eg, 0.1 mm to about 6 mm). In other contemplated embodiments, the first interlayer, single interlayer, monolithic sheet, substrate, or other article of borosilicate glass disclosed herein may have the thicknesses described above or other thicknesses (e.g., less than 200 μm and/or at least 20 μm, or at least 1 cm and/or less than 1 m), where the thickness on the article (e.g., glass sheet, interlayer) can be constant or approximately constant (e.g., on the average thickness of the individual article within 100 μm of the average thickness, for example within 10 μm of the average thickness), or the thickness may vary from product to product (for example, a glass container with a thicker lip or base).

According to an exemplary embodiment, the intermediate layer cushions the first interlayer relative to the second interlayer, thereby mitigating communication of cracks therebetween. In contemplated embodiments, the modulus of rigidity of the interlayer is less than (eg, 0.7 less than, eg, less than 0.5 of) the modulus of rigidity of the glass of the first and/or second interlayer.

According to an exemplary embodiment, the intermediate layer is adhered to the first interlayer, thereby controlling the loss of debris due to fracture of the first interlayer. In some embodiments, the intermediate layer directly contacts the first interlayer. As noted above, in some embodiments, the intermediate layer is adhered to the first interlayer, the second interlayer, and/or both, and couples the first and second interlayers. According to an exemplary embodiment, the second interlayer reinforces the first interlayer, stiffening the first interlayer to withstand a bending force applied thereto. However, in other contemplated embodiments, for example, the first interlayer may be separate from the second interlayer or intermediate layer, and may instead be a single body.

According to an exemplary embodiment, the first interlayer has a curvature such that the second major surface is concavely curved, and the second interlayer has a curvature such that the third major surface is convexly curved and cooperates with the second major surface together, and as disclosed above, such that the first major surface of the first interlayer is configured as the outwardly facing surface of the glazing (e.g., a laminated glazing, such as a windshield), and when mounted on a vehicle, is configured as outside.

According to an exemplary embodiment, the first interlayer includes a borosilicate glass composition, such as those disclosed herein. In terms of constituent oxides, the borosilicate glass composition of the first glass interlayer includes (i) SiO ₂ , B ₂ O ₃ , and/or Al ₂ O ₃ ; and (ii) one or more alkali metal oxides (also known as basic oxides; for example, Li ₂ O, Na ₂ O, K ₂ O, Rb ₂ O, Cs ₂ O) and/or one or more divalent cation oxides (zinc oxide and and/or alkaline earth metal oxides, also known as alkaline earth oxides, eg MgO, CaO, SrO, BaO).

According to some embodiments (such as those exhibiting the self-terminated crack loop behavior disclosed herein), SiO ₂ , B ₂ O ₃ , one or more alkali metal oxides, and Al ₂ O ₃ with one or more di Valence cationic oxides (when included in the composition) satisfy some (such as one or a combination of more than one) or all of the relationships: (Relationship 1) SiO ₂ ≥ 72 mole % (eg SiO ₂ ≥ 72.0, eg SiO ₂ ≥73.0, such as SiO ₂ ≥74.0, and/or SiO ₂ ≤92, such as SiO ₂ ≤90); (Relationship 2) B ₂ O ₃ ≥10 mole% (such as B ₂ O ₃ ≥10.0, such as B ₂ O ₃ ≥10.5, and/or B ₂ O ₃ ≤20, such as B ₂ O ₃ ≤18); (Relationship 3) (R ₂ O+R'O)≥Al ₂ O ₃ , such as (R ₂ O +R'O)≥(Al ₂ O ₃ +1), for example (R ₂ O+R'O)≥(Al ₂ O ₃ +2); and/or (Relationship 4) 0.80≤(1-[( 2R ₂ O+2R'O)/(SiO ₂ +2Al ₂ O ₃ +2B ₂ O ₃ )])≤0.93, wherein R ₂ O is the sum of the concentrations of one or more alkali metal oxides, and when When included in borosilicate glass compositions, the R'O series is the sum of the concentrations of one or more divalent cation oxides. R ₂ O may be, for example, the sum of Li ₂ O, Na ₂ O, K ₂ O, Rb ₂ O, Cs ₂ O, and R'O may be, for example, the sum of MgO, CaO, SrO, BaO, ZnO.

The inventive glasses disclosed herein may include additional components. In some embodiments, the borosilicate glass composition may further include P ₂ O ₅ . It should be noted that if _P2O5 is added to the glass, it should be considered as a non _- rotatable network former (u or v) when considering relation ( ₄ ) (for example, R2O or R'O), The relation (3) and (4) can be modified as (R ₂ O+R'O+P ₂ O ₅ )≥Al ₂ O ₃ , and 0.80≤(1-[(2R ₂ O+2R'O+2P ₂ O ₅ )/(SiO ₂ +2Al ₂ O ₃ +2B ₂ O ₃ )])≤0.93. Other minor chemical components (eg clarifiers SnO ₂ , Sb ₂ O ₃ , NaCl) are generally negligible in terms of rotatability and fracture behavior. Other minor chemical constituents such as colorants (e.g., at a concentration of less than 0.5 molar %) are negligible.

The applicant believes that relations (3) and (4) may be related to the fracture behavior of the borosilicate glass compositions disclosed herein, and are characteristic of the "rotatability" aspect of the respective compositions. For compositions in the form of xSiO ₂ ·yAl ₂ O ₃ ·zB ₂ O ₃ ·uR ₂ O ·vRO, where x, y, z, u, v can represent the mole % or mole of each type of oxide Fraction. If (u+v)≥y, the applicant believes that the fracture behavior is related to the rotatability of (1-[(2R ₂ O+2R'O)/(SiO ₂ +2Al ₂ O ₃ +2B ₂ O ₃ )]) parameter related. At values of the rotatability parameter between 0.80 and 0.93, applicants found that the Vickers indenter test produced radial and transverse cracks contained within smaller (diameter < 1 mm) crack loops. The upshot is that sheets of glass in this range may not crack to failure during the Vickers indenter test, but instead form small circular cracks that contain other cracks and prevent their propagation.

Similarly, Applicants believe that density may be related to the fracture behavior of the borosilicate glass compositions disclosed herein. According to an exemplary embodiment, the density of the glass is greater than 2.230 g/cm ³ and/or less than 2.397 g/cm ³ , and this cracking behavior is observed within this range.

The Vickers indenter test can be used to characterize the fracture behavior of glass, such as Gross et al. "Crack-resistant glass with high shear band density, Journal of Non-Crystalline Solids, 494 (2018) 13-20"; and Gross " Deformation and cracking behavior of glasses indented with diamond tips of various sharpness, Journal of Non-Crystalline Solids, 358 (2012) 3445-3452", both of which are incorporated herein by reference. In some embodiments, when the glass with the borosilicate glass composition of the first glass interlayer is formed to have a thickness of 1 mm and a major surface area (eg, 2 cm by ² cm squared) of at least 10 Polished flat samples (for example, 100 samples) were tested using a square-based 136° tetrahedron Vickers indenter pointing orthogonally to the center of the major surface at 25°C and 50% relative humidity (in Quasi-static displacement at a rate of 60 μm per second up to 3 kg force, the indentation load is maintained for 10 seconds (unless the breakage caused by the fracture of the sample occurs first)), under normal conditions (at least 51 times out of 100; at least 10 times) 6 times), all cracks extending radially and/or laterally through the sample from below the indenter tip (i.e., where the indenter tip contacts the glass) are interrupted by self-terminating crack loops (eg, annular cracks), Fracture of the samples from the Vickers indenter was therefore limited to cracks within the loop. Essentially, the indenter crushes the glass beneath the indenter and breaks it. However, crack loops form and prevent cracks originating from indenter contact from propagating beyond the crack loop. In contrast, transverse or radial cracks may form before and/or pass through these crack circuits in other glasses (e.g., abnormal cracks), or may not form crack circuits (e.g., normal cracks), And in either case, transverse or radial cracks will not be contained by the crack loop and may propagate through the entire glass article, causing an integral fracture through the article and breaking it.

_{Table 100 below summarizes the rotatable} The values of the property parameters, density, and Vickers indentation fracture behavior.

Table 100 (divided into three sections to fit on page) CE-101 CE-102 DSG DSX DQQ DQR DQS DQT SiO ₂ Mole % 77.18 78.97 76.42 76.38 75.35 76.72 76.14 75.18 Al ₂ O ₃ Mole % 1.98 2.04 2.04 3.56 3.54 3.54 3.54 4.07 B ₂ O ₃ Mole % 4.66 8.67 14.71 12.26 12.21 10.75 11.31 12.01 Na ₂ O Mole% 16.14 10.28 6.8 4.87 4.6 4.67 4.68 4.61 K ₂ O Mole % 1.01 2.13 2.18 2.18 2.93 MgO Mole % 1.81 0.99 0.99 0.99 0.02 CaO Mole % 0 1.03 1.02 1.02 1.05 _SnO2 Mole % 0.11 0.14 0.13 0.13 0.13 density g/ ^cm3 2.428 2.397 2.275 2.273 2.307 2.308 2.308 2.316 Rotatability value 0.64 0.8 0.88 0.86 0.84 0.83 0.83 0.84 fracture behavior normal normal Include Include Include Include Include Include QUR DQV DSP DSQ DSR DSS DST DSU SiO ₂ Mole % 77.19 76.36 76.34 76.06 76.15 76.19 76.23 76.09 Al ₂ O ₃ Mole% 4.04 4.07 3.56 3.54 3.54 3.55 3.55 3.54 B ₂ O ₃ Mole% 9.84 10.86 11.8 12.43 12.89 13.35 13.73 14.28 Na ₂ O Mole % 4.7 4.57 4.29 4.15 3.85 3.55 3.33 3.12 K ₂ O Mole % 3.05 2.94 1.96 1.95 1.8 1.65 1.58 1.51 MgO Mole% 0.02 0.02 0.95 0.86 0.82 0.77 0.71 0.66 CaO Mole % 1.03 1.03 0.99 0.9 0.86 0.82 0.76 0.7 _SnO2 Mole % 0.13 0.14 0.1 0.1 0.1 0.1 0.1 0.1 density g/ ^cm3 2.335 2.324 2.298 2.285 2.271 2.259 2.246 2.234 Rotatability value 0.83 0.84 0.85 0.85 0.87 0.88 0.88 0.89 fracture behavior Include Include Include Include Include Include Include Include DSV DSW DSX DSY DSZ DUE CE-103 CE-104 SiO ₂ Mole% 75.91 76.14 76.35 76.04 76.03 74.89 75.54 83.6 Al ₂ O ₃ Mole% 3.53 3.54 3.56 3.54 3.54 3.5 2.01 1.2 B ₂ O ₃ Mole% 12.63 12.31 12.26 12.4 12.37 13.6 19.76 11.6 Na ₂ O Mole % 4.98 6.09 4.87 4.97 6.13 5.22 2.66 3 K ₂ O Mole% 1.05 0 1.01 1.05 0 0.92 0.7 MgO Mole % 0.86 0.87 1.81 0.03 1.78 1.76 CaO Mole% 0.9 0.91 0.02 1.83 0.02 _SnO2 Mole% 0.11 0.11 0.11 0.11 0.1 0.11 density g/ ^cm3 2.286 2.284 2.273 2.295 2.273 2.273 2.147 2.23 Rotatability value 0.86 0.85 0.86 0.85 0.85 0.86 0.96 0.93 fracture behavior Include Include Include Include Include Include abnormal abnormal

In Table 100, for some compositions, fracture behavior is identified as "included," rather than "abnormal" or "normal" fracture behavior. Radial and transverse cracks contained in crack loops (eg, ring cracks) do not extend beyond the crack loop even hours after indentation testing (eg, after 12 hours, 24 hours, 72 hours). Therefore, samples containing cracks are only partially broken within the crack loop and do not break beyond the crack loop. As summarized in Table 100, Applicants observed that polished flat samples having a thickness of 1 mm to 3.3 mm were tested using a square-based 136° tetrahedron Vickers indenter with a quasi-static displacement at a rate of 60 μm per second, Until breakage or up to a maximum of 3kg force while the indentation load is maintained for 10 seconds. Furthermore, as evidenced by the inclusion of radial and transverse cracks, when rapidly cooled by placing the corresponding samples in cold water, the cracks did not propagate beyond the crack loops and the observed samples did not break outside the crack loops. Radial and transverse cracks contained in crack loops do not extend beyond the crack loop in rapidly cooled samples even hours after indentation testing (e.g., after 2 hours, 12 hours, 24 hours, 72 hours) .

For the compositions labeled DUE in Table 100, the crack loops were observed to form as rings or annular cracks (see generally Figures 5A and 6A). When loaded to a force of 2 kg, the radius of the rings ranged from 101 to 136 microns. When loaded to a force of 3 kg, the radius of the rings ranged from 119 to 229 microns.

Furthermore, for the composition marked DUE in Table 100, 19 different indentation tests were performed on a sample having a thickness of 1 mm, and the result was that 19 out of 19 occurrences included radial and transverse indentation from the indenter. Cracked ring crack. Applicants expect to obtain similar results with more tests (eg, at least 90 out of 100 samples, such as at least 95, such as at least 98).

Applicants have observed that for some samples cracks may be delayed but appear within approximately 2 hours of the indentation test. However, even hours after the indentation test (e.g., after 2 hours, 12 hours, 24 hours, 72 hours), the radial and transverse cracks of the DUE samples were contained within the crack loop and did not extend beyond the crack loop .

For the composition labeled DQS in Table 100, ten different indentation tests were carried out on samples having a thickness of 1 mm, and the result was that 10 out of 10 samples produced a composite containing radial and transverse cracks from the indenter. Crack circuit in the form of a ring crack. Even hours after indentation testing (eg, after 2 hours, 12 hours, 24 hours, 72 hours), radial and transverse cracks do not extend beyond the crack loop. Applicants expect to obtain similar results with more tests (eg, at least 90 out of 100 samples, such as at least 95, such as at least 98).

The same DQS composition was tested in a sample having a thickness of 3.3 mm, and 16 out of 20 different tests resulted in ring cracks comprising radial and transverse cracks from the indenter. Applicants expect to obtain similar results with more tests (eg, at least 50 out of 100 samples, such as at least 60, such as at least 75). Without being bound by any theory, applicants believe that the reduced percent occurrence of the 3.3 mm samples may be due to sample inhomogeneity rather than thickness.

For samples of the DSX composition in Table 100, 21 different indentation tests were performed on samples having a thickness of 1 mm, and the result was 19 occurrences of ring cracks including radial and transverse cracks from the indenter. Applicants expect to obtain similar results (eg, at least 70 out of 100 samples, such as at least 80, such as at least 90) with more tests. Even hours after the indentation test (eg, after 2 hours, 12 hours, 24 hours, 72 hours), those radial and transverse cracks did not extend beyond the crack loop.

As shown in Figure 14, Applicants were able to observe a cross-section of a sample of borosilicate glass as disclosed herein and observe the fracture of the sample via fracture photography. This image shows the rupture of a normal cone below the indentation location, showing that it then changes direction and returns to the same surface, possibly forming a crack loop. In addition, the crack cone continues to extend through the sample to the opposite surface. Applicants believe that this is a newly discovered fracture behavior of the glasses and structures of the present disclosure.

In contemplated embodiments, glass articles (e.g., sheets, interlayers, films, enclosures, tubes, containers) of borosilicate glass as disclosed herein include one or more crack loops as described above (eg having a generally circular perimeter, eg circular perimeter). The crack loops may be particularly small (e.g. less than 10 mm (e.g. less than 2 mm, e.g. less than 1 mm, e.g. less than 0.7 mm) in the direction along the surface of the glass article in cross-sectional dimension (e.g. as shown in Figure 6A) ) and/or at least 10 μm (eg at least 50 μm, eg at least 100 μm, eg at least 200 μm)).

The thickness of the article, the dimensional uniformity of the article, the rate of loading, the composition and microstructure of the borosilicate glass, the support beneath the article, the geometry of the indenter, or other parameters may affect the fracture behavior. For example, applicants demonstrated crack loops of different sizes with DUE compositions caused by different loadings as described above.

As shown in Figure 14, if the cone extends to the opposing surface and the crack loop intersects the cone, the ring crack combined with the cone can form a crack-closed section of the article that passes completely through the article. At least part of the crack closure section may have a circular perimeter (eg, at the surface of the article). The crack closure section may generally have a conical, hourglass, or other shape. Due to the unique fracture behavior of borosilicate glass disclosed herein, purposeful mechanical fracture of glass articles can be used to form holes or other precise geometries (e.g., cones that do not extend completely through surface dimples of the article) . Etchant, laser, plasma, heat, etc. may be used to further treat the article (eg, stop cracks, blunt sharp edges associated with cracks).

In contemplated embodiments, the article may have at least one crack loop and/or associated structure (e.g., holes) as described above, or the article may have more than one crack loop (eg, at least 10, at least 100 , at least 1000 crack loops), and when eg a mechanical or chemical etchant removes (broken) glass inside the crack loops, the crack loops can be connected with cones to pass completely through these articles to form holes. For example, these articles can be used as screens, screens, panels, substrates, or components in batteries or electronic devices. Segments of smaller crack loops in series (eg, perforated segments) can help control separation of sheets or shapes by guiding fractures between loops. Holes formed in the article may allow the article to be breathable and/or allow liquids, adhesives, polymers in a fluid state, conductive metals, etc. to pass through the article. The loop cracks can be arranged in one pattern or multiple patterns on the article. In some contemplated embodiments (e.g., articles (e.g., sheets) with more than one crack loop), the size of the crack loops may vary (e.g., one crack loop has a larger diameter than another crack loop of the same article at least 20%).

Controlled fracture of an article (e.g., a sheet of borosilicate glass disclosed herein) can be distinguished from using a laser to fracture a glass sheet to form vias or other holes or features because the crack loops disclosed herein There can be a single continuous loop of cracks rather than many smaller cracks extending in various directions. As evidenced by the tests disclosed herein, crack loops may be less likely to propagate beyond the loop. In some embodiments, articles comprising one or more crack loops or associated structures may require no or may require less etchant or other means of blunting or microfracturing the edges.

That being said, some of the inventive glasses disclosed herein may have conventional fracture behavior (eg, the glasses disclosed herein that are capable of fusion forming borosilicate glasses that have normal or abnormal fractures in the Vickers indentation test). Vice versa, some of the inventive glasses disclosed herein may have unique crack loop fracture behavior (for example, glasses that are borosilicate glasses but may be more difficult to fuse to form). Other embodiments may have unique fracture behavior and fusion formability, thereby providing glasses that are particularly advantageous for outer interlayers in laminated windshields or other articles disclosed herein.

U.S. Application Nos. 63/023518, filed May 12, 2020, 17/327870, filed May 24, 2021, 63/088525, filed October 7, 2020, October 12, 2020 17/068272 filed on 12 January 2021, 63/136381 filed on 12 January 2021, 63/151210 filed on 19 February 2021, 63/177536 filed on 21 April 2021 , No. 63/209489, filed May 11, 2021, is hereby incorporated by reference in its entirety. U.S. Application Serial No. 63/059105, filed July 30, 2020, is hereby incorporated by reference in its entirety. U.S. Application Serial No. 63/050181, filed July 10, 2020, is hereby incorporated by reference in its entirety.

Further examples are described herein in accordance with exemplary embodiments and to facilitate the knowledge disclosed above. Further examples are summarized in Table 200 below.

Form 200 example 26 27 28 29 SiO ₂ 75.93 75.71 76.06 75.70 Al ₂ O ₃ 3.46 3.56 3.54 3.49 B ₂ O ₃ 12.65 12.64 12.34 12.68 Na ₂ O 5.20 5.24 6.07 5.23 K ₂ O 0.92 0.94 0 0.93 MgO 1.74 1.77 .03 1.77 CaO 0 0 1.82 0.02 _SnO2 0.06 .06 0.11 0.06 _{Fe2O3 _} 0.04 0 0 0.12 Density (g/cm ³ ) 2.266 2.26 2.296 - Strain point (°C) 494 - - - Annealing point (°C) 540 - - - LTCTE (ppm/℃) 4.5 - - Young's modulus (GPa) 62.7 - - Poisson's ratio 0.196 - - Fulchers A -1.891 - - Fulchers B 7026.7 - - Fulchers T ₀ 25.3 - - 200P temperature (°C) 1702 - - 35kP temperature (°C) 1117 - - 200kP temperature (°C) 1002 - - Liquidus viscosity (kP) 1388 - - Mutually Cristobalite - -

As shown in Table 200, the composition of Example 26 includes B ₂ O ₃ greater than or equal to 12 mol %, Al ₂ O ₃ in an amount greater than or equal to 3 mol % and less than or equal to 5 mol %, greater than or equal to Or Na ₂ O in an amount equal to 4 mol % and less than or equal to 6 mol %, and satisfying the relationships (1), (2), (3) and (4) described herein. Thus, glasses constructed according to Example 26 exhibit the favorable fracture behavior described herein, and can also be fusion formed to produce glass articles suitable for the uses described herein.

In an embodiment, the amounts of Al ₂ O ₃ and Na ₂ O included in the glass composition described herein satisfy the relationship Na ₂ O>Al ₂ O ₃ +1 (for example, Na ₂ O>Al ₂ O ₃ +1.25 , Na ₂ O>Al ₂ O ₃ +1.5, Na ₂ O>Al ₂ O ₃ +1.75, Na ₂ O>Al ₂ O ₃ +2.0). In embodiments, the Al ₂ O ₃ content of the glass compositions described herein is greater than or equal to 2.0 mol % and less than or equal to 5.0 mol % (e.g., greater than or equal to 2.5 mol % and less than or equal to 5.0 mol%, greater than or equal to 3.0 mol%, or less than or equal to 5 mol%). When combined with B2O3 having greater _than or equal to 12.0 molar % (eg, greater _than or equal to 13.0 molar % B2O3, greater _than or equal to 14.0 molar _{% B2O3} , greater _than or equal to 15.0 molar % B ₂ O ₃ and less than or equal to 16 mole % B ₂ O ₃ ), this Al ₂ O ₃ content is sufficient to prevent phase separation of borosilicate glasses, but low enough that the SiO ₂ and B ₂ O ₃ are the main network formers in glass. At this level of Al ₂ O ₃ content, the Na ₂ O content in excess of Al ₂ O ₃ contributes to the dissolution of the silica during melting of the glass. _In embodiments, the Na2O content of the glass compositions described herein is less than or equal to 6.25 mole % (e.g., less than or equal to 6.20 mole %, less than or equal to 6.15 mole %, less than or equal to 6.10 mol%, less than or equal to 6.05 mol%, less than or equal to 6.0 mol%), because Na ₂ O in excess of this amount may lead to an undesirably high CTE of the glass. _In such embodiments, the Na2O content is at least 4.0 mole percent. _In the examples, since K2O tends to increase the CTE to a greater extent _than Na2O per unit of composition, the amount of K2O ₍ if included ₎ included when the Na2O content meets these criteria Less than Na ₂ O (eg, an amount greater than or equal to 0.8 mol % and less than or equal to 5 mol %, but less than the amount of Na ₂ O). For example, in embodiments, the glass compositions described herein include a ratio of _K2O to _Na2O of about 0.1 to about 0.75. Glass compositions meeting the above constraints may be suitable for fusion formation and exhibit the unique fracture behavior described herein, while still possessing an advantageously low CTE.

In embodiments, the glass compositions of the present disclosure comprise greater than or equal to 12.0 mole percent B2O3, greater _than or equal to 2.0 mole percent and less _than or equal to 5.0 mole percent _Al2O3 , or greater _than or equal to 3.0 mol% and less than or equal to 5.0 mol% of _Al2O3 , greater _than or equal to 4.0 mol% and less than or equal to 6.25 mol% of Na2O, and greater _than or equal to 0.8 mol% and less K ₂ O equal to or equal to 5.0 mole %, wherein Na ₂ O is greater than or equal to Al ₂ O ₃ +1.0, and the ratio of K ₂ O content to Na ₂ O content is greater than or equal to 0.1 and less than or equal to 0.75 . Such a set of compositional ranges facilitates the production of glasses described herein having liquidus viscosities greater than or equal to 500 kP and meeting the CTE requirements described herein (eg, LTCTE of 5.1 ppm/°C or less).

Samples having the composition of Example 26 provided in Table 300 were tested for various properties. In the first set of tests, various chemical treatments were performed on the samples to determine the chemical durability of the samples. The same chemical processing was performed on two glass samples (2 inches by 2 inches) with different compositions as a basis for comparison. Comparative Example 26A is composed of 83.60 mol% of SiO ₂ , 1.20 mol% of Al ₂ O ₃ , 11.60 mol% of B ₂ O ₃ , 3.00 mol% of Na ₂ O, and 0.70 mol% of K ₂ O borosilicate glass. Comparative Example 26B is uncolored soda lime glass. Each of the samples was immersed in a 5% w/w HCl solution at an elevated temperature of 95°C for a period of 24 hours. Samples of the same composition were also immersed in a 5% w/w NaOH solution at an elevated temperature of 95°C for a period of 6 hours. After immersion, the samples were rinsed and then dried. The light transmittance at 450 nm was measured for each sample. Haze was also measured. The results are shown in Table 300 below.

As used herein, the terms "transmittance haze" and "haze" refer to the amount of light measured in accordance with ASTM procedure D1003, entitled "Standard Test Method for Haze and Luminous Transmittance of Transparent Plastics," the contents of which are incorporated herein by reference in their entirety. Percentage of transmitted light scattered outside the pyramid of ±2.5. All haze measurements reported in this disclosure were taken on a Haze-Guard Transmittance Meter (Paul N. Gardner Company), unless otherwise noted. For optically smooth surfaces, the transmitted haze is usually close to zero.

Form 300 test medium sample discription Average weight change mg/cm ² Standard deviation mg/cm ² % Average Transmission at 450nm % average haze 5%w/w HCl Example 26 0.010 0.00 93.85 0.00 95°C Comparative Example 26A 0.010 0.00 92.69 0.00 24 hours Comparative Example 26B 0.011 0.00 91.90 0.00 5%w/w NaOH Example 26 3.09 0.03 91.99 0.00 95°C Comparative Example 26A 2.82 0.00 92.57 0.00 6 hours Comparative Example 26B 0.79 0.01 91.60 0.22

As shown in Table 300, the sample according to Example 26 described herein had a relatively low weight loss (about 0.010 mg/cm ² ) due to acidic chemical processing in HCl solution, and exhibited good optical quality, while relatively It has excellent transmittance in the two comparative examples. In the samples according to Example 26 and Comparative Example 26A, alkaline chemical processing in NaOH solution resulted in a relatively high weight loss. Although the sample according to Comparative Example 26B (soda lime glass) experienced a lower weight loss in alkaline solution, this processing resulted in increased haze representing a poorer optical appearance. These results indicate that the compositions described herein can be chemically durable for use in applications such as glass containers for various liquids, eg, pharmaceutical containers (eg, vials, syringes, ampoules, and cartridges).

As shown in Table 200, Example ₂₆ contained 0.1% by weight _Fe2O3 . The transmission spectra of the 3.3 mm thick samples were measured for comparison with the results contained in Table 5 herein. Figure 15 provides a graph of the transmittance measured according to ISO 13837 for the sample according to Example 26 and another example (Example ₃ in Table 1 above) with 0 mol % _Fe2O3 . It can be seen that the addition _{of Fe2O3} reduces the overall measured transmittance, especially in the infrared spectrum (greater than or equal to 750 nm). The UV cutoff wavelength is also greater than 300nm (approximately 320nm), indicating greater UV absorption than the iron-free embodiment, and the transmittance across the visible spectrum is greater than or equal to 90%. This result indicates that the glass described herein is suitable for use in windshields, providing shielding from solar heating and ultraviolet light, while still providing favorable transmission in the visible spectrum. The composition according to Example 26 has relatively high transmission throughout the visible spectrum, while providing beneficial transparency in windshield use, while still blocking the UV and IR portions of sunlight.

A 3.3 mm thick sample with a composition according to Example 26 and a 2.1 mm thick sample with a composition according to Example 29 were prepared for optical testing. Transmittance measurements of visible light transmittance (T _VIS ) and total solar transmittance (TTS) were performed for each sample. The results are provided in Table 400 below.

Form 400 Example 26 (3.3mm) Example 29 (2.1mm) Source of Fe Oxalate Oxalate Fe level 0.1% by weight 0.3% by weight UV cutoff 320 nm 378 nm tuv 59.5 12.0 Tvis 91.6 88.5 TTS 90.8 87.0

As shown in Table 400, the sample with 0.1 wt _{% Fe2O3} had a visible light transmittance value exceeding 90 _% despite having a larger thickness, while the sample with a larger _Fe2O3 content did not. Depending on visible light transmission requirements, the glass compositions described herein can be provided with a suitable amount of iron oxide.

Referring to FIG. 16 , samples having a thickness of 2 mm and compositions of Example 26 and Comparative Examples 26a and 26b were subjected to a flexural strength test before and after thermal shock was induced and after indentation by a Vickers indenter. Flexural strength testing is performed via ring-to-ring testing, which is generally performed according to ASTM C-1499-03 Standard Test Method for Monotonic Equibiaxial Flexural Strength of Advanced Ceramics at Ambient Temperature. More specifically, samples according to Example 26 and Comparative Examples 26a and 26b described herein were indented using a Vickers indenter at 3 kgf, as discussed above with respect to Figures 5A and 5B. Then, immediately after indentation, a ring-to-ring test was performed on some samples. After indentation, thermal shock was induced in some samples by heating the samples on a 125°C hot plate for 10 minutes. After heating, while the specimen is still hot, place a drop of water (25°C ± 5°C) on the indentation site. Then, after cooling, ring-to-ring tests were performed on the samples to determine the effect of thermal shock on flexural strength.

As shown in Figure 16, the sample according to Example 26 exhibits a level of retained strength comparable to that of the sample according to Comparative Example 26a after being subjected to thermal shock. This comparable result is expected to be the result of the ring-to-ring testing procedure. During the test, the ring is centered in the indenter and is in contact with the glass on the surface opposite the indentation. Due to the alignment between the ring and the indentation, it is believed that the glass according to Example 26 exhibits a fracture-containing behavior (annular crack comprising a radially extending crack) that has minimal influence on the retained strength measurement. Given the higher CTE of certain glasses of the present disclosure compared to conventional boron float glasses, it is not surprising that thermal shock results in a decrease in flexural strength compared to samples not subjected to thermal shock. However, despite the higher LTCTE, the sample according to Example 26 had a comparable level of retention strength as the sample constructed according to Relative Example 26a. The samples according to Example 26 had higher retained strength ratings compared to samples constructed according to Relative Example 26b, indicating that the glasses described herein offer advantages over certain existing glass compositions used in existing glass laminates. Retains strength and thermal performance.

Referring to FIGS. 17A to 17C , samples having the compositions according to Example 26 and Comparative Examples 26a and 26b were subjected to a transverse Knoop scratch test on their surfaces to determine scratch resistance. The surface of the sample was scratched using a mechanical tester holding a Knoop diamond at about 23°C and a relative humidity of about 50%. The scratch length on each sample was 5.0 mm, where the sample was scratched at a speed of 24 mm/min. Figure 17A depicts images of samples with a composition according to Example 26 and scratched with loads of 5N and 7N. Figure 17B depicts images of samples scratched with a load of 5N and 7N with a composition according to Comparative Example 26a. Figure 17C depicts images of samples scratched with a load of 5N and 7N with a composition according to Comparative Example 26b. As shown, the sample constructed according to Example 26 performed better than the comparative example in terms of scratch performance. When the samples were scratched with a load of 5N, the maximum value of the scratched transverse crack width of these samples was 67.7 μm. The maximum transverse crack widths of the samples constructed according to Comparative Examples 26a and 26b are 337.44 μm and 485 μm, respectively. Such results indicate that the glass compositions described herein can provide beneficial scratch resistance performance over certain glasses currently used in various applications (eg, automotive glazing). In an embodiment, a glass article comprising a glass composition according to the present disclosure may exhibit a maximum transverse crack width less than or equal to 80 μm (e.g. , less than or equal to 75 μm, less than or equal to 70 μm).

As described herein with respect to FIGS. 3-4 , the glass compositions described herein can be used in curved glass articles (eg, curved glass laminates). For example, a glass according to the present disclosure can be used as the first glass interlayer 310 depicted in FIGS. exchanged aluminoborosilicate glass, etc.) as the second glass interlayer 310 . For example, during manufacture of curved glass laminate 400 (see FIG. 4 ), glass interlayers 310, 320 may be subjected to a co-sagging process in which glass interlayers 310, 320, initially in a planar state, may be heated to a suitable relaxation. sag temperature to bend to the appropriate curvature depth. The "sag temperature" used herein refers to the temperature at which the viscosity of the glass substrate is 10 ¹¹ poise. The relaxation temperature is determined by fitting the Vogel-Fulcher-Tamman (VFT) equation: Log h=A+B/(TC), where T is temperature, A, B, and C are fitting constants, and h is is the dynamic viscosity, where is the annealing point data measured using a bending beam viscosity (BBV) measurement versus the softening point data measured by fiber elongation. In an embodiment, the glass compositions used in the glass interlayers 310, 320 include sag temperatures that differ from each other by 5°C or more, about 10°C or more, about 15°C or more, about 20°C or more , about 25°C or greater, about 30°C or greater, or about 35°C or greater.

In an embodiment, a glass described herein (eg, a glass according to an embodiment described herein) comprises a viscosity of 10 ¹¹ Poise at a temperature greater than or equal to 590°C and less than or equal to 630°C. This viscosity system is comparable to certain soda-lime compositions used in glass laminates at the same temperature. Thus, glasses according to the present disclosure are suitable for co-sagging using existing methods and processes, and are capable of forming laminates with good optical distortion and shape matching performance as described herein.

（等式1） 其中E係為玻璃夾層310的楊氏模量，α係為冷卻的溫度範圍內的玻璃的熱膨脹係數，t係為玻璃夾層310的厚度，R係為冷卻速率，K係為玻璃的熱擴散率，v係為玻璃的泊松比。從壓縮深度到玻璃夾層26的表面進行積分的壓縮應力可以計算為-2*

。計算根據本文所述的實例26及相對例26a及26b建構的玻璃的膜應力。結果係包含在下面的表500中。 After being heated to a suitable sag temperature and sagging to the desired curved shape, the glass interlayers 310, 320 may be cooled using a suitable cooling rate. As a result of the cooling, the surface of the glass interlayer 310 (which may be formed from glass compositions according to embodiments described herein) may be cooled at a greater rate than the central region of the glass interlayer 310, resulting in The surface of the glass interlayer 310 extends inwardly to compressive stress at the compressed depth and tensile stress in the central region extending inwardly from the compressed depth. Such tensile and compressive stresses are referred to as "annealing stresses". In an embodiment, the compressive stress from post-sagging cooling extends into the glass interlayer 310 to a compression depth equal to 0.21 times the thickness 210 of the glass interlayer 310 (see FIG. 2 ). In such an embodiment, the magnitude of the tensile stress induced by post-sag cooling can be approximated as

(Equation 1) where the E series is the Young's modulus of the glass interlayer 310, the α series is the thermal expansion coefficient of the glass in the cooling temperature range, the t series is the thickness of the glass interlayer 310, the R series is the cooling rate, and the K series is The thermal diffusivity of the glass, v is the Poisson's ratio of the glass. The compressive stress integrated from the depth of compression to the surface of the glass interlayer 26 can be calculated as -2*

. Film stresses were calculated for glasses constructed according to Example 26 and Comparative Examples 26a and 26b described herein. The results are contained in Table 500 below.

Form 500 CE 26b CE 26a Example 26 E (GPa) 72 62.8 62.7 Poisson's ratio 0.22 0.2 0.196 CTE (ppm/C) 8.8 3.25 4.5 Thermal diffusivity@600C (cm ² /s) 0.004813 0.006026 0.00565 Cooling rate (℃/s) 1.67 1.67 1.67 Glass thickness (mm) 2.1 2.1 2.1 CT (MPa) 0.52 0.13 0.19 CS (MPa) -1.03 -0.26 -0.38 CS ratio relative to Example 26 2.72 0.68 1 Glass thickness (mm) 3.8 3.8 3.8 CT (MPa) 1.69 0.42 0.62 CS (MPa) -3.38 -0.85 -1.25 CS ratio relative to Example 26 2.72 0.68 1

As shown, the magnitudes of annealed central tension (designated as "CT" in Table 500) and compressive stress (designated as "CS" in Table 500) for Example 26 were comparable to those of Comparative Example 26b (soda-lime glass) and Relative Between the values of Example 26a (existing borosilicate glass). CS and CT values are calculated under the thickness of 2.1mm and 3.8mm. 2.1mm is the commonly used thickness of the outer interlayer of automobile glass windows. As shown, at a thickness of 2.1 mm, samples constructed according to Example 26 contained an annealed tensile stress of 0.19 MPa, which is greater than the 0.13 MPa achieved by existing borosilicate glasses and less than that achieved by soda lime glasses 0.52MPa. At a thickness of 3.8 mm, samples constructed according to Example 26 contained an annealed tensile stress of 0.62 MPa, greater than the 0.42 MPa achieved by existing borosilicate glasses, and less than the 1.69 MPa achieved by soda-lime glass. Annealing stress can be measured using a SCALP device.

In accordance with exemplary embodiments and to facilitate the information disclosed above, further aspects of the exemplary glass compositions described herein are now described.

In the following paragraphs, when used to describe a specific constituent in a glass composition, the term "impurity" refers to a constituent that is not intentionally added to the glass composition and is present in an amount of less than 0.10 mol%. Impurities may be added to the glass composition inadvertently during processing of the glass composition as an impurity in another composition and/or by migration of the impurity into the composition.

In the following paragraphs, the terms "free" and "substantially free" are used interchangeably herein to refer to the amount of a particular ingredient in a glass composition that is not intentionally added to the glass composition and/or the absence of glass A specific component in a composition that is not intentionally added to a glass composition. It should be understood that the glass composition may contain trace amounts of less than 0.10 mole percent of certain constituents as contaminants or impurities.

In the following paragraphs, the term "glass former" is used herein to refer to an ingredient present in a glass composition by itself (that is, without ingredients other than impurities) capable of The rate at which glass is formed when the melt is cooled.

In the following paragraphs, the term "modifier" refers to an oxide of a monovalent or divalent metal (ie, R ₂ O or RO, where "R" represents a cation). Modifiers can be added to the glass composition to alter the atomic structure of the melt and the resulting glass. In some embodiments, modifiers can alter the coordination number of cations present in the glass former (e.g., boron in B2O3 ₎ , which can lead to the formation _of a more cohesive atomic network, and thus can provide more Good glass formation.

In the following paragraphs, the term "rare earth metals" refers to the metals listed in the lanthanide series of the IUPAC Periodic Table of the Elements, as well as yttrium and scandium. As used herein, the term "rare earth metal oxide" is used to refer to oxides of rare earth metals in different redox states (for example, " ₊₃ " for lanthanum in _La2O3 , " ₊₃ " for lanthanum in CeO2 "+4" for cerium, "+2" for europium in EuO, etc.). In general, the redox state of the rare earth metals in oxide glasses may vary, more specifically, depending on the redox state of the batch composition and/or the furnace in which the glass is melted and/or thermally processed (e.g., annealed). conditions, the redox state may change during melting. Unless otherwise stated, rare earth metal oxides are referred to herein by their normalized equations, where the rare earth metal has a redox state of "+3". Therefore, where rare earth metals with redox states other than "+3" are added to the glass composition batch, the glass composition is recalculated by adding or removing some oxygen to maintain stoichiometry. As an example, when CeO ₂ (cerium in the redox state "+4") is used as the batch ingredient, recalculate the resulting batch assuming that two moles of CeO ₂ are equal to one mole of Ce ₂ O ₃ . The material composition, and the obtained batch material composition system is represented by Ce ₂ O ₃ . As used herein, the term "RE _m O _n " is used to refer to the total content of rare earth metal oxides in all redox states present, while the term "RE ₂ O ₃ " is used to refer to the "+3" redox The total content of rare earth metal oxides in the state is also designated as "trivalent equivalent".

In the mathematical equations used in the following paragraphs, the term "min(A,B)" means the minimum of A and B, and the term "max(A,B)" means the maximum of A and B, where "A" and "B" can be any quantity (component concentration, property value, etc.). The term "abs(X)" means the absolute value (unsigned) of the quantity X.

In the glass compositions described herein, _SiO2 can function as the primary glass former. Without wishing to be bound by theory, it is believed that the tetrahedral [SiO ₄ ], which is part of the structural network of the glass, is connected to other structural units (eg, more specifically tetrahedral [AlO ₄ ] and triangular [BO ₃ ]) that are rotatable. This connection between the tetrahedra and the triangles may be responsible for the anomalous fracture behavior described here. Furthermore, it was found that _SiO2 increased the viscosity of the glass-forming melt, increased the liquidus viscosity, lowered the coefficient of thermal expansion, and increased Young's modulus, thereby improving the mechanical properties. Then, at higher levels of silica, the glass may become more chemically durable. However, when the _SiO2 content in the glass composition is too high, it may lead to unacceptably high high temperature viscosity, which may cause some melting difficulties (eg, corrosion of refractory materials in the glass melting tank). Furthermore, at very high _SiO2 content, the structural network of the glass may contain an insufficient amount of rotatable units, with the possible loss of unusual fracture behavior. Accordingly, in embodiments, in addition to the other ranges of SiO content described herein, the glass compositions described herein may contain SiO in an amount greater _than or equal to 60.0 mol % and less _than or equal to 96.0 mol % mol%, greater than or equal to 60.0 mol% and less than or equal to 80.0 mol%, greater than or equal to 60.0 mol% and less than or equal to 77.5 mol%, greater than or equal to 72.0 mol% and less than or equal to 78.0 Mole %, greater than or equal to 73.0 mole % and less than or equal to 77.0 mole %, greater than or equal to 73.4 mole % and less than or equal to 76.8 mole %, greater than or equal to 73.8 mole % and less than or equal to 76.4 mol%, greater than or equal to 74.62 mol% and less than or equal to 75.88 mol%, greater than or equal to 65.0 mol% and less than or equal to 75.9 mol%, greater than or equal to 72.0 mol% and less than or Equal to 75.9 mol%, greater than or equal to 73.0 mol% and less than or equal to 96.0 mol%, greater than or equal to 74.6 mol% and less than or equal to 75.9 mol%.

In the glass composition described herein, B ₂ O ₃ may function as a network former together with SiO ₂ and Al ₂ O ₃ . As part of the structural network of the glass, boron oxide can form tetrahedral [BO ₄ ] or triangular [BO ₃ ], depending on the content of other components. Without wishing to be bound by a particular theory, it is believed that when the content of modifiers (monovalent metal oxide R ₂ O and divalent metal oxide RO) exceeds the amount of alumina in a particular glass composition, the tetrahedral [BO ₄ ] increases in volume. In embodiments, both triangular [BO ₃ ] and tetrahedral [BO ₄ ] may play an important role in the glass compositions described herein. Tetrahedra [BO ₄ ] can increase the connectivity of the structural network, which can make the network more rigid and increase viscosity (especially at low temperatures) without causing undesired precipitation of refractory minerals from the melt. The triangle [BO ₃ ] can be a rotatable building block that can provide the unusual fracture behavior described here. Accordingly, the glass compositions of the present disclosure include boron oxide. However, when the _B2O3 content becomes too high, this may lower the liquidus viscosity, which may cause precipitation _of refractory minerals in the glass. Furthermore, at higher levels of boron oxide, the resistance of the glass composition to alkalis and acids may be unacceptable, or the glass-forming melt may be prone to liquid-liquid phase separation, which may render the glass opaque. In embodiments, in addition to the other ranges _of B2O3 content described herein, the glass compositions described herein may contain _B2O3 in an amount greater _than or equal to 1.0 mole % and less _than or equal to 25.0 mol%, greater than or equal to 5.0 mol% and less than or equal to 20.0 mol%, greater than or equal to 5.0 mol% and less than or equal to 17.0 mol%, greater than or equal to 10.5 mol% and less than or Equal to 19.0 mol%, greater than or equal to 11.75 mol% and less than or equal to 17.75 mol%, greater than or equal to 12.07 mol% and less than or equal to 13.8 mol%.

In studies, it has been empirically found that the addition of even small amounts of rare earth metal oxides to the glass compositions described herein can lead to increased liquidus temperatures and precipitation of refractory minerals. It has also been empirically found that the addition of rare earth oxides may reduce the chemical durability of the resulting glass, especially to acids. For this reason, in some embodiments of the present disclosure, the content of rare earth metal oxides in the glass composition is limited, or the glass composition may preferably not contain (or substantially contain) rare earth metal oxides.

The disclosed glass compositions may also include lithium oxide (Li ₂ O). Like other alkali metal oxides, lithium oxide can function as a modifier. However, it has been empirically found that the addition of _Li2O to the glass compositions of the present disclosure may result in increased liquidus temperature and decreased liquidus viscosity. Furthermore, glasses with _Li2O may have lower chemical durability compared to glasses with the same amount of other alkali metal oxides. It was also found that _Li2O may lead to a reduction in the anomalous fracture behavior described herein. Without wishing to be bound by theory, it is believed that the addition of _Li2O may result in a higher cation packing density, which in turn may increase the density and reduce the anomalous fracture behavior. Therefore, in embodiments, the content of Li ₂ O in the glass composition described herein may be limited, or the glass composition may preferably be free (or substantially free) of Li ₂ O.

The glass compositions of the present disclosure may also include magnesium oxide (MgO). In embodiments, magnesium oxide may be added to the glass composition to increase the Young's modulus of the resulting glass, and/or improve other mechanical properties. Magnesium oxide may beneficially not increase density, nor increase the coefficient of thermal expansion of the glass to the same extent as other glass modifiers. It is also found that adding a small amount of magnesium oxide to the glass composition of the present disclosure can improve the abnormal fracture behavior. However, when the content of MgO in the glass composition is too large, the glass-forming melt may precipitate refractory minerals, which may increase the liquidus temperature and/or cause crystallization defects in the glass product. Therefore, in an embodiment, the amount of magnesium oxide (MgO) contained in the glass composition of the present disclosure may be greater than or equal to 0.0 mol % to less than or equal to 5.0 mol %, and all ranges and subunits therebetween. scope. In an embodiment, the amount of MgO contained in the glass composition may be less than or equal to 5.0 mol%, less than or equal to 2.5 mol%, less than or equal to 2.0 mol%, less than or equal to 1.8 mol%. , or less than or equal to 1.75 mol%. In an embodiment, the amount of MgO contained in the glass composition may be greater than or equal to 0.0 mol% and less than or equal to 5.0 mol%, greater than or equal to 0.0 mol% and less than or equal to 2.0 mol%, greater than or equal to or equal to 0.0 mol% and less than or equal to 1.8 mol%, greater than or equal to 0.35 mol% and less than or equal to 1.75 mol%, greater than or equal to 0.68 mol% and less than or equal to 1.75 mol%, More than or equal to 0.0 mol% and less than or equal to 1.75 mol%.

The glass compositions of the present disclosure may also include calcium oxide (CaO). Calcium oxide can be added to glass compositions to improve chemical durability and to increase Young's modulus, thereby improving mechanical properties. In addition, alkaline earth metal oxides (eg, CaO and MgO) tend to decrease liquidus temperature and increase liquidus viscosity. It was found empirically that adding a small amount of CaO can improve the abnormal fracture behavior. However, when the CaO content is high, this may cause precipitation of refractory minerals, which may lead to crystallization defects in the glass product. In addition, when a large amount of CaO is added to a glass composition having a higher content _of B2O3, it may sometimes cause liquid _- liquid phase separation of the melt, resulting in loss of light transmittance. Therefore, in an embodiment, the amount of calcium oxide (CaO) included in the glass composition may be greater than or equal to 0.0 mol % to less than or equal to 5.0 mol %, and all ranges and subranges therebetween. In some other embodiments, the amount of CaO contained in the glass composition may be less than or equal to 5.0 mol%, less than or equal to 2.5 mol%, less than or equal to 2.0 mol%, less than or equal to 1.9 mol%. mol%, less than or equal to 1.7 mol%, less than or equal to 1.5 mol%, or less than or equal to 1.0 mol%. In some further embodiments, the glass composition may contain CaO in an amount greater than or equal to 0.0 mol % and less than or equal to 2.0 mol %, greater than or equal to 0.0 mol % and less than or equal to 1.9 mol % %, greater than or equal to 0.0 mol% and less than or equal to 1.7 mol%, greater than or equal to 0.0 mol% and less than or equal to 1.5 mol%, greater than or equal to 0.02 mol% and less than or equal to 1.02 mol% mol%, greater than or equal to 0.0 mol% and less than or equal to 5.0 mol%, greater than or equal to 0.0 mol% and less than or equal to 1.0 mol%.

In an embodiment, the total amount of CaO and MgO (CaO+MgO) in the glass composition of the present disclosure may be less than or equal to 5.0 mol%, or less than or equal to 2.5 mol%. In an embodiment, CaO+MgO is greater than or equal to 0.0 mol% and less than or equal to 5.0 mol%, or greater than or equal to 0.0 mol% and less than or equal to 2.5 mol%.

The glass compositions of the present disclosure may also include zirconia (ZrO ₂ ). Zirconia may be added to the glass compositions of the present disclosure to improve mechanical properties and/or increase the viscosity of the glass-forming melt. However, it has been empirically found that in some embodiments of the present disclosure, especially when the total content of alkali metal oxides (in mole %) does not exceed or only slightly exceeds the content (in mole %) of alumina , adding zirconia (sometimes even in very small amounts) to the glass composition may increase the liquidus temperature and/or cause precipitation of refractory minerals from the glass-forming melt. Accordingly, in some embodiments of the present disclosure, the amount of zirconia in the glass composition is limited, or the glass composition may be substantially free of ZrO ₂ . In an embodiment, the amount of zirconia (ZrO ₂ ) included in the glass composition may be greater than or equal to 0.0 mol% to less than or equal to 5.0 mol%, and all ranges and subranges therebetween. In some other embodiments, the glass composition may contain ZrO in an amount less _than or equal to 5.0 mol%, less than or equal to 2.5 mol%, less than or equal to 1.5 mol%, less than or equal to 1.35 mol%. Mole%, less than or equal to 1.2 mole%, or less than or equal to 1.0 mole%. In some more embodiments, the glass composition may contain ZrO in an amount greater than or equal to _0.0 mol % and less than or equal to 1.5 mol %, greater than or equal to 0.0 mol % and less than or equal to 1.35 mol % Mole %, greater than or equal to 0.0 mole % and less than or equal to 1.2 mole %, greater than or equal to 0.01 mole % and less than or equal to 1.01 mole %, greater than or equal to 0.0 mole % and less than or equal to To 5.0 mol%, greater than or equal to 0.0 mol%, and less than or equal to 1.0 mol%.

Glass compositions of the present disclosure may include barium oxide (BaO). Barium oxide may be added unintentionally to the glass composition as an impurity in other raw materials, or may be added intentionally to lower the melting temperature or increase the chemical durability. It has been empirically found that the addition of BaO to the glass compositions of the present disclosure can result in an increase in the liquidus temperature, possibly causing crystallization of the glass-forming melt upon cooling and formation. In addition, barium, which is a larger cation, can reduce abnormal fracture behavior. Therefore, in the glass composition of the present disclosure, the content of BaO is limited, but the glass composition preferably does not contain BaO. In an embodiment, the amount of barium oxide (BaO) included in the glass composition may be greater than or equal to 0.0 mol % to less than or equal to 0.2 mol %, and all ranges and subranges therebetween. In some other embodiments, the amount of BaO contained in the glass composition may be less than or equal to 0.2 mol%, or less than or equal to 0.1 mol%. In some more embodiments, the amount of BaO contained in the glass composition may be greater than or equal to 0.0 mol % and less than or equal to 0.2 mol %, greater than or equal to 0.0 mol % and less than or equal to 0.1 mol % Ear%.

Glass compositions of the present disclosure may include potassium oxide (K ₂ O). Potassium oxide may be added to the glass composition unintentionally as an impurity in other raw materials, or intentionally, for example to prevent the glass-forming melt from liquid-liquid phase separation. The addition of K ₂ O can improve the chemical durability of the glass and/or lower the liquidus temperature. Without wishing to be bound by theory, it is believed that K ₂ O may improve the balance between these structural units in the glass composition by converting the structural units established by boron oxide from triangular [BO ₃ ] to tetrahedral [BO ₄ ], and thus Improve abnormal breaking behavior. However, adding K ₂ O to the glass composition of the present disclosure may reduce the Young's modulus of the glass, which in turn may reduce the mechanical properties of the glass product. Furthermore, adding large amounts of _K2O may unacceptably increase the thermal expansion coefficient of the glass. Therefore, in some embodiments of the present disclosure, the content of K ₂ O in the glass composition is limited, or the glass composition may be substantially free of K ₂ O. In an embodiment, the amount of potassium oxide (K ₂ O) contained in the glass composition may be greater than or equal to 0.0 mol % to less than or equal to 10.0 mol %, and all ranges and subranges therebetween. In an embodiment, the amount of K ₂ O contained in the glass composition may be greater than or equal to 0.0 mol % and less than or equal to 3.0 mol %, greater than or equal to 0.3 mol % and less than or equal to 2.8 mol % , greater than or equal to 0.6 mol% and less than or equal to 2.5 mol%, greater than or equal to 0.92 mol% and less than or equal to 2.18 mol%, greater than or equal to 0.0 mol% and less than or equal to 10.0 mol% %, greater than or equal to 0.3 mol% and less than or equal to 2.2 mol%, greater than or equal to 0.6 mol% and less than or equal to 10.0 mol%, greater than or equal to 0.6 mol% and less than or equal to 2.2 mol% mol%, greater than or equal to 0.8 mol% and less than or equal to 2.2 mol%, greater than or equal to 0.9 mol% and less than or equal to 2.2 mol%, greater than or equal to 5.0 mol% and less than or equal to 7.0 Mole %.

The glass compositions of the present disclosure may also include aluminum oxide (Al ₂ O ₃ ). In the glass composition of the present disclosure, alumina acts as a network forming agent together with B ₂ O ₃ and SiO ₂ . As a network former, alumina can increase the viscosity of the glass-forming melt and increase the liquidus viscosity, as well as provide better protection against crystallization. Furthermore, addition of alumina (even in small amounts) prevents the melt from phase separation. Aluminum oxide then improves the chemical durability of the glass. Accordingly, the glass compositions of the present disclosure contain a certain amount of alumina. However, when added in large amounts, alumina may cause precipitation of refractory minerals from the melt, which may cause crystallization defects in the glass product. Furthermore, at higher alumina contents, the viscosity may become too high, which may cause corrosion of the refractory in the glass melting tank. Therefore, in some embodiments of the present disclosure, the amount of alumina is limited. In an embodiment, the amount of aluminum oxide (Al ₂ O ₃ ) included in the glass composition may be greater than or equal to 0.3 mol% to less than or equal to 5.3 mol%, and all ranges and subranges therebetween. In some embodiments, the glass composition may contain Al ₂ O ₃ in an amount greater than or equal to 0.3 mol%, greater than or equal to 2.0 mol%, greater than or equal to 2.2 mol%, greater than or equal to 2.4 mol% , greater than or equal to 2.5 mol%, greater than or equal to 3.45 mol%, greater than or equal to 3.8 mol%, greater than or equal to 4.3 mol%, greater than or equal to 4.8 mol%, or greater than or equal to 5.0 mol%. In some other embodiments, the glass composition may contain Al ₂ O ₃ in an amount less than or equal to 5.3 mol%, less than or equal to 5.0 mol%, less than or equal to 4.8 mol%, less than or equal to Equal to 4.3 mol%, less than or equal to 4.0 mol%, less than or equal to 3.9 mol%, less than or equal to 3.8 mol%, less than or equal to 3.65 mol%, less than or equal to 3.53 mol% , or less than or equal to 2.5 mol%. In some further embodiments, the glass composition may contain Al ₂ O ₃ in an amount greater than or equal to 0.3 mol % and less than or equal to 5.3 mol %, greater than or equal to 2.0 mol % and less than or equal to Equal to 4.0 mol%, greater than or equal to 2.2 mol% and less than or equal to 3.9 mol%, greater than or equal to 2.4 mol% and less than or equal to 3.65 mol%, greater than or equal to 3.45 mol% and less than Or equal to 3.53 mol%, greater than or equal to 0.3 mol% and less than or equal to 2.5 mol%, greater than or equal to 2.0 mol% and less than or equal to 5.3 mol%, greater than or equal to 2.0 mol% and less 2.5 mol% or more, 2.2 mol% or more and 2.5 mol% or less, 2.4 mol% or more and 2.5 mol% or less, 2.5 mol% or more and Less than or equal to 5.3 mol%, greater than or equal to 3.8 mol%, and less than or equal to 3.9 mol%.

The glass compositions of the present disclosure may also include sodium oxide (Na ₂ O). Sodium oxide can act as a modifier, converting the structural units formed by aluminum and boron cations into tetrahedral forms ([AlO ₄ ] and [BO ₄ ]), which may lead to our hypothesized rotatable and non-rotatable structures A better balance between cells may lead to improved anomalous fracture behavior of the glass. Furthermore, the addition of _Na2O can improve the chemical durability of the glass, lower the liquidus temperature, increase the liquidus viscosity, and thus better protect the glass-forming melt from crystallization. However, when added in large amounts, _Na2O may unacceptably reduce the Young's modulus and thus the mechanical properties of the glass article. _In addition, large amounts of Na2O in glass compositions may cause an unacceptable increase in the coefficient of thermal expansion and in some cases reduce the chemical durability of the glass. Therefore, in some embodiments of the present disclosure, the content of sodium oxide in the glass composition is limited, or the glass composition may be substantially free of Na ₂ O. In an embodiment, the amount of sodium _oxide (Na2O) contained in the glass composition may be greater than or equal to 0.0 mol % to less than or equal to 10.0 mol %, and all ranges and subranges between the foregoing values . In some embodiments, the amount of Na2O contained in the glass composition may be greater than or equal to _0.0 mol%, greater than or equal to 2.0 mol%, greater than or equal to 2.5 mol%, greater than or equal to 2.9 mol%, 3.4 mol% or more, 4.55 mol% or more, 5.0 mol% or more, 7.0 mol% or more, 8.0 mol% or more, or 9.0 mol% or more. In some other embodiments, the glass composition may contain Na ₂ O in an amount less than or equal to 10.0 mol%, less than or equal to 9.7 mol%, less than or equal to 9.0 mol%, less than or equal to 8.0 mol%, less than or equal to 7.0 mol%, less than or equal to 6.0 mol%, less than or equal to 5.5 mol%, less than or equal to 5.45 mol%, less than or equal to 5.3 mol%, 5.2 mol% or less, or 5.0 mol% or less. In some further embodiments, the glass composition may contain Na ₂ O in an amount greater than or equal to 0.0 mol % and less than or equal to 5.2 mol %, greater than or equal to 2.0 mol % and less than or equal to 8.0 mol%, greater than or equal to 2.0 mol% and less than or equal to 6.0 mol%, greater than or equal to 2.5 mol% and less than or equal to 5.3 mol%, greater than or equal to 2.9 mol% and less than or Equal to 5.5 mol%, greater than or equal to 3.4 mol% and less than or equal to 6.0 mol%, greater than or equal to 4.55 mol% and less than or equal to 5.45 mol%, greater than or equal to 0.0 mol% and less than or Equal to 10.0 mol%, greater than or equal to 2.0 mol% and less than or equal to 5.0 mol%, greater than or equal to 2.5 mol% and less than or equal to 5.0 mol%, greater than or equal to 3.4 mol% and less Or equal to 5.0 mol%, greater than or equal to 4.55 mol%, and less than or equal to 5.0 mol%.

The glass composition of the present disclosure may include fluorine (F). A small amount of fluorine may be added to the glass composition of the present disclosure as a raw material for a clarifying agent or as a component for lowering the liquidus temperature. However, adding fluorine to glass compositions may cause environmental problems. Therefore, in some embodiments of the present disclosure, the content of fluorine is limited, and preferably, the glass composition may not contain fluorine.

In an embodiment, the combined amount of iron, chromium, molybdenum, vanadium, copper, and cobalt (Fe+Cr+Mo+V+Cu+Co) included in the glass composition of the present disclosure may be less than or equal to 1.0 mole %, or less than or equal to 0.5 mole %. In an embodiment, Fe+Cr+Mo+V+Cu+Co is greater than or equal to 0.0 mol% and less than or equal to 1.0 mol%, or greater than or equal to 0.0 mol% and less than or equal to 0.5 mol% %.

In an embodiment, the combined amount of iron(II) and iron(III) oxide (FeO+Fe ₂ O ₃ ) contained in the glass composition of the present disclosure may be less than or equal to 0.5 mol%, or less than or equal to Equal to 0.25 mol%. In an embodiment, FeO+Fe ₂ O ₃ is greater than or equal to 0.0 mol% and less than or equal to 0.5 mol%, or greater than or equal to 0.0 mol% and less than or equal to 0.25 mol%.

In an embodiment, the combined amount of lanthanum oxide and yttrium (III) oxide (III) La ₂ O ₃ +Y ₂ O ₃ in the glass composition of the present disclosure may be less than or equal to 1.0 mol%, or less than or equal to 0.5 Mole %. In an embodiment, La ₂ O ₃ +Y ₂ O ₃ is greater than or equal to 0.0 mol% and less than or equal to 1.0 mol%, or greater than or equal to 0.0 mol% and less than or equal to 0.5 mol%.

In an embodiment, the combined amount of sodium oxide and potassium oxide (Na ₂ O+K ₂ O) contained in the glass composition of the present disclosure may be greater than or equal to 0.0 mol%, greater than or equal to 5.0 mol%, or greater than Or equal to 6.11 mole%. In an embodiment, Na ₂ O+K ₂ O is less than or equal to 6.84 mol%, or less than or equal to 5.0 mol%. In an embodiment, Na ₂ O+K ₂ O is greater than or equal to 0.0 mol% and less than or equal to 6.84 mol%, or greater than or equal to 0.0 mol% and less than or equal to 5.0 mol%.

In an embodiment, the combined amount of sodium oxide and aluminum oxide (Na ₂ O+Al ₂ O ₃ ) contained in the glass composition of the present disclosure may be greater than or equal to 0.0 mol%, greater than or equal to 5.0 mol%, or Greater than or equal to 7.7 mol%. In an embodiment, Na ₂ O+Al ₂ O ₃ is less than or equal to 9.7 mol%, less than or equal to 8.9 mol%, or less than or equal to 5.0 mol%. In an embodiment, Na ₂ O+Al ₂ O ₃ is greater than or equal to 0.0 mol% and less than or equal to 9.7 mol%, greater than or equal to 0.0 mol% and less than or equal to 8.9 mol%, greater than or equal to Equal to 0.0 mol% and less than or equal to 5.0 mol%, greater than or equal to 5.0 mol% and less than or equal to 9.7 mol%, greater than or equal to 5.0 mol% and less than or equal to 8.9 mol%, greater than Or equal to 7.7 mol% and less than or equal to 9.7 mol%.

In an embodiment, the glass composition disclosed herein has sodium oxide, potassium oxide, magnesium oxide, calcium oxide, zinc oxide, aluminum oxide, boron oxide, and silicon dioxide (Na ₂ O+K ₂ O+MgO+ The combined amount of CaO+ZnO+Al ₂ O ₃ +B ₂ O ₃ +SiO ₂ ) may be greater than or equal to 95.0 mol%.

In an embodiment, the value of the ratio (Na ₂ O+K ₂ O+MgO+CaO+SrO+BaO+ZnO)/(R ₂ O+RO) of the glass composition of the present disclosure may be greater than or equal to 0.000 , or greater than or equal to 0.95. Because it will not reduce the light transmittance of the glass product obtained, and can be well dissolved in the glass melt of the present disclosure, the oxides of sodium and potassium, alkaline earth metal oxides and zinc oxide are modifiers ( R ₂ O and RO) are the most common options. Other monovalent and divalent metal oxides (eg, MnO, NiO, _CuO , Ag2O, PbO, etc.) may have lower solubility, provide undesired color, cause ecological problems, or be more expensive.

In embodiments, glass compositions of the present disclosure may have values for the ratio of Na ₂ O/Al ₂ O ₃ . In the case where Na ₂ O is added to the glass composition, it can be expected to link with structural units formed of different network formers. When this occurs, the mobility of sodium ions may be reduced, which may result in improved chemical durability of the glass. Without wishing to be bound by theory, it is believed that this connection may occur when the Na2O content _of the glass composition is greater _than or equal to the _Al2O3 content. Accordingly, in some embodiments of the present disclosure, it may be desirable to have a ratio of Na ₂ O/Al ₂ O ₃ (in mole percent) greater than or equal to about 1.0. On the other hand, when the Na ₂ O/Al ₂ O ₃ ratio becomes too high, the abnormal fracture behavior described herein may be suppressed. Thus, in embodiments, the Na ₂ O/Al ₂ O ₃ system is greater than or equal to 1.0 mol%, greater than or equal to 1.01 mol%, greater than or equal to 1.1 mol%, or greater than or equal to 1.5 mol%. _In an embodiment, the Na2O/ _Al2O3 system is less _than or equal to 1.67 mol%, less than or equal to 1.6 mol%, less than or equal to 1.5 mol%, or less than or equal to 1.35 mol% . _In an embodiment, Na2O/ _Al2O3 is greater _than or equal to 1.0 mol% and less than or equal to 1.35 mol%, greater than or equal to 1.01 mol% and less than or equal to 1.67 mol%, greater than or equal to Equal to 1.0 mol% and less than or equal to 1.67 mol%, greater than or equal to 1.0 mol% and less than or equal to 1.6 mol%, greater than or equal to 1.0 mol% and less than or equal to 1.5 mol%, greater than or equal to 1.01 mol% and less than or equal to 1.6 mol%, greater than or equal to 1.01 mol% and less than or equal to 1.5 mol%, greater than or equal to 1.01 mol% and less than or equal to 1.35 mol%, Greater than or equal to 1.1 mol% and less than or equal to 1.67 mol%, greater than or equal to 1.1 mol% and less than or equal to 1.6 mol%, greater than or equal to 1.1 mol% and less than or equal to 1.5 mol% , or greater than or equal to 1.1 mol% and less than or equal to 1.35 mol%.

In embodiments, glass compositions of the present disclosure may include the parameter B ₂ O ₃ +3.5*Al ₂ O ₃ within certain numerical ranges. It has been empirically found that the anomalous fracture behavior described herein is best observed when the sum (B ₂ O ₃ +3.5*Al ₂ O ₃ ) is about 25 mol%. Thus, in an embodiment, B ₂ O ₃ +3.5*Al ₂ O ₃ is greater than or equal to 20.3 mol%, greater than or equal to 24.2 mol%, or greater than or equal to 25 mol%. In an embodiment, B ₂ O ₃ +3.5*Al ₂ O ₃ is less than or equal to 27.5 mole%, less than or equal to 25.9 mole%, or less than or equal to 25 mole%. In an embodiment, B ₂ O ₃ +3.5*Al ₂ O ₃ is greater than or equal to 20.3 mol % and less than or equal to 27.5 mol %, greater than or equal to 20.3 mol % and less than or equal to 25.9 mol % , greater than or equal to 20.3 mol% and less than or equal to 25 mol%, greater than or equal to 24.2 mol% and less than or equal to 27.5 mol%, greater than or equal to 24.2 mol% and less than or equal to 25.9 mol% %, greater than or equal to 24.2 mol% and less than or equal to 25 mol%, greater than or equal to 25 mol% and less than or equal to 27.5 mol%, or greater than or equal to 25 mol%% and less than or Equal to 25.9 mole%.

In some embodiments, the glass composition described herein exhibits a decimal logarithmic liquidus viscosity (Log(eta _liq P)) greater than or equal to 5.5 to less than or equal to 8.0, and all ranges between the foregoing values and subrange. In an embodiment, Log(eta _liq P) is greater than or equal to 5.5, greater than or equal to 5.9, greater than or equal to 6.0, greater than or equal to 6.5, greater than or equal to 7.4, greater than or equal to 7.5, greater than or equal to 7.6, or greater than or equal to Equal to 7.8. In an embodiment, Log(eta _liq P) is less than or equal to 8.0, less than or equal to 7.8, less than or equal to 7.7, less than or equal to 7.6, less than or equal to 7.5, less than or equal to 7.4, less than Or equal to 6.5, or less than or equal to 6.0. In an embodiment, Log(eta _liq P) is greater than or equal to 5.5 and less than or equal to 8.0, greater than or equal to 5.9 and less than or equal to 7.7, greater than or equal to 5.5 and less than or equal to 6.0, greater than or equal to 5.9 and Less than or equal to 6.0, greater than or equal to 6.0 and less than or equal to 8.0, greater than or equal to 6.0 and less than or equal to 6.5, greater than or equal to 7.4 and less than or equal to 8.0, greater than or equal to 7.4 and less than or equal to 7.5.

In embodiments, glass compositions according to the present disclosure may exhibit a modifier excess parameter M _exc calculated according to the following relationship: M _exc =max(0, (Alk ₂ O+RO)−(Al ₂ O ₃ +B ₂ O ₃ )), (Equation 2) wherein, Alk ₂ O is the sum of alkali metal oxides, RO is the sum of divalent metal oxides, and the chemical equation means the amount of the corresponding components in the glass composition. M _exc represents the excess of modifiers R ₂ O and RO over network formers Al ₂ O ₃ and B ₂ O ₃ . In case the total content of Al ₂ O ₃ +B ₂ O ₃ exceeds the total content of R ₂ O +RO, the modifier excess parameter is defined to be equal to zero. Without wishing to be bound by theory, it is believed that the value of M _exc is related to the amount of non-bridging oxygen atoms in the structural network of the glass.

In an embodiment, glass compositions according to the present disclosure may exhibit a total polyhedral parameter P _total calculated according to the following relationship: P _total =SiO ₂ +2*Al ₂ O ₃ +2*B ₂ O ₃ , (Equation 3) The chemical equations refer to the amounts of corresponding components in the glass composition. P _total can represent the total number of network-forming cations Si ⁴⁺ , Al ³⁺ , and B ³⁺ per 100 moles of gram atoms of oxides present in the glass composition.

In embodiments, glass compositions according to the present disclosure may exhibit a boron excess parameter B _exc calculated according to the following relationship: B _exc =max(0, B ₂ O ₃ −max(0, R ₂ O+RO—Al ₂ O ₃ )), (Equation 4) wherein, R ₂ O is the sum of monovalent metal oxides, RO is the sum of divalent metal oxides, and the chemical equation means the amount of the corresponding components in the glass composition. B _exc represents the oxidation in mol% exceeding the content (in mol% ₎ of modifiers R2O and RO after subtracting the content (in mol%) of alumina in the glass composition Boron excess. In cases where the alumina content is greater than or equal to the total content of R2O and RO, the boron excess parameter is assumed to be equal to the boron _oxide content of the glass composition.

In an embodiment, a glass composition according to the present disclosure may exhibit a silica excess parameter S _exc calculated according to the following relationship: Si _exc =SiO ₂ −6*min(Alk ₂ O,Al ₂ O ₃ )−2*min (Alk ₂ O+RO-Al ₂ O ₃ , B ₂ O ₃ ), (Equation 5) where, Alk ₂ O is the sum of alkali metal oxides, RO is the sum of divalent metal oxides, the chemical equation It means the amount of the corresponding component in the glass composition. S _exc approximates the content of silicon dioxide assumed not to be linked to the structural polyhedra formed by aluminum and boron cations.

In an embodiment, the parameters P _total , M _exc , B _exc , and S _exc of the glass composition described herein may satisfy the following relationship (abs(2*M _exc +2*min(B ₂ O ₃ , R ₂ O +RO-Al ₂ O ₃ )+0.65*P _total -80))-(3.4-0.5*(abs(Si _exc -max(24+2*B _exc , 44))))≤0.000

In an embodiment, the parameters P _total , M _exc , B _exc , and S _exc of the glass composition described herein may satisfy the following relationship (abs(2*M _exc +2*min(B ₂ O ₃ , R ₂ O +RO-Al ₂ O ₃ )+0.65*P _total -80))-(2.8-0.5*(abs(Si _exc -max(24+2*B _exc , 44))))≤0.000

In some embodiments, glasses comprising compositions described herein can have a quantity 1-2*(Alk ₂ O+RO)/P _total greater than or equal to 0.83.

Glasses comprising compositions described herein may also include a non-rotatable polyhedral parameter P _nr calculated as P _nr =2*max(0, (Alk ₂ O+RO)-(Al ₂ O ₃ +B ₂ O ₃ ))+2*min(B ₂ O ₃ , R ₂ O+RO-Al ₂ O ₃ ), (Equation 6) where, Alk ₂ O is the total amount of alkali metal oxides, and RO is the divalent metal The total amount of oxides, R ₂ O is the total amount of monovalent metal oxides, and the chemical equation means the amount of the corresponding components in the glass composition. Without wishing to be bound by theory, it is believed that _P represents the non-rotatable network-forming cations Si ⁴⁺ , Approximate numbers of Al ³⁺ and B ³⁺ .

Glasses comprising compositions described herein may also include a network rotatability ratio, R _nr , which is quantified by the following equation: R _nr =1-2*(Alk ₂ O+RO)/(SiO ₂ +2 *Al ₂ O ₃ +2*B ₂ O ₃ ), (Equation 7) where Alk ₂ O is the sum of alkali metal oxides, RO is the sum of divalent metal oxides, and the chemical equation means glass composition The amount of the corresponding component in the substance. Applicants believe that R _nr may be related to the fracture behavior of the borosilicate glass compositions disclosed herein and is characteristic of an aspect of "rotatability" of the respective compositions. For the composition in the form of xSiO ₂ ·yAl ₂ O ₃ ·zB ₂ O ₃ ·uR ₂ O ·vRO, where x, y, z, u, v can represent the mole % or mole fraction of each type of oxide . If (u+v)≥y, applicants believe that the fracture behavior is related to the network rotatability ratio _Rnr determined by Equation 7. With R _nr between about 0.80 and about 0.93, Applicants found that the Vickers indenter test produced radial and transverse cracks contained within smaller (diameter < 1 mm) crack loops. The result is that sheets of glass in this range may not crack to failure during the Vickers indenter test, but instead form small circular cracks that contain other cracks and prevent their propagation.

In an embodiment, glass compositions according to the present disclosure may include a network balance criterion C _nb , which is calculated as C _nb =abs(SiO ₂ -6*min(Alk ₂ O, Al ₂ O ₃ )-2*min(Alk ₂ O+RO-Al ₂ O ₃ , B ₂ O ₃ )-max(24+2*max(0, B ₂ O ₃ -max(0, R ₂ O+RO-Al ₂ O ₃ )), 44) ), Equation (8) Among them, Alk ₂ O is the total amount of alkali metal oxides, RO is the total amount of divalent metal oxides, R ₂ O is the total amount of monovalent metal oxides, the chemical equation It means the amount of the corresponding component in the glass composition. C _nb represents the relationship between the parameters Si _exc and B _exc described herein. When the values of the Si _exc parameter are plotted as a function of the B _exc parameter of the exemplary compositions described herein, the instances are grouped around the line segments y=24-x and y=44-3*x, where y corresponds to to the parameter Si _exc , and x corresponds to the parameter B _exc . The examples described herein lie near the highest values calculated by these equations, which can be expressed as follows: Si _exc =max(24-B _exc , 44-4*B _exc ), (equation 9)

Without wishing to be bound by theory, it is believed that the difference between Si _exc and the expression max(24-B _exc , 44-4*B _exc ) specified by the right-hand part of Equation 9 can be characterized by the silicon and The balance between boron connectivity. After substituting the absolute value of the above difference into the expressions of Si _exc and B _exc , the expression of C _nb is finally given. In other words, the network balance criterion can be expressed using Si _exc and B _exc as follows: C _nb =abs(Si _exc -max(24-B _exc , 44-4*B _exc )), (equation 10)

Exemplary compositions described herein that exhibit abnormal and intermediate fracture behavior are characterized by relatively small _Cnb values (e.g., 5.0 or less, or 4.5 or less, or 4.0 or less, or 3.5 or less, or 3.0 or less, or 2.5 or less, or even 2.0 or less).

The term "fracture category" refers to the type of fracture behavior observed when performing the Vickers indenter test, and is described into three categories: "normal", "abnormal", and "intermediate". The Vickers indenter test can be used to characterize the fracture behavior of glass, as in "Crack-resistant glass with high shear band density, Journal of Non-Crystalline Solids, 494 (2018) 13-20" by Gross et al.; and Gross et al. Discussed in "Deformation and cracking behavior of glasses indented with diamond tips of various sharpness, Journal of Non-Crystalline Solids, 358 (2012) 3445-3452", both of which are incorporated herein by reference. In some embodiments, when the glass with the borosilicate glass composition of the first glass interlayer is formed to have a thickness of 1 mm and a major surface area (eg, 2 cm by ² cm squared) of at least 10 Polished flat samples (for example, 100 samples) were tested using a square-based 136° tetrahedron Vickers indenter pointing orthogonally to the center of the major surface at 25°C and 50% relative humidity (in Quasi-static displacement at a rate of 60 μm per second up to 3 kg force, the indentation load is maintained for 10 seconds (unless the breakage caused by the fracture of the sample occurs first)), under normal conditions (at least 51 times out of 100; at least 10 times) 6 times), all cracks extending radially and/or laterally through the sample from below the indenter tip (i.e., where the indenter tip contacts the glass) are interrupted by self-terminating crack loops (eg, annular cracks), Fracture of the samples from the Vickers indenter was therefore limited to cracks within the loop. In this case, the fracture class is identified as "Intermediate". Essentially, the indenter crushes the glass beneath the indenter and breaks it. However, crack loops form and prevent cracks originating from indenter contact from propagating beyond the crack loop. In contrast, transverse or radial cracks may form before and/or pass through these crack circuits in other glasses (e.g., abnormal cracks), or may not form crack circuits (e.g., normal cracks), And in either case, transverse or radial cracks will not be contained by the crack loop and may propagate through the entire glass article, causing an integral fracture through the article and breaking it. This type of fracture behavior was identified as "normal".

In an embodiment, glass compositions according to the present disclosure may include a rotatability balance criterion C _rb in an amount calculated as C _rb =abs(2*max(0, (Alk ₂ O+RO)-(Al ₂ O ₃ +B ₂ O ₃ ))+2*min(B ₂ O ₃ , R ₂ O+RO-Al ₂ O ₃ )+0.65*(SiO ₂ +2*Al ₂ O ₃ +2*B ₂ O ₃ ) -80), (equation 11) wherein, Alk ₂ O is the total amount of alkali metal oxides, RO is the total amount of divalent metal oxides, R ₂ O is the total amount of monovalent metal oxides, The chemical equations mean the amounts of the corresponding components in the glass composition. C _rb represents the relationship between the numbers P _total and P _nr described herein. When the value of the P _nr parameter is plotted as a function of the value of the P _total parameter of the examples described herein, the P _nr value of the disclosed examples falls around the line segment y=80-0.65*x, where y corresponds to The parameter P _nr , while x corresponds to the parameter P _total , and can be expressed mathematically as follows: P _nr =80-0.65*P _total , (equation 12) where P _total and P _nr refer to the total polyhedral parameters described herein with non-rotatable polyhedron parameters. Without wishing to be bound by theory, it is believed that the difference between P _nr and the expression 80−0.65*P _total specified by the right-hand portion of Equation 12 may be characterized by a balance between rotatable and non-rotatable structural polyhedra. After substituting the absolute value of the above difference into the expressions of P _nr and P _total , the expression of C _rb is finally given. In other words, the network balance criterion can be expressed using Si _exc and B _exc as follows: C _rb =abs(P _nr -(80-0.65*P _total ), (Equation 13)

Density at room temperature (referred to herein using the term "d _RT ") is a property of glass that can be predicted from glass composition. Examples of the present disclosure were performed as well as linear regression analyzes of certain existing compositions to generate equations that could be used to predict the composition dependence of the density of various glass compositions.

To select from available glass compositions, search the SciGlass information system using the criteria listed in Table 600 below.

Form 600 nature d _RT , g/cm ³ ingredient restrictions Min, mole % Max, mole % SiO ₂ 60 80 Na ₂ O 1 10 Al ₂ O ₃ 0.3 10 K ₂ O 0 5 Li ₂ O 0 5 BaO 0 5 Na2O _{+ K2O} 5 unlimited B ₂ O ₃ +3.5*Al ₂ O ₃ 15 30 other substances 0 unlimited

Approximately 100 glass compositions were randomly selected from the search results as well as exemplary glasses from the examples presented herein. Linear regression analysis of the above datasets was used to determine the equations to exclude irrelevant variables and outliers. The resulting equations are presented in Table 700 below.

Form 700 nature abbreviation unit predictive parameters regression equation Composition unit standard deviation Density at room temperature _d g/ ^cm3 P _d Equation 14 Mole% 0.024

Another set of compositional species satisfying the criteria in table 600 served as a validation set to assess the ability of Equation 14 herein to interpolate within the predefined compositional limits, which correspond to the standard deviations specified in table 700 . An external dataset of prior art glass compositions was also randomly selected from the SciGlass Information System database for use in assessing the ability to predict properties beyond the limits of the specified composition with reasonable accuracy. Multiple iterations of this process are performed to determine the best variants for each property corresponding to the regression equations specified in table 700 above.

Data on the composition of the training dataset, the validation dataset, and the external dataset used in the linear regression modeling were obtained from the publicly available SciGlass Information System database. Equation 14 below was taken from linear regression analysis to predict the density of the glass: Pd = 2.487 - _0.0068998 * B2O3 _{+ 0.041371} * BaO + 0.13897 * _Bi2O3 + _0.011637 * CaO + 0.055366 * Cs ₂ O + 0.025420 * Fe ₂ O ₃ + 0.10294 * Gd ₂ O ₃ + 0.0051134 * K ₂ O + 0.079903 * La ₂ O ₃ + 0.0041594 * Li ₂ O + 0.0084582 * MgO + 0.019720 * MnO + 0.0064419 * Na ₂ O 0.018282 * NiO + 0.065781 * PbO - 0.002953 * SiO ₂ + 0.027682 * SrO + 0.0055367 * TiO ₂ + 0.0068497 * V ₂ O ₅ + 0.048699 * Y ₂ O ₃ + 0.021527 * ZnO + 0.026527 * ZrO ₂ + 0.011033 * (min( B ₂ O ₃ , max(0, Alk ₂ O + RO - Al ₂ O ₃ ))), (Equation 14)

In Equation 14, the density parameter P _d is a parameter for predicting the density [g/cm ³ ] at room temperature calculated using the components of the glass composition expressed in mol%. In Equation 14, each component of the glass composition is listed with its chemical formula, where the chemical formula refers to the concentration of that component expressed in mol%. For example, for Equation 14, B ₂ O ₃ refers to the concentration of B ₂ O ₃ in the glass composition expressed in mol %. It should be understood that not all of the ingredients listed in Equation 14 must be present in a particular glass composition, and that Equation 14 is equally applicable to glass compositions that contain less than all of the ingredients listed in the equation. It should also be understood that Equation 14 is also applicable to glass compositions within the scope of the present disclosure and claims that include ingredients other than those listed in the equation. If an ingredient listed in Equation 14 is not present in a particular glass composition, the concentration of the ingredient in the glass composition is 0 mole %, and the ingredient's contribution to the value calculated by the equation is zero. Equation 14 was used to generate predicted values for the density of the glasses described in the examples described herein as well as those found in the prior art. The predicted values are plotted as a function of the measured beam density d _RT at room temperature. Equation 14 was found to accurately predict the actual measured density within +/- 0.024 g/cm ³ .

Applicants have found that for certain glass compositions according to the examples contained herein, the density parameter _Pd , which represents the predicted value of the density according to the composition constituents of each composition, satisfies as _Na2O / _Al2 The relationship as a function of the ratio of O ₃ . The first set of examples described herein were selected to meet the following criteria listed in Table 800 below. In Table 800, "unrestricted" means that no restriction was considered when selecting the composition.

Form 800 quantity unit the smallest maximum SiO ₂ Mole % 60 77.5 B ₂ O ₃ Mole% 5 17 Na ₂ O Mole % 2.5 5.3 Al ₂ O ₃ Mole% 0.3 5.3 K ₂ O Mole % 0 3 Li ₂ O Mole% 0 0.2 BaO Mole% 0 0.2 Na2O _{+ K2O} Mole % 5 unlimited B ₂ O ₃ +3.5*Al ₂ O ₃ Mole % 20.3 27.5

For the first set of examples, the density parameter P _d values are plotted as a function of the value of Na ₂ O/Al ₂ O ₃ for each composition. The first set of examples was found to satisfy the following relationship: P _d -(2.58-0.2*Na ₂ O/Al ₂ O ₃ )<0.0, (Equation 15)

A subset of the first set of instances was found to satisfy the following relationship: P _d -(2.54-0.2*Na ₂ O/Al ₂ O ₃ )<0.0, (Equation 16)

Certain existing glass compositions do not satisfy the relationship defined by Equation 15 (and thus do not satisfy the relationship defined by Equation 16). That is, glass compositions according to the examples described herein _exhibit fewer density parameter values (and _{fewer measured dRT} value). As described herein, such lower densities may facilitate glasses according to the present disclosure to exhibit the unique fracture behavior described herein.

The second set of examples described herein were selected to meet the following criteria listed in Table 900 below.

Form 900 Composition Amount (mole%) SiO ₂ 60.0 to 96.0 mole % B ₂ O ₃ 1.0 to 25.0 mol% Al ₂ O ₃ ≥0.3 mole% The sum of (Na ₂ O+Al ₂ O ₃ ) ≥9.7 mol%

In an embodiment, the second group of examples may also satisfy each of the following conditions: 1.01≤Na ₂ O/Al ₂ O ₃ [mol%]≤1.67, B ₂ O ₃ +3.5*Al ₂ O ₃ [ Mole %]≤27.5, C _rb -(3.4-0.5*C _nb )＜0.000, where C _rb is the rotatability balance standard defined herein, C _nb is the network balance standard defined herein, or C _rb -(2.8-0.5*C _nb )<0.000, and 1-2*(Alk ₂ O+RO)/P _total >0.83, where P _total is the total polyhedral parameter. It has been found that some existing compositions do not satisfy the above conditions.

The third set of examples described herein were selected to meet the following criteria listed in Table 1000 below.

Form 1000 Composition Amount (mole%) SiO ₂ 60.0 to 77.5 mole % B ₂ O ₃ 5.0 to 17.0 mol% Na ₂ O 2.5 to 5.3 mol% Al ₂ O ₃ 0.3 to 5.3 mol%

A third set of examples was found to satisfy each of the following conditions: 20.3 B ₂ O ₃ +3.5*Al ₂ O ₃ [mol %]≦27.5, d _RT -(2.58-0.2*(Na ₂ O/Al ₂ O ₃ ))<0.00, d _RT is the density at room temperature, or in some cases, d _RT −(2.54-0.2*(Na ₂ O/Al ₂ O ₃ ))<0.000. It has been found that some existing compositions do not satisfy the above conditions.

The fourth set of examples described herein were selected to meet the following criteria listed in Table 1100 below.

Form 1100 quantity unit the smallest maximum SiO ₂ Mole % 60 80 Al ₂ O ₃ Mole% 0.3 unlimited Li ₂ O Mole% 0 0.3 _{Na2O + Al2O3} Mole % unlimited 9.7 BaO Mole % 0 0.1 f at% 0 0.05 RE _m O _n Mole % 0 0.1 _{Na2O / Al2O3} Mole % 1.01 1.67 B ₂ O ₃ +3.5*Al ₂ O ₃ Mole% unlimited 27.5 1- 2*(Alk ₂ O+RO)/P _total 0.83 unlimited

For each of the instances in the fourth group, the C _rb parameter was calculated and plotted as a function of the C _nb parameter. The C _rb and C _nb parameters for each of the examples in the fourth group were determined to satisfy the relationship C _rb −(3.4-0.5*C _nb )<0.00, (Equation 17) Glasses according to the present disclosure were found to be compatible with certain existing The composition differs by satisfying Equation 17.

For a subset of examples in the fourth group, it was found that the values of the C _rb and C _nb parameters also satisfy the relationship C _rb -(2.8-0.5*C _nb )<0.00, (Equation 16) This glass was found to be compatible with some existing The compositions are further distinguished by satisfying Equation 16.

Embodiments of the present disclosure can be further understood from the following aspects.

A first aspect of the present disclosure includes a borosilicate glass composition comprising: at least 74 mole % SiO ₂ ; at least 10 mole % B ₂ O ₃ ; having SiO ₂ , B ₂ O ₃ , and Al ₂ The sum of O ₃ is Al ₂ O ₃ in an amount of at least 90 mole percent; wherein the borosilicate glass composition comprises a liquidus viscosity greater than 500 kP; and wherein the borosilicate glass composition comprises The temperature at which the viscosity of the salt glass composition is 200P is 1725° C. or less.

A second aspect of the present disclosure includes the borosilicate glass according to the first aspect, further comprising about 2 mol% to about 8 mol% _Na20 .

A third aspect of the present disclosure includes the borosilicate glass according to any one of the first aspect to the second aspect, further comprising about 0.8 mol% to about ₄ mol% K2O.

A fourth aspect of the present disclosure includes the borosilicate glass according to any one of the first aspect to the third aspect, wherein the total amount of Na2O and _K2O is at least ₄ mole%.

A fifth aspect of the present disclosure includes the borosilicate glass according to any one of the first aspect to the fourth aspect, wherein the total amount of MgO and CaO is at most 5 mol%.

A sixth aspect of the present disclosure includes the borosilicate glass according to any one of the first aspect to the fifth aspect, further comprising P ₂ O ₅ , wherein the P ₂ O ₅ is present in an amount of up to 4 molar Ear%.

A seventh aspect of the present disclosure includes the borosilicate glass according to any one of the first aspect to the sixth aspect, further comprising about 0.05 mol % to about 0.25 mol % SnO ₂ .

An eighth aspect of the present disclosure includes the borosilicate glass according to any one of the first aspect to the seventh aspect, further comprising 0.05 mol % to 0.50 mol % of an iron compound.

A ninth aspect of the present disclosure includes the borosilicate glass according to any one of the first to eighth aspects, wherein the total solar transmittance measured according to ISO 13837A is 90% or less.

A tenth aspect of the present disclosure includes the borosilicate glass according to any one of the first aspect to the ninth aspect, wherein the visible light transmittance measured according to ISO 13837A is at least 73%.

An eleventh aspect of the present disclosure includes the borosilicate glass according to any one of the first aspect to the tenth aspect, comprising 5.6 ppm/°C or more measured over a temperature range of 0°C to 300°C Low coefficient of thermal expansion.

A twelfth aspect of the present disclosure includes the borosilicate glass according to any one of the first aspect to the eleventh aspect, comprising a density of less than 2.4 g/cm ³ .

A thirteenth aspect of the present disclosure includes the borosilicate glass according to any one of the first aspect to the twelfth aspect, comprising a strain point of about 480°C to about 560°C.

A fourteenth aspect of the present disclosure includes the borosilicate glass according to any one of the first aspect to the thirteenth aspect, including an annealing point of about 520°C to about 590°C.

A fifteenth aspect of the present disclosure includes the borosilicate glass according to any one of the first aspect to the fourteenth aspect, wherein the glass interlayer comprises the borosilicate glass according to any one of the preceding claims glass composition.

A sixteenth aspect of the present disclosure includes the borosilicate glass according to any one of the first aspect to the fifteenth aspect, wherein when the glass interlayer is subjected to a quasi-static 2 kgf indentation load with a Vickers tip, The glass interlayer presents an annular crack and a plurality of radial cracks, and each radial crack in the plurality of radial cracks is bounded by the annular crack.

A seventeenth aspect of the present disclosure includes the borosilicate glass according to any one of the first aspect to the sixteenth aspect, wherein the glass interlayer is formed by fusion stretching, and wherein the first major surface and the second The thickness between the two main surfaces is greater than 2 mm.

An eighteenth aspect of the present disclosure includes the borosilicate glass according to any one of the first aspect to the seventeenth aspect, wherein the thickness is at least 3 mm.

A nineteenth aspect of the present disclosure includes a laminate comprising: a first glass interlayer according to any one of the first to eighteenth aspects, a second glass interlayer, and bonding the first glass interlayer to the interlayer of the second glass interlayer.

A twentieth aspect of the present disclosure includes the laminate according to the nineteenth aspect, wherein the first glass interlayer is thicker than the second glass interlayer.

A twenty-first aspect of the present disclosure includes the laminate according to any one of the nineteenth to twentieth aspects, wherein the second glass interlayer is strengthened.

A twenty-second aspect of the present disclosure includes the laminate according to any one of the nineteenth aspect to the twenty-first aspect, wherein the first glass interlayer and the second glass interlayer are in a pair shape, wherein The first interlayer of glass includes a first depth of curvature of at least 2 mm, wherein the second interlayer of glass includes a second depth of curvature of at least 2 mm, and wherein the first depth of curvature is within 10% of the second depth of curvature.

A twenty-third aspect of the disclosure includes the laminate according to any one of the nineteenth to twenty-second aspects, wherein the first glass interlayer is sagging and includes a depth of curvature of at least 2 mm , and wherein the second laminated glass is cold formed to be consistent with the first laminated glass.

A twenty-fourth aspect of the present disclosure includes an automotive glazing including the laminate according to any one of the nineteenth to twenty-fourth aspects.

A twenty-fifth aspect of the present disclosure includes a vehicle comprising: a body defining an interior of the vehicle and at least one opening; the automotive glazing according to claim 24 disposed in the at least one opening; wherein the second glass interlayer is arranged to faces the interior of the vehicle, while the first glass interlayer faces the exterior of the vehicle.

A twenty-sixth aspect of the present disclosure includes the vehicle according to the twenty-fifth aspect, wherein the automotive glass is at least one of a sidelight, a windshield, a rear window, a window, or a sunroof.

A twenty-seventh aspect of the present disclosure includes a method of forming a glass interlayer comprising a first major surface and a second major surface, the method comprising the steps of: making At least two channels in the isopipe overflowing from at least two channels of a borosilicate glass composition having a viscosity of 1725°C at 200P or less, wherein the borosilicate glass composition contains at least 74 Mole % SiO ₂ and at least 10 mol % B ₂ O ₃ , wherein the combined amount of SiO ₂ , B ₂ O ₃ , and Al ₂ O ₃ is at least 90 mol %; at the root of the isopipe At least two streams of borosilicate glass composition are fused to form a glass interlayer having a thickness of at least 2 mm between the first major surface and the second major surface.

A twenty-eighth aspect of the present disclosure includes the method according to the twenty-seventh aspect, wherein the glass interlayer comprises a coefficient of thermal expansion of 5.6 ppm/°C or less measured over a temperature range of 0°C to 300°C.

A twenty-ninth aspect of the disclosure includes the method according to any one of the twenty-seventh to twenty-eighth aspects, wherein the glass interlayer comprises a density of less than 2.4 g/cm ³ .

A thirtieth aspect of the present disclosure includes the method according to any one of the twenty-seventh to twenty-ninth aspects, wherein the borosilicate glass composition further comprises from about 2 mole % to about 8 mole % Na ₂ O.

A thirty-first aspect of the present disclosure includes the method of any one of the twenty-seventh through thirtieth aspects, wherein the borosilicate glass composition further comprises from about 0.8 mole % to about 4 mole % K ₂ O.

A thirty-second aspect of the disclosure includes the method according to any one of the twenty _- seventh to thirtieth aspects, wherein the total amount of Na2O and K2O is at least ₄ mole%.

A thirty-third aspect of the present disclosure includes the method according to any one of the twenty-seventh to twenty-second aspects, wherein the borosilicate glass composition further comprises at least one of MgO or CaO, wherein The total amount of MgO and CaO is up to 5 mol%.

A thirty-fourth aspect of the present disclosure includes the method of any one of the twenty-seventh to thirty-third aspects, wherein the borosilicate glass composition further comprises from about 0.05 mole % to about 0.25 mole % % SnO ₂ .

A thirty-fifth aspect of the present disclosure includes the method according to any one of the twenty-seventh to thirty-fourth aspects, wherein the borosilicate glass composition further comprises 0.05 mol % to 0.50 mol % of Iron compounds.

A thirty-sixth aspect of the present disclosure includes the method according to any one of the twenty-seventh to thirty-fifth aspects, further comprising P ₂ O ₅ , wherein P ₂ O ₅ is present in an amount of up to 4 mo Ear%.

A thirty-seventh aspect of the present disclosure includes a glass interlayer comprising: a first major surface and a second major surface opposite to the first major surface, wherein the glass interlayer comprises a borosilicate glass composition; and wherein when the glass interlayer is subjected to Under the quasi-static 2kgf indentation load with a Vickers tip, the glass interlayer exhibits circular cracks and multiple radial cracks, and each of the multiple radial cracks is bounded by a circular crack.

A thirty-eighth aspect of the present disclosure includes the glass interlayer according to the thirty-seventh aspect, wherein the borosilicate glass composition comprises: at least 74 mol % SiO ₂ ; at least 10 mol % B ₂ O ₃ and Al ₂ O ₃ in an amount of at least 90 mole percent of the sum of SiO ₂ , B ₂ O ₃ , and Al ₂ O ₃ .

A thirty-ninth aspect of the present disclosure includes the glass interlayer according to the thirty-eighth aspect, wherein the borosilicate glass composition includes a liquidus viscosity greater than 500 kP.

A fortieth aspect of the present disclosure includes the glass interlayer according to any one of the thirty-eighth to thirty-ninth aspects, wherein the borosilicate glass composition contains The temperature at a viscosity of 200P is 1725°C or less.

A forty-first aspect of the present disclosure includes the glass interlayer according to any one of the thirty-eighth to fortieth aspects, wherein the borosilicate glass composition comprises from about 2 mol % to about 8 mol % Na ₂ O.

A forty-second aspect of the present disclosure includes the glass interlayer according to any one of the thirty-eighth to fortieth aspects, wherein the borosilicate glass composition comprises about 0.8 mole % to about 4 mole % K ₂ O.

A forty-third aspect of the disclosure includes the glass interlayer according to any one of the thirty-eighth to forty-second aspects, wherein the borosilicate composition comprises at least ₄ mole % Na2O and K _The total amount of 2O.

A forty-fourth aspect of the present disclosure includes the glass interlayer according to any one of the thirty-eighth to forty-third aspects, wherein the borosilicate glass composition comprises at least one of MgO or CaO, wherein The total amount of MgO and CaO is up to 5 mol%.

A forty-fifth aspect of the present disclosure includes the glass interlayer according to any one of the thirty-eighth to forty-fourth aspects, wherein the borosilicate glass composition comprises P2 in an amount of at most ₄ mol % O ₅ .

A forty-sixth aspect of the present disclosure includes the glass interlayer according to any one of the thirty-eighth to forty-fifth aspects, wherein the borosilicate glass composition comprises from about 0.05 mole % to about 0.25 mole % % SnO ₂ .

A forty-seventh aspect of the present disclosure includes the glass interlayer according to any one of the thirty-eighth to forty-sixth aspects, wherein the borosilicate glass composition contains 0.05 mol % to 0.50 mol % of Iron compounds.

A forty-eighth aspect of the present disclosure includes the glass interlayer according to any one of the thirty-eighth to forty-seventh aspects, wherein the total solar transmittance through the glass interlayer measured according to ISO 13837A is 90% or less.

A forty-ninth aspect of the present disclosure includes the glass interlayer according to any one of the thirty-eighth to forty-eighth aspects, wherein the visible light transmission through the glass interlayer measured according to ISO 13837A is at least 73%.

A fiftieth aspect of the present disclosure includes the glass interlayer according to any one of the thirty-eighth to forty-ninth aspects, wherein the first major surface exhibits an optical distortion detector according to ASTM 1561 using transmission optics. Optical distortion of up to 200 millidiopters.

A fifty-first aspect of the present disclosure includes a glass laminate comprising: a first glass interlayer comprising a first major surface and a second major surface opposite the first major surface, wherein the first glass interlayer comprises borosilicate A salt glass composition; a second glass interlayer comprising a third major surface and a fourth major surface opposite to the third major surface; and an interlayer bonding the second major surface of the first glass interlayer to the third major surface of the second glass interlayer The major surface; wherein the borosilicate glass composition comprises: at least 74 mole percent SiO ₂ ; at least 10 mole percent B ₂ O ₃ ; and having the sum of SiO ₂ , B ₂ O ₃ , and Al ₂ O ₃ Al ₂ O ₃ in an amount of at least 90 mol%.

A fifty-second aspect of the present disclosure includes the glass laminate according to the fifty-second aspect, wherein the first glass interlayer is thicker than the second glass interlayer.

A fifty-third aspect of the present disclosure includes the glass laminate according to any one of the fifty-first to fifty-second aspects, wherein the second glass interlayer is strengthened.

A fifty-fourth aspect of the present disclosure includes the glass laminate according to any one of the fifty-first to fifty-third aspects, wherein the second glass interlayer is chemically strengthened by an ion exchange process.

A fifty-fifth aspect of the disclosure includes the glass laminate according to any of the fifty-first to fifty-fourth aspects, wherein the glass laminate is configured for a body having a defined interior and opening In a vehicle of , wherein the glass laminate is configured to be positioned in the opening, and wherein the first glass interlayer is arranged to face the exterior of the vehicle and the second glass interlayer is arranged to face the interior of the vehicle.

A fifty-sixth aspect of the present disclosure includes the glass laminate according to any one of the fifty-first to fifty-fifth aspects, wherein the first glass interlayer has a glass interlayer between the first major surface and the second major surface. a first thickness of at least 2 mm, and wherein the second glass interlayer has a second thickness of less than 2 mm between the third major surface and the fourth major surface.

A fifty-seventh aspect of the present disclosure includes the glass laminate according to any one of the fifty-first to fifty-sixth aspects, wherein the glass laminate comprises a thickness equal to the sum of the first thickness and the second thickness. a total glass thickness, and wherein the ratio of the first glass thickness to the total glass thickness is at least 0.7.

A fifty-eighth aspect of the present disclosure includes the glass laminate according to any one of the fifty-first to fifty-seventh aspects, wherein the first glass thickness is at least 3 mm and the second glass thickness is 1.1mm or less.

A fifty-ninth aspect of the present disclosure includes the glass laminate according to any one of the fifty-first to fifty-eighth aspects, wherein the first glass thickness is at least 3.3 mm and the second glass thickness is 0.7mm or less.

A sixtieth aspect of the present disclosure includes the glass laminate according to any one of the fifty-first to fifty-ninth aspects, wherein the second glass interlayer includes the second glass composition.

A sixty-first aspect of the disclosure includes the glass laminate according to any one of the fifty-first to sixtieth aspects, wherein the second glass composition is different from the borosilicate glass composition.

A sixty-second aspect of the present disclosure includes the glass laminate according to any one of the fifty-first to sixty-first aspects, wherein the second glass composition is selected from the group consisting of soda lime silicate glass compositions, Aluminosilicate glass composition, alkali metal aluminosilicate glass composition, alkali borosilicate glass composition, alkali metal aluminophosphosilicate glass composition, alkali metal aluminoborosilicate glass composition, and their combinations.

A sixty-third aspect of the disclosure includes the glass laminate according to any one of the fifty-first to sixty-second aspects, wherein the visible light transmission through the glass laminate measured according to ISO 13837A is at least 73%.

A sixty-fourth aspect of the disclosure includes the glass laminate according to any one of the fifty-first to sixty-second aspects, wherein the total solar transmittance through the glass laminate measured according to ISO 13837A is 90% or less.

A sixty-fifth aspect of the disclosure includes the glass laminate according to any of the fifty-first to sixty-fourth aspects, wherein the first major surface, the fourth major surface, or the first major surface and Both fourth major surfaces exhibit an optical distortion of at most 200 millidiopters measured according to ASTM 1561 using an optical distortion detector of transmission optics.

A sixty-sixth aspect of the present disclosure includes the glass laminate according to any one of the fifty-first to sixty-fifth aspects, wherein the interlayer is selected from the group consisting of polyvinyl butyral (PVB), soundproofing Groups consisting of PVB (APVB), ionomers, vinyl acetate (EVA), thermoplastic polyurethane (TPU), polyester (PE), polyethylene terephthalate (PET), and combinations thereof .

A sixty-seventh aspect of the present disclosure includes the glass laminate according to any one of the fifty-first to sixty-second aspects, wherein the intermediate layer comprises a thickness in the range of about 0.5 mm to about 2.5 mm.

A sixty-eighth aspect of the present disclosure includes the glass laminate according to any one of the fifty-first to sixty-seventh aspects, wherein the intermediate layer comprises at least one functional layer or film.

A sixty-ninth aspect of the present disclosure includes the glass laminate according to any one of the fifty-first to sixty-eighth aspects, wherein the functional layer or film provides a function selected from ultraviolet absorbing, infrared absorbing, infrared reflecting, Functions of sound damping, coloring, antenna, adhesion promotion, anti-glare processing, anti-reflection processing, and combinations thereof.

A seventieth aspect of the present disclosure includes the glass laminate according to any one of the fifty-first to sixty-ninth aspects, wherein the first glass interlayer and the second glass interlayer are in a pair shape, wherein the first A glass interlayer includes a first depth of curvature of at least 2 mm, wherein a second glass interlayer includes a second depth of curvature of at least 2 mm, and wherein the first depth of curvature is within 10% of the second depth of curvature.

A seventy-first aspect of the present disclosure includes the glass laminate according to any of the fifty-first to seventieth aspects, wherein the first glass interlayer is sag and includes a depth of curvature of at least 2 mm, and Wherein the second laminated glass is cold formed to be consistent with the first laminated glass.

A seventy-second aspect of the present disclosure includes a system comprising: a sensor; a glass laminate comprising: a first glass interlayer comprising a first major surface and a second major surface opposite the first major surface, wherein The first glass interlayer includes a borosilicate glass composition; the second glass interlayer includes a third major surface and a fourth major surface opposite the third major surface; and an interlayer bonding the second major surface of the first glass interlayer to the third major surface of the second glass interlayer; wherein the borosilicate glass composition comprises: at least 74 mole percent SiO ₂ ; at least 10 mole percent B ₂ O ₃ ; and having SiO ₂ , B ₂ O ₃ , and Al ₂ O ₃ in an amount of at least 90 mole percent Al ₂ O ₃ ; wherein the sensor is configured to receive, transmit, or both receive and transmit a signal through the glass laminate; wherein the signal comprises 400nm to a peak wavelength in the range of 750nm or in the range of 1500nm or greater.

A seventy-third aspect of the disclosure includes the system according to the seventy-second aspect, wherein the sensor is a LIDAR.

A seventy-fourth aspect of the disclosure includes the system according to any one of the seventy-second to seventy-third aspects, wherein the glass laminate is a glazing for a vehicle.

A seventy-fifth aspect of the disclosure includes the system according to any of the seventy-second to seventy-fourth aspects, wherein the visible light transmission through the glass laminate measured according to ISO 13837A is at least 73% .

A seventy-sixth aspect of the present disclosure includes the system according to any one of the seventy-second to seventy-fifth aspects, wherein the total solar transmission through the glass laminate measured according to ISO 13837A is 90% or less.

A seventy-seventh aspect of the disclosure includes the system according to any of the seventy-second to seventy-sixth aspects, wherein the first major surface, the fourth major surface, or the first and fourth major surfaces Both surfaces exhibited an optical distortion of up to 200 millidiopters measured according to ASTM 1561 using an optical distortion detector of transmission optics.

A seventy-eighth aspect of the disclosure includes the system according to any one of the seventy-second to seventy-seventh aspects, wherein the first glass interlayer is thicker than the second glass interlayer.

A seventy-ninth aspect of the disclosure includes the system according to any one of the seventy-second to seventy-eighth aspects, wherein the second glass interlayer is strengthened.

An eightieth aspect of the disclosure includes the system according to any one of the seventy-second to seventy-ninth aspects, wherein the second glass interlayer is chemically strengthened by an ion exchange process.

An eighty-first aspect of the present disclosure includes a glass laminate comprising: a first glass interlayer comprising a first major surface and a second major surface opposite the first major surface, wherein the first glass interlayer comprises a fusion formed borosilicate glass composition; the second glass interlayer includes a third major surface and a fourth major surface opposite to the third major surface; and an interlayer bonding the second major surface of the first glass interlayer to the second glass The third major surface of the interlayer; wherein the transmittance of ultraviolet light having a wavelength in the range of 300-380 nm through the glass laminate is 75% or less; wherein the transmittance of light in the visible spectrum through the glass laminate is The transmission is 73% or more; and wherein the total solar transmission through the glass laminate is 61% or less.

An eighty-second aspect of the present disclosure includes the glass laminate according to the eighty-first aspect, wherein the borosilicate glass composition comprises at least 74 mol % SiO ₂ , at least 10 mol % B ₂ O _3. Al ₂ O ₃ having an amount of the sum of SiO ₂ , B ₂ O ₃ , and Al ₂ O ₃ being at least 90 mol%.

An eighty-third aspect of the disclosure includes the glass laminate according to any one of the eighty-first to eighty-second aspects, wherein the first glass interlayer is thicker than the second glass interlayer.

An eighty-fourth aspect of the present disclosure includes the glass laminate according to any one of the eighty-first to eighty-third aspects, wherein the second glass interlayer is strengthened.

An eighty-fifth aspect of the disclosure includes the glass laminate according to any one of the eighty-first to eighty-fourth aspects, wherein the second glass interlayer is chemically strengthened by an ion exchange process.

An eighty-sixth aspect of the present disclosure includes the glass laminate according to any one of the eighty-first to eighty-fifth aspects, wherein the second glass interlayer comprises a glass layer applied to the third major surface, the fourth major surface , or an ion-exchangeable glass frit of both the third major surface and the fourth major surface.

An eighty-seventh aspect of the present disclosure includes the glass laminate according to any one of the eighty-first to eighty-sixth aspects, wherein the first glass interlayer has a glass interlayer between the first major surface and the second major surface. a first thickness of at least 2 mm, and wherein the second glass interlayer has a second thickness of less than 2 mm between the third major surface and the fourth major surface.

An eighty-eighth aspect of the present disclosure includes the glass laminate according to any one of the eighty-first to eighty-seventh aspects, wherein the glass laminate comprises a thickness equal to the sum of the first thickness and the second thickness. a total glass thickness, and wherein the ratio of the first glass thickness to the total glass thickness is at least 0.7.

An eighty-ninth aspect of the disclosure includes the glass laminate according to any one of the eighty-first to eighty-eighth aspects, wherein the first glass thickness is at least 3 mm and the second glass thickness is 1.1mm or less.

A ninetieth aspect of the present disclosure includes the glass laminate according to any one of the eighty-first to eighty-ninth aspects, wherein the first glass thickness is at least 3.3 mm and the second glass thickness is 0.7mm or less.

A ninety-first aspect of the disclosure includes the glass laminate according to any one of the eighty-first to ninetieth aspects, wherein the second glass interlayer includes the second glass composition.

A ninety-second aspect of the disclosure includes the glass laminate according to any one of the eighty-first to ninety-first aspects, wherein the second glass composition is different from the borosilicate glass composition.

A ninety-third aspect of the present disclosure includes the glass laminate according to any one of the eighty-first to ninety-second aspects, wherein the second glass composition is selected from the group consisting of aluminosilicate glass compositions, Alkali aluminosilicate glass compositions, alkali borosilicate glass compositions, alkali aluminophosphosilicate glass compositions, alkali aluminoborosilicate glass compositions, and combinations thereof .

A ninety-fourth aspect of the disclosure includes the glass laminate according to any one of the eighty-first to ninety-third aspects, wherein the interlayer is selected from the group consisting of polyvinyl butyral (PVB), soundproofing Groups consisting of PVB (APVB), ionomers, vinyl acetate (EVA), thermoplastic polyurethane (TPU), polyester (PE), polyethylene terephthalate (PET), and combinations thereof .

A ninety-fifth aspect of the present disclosure includes the glass laminate according to any of the eighty-first to ninety-third aspects, wherein the intermediate layer comprises a thickness in the range of about 0.5 mm to about 2.5 mm.

A ninety-sixth aspect of the present disclosure includes the glass laminate according to any one of the eighty-first to ninety-fifth aspects, wherein the intermediate layer comprises at least one functional layer or film.

A ninety-seventh aspect of the present disclosure includes the glass laminate according to any one of the eighty-first to ninety-sixth aspects, wherein the functional layer or film provides a function selected from ultraviolet absorbing, infrared absorbing, infrared reflecting, Functions of sound damping, coloring, antenna, adhesion promotion, anti-glare processing, anti-reflection processing, and combinations thereof.

A ninety-eighth aspect of the present disclosure includes the glass laminate according to any one of the eighty-first to ninety-seventh aspects, wherein the first glass interlayer and the second glass interlayer are in a pair shape, wherein The first interlayer of glass includes a first depth of curvature of at least 2 mm, wherein the second interlayer of glass includes a second depth of curvature of at least 2 mm, and wherein the first depth of curvature is within 10% of the second depth of curvature.

A ninety-ninth aspect of the disclosure includes the glass laminate according to any one of the eighty-first to ninety-eighth aspects, wherein the first glass interlayer comprises a viscosity of the first glass interlayer at 10 ¹¹ poises the first temperature, and the second glass interlayer comprises a second temperature at which the viscosity of the second glass interlayer is 10 ¹¹ poise, and the first temperature is different from the second temperature.

A hundredth aspect of the present disclosure includes the glass laminate according to any of the eighty-first to ninety-ninth aspects, wherein the first glass interlayer is thicker than the second glass interlayer, and wherein the second temperature is greater than the first temperature.

A one hundred and first aspect of the present disclosure includes the glass laminate according to any one of the eighty first to one hundredth aspects, wherein the first glass interlayer is sag and comprises a depth of curvature of at least 2 mm , and wherein the second laminated glass is cold formed to be consistent with the first laminated glass.

A one hundred and second aspect of the present disclosure includes the glass laminate according to any one of the eighty first to one hundred and first aspects, wherein the second glass interlayer comprises a pigment coating on the third major surface.

A one hundred and third aspect of the present disclosure includes the glass laminate according to any one of the eighty first to one hundred and second aspects, wherein the first glass interlayer or the second glass interlayer comprises a coating.

The one hundred and fourth aspect of the present disclosure includes the glass laminate according to any one of the eighty-first to one hundred and third aspects, wherein the coating comprises at least one layer of metal and optionally at least one layer of dielectric Electric infrared reflective coating.

The one hundred and fifth aspect of the present disclosure includes a glass composition comprising: SiO ₂ in an amount ranging from about 72 mol % to about 80 mol %; about 2.5 mol % to about 5 mol % Al ₂ O ₃ in an amount in a range; B ₂ O ₃ in an amount in a range from about 11.5 mole percent to about 14.5 mole percent; wherein the glass composition comprises a liquidus viscosity greater than 500 kP; and wherein the glass composition The borosilicate glass composition contained has a viscosity of 200P and a temperature of 1725° C. or less.

The one hundred and sixth aspect of the present disclosure includes the glass composition according to the one hundred and fifth aspect, further including Na ₂ O in an amount ranging from about 4 mol % to about 8 mol %.

The one hundred and seventh aspect of the present disclosure includes the glass composition according to any one of the one hundred fifth to one hundred sixth aspects, wherein the amount of Na2O is from about 4.5 mole % to about ₈ in the mole % range.

The one hundred and eighth aspect of the present disclosure includes the glass composition according to any one of the one hundred fifth to one hundred seventh aspects, further comprising a range of about 0.5 mole % to about 3 mole % The amount of K ₂ O within.

The one hundred and ninth aspect of the present disclosure includes the glass composition according to any one of the one hundred fifth to one hundred eighth aspects, further comprising an amount in the range of about 0.5 to about 2.5 mole % MgO.

A one hundred and tenth aspect of the present disclosure includes the glass composition according to any one of the one hundred fifth to one hundred ninth aspects, further comprising up to about 4 mol % CaO.

A one hundred and eleventh aspect of the present disclosure includes the glass composition according to any one of the one hundred fifth to one hundred and tenth aspects, wherein the amount of SiO ₂ is at least 74 mole%.

The one hundred and twelfth aspect of the present disclosure includes a glass composition comprising: 74 mol% to 80 mol% SiO ₂ ; 2.5 mol% to 5 mol% Al ₂ O ₃ ; 11.5 mol% % to 14.5 mol% B2O3; 4.5 mol% to ₈ mol% Na2O; _0.5 mol% to ₃ mol% K2O; 0.5 mol% to _2.5 mol% MgO; and 0 mol% to 4 mol% CaO.

The one hundred and thirteenth aspect of the present disclosure includes the glass composition according to the one hundred and twelveth aspect, wherein the combined amount of Na ₂ O and K ₂ O is at least 5.5 mol%.

The one hundred and fourteenth aspect of the present disclosure includes the glass composition according to any one of the one hundred twelve to one hundred and thirteenth aspects, wherein the combined amount of MaO and CaO is at least 1.5 molar Ear%.

The one-hundred and fifteenth aspect of the present disclosure includes the glass composition according to any one of the one-hundred-twelfth to one-hundred-fourth aspects, wherein Na ₂ O, K ₂ O, MaO, and The combined amount of CaO is at least 7 mole percent.

A one-hundred-sixth aspect of the present disclosure includes the glass composition according to any one of the one-hundred-twelfth to one-hundred-fourth aspects, wherein the combined amount of Na ₂ O and K ₂ O is is at least 8 mol%.

A one-hundred seventeenth aspect of the present disclosure includes the glass composition according to any one of the one-hundred-twelfth to one-hundred-sixth aspects, comprising 0.03 mol% to 0.5 mol% of the total Amount of Fe ₂ O ₃ and FeO.

A one hundred and eighteenth aspect of the present disclosure includes an article comprising: a first glass interlayer comprising a first major surface and a second major surface opposite the first major surface, wherein the first glass interlayer comprises borosilicate A glass composition; a second glass interlayer comprising a third major surface and a fourth major surface opposite to the third major surface; and an interlayer bonding the second major surface of the first glass interlayer to the third major surface of the second glass interlayer surface; wherein: (A) the borosilicate glass composition of the first glass interlayer comprises: (i) SiO ₂ , B ₂ O ₃ and optionally Al ₂ O ₃ and/or P ₂ O ₅ ; and (ii ) one or more alkali metal oxides and optionally one or more alkaline earth metal oxides and/or ZnO; wherein SiO ₂ , B ₂ O ₃ , one or more alkali metal oxides and (when including When in the composition) the concentration of Al ₂ O ₃ , P ₂ O ₅ , and one or more alkaline earth metal oxides and/or ZnO molar percentages satisfies the relationship: SiO ₂ ≥ 72; B ₂ O ₃ ≥ 10 ; (R ₂ O+R'O+P ₂ O ₅ )≥Al ₂ O ₃ ; 0.80≤(1-[(2R ₂ O+2R'O+2P ₂ O ₅ )/(SiO ₂ +2Al ₂ O ₃ +2B ₂ O ₃ )])≤0.93; where R ₂ O is the sum of the concentrations of one or more alkali metal oxides, and (when borosilicate glass is included in the composition) R'O is is the sum of the concentrations of one or more alkaline earth metal oxides and/or ZnO; (B) when the glass with the borosilicate glass composition of the first glass interlayer uses a quasi-static indentation load of 2kg force and 136° When the Vickers indenter is used for the Vickers indentation test, the glass presents a plurality of radial cracks and circuit cracks that limit the expansion of radial cracks; (C) when the product is installed in the vehicle, the first glass interlayer is tied to the second The outside of the glass interlayer.

The one hundred and nineteenth aspect of the present disclosure includes the article according to the one hundred and eighteenth aspect, wherein the first glass interlayer is thicker than the second glass interlayer, and wherein the second glass interlayer is chemically strengthened by ion exchange processing .

A one-hundred-twentieth aspect of the present disclosure includes the article according to any one of the one-hundred-eighth to one-hundred-nineth aspects, wherein the first glass interlayer has a first major surface and a second major surface A first thickness of at least 2 mm between them, and wherein the second glass interlayer has a second thickness of less than 2 mm between the third major surface and the fourth major surface.

The one-hundred and twenty-first aspect of the present disclosure includes the article according to any one of the one-hundred-eighth to one-hundred-twentieth aspects, wherein the ratio of the first thickness to the sum of the first and second thicknesses is is at least 0.7.

The one-hundred and twenty-second aspect of the present disclosure includes the article according to any one of the one-hundred eighteenth to one hundred and twenty-first aspects, wherein the first thickness is at least 3.3 mm, and the second thickness The line is 0.7mm or less.

The one-hundred and twenty-third aspect of the present disclosure includes the article according to any one of the one-hundred eighteenth to one hundred and twenty-second aspects, wherein the second glass interlayer comprises borosilicate with the first glass interlayer A second glass composition different from the salt glass composition, and wherein the second glass composition is selected from the group consisting of soda lime silicate glass composition, aluminosilicate glass composition, alkali metal aluminosilicate glass composition, The group consisting of an alkali-containing borosilicate glass composition, an alkali metal aluminophosphosilicate glass composition, and an alkali metal aluminoborosilicate glass composition.

The one-hundred and twenty-fourth aspect of the present disclosure includes an article according to any one of the one-hundred-eighth to one-hundred-twenty-third aspects, wherein the visible light transmittance through the article measured according to ISO 13837A is At least 73%, and wherein the total solar transmission through the article measured according to ISO 13837A is 90% or less.

The one-hundred and twenty-fifth aspect of the disclosure includes an article according to any one of the one-hundred eighteenth to one hundred and twenty-fourth aspects, wherein the first major surface, the fourth major surface, or the first major surface Both the surface and the fourth major surface exhibit an optical distortion of at most 200 millidiopters measured according to ASTM 1561 using an optical distortion detector of transmission optics.

The one-hundred and twenty-sixth aspect of the present disclosure includes an article according to any one of the one-hundred-eighth to one-hundred-twenty-fifth aspects, wherein the middle layer is selected from polyvinyl butyral (PVB ), sound insulation PVB (APVB), ionomer, vinyl acetate (EVA), thermoplastic polyurethane (TPU), polyester (PE), polyethylene terephthalate (PET), and combinations thereof wherein the intermediate layer comprises a thickness in the range of about 0.5 mm to about 2.5 mm; wherein the intermediate layer comprises at least one functional layer or film, and wherein the functional layer or film provides a function selected from ultraviolet absorbing, infrared absorbing, infrared reflecting, Functions of sound damping, coloring, antenna, adhesion promotion, anti-glare processing, anti-reflection processing, and combinations thereof.

The one-hundred and twenty-seventh aspect of the present disclosure includes the article according to any one of the one-hundred-eighth to one-hundred-twenty-sixth aspects, wherein the first glass interlayer and the second glass interlayer are a pair shape, wherein the first interlayer of glass comprises a first depth of curvature of at least 2 mm, wherein the second interlayer of glass comprises a second depth of curvature of at least 2 mm, and wherein the first depth of curvature is within 10% of the second depth of curvature.

A one-hundred and twenty-eighth aspect of the disclosure includes the article according to any one of the one-hundred-eighth to one-hundred-twenty-seventh aspects, wherein the first glass interlayer is sagging and comprises at least 2 mm The depth of curvature, and wherein the second interlayer glass is cold-formed to be consistent with the first interlayer glass.

The one-hundred and twenty-ninth aspect of the present disclosure includes the article according to any one of the one-hundred-eighth to one-hundred-twenty-eighth aspects, wherein the first glass interlayer is formed by a downward stretching process Manufacture wherein the down draw process is a fusion down draw process, wherein the glass of the first glass interlayer having a borosilicate glass composition has a liquidus viscosity greater than or equal to 500 kpoise, and wherein the first The glass of the glass interlayer having a borosilicate glass composition has a 200 Poise temperature of less than or equal to 1725°C.

A one-hundred and thirtieth aspect of the present disclosure includes an article comprising: an outer interlayer comprising borosilicate glass and having a thickness of at least 200 μm and not more than 1 cm, wherein, in terms of constituent oxides, borosilicate glass The composition comprises: SiO ₂ , B ₂ O ₃ , Al ₂ O ₃ , one or more alkali metal oxides, and one or more compounds selected from the group consisting of MgO, CaO, SrO, BaO, and ZnO A plurality of divalent cationic oxides, wherein molar percentages based on oxides of SiO ₂ , B ₂ O ₃ , one or more alkali metal oxides, Al ₂ O ₃ , and one or more alkaline earth metal oxides The concentration satisfies the relationship: (R ₂ O+R'O)≥Al ₂ O ₃ , 0.80<(1-[(2R ₂ O+2R'O)/(SiO ₂ +2Al ₂ O ₃ +2B ₂ O ₃ ) ])<0.93, wherein R ₂ O is the sum of the concentration of one or more alkali metal oxides, and R'O is the sum of the concentration of one or more alkaline earth metal oxides; A second glass having a different composition of interlayer borosilicate glass, wherein the inner interlayer reinforces the outer interlayer, hardens the outer interlayer to withstand the bending forces applied thereto, and wherein the composition of the second glass is selected from Soda lime silicate glass composition, aluminosilicate glass composition, alkali metal aluminosilicate glass composition, alkali borosilicate glass composition, alkali metal aluminosilicate glass composition, and alkali A group composed of metal aluminoborosilicate glass composition; the middle layer couples the inner interlayer and the outer interlayer, wherein the middle layer is a polymer and inhibits the penetration of cracks from the outer interlayer to the inner interlayer.

The one-hundred and thirty-first aspect of the present disclosure includes the article according to the one-hundred and thirtieth aspect, wherein when the glass of the borosilicate glass composition with the outer interlayer is formed to a thickness of 1 mm and an area of 2×2 cm ² 100 polished flat samples of the main surface were tested using a square-shaped 136° four-sided cone Vickers indenter at 25°C and 50% relative humidity to guide orthogonally into the center of the main surface, and the indentation The indenter is subjected to a quasi-static displacement at a rate of 60 μm per second to a maximum force of 3 kg. When the indentation load is maintained for 10 seconds, under normal circumstances all cracks extending radially and/or transversely from the indenter through the sample are contained within the crack inside the loop.

The one-hundred and thirty-second aspect of the disclosure includes an article according to any one of the one-hundred thirty to one-hundred and thirty-first aspects, wherein when rapidly cooled from 25° C. by placing the sample in cold water Cracks extending radially and/or transversely through the sample do not propagate beyond the crack loop under normal conditions up to 1°C.

The one hundred and thirty third aspect of the present disclosure includes the article according to any one of the one hundred thirty to one hundred thirty second aspects, wherein a majority of the crack loops of the sample are circular and have less than 1mm radius.

A one-hundred thirty-fourth aspect of the present disclosure includes an article comprising: a first glass interlayer comprising a first major surface and a second major surface opposite the first major surface, wherein the first glass interlayer comprises boron Silicate glass, and wherein, in terms of constituent oxides, the composition of the borosilicate glass comprises: SiO ₂ , B ₂ O ₃ , Al ₂ O ₃ , one or more alkali metal oxides, and One or more divalent cation oxides of the group consisting of MgO, CaO, SrO, BaO, and ZnO, wherein based on SiO ₂ , B ₂ O ₃ , one or more alkali metal oxides, Al ₂ O _3. The molar percentage concentration of oxides of one or more divalent cation oxides satisfies the relationship: (R ₂ O+R'O)≥Al ₂ O ₃ , 0.80<(1-[(2R ₂ O +2R'O)/(SiO ₂ +2Al ₂ O ₃ +2B ₂ O ₃ )])<0.93, where R ₂ O is the sum of the concentrations of one or more alkali metal oxides, and R'O is is the sum of the concentrations of one or more divalent cation oxides; a second glass interlayer comprising a third major surface and a fourth major surface opposite the third major surface; The two major surfaces are bonded to the third major surface of the second glass interlayer; wherein the transmittance through the article of ultraviolet light having a wavelength in the range of 300-380 nm is 75% or less; wherein the transmittance through the article in the visible spectrum The light transmission is 73% or more; and wherein the total solar light transmission through the article is 61% or less.

The one-hundred thirty-fifth aspect of the present disclosure includes the article according to the one-hundred thirty-fourth aspect, wherein the borosilicate glass composition comprises at least 74 mole % SiO ₂ ; at least 10 mole % B ₂ O ₃ ; and Al ₂ O ₃ having a sum of SiO ₂ , B ₂ O ₃ , and Al ₂ O ₃ in an amount of at least 90 mole percent.

The one-hundred and thirty-sixth aspect of the present disclosure includes an article comprising: borosilicate glass, wherein in terms of constituent oxides, the composition of the borosilicate glass comprises: SiO ₂ , B ₂ O ₃ , Al ₂ O ₃ , one or more alkali metal oxides, and one or more divalent cation oxides selected from the group consisting of MgO, CaO, SrO, BaO, and ZnO, wherein based on SiO ₂ , B ₂ O ₃ , one or more alkali metal oxides, Al ₂ O ₃ , and the concentration of molar percentages of oxides of one or more divalent cation oxides satisfy the relationship: (R ₂ O+R 'O)≥Al ₂ O ₃ , 0.80<(1-[(2R ₂ O+2R'O)/(SiO ₂ +2Al ₂ O ₃ +2B ₂ O ₃ )])<0.93, where R ₂ O is The sum of the concentrations of one or more alkali metal oxides, and the R'O series is the sum of the concentrations of one or more divalent cation oxides; crack loops, formed in borosilicate glasses, of which the article has no A radial or transverse crack that intersects a crack loop and extends outward beyond the crack loop.

The one-hundred thirty-seventh aspect of the disclosure includes the article according to the one-hundred thirty-sixth aspect, wherein the crack loop has a circular perimeter.

A one-hundred thirty-eighth aspect of the present disclosure includes the article according to any one of the one-hundred thirty-sixth to one-hundred thirty-seventh aspects, wherein the circular perimeter has a diameter of less than 1 mm.

The one-hundred and thirty-ninth aspect of the disclosure includes the article according to any one of the one-hundred thirty-sixth to one hundred and thirty-eighth aspects, wherein the borosilicate glass has a thickness of at least 200 μm and no more than 1 cm thickness of.

The one-hundred fortieth aspect of the disclosure includes the article according to any one of the one-hundred thirty-sixth to one hundred thirty-ninth aspects, wherein the borosilicate glass has an Low temperature thermal expansion coefficient of 8.7ppm/℃.

The one-hundred forty-first aspect of the present disclosure includes the article according to any one of the thirty-thirty to one-hundred-twenty-ninth aspects, wherein the thickness is greater than or equal to 2.0 mm.

The one hundred and forty second aspect of the disclosure includes the article according to any one of the thirty to one hundred and twenty ninth aspects, wherein the composition of the borosilicate glass comprises greater than or equal to 4 mole % And less than or equal to 6 mol% Na ₂ O.

The one hundred and forty third aspect of the present disclosure includes the article according to any one of the thirty to one hundred and twenty ninth aspects, wherein the composition of the borosilicate glass comprises: greater than or equal to 3 moles % and less than or equal to 5 mol % of Al ₂ O ₃ ; and greater than or equal to 12 mol % and less than or equal to 16 mol % of B ₂ O ₃ .

The one-hundred forty-fourth aspect of the present disclosure includes the article according to any one of the thirtieth to one-hundred-twenty-ninth aspects, which includes at least one of the following: the composition of borosilicate glass includes Greater than or equal to 0.03 mol% and less than or equal to 0.5 mol% _{of Fe2O3} , and the thickness is less than or equal to 3.3mm, and the outer interlayer has greater than or equal to 90% and less than or Equal to 92.5% transmittance.

A one hundred and forty fifth aspect of the present disclosure includes the article according to any one of the thirty to one hundred and twenty ninth aspects, wherein the outer glass interlayer is composed of borosilicate glass.

The one hundred and forty-sixth aspect of the present disclosure includes a borosilicate glass composition comprising: greater than or equal to 60 mol % and less than or equal to 96.0 mol % of SiO ₂ ; greater than or equal to 1.0 mol % and less than or equal to 25.0 mol% of B2O3, greater _than or equal to 0.3 mol% of _{Al2O3 ;} greater than or equal to _0.0 mol% and less than or equal to 0.3 mol% of _Li2O ; not zero amount of Na ₂ O; and one or more divalent metal oxides RO, wherein: the composition amount of each component expressed in mole % expressed by the molecular formula of each component satisfies the relationship B ₂ O ₃ +3.5 *Al ₂ O ₃ ≤27.5 mol%, and at least one of the following: (A) The composition of each component satisfies two of the following conditions: (i) C _rb - (3.4 - 0.5 * C _nb ) <0.000; and (ii) 1 - 2 * (Alk ₂ O + RO) / P _total > 0.83, where: (a) C _rb is calculated from the composition expressed in mole % of composition according to the following equation Value of the rotational balance parameter: C _rb = abs(2 * max(0, (Alk ₂ O + RO) - (Al ₂ O ₃ + B ₂ O ₃ )) + 2 * min(B ₂ O ₃ , R ₂ O+RO-Al ₂ O ₃ ) + 0.65 * (SiO ₂ + 2 * Al ₂ O ₃ + 2 * B ₂ O ₃ ) - 80), (b) the C _nb system is based on the Mo of the composition according to the following equation The value of the network balance parameter calculated from the composition expressed in mol%: C _nb = abs(SiO ₂ - 6 * min(Alk ₂ O, Al ₂ O ₃ ) - 2 * min(Alk ₂ O + RO - Al ₂ O ₃ , B ₂ O ₃ ) - max(24 + 2 * max(0, B ₂ O ₃ - max(0, R ₂ O+RO-Al ₂ O ₃ )), 44)), (c) Alk ₂ O means One or more alkali metal oxides (if present in the composition), (d) Ptotal is the value of the _total polyhedral parameter calculated from the glass composition expressed in mole % of composition according to the following equation: P _total = SiO ₂ + 2 * Al ₂ O ₃ + 2 * B ₂ O ₃ , and (B) the composition amount of each component satisfies the following condition: Pd - (2.58 - 0.2 * (Na ₂ O / Al ₂ O ₃ ) ) < 0.000, where _Pd is the value of the density parameter calculated from the glass composition expressed in mole % of composition according to the following equation: _Pd = 2.487 - 0.0068998 * B ₂ O ₃ + 0.041371 * BaO + 0.13897 * Bi ₂ O ₃ + 0.011637 * CaO + 0.055366 * Cs ₂ O + 0.025420 * Fe ₂ O ₃ + 0.10294 * Gd ₂ O ₃ + _0.0 K5 + 0.079903 * La ₂ O ₃ + 0.0041594 * Li ₂ O + 0.0084582 * MgO + 0.019720 * MnO + 0.0064419 * Na ₂ O + 0.018282 * NiO + 0.065781 * PbO - 0.002953 * SiO ₂ + 0.027682 * SrO + 0.0055367 * TiO ₂ + 0.0068497 * V ₂ O ₅ + 0.048699 * Y ₂ O ₃ + 0.021527 * ZnO + 0.026527 * ZrO ₂ + 0.011033 * (min(B ₂ O ₃ , max(0, Alk ₂ O + RO - Al ₂ O ₃ ))) .

A one-hundred and forty-seventh aspect of the present disclosure includes the borosilicate glass composition according to the one-hundred and forty-sixth aspect, wherein: the composition amount of each component satisfies two of the following conditions: (i) C _rb - (3.4 - 0.5 * C _nb ) <0.000; and (ii) 1 - 2 * (Alk ₂ O + RO) / P _total > 0.83, the composition contains less than or equal to 9.7 mol% of Na ₂ O and The combined amount of Al ₂ O ₃ , the composition basically does not contain BaO, fluorine, and rare earth oxides.

The one hundred and forty-eighth aspect of the present disclosure includes the borosilicate glass composition according to any one of the one hundred forty-sixth to one hundred forty-seventh aspects, wherein: the composition comprises: greater than or SiO ₂ equal to 60.0 mol % and less than or equal to 78 mol %, B ₂ O ₃ greater than or equal to 5.0 mol % and less than or equal to 17.0 mol %, greater than or equal to 2.5 mol % and less than Or equal to 5.3 mol% of Na ₂ O, greater than or equal to 0.3 mol% and less than or equal to 5.3 mol% of Al ₂ O ₃ , greater than or equal to 0.0 mol% and less than or equal to 3.0 mol% of K2O, _0.0 mol% or more and 1.5 mol% or less of CaO, 0.0 mol% or more and 0.2 mol% or less of _Li2O , 5.0 mol% or more % Na ₂ O+K ₂ O, and the composition amount of each component therein satisfies the following condition: 20.3 ≤ B ₂ O ₃ + 3.5 * Al ₂ O ₃ ≤ 27.5.

The one hundred and forty-ninth aspect of the disclosure includes the borosilicate glass composition according to any one of the one hundred forty-sixth to one hundred forty-eighth aspects, wherein the composition comprises: greater than or equal to 0.0 mol% and less than or equal to 5.0 mol% of MgO; greater than or equal to 0.0 mol% and less than or equal to 4.0 mol% of _P2O5 , greater than or equal to ₀ mol% and less than or equal to 0.25 mol% of SnO ₂ , a combined amount of (Na ₂ O+K ₂ O+MgO+CaO+ZnO+Al ₂ O ₃ +B ₂ O ₃ +SiO ₂ ) greater than or equal to 95.0 mol%, greater than or A combined amount of (CaO+MgO) equal to 0.0 mol% and less than or equal to 5.0 mol%, and (FeO+Fe ₂ O ₃ ), and the composition amount of each component of the composition satisfies the following two conditions at the same time: (C) (Na ₂ O+K ₂ O+MgO+CaO+SrO+BaO+ZnO)/(R ₂ O +RO) ≤ 0.95, and (D) 1.01 ≤ Na ₂ O/Al ₂ O ₃ ≤ 1.35.

The one hundred and fiftieth aspect of the present disclosure includes the borosilicate glass composition according to any one of the one hundred forty-sixth to one hundred forty-ninth aspects, wherein the composition comprises: greater than or equal to 72.0 Mole % and less than or equal to 78.0 mole % of SiO ₂ , greater than or equal to 5.0 mole % and less than or equal to 20.0 mole % of B ₂ O ₃ , greater than or equal to 2.0 mole % and less than or equal to 8.0 mol% of Na2O, greater _than or equal to 2.0 mol% and less than or equal to 4.0 mol% of _Al2O3 , greater than or equal to _0.0 mol% and less _than or equal to 3.0 mol% of K2 O, CaO greater than or equal to 0.0 mol% and less than or equal to 2.0 mol%, MgO greater than or equal to 0.0 mol% and less than or equal to 2.0 mol%, and greater than or equal to 0.0 mol% and less SnO ₂ equal to or equal to 0.2 mol%.

A one hundred fifty first aspect of the present disclosure includes the borosilicate glass composition according to any one of the one hundred forty six to one hundred fifty aspects, wherein the composition comprises: greater than or equal to 0.0 mol% and less than or equal to 0.5 mol% of MnO ₂ , greater than or equal to 0.0 mol% and less than or equal to 0.5 mol% of MnO, greater than or equal to 0.0 mol% and less than or equal to 0.5 mol% % of TiO ₂ , and greater than or equal to 0.0 mol% and less than or equal to 1.0 mol% (Fe+Cr+Mo+V+Cu+Co), wherein the composition system is: substantially free of Li ₂ O , and substantially free of PbO.

The one-hundred and fifty-second aspect of the disclosure includes the borosilicate glass composition according to any one of the one-hundred forty-sixth to one hundred and fifty-first aspects, wherein each component of the composition is The composition amount meets the following conditions: (E) _0.0≤2 *M exc +2*min(B ₂ O ₃ , R ₂ O+RO-Al ₂ O ₃ )+0.65*P _total -80≤3.0, where: M _exc is the value of the modifier excess parameter calculated from the glass composition in mole % of composition according to the following equation: M _exc = max(0, (Alk ₂ O + RO) - (Al ₂ O ₃ + B ₂ O ₃ )), and (F)0.0 ≤ abs(Si _exc - 3 * ((B ₂ O ₃ + Al ₂ O ₃ ) - (Alk ₂ O + RO)) - max(24 - B _exc , 44 - 3 * B _exc )) ≤ 3.0, where: (i) Si _exc is the value of the silica excess parameter calculated from the glass composition expressed in mole % of composition according to the following equation: Si _exc = SiO ₂ – 6 * min(Alk ₂ O, Al ₂ O ₃ O ₃ ) – 2 * min(Alk ₂ O+RO-Al ₂ O ₃ O ₃ , B ₂ O ₃ ), and (ii) B _exc is based on the following equation And the value of the boron excess parameter calculated from the glass composition in mole % of composition: B _exc = max (0, B ₂ O ₃ - max(0, R ₂ O + RO - Al ₂ O ₃ )).

The one hundred and fifty third aspect of the present disclosure includes the borosilicate glass composition according to any one of the one hundred forty six to one hundred fifty second aspects, wherein the composition amount of each component satisfies The following condition: P _d - (2.58 - 0.2 * (Na ₂ O / Al ₂ O ₃ O ₃ )) < 0.000.

The one hundred and fifty-fourth aspect of the disclosure includes the borosilicate glass composition according to any one of the one hundred forty-sixth to one hundred fifty-third aspects, wherein the composition comprises: greater than or equal to 60.0 mol % and less than or equal to 77.5 mol % of SiO ₂ , greater than or equal to 5.0 mol % and less than or equal to 17.0 mol % of B ₂ O ₃ , greater than or equal to 2.5 mol % and less than or Na ₂ O equal to 5.3 mol%, Al ₂ O ₃ greater than or equal to 0.3 mol% and less than or equal to 5.3 mol%, K greater than or equal to 0.0 mol% and less than or equal to 3.0 mol% ₂ O, _Li2O greater than or equal to 0.0 mol% and less than or equal to 0.2 mol%, BaO greater than or equal to 0.0 mol% and less than or equal to 0.2 mol%, and 5.0 mol% or greater The combined amount of (Na ₂ O+K ₂ O).

The one hundred and fifty-fifth aspect of the disclosure includes the borosilicate glass composition according to any one of the one hundred forty-sixth to one hundred fifty-fourth aspects, wherein the composition comprises: greater than or equal to 5.0 mol% and less than or equal to 5.2 mol% of Na2O, greater _than or equal to 0.3 mol% of MgO, and greater than or equal to 0.0 mol% and less than or equal to 0.3 mol% of _TiO2 , wherein The composition basically does not contain fluorine.

The one hundred and fifty-sixth aspect of the present disclosure includes the borosilicate glass composition according to any one of the one hundred forty-sixth to one hundred and fifty-fifth aspects, wherein the composition amount of each component satisfies The following conditions: 1 - 2 * (Alk ₂ O + RO) / P _total > 0.83.

The one hundred and fifty seventh aspect of the present disclosure includes the borosilicate glass composition according to any one of the one hundred forty-sixth to one hundred fifty-sixth aspects, wherein the composition amount of each component satisfies The following conditions: (G) 77 ≤ (2 * M _exc + 2 * min(B ₂ O ₃ , R ₂ O + RO - Al ₂ O ₃ )) + 0.65 * P _total ≤ 82, where: M _exc is based on The value of the modifier excess parameter calculated from the glass composition expressed in mole % of composition is calculated from the following equation: M _exc = max(0, (Alk ₂ O + RO) - (Al ₂ O ₃ + B ₂ O ₃ )), and (H)0.84 ≤ 1 - 2 * (Alk ₂ O + RO) / P _total ≤ 0.90.

The one hundred and fifty-eighth aspect of the disclosure includes the borosilicate glass composition according to any one of the one hundred forty-sixth to one hundred fifty-seventh aspects, wherein the composition comprises: greater than or equal to 0.0 mol% and less than or equal to 4.0 mol% of P ₂ O ₅ , greater than or equal to 0 mol% and less than or equal to 0.25 mol% of SnO ₂ , greater than or equal to 95.0 mol% of (Na _{2 ( CaO + MgO _ _} ), and the combined amount of (FeO+Fe ₂ O ₃ ) greater than or equal to 0.0 mol% and less than or equal to 0.5 mol%, and the composition amount of each component of the composition satisfies the two conditions : (I) (Na ₂ O + K ₂ O + MgO + CaO + SrO + BaO + ZnO) / (R ₂ O + RO) ≤ 0.95, and (J) 1.01 ≤ Na ₂ O/Al ₂ O ₃ ≤ 1.35 .

The one hundred and fifty-ninth aspect of the disclosure includes the borosilicate glass composition according to any one of the one hundred forty-sixth to one hundred fifty-eighth aspects, wherein the composition comprises: greater than or equal to 72.0 mol % and less than or equal to 77.5 mol % of SiO ₂ , greater than or equal to 2.0 mol % and less than or equal to 4.0 mol % of Al ₂ O ₃ , greater than or equal to 0.0 mol % and less than or CaO equal to 2.0 mol%, MgO greater than or equal to 0.0 mol% and less than or equal to 2.0 mol%, and SnO ₂ greater than or equal to 0.0 mol% and less than or equal to 0.2 mol%.

The one hundred and sixtieth aspect of the present disclosure includes the borosilicate glass composition according to any one of the one hundred forty-sixth to one hundred fifty-ninth aspects, wherein the composition comprises: greater than or equal to 0.0 mol% and less than or equal to 0.5 mol% of MnO ₂ , greater than or equal to 0.0 mol% and less than or equal to 0.5 mol% of MnO, greater than or equal to 0.0 mol% and less than or equal to 0.5 mol% % of TiO ₂ , the combined amount of (Fe+Cr+Mo+V+Cu+Co) greater than or equal to 0.0 mol% and less than or equal to 1.0 mol%, and greater than or equal to 0.0 mol% and less than Or a combined amount of (La ₂ O ₃ +Y ₂ O ₃ ) equal to 1.0 mol%.

The one hundred and sixty-first aspect of the present disclosure includes the borosilicate glass composition according to any one of the one hundred forty-sixth to one hundred sixty aspects, wherein the composition is substantially free of fluorine, BaO, LiO ₂ , and PbO.

The one hundred and sixty-second aspect of the present disclosure includes the borosilicate glass composition according to any one of the one hundred forty-sixth to one hundred sixty-first aspects, wherein each component of the composition is The quantity meets the following conditions: (K) 0.0 ≤ 2 * M _exc + 2 * min(B ₂ O ₃ , R ₂ O + RO - Al ₂ O ₃ ) + 0.65 * P _total - 80 ≤ 3.0, where: M _exc is the value of the modifier excess parameter calculated from the glass composition expressed in mole % of composition according to the following equation: M _exc = max(0, (Alk ₂ O + RO) - (Al ₂ O ₃ + B ₂ O ₃ )), and (L)0.0 ≤ abs(Si _exc - 3 * ((B ₂ O ₃ + Al ₂ O ₃ ) - (Alk ₂ O + RO)) - max(24 - B _exc , 44 - 3 * B _exc )) ≤ 3.0, where: (i) Si _exc is the value of the silica excess parameter calculated from the glass composition expressed in mole % of composition according to the following equation: Si _exc = SiO ₂ – 6 * min(Alk ₂ O, Al ₂ O ₃ O ₃ ) – 2 * min(Alk ₂ O+RO-Al ₂ O ₃ O ₃ , B ₂ O ₃ ), and (ii) B _exc are calculated according to the following equation Value of the boron excess parameter calculated from the glass composition in mole % of composition: B _exc = max (0, B ₂ O ₃ - max(0, R ₂ O + RO - Al ₂ O ₃ )).

The one hundred and sixty third aspect of the disclosure includes the borosilicate glass composition according to any one of the one hundred forty six to one hundred sixty second aspects, wherein the composition comprises: greater than or equal to 11 mol% and less than or equal to 16 mol% of B2O3, greater than or equal to ₂ mol% and less than or equal to ₆ mol% _{of Al2O3} , and greater than or equal to or equal to 7.0 mol% % of the total amount of Na ₂ O, K ₂ O, MgO, and CaO.

The one hundred and sixty-fourth aspect of the present disclosure includes the borosilicate glass composition according to any one of the one hundred forty-sixth to one hundred sixty-third aspects, wherein the composition comprises 4 or more mol% and less than or equal to 6 mol% Na ₂ O.

The one hundred and sixty-fifth aspect of the disclosure includes the borosilicate glass composition according to any one of the one hundred forty-sixth to one hundred sixty-fourth aspects, wherein the composition of the borosilicate glass is The compound comprises: greater than or equal to 3 mol% and less than or equal to 5 mol% of Al ₂ O ₃ ; and greater than or equal to 12 mol% and less than or equal to 16 mol% of B ₂ O ₃ .

The one hundred and sixty-sixth aspect of the present disclosure includes a glass article comprising the borosilicate glass composition according to any one of the one hundred forty-sixth to one hundred sixty-fifth aspects.

A one hundred and sixty seventh aspect of the present disclosure includes the glass article according to the one hundred sixty sixth aspect, wherein the glass article comprises a density measured at 20°C of less than 2.5 g/cm ³ .

A one hundred sixty eighth aspect of the present disclosure includes the glass article according to the one hundred sixty seventh aspect, wherein the density measured at 20°C is less than 2.3 g/cm ³ .

The one hundred and sixty-ninth aspect of the present disclosure includes the glass article according to any one of the one hundred sixty-seventh to one hundred sixty-eighth aspects, wherein when the glass having the borosilicate glass composition is formed 100 polished flat samples with a thickness of 1 mm and a major surface of 2 x 2 ^cm2 area, and guided orthogonally using a square-shaped 136° four-sided cone Vickers indenter at 25°C and 50% relative humidity The test is carried out into the center of the main surface, and the indenter utilizes a quasi-static displacement at a rate of 60 μm per second to a force of up to 3 kg. When the indentation load is held for 10 seconds, under normal conditions, radial and/or lateral from the indenter All cracks extending through the sample are contained within crack loops.

A one hundred and seventieth aspect of the present disclosure includes the glass article according to the one hundred and sixty ninth aspect, wherein a majority of the crack loops of the sample are circular and have a radius of less than 1 mm.

As shown in the various exemplary embodiments, the construction and arrangement of compositions, components, and structures are illustrative only. Although this disclosure describes only a few embodiments in detail, many modifications are possible (e.g., changes in size, dimension, structure, shape, and proportions of various elements, values of parameters, mounting arrangements, use of materials, colors, orientation ), without materially departing from the novel teachings and advantages of the subject matter described herein. Materials (eg, glazing disclosed herein) can be used in glazing in architectural applications (eg, windows, partitions), or can be used in other ways (eg, for packaging (eg, containers)). The order or sequencing of any processes, logical algorithms, or method steps may be varied or re-sequenced according to alternative embodiments. Other substitutions, modifications, changes, and omissions may also be made in the design, operating conditions, and arrangement of the various exemplary embodiments without departing from the scope of the technology.

100:vehicle 110: subject 120: opening 130: Auto glass window 200: Glass interlayer 202: the first main surface 204: second main surface 206: Subsurface 210: first thickness 300: laminated structure 310: The first glass interlayer 320: second glass interlayer 330: middle layer 332: the third main surface 334: the fourth main surface 336: Subsurface 340: second thickness 400: Curved Glass Laminates 410: first curvature depth 420: second curvature depth 510: radial crack 520: Ring crack 530: valley value 540: Peak 550: arrow 560: curve 570: Asterisk 700: Equipment 702: Isobaric tube 704: Groove 706: The first forming surface 708: second forming surface 710: root 712: glass composition 714: Glass interlayer 716: Second isobaric pipe 718: second groove 720: The third forming surface 722: The fourth forming surface 724: glass composition 726a: cladding layer 726b: cladding layer 800: system 810: sensor 820: input signal 830: output signal

The accompanying drawings are included to provide a further understanding and are incorporated into and constitute a part of this specification. The drawings illustrate one or more embodiments, and together with the description illustrate the principles and operation of the various embodiments. In the schema:

FIG. 1 is an illustration of a vehicle including glazing or laminate according to one or more embodiments;

Figure 2 is a side view of a glass article according to one or more embodiments;

Figure 3 is a side view of a laminate including glass articles according to one or more embodiments;

Figure 4 is a side view of a laminate including glass articles according to one or more embodiments;

Figures 5A-5C illustrate for the disclosed fusion formed borosilicate glass composition (Figure 5A), the comparative soda lime glass composition (Figure 5B), and the comparative float formed boron Micrographs of cracks induced by indentation testing of silicate glass compositions (Fig. 5C) and their correlations;

Figures 6A and 6B illustrate the results of thermal shock tests for the disclosed fusion-formed borosilicate glass composition (Figure 6A) and a comparative soda-lime glass composition (Figure 6B);

FIG. 7 illustrates a fusion forming apparatus for fusion forming a glass interlayer of a borosilicate glass composition according to an exemplary embodiment;

Figure 8 illustrates a graph of solar transmittance for various borosilicate glass compositions according to an exemplary embodiment;

FIG. 9 illustrates a system including sensors configured to transmit and receive signals;

Figures 10 and 11 illustrate graphs of transmittance of visible light, total sunlight, and ultraviolet light as a function of iron content in glass, according to exemplary embodiments; and

12 and 13 illustrate graphs comparing visible light transmittance and total solar transmittance of glass compositions according to exemplary embodiments.

Figure 14 is a digital image of a cross-section of a glass article according to an exemplary embodiment.

Figure 15 is a graph of transmittance measurements for two exemplary compositions according to an exemplary embodiment.

Figure 16 is a graph of measured retention strength after indentation before and after thermal shock of samples constructed using exemplary compositions described herein, according to an exemplary embodiment.

Figure 17A is an image of a sample constructed from the exemplary compositions described herein with scratches from the Knoop scratch test, according to an exemplary embodiment.

Figure 17B is an image of a sample constructed from comparative exemplary compositions described herein with scratches from the Knoop scratch test, according to an exemplary embodiment.

Figure 17C is an image of a sample constructed from comparative exemplary compositions described herein with scratches from a Knoop scratch test, according to an exemplary embodiment.

Domestic deposit information (please note in order of depositor, date, and number) none Overseas storage information (please note in order of storage country, institution, date, and number) none

Claims (30)

A borosilicate glass composition comprising: at least 75 mole percent SiO ₂ ; at least 10 mole percent B ₂ O ₃ ; and having a sum of SiO ₂ , B ₂ O ₃ , and Al ₂ O ₃ of at least An amount of Al ₂ O ₃ of 90 mole percent; wherein the borosilicate glass composition comprises a liquidus viscosity greater than 500 kP; and wherein the borosilicate glass composition comprises borosilicate in the borosilicate A temperature range at which the salt glass composition has a viscosity of 200P is 1725° C. or less. The borosilicate glass composition as claimed in claim 1, further comprising about 2 mol % to about 8 mol % Na ₂ O. The borosilicate glass composition as claimed in claim 1, further comprising about 1 mol% to about 4 mol% K ₂ O. The borosilicate glass composition according to any one of claims 1-3, wherein a total amount of Na ₂ O and K ₂ O is at least 4 mol%. The borosilicate glass composition according to claim 4, further comprising at least one of MgO or CaO, wherein a total amount of MgO and CaO is at most 5 mol%. The borosilicate glass composition as claimed in claim 5, wherein a total amount of Na ₂ O, K ₂ O, MgO, and CaO is at least 7 mol%. The borosilicate glass composition of any one of claims 1-3, further comprising P ₂ O ₅ , wherein P ₂ O ₅ is present in an amount up to 4 mol%. The borosilicate glass composition of any one of claims 1-3, further comprising about 0.05 mol% to about 0.25 mol% _SnO2 . The borosilicate glass composition according to any one of claims 1-3, further comprising 0.05 mol% to 0.50 mol% Fe ₂ O ₃ . The borosilicate glass composition of any one of claims 1-3, comprising a density of less than 2.4 g/cm ³ . The borosilicate glass composition of any one of claims 1-3, comprising a strain point of about 500°C to about 560°C. The borosilicate glass composition of any one of claims 1-3, comprising an annealing point of about 550°C to about 590°C. An article comprising: an outer interlayer comprising a borosilicate glass and having a thickness of at least 200 μm and not more than 1 cm, wherein the composition of the borosilicate glass, in terms of constituent oxides, comprises: SiO ₂ , B ₂ O ₃ , Al ₂ O ₃ , one or more alkali metal oxides, one or more divalent cation oxides composed of MgO, CaO, SrO, BaO, and ZnO, greater than or equal to 11 Mo Mole % and less than or equal to 16 mole % of B2O3; greater than or equal to ₂ mole % and less than or equal to ₆ mole % of _{Al2O3 ;} and greater _than or equal to 7.0 mole % of Na2O, K A total amount of ₂ O, CaO, and MgO; wherein SiO ₂ , B ₂ O ₃ , the one or more alkali metal oxides, Al ₂ O ₃ , and one or more of the one or more alkaline earth metal oxides The molar percentage concentration of the oxide substrate satisfies the following relationship: (R ₂ O+R'O)≥Al ₂ O ₃ 0.80<(1-[(2R ₂ O+2R'O)/(SiO ₂ +2Al ₂ O ₃ +2B ₂ O ₃ )])<0.93, wherein R ₂ O is the sum of the concentrations of the one or more alkali metal oxides, R'O is the one or more alkaline earth metal oxides the sum of the concentrations of; an inner interlayer comprising a second glass different in composition from the borosilicate glass of the outer interlayer, wherein the inner interlayer reinforces the outer interlayer, hardens the outer interlayer, and withstand bending forces applied thereto, and wherein the composition of the second glass is selected from a soda lime silicate glass composition, an aluminosilicate glass composition, an alkali metal aluminosilicate glass composition , a group consisting of an alkali-containing borosilicate glass composition, an alkali metal aluminophosphosilicate glass composition, and an alkali metal aluminoborosilicate glass composition; an intermediate layer coupled to the inner The interlayer and the outer interlayer, wherein the middle layer is a polymer, inhibit the penetration of cracks from the outer interlayer to the inner interlayer. The article of claim 13, wherein when the glass of the composition of the borosilicate glass with the outer interlayer is formed as 100 polished flat samples of a major surface with a thickness of 1 mm and an area of ² x 2 cm , and use a square-shaped 136° four-sided cone Vickers indenter to guide orthogonally into a center of the main surface at 25°C and 50% relative humidity for testing, and the indenter uses a 60μm per second Rate quasi-static displacement to a maximum force of 3 kg When the indentation load is held for 10 seconds, all cracks extending radially and/or transversely from the indenter through the samples are typically contained within a crack loop. The article of claim 14, wherein when the samples are rapidly cooled from 25°C to 1°C by placing the samples in cold water, cracks extending radially and/or transversely through the samples do not normally will propagate beyond the crack loop. The article of claim 14, wherein a majority of the crack loops of the samples are circular and have a radius of less than 1 mm. The article of any one of claims 13-16, wherein the borosilicate glass of the outer interlayer comprises at least 74 mol % SiO ₂ and at least 10 mol % B ₂ O ₃ ; and wherein The borosilicate glass of the outer interlayer includes a sum of SiO ₂ , B ₂ O ₃ , and Al ₂ O ₃ of at least 90 mole percent. The article of any one of claims 13-16, wherein the outer interlayer is thicker than the inner interlayer, and wherein the second glass of the inner interlayer is chemically strengthened by an ion exchange process. The article of any one of claims 13-16, wherein the thickness of the outer interlayer is a first thickness, wherein the first thickness is at least 2mm, and wherein the inner interlayer has a thickness of less than 2mm a second thickness. The article of any one of claims 13-16, wherein a ratio of the first thickness to the sum of the first and second thicknesses is at least 0.7. The article of any one of claims 13-16, wherein the first thickness is at least 3.3 mm and the second thickness is 0.7 mm or less. The article of any one of claims 13-16, wherein the visible light transmittance through the article measured according to ISO 13837A is at least 73%; and wherein the total solar transmittance through the article measured according to ISO 13837A Department is 90% or less. The article of any one of claims 13-16, wherein a major surface of the outer interlayer furthest from the inner interlayer and a major surface of the inner interlayer further from the outer interlayer both exhibit Optical distortion up to 200 millidiopters as measured by an optical distortion detector using a transmittance optic according to ASTM 1561. The article as described in any one of claims 13-16, wherein the intermediate layer is selected from a polyvinyl butyral (PVB), an acoustic PVB (APVB), an ionomer, a vinyl acetate ( EVA), a thermoplastic polyurethane (TPU), a polyester (PE), a polyethylene glycol terephthalate (PET), and a group consisting of combinations thereof; wherein a thickness of the middle layer is a The range is 0.5mm to 2.5mm. The article of any one of claims 13-16, wherein the outer interlayer and the inner interlayer are in a paired shape, wherein the outer interlayer comprises a first depth of curvature of at least 2 mm, wherein the inner interlayer comprises at least A second depth of curvature of 2 mm, and wherein the first depth of curvature is within 10% of the second depth of curvature. The article of any one of claims 13-16, wherein the outer interlayer comprises a depth of curvature of at least 2 mm, and wherein the inner interlayer has a stress that is cold formed to conform to the outer interlayer. The article according to any one of claims 13-16, wherein the glass of the borosilicate glass composition having the outer interlayer has a liquidus viscosity greater than or equal to 500 kpoise, and wherein the glass having the borosilicate glass composition The -200 Poise temperature of the glass of the borosilicate glass composition of the outer interlayer is less than or equal to 1725°C. The article of any one of claims 13-16, wherein the outer sandwich layer is configured to be located outside the inner sandwich layer when the article is installed in a vehicle. The article according to any one of claims 13-16, wherein the transmittance of ultraviolet light having a wavelength in a range of 300-380 nm passing through the article is 75% or less; wherein passing through the article wherein the transmittance of light in the visible spectrum is 73% or more; and wherein the total sunlight transmittance through the article is 61% or less. The article of any one of claims 13-16, wherein the borosilicate glass has a low temperature coefficient of thermal expansion greater than 3.25 ppm/°C and less than 8.7 ppm/°C.

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