JP2016108173A - Glass material and dental prosthesis - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a glass material that can be sintered at a low temperature, has small changes in thermal expansion coefficient and transparency caused by sintering, and has high acid resistance.SOLUTION: A glass material comprises a glass phase. The glass phase comprises 65.1 mass%-79.9 mass% of SiOcomponent, 4 mass%-8 mass% of AlOcomponent, 3 mass%-14.9 mass% of BOcomponent, 0.1 mass%-5 mass% of LiO component, 2 mass%-5 mass% of NaO component, and 1 mass%-4 mass% of ZnO component.SELECTED DRAWING: None

Description

  The present invention relates to a glass material and a dental prosthesis having the glass material.

  Glass materials are used, for example, as dental porcelain (see, for example, Patent Documents 1 and 2). Dental porcelain is a base material for dental prostheses such as crystallized glass and zirconia in order to reproduce the same appearance as natural teeth in a dental prosthesis or to adjust the external shape of a dental prosthesis. It is to be baked on (also called a ceramic frame or ceramic core).

Patent Document 1 discloses dental porcelain comprising glass containing silicon oxide, aluminum oxide, boron oxide, zinc oxide, sodium oxide, and lithium oxide as main components, and each of these components in the glass. The content ratio of each component is expressed in terms of% by weight relative to the total of these components when each component is converted to SiO ₂ , Al ₂ O ₃ , B ₂ O ₃ , ZnO, Na ₂ O, and Li ₂ O, respectively. SiO _2: 57-65 _{wt%, Al} 2 O 3: _{8~18 wt%, B} 2 O 3: _15~25 wt%, ZnO: 0.1 to 2 _wt%, Na 2 O: _3~7 wt% , And Li ₂ O: 2-8 wt% dental porcelain is disclosed.

Patent Document 2 discloses a dental glaze material raw material composition that is applied to the surface of a dental prosthesis base material made of crystallized glass and then fired to become a glaze material, and has a thermal expansion coefficient of 42 to 60 after firing. × 10 ⁻⁷ / ° C., SiO ₂ 66 to 73 wt%, B ₂ O ₃ 6.0 to 15.5 wt%, Al ₂ O ₃ 4.0 to 5.5 wt%, Li ₂ O 0 to 5 .5 _wt%, Na 2 _{O1.0~8.0 wt%,} K 2 _O0.2~1.1 wt%, CaO0.1~4.0 wt%, BaO0.1~5.5 wt%, ZnO0 A dental glaze material raw material composition comprising ˜20% by weight and TiO ₂ 0˜5.0% by weight is disclosed.

JP 2000-139959 A JP-A-8-157319

  The following analysis is given from the perspective of the present invention.

  An example of a method of using a glass material as dental porcelain will be described. First, a powdery glass material is dispersed in a solvent to produce a liquid glass material. Next, after the liquid material is built (applied) on the base material of the dental prosthesis, it is baked together with the base material, and the glass material is baked (sintered) on the base material. Thereby, the dental prosthesis which has porcelain on a base material is produced. The build-up and firing of the glass material may be repeated a plurality of times for one substrate.

  In the above use example of the glass material, if the temperature at which the glass material can be sintered is high, the deformation amount of the glass material and the base material becomes large, and it becomes difficult to adjust the outer shape. In addition, the substrate may be damaged by high temperatures.

  In the above use example of the glass material, those having a close thermal expansion coefficient are usually selected as the glass material and the base material. Therefore, when the thermal expansion coefficient of the glass material varies greatly by firing, the difference in the thermal expansion coefficient between the glass material and the base material becomes large, which may cause a problem.

  In the above-mentioned use examples of the glass material, the appearance of the glass material is important. Therefore, if the transparency of the glass material is changed by firing, it is difficult to adjust the appearance, and it is difficult to reproduce the appearance of natural teeth.

  In the above example of use of the glass material, the glass material is exposed in the human oral cavity. The human oral environment is acidic. Therefore, it is desired that the glass material used as dental porcelain has acid resistance.

  From the above, when a glass material is used for a dental prosthesis, it has a low sinterable temperature, a small change in thermal expansion coefficient due to firing, a small change in transparency due to firing, and high acid resistance. It is desirable. In Patent Document 1 and Patent Document 2, a glass material having these properties cannot be obtained.

According to the 1st viewpoint of this invention, the glass material containing a glass phase is provided. The glass phase is composed of 65.1 mass% to 79.9 mass% SiO ₂ component, 4 mass% to 8 mass% Al ₂ O ₃ component, 3 mass% to 14.9 mass% B ₂ O ₃ component, 0.1 wt% to 5 wt% of Li ₂ O component, Na ₂ O component of 2% to 5% by weight and containing 1 wt% to 4 wt% of ZnO component.

  According to the 2nd viewpoint of this invention, a dental prosthesis provided with a base material and the sintered compact of the glass material which concerns on the 1st viewpoint distribute | arranged on the base material is provided.

  According to the present invention, the sinterable temperature of the glass material can be lowered. In the sintered body of the glass material, it is possible to suppress a change in the coefficient of thermal expansion accompanying firing. It is possible to suppress the decrease in transparency associated with the sintering of the sintered glass material. The acid resistance of the glass material can be increased.

  It is possible to provide a dental prosthesis suitable for the oral environment while the occurrence of defects is suppressed.

  Below, the preferable form of each said viewpoint is described.

According to a preferred form of the first aspect, the glass phase is 2% by mass to 5% by mass of K ₂ O component, 0.4% by mass to 2% by mass of CaO component, and 0.3% by mass to 1% by mass. And at least one component selected from the group consisting of% CeO ₂ component.

According to the preferable form of the first aspect, the amount of dissolution with respect to the acid measured in accordance with JIST6526 for the sintered body of the glass material is 100 μg / cm ² or less.

According to a preferred form of the first aspect, the thermal expansion coefficient measured according to JIST6526 for a sintered body of glass material fired once under sintering conditions is 5 × 10 ⁻⁶ K ⁻¹ or less.

According to the preferred form of the first aspect, the first thermal expansion coefficient measured in accordance with JIST6526 for the first sintered body of the glass material fired once under the sintering conditions, and the first sintered body The difference (absolute value) from the second thermal expansion coefficient measured in accordance with JIST6526 for the second sintered body of the glass material fired three times further under the sintering conditions is 0.8 × 10 ⁻⁶ K ^{−. 1} or less.

  According to the preferable form of the first aspect, the glass material further contains at least one of a pigment, a fluorescent pigment, and an opacifying agent.

  According to a preferred embodiment of the first aspect, the glass material is a sintered body sintered at 850 ° C. or lower.

  According to a preferred form of the second aspect, the substrate is zirconia ceramic, alumina ceramic, or glass.

  According to a preferred form of the second aspect, the substrate is crystallized glass containing mica crystals.

  The glass material of the present invention will be described.

  The glass material may be a composition or a sintered body. The composition includes a particulate state, powder, a liquid (including slurry) dispersed in a solvent, a molded body, and a calcined body fired at a temperature that does not lead to sintering. The sintered body includes those obtained by sintering particles of the composition.

  The glass material can be mainly amorphous and may contain crystallized glass. The glass material includes a glass phase. The glass phase can contain the following components.

The glass material can contain a SiO ₂ component as a component constituting the glass phase. In the glass phase, the SiO ₂ component is preferably 65.1% by mass or more, more preferably 66% by mass or more, and further preferably 67% by mass or more. In the glass phase, the SiO ₂ component is preferably 79.9% by mass or less, more preferably 75% by mass or less, and further preferably 73% by mass or less.

The glass material can contain an Al ₂ O ₃ component as a component constituting the glass phase. In the glass phase, the Al ₂ O ₃ component is preferably 4% by mass or more, more preferably 5% by mass or more, and further preferably 6% by mass or more. In the glass phase, the Al ₂ O ₃ component is preferably 8% by mass or less, more preferably 7.8% by mass or less, and further preferably 7.6% by mass or less.

The glass material can contain a B ₂ O ₃ component as a component constituting the glass phase. In the glass phase, the B ₂ O ₃ component is preferably 3% by mass or more, more preferably 6% by mass or more, and further preferably 9% by mass or more. In the glass phase, the B ₂ O ₃ component is preferably 14.9% by mass or less, more preferably 14.7% by mass or less, and even more preferably 14.4% by mass or less.

The glass material can contain a Li ₂ O component as a component constituting the glass phase. In the glass phase, the Li ₂ O component is preferably 0.1% by mass or more, more preferably 1% by mass or more, and further preferably 1.9% by mass or more. In the glass phase, the Li ₂ O component is preferably 5% by mass or less, more preferably 4.5% by mass or less, and further preferably 4.1% by mass or less.

The glass material can contain a Na ₂ O component as a component constituting the glass phase. In the glass phase, the Na ₂ O component is preferably 2% by mass or more, more preferably 2.1% by mass or more, and further preferably 2.2% by mass or more. In the glass phase, the Na ₂ O component is preferably 5% by mass or less, more preferably 4.4% by mass or less, and even more preferably 4.1% by mass or less.

The glass material can contain a K ₂ O component as a component constituting the glass phase. In the glass phase, the K ₂ O component can be 0% by mass or more, more preferably 2% by mass or more, and further preferably 3% by mass or more. In the glass phase, the K ₂ O component is preferably 5% by mass or less, more preferably 4.8% by mass or less, and further preferably 4.6% by mass or less.

  The glass material can contain a CaO component as a component constituting the glass phase. In the glass phase, the CaO component can be 0% by mass or more, more preferably 0.4% by mass or more, and further preferably 0.5% by mass or more. In the glass phase, the CaO component is preferably 2% by mass or less, more preferably 1.8% by mass or less, and further preferably 1.5% by mass or less.

  The glass material can contain a ZnO component as a component constituting the glass phase. In the glass phase, the ZnO component is preferably 1% by mass or more, more preferably 1.2% by mass or more, and further preferably 1.3% by mass or more. In the glass phase, the ZnO component is preferably 4% by mass or less, more preferably 3.5% by mass or less, and further preferably 3% by mass or less.

The glass material can contain a CeO ₂ component as a component constituting the glass phase. In the glass phase, the CeO ₂ component can be 0% by mass or more, more preferably 0.3% by mass or more, and further preferably 0.4% by mass or more. In the glass phase, the CeO ₂ component is preferably 1% by mass or less, more preferably 0.7% by mass or less, and further preferably 0.5% by mass or less.

The glass phase is selected from the group consisting of SiO ₂ component, Al ₂ O ₃ component, Li ₂ O component, Na ₂ O component, K ₂ O component, CaO component, ZnO component, B ₂ O ₃ component and CeO ₂ component. At least one component.

The glass phase preferably contains a SiO ₂ component, an Al ₂ O ₃ component, a B ₂ O ₃ component, a Li ₂ O component, a Na ₂ O component, and a ZnO component. The glass phase may further contain at least one component selected from the group consisting of a K ₂ O component, a CaO component, and a CeO ₂ component.

In the first combination example, the glass phase can include a SiO ₂ component, an Al ₂ O ₃ component, a B ₂ O ₃ component, a Li ₂ O component, a Na ₂ O component, and a ZnO component. In the second combination example, the glass phase is composed of SiO ₂ component, Al ₂ O ₃ component, B ₂ O ₃ component, Li ₂ O component, Na ₂ O component, K ₂ O component, CaO component, ZnO component and CeO. _Two components can be included. In the third combination example, the glass phase is composed of SiO ₂ component, Al ₂ O ₃ component, B ₂ O ₃ component, Li ₂ O component, Na ₂ O component, K ₂ O component, CaO component, and ZnO component. Can be included. In the fourth combination example, the glass phase includes a SiO ₂ component, an Al ₂ O ₃ component, a B ₂ O ₃ component, a Li ₂ O component, a Na ₂ O component, a CaO component, a ZnO component, and a CeO ₂ component. be able to. In the fifth combination example, the glass phase is composed of SiO ₂ component, Al ₂ O ₃ component, B ₂ O ₃ component, Li ₂ O component, Na ₂ O component, K ₂ O component, ZnO component, and CeO ₂ component. Can be included.

  The glass material can contain components other than the above components constituting the glass phase within a range that does not affect the properties thereof.

The glass material can also contain at least one of a pigment (colorant), a fluorescent pigment (fluorescent material), and an opaque agent (opacifier). The pigment can be added to such an extent that it does not affect the composition. At least one of the pigment, the fluorescent pigment, and the opacifying agent (opacifier) may not constitute the glass phase. Examples of the pigment or fluorescent pigment include P, Ti, V, Cr, Mn, Fe, Co, Ni, Zn, Y, Zr, Sn, Sb, Bi, Ce, Pr, Sm, Eu, Gd, Tb, and Er. An oxide of at least one element selected from the group can be used. As the opacifying agent, for example, at least one compound selected from the group of TiO ₂ , ZrO ₂ , ZrSiO ₄ , SnO ₂ and CeO ₂ can be used. The pigment, fluorescent pigment, and opacifying agent added to the glass material may be one compound or a plurality of compounds. In the glass material, the content of at least one of a pigment, a fluorescent pigment, and an opacifying agent (opacifier) can be, for example, 20% by mass or less.

In the composition of the glass material, the content of the SiO ₂ component, Al ₂ O ₃ component, Na ₂ O component, K ₂ O component, and CaO component can be measured by, for example, fluorescent X-ray analysis. Content of li 2 _O component, for example, can be measured by atomic absorption spectroscopy. The content rates of the B ₂ O ₃ component, the ZnO component, and the CeO ₂ component can be measured by, for example, inductively coupled plasma (ICP) emission spectroscopic analysis. Or the composition computed from the compounding ratio in the raw material of each component which comprises glass material can be considered as composition of glass material. This is because the composition of the glass material and the composition of the raw material can be regarded as substantially the same.

  The composition of the glass material (content ratio of each component) can be derived by composition analysis of the composition or the sintered body. The composition of the glass material can also be derived from an oxide-converted composition based on the raw material of the glass material (oxide and a compound that generates an oxide).

  The sinterable temperature of the composition of the glass material is preferably less than 860 ° C., more preferably 850 ° C. or less, more preferably 840 ° C. or less, and further preferably 800 ° C. or less. Thereby, for example, when the glass material is used as a dental adjustment material and sintered on the base material, the base material can be prevented from being damaged. Moreover, the deformation amount of a glass material and a base material can be suppressed. The composition of the glass material can be sintered at a firing temperature of 740 ° C. or higher, for example.

  When the glass material of the present invention is used as an adjustment material for other materials (base materials), the glass material preferably has a thermal expansion coefficient in a range close to the thermal expansion coefficient of the base material. The thermal expansion coefficient of the sintered body of the glass material is preferably measured in a temperature range of 25 ° C. to 500 ° C. according to JIST6526 (2012). In the present specification, the thermal expansion coefficient of a sintered body that has not been fired other than firing for sintering (that is, a sample piece fired once under sintering conditions) is referred to as a “first thermal expansion coefficient”. Called. In addition, re-firing (blank firing) in which a sintered body that has been fired only during sintering (a sample piece fired once) is further fired under the same firing conditions as during sintering and then cooled to room temperature. The thermal expansion coefficient of a sintered body that has been subjected to the process three times (that is, a sample piece that has been fired four times under the sintering conditions) is referred to as a “second thermal expansion coefficient”. The second thermal expansion coefficient is preferably measured by using a sample piece obtained by further firing the sample piece whose first thermal expansion coefficient was measured under sintering conditions three times.

The first thermal expansion coefficient of the sintered body of the glass material of the present invention, for example, preferable to be 6 × ¹⁰ -6 ^{K -1} or less, more preferably 5 × ¹⁰ -6 ^{K -1} or less. Further, the first thermal expansion coefficient of the sintered body of the glass material is preferably 3 × 10 ⁻⁶ K ⁻¹ or more. Thereby, even if the composition of glass material is applied to a base material and fired, the occurrence of defects can be suppressed.

The second thermal expansion coefficient of the sintered body of the glass material of the present invention is preferably 7 × 10 ⁻⁶ K ⁻¹ or less, more preferably 6 × 10 ⁻⁶ K ⁻¹ or less, and 5 × 10 ^−5. More preferably, it is ⁶ K ⁻¹ or less. Thereby, when using the glass material of this invention for a dental prosthesis, even if baking is repeated in multiple times, generation | occurrence | production of a defect can be suppressed.

Further, in order to suppress the occurrence of problems due to the difference in the thermal expansion coefficient between the glass material and the substrate, it is preferable that the variation in the thermal expansion coefficient is small even if the sintered body of the glass material is fired a plurality of times. Therefore, it is preferable that the difference between the second thermal expansion coefficient and the first thermal expansion coefficient is smaller. The absolute value of the difference between the second thermal expansion coefficient and the first thermal expansion coefficient is preferably 0.8 × 10 ⁻⁶ K ⁻¹ or less, more preferably 0.6 × 10 ⁻⁶ K ⁻¹ or less. 0.5 × 10 ⁻⁶ K ⁻¹ or less, more preferably 0.3 × 10 ⁻⁶ K ⁻¹ or less, and further preferably 0.2 × 10 ⁻⁶ K ⁻¹ or less. preferable.

Dissolution amount to acid of sintered glass material, preferable to be 100 [mu] g / cm ² or less, preferable to be 50 [mu] g / cm ² or less and further preferably 20 [mu] g / cm ² or less. For example, when using a glass material as a dental prosthesis, it is for suppressing the loss of the glass material in an intraoral area. The amount of acid dissolved is preferably measured according to JIST6526 (2012).

  It is preferable that the transparency (translucency) of the sintered body of the glass material is small in change (for example, reduction) due to firing. For example, even if a sintered body of a transparent glass material is fired a plurality of times (for example, 4 times including firing at the time of sintering), it is preferable that the sintered body does not cause white turbidity.

  The dental prosthesis of the present invention will be described.

  A dental prosthesis includes a base material and the glass material disposed on the base material. The glass material on the substrate can be a sintered body. The glass material may be a laminate of a plurality of layers having different compositions. As the substrate, for example, zirconia ceramics, alumina ceramics, glass and the like can be used. The glass of the substrate can include crystallized glass and may be amorphous. The glass of the base material can contain, for example, mica crystals.

  Generation | occurrence | production of a defect can be suppressed by using the said glass material for a dental prosthesis. Moreover, a dental prosthesis suitable for the oral environment can be produced.

  Next, an example of a manufacturing method of a glass material and a dental prosthesis will be described.

  First, the compound which produces | generates each component which comprises the glass phase of the target glass material is prepared. As the said compound, the oxide which comprises a glass phase, or the compound which produces | generates the said oxide can be used, for example. Next, each compound is dried and then weighed according to the composition. Next, each compound is mixed. Next, for example, the mixture is melted and then cooled to produce a cullet. Next, after pulverizing the cullet, the cullet is sieved to become particles having a predetermined particle size range. Thereby, the composition of glass material can be obtained.

  When adjusting the color, fluorescence, transmittance, etc. of the glass material, at least one of a pigment, a fluorescent pigment, and an opaque agent can be added to the composition of the glass material and mixed.

  Next, the composition of the glass material is mixed and slurried in a solvent such as alcohol or purified water, and if necessary, formed into a predetermined shape and size. When manufacturing a dental prosthesis, a composition of a glass material is formed on a substrate. Next, after the molded body is dried, the molded body is heated to sinter the composition of the glass material to obtain a sintered body of the glass material. The sintering temperature can be, for example, 740 ° C. or more and less than 860 ° C.

A glass material composition and a sintered body were prepared, and the sintered body was subjected to measurement of a coefficient of thermal expansion and an acid resistance test. Comparative Examples 3 and 4 are test examples in which reproduction of the compositions of Examples 1 and 2 described in Patent Document 1 was attempted. Comparative Examples 5 and 6 are test examples described in Patent Document 2 in which the thermal expansion coefficients of 4.2 × 10 ⁻⁶ / K and 5.0 × 10 ⁻⁶ / K are attempted to be reproduced. (The compositional unit in Patent Document 2 was interpreted as mass%).

  First, the compound for producing | generating each component which comprises a glass phase was heated and dried at 120 degreeC. Next, each compound was weighed so that the composition of the oxide in the glass phase was as shown in Tables 1 and 2, and mixed using a ball mill. Table 1 shows the compositions of Examples 1-9. Table 2 shows the compositions of Comparative Examples 1-6. The compositions shown in Table 1 and Table 2 are compositions converted into oxides of the constituent elements of the glass phase based on the blending ratio of the raw material compounds. The unit of Table 1 and Table 2 is mass%.

  Next, the mixture was filled in a melting crucible and melted at 1500 ° C. in the atmosphere. After cooling the melt, it was culleted, and the cullet was further pulverized using a ball mill. Next, the pulverized product was passed through a # 200 mesh sieve and sieved. Thereby, the composition (powder) of the glass material was produced.

  Next, the composition (powder) of the glass material was mixed with purified water and slurried, and then molded into sample pieces for measuring various physical properties. After the molded body was dried, it was heated at the sintering temperature shown in Table 3 for 1 minute to produce a sintered body of glass material. The sintering temperature shown in Table 3 is an appropriate sintering temperature at which the powder of the glass material composition reaches sintering. The proper sintering temperature is a state in which the surface of the fired body is slightly glossy (that is, a state that has resulted in sintering), and a state in which the shape before firing is maintained (that is, deformation occurs due to excessive firing). This is the temperature at which (not) is obtained.

  The composition analysis was performed about the obtained sintered compact. As a result, it was confirmed that the analysis results matched the composition based on the raw materials shown in Table 1. That is, it was confirmed that the compositions shown in Tables 1 and 2 can be equated with the composition of the glass material and the composition of the sintered body.

  About the obtained sintered compact of the glass material, the above-mentioned first thermal expansion coefficient and second thermal expansion coefficient were measured according to JIST6526 (2012) (temperature range 25 ° C. to 500 ° C.). Further, the amount dissolved in acid was measured according to JIST6526 (2012). Furthermore, the change in the transparency of the sintered body due to multiple firings was observed by comparing the sample piece for measuring the first thermal expansion coefficient with the sample piece for measuring the second thermal expansion coefficient. The results are shown in Table 3.

Range of each component in Examples 1 to 9 in Table 1, SiO ₂ component 65.3 wt% ～79.5 wt%, _Al 2 _{O 3} component 4.7 wt% to 8.0 _{wt%, B} 2 O ₃ components 3.4 mass% to 14.4 mass%, Li ₂ O component 0.9% to 4.1%, Na ₂ O component 2.2% to 4.5 mass%, K ₂ O component 0 mass% to 4.6 mass%, CaO component 0 wt% to 1.5 wt%, ZnO ingredient 1.0 wt% to 2.7 wt%, and was CeO ₂ component 0 wt% to 0.7 wt%.

  In Examples 1 to 9, the proper sintering temperature was 850 ° C. or lower. On the other hand, in Comparative Examples 1 and 2, the proper sintering temperature was 860 ° C. or higher. The proper sintering temperature in Examples 1 to 9 could be lowered as well as the proper sintering temperature in Comparative Examples 1 and 2. When a glass material is applied to a dental prosthesis, the composition of the glass material is sintered on a substrate such as a mica-based ceramic material. If the proper sintering temperature is high, there is a high possibility that problems such as damage to the substrate will occur. Therefore, it turns out that the glass material of this invention is applicable suitably for a dental prosthesis, for example.

In Examples 1-9, about the sintered compact of the glass material, the dissolution amount with respect to an acid was 50 microgram / cm < ² > or less. On the other hand, in Comparative Examples 3, 5 and 6, the amount dissolved in the acid was 100 μg / cm ² or more. The acid resistance in Examples 1-9 could be higher than the acid resistance in Comparative Examples 3, 5, and 6. Since the human oral environment is acidic, it can be seen that the glass material of the present invention can be suitably applied to a dental prosthesis.

In Examples 1 to 9, the difference between the first thermal expansion coefficient and the second thermal expansion coefficient was 0.3 × 10 ⁻⁶ K ⁻¹ or less. On the other hand, in Comparative Examples 1 and 3, the difference was 0.9 × 10 ⁻⁶ K ⁻¹ or more. In Examples 1-9, the change of the thermal expansion coefficient by baking could be made smaller than Comparative Examples 1 and 3. When a glass material is applied to a dental prosthesis, if the change in the thermal expansion coefficient is large, damage may occur due to the difference in the thermal expansion between the substrate and the glass material. Therefore, it turns out that the glass material of this invention is applicable suitably for a dental prosthesis, for example.

  In Examples 1 to 9, a decrease in transparency of the sintered body was not observed even after a total of four firings. On the other hand, in Comparative Examples 3, 4, and 6, white turbidity was generated in the sintered body by refiring, and a decrease in transparency was observed. When applying a glass material to a dental prosthesis, if the transparency of the glass material changes depending on the number of firings, it becomes difficult to reproduce the appearance of natural teeth. Therefore, it turns out that the glass material of this invention is applicable suitably for a dental prosthesis, for example.

  As mentioned above, in Examples 1-9, low sintering temperature, high acid resistance, suppression of the change of a thermal expansion coefficient, and suppression of the fall of transparency were able to be implement | achieved. On the other hand, in Comparative Examples 1-6, the sintered compact which implement | achieves all these was not able to be obtained. Therefore, it can be seen that a suitable dental prosthesis can be produced by using the glass material of the present invention.

  Each disclosure of the above patent document is incorporated herein by reference. The glass material and dental prosthesis of the present invention have been described based on the above embodiment, but are not limited to the above embodiment, and are within the scope of the entire disclosure of the present invention and the basic of the present invention. Various modifications, changes, and improvements may be included in various disclosed elements (including each element of each claim, each element of each embodiment or example, each element of each drawing, etc.) based on the technical idea. Needless to say, it can be done. Various combinations and replacements of various disclosed elements (including each element of each claim, each element of each embodiment or example, each element of each drawing, etc.) within the scope of the entire disclosure of the present invention. Selection is possible.

  Further problems, objects, and developments of the present invention will become apparent from the entire disclosure of the present invention including the claims.

  Regarding numerical ranges described in this document, any numerical value or small range included in the range should be construed as being specifically described even if there is no specific description.

Claims (10)

A glass material containing a glass phase,
The glass phase is
SiO ₂ component of 65.1 wt% ～79.9 wt%,
4% by mass to 8% by mass of Al ₂ O ₃ component,
3 wt% ～14.9 wt% of _B 2 _{O 3} component,
0.1 wt% to 5 wt% of Li ₂ O component,
2% to 5 wt% of Na ₂ O component, and containing 1 wt% to 4 wt% of ZnO component, a glass material. Select the glass phase, 2% to 5 wt% of _{K 2} O component, 0.4 mass% to 2 mass% of CaO component, and from the group consisting of 0.3 wt% to 1 wt% of CeO ₂ component The glass material according to claim 1, further comprising at least one component. The glass material according to claim 1 or 2, wherein the sintered body of the glass material has a dissolution amount with respect to an acid measured according to JIST6526 of 100 µg / cm ² or less. The thermal expansion coefficient measured based on JIST6526 about the sintered body of the said glass material baked once on sintering conditions is 5 * 10 < ^-6 > K < ^-1 > or less, As described in any one of Claims 1-3. The glass material described. The first thermal expansion coefficient measured according to JIST6526 for the first sintered body of the glass material fired once under the sintering conditions, and the first sintered body further three times under the sintering conditions. The difference (absolute value) from the second thermal expansion coefficient measured in accordance with JIST6526 for the second sintered body of the fired glass material is 0.8 × 10 ⁻⁶ K ⁻¹ or less. Glass material as described in any one of 1-4.   The glass material according to any one of claims 1 to 5, further comprising at least one of a pigment, a fluorescent pigment, and an opacifying agent.   The glass material according to any one of claims 1 to 6, which is a sintered body sintered at 850 ° C or lower. A substrate;
The sintered body of the glass material according to any one of claims 1 to 7, which is disposed on the base material,
A dental prosthesis comprising:   The dental prosthesis according to claim 8, wherein the base material is zirconia ceramic, alumina ceramic, or glass.   The dental prosthesis according to claim 8, wherein the base material is crystallized glass containing mica crystals.