DE60207007T2 - Coated cemented carbide cutting tool - Google Patents

Description

BACKGROUND THE INVENTION

Territory of invention

The The present invention relates to a scissoring tool which comprises a surface-coated carbide alloy (hereinafter referred to as a coated cemented carbide tool designated), which neither a detachment nor a chipping (micro-chipping) in a wear-resistant Coating layer causes when different types of steel and cast iron intermittently cut under deep cutting conditions be as under a thick cutting depth and a high feed, where high mechanical and thermal effects are used, because the wear resistant Coating layer a superior adhesion on the surface a tungsten carbide based carbide alloy substrate (hereinafter as a cemented carbide substrate) and also a superior one wear resistance across from Has chipping, which gives them excellent resistance over a long period shows.

description of the related department

In general, cutting tools include, for example, a disposable insert removably attached to the tip portion of a drilling tool when cutting and planing workpieces, such as those of various types of steel and cast iron, drills and miniature drills used in drilling the workpiece materials, and solid-type face milling cutters or shank cutters used in long milling, fluting and chamfering or folding of workpieces. There is also known a disposable face milling tool which is used for cutting in the same manner as in the case of the solid type end mill after the disposable insert has been detachably mounted. The JP 58 107 482 discloses a cutting tool coated with an anionic vapor deposited layer of amorphous metal.

It For example, a coated cemented carbide tool is known which can be deposited by deposition on the surface a cemented carbide substrate of a wear resistant coating layer, which consists of one layer or a plurality of two or more Layers, including a layer of carbide of Ti (hereinafter as TiC), a nitride layer of Ti (hereinafter TiN), a layer of carbonitride of Ti (hereinafter as TiCN), a layer of carboxy of Ti (hereinafter TiCO) and a layer of carbon dioxide of Ti (in Hereinafter referred to as TiCNO), and has an average thickness from 1 to 15 μm has, using a conventional chemical deposition device is produced. It is too It is well known that this coated cemented carbide tool for continuous cutting and discontinuous cutting various types of steel and cast iron can be used.

There is also known a coated cemented carbide tool made by depositing on the surface of the cemented carbide substrate a wear resistant coating layer composed of: (a) a lower coating layer consisting of one or a plurality of layers including one A layer of carbide of Ti (hereinafter referred to as TiC), a layer of nitride of Ti (hereinafter referred to as TiN), a layer of carbonitride of Ti (hereinafter referred to as TiCN), a layer of carboxy of Ti (hereinafter TiCO) and a layer of carbon dioxide of Ti (hereinafter referred to as TiCNO) and having an average thickness of 0.5 to 15 μm, which is deposited using a conventional chemical deposition apparatus; and (b) an upper coating layer consisting of either one or both of an alumina (hereinafter referred to as Al ₂ O ₃ ) layer and an Al ₂ O ₃ -ZrO ₂ mixed layer consisting of a matrix of Al ₂ O. ₃ and a zirconia (hereinafter referred to as ZrO ₂ ) phase dispersed therein (hereinafter referred to as Al ₂ O ₃ -ZrO ₂ mixed layer) dispersed therein and distributed in Japanese Patent Application, First Publication Nos. Sho 57-39168 and Japanese Patent Application, First Publication No. Sho 61-201778, and has an average thickness of 0.5 to 15 microns, which is deposited using the same conventional chemical deposition apparatus. It is also known that this coated cemented carbide tool can be used in continuous cutting and discontinuous cutting of various types of steel and cast iron.

It is also known that a coated cemented carbide tool is made by depositing on the surface of a cemented carbide substrate of a wear resistant coating layer, which consists of a single-layer or multi-layer hard surface layer of either one or both of a composite nitride layer of Ti and Al (hereinafter referred to as a (Ti, Al) N layer) and a composite carbonitride layer of Ti and Al (hereinafter referred to as a (Ti, Al) CN layer) each having the following compositional formula: (Ti _1-x Al _x ) N and the compositional formula: (Ti _1-x Al _x ) C _{1 -y} N _y satisfy (where X is 0.15 to 0.65 and Y is 0.5 to 0.99 in terms of atomic ratio), and has an average thickness of 0.5 to 15 microns, as in Japanese Patent Application, First Publication no. Sho 62-56565, using an arc ion plating apparatus as a kind of physical deposition apparatus, which is a schematic explanatory drawing view of FIG 1 is shown under the conditions that an arc discharge between an anode electrode and a cathode electrode (vapor source) is generated, in which a Ti-Al alloy having a predetermined composition is introduced under the conditions of a voltage of 35 V and a current of 90 A in the state in which the atmosphere of the apparatus is evacuated to 0.5 Pa and heated to a temperature of 500 ° C by means of a heater and at the same time a nitrogen gas and / or a methane gas are introduced into the apparatus as a reactive gas, and a grid bias of -200 V is applied to the cemented carbide substrate.

There is also known a coated cemented carbide tool made by physical deposition on the surface of a cemented carbide substrate of a single-layer or multi-layer hard bottom layer of a wear resistant coating layer made of either one or both of a composite nitride layer of Ti and Al (in U.S.P. Hereafter referred to as a (Ti, Al) N layer) and a composite carbonitride layer of Ti and Al (hereinafter referred to as a (Ti, Al) CN layer) each having the following composition formula: (Ti _{1 -x} Al _x ) N and the composition formula: (Ti _1-x Al _x ) C _{1 -y} N _y (where X is 0.15 to 0.65 and Y is 0.5 to 0.99, in terms of atomic ratio) , and an average thickness of 0.5 to 15 microns, as in Japanese Patent Application, First Publication no. Sho 62-56565, using an arc ion plating apparatus as a kind of physical deposition apparatus, which is a schematic explanatory drawing view of FIG 1 is shown under the conditions that the arc discharge between an anode electrode and a cathode electrode (vapor source) is generated, in which a Ti-Al alloy is introduced with a predetermined composition under the conditions of a voltage of 35 V and a current of 90 A in the state in which the atmosphere of the apparatus is evacuated to 0.5 Pa and heated to a temperature of 500 ° C by means of a heater and at the same time a nitrogen gas and / or a methane gas are introduced into the apparatus as a reactive gas, and a grid bias voltage of -200 V is applied to the cemented carbide substrate and further chemically deposited thereon an upper cladding layer consisting of either one or both of an alumina (hereinafter referred to as Al ₂ O ₃ ) layer and an Al ₂ O ₃ ZrO ₂ mixed layer of a matrix of Al ₂ O ₃ and a zirconium oxide dispersed therein (hereinafter a ZrO ₂ ) phase (hereinafter referred to as an Al ₂ O ₃ -ZrO ₂ mixed layer), which is disclosed in Japanese Patent Application, First Publication no. Sho 57-39168 and Japanese Patent Application, First Publication No. Sho 61-201778, and having an average thickness of 0.5 to 10 μm using a conventional chemical deposition apparatus. It is also known that this coated cemented carbide tool can be used in continuous cutting and discontinuous cutting of various types of steel and cast iron.

recently High performance cutting devices made remarkable progress. With an increase in the strong demands of labor savings and energy saving as well as the cost reduction to the cutting operation Cutting tools tend to have the adaptability require that this hardly be affected by the cutting conditions and as little as possible being affected. If a conventional coated cemented carbide tool during continuous cutting and discontinuous cutting of steel and cast iron underneath normal conditions is used, no problems arise. If however, a cutting operation using a face mill or a drill, the cutting edge of a discontinuous cutting is exposed, and a discontinuous cutting operation (im Following as "discontinuous Cutting ") using a disposable insert under deep cutting conditions, how to perform a thick cutting depth and a high load, dissolves the hard surface layer slightly off the surface of the cemented carbide substrate due to high mechanical and thermal Actions that during cutting produced. Because the primary layer and the hard surface layer are very hard, it is easy to chipping in the cutting edge area in discontinuous cutting under deep cutting conditions, accompanied by high mechanical and thermal effects be, and there will be a failure within a relatively short time Time.

SUMMARY THE INVENTION

Around the above-mentioned problems according to the present invention To solve the invention were the following cutting tools made of a surface-coated Carbide alloy consisting of a wear-resistant coating layer have developed.

The from a surface-coated Carbide alloy existing cutting tool in the first aspect of The present invention includes a carbide alloy substrate Tungsten carbide base with an amorphous layer formed by an arc ion plating surface treatment formed at a mean depth of 1 to 50 nm from the surface becomes; and a wear-resistant Coating layer chemically and / or physically on the surface of the tungsten carbide based carbide alloy substrate being, being the wear resistant Coating layer of one layer or a plurality of two or more layers, including a layer of carbide of Ti, a layer of nitride of Ti, a layer of carbonitride of Ti, a layer of carboxy of Ti and a layer of carbonic oxide of Ti, and has an average thickness of 1 to 15 microns, and the wear-resistant Coating layer has excellent adhesion.

at the surface-coated Cemented carbide tool of this embodiment it comes because the surface area of the cemented carbide substrate formed a strong amorphous layer adhesion between the surface the cemented carbide substrate and the wear resistant coating layer ensures no detachment by bad adhesion at the wear resistant Coating layer during the discontinuous cutting operation under deep cutting conditions of steel and cast iron, accompanied by drastically high thermal and mechanical actions, and the wear resistant coating layer has excellent wear resistance. In contrast comes it in the conventional Coated cemented carbide tool to peel off due to poor adhesion of wear resistant Coating layer during of the batch cutting operation among those described above Deep cutting conditions, and it is obvious that it is within comes to a failure in a relatively short time.

As As described above, the coated cemented carbide tool has this Invention excellent adhesion the wear-resistant Coating layer on the surface of the cemented carbide substrate and also shows excellent cutting performance over a long period, even when used in discontinuous cutting operation under deep cutting conditions, by particularly high mechanical and thermal effects are accompanied, not to mention the Use in continuous cutting operation and discontinuous Cutting operation of various types of steel and cast iron under normal Conditions, making it possible will satisfactorily match the variability of the cutting operation getting ready and saving more labor and energy and to reduce costs in the cutting operation.

The surface-coated carbide alloy cutting tool in the second aspect of the present invention comprises a tungsten carbide-based cemented carbide substrate having an amorphous layer formed from the surface by an arc ion plating surface treatment at an average depth of 1 to 50 nm; and a monolayer or multilayer hardcoat layer physically deposited on the surface of the tungsten carbide-based cemented carbide substrate, the monolayer or multilayer hardcoat layer comprising either one or both of a composite nitride layer of Ti and Al and a composite carbonitride layer. Layer of Ti and Al each satisfying the compositional formula: (Ti _1-x Al _x ) N and the composition formula: (Ti _1-x Al _x ) C _{1 -y} N _y (wherein X is 0.15 to 0.65 and Y is 0.5 to 0.99 in terms of atomic ratio), and has an average thickness of 0.5 to 15 μm, and the hard coat layer shows excellent wear resistance.

The from a surface-coated Carbide alloy existing cutting tool of the second embodiment showed excellent cutting performance over a long period of time itself when used in discontinuous cutting operation under Deep cutting conditions, high mechanical and thermal Actions similar as in the first embodiment are accompanied, because the wear-resistant coating an excellent adhesion on the surface of the cemented carbide substrate.

The surface-coated carbide alloy cutting tool in the third aspect of the present invention comprises a tungsten carbide-based cemented carbide substrate having an amorphous one A layer formed by an arc ion plating surface treatment at an average depth of 1 to 50 nm from the surface; and a wear-resistant coating layer physically deposited on the surface of the tungsten carbide-based cemented carbide substrate, wherein the wear-resistant coating layer is composed of: (a) a lower coating layer consisting of one or more of two or more layers including a layer Carbide of Ti, a layer of nitride of Ti, a layer of carbonitride of Ti, a layer of carboxy of Ti and a layer of carbonitroxide of Ti, and an average thickness of 0.5 to 15 μm; and (b) an upper coating layer consisting of either one or both of an alumina layer and an alumina-zirconia mixed layer consisting of a matrix of alumina and a zirconia phase dispersed and dispersed therein, and having an average thickness of from 0.5 to 15 microns has.

The coated cemented carbide tool of this embodiment shows excellent Cutting power over a long period of time, because the wear-resistant coating layer an excellent adhesion even when used in discontinuous cutting operation under Deep cutting conditions shows that of particularly high mechanical and thermal effects are accompanied, not to mention the use in continuous cutting operation and discontinuous cutting operation various types of steel and cast iron under normal conditions, making it possible will satisfactorily match the variability of the cutting operation getting ready and saving more labor and energy and to reduce costs in the cutting operation.

The surface-coated carbide alloy cutting tool in the fourth aspect of the present invention was formed by depositing the following layers (a) and (b) on the surface of a tungsten carbide-based cemented carbide substrate having an amorphous layer by an arc ion plating surface treatment at a mean depth of 1 to 50 nm is formed from the surface by physical deposition. These coating layers each consist of: (a) a tough primary layer consisting of a titanium nitride layer and having an average thickness of 0.1 to 5 μm; and (b) a monolayer or multilayer hard surface layer consisting of either one or both of a composite nitride layer of Ti and Al and a composite carbonitride layer of Ti and Al, each having the composition formula: (Ti _{1- x} Al _x ) N and the composition formula: (Ti _1-x Al _x ) C _1-y N _y (where X is 0.15 to 0.65 and Y is 0.5 to 0.99 in terms of atomic ratio) and has an average thickness of 0.5 to 15 μm, and the wear-resistant coating layer exhibits excellent adhesion. Since the thus obtained carbide alloy cutting tool has excellent adhesion of the surface coating layer to the substrate and also excellent in chipping resistance, this cutting tool made of a surface-coated carbide alloy exhibits excellent performance.

The coated cemented carbide tool of this embodiment has an excellent Adhesion of the wear resistant Coating layer on the surface of the cemented carbide substrate and also shows excellent cutting performance over a long period, even when used in discontinuous cutting operation under deep cutting conditions, by particularly high mechanical and thermal effects are accompanied, not to mention the Use in continuous cutting operation and discontinuous Cutting operation of various types of steel and cast iron below normal conditions, which makes it possible in more satisfactory Way with the variability the cutting operation and another labor saving and to save energy and reduce costs in cutting operations.

The surface-coated carbide alloy cutting tool in the fifth aspect of the present invention comprises a tungsten carbide-based carbide alloy substrate having an amorphous layer formed by arc ion plating surface treatment at an average depth of 1 to 50 nm from the surface; and a wear-resistant coating layer physically and / or chemically deposited on the surface of the tungsten carbide-based carbide alloy substrate, the wear-resistant coating layer being composed of: (a) a tough primary layer consisting of a titanium nitride layer and having an average thickness of 0.1 to 5 μm; and (b) a monolayer or multilayer hard bottom layer consisting of either one or both of a composite nitride layer of Ti and Al and a composite carbonitride layer of Ti and Al, each of which has the composition: (Ti _1-x Al _x ) N and the composition formula: (Ti _1-x Al _x ) C _{1 -y} N _y (where X is 0.15 to 0.65 and Y is 0.5 to 0.99, as the atomic ratio ), and has an average thickness of 0.5 to 15 μm; and (c) a single-layer or multi-layer hard top layer comprising either one or both of an alumina layer and an alumina-zirconia mixed layer consisting of a matrix of alumina and a zirconia phase dispersed and dispersed therein is prepared, and has an average thickness of 0.5 to 10 microns, and the wear-resistant coating layer has excellent adhesion and resistance to chipping.

at the coated cemented carbide tool of this embodiment it comes because the surface area of the cemented carbide substrate formed a strong amorphous layer adhesion between the surface the cemented carbide substrate and the wear resistant coating layer ensures no detachment by bad adhesion at the wear resistant Coating layer during discontinuous cutting operation under deep cutting conditions of steel and cast iron, accompanied by extremely high thermal and mechanical actions, and the wear resistant coating layer has excellent wear resistance. In contrast comes it in the conventional Coated cemented carbide tool to peel off due to poor adhesion of wear resistant Coating layer during of the batch cutting operation among those described above Deep cutting conditions, and it is obvious that it is within comes to a failure in a relatively short time.

As As described above, the coated cemented carbide tool has the present invention excellent adhesion of the wear-resistant coating layer on the surface of the cemented carbide substrate, and also has an excellent Cutting power over a long period of time, even when used in discontinuous Cutting operation under deep cutting conditions, particularly high mechanical and thermal effects are not to mention the use in continuous cutting and discontinuous Cutting operation of various types of steel and cast iron below normal conditions, where by it becomes possible in more satisfactory Way with the variability the cutting operation and another labor saving and to save energy and reduce costs in cutting operations.

SHORT DESCRIPTION THE DRAWINGS

The 1 Fig. 12 is a schematic explanatory view of an arc ion plating apparatus.

The 2A and the 2 B show a coated cemented carbide insert; the 2A is a schematic perspective view of the coated cemented carbide insert while the 2 B a schematic longitudinal sectional view of the coated cemented carbide insert shows.

The 3A and the 3B show an end mill made of a cemented carbide;

The 3A is a schematic front view of the end mill of a coated cemented carbide, while the 3B a schematic cross-sectional view of the cutting edge region is.

The 4A and the 4B show a drill made of a coated cemented carbide;

The 4A is a schematic front view of the drill bit from a coated cemented carbide, while the 4B a schematic cross-sectional view of the chip groove is.

DETAILED DESCRIPTION OF THE INVENTION

preferred embodiments of the surface-coated Carbide alloy of the present invention produced cutting tool be with reference to the attached Drawings described. The present invention is not on the following examples are limited and may, for example individual features of these embodiments be suitably used in combination.

First embodiment

• (a) Wenn das oben beschriebene Sintercarbidsubstrat in eine Lichtbogenionenplattierungsvorrichtung als eine Art physikalischer Abscheidungsvorrichtung gegeben wird, wie in einer schematischen erläuternden Ansicht von 1 gezeigt, und die Oberfläche des Sintercarbidsubstrats ohne den Einsatz einer Kathodenelektrode unter den folgenden Bedingungen einer Vorbehandlung unterworfen wird: Atmosphärentemperatur in der Vorrichtung (Temperatur des Sintercarbidsubstrats): 300 bis 500°C, atmosphärisches Gas: Ar, Atmosphärendruck: 1 bis 10 Pa, Lichtbogenentladungsstrom: (Lichtbogen-Pulver – Aus), auf das Sintercarbidsubstrat angewandter Vordruck: –800 bis –1000 V, und Behandlungszeit: 2 bis 10 min, und dann die Oberfläche des Sintercarbidsubstrats weiter einer Lichtbogenionenplattierungsoberflächenbehandlung unter Verwendung von metallischem Ti als Kathodenelektrode unter den folgenden Bedingungen unterworfen wird: Atmosphärentemperatur in der Vorrichtung: 450 bis 550°C, atmosphärisches Gas: Ar, Atmosphärendruck: 1 bis 10 Pa, Lichtbogenentladungsstrom: 100 bis 200 A, und auf das Sintercarbidsubstrat angewandter Vordruck: –900 bis –1200 V, wird eine metallische Ti-Schicht als Abscheidungsschicht nicht auf der Oberfläche des Sintercarbidsubstrats gebildet. Die Struktur der Oberfläche des Sintercarbidsubstrats selbst wird mit Hilfe eines Transmissionselektronenmikroskops betrachtet. Als ein Ergebnis wird die Bildung einer amorphen Schicht nachgewiesen.
• (b) Die Bildung der metallischen Ti-Schicht mit Hilfe der Lichtbogenionenplattierungsvorrichtung wird unter den folgenden Bedingungen durchgeführt: Atmosphärentemperatur in der Vorrichtung: 300 bis 500°C, atmosphärisches Gas: (nicht verwendet), Atmosphärendruck: Vakuum bei 0,1 Pa oder weniger, Kathodenelektrode: metallisches Ti, Lichtbogenentladungsstrom: 50 bis 100 A, und auf das Sintercarbidsubstrat angewandter Vordruck: –30 bis –100 V.
• (c) In dem Zustand, in welchem eine amorphe Schicht in einer mittleren Tiefe von 1 bis 50 nm von der Oberfläche gebildet wird, wenn eine abnutzungsbeständige Beschichtungsschicht des herkömmlichen beschichteten Sintercarbidwerkzeugs auf der Oberfläche des Sintercarbidsubstrats mit der auf der Oberfläche davon gebildeten amorphen Schicht mit Hilfe der oben beschriebenen physikalischen Abscheidungsvorrichtung oder einer herkömmlichen chemischen Abscheidungsvorrichtung gebildet wird, reagiert, da die amorphe Schicht eine hohe Aktivität und eine hohe Reaktivität aufweist, die amorphe Schicht mit der abnutzungsbeständigen Beschichtungsschicht bei deren Bildung mit Abscheidung, um dadurch eine bemerkenswert starke Adhäsion zwischen der Oberfläche des Sintercarbidsubstrats und der abnutzungsbeständigen Beschichtungsschicht sicherzustellen. Als ein Ergebnis ist das so erhaltene beschichtete Sintercarbidwerkzeug frei von Ablösung der abnutzungsbeständigen Beschichtungsschicht, selbst bei einer Verwendung im diskontinuierlichen Schneidebetrieb unter Tiefschneidebedingungen. Daher wird es möglich, eine hervorragende Abnutzungsbeständigkeit der abnutzungsbeständigen Beschichtungsschicht in zufrieden stellender Weise zu erhalten.

From the above-described point of view, applicants of the present invention conducted research to further improve the adhesion of the wear-resistant coating layer constituting the above-described conventional coating alloy tool to the surface of the cemented carbide substrate. As a result, the following statement was made:

• (a) When the above-described cemented carbide substrate is placed in an arc ion plating apparatus as a kind of physical deposition apparatus, as in a schematic explanatory view of FIG 1 and the surface of the cemented carbide substrate without the use of cathodes Electrode is subjected to a pretreatment under the following conditions: atmosphere temperature in the apparatus (temperature of the cemented carbide substrate): 300 to 500 ° C, atmospheric gas: Ar, atmospheric pressure: 1 to 10 Pa, arc discharge current: (arc powder - off), on the Substrate applied to cemented carbide substrate: -800 to -1000 V, and treatment time: 2 to 10 minutes, and then the surface of the cemented carbide substrate is further subjected to arc ion plating surface treatment using metallic Ti as a cathode electrode under the following conditions: Atmospheric temperature in the device: 450 to 550 ° C, atmospheric gas: Ar, atmospheric pressure: 1 to 10 Pa, arc discharge current: 100 to 200 A, and pre-pressure applied to the cemented carbide substrate: -900 to -1200 V, a metallic Ti layer as a deposition layer does not become on the surface of the cemented carbide substrate educated. The structure of the surface of the cemented carbide substrate itself is observed by means of a transmission electron microscope. As a result, the formation of an amorphous layer is detected.
• (b) The formation of the metallic Ti layer by means of the arc ion plating apparatus is conducted under the following conditions: atmospheric temperature in the apparatus: 300 to 500 ° C, atmospheric gas: (not used), atmospheric pressure: vacuum at 0.1 Pa or less , Cathode electrode: metallic Ti, arc discharge current: 50 to 100 A, and applied to the cemented carbide substrate pre-pressure: -30 to -100 V.
• (c) In the state in which an amorphous layer having an average depth of 1 to 50 nm is formed by the surface when a wear resistant coating layer of the conventional coated cemented carbide tool is coated on the surface of the cemented carbide substrate with the amorphous layer formed on the surface thereof With the aid of the above-described physical deposition apparatus or a conventional chemical deposition apparatus, since the amorphous layer has high activity and high reactivity, the amorphous layer reacts with the wear-resistant coating layer as it is formed to thereby exhibit remarkably strong adhesion between the substrate To ensure surface of the cemented carbide substrate and the wear-resistant coating layer. As a result, the coated cemented carbide tool thus obtained is free from peeling off of the wear resistant coating layer even when used in the batch cutting operation under deep cutting conditions. Therefore, it becomes possible to satisfactorily obtain excellent wear resistance of the wear-resistant coating layer.

These embodiment was accomplished on the basis of the above-described finding and is characterized by a coated cemented carbide tool, a wear resistant coating layer, the excellent adhesion characterized, comprising: a cemented carbide substrate with an amorphous layer formed by an arc ion plating surface treatment formed at a mean depth of 1 to 50 nm from the surface becomes; and a wear-resistant Coating layer chemically and / or physically on the surface of the tungsten carbide-based cemented carbide substrate is deposited, being the wear resistant Coating layer of one layer or a plurality of two or several layers, including a TiC layer, a TiN layer, a TiCN layer, a TiCO layer and a TiCNO layer, and has an average thickness of 1 to 15 microns.

When next will be the reason why the average thickness of the on the surface of the Sintercarbidsubstrats formed amorphous layer and the middle Thickness of the wear-resistant Coating layer as described above in the coated Carbide alloy of this invention were limited explained.

(1) Average thickness of one amorphous layer on the surface of the cemented carbide substrate

The amorphous layer has the effect of providing excellent adhesion between it and the wear-resistant coating layer as described above. However, if the depth is less than 1 nm, the desired excellent adhesion can not be ensured. At On the other hand, the effect of improving the adhesion of the wear-resistant layer to the surface of the cemented carbide substrate is satisfactory when the average depth from the surface is 50 nm. Therefore, the average depth was set to 1 to 50 nm.

(2) Average thickness of the wear resistant coating layer

A Ti compound layer, which is the wear-resistant coating layer forms, has the effect of improving the wear resistance a cutting tool. If, however, the average thickness less than 1 μm is, let yourself the desired wear resistance do not make sure. On the other hand, if the average thickness exceeds 15 μm, it comes easily to a plastic deformation, which easily a one-sided wear caused by the wear-resistant coating layer in discontinuous cutting operation under deep cutting conditions. Therefore, the average depth was set to a range of 1 to 15 μm.

The Coated cemented carbide tool of this embodiment will be detailed described.

Example 1-1

The cemented carbide substrates A1-1 to A1-6, each having the shape of a disposable insert as defined in ISO · CNMG120408, were prepared by preparing a WC powder, a (Ti, W) C (TiC / WC = 30/70 by weight ratio powder, (Ti, W) CN (TiC / TiN / WC = 24/20/56) powder, one (Ta, Nb) C (TaC / NbC = 90/10) Powder, a Cr ₃ C ₂ powder and a Co powder each having a predetermined mean grain size of 0.5 to 4 μm, compounding these raw powders according to each individual formulation in Table 1-1, wet blending them in a ball mill for 72 hours , Drying the mixture, compacting the dried mixture under a pressure of 100 MPa to form green compacts, and vacuum-sintering these unsintered moldings under conditions of a vacuum degree of 6 Pa and a temperature of 1410 ° C for 1 hour.

These cemented carbide substrates A1-1 to A1-6 were subjected to ultrasonic cleaning in acetone, dried, and then immersed in a conventional arc ion plating apparatus as shown in FIG 1 and the surface of each of the cemented carbide substrates A1-1 to A1-6 was subjected to pretreatment under the following conditions:
Atmospheric temperature (temperature of the cemented carbide substrate): 400 ° C,
atmospheric gas: Ar,
Atmospheric pressure: 3 Pa,
Cathode electrode: (not used),
Arc discharge current: (arc powder - off),
applied to the cemented carbide substrate pre-pressure: -900 V, and
Treatment time: 3 min
and this was then subjected to an arc ion plating surface treatment under the following conditions:
Atmospheric temperature in the device: 500 ° C,
atmospheric gas: Ar,
Atmospheric pressure: 3 Pa,
Cathode electrode: metallic Ti,
Arc discharge current: 150 A, and
applied to the cemented carbide substrate: -1000 V to thereby form an amorphous layer on the surface of the cemented carbide substrates A1-1 to A1-6. The depth of the amorphous layer formed on the surface thereof was adjusted by regulating the treatment time of the arc ion plating surface treatment under the conditions described above.

The Structure of the surface the sintered carbide substrates A1-1 to A1-6 formed amorphous layer was measured by means of a transmission electron microscope (magnification: 500,000), and the rating and measurement were based on the observed results. As a result, the mean depths (average depths measured at five points) from the surface each shown in Table 3.

By using a conventional chemical deposition apparatus, a wear resistant coating layer of a Ti compound layer having a target composition and a target thickness as shown in Table 1-3 on the surface of these cemented carbide substrates A1-1 to A1-6 under the conditions (1-TiCN in the Table represents the conditions for forming a TiCN layer having a crystal structure in the longitudinal direction such as in Japanese Patent Application, First Publication No. Hei 6-8010) as shown in Table 1-2, thereby constituting the disposable inserts of a surface-coated carbide alloy of this embodiment (hereinafter referred to as coated cemented carbide inserts of the present invention) 1 -1 to 1-6 as a coated cemented carbide tool of the present invention having a shape which is in a schematic perspective view of 2 (a) and a schematic longitudinal sectional view of 2 B) is shown. In addition, the cemented carbide substrates A1-2, A1-4, A1-5 and A1-6 were incorporated into a conventional arc ion plating apparatus as shown in FIG 1 and the same wear-resistant coating layer of a Ti compound layer having a target composition and a target thickness as shown in Table 1-3 was formed on the surface of the cemented carbide substrates under the following conditions:
Atmosphere temperature in the oven: 650 ° C,
atmospheric gas: nitrogen gas, methane gas or mixed gas of nitrogen gas and methane gas in a predetermined ratio,
Atmospheric pressure: 5 Pa,
Cathode electrode: metallic Ti,
Arc discharge current: 80 A, and
pre-pressure applied to the cemented carbide substrate: -200 V to thereby produce the coated cemented carbide inserts 1-7 to 1-10 having the same shape as in FIG 2 (a) and 2 B) shown to form the present invention.

To the A comparison was made, as shown in Table 1-4, one-time use a conventional one Coated cemented carbide (hereinafter referred to as conventional coated cemented carbide inserts 1-1 to 1-10 as a conventional coated cemented carbide tool each under the same conditions as described above except that the pretreatment and the arc ion plating surface treatment under the above conditions at the surface of the cemented carbide substrates A1-1 to A1-6 were not performed in the arc ion plating apparatus and therefore not the amorphous layer on the surface of the Sintercarbidsubstrate A1-1 to A1-6 was formed.

Tabelle 1-2

Tabelle 1-3

Tabelle 1-4

Tabelle 1-5

(Das Versagen wurde durch Ablösen der abnutzungsbeständigen Schicht verursacht.)Subsequently, the coated cemented carbide inserts 1-1 to 1-10 of the present invention and the conventional coated cemented carbide inserts 1-1 to 1-10 were subjected to a dry-type discontinuous thickness-cutting-depth cutting test of an alloy steel under the following conditions:
Workpiece: JIS · SCM440 rod with four longitudinal grooves equidistant from each other,
Cutting speed: 120 m / min,
Cutting depth: 5.4 mm,
Feed: 0.19 mm / rev, and
Cutting time: 5 minutes, and subjected to a dry-type discontinuous thickness-cutting-depth cutting test of a carbon steel under the following conditions:
Workpiece: JIS · S20C rod with four longitudinal grooves equidistant from each other,
Cutting speed: 115 m / min,
Cutting depth: 1.5 mm,
Feed: 0.48 mm / rev, and
Cutting time: 5 minutes, and subjected to a dry-type discontinuous thickness-cutting-depth cutting test of a cast iron under the following conditions:
Workpiece: JIS · FC200 rod with four longitudinal grooves equidistant from each other,
Cutting speed: 155 m / min,
Cutting depth: 6.5 mm,
Feed: 0.17 mm / rev, and
Cutting time: 5 minutes, screwed into the tip portion of a tool steel insert using a fixture tool clamping device. In all cutting tests, the edge wear width of the cutting edge was measured. The measurement results are listed in Table 1-5. Table 1-1

Table 1-2

Table 1-3

Table 1-4

Table 1-5

(The failure was caused by peeling off the wear-resistant layer.)

Example 1-2

The cemented carbide substrates B1-1 to B1-8 for end mills each having a size of 6 mm × 13 mm, 10 mm × 22 mm and 20 mm × 45 mm in diameter and length of the cutting edge portion were made in accordance with the combination shown in Table 1-6 by preparing a WC powder of medium-grain grains having an average grain size of 5.5 μm, a WC powder of fine grains having an average grain size of 0.8 μm, a TaC powder having an average grain size of 1.3 μm, a NbC powder having an average particle size of 1.2 microns, a ZrC powder having a mean particle size of 1.2 microns, a Cr ₃ C ₂ powder having a mean particle size of 2.3 microns, a VC powder with a mean grain size of 1.5 μm, a (Ti, W) C powder having a mean grain size of 1.0 μm and a Co powder having a mean grain size of 1.8 μm, compounding these raw powders according to each of the formulations in Table 1-6, Adding a wake ses, mixing them in acetone in a ball mill for 24 hours, drying the mixture under reduced pressure, compacting the dried mixture under a pressure of 100 MPa to form unsintered moldings, sintering these unsintered moldings under conditions of heating to a predetermined temperature within a range of 1370 to 1470 ° C at a heating rate of 7 ° C / min in a vacuum atmosphere of 6 Pa, holding at this temperature for 1 hour and cooling in the furnace, whereby three kinds of sintered round bars for forming cemented carbide substrates each having a Diameter of 8 mm, 13 mm and 26 mm were formed, and cutting of three types of sintered round rods produced.

These cemented carbide substrates B1-1 to B1-8 were subjected to ultrasonic cleaning in acetone, dried, and then immersed in the same arc ion plating apparatus as in 1 shown ge and the surface of each of these cemented carbide substrates was subjected to the pretreatment and the arc ion plating surface treatment under the same conditions as in Example 1 to form an amorphous layer on the surface of the cemented carbide substrates B1-1 to B1-8. The depth of the amorphous layer formed on the surface thereof was also adjusted by controlling the treatment time of the arc ion plating surface treatment under the conditions described above.

The Structure of the surface the sintered carbide substrates B1-1 to B1-8 formed amorphous layer was measured by means of a transmission electron microscope (magnification: 500,000) were observed, and the rating and measurement were based on the results determined. As a result, the mean depth (average of the mean measured at five points) Depths) from the surface each shown in Table 1-7.

By using a conventional chemical deposition apparatus, a wear resistant coating layer of a Ti compound layer having a target composition and a target thickness as shown in Table 1-7 on the surface of these cemented carbide substrates B1-1 to B1-8 under the same conditions as in Table 1-2 shown formed in the state of subjecting a draw grinding treatment to make therefrom surface-coated carbide alloy end mills of the present invention (hereinafter referred to as coated cemented carbide end mills of the present invention) 1-1 'to 1-8' as the coated cemented carbide tool of the present invention has a shape which is shown in a schematic front view of 3A and a schematic cross-sectional view of 3B of the cutting edge portion is shown.

To the As shown in Table 1-8, end mills were compared a conventional one Coated cemented carbide (hereinafter referred to as conventional coated cemented carbide end mills) 1-1 'to 1-8' as conventional coated cemented carbide tool under the same conditions manufactured as described above, with the exception that the pre-treatment and the arc ion plating surface treatment among the above conditions on the surface of the cemented carbide substrates B1-1 to B1-8 were not performed in the arc ion plating apparatus and therefore the amorphous layer is not on the surface of the Sintercarbidsubstrate B1-1 to B1-8 was formed.

Tabelle 1-7

Tabelle 1-8

(Das Versagen wurde durch Ablösen der abnutzungsbeständigen Schicht verursacht.)Subsequently, the coated cemented carbide end mills 1-1 'to 1-3' of the present invention and the conventional coated cemented carbide end mills 1-1 'to 1-3' under the coated cemented carbide end mills 1-1 'to 1-8'. of the present invention and the conventional coated cemented carbide end mills 1-1 'to 1-8' are subjected to a wet-type thickness cutting side cutting test of a cast iron under the following conditions:
Workpiece: JIS FC250 plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Rotation speed: 5350 min ^-1,
Cutting depth in the axial direction: 1.2 mm
Cutting depth in the radial direction: 1.6 mm, and
Feed: 590 mm / min. The coated cemented carbide end mills 1-4 'to 1-6' of the present invention and the conventional coated cemented carbide end mills 1-4 'to 1-6' were subjected to a wet-type thickness cutting side cutting test of a carbon steel among those subject to the following conditions:
Workpiece: JIS · S10C plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Rotation speed: 2000 min ^-1,
Cutting depth in axial direction: 20 mm
Cutting depth in the radial direction: 2.6 mm, and
Feeding: 260 mm / min. The coated cemented carbide end mills 1-7 'to 1-8' of the present invention and the coated cemented carbide end mills 1-7 'to 1-8' were subjected to a wet-type side cutting test of wet type hardened steel subject to the following conditions:
Workpiece: JIS · SKD61 (hardness: HRC52) plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Rotation speed: 650 min ^-1 ,
Cutting depth in the axial direction: 26 mm
Cutting depth in the radial direction: 1.4 mm, and
Feed: 72 mm / min. In all the side cutting tests (water soluble drilling oil is used in all tests), the cut length was measured until the flank wear rate of the peripheral edge reached 0.1 mm as a life criterion. The measurement results are listed in Table 1-7 and Table 1-8. Table 1-6

Table 1-7

Table 1-8

(The failure was caused by peeling off the wear-resistant layer.)

Example 1-3

Under Use of three types of sintered round rods, each with a diameter of 8 mm (to form the cemented carbide substrates B1-1 to B1-3), a diameter of 13 mm (to form the cemented carbide substrates B1-4 to B1-6) and 26 mm (to form the cemented carbide substrates B1-7 to B1-8) prepared in Example 1-2 became the Cemented carbide substrates C1-1 to C1-8 for each size 4 drill bit mm × 13 mm (cemented carbide substrates C1-1 to C 1-3), 8 mm × 22 mm (cemented carbide substrates C1-4 to C 1-6) and 16 mm × 45 mm (Cemented carbide substrates C1-7 to C1-8) for diameter and length of the chip groove made from these three types of sintered rods.

These cemented carbide substrates C1-1 to C1-8 were subjected to ultrasonic cleaning in acetone, dried, and then immersed in the same arc ion plating apparatus as in 1 and the surface of each of these cemented carbide substrates was subjected to the pretreatment and the arc ion plating surface treatment under the same conditions as in Example 1 to form an amorphous layer on the surface of the cemented carbide substrates C1-1 to C1-8. The depth of the amorphous layer formed on the surface thereof was also adjusted by controlling the treatment time of the arc ion plating surface treatment under the conditions described above.

The Structure of the surface the sintered carbide substrates C1-1 to C1-8 formed amorphous layer was measured by means of a transmission electron microscope (magnification: 500,000) were observed, and the rating and measurement were based on the results determined. As a result, the mean depth (average of the mean measured at five points) Depths) from the surface each shown in Table 1-9.

Using a conventional chemical deposition apparatus, a wear resistant coating layer of a Ti compound layer having a target composition and a target thickness as shown in Table 1-9 was surface-treated on these cemented carbide substrates B1-1 to B1-8 under the same conditions as in Table 1-2 shown in the state of subjecting a pull grind treatment to making drills of a surface-coated carbide alloy of the present invention (hereinafter referred to as coated cemented carbide drills of the present invention) 1-1 "to 1-8" as the coated cemented carbide tool of the present invention , which has a shape which is shown in a schematic front view of 4A and a schematic cross-sectional view of 4B the chip groove is shown.

To the Comparison was made, as shown in Table 1-10, end drill from a usual Coated cemented carbide (hereinafter referred to as conventional coated cemented carbide drills) 1-1 "to 1-8 '' as conventional coated cemented carbide tool under the same conditions manufactured as described above, with the exception that the pre-treatment and the arc ion plating surface treatment among the above conditions on the surface of the cemented carbide substrates C1-1 until C1-8 were not performed in the arc ion plating apparatus and therefore the amorphous layer is not on the surface of the Sintercarbidsubstrate C 1-1 to C 1-8 was formed.

Tabelle 1-10

(Das Versagen wurde durch Ablösen der abnutzungsbeständigen Schicht verursacht.)Subsequently, the coated cemented carbide end drills 1-1 "to 1-3" of the present invention and the conventional coated cemented carbide drills 1-1 "to 1-3" among the coated cemented carbide drills 1-1 " 1-8 "of the present invention is subjected to a wet-type high-load boring test of a cast iron under the following conditions:
Workpiece: JIS FC250 plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Cutting speed: 45 m / min, and
Feed: 0.42 mm / div. The coated cemented carbide drills 1-4 '' to 1-6 '' of the present invention and the conventional coated cemented carbide drills 1-4 '' to 1-6 '' have been subjected to a wet type high load boring test of a carbon steel among the subject to the following conditions:
Workpiece: JIS · S10C plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Cutting speed: 48 m / min, and
Feeding: 0.36 mm / div. The coated cemented carbide drills 1-7 \ "to 1-8 \" of the present invention and the conventional coated cemented carbide drills 1-7 \ "to 1-8 \" were subjected to a wet-type high-load boring test of an alloy steel among those subject to the following conditions:
Workpiece: JIS · SCM440 plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Cutting speed: 63 m / min, and
Feed: 0.43 mm / div. In all wet-type high load rigging tests (water soluble drill oil was used in all tests), the number of drilled holes was measured until the edge wear area of the tip edge surface reached 0.3 mm. The measurement results are listed in Table 1-9 and Table 1-10. Table 1-9

Table 1-10

(The failure was caused by peeling off the wear-resistant layer.)

The composition and thickness of the hard coating layer of the coated cemented carbide inserts 1-1 to 1-10 of the present invention, the coated cemented carbide endmills 1-1 'to 1-8' of the present invention, and the coated cemented carbide drills 1-1 '' 1-8 "of the present invention as the coated cemented carbide tool of the present invention and the conventional coated cemented carbide inserts 1-1 to 1-10, the conventional coated cemented carbide end mills 1-1 'to 1-8', and the conventional coated cemented carbide end mills. Drills 1-1 "to 1-8" as the conventional coated cemented carbide tool of the present invention were measured by means of an energy dispersive X-ray measuring apparatus, an Auger spectrometer and a scanning electron microscope. As a result, they showed the composition and the average thickness (compared with an average of the thicknesses measured at five points), which are substantially the same as the target composition and the middle one Target Thickness in Table 1-3, Table 1-4 and Table 1-7 through Table 1-10.

Second embodiment

The second embodiment of the present invention has been accomplished on the basis of the findings (a) to (c) obtained in the first embodiment described above, and is characterized by a coated cemented carbide tool, a hard coating layer having excellent adhesion, comprising: a tungsten carbide-based cemented carbide substrate having an amorphous layer formed by an arc ion plating surface treatment at an average depth of 1 to 50 nm from the surface; and a single-layer or multi-layered hard coating layer physically deposited on the surface of the tungsten carbide-based cemented carbide substrate, the single-layer or multi-layered hard coating layer being formed of either or both of a (Ti, Al) N layer and a (Ti, Al) CN layer each satisfying the composition formula: (Ti _1-x Al _x ) N and the composition formula: (Ti _1-x Al _x ) C _{1 -y} N _y (wherein X is 0.15 to 0.65 and Y is 0.5 to 0.99 in terms of atomic ratio) and has an average thickness of 0.5 to 15 μm.

The average thickness of the on the surface of the cemented carbide substrate formed amorphous layer, which is the coated cemented carbide substrate of the present invention, in the coated cemented carbide tool this embodiment was set to a range of 1 to 50 nm for the following reasons. That is, if the depth is less than 1 nm, the desired excellent Adhesion between this and the TiN layer as tougher primary layer be ensured. In contrast, is the effect of improving the adhesion of the TiN layer to the surface of the cemented carbide substrate satisfying when the average depth from the surface 50 nm.

In the coated cemented carbide tool of this invention, Al is incorporated in the (Ti, Al) N layer and the (Ti, Al) CN layer constituting the hard coating layer in TiCN in the form of a solid solution for the purpose of improving the hardness thereby improving the wear resistance. For this reason, the X value was set in a range of 0.15 to 0.65 (atomic ratio) for the following reason. Namely, when the X value in the composition formula: (Ti _1-x Al _x ) N and the composition formula: (Ti _1-x Al _x ) C _{1 -y} N _{y is} less than 0.15, the desired wear resistance can not be ensured become. On the other hand, when the X value is larger than 0.65, chipping tends to occur in the edge area. Since the component C in the (Ti, Al) CN layer has the effect of improving the hardness, the (Ti, Al) CN layer has a comparatively high hardness as compared with the (Ti, Al) N layer. When the amount of the component C is less than 0.01, that is, the Y value is larger than 0.99, a predetermined effect of improving the hardness can not be obtained. On the other hand, when the amount of the component C is larger than 0.5, that is, the Y value is smaller than 0.5, the toughness is rapidly reduced. Therefore, the Y value was set in a range of 0.5 to 0.99, and preferably 0.55 to 0.9.

Of the Reason why the average thickness of the hard coating layer to a range of 0.5 to 15 microns is set is the following. If the thickness is less than 0.5 microns, can the desired excellent wear resistance can not be ensured. In contrast, when the thickness is greater than 15 μm, Slight chipping occurs at the cutting edge.

The Coated cemented carbide tools of this embodiment will be described in detail.

Example 2-1

The cemented carbide substrates A2-1 to A2-6, each having the shape of an insert as defined in ISO · SNGA120412, and the cemented carbide substrates A2-7 to A2-10 each having a shape of an insert defined in accordance with ISO · SNMA120412 were prepared by preparing a WC powder, a TiC powder, a ZrC powder, a VC powder, a TaC powder, a NbC powder, a Cr ₃ C ₂ powder, a TiN powder, a TaN powder and a CoN powder. Powder each having a predetermined mean grain size of 1 to 3 μm, compounding these raw powders according to each individual formulation in Table 2-1, wet mixing them in a ball mill for 72 hours, drying the mixture, compacting the dried mixture under a pressure of 100 MPa to form green sheets, vacuum-sintering these green sheets under the conditions of a vacuum degree of 6 Pa and a temperature of 1410 ° C for 1 hour and subjecting the cutting edge a grinding range (R: 0.05).

These cemented carbide substrates A2-1 to A2-10 were subjected to ultrasonic cleaning in acetone, and were then placed in a conventional arc ion plating apparatus as in 1 and the surface of each of the cemented carbide substrates A2-1 to A2-10 was subjected to pretreatment under the following conditions:
Atmospheric temperature in the device (temperature of the cemented carbide substrate): 400 ° C,
atmospheric gas: Ar,
Atmospheric pressure: 3 Pa,
Cathode electrode: (not used),
Arc discharge current: (arc powder - off),
applied to the cemented carbide substrate pre-pressure: -900 V, and
Treatment time: 3 minutes, and then subjected to arc ion plating surface treatment under the following conditions:
Atmospheric temperature in the device: 500 ° C,
atmospheric gas: Ar,
Atmospheric pressure: 3 Pa,
Cathode electrode: metallic Ti,
Arc discharge current: 150 A, and
applied to the cemented carbide substrate: -1000 V to thereby form an amorphous layer on the surface of the cemented carbide substrates A2-1 to A2-10. The depth of the amorphous layer formed on the surface thereof was adjusted by regulating the treatment time of the arc ion plating surface treatment under the conditions described above.

The Structure of the surface the sintered carbide substrates A2-1 to A2-10 formed amorphous layer was measured by means of a transmission electron microscope (magnification: 500,000), and the rating and measurement were based on the results determined. As a result, the mean depths (average depths measured at five points) from the surface shown in Table 2-2 and Table 2-3, respectively.

Using the same chemical deposition apparatus, a hard coating layer having a target composition and a target thickness as shown in Table 2-2 and Table 2-3 was set on the surface of these cemented carbide substrates A2-1 to A2-10 with the amorphous layer formed on the surface thereof deposited according to the following conditions:
Atmospheric temperature in the oven: 500 ° C,
atmospheric gas: nitrogen gas, methane gas or mixed gas of nitrogen gas and methane gas in a predetermined ratio,
Atmospheric pressure: 5 Pa,
Cathode electrode: Ti-Al alloy with different compositions,
Arc discharge current: 70 A, and
applied to the cemented carbide substrate: -100 V, whereby the coated cemented carbide inserts 2-1 to 2-20 with the in a schematic perspective view of 2A and a schematic longitudinal sectional view of 2 B of the present invention.

To the Comparison, as shown in Table 2-4 and Table 2-5, the usual coated cemented carbide inserts 2-1 to 2-20 (hereinafter referred to as conventional coated cemented carbide inserts) each produced under the same conditions as described above, with the exception that the pre-treatment and the arc ion plating surface treatment under the above conditions on the surface of the Cemented carbide substrates A2-1 to A2-10 in the arc ion plating apparatus not done and thus the amorphous layer did not on the surface of the Sintercarbidsubstrate A2-1 to A2-10 was formed.

Tabelle 2-2

Tabelle 2-3

Tabelle 2-4

Tabelle 2-5

Tabelle 2-6

(Das Versagen wurde durch ein Ablösungsphänomen bei der harten Beschichtungsschicht verursacht.) Tabelle 2-7

(Das Versagen wurde durch ein Ablösungsphänomen bei der harten Beschichtungsschicht verursacht.)Subsequently, the coated cemented carbide inserts 2-1 to 2-20 of the present invention and the conventional coated cemented carbide inserts 2-1 to 2-20 were subjected to a dry-type discontinuous thickness-cutting-depth cutting test of an alloy steel under the following conditions:
Workpiece: JIS · SCM440 rod with four longitudinal grooves at equal distances,
Cutting speed: 125 m / min,
Cutting depth: 5 mm
Feed: 0.2 mm / rev, and
Cutting time: 5 minutes, a dry-type discontinuous high-speed cutting test of a carbon steel under the following conditions:
Workpiece: JIS · S20C rod with four longitudinal grooves equidistant from each other,
Cutting speed: 120 m / min,
Cutting depth: 1.5 mm,
Feed: 0.45 mm / rev, and
Cutting time: 5 minutes, and subjected to a high-speed dry-type batch cutting test of a carbon steel under the following conditions:
Workpiece: JIS · A10C rod with four longitudinal grooves equidistant from each other
Cutting speed: 250 m / min,
Cutting depth: 2 mm,
Feed: 0.2 mm / rev, and
Cutting time: 4 minutes, when screwed in, into the tip portion of a tool steel insert using a fixture tool clamping device. In all cutting tests, the edge wear width of the cutting edge was measured. The measurement results are listed in Table 2-6 and Table 2-7. Table 2-1

Table 2-2

Table 2-3

Table 2-4

Table 2-5

Table 2-6

(The failure was caused by a peeling phenomenon in the hard coating layer.) Table 2-7

(The failure was caused by a peeling phenomenon in the hard coating layer.)

Example 2-2

The cemented carbide substrates B2-1 to B2-8 for a face mill, each in a size of 6 mm x 13 mm, 10 mm x 22 mm and 20 mm x 45 mm for diameter and length of the cutting edge area, were made in accordance with Table 2-8 combination shown by preparing a WC powder of medium grain size grains with a mean grain size of 5.5 microns, a WC powder of fine grains having a mean grain size of 0.8 microns, a TaC powder having a mean grain size of 1.3 μm, a NbC powder having an average particle size of 1.2 μm, a ZrC powder having a mean particle size of 1.2 μm, a Cr ₃ C ₂ powder having an average particle size of 2.3 μm, a VC Powder having a mean particle size of 1.5 microns, a (Ti, W) C powder having a mean particle size of 1.0 microns and a co-powder with a average particle size of 1.8 microns, compounding these raw powders according to each of the formulations in Table 2-8, adding a wax, mixing them in acetone in a ball mill for 24 hours, drying the mixture under reduced pressure, compacting the dried mixture under one Pressure of 100 MPa to form green compacts, sintering these green compacts under conditions of heating to a predetermined temperature within a range of 1370 to 1470 ° C at a heating rate of 7 ° C / min in a vacuum atmosphere of 6 Pa, hold This temperature for 1 hour and cooling in the oven, whereby three types of sintered round bars for forming cemented carbide substrate each having a diameter of 8 mm, 13 mm and 26 mm were formed, and cutting three types of sintered round bars.

These cemented carbide substrates B2-1 to B2-8 were subjected to ultrasonic cleaning in acetone, dried, and then immersed in the same arc ion plating apparatus as in 1 and the surface of each of these cemented carbide substrates was subjected to the pretreatment and the arc ion plating surface treatment under the same conditions as in Example 1 to form an amorphous layer on the surface of the cemented carbide substrates B2-1 to B2-8. The depth of the amorphous layer formed on the surface thereof was also adjusted by controlling the treatment time of the arc ion plating surface treatment under the conditions described above.

The Structure of the surface the sintered carbide substrates B2-1 to B2-8 formed amorphous layer was measured by means of a transmission electron microscope (magnification: 500,000), and the rating and measurement were based on the results determined. As a result, the mean depths (average of the mean measured at five points) Depths) from the surface shown in Table 2-9 and Table 2-10, respectively.

Using the same chemical deposition apparatus, a single-layer or multi-layer hard surface layer was formed of either one or both of a (Ti, Al) N layer and a (Ti, Al) CN layer having the characteristics shown in Table 2-9 and Table 2-. 10 having the target composition and target thickness shown on the surface of these cemented carbide substrates under the same conditions as in Example 1, whereby the surface-finished carbide alloy end mills of the present invention (hereinafter referred to as coated cemented carbide end mills of the present invention) 2-1 'to 2-16 'were produced as the coated cemented carbide tool of the present invention, which in a schematic front view of 3A and a schematic cross-sectional view of 3B having shown shape of the cutting edge region.

To the Comparison, as shown in Table 2-11 and Table 2-12, end mill from a conventional one coated carbide alloy (hereinafter referred to as conventional coated cemented carbide end mills) 2-1 'to 2-16' as conventional coated cemented carbide tool under the same conditions manufactured as described above, with the exception that the pre-treatment and the arc ion plating surface treatment among the above conditions on the surface of the cemented carbide substrates B2-1 to B2-8 in the arc ion plating device not were carried out and therefore the amorphous layer is not on the surface of the Sintercarbidsubstrate B2-1 to B2-8 was formed.

Tabelle 2-9

Tabelle 2-10

Tabelle 2-11

(Das Versagen wurde durch ein Ablösungsphänomen bei der harten Beschichtungsschicht verursacht.) Tabelle 2-12

(Das Versagen wurde durch ein Ablösungsphänomen bei der harten Beschichtungsschicht verursacht.)Subsequently, the coated cemented carbide end mills 2-1 'to 2-3' and 2-9 'to 2-11' of the present invention and the conventional coated cemented carbide end mills 2-1 'to 2-3' and 2-9 'were prepared. to 2-11 'among the coated cemented carbide end mills 2-1' to 2-16 'of the present invention and the conventional coated cemented carbide end mills 2-1' to 2-16 ', a wet type thickness cutting side cutting test Cast iron subjected under the following conditions:
Workpiece: JIS FC250 plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Rotation speed: 5050 min ^-1,
Cutting depth in the axial direction: 12 mm,
Cutting depth in the radial direction: 1.6 mm, and
Feeding: 610 mm / min. The coated cemented carbide end mills 2-4 'to 2-6' and 2-12 'to 2-14' of the present invention and the conventional coated cemented carbide end mills 2-4 'to 2-6' and 2-12 'to 2 -14 'were subjected to a wet-type thickness cutting side cutting test of a carbon steel under the following conditions:
Workpiece: JIS · S10C plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Rotational speed: 1910 min ^-1,
Cutting depth in axial direction: 20 mm
Cutting depth in the radial direction: 2.6 mm, and
Feed: 280 mm / min. The coated cemented carbide end mills 2-7 'to 2-8' and 2-15 'to 2-16' of the present invention and the conventional coated cemented carbide end mills 2-7 'to 2-8' and 2-15 'to 2 -16 'were subjected to a wet-type side-by-side cutting test of a hardened steel under the following conditions:
Workpiece: JIS · SKD61 (hardness: HRC52) plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Rotation speed: 620 min ^-1
Cutting depth in the axial direction: 26 mm
Cutting depth in the radial direction: 1.4 mm, and
Feeding: 75 mm / min. In all side cutting tests (water soluble drilling oil was used in all tests), the cut length was measured until the edge wear rate of the peripheral edge reached 0.1 mm as a life criterion. The measurement results are listed in Table 2-9 and Table 2-12. Table 2-8

Table 2-9

Table 2-10

Table 2-11

(The failure was caused by a peeling phenomenon in the hard coating layer.) Table 2-12

(The failure was caused by a peeling phenomenon in the hard coating layer.)

Example 2-3

Using three types of sintered rods each with a diameter of 8 mm (for forming the cemented carbide substrates B2-1 to B2-3), a diameter of 13 mm (for forming the cemented carbide substrates B2-4 to B2-6) and 26 mm (for forming the cemented carbide substrates B2-7 to B2-8), In Example 2-2, the cemented carbide substrates C2-1 to C2-8 were prepared for drills each having a size of 4 mm × 13 mm (cemented carbide substrates C2-1 to C2-3), 8 mm × 22 mm (cemented carbide substrates C2 -4 to C2-6) and 16 mm x 45 mm (cemented carbide substrates C2-7 to C2-8) for the diameter and length of the chip groove made from these three types of sintered rods.

These cemented carbide substrates C2-1 to C2-8 were subjected to ultrasonic cleaning in acetone, dried, and then immersed in the same arc ion plating apparatus as in 1 and the surface of each of these cemented carbide substrates was subjected to the pretreatment and the arc ion plating surface treatment under the same conditions as in Example 1 to form an amorphous layer on the surface of the cemented carbide substrates C2-1 to C2-8. The depth of the amorphous layer formed on the surface thereof was also adjusted by controlling the treatment time of the arc ion plating surface treatment under the conditions described above.

The Structure of the surface the sintered carbide substrates C2-1 to C2-8 formed amorphous layer was measured by means of a transmission electron microscope (magnification: 500,000), and the rating and measurement were based on the results determined. As a result, the mean depths (average depths measured at five points) from the surface shown in Table 2-13 and Table 2-14, respectively.

Using the same conventional chemical deposition apparatus, a single-layer or multi-layered hard surface layer of either one or both of a (Ti, Al) N layer and a (Ti, Al) CN layer having a target composition and a target thickness was prepared as shown in Table 2 13 and Table 2-14 shown on the surface of these cemented carbide substrates under the same conditions as in Example 1 to form drills of a surface-coated cemented carbide of the present invention (hereinafter referred to as coated cemented carbide drills of the present invention) 2-1 ' to produce 2-16 "as a coated cemented carbide tool of the present invention, which has a shape which is in a schematic front view of 4A and a schematic cross-sectional view of 4B the chip groove is shown.

Tabelle 2-14

Tabelle 2-15

(Das Versagen wurde durch ein Ablösungsphänomen bei der harten Beschichtungsschicht verursacht.) Tabelle 2-16

(Das Versagen wurde durch ein Ablösungsphänomen bei der harten Beschichtungsschicht verursacht.)For comparison, as shown in Table 2-15 and Table 2-16, end drills made of a conventional coated cemented carbide (hereinafter referred to as conventional coated cemented carbide drills) were 2-1 "to 2-16" as a conventional coated cemented carbide tool, respectively under the same conditions as described above, except that the pretreatment and the arc ion plating surface treatment under the above conditions were not performed on the surface of the cemented carbide substrates C2-1 to C2-8 in the arc ion plating apparatus and hence the amorphous layer was not on the surface Surface of the cemented carbide substrates C1-1 to C1-8 was formed. Subsequently, the coated cemented carbide drills 2-1 "to 2-3" and 2-9 "to 2-11" of the present invention and the conventional coated cemented carbide drills 2-1 "to 2-3 'were prepared. 'and 2-9''to2-11''among the coated cemented carbide drills 2-1''to2-16''of the present invention and the conventional coated cemented carbide drills 2-1''to2-16' subjected to a wet-type high-load drilling test of a cast iron under the following conditions:
Workpiece: JIS FC250 plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Cutting speed: 42 m / min, and
Feed: 0.43 mm / div. The coated cemented carbide drills 2-4 '' to 2-6 '' and 2-12 '' to 2-14 '' of the present invention and the conventional coated cemented carbide drills 2-4 '' to 2-6 '' and 2-12 " to 2-14 " were subjected to a wet type high load boring test of a carbon steel under the following conditions:
Workpiece: JIS · S10C plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Cutting speed: 45 m / min, and
Feed: 0.37 mm / div. The coated cemented carbide drills 2-7 ", 2-8", 2-15 "and 2-16" of the present invention and the conventional coated cemented carbide drills 2-7 ", 2-8", 2-15 "and 2-16" were subjected to a wet-type high-load boring test of an alloy steel under the following conditions:
Workpiece: JIS · SCM-440 plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Cutting speed: 60 m / min, and
Feeding: 0.45 mm / div. In all wet-type high load rigging tests (water soluble drill oil was used in all tests), the number of drilled holes was measured until the edge wear area of the tip edge surface reached 0.3 mm. The results are shown in Table 2-13 and Table 2-16 listed. Table 2-13

Table 2-14

Table 2-15

(The failure was caused by a peeling phenomenon in the hard coating layer.) Table 2-16

(The failure was caused by a peeling phenomenon in the hard coating layer.)

The composition and thickness of the hard coating layer of the coated cemented carbide inserts 2-1 to 2-20 of the present invention, the coated cemented carbide end mills 2-1 'to 2-16' of the present invention, and the coated cemented carbide drills 2-1 '' 2-16 "of the present invention as the coated cemented carbide tool of the present invention and the conventional be Coated cemented carbide inserts 2-1 to 2-20, the conventional coated cemented carbide end mills 2-1 'to 2-16' and the conventional coated cemented carbide drills 2-1 '' to 2-16 '' as the conventional coated cemented carbide tool were used Assistance of an energy dispersive X-ray measuring device, an Auger spectrometer and a scanning electron microscope measured. As a result, they showed the composition and the average thickness (as compared with an average of the thicknesses measured at five points), which are substantially the same as the target composition and the average target thickness in Table 2-2 to Table 2-5 and Table 2 -9 to Table 2-16.

Third embodiment

The third embodiment of the present invention was carried out based on the findings (a) to (c). This embodiment is characterized by a coated cemented carbide tool having a wear-resistant coating layer thereof excellent in adhesion, comprising: a tungsten carbide-based cemented carbide substrate having an amorphous layer formed by arc ion plating surface treatment at an average depth of 1 to 50 nm from the surface; and a wear-resistant coating layer physically and / or chemically deposited on the surface of the tungsten carbide-based cemented carbide substrate, the wear-resistant coating layer being composed of: (a) a lower coating layer consisting of one or more of two or more layers; including a TiC layer, a TiN layer, a TiCN layer, a TiCO layer, and a TiCNO layer (hereinafter referred to collectively as Ti compound layer) and having an average thickness of 0.5 to 15 μm; and (b) an upper coating layer consisting of either or both of an Al ₂ O ₃ layer and an Al ₂ O ₃ -ZrO ₂ mixed layer consisting of a matrix of Al ₂ O ₃ and a ZrO dispersed and dispersed therein ₂ phase, and has an average thickness of 0.5 to 15 microns.

at the coated cemented carbide tool of the present invention has re the on the surface the sintered carbide substrate formed amorphous layer and the wear-resistant coating layer the on the surface of the cemented carbide substrate, the effect of the Award of an excellent adhesion between this and the wear resistant Coating layer (lower coating layer) as above described. However, if the depth is less than 1 nm, can the desired excellent adhesion can not be ensured. On the other hand, the effect of the improvement the adhesion the lower coating layer on the surface of the cemented carbide substrate satisfactory if the average depth of the surface is 50 nm is. Therefore, the average depth was in a range of 1 to 50 nm set.

A has the lower coating layer forming Ti compound layer essentially the effect of improving toughness the wear-resistant Coating layer, whereby the occurrence of chipping at the wear-resistant Coating layer even in discontinuous cutting operation, accompanied by high mechanical and thermal effects below Deep cutting conditions, is noticeably suppressed. If, however, the average thickness less than 0.5 microns is, can not be the desired toughness at the wear resistant Ensure coating layer. On the other hand, if the middle one Thickness exceeds 15 μm, it comes easily to a plastic deformation, which easily a one-sided wear caused by the wear-resistant coating layer in discontinuous cutting operation under deep cutting conditions. Therefore, the average depth was set in a range of 0.5 to 15 μm.

The Al ₂ O ₃ layer and the Al ₂ O ₃ -ZrO ₂ mixed layer constituting the upper coating layer have the effect of imparting hardness and heat resistance to the wear-resistant coating layer, resulting in excellent wear resistance without chipping cause the co-existing with this lower coating layer. If the average thickness is less than 0.5 μm, the desired excellent wear resistance can not be ensured. On the other hand, if the average thickness exceeds 15 μm, chipping will likely occur in the wear-resistant coating layer. Therefore, the average depth was set in a range of 0.5 to 15 μm.

The Coated cemented carbide tools of this embodiment will be described in detail.

Example 3-1

The cemented carbide substrates A3-1 to A3-6 each having the shape of a disposable insert as shown in FIG ISO · SNGA120412 were defined by preparing a WC powder, a (Ti, W) C (TiC / WC = 30/70 by weight, as with other powders) powder, one (Ti, W) CN (TiC / TiN / WC = 24/20/56) powder, a (Ta, Nb) C (TaC / NbC = 90/10) powder, a Cr ₃ C ₂ powder and a Co powder each having a predetermined average grain size from 0.5 to 4 μm, compounding these raw powders according to each of the formulations in Table 3-1, wet mixing them in a ball mill for 72 hours, drying the mixture, compacting the dried mixture under a pressure of 100 MPa to form unsintered moldings, Vacuum-sintering these green sheets under the conditions of a vacuum degree of 6 Pa and a temperature of 1410 ° C for 1 hour and subjecting the cutting edge portion to a draw grinding (R: 0.05).

These cemented carbide substrates A3-1 to A3-6 were subjected to ultrasonic cleaning in acetone, dried and then placed in a conventional arc ion plating apparatus as in 1 and the surface of each of the cemented carbide substrates A-F was subjected to pretreatment under the following conditions:
Atmospheric temperature in the device (temperature of the cemented carbide substrate): 400 ° C,
atmospheric gas: Ar,
Atmospheric pressure: 3 Pa,
Cathode electrode: (not used),
Arc discharge current: (arc powder - off),
applied to the cemented carbide substrate pre-pressure: -900 V, and
Treatment time: 3 minutes, and then subjected to arc ion plating surface treatment under the following conditions:
Atmospheric temperature in the device: 500 ° C,
atmospheric gas: Ar,
Atmospheric pressure: 3 Pa,
Cathode electrode: metallic Ti,
Arc discharge current: 150 A, and
applied on the cemented carbide substrate pre-pressure: -1000 V, thereby forming an amorphous layer on the surface of the cemented carbide substrates A to F. The depth of the amorphous layer formed on the surface thereof was adjusted by regulating the treatment time of the arc ion plating surface treatment under the conditions described above.

The Structure of the surface the cemented carbide substrates A3-1 to A3-6 formed amorphous layer was measured by means of a transmission electron microscope (magnification: 500,000), and the rating and measurement were based on the results determined. As a result, the mean depth (average of the depths measured at five points) from the surface each shown in Table 3-3.

By using a conventional chemical deposition apparatus, a wear resistant coating layer consisting of a Ti compound layer (lower coating layer) having a target composition and a target thickness as shown in Table 3-3 and an Al ₂ O ₃ layer and / or an Al ₂ O ₃ -ZrO ₂ mixed layer (upper layer) is composed, on the surface of these cemented carbide A3-1 to A3-6 under the conditions of (1-TiCN in Table is cultured with a longitudinally for the conditions for the formation of a TiCN layer Crystal structure as described in Japanese Patent Application, First Publication No. Hei 6-8010) shown in Table 3-2, thereby forming disposable inserts of a surface-coated carbide alloy of this embodiment (hereinafter referred to as coated cemented carbide inserts of the present invention) 3-1 to 3-10 as a coated cemented carbide mill Eug of the present invention have been prepared, which has a shape in a schematic perspective view of 2A and a schematic longitudinal sectional view of 2 B is shown.

To the Comparison was made as shown in Table 3-4, the conventional coated cemented carbide inserts 3-1 to 3-10 (hereinafter referred to as conventional coated cemented carbide inserts) each produced under the same conditions as described above, with the exception that the pre-treatment and the arc ion plating surface treatment under the above conditions on the surface of the Cemented carbide substrates A3-1 to A3-6 in the arc ion plating apparatus not done and thus the amorphous layer did not on the surface of the Sintercarbidsubstrate A3-1 to A3-6 was formed.

Tabelle 3-2

(Der Prozentanteil von ZrO₂ in den Mischschichten ➀ und ➁ steht für einen Zielgehalt) Tabelle 3-3

Tabelle 3-4

Tabelle 3-5

(Das Versagen wurde durch das Ablösen der abnutzungsbeständigen Beschichtungsschicht verursacht.)Subsequently, the coated cemented carbide inserts 3-1 to 3-10 of the present invention and the conventional coated cemented carbide inserts 3-1 to 3-10 are subjected to a dry type discontinuous thickness-cutting-depth cutting test of an alloy steel under the following conditions:
Workpiece: JIS SCM440 rod with four longitudinal grooves at equal intervals,
Cutting speed: 130 m / min,
Cutting depth: 5.3 mm,
Feed: 0.18 mm / rev, and
Cutting time: 5 min,
and a dry type discontinuous high-speed cutting test of a carbon steel under the following conditions:
Workpiece: JIS · S20C rod with four longitudinal grooves equidistant from each other,
Cutting speed: 135 m / min,
Cutting depth: 1.4 mm,
Feed: 0.5 mm / rev, and
Cutting time: 5 min,
and a high-speed dry type discontinuous cutting test of a ductile cast iron under the following conditions:
Workpiece: JIS · FC450 rod with four longitudinal grooves equidistant from each other,
Cutting speed: 170 m / min,
Cutting depth: 7 mm,
Feed: 0.2 mm / rev, and
Cutting time: 5 minutes, screwed into the tip portion of a tool steel insert using a fixture tool clamping device. In all cutting tests, the edge wear width of the cutting edge was measured. The measurement results are listed in Table 3-5. Table 3-1

Table 3-2

(The percentage of ZrO ₂ in the mixed layers ➀ and ➁ stands for a target content) Table 3-3

Table 3-4

Table 3-5

(The failure was caused by the detachment of the wear-resistant coating layer.)

Example 3-2

The cemented carbide substrates B3-1 to B3-8 for a face mill, each in a size of 6 mm x 13 mm, 10 mm x 22 mm and 20 mm x 45 mm for diameter and length of the cutting edge area, were made in accordance with the procedure given in Table 3-6 combination shown by preparing a WC powder of medium grain size grains with a mean grain size of 5.5 microns, a WC powder of fine grains having a mean grain size of 0.8 microns, a TaC powder having a mean grain size of 1.3 μm, a NbC powder having an average particle size of 1.2 μm, a ZrC powder having a mean particle size of 1.2 μm, a Cr ₃ C ₂ powder having an average particle size of 2.3 μm, a VC Powder having a mean particle size of 1.5 microns, a (Ti, W) C powder having a mean particle size of 1.0 microns and a co-powder with a average grain size of 1.8 μm, compounding these raw powders according to each formulation in Table 3-6, adding a wax, mixing them in acetone in a ball mill for 24 hours, drying the mixture under reduced pressure, compacting the dried mixture under pressure of 100 MPa for forming green sheets, sintering these green sheets under conditions of heating to a predetermined temperature within a range of 1370 to 1470 ° C at a heating rate of 7 ° C / min. in a vacuum atmosphere of 6 Pa, holding thereon Temperature for one hour and cooling in the furnace, thereby forming three kinds of sintered round bars for forming cemented carbide substrates each having a diameter of 8 mm, 13 mm and 26 mm, and cutting three kinds of sintered round bars.

These cemented carbide substrates B3-1 to B3-8 were subjected to ultrasonic cleaning in acetone, dried, and then immersed in the same arc ion plating apparatus as in 1 and the surface of each of the cemented carbide substrates was subjected to the pretreatment and the arc ion plating surface treatment under the same conditions as in Example 1 to form an amorphous layer on the surface of the cemented carbide substrates B3-1 to B3-8. The depth of the amorphous layer formed on the surface thereof was also adjusted by controlling the treatment time of the arc ion plating surface treatment under the conditions described above.

The Structure of the surface the cemented carbide substrates B3-1 to B3-8 formed amorphous layer was measured by means of a transmission electron microscope (magnification: 500,000), and the rating and measurement were based on the results determined. As a result, the mean depth (average of the depths measured at five points) from the surface each listed in Table 3-7.

Using the same chemical deposition apparatus, a wear resistant coating layer consisting of a Ti compound layer (lower coating layer) having a target composition and a target thickness as shown in Table 3-7 and an Al ₂ O ₃ layer and / or an Al ₂ O ₃ ZrO ₂ mixed layer (upper coating layer) is formed on the surface of these cemented carbide substrates under the conditions shown in Table 3-2, whereby a surface-coated carbide alloy face milling cutter of the present invention (hereinafter referred to as coated cemented carbide inserts of the present invention) 3- 1 'to 3-8' were produced as a coated cemented carbide tool of the present invention, which has a shape which is shown in a schematic front view of 3A and a schematic cross-sectional view of the cutting edge region of 3B is shown.

To the Comparison was made, as shown in Table 3-8, end mill a conventional one Coated cemented carbide (hereinafter referred to as conventional coated cemented carbide end mills) 3-1 'to 3-8' as conventional coated cemented carbide tool under the same conditions manufactured as described above, with the exception that the pre-treatment and the arc ion plating surface treatment among the above conditions on the surface of the cemented carbide substrates B3-1 to B3-8 were not performed in the arc ion plating apparatus and therefore the amorphous layer is not on the surface of the Sintercarbidsubstrate B3-1 to B3-8 was formed.

Subsequently, the coated cemented carbide end mills 3-1 'to 3-3' of the present invention and the conventional coated cemented carbide inserts 3-1 'to 3-3' under the coated cemented carbide end mills 3-1 'to 3-8' of the present invention Invention and the conventional coated cemented carbide end mills 3-1 'to 3-8' are subjected to a wet-type thickness cutting side cutting test of a cast iron under the following conditions:
Workpiece: JIS FC250 plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Rotational speed: 5500 min ^-1,
Cutting depth in the axial direction: 12 mm,
Cutting depth in the radial direction: 1.6 mm, and
Feed: 590 mm / min.

The coated cemented carbide end mills 3-4 'to 3-6' of the present invention and the conventional coated cemented carbide end mills 3-4 'to 3-6' were subjected to a wet-type thickness cutting side cutting test of a carbon steel under the following conditions subjected to:
Workpiece: JIS · S10C plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Rotational speed: 2200 min ^-1,
Cutting depth in axial direction: 20 mm
Cutting depth in the radial direction: 2.5 mm, and
Feeding: 260 mm / min.

The coated cemented carbide end mills 3-7 'to 3-8' of the present invention and the conventional coated cemented carbide end mills 3-7 'to 3-8' were subjected to a wet-type thickness cutting side cutting test of a hardened steel among the following Subject to conditions:
Workpiece: JIS · SKD61 (hardness: HRC52) plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Rotational speed: 670 min ^-1
Cutting depth in the axial direction: 26 mm
Cutting depth in the radial direction: 1.4 mm, and
Feed: 70 mm / min.

Tabelle 3-7

Tabelle 3-8

(Das Versagen wurde durch Ablösen der abnutzungsbeständigen Schicht verursacht.)In all side cutting tests (water soluble drilling oil was used in all tests), the cut length was measured until the edge wear rate of the peripheral edge reached 0.1 mm as a life criterion. The measurement results are listed in Table 3-7 and Table 3-8. Table 3-6

Table 3-7

Table 3-8

(The failure was caused by peeling off the wear-resistant layer.)

Example 3-3

Under Use of three types of sintered round rods, each with a diameter 8 mm (to form the cemented carbide substrates B3-1 to B3-3), a diameter of 13 mm (to form the cemented carbide substrates B3-4 to B3-6) and 26 mm (to form the cemented carbide substrates B3-7 to B3-8) prepared in Example 3-2 became the Cemented carbide substrates C3-1 through C3-8 for each sized 4 drill bit mm × 13 mm (cemented carbide substrates C3-1 to C3-3), 8 mm × 22 mm (cemented carbide substrates C3-4 to C3-6) and 16 mm x 45 mm (Cemented carbide substrates C3-7 to C3-8) for diameter and length of the chip groove made from these three types of sintered rods.

These cemented carbide substrates C3-1 to C3-8 were subjected to ultrasonic cleaning in acetone, dried, and then immersed in the same arc ion plating apparatus as in 1 and the surface of each of these cemented carbide substrates was subjected to the pretreatment and the arc ion plating surface treatment under the same conditions as in Example 1 to form an amorphous layer on the surface of the cemented carbide substrates C3-1 to C3-8. The depth of the amorphous layer formed on the surface thereof was also adjusted by controlling the treatment time of the arc ion plating surface treatment under the conditions described above.

The structure of the amorphous formed on the surface of the cemented carbide substrates C3-1 to C3-8 Layer was observed by means of a transmission electron microscope (magnification: 500,000), and the evaluation and measurement were carried out on the basis of the observed results. As a result, the mean depths (average of the mean depths measured at five points) from the surface are shown in Table 3-9, respectively.

By using the same conventional chemical deposition apparatus, a wear resistant coating layer composed of a Ti compound layer (lower coating layer) having a target composition and a target thickness as shown in Table 3-9 and an Al ₂ O ₃ layer and / or an Al ₂ O ₃ -ZrO ₂ mixed layer (upper coating layer) formed on the surface of these cemented carbide substrates under the conditions shown in Table 3-2, whereby drills of a surface-coated carbide alloy of the present invention (hereinafter referred to as coated cemented carbide drills of the present invention ) 3-1 to 3-8 were produced as coated cemented carbide drills of the present invention having a shape which is shown in a schematic front view of FIG 4A and a schematic cross-sectional view of the chip groove of 4B is shown.

To the Comparison was made, as shown in Table 3-10, end drill from a usual Coated cemented carbide (hereinafter referred to as conventional coated cemented carbide drills) 3-1 '' to 3-8 '' as conventional coated cemented carbide tool under the same conditions manufactured as described above, with the exception that the pre-treatment and the arc ion plating surface treatment among the above conditions on the surface of the cemented carbide substrates C3-1 to C3-8 were not performed in the arc ion plating apparatus and therefore the amorphous layer is not on the surface of the Sintercarbidsubstrate C3-1 to C3-8 was formed.

Tabelle 3-10

(Das Versagen wurde durch Ablösen der abnutzungsbeständigen Schicht verursacht.)Subsequently, the coated cemented carbide drills 3-1 "to 3-3" of the present invention and the conventional coated cemented carbide drills 3-1 "to 3-3" under the coated cemented carbide drills 3-1 " 3-8 " of the present invention and the conventional coated cemented carbide drills 3-1 " to 3-8 " are subjected to a wet-type high-load boring test of a cast iron under the following conditions:
Workpiece: JIS FC250 plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Cutting speed: 48 m / min, and
Feed: 0.41 mm / div. The coated cemented carbide drills 3-4 "to 3-6" of the present invention and the conventional coated cemented carbide drills 3-4 "to 3-6" were subjected to a wet-type high load boring test of a carbon steel among those subject to the following conditions:
Workpiece: JIS · S10C plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Cutting speed: 50 m / min, and
Feeding: 0.36 mm / div. The coated cemented carbide drills 3-7 '' and 3-8 '' of the present invention and the conventional coated cemented carbide drills 3-7 '' to 3-8 '' were subjected to a wet type high load boring test of an alloy steel among the subject to the following conditions:
Workpiece: JIS · SCM440 plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Cutting speed. 65 m / min, and
Feed: 0.42 mm / div. In all wet-type high load rigging tests (water soluble drill oil was used in all tests), the number of drilled holes was measured until the edge wear area of the tip edge surface reached 0.3 mm. The measurement results are listed in Table 3-9 and Table 3-10. Table 3-9

Table 3-10

(The failure was caused by peeling off the wear-resistant layer.)

The composition and thickness of the hard coating layer of the coated cemented carbide inserts 3-1 to 3-10 of the present invention, the coated cemented carbide end mills 3-1 'to 3-8' of the present invention and the coated cemented carbide drills 3-1 '' 3-8 "of the present invention as the coated cemented carbide tool of the present invention and the conventional coated cemented carbide inserts 3-1 to 3-10, the conventional coated cemented carbide end mills 3-1 'to 3-8', and the conventional coated cemented carbide end mills. Drills 3-1 "to 3-8" as the conventional coated cemented carbide tool were measured by means of an energy dispersive X-ray measuring apparatus, an Auger spectrometer and a scanning electron microscope. As a result, they showed the composition and the average thickness (compared with an average of the thicknesses measured at five points), which are substantially the same as the target composition and the mean target thickness in Table 3-3, Table 3-4 and Table 3-7 to Table 3-10.

Fourth embodiment

• (a) Wenn das Sintercarbidsubstrat in die Lichtbogenionenplattierungsvorrichtung gegeben wurde und die Oberfläche des Sintercarbidsubstrats einer Vorbehandlung unterworfen wurde, ohne den Einsatz einer Kathodenelektrode unter den folgenden Bedingungen einer Atmosphärentemperatur in der Vorrichtung (Temperatur des Sintercarbidsubstrats): 300 bis 500°C, eines atmosphärischen Gases: Ar, eines Atmosphärendrucks: 1 bis 10 Pa, eines Lichtbogenentladungsstroms: (Lichtbogen-Pulver – Aus), eines auf das Sintercarbidsubstrat angewandten Vordrucks: –800 bis –1000 V, und einer Behandlungszeit: 2 bis 10 min, und dann die Oberfläche des Sintercarbidsubstrats weiter einer Lichtbo genionenplattierungsoberflächenbehandlung unter Verwendung von metallischem Ti als Kathodenelektrode unter den folgenden Bedingungen unterworfen wird: Atmosphärentemperatur in der Vorrichtung: 450 bis 550°C; atmosphärisches Gas: Ar; Atmosphärendruck: 1 bis 10 Pa; Lichtbogenentladungsstrom: 100 bis 200 A; und auf das Sintercarbidsubstrat angewandter Vordruck: –900 bis –1200 V, wird eine metallische Ti-Schicht als Abscheidungsschicht nicht auf der Oberfläche des Sintercarbidsubstrats gebildet. Die Struktur der Oberfläche des Sintercarbidsubstrats selbst wird mit Hilfe eines Transmissionselektronenmikroskops betrachtet. Als ein Ergebnis wird die Bildung einer amorphen Schicht nachgewiesen. Die Bildung der metallischen Ti-Schicht mit Hilfe der Lichtbogenionenplattierungsvorrichtung wird unter den folgenden Bedingungen durchgeführt: Atmosphärentemperatur in der Vorrichtung: 300 bis 500°C; atmosphärisches Gas: (nicht verwendet); Atmosphärendruck: Vakuum bei 0,1 Pa oder weniger; Kathodenelektrode: metallisches Ti; Lichtbogenentladungsstrom: 50 bis 100 A, und auf das Sintercarbidsubstrat angewandter Vordruck: –30 bis –100 V.
• (b) In dem Zustand, in welchem eine amorphe Schicht in einer mittleren Tiefe von 1 bis 50 nm von der Oberfläche gebildet wird, wenn eine abnutzungsbeständige Beschichtungsschicht des herkömmlichen beschichteten Sintercarbidwerkzeugs gebildet wird, wenn eine (Ti, Al)N-Schicht und eine (Ti, Al)CN-Schicht, welche eine harte Oberflächenschicht des herkömmlichen beschichteten Sintercarbidsubstrats bilden, auf der Oberfläche des Sintercarbidsubstrats mit der amorphen Schicht gebildet wird, die auf dessen Oberfläche durch ein Titannitrid (im Folgenden als TiN bezeichnet) mit einer Vickers-Härte von 2000 bis 2500 und einer ausgeprägten hervorragenden Zähigkeit unter Verwendung der gleichen Lichtbogenionenplattierungsvorrichtung gebildet wird, reagiert die amorphe Schicht mit der TiN-Schicht bei deren Bildung unter Abscheidung, da die amorphe Schicht eine hohe Aktivität und eine hohe Reaktivität besitzt, wodurch eine bemerkenswert starke Adhäsion zwischen der Oberfläche des Sintercarbidsubstrats und der TiN-Schicht sichergestellt wird. Eine starke Adhäsion zwischen der TiN-Schicht und der Oberflächenbeschichtungsschicht wird ebenfalls sichergestellt.
• (c) Als ein Ergebnis ist das so erhaltene beschichtete Sintercarbidwerkzeug frei von Ablösung der abnutzungsbeständigen Beschichtungsschicht, die sich aus der TiN-Schicht und der Oberflächenbeschichtungsschicht zusammensetzt, selbst bei einer Verwendung im diskontinuierlichen Schneidebetrieb in Verbindung mit hohen mechanischen und thermischen Einwirkungen unter Tiefschneidebedingungen. Auch die Zähigkeit der abnutzungsbeständigen Beschichtungsschicht selbst wird durch das Vorliegen der TiN-Schicht deutlich verbessert wird und das Auftreten von Absplitterung des Schneidekantenbereichs kann unterdrückt werden. Deshalb wird es möglich, eine in befriedigender Weise hervorragende Abnutzungsbeständigkeit der abnutzungsbeständigen Beschichtungsschicht zu erhalten.

In the fourth embodiment, to further improve the adhesion of a wear resistant coating layer (hard surface layer) constituting the conventional coated cemented carbide tool to the surface of the cemented carbide substrate, adhesion was further improved based on the above-described findings (a) to (c). With the help of in 1 Tests were performed on the arc ion plating apparatus shown and the following test results were obtained.

• (a) When the cemented carbide substrate was placed in the arc ion plating apparatus and the surface of the cemented carbide substrate was subjected to a pretreatment without the use of a cathode electrode under the following conditions of an atmospheric temperature in the apparatus (temperature of the cemented carbide substrate): 300 to 500 ° C, of an atmospheric gas : Ar, an atmospheric pressure: 1 to 10 Pa, an arc discharge current: (arc powder - off), a pre-pressure applied to the cemented carbide substrate: -800 to -1000 V, and a treatment time: 2 to 10 minutes, and then the surface of the A cemented carbide substrate is further subjected to a Lichtbo genionenplattierungsoberflächenbehandlung using metallic Ti as a cathode electrode under the following conditions: Atmospheric temperature in the device: 450 to 550 ° C; atmospheric gas: Ar; Atmospheric pressure: 1 to 10 Pa; Arc discharge current: 100 to 200 A; and pre-pressure applied to the cemented carbide substrate: -900 to -1200 V, a metallic Ti layer as a deposition layer is not formed on the surface of the cemented carbide substrate. The structure of the surface of the cemented carbide substrate itself is observed by means of a transmission electron microscope. As a result, the formation of an amorphous layer is detected. The formation of the metallic Ti layer by means of the arc ion plating apparatus is carried out under the following conditions: atmospheric temperature in the apparatus: 300 to 500 ° C; atmospheric gas: (not used); Atmospheric pressure: vacuum at 0.1 Pa or less; Cathode electrode: metallic Ti; Arc discharge current: 50 to 100 A, and applied to the cemented carbide substrate pre-pressure: -30 to -100 V.
• (b) In the state in which an amorphous layer is formed at an average depth of 1 to 50 nm from the surface when a wear resistant coating layer of the conventional coated cemented carbide tool is formed, when a (Ti, Al) N layer and a (Ti, Al) CN layer forming a hard surface layer of the conventional coated cemented carbide substrate is formed on the surface of the cemented carbide substrate having the amorphous layer formed on its surface by a titanium nitride (hereinafter referred to as TiN) having a Vickers hardness from 2000 to 2500 and markedly excellent toughness is formed by using the same arc ion plating apparatus, the amorphous layer reacts with the TiN layer as it is formed to be deposited because the amorphous layer has high activity and high reactivity, resulting in remarkably strong adhesion between the surface of the sinter carbid substrate and the TiN layer is ensured. Strong adhesion between the TiN layer and the surface coating layer is also ensured.
• (c) As a result, the coated cemented carbide tool thus obtained is free from peeling of the wear resistant coating layer composed of the TiN layer and the surface coating layer even when used in the batch cutting operation in combination with high mechanical and thermal effects under deep cutting conditions. Also, the toughness of the wear resistant coating layer itself is significantly improved by the presence of the TiN layer, and the occurrence of chipping of the cutting edge portion can be suppressed. Therefore, it becomes possible to obtain satisfactorily excellent wear resistance of the wear-resistant coating layer.

This invention has been accomplished on the basis of the above-described finding, and is characterized by a coated cemented carbide tool having a wear-resistant coating layer excellent in adhesion and chipping resistance, comprising: a tungsten carbide-based cemented carbide substrate having an amorphous layer formed by an arc ion plating surface treatment an average depth of 1 to 50 nm is formed from the surface; and a wear-resistant coating layer physically deposited on the surface of the tungsten carbide-based cemented carbide substrate, wherein the wear-resistant coating layer is composed of: (a) a tough primary layer consisting of a TiN layer and having an average thickness of 0.1 to 5 μm Has; and (b) a single-layer or multi-layered hard layer consisting of either or both of a (Ti, Al) N layer and a (Ti, Al) CN layer each having the compositional formula: (Ti _1-x Al _x ) N and the composition formula: (Ti _1-x Al _x ) C _{1 -y} N _y (where X is from 0.15 to 0.65 and Y is 0.5 to 0.99, in terms of atomic ratio) and has an average thickness of 0.5 to 15 μm.

The average thickness of the on the surface of the cemented carbide substrate formed amorphous layer containing the coated cemented carbide tool of the present invention was set to a range of 1 to 50 nm for the following reasons set. If indeed the depth is less than 1 nm, can the desired excellent adhesion be ensured between this and the TiN layer as a tough primary layer. In contrast, is the effect of improving the adhesion of the TiN layer to the Surface of the Sintercarbidsubstrats satisfactory when the average depth of the surface 50 nm.

In the coated cemented carbide tool of this invention, Al is incorporated in the (Ti, Al) N layer and the (Ti, Al) CN layer constituting the hard coating layer in TiCN in the form of a solid solution for the purpose of improving the hardness thereby improving the wear resistance. For this reason, the X value was set in a range of 0.15 to 0.65 (atomic ratio) for the following reason. Namely, when the X value in the composition formula: (Ti _1-x Al _x ) N and the composition formula: (Ti _1-x Al _x ) C _{1 -y} N _{y is} less than 0.15, the desired wear resistance can not be ensured become. In contrast, when the X value is larger than 0.65, chipping easily occurs in the cutting edge. Since the component C in the (Ti, Al) CN layer has the effect of improving the hardness, the (Ti, Al) CN layer has a relatively high hardness as compared with the (Ti, Al) N layer. When the amount of the component C is less than 0.01, that is, the Y value is larger than 0.99, a predetermined effect of improving the hardness can not be obtained. On the other hand, if the amount of the component C is greater than 0.5, ie, the Y value is less than 0.5, the toughness is rapidly reduced. Therefore, the Y value was set in a range of 0.5 to 0.99, and preferably 0.55 to 0.9.

Of the Reason why the average thickness of the hard surface layer to a range of 0.5 to 15 microns is set is the following. If the thickness is less than 0.5 microns, can the desired excellent wear resistance can not be ensured. In contrast, when the thickness is greater than 15 μm, Slight chipping occurs at the cutting edge.

Of the Reason why the average thickness of the tough bottom layer on one Range of 0.1 to 5 microns set was, is the following. If indeed the thickness is less than 1 μm is, let yourself not the desired one toughness at the wear resistant Ensure coating layer. On the other hand, if the thickness Exceeds 5 μm, it comes easily to a plastic deformation, which easily a causes unilateral wear in the wear resistant coating layer in discontinuous cutting operation under deep cutting conditions.

The Coated cemented carbide tool of this embodiment will be detailed described.

Example 4-1

The cemented carbide substrates A4-1 to A4-6, each having the shape of an insert as defined in ISO · SNGA120412, and cemented carbide substrates A4-7 to A4-10 each having a shape of insert as defined in ISO · SNMA120412, were prepared by molding WC powder, TiC powder, ZrC powder, VC powder, TaC powder, NbC powder, Cr ₃ C ₂ powder, TiN powder, TaN powder and Co Powder each having a predetermined mean grain size of 1 to 3 μm, compounding these raw powders according to each formulation in Table 1, wet-mixing them in a ball mill for 72 hours, drying the mixture, compacting the dried mixture under a pressure of 100 MPa Forming green sheets and vacuum-sintering these green sheets under the conditions of a vacuum degree of 6 Pa, a temperature of 1400 ° C for 1 hour and subjecting the cutting edge edge I made a grinding (R: 0.05).

These cemented carbide substrates A4-1 to A4-10 were subjected to ultrasonic cleaning in acetone, dried and thereafter placed in a conventional arc ion plating apparatus as in 1 and the surface of each of the cemented carbide substrates A4-1 to A4-10 was subjected to pretreatment under the following conditions:
Atmospheric temperature in the device (temperature of the cemented carbide substrate): 400 ° C,
atmospheric gas: Ar,
Atmospheric pressure: 3 Pa,
Cathode electrode: (not used),
Arc discharge current: (arc powder - off),
applied to the cemented carbide substrate pre-pressure: -900 V, and
Treatment time: 3 min,
and then subjected to an arc ion plating surface treatment under the following conditions:
Atmospheric temperature in the device: 500 ° C,
atmospheric gasL: Ar,
Atmospheric pressure: 3 Pa,
Cathode electrode: metallic Ti,
Arc discharge current: 150 A, and
applied to the cemented carbide substrate: -1000 V to thereby form an amorphous layer on the surface of the cemented carbide substrates A4-1 to A4-10. The depth of the amorphous layer formed on the surface thereof was adjusted by regulating the treatment time of the arc ion plating surface treatment under the conditions described above.

• (A) Unter Verwendung derselben Lichtbogenionenbeschichtungsvorrichtung wurde eine TiN-Schicht als zähe Primärschicht mit der in Tabelle 4-2 und Tabelle 4-3 gezeigten Zieldicke auf jeder Oberfläche der Sintercarbidsubstrate A4-1 bis A4-10 mit der auf der Oberfläche davon gebildeten amorphen Schicht unter den folgenden Bedingungen gebildet: Atmosphärentemperatur im Ofen: 500°C, atmosphärisches Gas: Stickstoffgas, Atmosphärendruck: 6 Pa, Kathodenelektrode: metallisches Ti, Lichtbogenentladungsstrom: 70 A, und auf das Sintercarbidsubstrat angewandter Vordruck: –50 V, und danach
• (B) wurde eine einschichtige oder mehrschichtige Schicht entweder aus einem oder beiden aus einer (Ti, Al)N-Schicht und einer (Ti, Al)CN-Schicht, welche die in Tabelle 4-2 und Tabelle 4-3 gezeigte Zielzusammensetzung und Zieldicke haben, auf der Oberfläche der TiN-Schicht unter den folgenden Bedingungen abgeschieden: Atmosphärentemperatur im Ofen: 500°C, atmosphärisches Gas: Stickstoffgas, Methangas oder Mischgas von Stickstoffgas und Methangas in einem vorbestimmten Verhältnis, Atmosphärendruck: 6 Pa, Kathodenelektrode: Ti-Al-Legierung mit unterschiedlichen Zusammensetzungen, Lichtbogenentladungsstrom: 70 A, und auf das Sintercarbidsubstrat angewandter Vordruck: –90 V, um dadurch die Einmaleinsätze aus einer beschichteten Carbidlegierung (im Folgenden als beschichtete Sintercarbideinsätze der vorliegenden Erfindung bezeichnet) 4-1 bis 4-20 herzustellen, welche eine Gestalt aufweisen, die in einer schematischen perspektivischen Ansicht von 2(A) und einer schematischen Längsschnittsdarstellung von 2(B) der vorliegenden Erfindung gezeigt ist.

The structure of the amorphous layer formed on the surface of the cemented carbide substrates A4-1 to A4-10 was observed by means of a transmission electron microscope (magnification: 500,000), and the evaluation and measurement were carried out on the basis of the observed results. As a result, the mean depths (average of the depths measured at five points) from the surface are shown in Tables 4-2 and 4-3, respectively.

• (A) Using the same arc ion plating apparatus, a TiN layer as a tough primary layer having the target thickness shown in Table 4-2 and Table 4-3 was formed on each surface of the cemented carbide substrates A4-1 to A4-10 with the amorphous layer formed on the surface thereof formed under the following conditions: atmospheric temperature in the oven: 500 ° C, atmospheric gas: nitrogen gas, atmospheric pressure: 6 Pa, cathode electrode: metallic Ti, arc discharge current: 70 A, and applied to the cemented carbide substrate pre-pressure: -50 V, and thereafter
• (B) was a single-layered or multi-layered layer of either one or both of a (Ti, Al) N layer and a (Ti, Al) CN layer having the target composition shown in Table 4-2 and Table 4-3 Target thickness, deposited on the surface of the TiN layer under the following conditions: atmospheric temperature in the oven: 500 ° C, atmospheric gas: nitrogen gas, methane gas or mixed gas of nitrogen gas and methane gas in a predetermined ratio, atmospheric pressure: 6 Pa, cathode electrode: Ti Al alloy with different compositions, arc discharge current: 70 A, and applied to the cemented carbide substrate pre-pressure: -90 V, thereby to produce the disposable inserts of a coated carbide alloy (hereinafter referred to as coated cemented carbide inserts of the present invention) 4-1 to 4-20 which have a shape which in a schematic perspective view of 2 (A) and a schematic longitudinal sectional view of 2 B) of the present invention.

To the A comparison was made, as shown in Table 4-4 and Table 4-5, disposable inserts a conventional one Coated cemented carbide (hereinafter referred to as conventional coated cemented carbide inserts) 4-1 to 4-20 each under the same conditions as described above except that the pretreatment and the arc ion plating surface treatment under the above conditions on the surface of the Cemented carbide substrates A4-1 to A4-10 in the arc ion plating apparatus not done and thus the amorphous layer did not on the surface of the Sintercarbidsubstrate A4-1 to A4-10 was present and the TiN layer as tough primary layer was not formed.

Tabelle 4-2

Tabelle 4-3

Tabelle 4-4

Tabelle 4-5

Tabelle 4-6

(* gibt an, dass das Versagen durch Absplitterung an der Schneidekante verursacht wurde, und ** gibt an, dass das Versagen durch Ablösen bei der abnutzungsbeständigen Beschichtungsschicht verursacht wurde.) Tabelle 4-7

(* gibt an, dass das Versagen durch Absplitterung an der Schneidekante verursacht wurde, und ** gibt an, dass das Versagen durch Ablösen bei der abnutzungsbeständigen Beschichtungsschicht verursacht wurde.)Subsequently, the coated cemented carbide inserts 4-1 to 4-20 of the present invention and the conventional coated cemented carbide inserts 4-1 to 4-20 were subjected to a dry-type discontinuous thickness-cutting-depth cutting test of an alloy steel under the following conditions:
Workpiece: JIS SCM439 round rod with four longitudinal grooves at equal intervals,
Cutting speed: 110 m / min,
Cutting depth: 5.0 mm
Feed: 0.2 mm / rev, and
Cutting time: 5 min,
subjected to a dry type discontinuous high-speed cutting test of an alloy steel under the following conditions:
Workpiece: JIS · SKD61 round rod with four longitudinal grooves equidistant from each other,
Cutting speed: 30 m / min,
Cutting depth: 1.4 mm,
Feed: 0.45 mm / rev, and
Cutting time: 2 min,
and a high-speed dry-type cutting test of a structural steel under the following conditions:
Workpiece: JIS · FC300 round rod with four longitudinal grooves equidistant from each other,
Cutting speed: 150 m / min,
Cutting depth: 7 mm,
Feed: 0.2 mm / rev, and
Cutting time: 3 min,
in the screwed state in the tip portion of a tool steel insert using a fixing tool clamping device. In all cutting tests, the edge wear width of the cutting edge was measured. The measurement results are listed in Table 4-6 and Table 4-7. Table 4-1

Table 4-2

Table 4-3

Table 4-4

Table 4-5

Table 4-6

(* indicates that the failure was caused by chipping at the cutting edge, and ** indicates that the failure was caused by peeling off the wear-resistant coating layer.) Table 4-7

(* indicates that the failure was caused by chipping at the cutting edge, and ** indicates that the failure was caused by peeling off the wear-resistant coating layer.)

Example 4-2

The cemented carbide substrates B4-1 to B4-8 for a face mill each having a size of 6 mm x 13 mm, 10 mm x 22 mm and 20 mm x 45 mm for diameter and length of the cutting edge area were made in accordance with the procedure shown in Table 4-8 Combination by preparing a WC powder of medium-grain grains having an average grain size of 5.5 μm, a WC powder of fine grains having an average grain size of 0.8 μm, a TaC powder having an average grain size of 1.3 μm , a NbC powder having a mean grain size of 1.2 μm, a ZrC powder having a mean grain size of 1.2 μm, a Cr ₃ C ₂ powder having a mean grain size of 2.3 μm, a VC powder having a mean grain size of 1.5 μm, a (Ti, W) C powder having a mean grain size of 1.0 μm and a co-powder having a average particle size of 1.8 microns, compounding these raw powders according to each of the formulations in Table 4-8, adding a wax, mixing them in acetone in a ball mill for 24 hours, drying the mixture under reduced pressure, compacting the dried mixture under one Pressure of 100 MPa to form green compacts, sintering these green compacts under conditions of heating to a predetermined temperature within a range of 1370 to 1470 ° C at a heating rate of 7 ° C / min in a vacuum atmosphere of 6 Pa, hold This temperature for 1 hour and cooling in the oven, whereby three types of sintered round bars for forming cemented carbide substrate each having a diameter of 8 mm, 13 mm and 26 mm were formed, and cutting three types of sintered round bars.

These cemented carbide substrates B4-1 to B4-8 were subjected to ultrasonic cleaning in acetone, dried, and then immersed in the same arc ion plating apparatus as in 1 and the surface of each of these cemented carbide substrates was subjected to the pretreatment and the arc ion plating surface treatment under the same conditions as in Example 1 to form an amorphous layer on the surface of the cemented carbide substrates B4-1 to B4-8. The depth of the amorphous layer formed on the surface thereof was also adjusted by controlling the treatment time of the arc ion plating surface treatment under the conditions described above.

The Structure of the surface the cemented carbide substrates B4-1 to B4-8 formed amorphous layer was measured using a transmission microscope (magnification: 500,000), and the rating and measurement were based on the results determined. As a result the mean depths (average of the mean measured at five points) Depths) from the surface in Table 4-9 and Table 4-10, respectively.

Using the same arc ion plating apparatus, a TiN layer as a tough primary layer having a target thickness as shown in Table 4-9 and Table 4-10 was deposited on the surface of these cemented carbide substrates, and then a single-layer or multi-layer hard surface layer was formed from either one or both a (Ti, Al) N layer and a (Ti, Al) CN layer having the target composition and target thickness shown in Table 4-9 and Table 4-10 formed thereon, whereby the face cutters of a surface-coated cemented carbide of the present invention Invention (hereinafter referred to as coated cemented carbide end mills of the present invention) 4-1 'to 4-16' were prepared as the coated cemented carbide tool of the present invention, which is a in a schematic front view of 3A and a schematic cross-sectional view of 3B having shown shape of the cutting edge region.

To the Comparison, as shown in Table 4-11 and Table 4-12, end mill from a conventional one Coated cemented carbide (hereinafter referred to as conventional coated cemented carbide end mills) 4-1 'to 4-16' as conventional coated cemented carbide tool under the same conditions manufactured as described above, with the exception that the pre-treatment and the arc ion plating surface treatment among the above conditions on the surface of the cemented carbide substrates B4-1 to B4-8 in the arc ion plating device not were carried out and therefore the amorphous layer is not on the surface of the Sintercarbidsubstrate B4-1 to B4-8 was present and the TiN layer as the tough one primary layer was not formed.

Subsequently, the coated cemented carbide end mills 4-1 'to 4-3' and 4-9 'to 4-11' of the present invention and the conventional coated cemented carbide end mills 4-1 'to 4-3' and 4-9 'were used. 4-11 'among the coated cemented carbide end mills 4-1' to 4-16 'of the present invention and the conventional coated cemented carbide end mills 4-1' to 4-16 ', a wet type thickness cutting side cutting test Cast iron subjected under the following conditions:
Workpiece: JIS FC300 plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Rotational speed: 5150 min ^-1
Cutting depth in the axial direction: 12 mm,
Cutting depth in the radial direction: 1.6 mm, and
Feeding: 600 mm / min.

The coated cemented carbide end mills 4-4 'to 4-6' and 4-12 'to 4-14' of the present invention and the conventional coated cemented carbide end mills 4-4 'to 4-6' and 4-12 'to 4 -14 'were subjected to a wet-type thickness-cutting side cutting test of a cast iron under the following conditions:
Workpiece: JIS · SNCM439 plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Rotational speed: 1900 min ^-1,
Cutting depth in axial direction: 20 mm
Cutting depth in the radial direction: 2.6 mm, and
Feeding: 270 mm / min.

The coated cemented carbide end mills 4-7 ', 4-8', 4-15 'and 4-16' of the present invention and the conventional coated cemented carbide end mills 4-7 ', 4-8', 4-15 'and 4 -16 'were subjected to a wet-type thickness-cutting side cutting test of a hardened steel under the following conditions:
Workpiece: JIS · SKD61 (hardness: HRC52) plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Rotation speed: 625 min ^-1 ,
Cutting depth in the axial direction: 26 mm
Cutting depth in the radial direction: 1.4 mm, and
Feed: 71 mm / min.

Tabelle 4-9

Tabelle 4-10

Tabelle 4-11

(* gibt an, dass das Versagen durch Absplitterung an der Schneidekante verursacht wurde, und ** gibt an, dass das Versagen durch Ablösen bei der abnutzungsbeständigen Beschichtungsschicht verursacht wurde.) Tabelle 4-12

(* gibt an, dass das Versagen durch Absplitterung an der Schneidekante verursacht wurde, und ** gibt an, dass das Versagen durch Ablösen bei der abnutzungsbeständigen Beschichtungsschicht verursacht wurde.)In all side cutting tests (water soluble drilling oil was used in all tests), the cut length was measured until the edge wear rate of the peripheral edge reached 0.1 mm as a life criterion. The measurement results are listed in Table 4-9 and Table 4-12. Table 4-8

Table 4-9

Table 4-10

Table 4-11

(* indicates that the failure was caused by chipping at the cutting edge, and ** indicates that the failure was caused by peeling off the wear-resistant coating layer.) Table 4-12

(* indicates that the failure was caused by chipping at the cutting edge, and ** indicates that the failure was caused by peeling off the wear-resistant coating layer.)

Example 4-3

Using three kinds of sintered round bars each having a diameter of 8 mm (for forming the cemented carbide substrates B4-1 to B4-3), a diameter of 13 mm (for forming the cemented carbide substrates B4-4 to B4-6) and 26 mm (for forming the cemented carbide substrates B4-7 to B4-8) prepared in Example 4-2, the cemented carbide substrates C4-1 to C4-8 for drills each having a size of 4 mm x 13 mm (cemented carbide substrates C4-1 to C4-3), 8 mm × 22 mm (cemented carbide substrates C4-4 to C4-6) and of 16 mm × 45 mm (cemented carbide substrates C4-7 to C4-8) for diameter and length of Chip groove made from these three types of sintered rods.

These cemented carbide substrates C4-1 to C4-8 were subjected to ultrasonic cleaning in acetone, dried, and then immersed in the same arc ion plating apparatus as in 1 and the surface of each of these cemented carbide substrates was subjected to the pretreatment and the arc ion plating surface treatment under the same conditions as in Example 1 to form an amorphous layer on the surface of the cemented carbide substrates C4-1 to C4-8. The depth of the amorphous layer formed on the surface thereof was also adjusted by controlling the treatment time of the arc ion plating surface treatment under the conditions described above.

The Structure of the surface the cemented carbide substrates C4-1 to C4-8 formed amorphous layer was measured by means of a transmission electron microscope (magnification: 500,000), and the rating and measurement were based on the results determined. As a result, the mean depths (average of the mean measured at five points) Depths) from the surface in Table 4-13 and Table 4-14, respectively.

Using the same arc ion plating apparatus as a tough primary layer, a TiN layer having a target thickness as shown in Table 4-13 and Table 4-14 was deposited on the surface of these cemented carbide substrates under the same conditions as in Example 1, followed by a single-layer or multilayer hard surface layer of either or both of a (Ti, Al) N layer and a (Ti, Al) CN layer having the target composition and target thickness shown in Table 4-13 and Table 4-14 formed thereon the surface-coated cemented carbide drills of the present invention (hereafter referred to as coated cemented carbide drills of the present invention) 4-1 "to 4-16" were fabricated as the coated cemented carbide tool of the present invention, which is a schematic front view of FIG 4A and a schematic cross-sectional view of 4B having shown shape of the chip groove.

To the Comparison, as shown in Table 4-15 and Table 4-16, End drill from a conventional one Coated cemented carbide (hereinafter referred to as conventional coated cemented carbide drills) 4-1 "to 4-16 '' as conventional coated cemented carbide tool under the same conditions manufactured as described above, with the exception that the pre-treatment and the arc ion plating surface treatment among the above conditions on the surface of the cemented carbide substrates C4-1 to C4-8 in the arc ion plating device not were carried out and therefore the amorphous layer is not on the surface of the Sintercarbidsubstrate C1-1 to C1-8 was present and the TiN layer as the tough one primary layer was not formed.

Subsequently, the coated cemented carbide drills 4-1 "to 4-3" and 4-9 "to 4-11" of the present invention and the conventional coated cemented carbide drills 4-1 "to 4-3 'were prepared. and 4-9 "to 4-11" among the coated cemented carbide drills 4-1 "to 4-16" of the present invention and the conventional coated cemented carbide drills 4-1 "through 4-16". subjected to a wet-type high load boring test of a cast iron under the following conditions:
Workpiece: JIS FC300 plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Cutting speed: 40 m / min,
Feed: 0.42 mm / div.

The coated cemented carbide drills 4-4 "to 4-6" and 4-12 "to 4-14" of the present invention and the conventional coated cemented carbide drills 4-4 "to 4-6" and 4-12 "to 4-14" were subjected to a wet-type high-load boring test of an alloy steel under the following conditions:
Workpiece: JIS · SSNCM439 plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Cutting speed: 40 m / min,
Feed: 0.37 mm / div.

The coated cemented carbide drills 4-7 ", 4-8", 4-15 "and 4-16" of the present invention and the conventional coated cemented carbide drills 4-7 ", 4-8", 4-15 "and 4-16" were subjected to a wet-type high-load drilling test of a hardened steel under the following conditions:
Workpiece: JIS · SKD61 (hardness: HRC53) plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Cutting speed: 24 m / min, and
Feeding: 0.36 mm / div.

Tabelle 4-14

Tabelle 4-15

(* gibt an, dass das Versagen durch Absplitterung an der Schneidekante verursacht wurde, und ** gibt an, dass das Versagen durch Ablösen bei der abnutzungsbeständigen Beschichtungsschicht verursacht wurde.) Tabelle 4-16

(* gibt an, dass das Versagen durch Absplitterung an der Schneidekante verursacht wurde, und ** gibt an, dass das Versagen durch Ablösen bei der abnutzungsbeständigen Beschichtungsschicht verursacht wurde.)In all wet type high load rigging tests (water soluble drilling oil was used in all tests), the number of drilled holes was measured until the edge wear surface's edge wear area reached 0.3 mm. The measurement results are listed in Table 4-13 and Table 4-16. Table 4-13

Table 4-14

Table 4-15

(* indicates that the failure was caused by chipping at the cutting edge, and ** indicates that the failure was caused by peeling off the wear-resistant coating layer.) Table 4-16

(* indicates that the failure was caused by chipping at the cutting edge, and ** indicates that the failure was caused by peeling off the wear-resistant coating layer.)

The Composition and the thickness of the hard coating layer of coated silicon carbide inserts 4-1 to 4-20 of the present invention, the coated cemented carbide end mills 4-1 'to 4-16' of the present invention Invention and the coated cemented carbide drills 4-1 '' to 4-16 '' of present invention as the coated cemented carbide tool of the present invention and the conventional coated cemented carbide inserts 4-1 to 4-20, the conventional ones coated cemented carbide end mill 4-1 'to 4-16' and the conventional coated cemented carbide drills 4-1 "to 4-16" as the conventional coated cemented carbide tool were determined by means of an energy dispersive X-ray measuring device, an Auger spectrometer and a scanning electron microscope. As a result, they showed the composition and the middle one Thickness (compared to an average of the thicknesses measured at five points), which are essentially the same as the target composition and the mean target thickness in Table 4-2 to Table 4-5 and Table 4-9 to Table 4-16.

Fifth embodiment

The fifth embodiment was used to produce a cutting tool for a surface-coated Carbide alloy performed, the adhesion a wear resistant Layer on the carbide alloy based on the findings (a) to (c) has been further improved as described above.

• (a) einer zähen Primärschicht, die aus einer TiN-Schicht besteht und eine mittlere Dicke von 0,1 bis 5 μm hat;
• (b) einer einschichtigen oder mehrschichtigen harten unteren Schicht, die entweder aus einer oder aus beiden aus einer (Ti, Al)N-Schicht und einer (Ti, Al)CN-Schicht besteht, welche jeweils der Zusammensetzungsformel: (Ti_1-xAl_x)N und der Zusammensetzungsformel: (Ti_1-xAl_x)C_1-yN_y genügen und eine mittlere Dicke von 0,5 bis 15 μm haben; und
• (c) einer einschichtigen oder mehrschichtigen harten oberen Schicht, die entweder aus einem oder beiden aus einer Al₂O₃-Schicht und einer Al₂O₃-ZrO₂-Mischschicht aus einer Matrix von Al₂O₃ und einer darin dispergierten und verteilten ZrO₂-Phase besteht und eine mittlere Dicke von 0,5 bis 10 μm hat.

This embodiment is characterized by a coated cemented carbide tool wherein a wear resistant coating layer thereof has excellent adhesion and chipping resistance, comprising:
a tungsten carbide-based cemented carbide substrate having an amorphous layer formed by an arc ion plating surface treatment at an average depth of 1 to 50 nm from the surface;
and a wear resistant coating layer physically and / or chemically deposited on the surface of the tungsten carbide based cemented carbide substrate, wherein the wear resistant coating layer is composed of:

• (a) a tough primary layer consisting of a TiN layer and having an average thickness of 0.1 to 5 μm;
• (b) a single-layered or multi-layered hard bottom layer consisting of either one or both of a (Ti, Al) N layer and a (Ti, Al) CN layer each having the compositional formula: (Ti _1-x Al _x ) N and the composition formula: (Ti _1-x Al _x ) C _{1 -y} N _y satisfy and have an average thickness of 0.5 to 15 microns; and
• (c) a single-layered or multi-layered hard top layer comprising either one or both of an Al ₂ O ₃ layer and an Al ₂ O ₃ -ZrO ₂ mixed layer of a matrix of Al ₂ O ₃ and one dispersed and dispersed therein ZrO ₂ phase and has an average thickness of 0.5 to 10 microns.

Of the Reason why the numerical limit performed as described above was re the on the surface the sintered carbide substrate formed amorphous layer and the wear-resistant coating layer in the coated cemented carbide tool of this invention explained below.

(1) Amorphous layer on the surface of the cemented carbide substrate

The amorphous layer has the effect of giving excellent adhesion between them and the wear-resistant coating layer (the tough primary layer) as described above. However, if the depth is less than 1 nm, the desired excellent adhesion between it and the TiN layer as the tough primary layer can not be ensured. On the other hand, the effect of improving the adhesion of the wear-resistant layer to the surface of the cemented carbide substrate is satisfactory when the average depth from the surface is 50 nm. Therefore, the average depth was set in a range of 1 to 50 nm.

(2) Tough primary layer

The tough primary layer has the effect of improving the toughness of the wear-resistant coating layer, whereby the occurrence of chipping in the wear-resistant coating layer even in discontinuous cutting operation, accompanied by high mechanical and thermal effects under deep cutting conditions as described above, is noticeably suppressed. If, however, the average thickness less than 0.1 μm is, let yourself not the desired one toughness at the wear resistant Ensure coating layer. On the other hand, if the middle one Thickness exceeds 5 μm, it comes easily to a plastic deformation, which easily a one-sided wear caused by the wear-resistant coating layer in discontinuous cutting operation under deep cutting conditions. Therefore, the average depth was set to a range of 0.1 to 5 μm.

(3) Hard bottom layer

The (Ti, Al) N layer and the (Ti, Al) CN layer forming the hard lower coating layer have the effect of imparting hardness and toughness to the wear-resistant coating layer, to thereby obtain excellent wear resistance without to cause chipping in the simultaneous presence of the lower coating layer. That is, Al in the hard lower layer is incorporated in TiN having a high toughness in the form of a solid solution for the purpose of improving the hardness, thereby improving the wear resistance. For this reason, the X value was set in a range of 0.15 to 0.65 (atomic ratio) for the following reason. Namely, when the X value in the composition formula: (Ti _1-x Al _x ) N and the composition formula: (Ti _1-x Al _x ) C _{1 -y} N _{y is} less than 0.15, the desired wear resistance can not be ensured become. On the other hand, when the X value is larger than 0.65, chipping tends to occur in the edge area. Since the component C in the (Ti, Al) CN layer has the effect of improving the hardness, the (Ti, Al) CN layer has a relatively high hardness as compared with the (Ti, Al) N layer. When the amount of the component C is less than 0.01, that is, the Y value is larger than 0.99, a predetermined effect of improving the hardness can not be obtained. On the other hand, if the amount of the component C is greater than 0.5, ie, the Y value is less than 0.5, the toughness is rapidly reduced. Therefore, the Y value was set in a range of 0.5 to 0.99, and preferably adjusted from 0.55 to 0.9.

If the average thickness is less than 0.5 μm, the desired can be excellent wear resistance can not be ensured. In contrast, if the thickness exceeds 15 μm, it comes easily to the occurrence of a chipping at the cutting edge. For this reason, the average thickness has been reduced to a range of 0.5 to 15 μm set.

(4) Hard upper layer

The Al ₂ O ₃ layer and the Al ₂ O ₃ -ZrO ₂ mixed layer forming the hard top layer have excellent hardness at a high temperature and heat resistance, and also have the effect of noticeably improving the wear resistant coating layer at the same time Presence of the lower coating layer described above. If the average thickness is less than 0.5 μm, the desired excellent wear resistance can not be ensured. In contrast, when the thickness exceeds 10 μm, chipping occurs easily in the wear-resistant coating layer. For this reason, the average depth was set in a range of 0.5 to 10 μm.

The Coated cemented carbide tools of this embodiment will be described in detail.

Example 5-1

The cemented carbide substrates A5-1 to A5-10 each having an insert shape as defined in ISO · SNGA120412 were prepared by preparing a WC powder, a TiC powder, a ZrC powder vers, a VC powder, a TaC powder, a NbC powder, a Cr ₃ C ₂ powder, a TiN powder, a TaN powder and a Co powder each having a predetermined mean grain size of 1 to 3 microns Compounding these raw powders according to each individual formulation in Table 5-1, wet blending them in a ball mill for 72 hours, drying the mixture, compacting the dried mixture under a pressure of 100 MPa to form unsintered greenware, vacuum-sintering these green forms under conditions of a vacuum degree of 6 Pa and a temperature of 1400 ° C for 1 hour and subjecting the cutting edge portion to a draw grinding (R: 0.05).

These cemented carbide substrates A5-1 to A5-10 were subjected to ultrasonic cleaning in acetone, dried, and then immersed in a conventional arc ion plating apparatus as in 1 and the surface of each of the cemented carbide substrates A5-1 to A5-10 was subjected to pretreatment under the following conditions:
Atmospheric temperature in the device (temperature of the cemented carbide substrate): 400 ° C,
atmospheric gas: Ar,
Atmospheric pressure: 3 Pa,
Cathode electrode: (not used),
Arc discharge current: (arc powder - off),
applied to the cemented carbide substrate pre-pressure: -900 V, and
Treatment time: 3 minutes, and then subjected to arc ion plating surface treatment under the following conditions:
Atmospheric temperature in the device: 500 ° C,
atmospheric gas: Ar,
Atmospheric pressure: 3 Pa,
Cathode electrode: metallic Ti,
Arc discharge current: 150 A, and
pre-pressure applied to the cemented carbide substrate: -1000 V to thereby form an amorphous layer on the surface of the cemented carbide substrates A5-1 to A5-10. The depth of the amorphous layer formed on the surface thereof was adjusted by regulating the treatment time of the arc ion plating surface treatment under the conditions described above.

• (A) Unter Verwendung der gleichen Lichtbogenionenbeschichtungsvorrichtung wurde eine TiN-Schicht als zähe Primärschicht mit der in Tabelle 5-3 und Tabelle 5-5 gezeigten Zieldicke auf jeder Oberfläche der Sintercarbidsubstrate A5-1 bis A5-10 mit der auf der Oberfläche davon gebildeten amorphen Schicht unter den folgenden Bedingungen abgeschieden: Atmosphärentemperatur im Ofen: 500°C, atmosphärisches Gas: Stickstoffgas, Atmosphärendruck: 6 Pa, Kathodenelektrode: metallisches Ti, Lichtbogenentladungsstrom: 70 A, und auf das Sintercarbidsubstrat angewandter Vordruck: –50 V, und anschließend
• (B) eine einschichtige oder mehrschichtige Schicht entweder aus einem oder beiden aus einer (Ti, Al)N-Schicht und einer (Ti, Al)CN-Schicht, welche die in Tabelle 5-3 und Tabelle 5-5 gezeigte Zielzusammensetzung und Zieldicke aufweisen, wurde auf der Oberfläche der TiN-Schicht unter den folgenden Bedingungen abgeschieden: Atmosphärentemperatur im Ofen: 500°C, atmosphärisches Gas: Stickstoffgas, Methangas oder Mischgas von Stickstoffgas und Methangas in einem vorbestimmten Verhältnis, Atmosphärendruck: 6 Pa, Kathodenelektrode: Ti-Al-Legierung mit verschiedenen Zusammensetzungen, Lichtbogenentladungsstrom: 70 A, und auf das Sintercarbidsubstrat angewandter Vordruck: –90 V, und darüber hinaus
• (C) eine Al₂O₃-Schicht mit Kristallstruktur vom α- oder κ-Typ mit der in Tabelle 5-4 und Tabelle 5-6 gezeigten Zielstruktur oder eine Al₂O₃-ZrO₂-Mischschicht als harte obere Schicht wurde auf der Oberfläche der harten unteren Schicht unter den gleichen Bedingungen wie in Tabelle 5-2 gezeigt abgeschieden unter Verwendung einer herkömmlichen chemischen Abscheidungsvorrichtung, um dadurch Einmaleinsätze aus einer beschichteten Carbidlegierung (im Folgenden als beschichtete Sintercarbideinsätze der vorliegenden Erfindung bezeichnet) 5-1 bis 5-20 herzustellen, welche eine Gestalt aufweisen, die in einer schematischen perspektivischen Ansicht von 2A und einer schematischen Längsschnittsdarstellung von 2B der vorliegenden Erfindung gezeigt ist.

The structure of the amorphous layer formed on the surface of the cemented carbide substrates A5-1 to A5-10 was observed by means of a transmission electron microscope (magnification: 500,000), and the evaluation and measurement were carried out on the basis of the observed results. As a result, the mean depths (average of the depths measured at five points) from the surface are shown in Table 5-3 and Table 5-5, respectively.

• (A) Using the same arc ion plating apparatus, a TiN layer as a tough primary layer having the target thickness shown in Table 5-3 and Table 5-5 was formed on each surface of the cemented carbide substrates A5-1 to A5-10 having the amorphous surface formed on the surface thereof Layer under the following conditions: atmospheric temperature in the oven: 500 ° C, atmospheric gas: nitrogen gas, atmospheric pressure: 6 Pa, cathode electrode: metallic Ti, arc discharge current: 70 A, and applied to the cemented carbide substrate pre-pressure: -50 V, and then
• (B) a monolayer or multilayer of either one or both of a (Ti, Al) N layer and a (Ti, Al) CN layer having the target composition and target thickness shown in Table 5-3 and Table 5-5 Atmospheric temperature in the furnace: 500 ° C, atmospheric gas: nitrogen gas, methane gas, or mixed gas of nitrogen gas and methane gas in a predetermined ratio, atmospheric pressure: 6 Pa, cathode electrode: TiO 2, was deposited on the surface of the TiN layer. Al alloy with various compositions, arc discharge current: 70 A, and applied to the cemented carbide substrate pre-pressure: -90 V, and beyond
• (C) An Al ₂ O ₃ layer having an α- or κ-type crystal structure with the target structure shown in Table 5-4 and Table 5-6 or an Al ₂ O ₃ -ZrO ₂ mixed layer as a hard upper layer the surface of the hard lower layer under the same conditions as shown in Table 5-2 deposited using a conventional chemical deposition apparatus, thereby disposable from a coated carbide alloy (hereinafter referred to as coated cemented carbide inserts of the present invention) 5-1 to 5-20, which have a shape which is in a schematic perspective view of 2A and a schematic longitudinal sectional view of 2 B of the present invention.

To the Comparison, as shown in Table 5-7 to Table 5-10, disposables a conventional one coated carbide alloy (hereinafter referred to as conventional coated cemented carbide inserts 5-1 to 5-20 each under the same conditions manufactured as described above, with the exception that the pre-treatment and the arc ion plating surface treatment among the above Conditions on the surface the cemented carbide substrates A5-1 to A5-10 in the arc ion plating apparatus not done and thus the amorphous layer was not on the surface of the cemented carbide substrates A5-1 to A5-10 was formed and also the TiN layer as a tough primary layer was not formed.

Tabelle 5-2

Tabelle 5-3

Tabelle 5-4

Tabelle 5-5

Tabelle 5-6

Tabelle 5-7

Tabelle 5-8

(* gibt an, dass das Versagen durch Absplitterung an der Schneidekante verursacht wurde, und ** gibt an, dass das Versagen durch Ablösen bei der abnutzungsbeständigen Beschichtungsschicht verursacht wurde.) Tabelle 5-9

Tabelle 5-10

(* gibt an, dass das Versagen durch Absplitterung an der Schneidekante verursacht wurde, und ** gibt an, dass das Versagen durch Ablösen bei der abnutzungsbeständigen Beschichtungsschicht verursacht wurde.)Subsequently, the coated cemented carbide inserts 5-1 to 5-20 of the present invention and the conventional coated cemented carbide inserts 5-1 to 5-20 were subjected to a dry-type discontinuous thickness-cutting-depth cutting test of an alloy steel under the following conditions:
Workpiece: JIS · SNCM439 round rod with four longitudinal grooves at equal intervals,
Cutting speed: 130 m / min,
Cutting depth: 5 mm
Feed: 0.19 mm / rev, and
Cutting time: 5 min,
a discontinuous high-speed dry-type cutting test of a structural steel under the following conditions:
Workpiece: JIS · SKD61 round rod with four longitudinal grooves equidistant from each other,
Cutting speed: 35 m / min,
Cutting depth: 1.6 mm,
Feed: 0.45 mm / rev, and
Cutting time: 5 min,
and a dry type discontinuous thickness-cutting test for a ductile cast iron under the following conditions:
Workpiece: JIS · FCD500 rod with four longitudinal grooves equidistant from each other,
Cutting speed: 160 m / min,
Cutting depth: 7 mm,
Feed: 0.15 mm / rev, and
Cutting time: 5 minutes, screwed into the tip portion of a tool steel insert using a fixture tool clamping device. In all cutting tests, the edge wear width of the cutting edge was measured. The measurement results are listed in Table 5-4, Table 5-6, Table 5-8, and Table 5-10. Table 5-1

Table 5-2

Table 5-3

Table 5-4

Table 5-5

Table 5-6

Table 5-7

Table 5-8

(* indicates that the failure was caused by chipping at the cutting edge, and ** indicates that the failure was caused by peeling off the wear-resistant coating layer.) Table 5-9

Table 5-10

(* indicates that the failure was caused by chipping at the cutting edge, and ** indicates that the failure was caused by peeling off the wear-resistant coating layer.)

Example 5-2

The cemented carbide substrates B5-1 to B5-8 for a face milling cutter each having a size of 6 mm × 13 mm, 10 mm × 22 mm and 20 mm × 45 mm for diameter and length of the cutting edge area were in According to the combination shown in Table 5-11, by preparing a medium grain size WC powder having a mean grain size of 5.5 μm, a WC powder of fine grains having an average grain size of 0.8 μm, a TaC powder having a mean grain size of 1.3 μm, a NbC powder having a mean grain size of 1.2 μm, a ZrC powder having a mean grain size of 1.2 μm, a Cr ₃ C ₂ powder having an average grain size of 2.3 μm, a VC powder having an average particle size of 1.5 μm, a (Ti, W) C powder having a mean particle size of 1.0 μm and a Co powder having a mean particle size of 1.8 μm, compounding these raw powders according to each of the formulations in Table 5-8, adding a wax, mixing them in acetone in a ball mill for 24 hours, drying the mixture under reduced pressure, patting the dried mixture under a pressure of 100 MPa e.g. For forming green sheets, sintering these green sheets under conditions of heating to a predetermined temperature within a range of 1370 to 1470 ° C at a heating rate of 7 ° C / min in a vacuum atmosphere of 6 Pa, keeping at this temperature for 1 hour and cooling in the furnace, thereby forming three kinds of sintered round bars for forming cemented carbide substrates each having a diameter of 8 mm, 13 mm and 26 mm, and cutting three types of sintered round bars.

These cemented carbide substrates B5-1 to B5-8 were subjected to ultrasonic cleaning in acetone, dried, and then immersed in the same arc ion plating apparatus as in 1 and the surface of each of these cemented carbide substrates was subjected to the pretreatment and the arc ion plating surface treatment under the same conditions as in Example 1 to form an amorphous layer on the surface of the cemented carbide substrates B5-1 to B5-8. The depth of the amorphous layer formed on the surface thereof was also adjusted by controlling the treatment time of the arc ion plating surface treatment under the conditions described above.

The Structure of the surface the cemented carbide substrates B5-1 to B5-8 formed amorphous layer was measured by means of a transmission electron microscope (magnification: 500,000), and the rating and measurement were based on the results determined. As a result, the mean depth (average of the mean measured at five points) Depths) from the surface shown in Table 5-12 and Table 5-14, respectively.

Using the same arc ion plating apparatus, a TiN layer as a tough primary layer having a target thickness as shown in Table 5-12 and Table 4-14 was deposited on the surface of these cemented carbide substrates under the same conditions as in Example 1, followed by a single-layered or multi-layered hard lower layer either of one or both of a (Ti, Al) N layer and a (Ti, Al) CN layer having the target composition and target thickness shown in Table 5-12 and Table 5-14 formed on the surface thereof and also an Al ₂ O ₃ layer having an α- or κ-type crystal structure having the target structure shown in Table 5-13 and Table 5-15 or an Al ₂ O ₃ -ZrO ₂ mixed layer as a hard upper layer deposited on the surface of the hard bottom layer under the same conditions as shown in Example 5-2 using a conventional chemical deposition apparatus; whereby the surface-coated carbide alloy end mills of the present invention (hereinafter referred to as coated cemented carbide end mills of the present invention) were fabricated 5-1 'to 5-16' as the coated cemented carbide tool of the present invention, which is a schematic front view of FIG 3A and a schematic cross-sectional view of 3B having shown shape of the cutting edge region.

To the Comparison, as shown in Table 5-16 and Table 5-19, end mill from a conventional one coated carbide alloy (hereinafter referred to as conventional coated cemented carbide end mills) 5-1 'to 5-16' as conventional coated cemented carbide tool under the same conditions manufactured as described above, with the exception that the pre-treatment and the arc ion plating surface treatment among those above conditions on the surface of the cemented carbide substrates B5-1 to B5-8 in the arc ion plating device not were carried out and therefore, the amorphous layer was on the surface of the cemented carbide substrates B5-1 to B5-8 are absent and also the TiN layer as the tough primary layer was not formed.

Subsequently, the coated cemented carbide end mills 5-1 'to 5-3' and 5-9 'to 5-11' of the present invention and the conventional coated cemented carbide end mills 5-1 'to 5-3' and 5-9 'were prepared. 5-11 'among the coated cemented carbide end mills 5-1' to 5-16 'of the present invention and the conventional coated cemented carbide end mills 5-1' to 5-16 'are a wet type depth cutting side cutting test Cast iron subjected under the following conditions:
Workpiece: JIS FC300 plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Rotation speed: 5300 min ^-1,
Cutting depth in the axial direction: 12 mm,
Cutting depth in the radial direction: 1.6 mm, and
Feed: 585 mm / min.

The coated cemented carbide end mills 5-4 'to 5-6' and 5-12 'to 5-14' of the present invention and the conventional coated cemented carbide end mills 5-4 'to 5-6' and 5-12 'to 5 -14 'were subjected to a wet-type thickness-cutting side cutting test of an alloy steel under the following conditions:
Workpiece: JIS · SNCM439 plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Rotational speed: 2100 min ^-1
Cutting depth in axial direction: 20 mm
Cutting depth in the radial direction: 2.6 mm, and
Feeding: 250 mm / min.

The coated cemented carbide end mills 5-7 ', 5-8', 5-15 'and 5-16' of the present invention and the conventional coated cemented carbide end mills 5-7 ', 5-8', 5-15 'and 5 -16 'were subjected to a wet-type thickness-cutting side cutting test of a hardened steel under the following conditions:
Workpiece: JIS · SKD61 (hardness: HRC52) plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Rotation speed: 650 min ^-1 ,
Cutting depth in the axial direction: 26 mm
Cutting depth in the radial direction: 1.4 mm, and
Feeding: 68 mm / min.

Tabelle 5-12

Tabelle 5-13

Tabelle 5-14

Tabelle 5-15

Tabelle 5-16

Tabelle 5-17

(* gibt an, dass das Versagen durch Absplitterung an der Schneidekante verursacht wurde, und ** gibt an, dass das Versagen durch Ablösen bei der abnutzungsbeständigen Beschichtungsschicht verursacht wurde.) Tabelle 5-18

Tabelle 5-19

(* gibt an, dass das Versagen durch Absplitterung an der Schneidekante verursacht wurde, und ** gibt an, dass das Versagen durch Ablösen bei der abnutzungsbeständigen Beschichtungsschicht verursacht wurde.)In all side cutting tests (water soluble drilling oil was used in all tests), the cut length was measured until the edge wear rate of the peripheral edge reached 0.1 mm as a life criterion. The measurement results are listed in Table 5-13, Table 5-15, Table 5-17 and Table 5-19. Table 5-11

Table 5-12

Table 5-13

Table 5-14

Table 5-15

Table 5-16

Table 5-17

(* indicates that the failure was caused by chipping at the cutting edge, and ** indicates that the failure was caused by peeling off the wear-resistant coating layer.) Table 5-18

Table 5-19

(* indicates that the failure was caused by chipping at the cutting edge, and ** indicates that the failure was caused by peeling off the wear-resistant coating layer.)

Example 5-3

Under Use of three types of sintered round rods, each with a diameter of 8 mm (to form the cemented carbide substrates B5-1 to B5-3), a diameter of 13 mm (to form the cemented carbide substrates B5-4 to B5-6) and 26 mm (to form the cemented carbide substrates B5-7 to B5-8) prepared in Example 5-2 became the Cemented carbide substrates C5-1 to C5-8 for 4-size drills each mm × 13 mm (cemented carbide substrates C5-1 to C5-3), 8 mm × 22 mm (cemented carbide substrates C5-4 to C5-6) and 16 mm x 45 mm (Cemented carbide substrates C5-7 to C5-8) for the diameter and length of the chip groove made from these three types of sintered rods.

These cemented carbide substrates C5-1 to C5-8 were subjected to ultrasonic cleaning in acetone, dried, and then immersed in the same arc ion plating apparatus as in 1 and the surface of each of these cemented carbide substrates was subjected to the pretreatment and the arc ion plating surface treatment under the same conditions as in Example 1 to form an amorphous layer on the surface of the cemented carbide substrates C5-1 to C5-8. The depth of the amorphous layer formed on the surface thereof was also adjusted by controlling the treatment time of the arc ion plating surface treatment under the conditions described above.

The Structure of the surface the cemented carbide substrates C5-1 to C5-8 formed amorphous layer was measured by means of a transmission electron microscope (magnification: 500,000), and the rating and measurement were based on the results determined. As a result, the mean depth (average of the mean measured at five points) Depths) from the surface shown in Table 5-20 and Table 5-22, respectively.

Using the same arc ion plating apparatus, a TiN layer as a tough primary layer having a target thickness as shown in Table 5-13 and Table 5-14 was deposited on the surface of these cemented carbide substrates under the same conditions as in Example 1, followed by a single-layered or multi-layered hard bottom layer either of one or both of a (Ti, Al) N layer and a (Ti, Al) CN layer having the target composition and target thickness shown in Tables 5-20 and 5-22 formed on the surface thereof and Further, an Al ₂ O ₃ layer having an α- or κ-type crystal structure having the target structure shown in Table 5-21 and Table 5-23, or a Al ₂ O ₃ -ZrO ₂ mixed layer as a hard top layer on the surface of the hard bottom layer under the same conditions as shown in Example 5-2 using a conventional chemical deposition apparatus, whereby the surface coated carbide alloy drills of the present invention ( hereinafter referred to as coated cemented carbide drills of the present invention) 5-1 "to 5-16" were produced as the coated cemented carbide tool of the present invention, which is a schematic front view of FIG 4A and a schematic cross-sectional view of 4B having shown shape of the chip groove.

To the Comparison, as shown in Table 5-24 to Table 5-27, End drill from a conventional coated carbide alloy (hereinafter referred to as conventional coated cemented carbide drills) 5-1 "to 5-16 '' as conventional coated cemented carbide tool under the same conditions manufactured as described above, with the exception that the pre-treatment and the arc ion plating surface treatment among the above conditions on the surface of the cemented carbide substrates C5-1 to C5-8 in the arc ion plating device not were carried out and therefore the amorphous layer is not on the surface of the Sintercarbidsubstrate C1-1 to C1-8 was present and the TiN layer as the tough one primary layer was not formed.

Subsequently, the coated cemented carbide drills were 5-1 "to 5-3" and 5-9 "to 5-11" of the present invention and the conventional coated cemented carbide drills 5-1 "to 5-3 '. 'and 5-9''to5-11''among the coated cemented carbide drills 5-1''to5-16''of the present invention and the conventional coated cemented carbide drills 5-1''to5-16' subjected to a wet-type high load boring test of a cast iron under the following conditions:
Workpiece: JIS FC300 plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Cutting speed: 48 m / min,
Feed: 0.40 mm / div.

The coated cemented carbide drills 5-4 '' to 5-6 '' and 5-12 '' to 5-14 '' of the present invention and the conventional coated cemented carbide drills 5-4 '' to 5-6 '' and 5-12 "to 5-14" were subjected to a wet-type high-load boring test of an alloy steel under the following conditions:
Workpiece: JIS · SNCM439 plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Cutting speed: 50 m / min,
Feeding: 0.38 mm / div.

The coated cemented carbide drills 5-7 '', 5-8 '', 5-15 '' and 5-16 '' of the present invention and the conventional coated cemented carbide drills 5-7 '', 5-8 '', 5-15 "and 5-16" were subjected to a wet-type high-load drilling test of a hardened steel under the following conditions:
Workpiece: JIS · SKD61 (hardness: HRC53) plate with a planar size of 100 mm × 250 mm and a thickness of 50 mm,
Cutting speed: 30 m / min, and
Feed: 0.34 mm / div.

Tabelle 5-21

Tabelle 5-22

Tabelle 5-23

Tabelle 5-24

Tabelle 5-25

(* gibt an, dass das Versagen durch Absplitterung an der Schneidekante verursacht wurde, und ** gibt an, dass das Versagen durch Ablösen bei der abnutzungsbeständigen Beschichtungsschicht verursacht wurde.) Tabelle 5-26

Tabelle 5-27

(* gibt an, dass das Versagen durch Absplitterung an der Schneidekante verursacht wurde, und ** gibt an, dass das Versagen durch Ablösen bei der abnutzungsbeständigen Beschichtungsschicht verursacht wurde.)In all wet-type high load drilling tests (water-soluble drill oil was used in all tests), the number of drilled holes was measured until the edge wear width of the tip edge surface reached 0.3 mm. The measurement results are listed in Table 5-21, Table 5-23, Table 5-25 and Table 5-27. Table 5-20

Table 5-21

Table 5-22

Table 5-23

Table 5-24

Table 5-25

(* indicates that the failure was caused by chipping at the cutting edge, and ** indicates that the failure was caused by peeling off the wear-resistant coating layer.) Table 5-26

Table 5-27

(* indicates that the failure was caused by chipping at the cutting edge, and ** indicates that the failure was caused by peeling off the wear-resistant coating layer.)

The Composition and the thickness of the hard coating layer of coated cemented carbide inserts 5-1 to 5-20 of the present invention, the coated cemented carbide end mills 5-1 'to 5-16' of the present invention Invention and the coated cemented carbide drills 5-1 '' to 5-16 '' of present invention as the coated cemented carbide tool of the present invention and the conventional coated cemented carbide inserts 5-1 to 5-20, the conventional ones coated cemented carbide end mill 5-1 'to 5-16' and conventional coated cemented carbide drills 5-1 "to 5-16" as the conventional coated cemented carbide tool were using an energy-dispersive X-ray measuring device, a Auger spectrometer and a scanning electron microscope. As a result, they showed the composition and the middle one Thickness (compared to an average of the thicknesses measured at five points), essentially with the target composition and the middle one Target Thickness in Table 5-3 to Table 5-10 and Table 5-12 to Table 5-27 match.

Claims (5)

Cutting tool, which consists of a surface-coated Carbide alloy consists of their wear-resistant coating layer an excellent adhesion comprising: a tungsten carbide based carbide alloy substrate, which has an amorphous layer formed by an arc ion plating surface treatment is formed at an average depth of 1 to 50 nm, as the outermost layer the substrate surface; and a wear-resistant Coating layer chemically and / or physically on the surface of the tungsten carbide-based carbide alloy substrate is wherein the wear resistant coating layer comprises a layer or a plurality of two or more layers, the selected be from the group, which consists of a layer of a carbide of Ti, a layer of a nitride of Ti, a layer of a carbonitride of Ti, a layer of a carboxy of Ti and a layer of a carbonic oxide of Ti, and in which the wear-resistant Coating layer has a thickness of 1 to 15 microns. A surface-coated carbide alloy cutting tool according to claim 1, modified to replace the wear-resistant coating layer defined in claim 1 by: a monolayer or multilayer hardcoat layer physically deposited on the surface of the tungsten carbide-based carbide alloy substrate, wherein the monolayer or multilayer hardcoat layer is either one or both of a composite nitride layer of Ti and Al and a composite carbonitride layer of Each of Ti and Al satisfies the compositional formulas: (Ti _1-x Al _x ) N and the compositional formula: (Ti _1-x Al _x ) C _{1 -y} N _y (where X is 0.15 to 0.65 and Y is 0.5 to 0.99 in terms of atomic ratio), and wherein the single-layered or multi-layered hard coating layer has an average thickness of 0.5 to 15 μm. The cutting tool made of a surface-coated carbide alloy according to claim 1, wherein the wear-resistant coating layer is physically deposited on the surface of the tungsten carbide-based carbide alloy substrate and comprises: a primary hard layer made of a titanium nitride layer and modified such that the average thickness of the wear-resistant coating layer is from 0.1 to 5 μm; and wherein the cutting tool further comprises a single-layer or multi-layer hard surface layer made of either one or both of a composite nitride layer of Ti and Al and a composite carbinitride layer of Ti and Al each having the compositional formula: (Ti _1-x Al _x ) N and the composition formula: (Ti _1-x Al _x ) satisfy C _1-y N _y (wherein X represents 0.15 to 0.65 and Y represents 0.5 to 0.99 as the atomic ratio ), and wherein the single-layered or multi-layered hard coating layer has an average thickness of 0.5 to 15 μm. Made of a surface-coated Carbide alloy produced cutting tool according to claim 1 to the effect modified that the average thickness of the wear resistant coating layer 0.5 to 15 μm is, the Cutting tool further comprising: an upper coating layer, which either from one or both of an aluminum oxide layer and an alumina-zirconia mixed layer is made of a matrix of alumina and a dispersed and dispersed zirconia phase, and wherein the single-layered or multi-layered hard coating layer has an average thickness of 0.5 to 15 microns. Made of a surface-coated Carbide alloy produced cutting tool according to claim 3, in addition full a single-layered or multi-layered upper hard Layer consisting of either one or both of an aluminum oxide layer and an alumina-zirconia mixed layer, which consists of a matrix of alumina and a dispersed therein and distributed zirconium oxide phase is prepared, the single-layered or multi-layered upper hard layer a middle one Thickness of 0.5 to 10 microns having.