JP2008207286A - Wear-resistant member and cutting tool using it - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a long-life wear-resistant member having excellent wear-resistance, which restrains components of a base body from diffusing into its coating layer formed by a chemical vapor deposition method (CVD) to reduce the strength of the coating layer. <P>SOLUTION: The wear-resistant member comprises a base body and a coating layer formed on the base body. The base body contains a hard phase having, in major proportions, at least one of tungsten carbide, titanium carbide, titanium nitride, and titanium carbonitride and a binding phase containing at least one of Co and Ni. The coating layer is formed in contact with the base body and equipped with a first layer containing at least 25 atomic percentage of Al element and a second layer formed on the first layer by a chemical vapor deposition method. <P>COPYRIGHT: (C)2008,JPO&INPIT

Description

  The present invention relates to a wear-resistant member having a coating layer formed by a chemical vapor deposition method.

  Conventionally, wear-resistant members having a coating layer formed on the surface of a substrate have been used for various purposes. For example, a cutting tool widely used for metal cutting has a coating layer such as a TiC layer, a TiN layer, a TiCN layer, an Al2O3 layer, and a TiAlN layer on a surface of a substrate such as cemented carbide, cermet, or ceramic. A tool in which a layer or a plurality of layers are formed is frequently used. Among them, in the turning of general steel, a multilayer film formed by chemical vapor deposition (CVD) with good throwing power and high layer thickness uniformity is suitably used. For example, in Patent Document 1, on a surface of a tungsten carbide-based cemented carbide substrate, a granular titanium nitride (TiN) layer having an average layer thickness of 0.1 to 5 μm—titanium carbonitride having a vertically grown crystal structure having an average layer thickness of 2 to 15 μm. Hard coating layer composed of (l-TiCN) layer-aluminum oxide (Al2O3) layer having an average layer thickness of 0.5 to 10 [mu] m-titanium carbide (l-TiC) layer having an average growth thickness of 2 to 10 [mu] m A surface-coated tungsten carbide-based cemented carbide cutting tool is disclosed. With such a configuration, the l-TiC layer has substantially the same fracture surface structure as the l-TiC layer, so that it has excellent toughness and therefore exhibits excellent wear resistance. Has been.

  Further, in Patent Document 2, a granular titanium nitride (TiN) layer having an average layer thickness of 0.1 to 2 μm and a vertically grown crystal structure carbon having an average layer thickness of 0.5 to 3 μm is formed on the surface of the tungsten carbide base cemented carbide substrate. Titanium oxynitride (l-TiCNO) layer-titanium carbonitride (l-TiCN) layer with an average growth thickness of 2 to 20 μm and a granular carbon structure with an average layer thickness of 0.05 to 2 μm A cutting tool made of a surface-coated tungsten carbide-based cemented carbide comprising a hard coating layer composed of an aluminum oxide (Al2O3) layer having a granular crystal structure of (TiCNO) layer—average layer thickness of 0.2 to 15 μm is disclosed. With such a configuration, it is disclosed that the TiN layer, which is the first layer, can prevent the diffusion movement of the constituent components of the cemented carbide substrate into the hard coating layer, thereby suppressing the wear resistance deterioration of the hard coating layer. . Further, by forming an l-TiCNO layer as an upper layer of the TiN layer and forming an l-TiCN layer thereon, an l-TICN layer having a finer crystal structure can be formed, and excellent wear resistance is exhibited. It is disclosed.

Further, in Patent Document 3, the binder phase constituent component of the substrate diffuses into the hard coating layer on the surface of the titanium carbonitride-based cermet containing the binder phase forming component mainly composed of Co and Ni, and the strength of the hard coating layer is increased. In order to suppress the decrease, it is described that a titanium nitride (TiN) layer is formed to a thickness of 0.5 μm to 5 μm.
JP 2000-158207 A JP-A-11-172464 Japanese Patent Laid-Open No. 04-289003

  However, since the coating layers described in Patent Documents 1 and 2 are formed by a chemical vapor deposition method in which the film is formed at a high temperature of about 1000 ° C., the components of the substrate diffuse into the coating layer, and the original coating layer is formed. The strength of was not obtained.

  In particular, a base material composed of a fine hard phase with a large amount of binder phase or a base material with a large amount of carbon contained makes the base material more easily diffused. Therefore, the coating described in Patent Documents 2 and 3 is applied to such a base material. Even if the layer was formed, it was not possible to suppress the binder phase component and carbon of the base from diffusing into the coating layer, and the strength of the coating layer was significantly reduced. As a result, the wear resistance and fracture resistance inherent in the coating layer formed by the chemical vapor deposition method could not be fully exhibited.

  Further, in the cermet-based cutting tool described in Patent Document 3, the coating layer is also formed at a high temperature, so that even if a TiN layer is formed as a diffusion preventing layer, diffusion of the components of the substrate is sufficiently suppressed. I couldn't.

  Further, when a layer containing carbon, particularly a TiCN layer made of a columnar structure, is to be formed on a substrate made of a cermet using a binder phase containing Ni as in the cermet-based cutting tool described in Patent Document 3. Further, there is a problem that Ni as a constituent component of the substrate diffuses into the coating layer and reacts with a reaction gas at the time of film formation to cause film formation failure. Therefore, in a substrate made of cermet using a binder phase containing Ni, it is difficult to form a carbon-containing layer such as a TiCN layer made of a columnar structure without abnormal growth as a coating layer. Therefore, it has been difficult to improve wear resistance by forming a carbon-containing layer including a TiCN layer made of a columnar structure as a coating layer in a cutting tool made of a cermet substrate.

  Accordingly, the present invention has been made to solve the above-described problems, and the object thereof is to reduce the strength of the coating layer by diffusing the components of the substrate into the coating layer formed by chemical vapor deposition (CVD). It is an object of the present invention to provide a long-life wear-resistant member that suppresses the above and has excellent wear resistance.

  Therefore, the present inventor forms a first layer containing a large amount of Al element as a layer in contact with the substrate as a coating layer formed on the substrate, and forms at least one layer thereon by a CVD method. It has been found that the binder phase component and carbon of the substrate can be more effectively suppressed from diffusing into the coating layer.

  That is, the wear-resistant member of the present invention is a wear-resistant member comprising a base and a layer formed on the base, and the base includes tungsten carbide, titanium carbide, titanium nitride, and A hard phase mainly composed of one or more types of titanium carbonitride, and a binder phase containing one or more types of Co and Ni, wherein the layer is formed in contact with the substrate, and includes an Al element. Is a wear-resistant member comprising a first layer containing 25 atomic% or more and a second layer formed on the first layer by chemical vapor deposition.

  Here, the first layer is made of AlN, AlON, (Ti, Al) N, (Al, M) N, (Ti, Al, M) N: (M is a Group 4, 5, 6 metal excluding Ti. It is desirable to use any one of element and one or more elements selected from Si.

  Moreover, it is desirable that the thickness of the first layer be 0.5 to 2 μm.

  Furthermore, it is desirable that the first layer is a layer formed by physical vapor deposition.

  The hard phase of the substrate preferably has an average particle diameter of 1 μm or less.

  Furthermore, the base is made of a titanium-based cermet having a binder phase containing at least Ni and a hard phase mainly composed of a titanium compound, and the second layer has a layer containing carbon. Is desirable.

  In addition, the carbon-containing layer of the second layer preferably includes a TICN layer having a columnar structure.

  Furthermore, the second layer preferably includes a TiN layer formed adjacent to the first layer.

  Moreover, it is desirable to use the above wear-resistant member as a cutting tool.

  According to the wear resistant member of the present invention, as the coating layer formed on the substrate, the first layer formed in contact with the substrate contains the Al element in an amount of 25 atomic% or more. When the second layer, which is the upper layer of the first layer, is formed, the role of a barrier layer that suppresses the diffusion of the components contained in the substrate, in particular, the components of carbon and the binder phase. Therefore, film formation defects due to diffusion of the base component can be suppressed, and a coating layer having high strength and high hardness can be obtained.

  Here, the first layer is made of AlN, AlON, (Ti, Al) N, (Al, M) N, (Ti, Al, M) N: (M is a Group 4, 5, 6 metal excluding Ti. 1 or more elements selected from Si and Si) is sufficient for cutting the adhesive force, strength, and hardness of the first layer, and further bonds the substrate. It is desirable because it can sufficiently suppress the diffusion of phases and carbon.

  Moreover, it is desirable that the thickness of the first layer be 0.5 to 2 μm because diffusion of the components of the substrate can be sufficiently suppressed and a decrease in the toughness of the film can be suppressed. .

  Furthermore, since the first layer is a layer formed by physical vapor deposition, the first layer is formed at a low temperature of 700 ° C. or less, and therefore, the components of the substrate are difficult to diffuse in the layer in contact with the substrate. It can be formed in a state. Therefore, the layer in contact with the substrate can be a layer in which the component of the substrate is not diffused, and the component of the substrate is diffused in the second layer formed as the upper layer of the coating layer in contact with the substrate. The effect which suppresses doing can be improved. In addition, since the first layer is composed of finer particles than the layer formed by the CVD method, the gap in which the base component enters the first layer is reduced, and the base component is contained in the coating layer. This is desirable because the effect of suppressing the diffusion to the surface is further improved.

  In addition, when the hard phase of the substrate is a fine particle having an average particle size of 1 μm or less, the diffusion can be sufficiently suppressed, and an abrasion-resistant member having both a strong substrate and a coating layer is obtained. be able to.

  Furthermore, the substrate is made of a titanium-based cermet having at least Ni as a binder phase and a hard phase mainly composed of a titanium compound, and the second layer has a layer containing carbon. , Preventing Ni in the binder phase from diffusing into the layer containing carbon, suppressing a decrease in strength of the coating layer, and suppressing reaction with Ni, thereby reducing abnormal growth of the layer containing carbon. it can.

  In addition, the carbon-containing layer of the second layer is a TiCN layer having a columnar structure, so that excellent wear resistance can be exhibited by the high toughness of the TiCN layer having a columnar structure.

  Furthermore, the second layer is desirable because it has a TiN layer formed adjacent to the first layer, thereby further improving the effect of diffusing the components of the substrate.

  Further, by using the above wear-resistant member as a cutting tool, a cutting tool that exhibits a long life and excellent cutting performance is obtained.

  FIG. 1A is a schematic overall perspective view of a throwaway tip type cutting tool used for turning as an example of an embodiment of an abrasion resistant member according to the present invention, and FIG. Based on

  According to FIG. 1, a throw-away tip (hereinafter simply abbreviated as “tip”) 1 uses an abrasion-resistant member having a base 2 and a coating layer 8 formed on the base 2. The surface is a flat plate shape in which the rake face 3 and the seating face 4 are formed, and the side face forms the flank 5. Then, a cutting edge 6 is formed at the intersecting ridge line between the rake face 3 and the flank face 5.

  The substrate 2 is a superstructure in which a hard phase mainly composed of tungsten carbide (WC) is bonded with a binder phase mainly composed of one or more iron group metals of cobalt (Co) and nickel (Ni). It consists of a hard alloy or a cermet in which a hard phase mainly composed of at least one of titanium carbide, titanium nitride and titanium carbonitride is bonded in a binder phase containing at least Ni.

  Next, the coating layer 8 formed on the surface of the substrate 2 is composed of a multilayer film including a layer formed by chemical vapor deposition (CVD).

  Here, according to the present invention, the covering layer 8 is composed of a first layer 9 in contact with the substrate 2, a second layer 10 formed on the first layer 9 by chemical vapor deposition, and The chip is characterized in that 25 atomic% or more of Al element is present in the first layer 9.

  Since Al element has low affinity with carbon, it does not easily react with carbides or substances in which carbon is dissolved. Therefore, even if the first layer 9 which is the layer closest to the substrate 2 contains a certain amount or more of Al element, even if the substrate 2 is in a high temperature state when the second layer 10 is formed, carbide or It is possible to prevent the component of the substrate 2 having a binder phase in which carbon is dissolved in the second layer 10 from diffusing.

  That is, by containing 25 atomic% or more of Al element in the first layer 9, it is possible to reduce the occurrence of abnormal particles and defects in the coating layer 8 due to diffusion of the base 2 components in the coating layer 8. . As a result, a decrease in strength and hardness of the coating layer 8 can be suppressed.

  In other words, when the amount of Al element contained in the first layer 9 is 25 atomic% or more, the affinity between the first layer 9 and the base 2 component is reduced, and the base 2 component is covered. Diffusion into the layer 8 can be suppressed.

  In addition, the amount of Al element contained in the first layer 9 is 75 atomic% or less, particularly 50 atomic% or less in that it exhibits excellent wear resistance while maintaining the hardness of the first layer 9. More preferably.

  In the present embodiment, the first layer 9 is composed of one layer. However, the first layer 9 satisfying the above configuration may be composed of a plurality of layers. Thus, when the 1st layer 9 consists of multiple layers, what is necessary is just to make it the atomic% of Al element in the multiple layers whole satisfy | fill the value mentioned above. That is, when the Al element contained in the layer formed between the second layer 10 formed by the CVD method and the substrate is 25 atomic% or more, the function as a barrier layer can be exhibited.

  Here, the first layer 9 is made of AlN, AlON, (Ti, Al) N, (Al, M) N, (Ti, Al, M) N: (M is a Group 4, 5, 6 metal excluding Ti. 1 or more elements selected from Si and Si) improves the adhesion, strength and hardness of the first layer, and further suppresses the binder phase component and carbon diffusion of the substrate. This is desirable because it can enhance the effect. In particular, since (Ti, Al) N and (Al, M) N are both high in hardness and strength, and the film characteristics do not change even at a high temperature of about 1000 degrees, the upper layer of the first layer 9 Even at a high temperature when a certain second layer 10 is formed by the CVD method, the characteristics of the first layer 9 do not change. Therefore, the effect of suppressing the diffusion of the components of the substrate can be further enhanced. Therefore, the wear-resistant member according to the present invention can exhibit excellent wear resistance even under severer cutting conditions including high-speed cutting, and thus can be suitably used as a cutting tool.

  Moreover, when the layer thickness of the first layer 9 is in the range of 0.5 to 2 μm, particularly 0.5 to 1 μm, the effect of suppressing the diffusion of the components of the substrate 2 is enhanced, and the toughness of the film is increased. This is desirable because the decrease can be suppressed.

  Further, by forming the first layer 9 by physical vapor deposition (PVD), which has a lower film formation temperature than chemical vapor deposition (CVD), the first layer 9 is formed in a state in which the components of the substrate 2 are difficult to diffuse. The components of the base 2 are not diffused to the first layer 9 when the first layer 9 is formed, and the components of the base 2 are diffused when the second layer 10 is formed. The effect of suppressing increases. Further, when the film is formed by the PVD method, it can be constituted by finer particles than the coating layer formed by the CVD method, and therefore, a gap in which the components of the base 2 enter the first layer 9 formed by the PVD method. This is desirable because the effect of suppressing the diffusion of the components of the substrate 2 into the coating layer is further improved.

  Here, the PVD method usable in the present invention includes an ion plating method, a sputtering method, plating, vapor deposition, and the like. In particular, it is desirable to form the first layer 9 by an ion plating method or a sputtering method because the first layer 9 having high adhesion to the substrate 2 and difficult to peel off can be formed.

  Further, since the hard phase of the substrate 2 is a fine particle having an average particle size of 1 μm or less, the thickness of the binder phase in the substrate 2 increases, and the contact area between the coating layer 8 and the binder phase increases. It is possible to suppress the binder phase and carbon in the substrate 2 from being easily diffused into the coating layer 8. In addition, the strength and hardness of the substrate 2 can be improved. As a result, it is possible to realize a wear-resistant member that has both the suppression of diffusion of the base 2 component into the covering layer 8 and the provision of the strong base 2 and the covering layer 8.

  Furthermore, the substrate 2 is composed of a titanium-based cermet having a binder phase containing at least Ni and a hard phase mainly composed of a titanium compound, and the second layer 10 reacts with Ni to generate abnormal grains. Even when forming a layer containing carbon easily, for example, a layer made of (titanium carbide), titanium carbonitride (TiCN), titanium carbonitride oxide (TiCNO), etc. Since the first layer 9 containing Al element can exhibit an excellent effect as a diffusion preventing layer (barrier layer), it prevents the Ni in the binder phase from diffusing into the second layer, and causes abnormal grains on the cermet substrate. The second layer 10 containing carbon that is not contained can be obtained. Therefore, in addition to the high wear resistance of the cermet substrate, the wear resistance can be further improved by the excellent hardness of the carbon-containing layer.

  In particular, by using a TiCN layer composed of a columnar structure having high toughness for the carbon-containing layer of the second layer 10, in addition to high wear resistance, the fracture resistance is improved by a tough hard film. be able to.

  The TiCN layer having a columnar structure referred to here is a layer containing columnar TiCN particles. In particular, it is more preferable to have TiCN particles having a high aspect ratio in terms of excellent toughness.

  The second layer 10 includes a titanium nitride (TiN) layer 11 formed adjacent to the first layer 9, so that the TiN layer 11 cannot be suppressed by the first layer 9. And the adhesion of the coating layer 8 can be improved. As a result, it is desirable because film peeling of the coating layer 8 can be suppressed.

  In the present embodiment, the covering layer 8 is exemplified by a form in which the first layer 9 and the second layer 10 are formed adjacent to each other. However, the present invention is not limited to this. Another layer may be formed between the second layer 19 and the second layer 19. That is, a layer that does not contain Al element in the above ratio and is formed by the PVD method (intermediate layer) is formed between the first layer 9 and the second layer 10. Also good.

  As such an intermediate layer, various types of layers such as a TiN layer and a TiCN layer can be used. In particular, the TiN layer formed by the PVD method is interposed between the first layer 9 and the second layer 10 as an intermediate layer, thereby reducing the diffusion of the two components of the substrate into the second layer 10. In addition, it is desirable in that the effect of improving the adhesion of the coating layer 8 is achieved.

  When the TiN layer is formed as a layer adjacent to the first layer 9, the form having the TiN layer 11 formed by the CVD method is applied to the covering layer 8 as in the above-described embodiment. This is more preferable because the adhesion force is large and film peeling of the coating layer 8 can be further reduced.

  Moreover, although the cutting tool was demonstrated here as an example, the performance which was excellent also as an abrasion-resistant material and a cutting blade can be exhibited as another use.

(Production method)
An example of a method for producing the cutting tool, which is an example of the wear-resistant member of the surface covering according to the present invention, will be described.

  First, metal powder, carbon powder, and the like are appropriately added to and mixed with inorganic powders such as metal carbide, nitride, carbonitride, and oxide that can form the above-described substrate by firing to obtain a mixed powder. The obtained mixed powder is molded into a predetermined tool shape by a known molding method such as press molding, casting molding, extrusion molding, or cold isostatic pressing. The obtained molded body is fired in a vacuum or in a non-oxidizing atmosphere, so that the substrate 2 made of the hard alloy described above is produced.

  Then, the first layer 9 is formed on the surface of the substrate 2. For example, the first layer 9 can be formed by a PVD method, specifically, an arc ion plating method. According to the present invention, as a film formation condition using the arc ion plating method, for example, when a (Ti, Al) N layer is formed as the first layer 9, the gas pressure during film formation is 2 to 5 Pa, The bias voltage is controlled to 20 to 300 V, and the film forming temperature is controlled to 500 to 600 ° C.

  As described above, by forming the first layer 9 by the PVD method, it is possible to maintain the temperature of the substrate at the time of forming the first layer 9 at a lower temperature than in the case of the CVD method. The effect of suppressing the diffusion of the base 2 components into the coating layer 8 is enhanced.

  Here, according to the present invention, the bias voltage at the time of film formation is set to 15 to 50 V only for an initial period of about 1 minute, and in the subsequent film formation, the bias voltage is changed to 150 to 300 V, whereby the first layer 9 These particles have a finer crystal structure, and the effect of suppressing the diffusion of the components of the substrate 2 into the coating layer 8 is further improved.

  Further, in particular, nitrogen having a flow rate ratio of nitrogen to an inert gas of 2: 1 to 30: 1, preferably 2: 1 to 10: 1 as a reaction gas introduced during film formation It is desirable to introduce the mixed gas of the inert gas into the vacuum chamber in which the plasma is generated because the inert gas can be stably contained in the first layer 9. When a plurality of types of inert gases are used, the ratio between the flow rate of nitrogen and the total flow rate of the plurality of types of inert gases is adjusted to the above ratio.

The target to be used is a titanium aluminum alloy having a composition (x: 0.5 to 0.7) made of (Ti _x , Al _1-x ).

  Here, the component of the target is an alloy having a composition such as (Al, M), (Ti, Al, M), etc. (M is one or more selected from Group 4, 5, 6 metals and Si in the periodic table excluding Ti) By changing to (element), various types of films can be formed.

  When forming the AlN layer as the first layer 9, for example, aluminum is used as a target, the film forming temperature is 300 to 800 ° C., the bias voltage is −5 to −100 V, the arc current value is 150 A, nitrogen It is performed under film forming conditions where the atmospheric pressure is 3 to 12 Pa.

On the other hand, when the first layer 9 is formed by the CVD method, for example, when an AlN layer is formed as the first layer 9 by the CVD method, ₃ to 20% by volume of AlCl ₃ gas and 0.1% of HCl gas are added. 5 to 8.0% by volume, N ₂ gas is 0.1 to 60% by volume, H ₂ S gas is 0 to 1% by volume, and the balance is H ₂ gas. 10 kPa is desirable.

Further, when an AlON layer is formed as the first layer 9 by the CVD method, AlCl ₃ gas is 1 to 10% by volume, HCl gas is 2 to 15% by volume, CO ₂ gas is 1 to 10% by volume, N Using a mixed gas composed of 3 to 20% by volume of ₂ gas and the remainder of H2 gas, a film is formed under film forming conditions of a film forming temperature of 900 ° C. to 1100 ° C. and a furnace pressure of 5 to 10 kPa.

  Next, the second layer 10 is formed on the substrate on which the first layer 9 is formed by the CVD method. The second layer 10 here may be a single layer or a plurality of layers. It can select suitably according to the use of an abrasion-resistant member. In the wear-resistant member used for a cutting tool, it is preferable that the second layer 10 includes a plurality of layers having a plurality of layers made of different chemical species. As a result, the wear resistance and fracture resistance can be improved.

First, when forming a TiN layer as the second layer 10, the reaction gas composition is titanium chloride (TiCl ₄ ) gas 0.1 to 10% by volume, nitrogen (N ₂ ) gas 0 to 60% by volume, A mixed gas consisting of hydrogen (H ₂ ) gas is prepared and introduced into the reaction chamber, and the inside of the chamber is formed under conditions of 800 to 1000 ° C. and 10 to 30 kPa.

Next, when a TiCN layer having a columnar structure is formed as the second layer 10, the reaction gas composition is 0.1 to 10% by volume of titanium chloride (TiCl ₄ ) gas and nitrogen (N ₂ ) in volume%. 20 to 60% by volume of gas, 0 to 0.1% by volume of methane (CH ₄ ) gas, 0.1 to 0.4% by volume of acetonitrile (CH ₃ CN) gas, and the remainder from hydrogen (H ₂ ) gas The mixed gas is adjusted and introduced into the reaction chamber, and film formation is performed at a film formation temperature of 780 to 880 ° C. and 5 to 25 kPa.

Next, when forming a TiCNO layer as the second layer 10, titanium chloride (TiCl ₄ ) gas is 0.1 to 3% by volume, methane (CH ₄ ) gas is 0.1 to 10% by volume, carbon dioxide. (CO ₂ ) gas is 0.01 to 5% by volume, nitrogen (N ₂ ) gas is 0 to 60% by volume, and the remainder is hydrogen (H ₂ ) gas, and is introduced into the reaction chamber. The inside of the chamber is set to 800 to 1100 ° C. and 5 to 30 kPa.

When forming an Al ₂ O ₃ layer as the second layer 10, aluminum chloride (AlCl ₃ ) gas is 3 to 20% by volume, hydrogen chloride (HCl) gas is 0.5 to 3.5% by volume, Carbon dioxide (CO ₂ ) gas is used in a mixed gas of 0.01 to 5% by volume, hydrogen sulfide (H ₂ S) gas is 0 to 0.01% by volume, and the remainder is hydrogen (H ₂ ) gas. It is desirable to set it as 1100 degreeC and 5-10kPa.

  Further, the second TiN layer 10 (11) described above is preferably formed adjacent to the first layer 9 as shown in FIG.

  The raw materials are mixed and pulverized in the proportions shown in Table 3, and formed into a cutting tool shape (CNMA120204) by press molding, then subjected to binder removal treatment, and fired at 1500 ° C. for 1 hour in a vacuum of 0.01 Pa. A substrate was prepared. Further, the prepared cemented carbide substrate was subjected to blade edge processing (R honing) from the rake face by brushing.

Next, a coating layer composed of a plurality of layers having the structure shown in Table 3 was formed on the cemented carbide substrate. 01 to 16 cutting tools were produced. The film forming conditions for each layer in Table 3 are shown in Table 1 for the CVD method and Table 2 for the PVD method. Here, the content ratio (atomic%) of the Al element in each layer in Tables 1 and 2 is the ratio of the Al element to the elements including all of the metal elements and non-metal elements constituting each layer, and the measurement is performed using a general XPS. It was measured by (X-ray photoelectron spectroscopy) method.

  About the obtained tool, the average particle diameter of the particle | grains which comprise the hard phase of a base | substrate was performed according to CIS-019D-2005. The results are shown in Table 3 as “WC particle size”.

  In addition, a scanning electron microscope (SEM) photograph was taken at a magnification of 3000 times at five arbitrary fractured surfaces including the cross section of the coating layer, the layer thickness of each layer in each photograph was measured, and the measured layer thicknesses at five locations Tables 3 and 5 show the average of the average layer thickness.

  Furthermore, the cross section was measured arbitrarily at three points by the wavelength dispersion type X-ray microanalyzer (WDS) for the amount of the component (W, Co, C) of the substrate existing in the entire second layer, and the average value was calculated. . The results are shown in Table 3.

Furthermore, among the obtained tools, the content ratio of the Al element in the entire first layer was measured for those in which the first layer was composed of a plurality of layers. The results are shown in Table 3. In addition, although it overlaps with the value shown in Table 1 and Table 3 also about what a 1st layer is comprised by a single layer, it showed in Table 3 collectively.

  Then, using this cutting tool, a continuous cutting test and an intermittent cutting test were performed under the following conditions to evaluate the wear resistance and fracture resistance. The results are shown in Table 4.

(Continuous cutting conditions)
Work material: Ductile cast iron (FCD700 sleeve material)
Tool shape: CNMG120408
Cutting speed: 250 m / min Feeding speed: 0.3 mm / rev
Cutting depth: 1.5mm
Cutting time: 30 minutes Others: Use of water-soluble cutting fluid Evaluation item: Observe cutting edge with microscope and measure flank wear and boundary wear (intermittent cutting conditions)
Work material: Ductile cast iron (FCD7004 grooved sleeve material)
Tool shape: CNMG12041
Cutting speed: 150 m / min Feeding speed: 0.2 mm / rev
Cutting depth: 1mm
Other: Use of water-soluble cutting fluid Evaluation item: Number of impacts leading to breakage
Observe the peeling state of the coating layer of the cutting edge with a microscope when the number of impacts is 1000

  From Tables 1-4, sample No. in which a layer containing 25 atomic% or more of Al element is not formed as the first layer. In Nos. 13 to 16, the base component diffuses into the coating layer, and as a result, the strength of the coating layer decreases, and both wear resistance and fracture resistance are low.

  On the other hand, sample No. which is within the scope of the present invention. In Nos. 1 to 12, the components of the substrate hardly diffused in the coating layer, and excellent performance in both wear resistance and fracture resistance is exhibited.

  The raw materials were mixed and pulverized in the proportions shown in Table 5 and formed into a cutting tool shape (CNMA120204) by press molding, then subjected to binder removal treatment, and fired at 1500 ° C. for 1 hour in a vacuum of 0.01 Pa for a cermet substrate Was made. Further, the prepared cermet substrate was subjected to blade edge processing (Honing R) from the rake face by brushing.

  Next, a coating layer composed of a plurality of layers having the structure shown in Table 5 was formed on the cermet substrate. 17 to 32 cutting tools were produced. As in the case of Example 1, Table 1 and Table 2 were used as the film forming conditions for each layer in Table 5.

  For the obtained tool, as in Example 1, measurement of the particle size of the hard phase of the substrate and scanning electron microscope (SEM) photographs were taken at five arbitrary fractured surfaces including the cross section of the coating layer. The thickness of each layer was measured.

In addition, the amount of the component (Co, Ni) of the substrate present in the entire second layer was measured for the cross section with a wavelength dispersive X-ray microanalyzer (WDS). The results are shown in Table 5.

  Then, using this cutting tool, a continuous cutting test and an intermittent cutting test were performed under the following conditions to evaluate the wear resistance and fracture resistance. The results are shown in Table 6.

(Continuous cutting conditions)
Work material: Ductile cast iron (FCD700 sleeve material)
Tool shape: CNMG12041
Cutting speed: 300 m / min Feeding speed: 0.2 mm / rev
Cutting depth: 1.5mm
Cutting time: 30 minutes Others: Dry evaluation items: Observe the cutting edge with a microscope and measure the flank wear and boundary wear (intermittent cutting conditions)
Work material: Ductile cast iron (FCD7004 grooved sleeve material)
Tool shape: CNMG12041
Cutting speed: 200 m / min Feed speed: 0.2 mm / rev
Cutting depth: 1mm
Others: Dry evaluation items: Number of impacts that lead to defects
Observe the peeling state of the coating layer of the cutting edge with a microscope when the number of impacts is 1000

  From Tables 5 and 6, Sample No. in which a layer containing 25 atomic% or more of Al element is not formed as the first layer. In Nos. 29 to 32, the components of the substrate are diffused in the coating layer. As a result, the coating layer grows abnormally, the strength of the coating layer is lowered, and both the wear resistance and the fracture resistance are low.

  On the other hand, sample No. which is within the scope of the present invention. In Nos. 13 to 28, the components of the substrate hardly diffused in the coating layer, and almost no defects were observed in the coating layer. Therefore, excellent performance in both wear resistance and fracture resistance was exhibited.

It is (a) general | schematic whole perspective view about the throw away tip which is an example of the abrasion-resistant member of this invention, (b) It is a principal part expanded sectional view.

Explanation of symbols

1: Throw away tip (chip)
2: Substrate 3: Rake face 4: Seating face 5: Flank face 6: Cutting edge 8: Coating layer 9: First layer 10: Second layer

Claims (9)

A wear-resistant member comprising a substrate and a coating layer formed on the substrate,
The substrate is
A hard phase mainly composed of one or more of tungsten carbide, titanium carbide, titanium nitride, and titanium carbonitride;
A binder phase containing one or more of Co and Ni,
The coating layer is
A first layer formed in contact with the substrate and containing 25 atomic% or more of Al element;
And a second layer formed on the first layer by chemical vapor deposition.   The first layer is made of AlN, AlON, (Ti, Al) N, (Al, M) N, (Ti, Al, M) N: (M is a Group 4, 5, 6 metal element excluding Ti, Si The wear-resistant member according to claim 1, comprising at least one element selected from the group consisting of one or more elements selected from: The wear-resistant member according to claim 1 or 2, wherein the first layer has a thickness of 0.5 to 2 µm. The wear-resistant member according to any one of claims 1 to 3, wherein the first layer is a layer formed by physical vapor deposition. The wear resistant member according to any one of claims 1 to 4, wherein the hard phase of the substrate has an average particle size of 1 µm or less.   The base is made of a titanium-based cermet having a binder phase containing at least Ni and a hard phase mainly composed of a titanium compound, and the second layer has a layer containing carbon. The wear-resistant member according to any one of claims 1 to 5.   The wear-resistant member according to claim 6, wherein the carbon-containing layer of the second layer includes a TiCN layer having a columnar structure.   The wear-resistant member according to any one of claims 1 to 7, wherein the second layer has a TiN layer formed adjacent to the first layer. A cutting tool using the wear-resistant member according to claim 1.

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