JP5087427B2 - Hard coating for cutting tools - Google Patents

Description

  TECHNICAL FIELD The present invention relates to a hard film for a cutting tool that covers a tool used for cutting of hard steel and the like.

  Conventionally, TiN, TiCN, or TiAlN has been used as a hard wear-resistant coating for coating metal cutting tools. In particular, TiAlN-based coatings represented by Patent Document 1 and Patent Document 2 are improved in hardness and heat resistance by adding Al to TiN, and work on steel materials including hardened steel because of their good wear resistance. It is widely used as a hard coating for cutting tools.

  However, in recent years, a tool for realizing cutting of a material with higher hardness has been demanded, and cutting as disclosed in Patent Document 3 and Patent Document 4 in which a TiAlN-based film and a TiSiN-based film are laminated. Hard coatings for tools have been proposed.

JP-A 62-56565 Japanese Patent Laid-Open No. 2-194159 Japanese Patent No. 3248897 Japanese Patent No. 3248898

  However, in the cutting of high hardness hardened steel represented by high-speed steel, the hard coating for cutting tools with higher wear resistance is not sufficient even with the above-mentioned conventional Si-containing multilayer coating. Development is required.

  In view of the present situation as described above, the present inventors have studied the film structure, the film layer structure and the film composition in the hard film for cutting tools, and as a result, devised the film structure, the film layer structure and the film composition. As a result of the knowledge that the above-mentioned problems can be solved, the wear resistance in cutting of hardened steel represented by high-speed steel is improved compared to conventional hard coatings for cutting tools. The present invention provides a hard coating for a cutting tool that is extremely practical.

  The gist of the present invention will be described.

A hard film for a cutting tool formed on a substrate, the hard film including a multilayer film layer in which two or more first film layers and second film layers are alternately laminated, coating layer is a coating layer contain inevitable impurities include N as a non-metal component and at least Al and Cr as metal components, non-metallic and at least Ti and Si the second coating layer is a metal and metalloid components A film layer containing N as an ingredient and containing inevitable impurities, the film thickness of each of the first film layer and the second film layer is set to 1 nm or more and 20 nm or less, and the multilayer film layer is formed by a cross-sectional TEM method. when viewed, the a component of the first coating layer and the component of the second coating layer is present mixed tissue section having a tissue mixed with 5% of the cross-sectional area of the area of the mixed tissue section the multilayer coating layer More than 80% Those of the hard film for a cutting tool to.

Further, in the hard film for a cutting tool according to claim 1, the first film layer has an atomic% metal and metalloid component,
Al (100-xyz) Cr (x) V (y) B (z)
However, 20 ≦ x ≦ 40, 2 ≦ y ≦ 15, 2 ≦ z ≦ 15
And the second coating layer is an atomic% metal and metalloid component,
Ti (100-vw) Cr (v) Si (w)
However, 5 ≦ v ≦ 30, 5 ≦ w ≦ 30
It is based on the hard film | membrane for cutting tools characterized by these.

  The hard coating for a cutting tool according to any one of claims 1 and 2, wherein a third coating layer is provided between the base material and the multilayer coating layer, and the metal component of the third coating layer Alternatively, the metal component and the metalloid component are the same as the metal component or the metal component and the metalloid component of the first coating layer, and the hard coating for a cutting tool is characterized.

  Further, in the hard coating for a cutting tool according to any one of claims 1 to 3, a fourth coating layer is provided immediately above the base material, and the fourth coating layer is a nitride mainly composed of Ti or It is made of carbonitride, and the film thickness of the fourth coating layer is related to a hard coating for a cutting tool, which is set to 0.01 μm to 0.5 μm.

  Further, in the hard coating for a cutting tool according to any one of claims 1 to 3, a fourth coating layer is provided immediately above the base material, and the fourth coating layer is a nitride containing Cr as a main component or It is made of carbonitride, and the film thickness of the fourth coating layer is related to a hard coating for a cutting tool, which is set to 0.01 μm to 0.5 μm.

  Further, in the hard film for a cutting tool according to any one of claims 1 to 5, a fifth film layer is provided on a surface layer side of the multilayer film layer, and a metal component and a semimetal component of the fifth film layer. Is the same as the metal component and the semi-metal component of the second coating layer, and relates to a hard coating for a cutting tool.

  Further, in the hard film for a cutting tool according to any one of claims 1 to 5, a fifth film layer is provided on a surface layer side of the multilayer film layer, and the metal component or metal component of the fifth film layer and The metalloid component is the same as the metal component of the first coating layer or the metal component and the metalloid component.

  The hard film for a cutting tool according to any one of claims 1 to 7, wherein the base material is a cemented carbide composed of hard particles mainly containing WC and a binder mainly containing Co. According to the hard coating for a cutting tool, the average particle diameter of the WC particles is set to 0.1 μm to 2 μm, and the Co content is set to 5 to 15% by weight%. Is.

  Since the present invention is configured as described above, the interlaminar adhesion between the first coating layer and the second coating layer is enhanced, and the high hardness firing typified by high-speed steel as compared with the conventional hard coating for cutting tools. It becomes a hard coating for cutting tools with excellent practicality that improves wear resistance in cutting of steel.

  The preferred embodiment of the present invention will be briefly described by showing the operation of the present invention.

  A multi-layer coating layer in which the first coating layer and the second coating layer are mixed in the interlayer portion between the first coating layer and the second coating layer (the first coating layer and the first coating layer as shown in FIGS. The second coating layer is not clearly distinguished, and there is a portion where the components of the first coating layer and the second coating layer are mixed), so the bond between the first coating layer and the second coating layer is strong. As a result, the interlayer adhesion is enhanced, and the abrasion resistance to high hardness hardened steel represented by high speed steel is improved.

  Specific embodiments of the present invention will be described with reference to the drawings.

  The present example is a hard coating for a cutting tool formed on a substrate, and this hard coating is a multilayer coating layer in which two or more first coating layers and second coating layers are alternately laminated. The first coating layer is a coating layer containing at least Al and Cr as metal components, N as a non-metallic component and unavoidable impurities, and the second coating layer includes at least Ti and Si as metal and metalloid components. Is a coating layer containing N as a non-metallic component and containing inevitable impurities, and the thickness of each of the first coating layer and the second coating layer is set to 1 nm or more and 20 nm or less, and the multilayer coating layer is When observed by a cross-sectional TEM method, there is a mixed structure part in which the first film layer and the second film layer are mixed, and the area of the mixed structure part is 5% or more and 80% of the cross-sectional area of the multilayer film layer. It is as follows.

  Each part will be specifically described.

  As the base material, a cemented carbide alloy composed of hard particles mainly composed of WC (tungsten carbide) and a binder mainly composed of Co (cobalt) is employed. Specifically, the average particle diameter of the WC particles is set to 0.1 μm to 2 μm, and the Co content is set to 5 to 15% by weight.

  A fourth coating layer made of a nitride or carbonitride containing Ti (titanium) as a main component is provided immediately above the base material. The film thickness of the fourth coating layer is set to 0.01 μm to 0.5 μm. Note that a nitride or carbonitride containing Cr (chromium) as a main component may be employed as the fourth coating layer. In this case, the film thickness is preferably set to 0.01 μm to 0.5 μm.

  A third coating layer is provided on the fourth coating layer. The metal component or metal component and metalloid component of the third coating layer are set to be the same as the metal component or metal component and metalloid component of the first coating layer. In the present embodiment, as will be described later, the first coating layer includes a metal component and a metalloid component, and the metal component and the metalloid component of the third coating layer are combined with the metal component and the metalloid component of the first coating layer. Is set to be the same.

  In this embodiment, a multilayer coating layer formed by alternately laminating the first coating layer and the second coating layer is provided on the third coating layer.

The first film layer is atomic% of metal and metalloid components,
Al _(100-xyz) Cr _(x) V _(y) B _(z)
However, 20 ≦ x ≦ 40, 2 ≦ y ≦ 15, 2 ≦ z ≦ 15
And includes N as a non-metallic component and unavoidable impurities.

In addition, the second coating layer is atomic% of metal and metalloid components,
Ti _(100-vw) Cr _(v) Si _(w)
However, 5 ≦ v ≦ 30, 5 ≦ w ≦ 30
And includes N as a non-metallic component and unavoidable impurities.

  On the surface side of the multilayer coating layer, a fifth coating layer is provided, and the metal component, semi-metal component and non-metal component of the fifth coating layer are the metal component, semi-metal component and non-metal of the second coating layer. It is set the same as the component. The metal component, metalloid component, and nonmetal component of the fifth coating layer may be set the same as the metal component, metalloid component, and nonmetal component of the first coating layer.

  The reason why the above configuration is adopted and the operation and effect of the above configuration will be described below.

  First, the characteristics and problems of the Al—Cr—N based coating and the Ti—Si—N based coating will be described. The Al—Cr—N coating proposed in Japanese Patent No. 3039381 is based on CrN instead of TiN, compared to the Ti—Al—N coating that has been widely used as a hard coating for cutting tools. It has improved heat resistance, and has high heat resistance and relatively high toughness, but it has a slightly low hardness and wear resistance when cutting high-hardness hardened steel such as high-speed steel. Is not enough. On the other hand, according to Veprek et al. (S. Christiansen, M. Albrecht, HP Strunk, and S. Veprek, J. Vac. Sci. Technol. B16 (1), Jan / Feb 1998.), the Ti-Si-N coating is It is said that it has a structure in which granular TiN fine crystals and Si—N amorphous parts coexist, resulting in a very high hardness and a high heat resistance. However, although the hardness and heat resistance are high, the toughness is slightly low, and when cutting a high-hardness work material, there is a case where minute chipping occurs on the cutting edge. The inventors of the present invention have made a thin layer of an Al—Cr—N film and a thin layer of a Ti—Si—N film to make up for the disadvantages of both, and to improve the wear resistance against high-hardness work materials. I thought I could do it and I did research.

  The inventors of the present invention conducted research on a multilayered film of an Al—Cr—N-based film layer and a Ti—Si—N-based film layer under various film formation conditions. It was found that good or bad adhesion greatly affects the wear resistance of the coated tool. In other words, good interlaminar adhesion within the film stack provides good wear resistance for high-hardness workpieces, but poor interlaminar adhesion results in a tool wear form with microchipping and sufficient wear resistance. I can't get it. In the latter coated tool, microfracture occurs in the laminated portion, and it is considered that the tool wear has progressed from that. When the laminated part was observed by a cross-sectional TEM method, it was found that a film with good wear resistance had a portion of a structure in which a Ti—Si—N film layer and an Al—Cr—N film layer were mixed. It was. A part of the multilayer coating layer becomes a mixed structure of the first coating layer and the second coating layer, so that the interlaminar adhesion within the coating layer is increased, and as a result, the wear resistance of the coated tool is improved. I think. This example is based on this result, by controlling the film structure so that a part of the film lamination part becomes a mixed structure, the interlaminar adhesion in the film lamination part is increased, and cutting with excellent wear resistance is achieved. A multilayer hard coating for a tool is provided. If the ratio of the mixed structure that closes to the cross section of the film stack is too small, the effect of improving the interlaminar adhesion will be low. On the other hand, if the ratio of the mixed structure is too large, the heat resistance will be slightly reduced. It is desirable to make it 80% or less. Future research is awaiting the mechanism of formation of the mixed tissue, but it seems that the incorporation of fine metal particles called droplets into the film has an effect. It seems that the proportion of mixed tissue can be controlled to some extent by appropriately controlling the density of droplets. Although not clearly understood, the mixed structure portion is estimated to have a structure in which fine crystals mainly composed of TiN are dispersed in a matrix of an Al-Cr-Ti-Si-N-based material. . The mixed tissue part is characterized in that the boundary between the first film layer and the second film layer is unclear.

  Next, the film thickness per layer of the first coating layer and the second coating layer will be described. When the film thickness per layer is less than 1 nm, the first film layer and the second film layer are likely to be mixed, and the ratio of the mixed structure of the first film layer and the second film layer regardless of the density of the droplets. Tends to exceed 80%, resulting in a decrease in heat resistance. On the other hand, if the film thickness per layer is greater than 20 nm, the second film layer becomes too thick and the toughness of the entire laminated film cannot be sufficiently increased. Also, if the first film layer is too thin, the toughness of the entire laminated film will not be high, and if it is too thick, the hardness of the entire laminated film will be low. From the above, it is desirable that the thickness of each of the first coating layer and the second coating layer be 1 nm or more and 20 nm or less.

  Next, the composition of the first coating layer will be described. In this example, a composition containing at least Al and Cr as the metal and metalloid components and N as the nonmetal component is within the scope of the invention, and is based on AlCrN. The inventors of the present invention have studied a film in which various third elements are added to an AlCrN film, and have found that the wear resistance against a steel material can be improved by containing a predetermined amount of V and B. This is thought to be due to the improved hardness and lubricity of the film. The effect is small when the amount of B is less than 2% with only atomic% of metal and metalloid, but the effect of improving hardness appears at 2% or more. When the B content exceeds 15%, the hardness value does not change much. Since B is an expensive element compared to Al and Cr, in consideration of film hardness and economy, B may be contained in a composition range of 2% or more and 15% or less in terms of atomic% of only metal and metalloid. desirable. Moreover, about the content of V, if the content is increased, the lubricity of the film is improved. The effect is small when the amount of V is less than 2% with atomic% of metal and metalloid only, but the effect of improving lubricity appears at 2% or more, and the wear resistance of the tool coated with the coating on the steel material improves. On the other hand, when the V content is excessively increased, the hardness of the coating is lowered and the wear resistance against the steel material is lowered. Further, since V is an extremely expensive element compared to Al and Cr, the composition of 2% or more and 15% or less in terms of atomic% of only metal and metalloid in consideration of the lubricity, hardness and economics of the film. It is desirable to contain V in the range.

  Next, the composition of the second coating layer will be described. In the present embodiment, at least Ti and Si are included as the metal component and the semimetal component, and N is included as the nonmetal component, but the base is TiSiN. The present inventors tried to add various kinds of third elements based on TiSiN in order to further improve the wear resistance of the coating. As a result, it was confirmed that inclusion of a predetermined amount of Cr improves lubricity and improves the wear resistance of the film. That is, when the atomic percentage of only metal and metalloid is less than 5%, the effect is small, but the effect of improving lubricity appears at 5% or more, and the cemented carbide base material coated with the coating is cut. It was confirmed that the wear resistance of the tool against a high-hardness work material is improved. It was also confirmed that if the Cr content is excessively increased, the hardness of the coating is lowered, and the wear resistance of the cemented carbide base cutting tool coated with the coating on the high-hardness work material is reduced. For these reasons, the Cr content is desirably 5% or more and 30% or less in terms of atomic% of only metals and metalloids. On the other hand, regarding the content of Si, if the content is increased, the oxidation resistance and hardness of the film are improved. That is, when the atomic percentage of only metal and metalloid is less than 5%, the effect is small, but the effect of improving oxidation resistance and hardness appears at 5% or more, and the cemented carbide coated with the coating. It was confirmed that the wear resistance of the base material cutting tool against the high-hardness work material is improved. It was also confirmed that if the Si content is excessively increased, the wear resistance of the cemented carbide substrate cutting tool coated with the coating on the high-hardness work material is reduced. This is considered to be because if the amount of Si is too large, the internal stress of the film becomes too large, and microcracks are likely to occur in the film. For these reasons, the Si content is preferably 5% or more and 30% or less in terms of atomic% of only metals and metalloids.

  Next, the third coating layer will be described. The inventors of the present invention tried a cutting test by coating a cemented carbide cutting tool with a multilayer coating layer, and confirmed that peeling of the coating may occur during cutting. This is probably because the adhesion between the cemented carbide substrate and the coating is not sufficient. Therefore, a third coating layer is formed between the cemented carbide substrate and the multilayer coating layer, and the metal component and the semimetal component of the third coating layer have the same composition as the metal component and the semimetal component of the first coating layer. As a result, film peeling during cutting was significantly reduced. It is considered that the adhesion between the cemented carbide base material and the film is greatly improved by forming the third film layer. The film thickness of the third coating layer is not particularly limited, but if it is too thin, the effect of improving the adhesion is difficult to appear, so it is desirable that the film thickness be 0.1 μm or more.

  As another measure for reducing film peeling, a Ti-based or Cr-based nitride or carbonitride (fourth coating layer) having excellent adhesion to the substrate may be formed directly on the substrate. Even if the fourth coating layer is formed directly on the substrate and the multilayer coating layer is formed thereon, film peeling is greatly reduced. A more preferable coating configuration is a configuration in which a fourth coating layer is formed directly on the substrate, a third coating layer is formed thereon, and a multilayer coating layer is further formed thereon. The film thickness of the fourth film layer is such that when the third film layer is formed thereon, the effect of improving the adhesion with the substrate appears even if the film thickness is relatively thin. It is desirable to have a thickness of In addition, since the purpose of the fourth coating layer is to improve the adhesion to the substrate, it is not necessary to make the film thickness too thick, and it is desirable to make the film thickness 0.5 μm or less.

  Next, the fifth coating layer will be described. The inventors of the present invention applied an Al—Cr—N-based film (metal component and semi-metal component are the same composition as the first film layer) or a Ti—Si—N-based film (metal component and semi-metal component are present on the outermost layer). It was confirmed that the wear resistance of the coated tool may be further enhanced by forming the same composition as the second coating layer) depending on the type of work material. For the SKH51 material (high speed steel) heat-treated to 65HRC, the wear resistance of the coated tool was slightly improved by forming a Ti—Si—N-based film on the outermost surface. On the other hand, for the STAVAX material heat-treated to 53HRC, the wear resistance of the coated tool was slightly improved by forming an Al—Cr—N-based film on the outermost surface. As described above, the Al—Cr—N-based film has a relatively high toughness, but the hardness is slightly low, and the Ti—Si—N-based film has a high hardness, but has a slightly low toughness. Although the detailed mechanism is unknown, it is considered that these characteristics have had a good effect on the wear resistance of the coated tool by providing the fifth coating layer on the outermost surface. The film thickness of the fifth film layer is not particularly limited, but if it is too thin, the effect is difficult to appear, and if it is too thick, the hardness is low (Al-Cr-N-based film) and the toughness is low. (Ti-Si-N-based film) appears, so it is desirable that the thickness be 0.1 μm or more and 1 μm or less.

  The hard coating of this example was invented for a cutting tool for steel materials, and the base material thereof is a cemented carbide alloy composed of hard particles mainly composed of WC and a binder mainly composed of Co. However, it is desirable because it is a material having a balance between hardness and toughness as a cutting tool for steel materials. If the average particle size of the WC particles is too small, it will be difficult to uniformly disperse the WC particles in the binder, which tends to cause a reduction in the bending strength of the cemented carbide. On the other hand, if the WC particles are too large, the hardness of the cemented carbide decreases. Further, if the Co content is too small, the bending strength of the cemented carbide decreases, and conversely if the Co content is excessively increased, the hardness of the cemented carbide decreases. Therefore, it is desirable to use a cemented carbide having a mean particle size of WC particles of 0.1 μm to 2 μm and a Co content of 5 to 15% by weight as a base material.

  Since the present embodiment is configured as described above, when there is a predetermined amount of mixed tissue portion in which the first coating layer and the second coating layer are mixed in the multilayer coating layer, the first coating layer and the second coating layer Interlayer adhesion is enhanced, and the wear resistance against high hardness hardened steel represented by high speed steel is improved accordingly.

  In particular, in this example, a fourth coating layer, a third coating layer, a multilayer coating layer, and a fifth coating layer are sequentially laminated on the base material, and each of the multilayer coating layers is further provided on the base material side and the surface layer side, respectively. A film layer having characteristics is provided. In other words, a coating layer having excellent toughness is disposed on the base material side of the coating film where the film stress is increased, and a coating layer having excellent hardness is disposed on the surface layer side in contact with the work to be cut. It is difficult to peel off from the material and the surface layer is difficult to wear, and chipping is extremely difficult to occur.

  Therefore, in this example, the interlaminar adhesion between the first coating layer and the second coating layer is enhanced, and the cutting of high hardness hardened steel represented by high-speed steel and the like compared with the conventional hard coating for cutting tools. It becomes a hard coating for a cutting tool with extremely high practicality, which improves the wear resistance at.

  Hereinafter, experimental examples supporting the effects of the present embodiment will be described.

[Experimental Example 1]
In Experimental Example 1, an arc discharge ion plating apparatus is used as a film forming apparatus, and Al ₆₀ Cr ₂₇ V ₅ B ₈ and Ti ₆₂ Cr ₁₅ Si ₂₃ targets are used as evaporation sources of metal and metalloid components in the film forming apparatus. At the same time, N ₂ gas is introduced into the film forming apparatus as a reaction gas, the gas pressure is set to 6 Pa, the bias voltage is set to −100 V, and the base material temperature is 600 ° C. to form a film on the cemented carbide plate as the film forming base. did. Two types of targets were arranged in the film forming apparatus so as to face each other, and a film forming substrate was set at the center and rotated at a rotation speed of 3 min ⁻¹ (the rotation axis was parallel to the target surface). In the initial stage of film formation, the discharge of the Ti ₆₂ Cr ₁₅ Si ₂₃ target is turned off to form (Al ₆₀ Cr ₂₇ V ₅ B ₈ ) N (third coating layer) directly on the carbide substrate, and then Ti ₆₂ Cr ₁₅ Si ₂₃ target is also turned on (simultaneous discharge of Al ₆₀ Cr ₂₇ V ₅ B ₈ target and Ti ₆₂ Cr ₁₅ Si ₂₃ target), (Al ₆₀ Cr ₂₇ V ₅ B ₈ ) N (first coating layer) And (Ti ₆₂ Cr ₁₅ Si ₂₃ ) N (second coating layer) were alternately laminated with the rotation of the substrate to form a multilayer coating layer. The layer that appears relatively black in the laminated portion of FIGS. 1 and 2 is the second coating layer, and the layer that appears relatively white is the first coating layer. From the TEM image, it can be confirmed that a structure in which the first coating layer and the second coating layer are mixed exists in a part of the laminated portion. By introducing this mixed structure into the laminated portion, the interlaminar adhesion of the multilayer coating layer can be greatly improved, thereby improving the wear resistance of the coated tool.

[Experiment 2]
In Experimental Example 2, an arc discharge ion plating apparatus is used as a film forming apparatus, targets of various compositions are attached in the film forming apparatus as evaporation sources of metal and metalloid components, and N ₂ gas, CH are used as reaction gases. One or two of the _four gases were introduced into the film forming apparatus, and a predetermined film was formed on a cemented carbide two-blade ball end mill (outer diameter: 3 mm) as a film forming substrate. . Using a film forming apparatus to which three types of targets were attached, two or three types of targets were attached to form a film. In forming the film, the conditions are such that the gas pressure is 6 Pa, the bias voltage is −30 V to −200 V, the substrate temperature is 500 ° C. to 600 ° C., and the film thickness of the entire film is 3.0 to 4.0 μm. A film was formed. Using an end mill coated with a predetermined film, a cutting test was performed under the following cutting conditions, and the wear width of the end mill flank was measured. That is, the work material is SKH51 hardened material (65HRC), an end mill with an outer diameter of 3 mm is rotated at a rotation speed of 19000 min ⁻¹ , a feed speed is 1440 mm / min, a cutting amount Ad = 0.15 mm, Pf = 0.45 mm. The test was conducted using air blow as a coolant. The results of the cutting test are shown in Table 1.

  No. The fourth coating layers (TiCN) of 8, 11 and 12 were formed while the C amount immediately above the base material was 0, that is, TiN, and the C amount was gradually increased toward the surface layer portion. No. The fourth coating layer (CrCN) No. 9 was formed while the C amount immediately above the base material was 0, that is, CrN, and the C amount was gradually increased toward the surface layer portion.

  No. In the examples of 1 to 9, the cross-sectional TEM image of the multilayer coating layer includes a portion of the structure in which the first coating layer and the second coating layer are mixed, and the area of the mixed tissue portion is the cross-sectional area of the multilayer coating layer. It was 5% or more and 80% or less. No. In the comparative example of 10, the structure in which the first coating layer and the second coating layer were mixed could not be confirmed in the cross-sectional TEM image of the multilayer coating layer.

  Table 1 shows, as a comparative example, the results of a cutting test performed with an end mill in which a conventional hard coating and a hard coating out of the range of the embodiment are coated by the same means as in the embodiment.

  From Table 1, it can be seen that this example has a reduction in end mill flank wear width, that is, an improvement in wear resistance with respect to hardened hardened steel, as compared with the comparative example.

It is explanatory sectional drawing of the principal part of a present Example. It is expansion explanatory sectional drawing of the principal part of a present Example.

Claims (8)

A hard film for a cutting tool formed on a substrate, the hard film including a multilayer film layer in which two or more first film layers and second film layers are alternately laminated, coating layer is a coating layer contain inevitable impurities include N as a non-metal component and at least Al and Cr as metal components, non-metallic and at least Ti and Si the second coating layer is a metal and metalloid components A film layer containing N as an ingredient and containing inevitable impurities, the film thickness of each of the first film layer and the second film layer is set to 1 nm or more and 20 nm or less, and the multilayer film layer is formed by a cross-sectional TEM method. when viewed, the a component of the first coating layer and the component of the second coating layer is present mixed tissue section having a tissue mixed with 5% of the cross-sectional area of the area of the mixed tissue section the multilayer coating layer More than 80% The hard film for a cutting tool to be with. The hard film for a cutting tool according to claim 1, wherein the first film layer is composed of metal and a metalloid component in atomic%.
Al (100-xyz) Cr (x) V (y) B (z)
However, 20 ≦ x ≦ 40, 2 ≦ y ≦ 15, 2 ≦ z ≦ 15
And the second coating layer is an atomic% metal and metalloid component,
Ti (100-vw) Cr (v) Si (w)
However, 5 ≦ v ≦ 30, 5 ≦ w ≦ 30
A hard coating for a cutting tool, characterized by:   The hard film for a cutting tool according to any one of claims 1 and 2, wherein a third film layer is provided between the base material and the multilayer film layer, and a metal component or metal of the third film layer is provided. The hard coating for a cutting tool, wherein the component and the metalloid component are the same as the metal component or the metal component and the metalloid component of the first coating layer.   The hard film for a cutting tool according to any one of claims 1 to 3, wherein a fourth film layer is provided immediately above the base material, and the fourth film layer is a nitride or carbonitride containing Ti as a main component. A hard film for a cutting tool, characterized in that the film thickness of the fourth film layer is set to 0.01 μm to 0.5 μm.   The hard film for a cutting tool according to any one of claims 1 to 3, wherein a fourth film layer is provided immediately above the base material, and the fourth film layer is a nitride or carbonitride containing Cr as a main component. A hard film for a cutting tool, characterized in that the film thickness of the fourth film layer is set to 0.01 μm to 0.5 μm.   The hard film for a cutting tool according to any one of claims 1 to 5, wherein a fifth film layer is provided on a surface layer side of the multilayer film layer, and the metal component and the semimetal component of the fifth film layer are A hard coating for a cutting tool, characterized by being the same as the metal component and the semi-metal component of the second coating layer.   The hard film for a cutting tool according to any one of claims 1 to 5, wherein a fifth film layer is provided on a surface layer side of the multilayer film layer, and a metal component or a metal component and a semimetal of the fifth film layer are provided. The hard coating for a cutting tool, wherein the component is the same as the metal component or the metal component and the metalloid component of the first coating layer.   The hard film for a cutting tool according to any one of claims 1 to 7, wherein the substrate is a cemented carbide composed of hard particles mainly composed of WC and a binder mainly composed of Co, and A hard film for a cutting tool, wherein an average particle diameter of WC particles is set to 0.1 μm to 2 μm, and the Co content is set to 5 to 15% by weight.