WO2018181123A1 - Outil de coupe à revêtement de surface présentant une couche de revêtement dure présentant une excellente résistance à l'écaillage et à l'usure - Google Patents

Outil de coupe à revêtement de surface présentant une couche de revêtement dure présentant une excellente résistance à l'écaillage et à l'usure Download PDF

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Publication number
WO2018181123A1
WO2018181123A1 PCT/JP2018/012025 JP2018012025W WO2018181123A1 WO 2018181123 A1 WO2018181123 A1 WO 2018181123A1 JP 2018012025 W JP2018012025 W JP 2018012025W WO 2018181123 A1 WO2018181123 A1 WO 2018181123A1
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Prior art keywords
layer
average
composite
cutting tool
nitride
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PCT/JP2018/012025
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English (en)
Japanese (ja)
Inventor
佐藤　賢一
光亮 柳澤
卓也 石垣
西田　真
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三菱マテリアル株式会社
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Priority claimed from JP2018024752A external-priority patent/JP6935058B2/ja
Application filed by 三菱マテリアル株式会社 filed Critical 三菱マテリアル株式会社
Publication of WO2018181123A1 publication Critical patent/WO2018181123A1/fr

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Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23B—TURNING; BORING
    • B23B27/00—Tools for turning or boring machines; Tools of a similar kind in general; Accessories therefor
    • B23B27/14—Cutting tools of which the bits or tips or cutting inserts are of special material
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23C—MILLING
    • B23C5/00—Milling-cutters
    • B23C5/16—Milling-cutters characterised by physical features other than shape
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C16/00—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
    • C23C16/22—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes characterised by the deposition of inorganic material, other than metallic material
    • C23C16/30—Deposition of compounds, mixtures or solid solutions, e.g. borides, carbides, nitrides
    • C23C16/34—Nitrides
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C16/00—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
    • C23C16/22—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes characterised by the deposition of inorganic material, other than metallic material
    • C23C16/30—Deposition of compounds, mixtures or solid solutions, e.g. borides, carbides, nitrides
    • C23C16/36—Carbonitrides

Definitions

  • the present invention is a high-speed, high-feed, intermittent cutting process involving high heat generation such as alloy steel and an impact load on the cutting edge, and the hard coating layer has excellent chipping resistance and wear resistance.
  • the present invention relates to a surface-coated cutting tool (hereinafter sometimes referred to as a coated tool) that exhibits excellent cutting performance over a long period of use.
  • WC tungsten carbide
  • TiCN titanium carbonitride
  • cBN cubic boron nitride
  • Patent Document 1 has a NaCl-type face-centered cubic structure on the surface of a tool base and is represented by a composition formula: (Ti 1-X Al X ) (C Y N 1-Y )
  • the average composition X avg of Al is 0.60 ⁇ X avg ⁇ 0.95
  • the average composition Y avg of C is 0 ⁇ Y avg ⁇ 0.005)
  • a hard coating layer including at least a TiAlCN layer is formed
  • the TiAlCN layer is used to determine the tilt angle distribution by measuring the tilt angle formed by the normal of the ⁇ 111 ⁇ plane of the TiAlCN crystal grain with respect to the normal direction of the tool base surface using an electron beam backscatter diffraction device
  • the highest peak exists in the inclination angle section within the range of 0 to 12 degrees, and the total of the frequencies existing within the range of 0 to 12 degrees is 45% or more of the entire degrees in the inclination angle frequency distribution.
  • a structure having a triangular shape and a facet formed by an equivalent crystal plane represented by ⁇ 111 ⁇ of the crystal grains occupies an area ratio of 35% or more of the whole in a plane perpendicular to the layer thickness direction.
  • a coating tool with improved chipping resistance of a hard coating layer in high-speed interrupted cutting and the like that is accompanied by high heat generation such as stainless steel and an impact load on the cutting edge has been proposed. .
  • Patent Document 2 As in Patent Document 1, high heat generation of stainless steel or the like is accompanied, and chipping resistance of the hard coating layer in high-speed intermittent cutting processing in which an impact load is applied to the cutting edge.
  • the composition formula (Ti 1-X Al X ) (C Y N 1-Y ) (however, in terms of atomic ratio, the average composition X avg of Al is 0.60 ⁇ X avg ⁇ 0.95, the average composition Y avg of C is 0 ⁇ Y avg ⁇ 0.005), and a hard coating layer including at least a TiAlCN layer having a NaCl-type face-centered cubic structure is formed, and the TiAlCN When the inclination angle number distribution was obtained by measuring the inclination angle formed by the normal of the ⁇ 100 ⁇ plane of the TiAlCN crystal grain with respect to the normal direction of the tool base surface using an electron beam backscatter diffraction apparatus,
  • a coated tool having a structure that occupies an area ratio of 50% or more of the whole in a plane perpendicular to the thickness direction has been proposed. Further, when XRD analysis is performed on the TiAlCN layer in the coated tool, Ic ⁇ 200 between the peak intensity Ic ⁇ 200 ⁇ derived from the cubic structure and the peak intensity Ih ⁇ 200 ⁇ derived from the hexagonal structure. ⁇ / Ih ⁇ 200 ⁇ ⁇ 3.0 holds true, the effect of improving wear resistance is further enhanced.
  • a 3 to 25 ⁇ m wear-resistant coating layer formed by CVD is formed on a tool substrate, and the coating layer includes at least Ti 1-1.
  • the layer thickness 1.5 to 17 ⁇ m satisfying 0.70 ⁇ x ⁇ 1, 0 ⁇ y ⁇ 0.25 and 0.75 ⁇ z ⁇ 1.15 is satisfied.
  • TiAlCN layer having said layer has a lamellar structure of the lamellar spacing of less than 150 nm, the cutting edge is the same crystal structure have, Ti and Al Ti 1-x Al x having a stoichiometry is different alternately It is composed of Ti 1-x Al x C y N z in which C y N z is alternately and periodically arranged, and the Ti 1-x Al x C y N z layer has a face-centered cubic structure of at least 90% by volume or more.
  • the TC value of the layer is TC (111)> 1 5 satisfied, the half value width of the X-ray diffraction peak intensity of ⁇ 111 ⁇ plane is coated tool have been proposed less than 1 degree.
  • the present invention provides a coated tool that solves the above-described problems and exhibits excellent chipping resistance and wear resistance over a long period of use even when subjected to high-speed high-feed interrupted cutting such as alloy steel.
  • the purpose is to do.
  • the present inventors have disclosed a composite nitride or composite carbonitride (hereinafter, referred to as “TiAlCN” or “(Ti 1-x Al x ) (C y N 1-y )”) layer of Ti and Al.
  • TiAlCN composite nitride or composite carbonitride
  • (Ti 1-x Al x ) (C y N 1-y )) layer of Ti and Al As a result of intensive research aimed at improving the chipping resistance and wear resistance of the coated tool provided with a hard coating layer containing at least a hard coating layer on the surface of the tool base, the following findings were obtained.
  • the TiAlCN crystal grains constituting the TiAlCN layer have high toughness in high-speed high-feed intermittent cutting such as alloy steel, they do not have sufficient chipping resistance and wear resistance.
  • the inventors of the present invention have intensively studied the lattice strain in each crystal lattice of the TiAlCN crystal grains constituting the TiAlCN layer. As a result, the present inventors have included a crystal grain having an NaCl-type face-centered cubic structure and the NaCl.
  • a TiAlCN layer that is a composite nitride or composite carbonitride containing a predetermined amount of Me, that is, a NaCl-type face center of the TiAlMeCN layer.
  • ⁇ A measured for crystal grains having a cubic structure is 0.007 to 0.050 mm, both excellent chipping resistance and wear resistance characteristics are obtained in high-speed, high-feed, interrupted cutting processing of alloy steel and the like. It has been found that it is possible to have both, and if at least one of Si and B is further added, the hardness of the TiAlMeCN layer, that is, the wear resistance is further improved.
  • the present invention has been made based on the above findings, “(1) Surface-coated cutting in which a hard coating layer is provided on the surface of a tool base made of any of tungsten carbide-based cemented carbide, titanium carbonitride-based cermet, or cubic boron nitride-based ultrahigh-pressure sintered body
  • the hard coating layer is a composite nitride or composite charcoal of Ti, Al, and Me (wherein Me is at least one of Zr, V, and Cr) having an average layer thickness of 1.0 to 20.0 ⁇ m.
  • nitride layer Including at least a nitride layer, the composite nitride or composite carbonitride, Composition formula: (Ti 1-xy Al x Me y ) (C z N 1-z )
  • the ratio z (where x, y, and z are atomic ratios) are 0.60 ⁇ x ⁇ 0.95, 0.005 ⁇ y ⁇ 0.100, 0.60 ⁇ x + y ⁇ 0.95, respectively.
  • the present invention provides a surface-coated cutting tool in which a hard coating layer is provided on the surface of a tool substrate, and includes at least a TiAlMeCN layer having an average layer thickness of 1.0 to 20.0 ⁇ m as the hard coating layer.
  • a hard coating layer is provided on the surface of a tool substrate, and includes at least a TiAlMeCN layer having an average layer thickness of 1.0 to 20.0 ⁇ m as the hard coating layer.
  • the TiAlMeCN layer containing Me has an appropriate lattice strain (0.007 ⁇ ⁇ ⁇ A ⁇ 0.050 ⁇ ) and high hardness is achieved, high heat generation such as alloy steel is generated.
  • the TiAlMeCN layer has excellent chipping resistance and exhibits excellent wear resistance over a long period of use when subjected to high-speed, high-feed, intermittent cutting with an impact load on the cutting edge. To do.
  • the hard coating layer of the present invention includes at least a TiAlMeCN layer represented by the composition formula: (Ti 1-xy Al x Me y ) (C z N 1-z ) (where Me is Zr, V, Cr) And at least one of Si and B may be added).
  • This TiAlMeCN layer has high hardness and excellent wear resistance, but the effect is particularly remarkable when the average layer thickness is 1.0 to 20.0 ⁇ m.
  • the average layer thickness is set to 1.0 to 20.0 ⁇ m.
  • the TiAlMeCN layer in the present invention is The content of Al in the total amount of Ti, Al and Me (hereinafter referred to as the “average content ratio of Al”) x, The content of Me in the total amount of Ti, Al and Me (hereinafter referred to as “the average content of Me”) y, The average content ratio (hereinafter referred to as “average content ratio of C”) z of the total amount of C and C in C is: 0.60 ⁇ x ⁇ 0.95, 0.005 ⁇ y ⁇ 0.100, 0.60 ⁇ x + y ⁇ 0.95, 0.0000 ⁇ z ⁇ 0.0050 (where x, y, and z are Both are determined so as to satisfy the atomic ratio).
  • the average Al content ratio x is less than 0.60, the TiAlMeCN layer is inferior in hardness, so that when it is subjected to high-speed high-feed intermittent cutting such as alloy steel, the wear resistance is not sufficient.
  • the average content ratio y of Me is less than 0.005
  • chipping resistance which is an effect of adding Me (Zr, Cr, V) and hardness which is an effect of adding Si or / and B which are optionally added Is not sufficiently exhibited, and when it exceeds 0.100, Se segregates to the grain boundary, and the toughness is lowered to deteriorate the chipping resistance.
  • the average content ratio x of Al and the average content ratio y of Me exceeds 0.60, and if it exceeds 0.95, the content ratio of Ti is relatively reduced. , Resulting in embrittlement and reduced chipping resistance. Therefore, the average content ratio x of Al and the average content ratio y of Me were determined as 0.60 ⁇ x ⁇ 0.95, 0.005 ⁇ y ⁇ 0.100, and 0.60 ⁇ x + y ⁇ 0.95.
  • the average content ratio z of C contained in the TiAlMeCN layer is a minute amount in the range of 0.0000 ⁇ z ⁇ 0.0050, the adhesion between the TiAlMeCN layer and the tool substrate or the lower layer is improved, and By improving lubricity, the impact during cutting is relieved, and as a result, the chipping resistance and fracture resistance of the TiAlMeCN layer are improved.
  • the average content ratio z of C deviates from the range of 0.0000 ⁇ z ⁇ 0.0050, the toughness of the TiAlMeCN layer is lowered, and chipping resistance and fracture resistance are adversely lowered.
  • the average content ratio z of C was determined to be 0.0000 ⁇ z ⁇ 0.0050. Further, when the average content ratio s of Cl contained in the TiAlMeCN layer is in the range of 0.0001 ⁇ s ⁇ 0.0040, the lubricity can be enhanced without reducing the toughness of the layer. That is, if the average chlorine content is less than 0.0001, the effect of improving lubricity is small. On the other hand, if the average chlorine content exceeds 0.0040, chipping resistance is lowered, which is not preferable. Therefore, the average Cl content is defined as 0.0001 ⁇ s ⁇ 0.0040.
  • lattice strain by controlling film formation conditions is introduced into cubic TiAlMeCN crystal grains of the TiAlMeCN layer, and further, by adding Me, the chipping resistance and wear resistance of the TiAlCN layer are improved.
  • the introduction of lattice strain and the addition of Me by controlling the film forming conditions can be performed by, for example, a thermal CVD method using NH 3 in forming a TiAlMeCN layer. Specifically, it is as follows.
  • At least one of gas group A composed of NH 3 and H 2 , TiCl 4 , AlCl 3 , N 2 , H 2, ZrCl 4 , CrCl 2 , and VCl 4 is optionally added to SiCl 4.
  • a gas group B made of at least one of BCl 3 (hereinafter sometimes referred to as “MeCl x ”) is supplied into the reaction apparatus from a separate gas supply pipe, and the reaction apparatus of the gas group A and the gas group B is supplied.
  • the gas is supplied in such a manner that gas flows for a time shorter than that period at a constant time interval, and the gas supply time for the gas group A and the gas group B is less than the gas supply time.
  • the N 2, AlCl 3, Al ( CH 3) 3 is a gas component
  • feed ratio N 2 / (AlCl 3 + Al CH 3) 3) is by chemical vapor deposition to adjust the supply amount of the gas components to be a relatively large value, it is possible to form a TiAlMeCN layer predetermined lattice strain is introduced.
  • ⁇ A tends to increase generally.
  • Reaction gas composition (volume% with respect to the total of gas group A and gas group B): Gas group A: NH 3 : 2.0 to 6.0%, H 2 : 65 to 75%, Gas group B: AlCl 3 : 0.50 to 0.90%, TiCl 4 : 0.20 to 0.30%, MeCl x : 0.10 to 0.20%, N 2 : 3 to 12%, Al ( CH 3 ) 3 : 0.00 to 0.10%, H 2 : remaining, N 2 / (AlCl 3 + Al (CH 3 ) 3 ): 3.0 to 24.0 Reaction atmosphere pressure: 4.5 to 5.0 kPa, Reaction atmosphere temperature: 700 to 900 ° C.
  • Supply cycle 6.0 to 9.0 seconds
  • Gas supply time per cycle 0.15 to 0.25 seconds
  • Phase difference in supply of gas group A and gas group B 0.10 to 0.20 seconds
  • the cubic lattice strain in the TiAlMeCN layer formed as described above can be measured by the following method, and the lattice strain index ⁇ A can be obtained as follows. First, X-ray diffraction is performed on the TiAlMeCN layer, and X-ray diffraction spectra for the (111) plane and the (200) plane of the TiAlMeCN crystal grains are obtained.
  • the TiAlMeCN layer having the lattice strain index ⁇ A defined above has high hardness due to the presence of lattice strain in the layer by controlling the film formation conditions in addition to lattice strain related to improvement of toughness and chipping resistance by adding Me. As a result, excellent wear resistance is exhibited. However, when ⁇ A is less than 0.007 mm, the lattice distortion is small, so the effect of improving the hardness is not sufficient. On the other hand, when ⁇ A exceeds 0.050 mm, Since the strain becomes excessive and the fracture resistance at the time of cutting is reduced, the ⁇ A is set in the range of 0.007 ⁇ ⁇ ⁇ A ⁇ 0.050 ⁇ .
  • the present invention is the interplanar spacing of the (111) plane and the (200) plane obtained by performing X-ray diffraction on the crystal grains having the NaCl-type face-centered cubic structure constituting the TiAlMeCN layer.
  • the absolute value ⁇ A of the difference between the lattice constants A (111) and A (200) calculated from d (111) and d (200) is increased.
  • the present inventors have found that a coated tool excellent in both chipping resistance and wear resistance can be obtained by improving the wear resistance and applying this to a tool.
  • the average grain width W of each crystal grain having a NaCl-type face-centered cubic structure in the composite nitride or composite carbonitride layer is 0.10 to 2
  • the hardness and toughness of the crystal grains are improved, which is combined with the effect of the TiAlCN layer as a hard coating layer.
  • even more excellent characteristics can be exhibited. That is, by setting the average particle width W to 0.10 ⁇ m or more and 2.00 ⁇ m or less, the reactivity with the work material is reduced, the wear resistance is exhibited, the toughness is improved, and the chipping resistance is improved.
  • the average particle width W is more preferably 0.10 to 2.00 ⁇ m.
  • the average aspect ratio A is more preferably 2.0 to 10.0.
  • the average aspect ratio A refers to the surface of the tool base when the longitudinal section of the hard coating layer is observed in a range including a width of 100 ⁇ m and a height including the entire hard coating layer using a scanning electron microscope.
  • Lower layer and upper layer In the present invention, by providing the TiAlMeCN layer as the hard coating layer, it has sufficient chipping resistance and wear resistance, but Ti carbide layer, nitride layer, carbonitride layer, carbonate layer and carbonitride oxide When a lower layer comprising a Ti compound layer comprising one or more of the layers and having a total average layer thickness of 0.1 to 20.0 ⁇ m is provided, and / or an upper portion including at least an aluminum oxide layer When the layers are provided with a total average layer thickness of 1.0 to 25.0 ⁇ m, combined with the effects exhibited by these layers, it is possible to exhibit further excellent characteristics.
  • Ti consisting of one or more of Ti carbide layer, nitride layer, carbonitride layer, carbonate layer and carbonitride layer, and having a total average layer thickness of 0.1 to 20.0 ⁇ m
  • a lower layer including a compound layer When a lower layer including a compound layer is provided, if the total average layer thickness of the lower layer is less than 0.1 ⁇ m, the effect of the lower layer is not sufficiently achieved. On the other hand, if it exceeds 20.0 ⁇ m, the crystal grains are likely to be coarsened. , Chipping is likely to occur. Moreover, if the total average layer thickness of the upper layer including the aluminum oxide layer is less than 1.0 ⁇ m, the effect of the upper layer is not sufficiently achieved. On the other hand, if it exceeds 25.0 ⁇ m, the crystal grains tend to be coarsened and chipping occurs. It tends to occur.
  • the coated tool of the present invention will be specifically described with reference to examples.
  • the case where a WC-based cemented carbide or TiCN-based cermet is used as the tool substrate will be described.
  • WC powder, TiC powder, TaC powder, NbC powder, Cr 3 C 2 powder and Co powder each having an average particle diameter of 0.1 to 3 ⁇ m were prepared. These raw material powders are shown in Table 1. Then, after adding wax, ball mill mixing in acetone for 24 hours, drying under reduced pressure, press-molding into a green compact of a predetermined shape at a pressure of 98 MPa, and this green compact in a vacuum of 5 Pa , Sintered in a vacuum at a predetermined temperature within a range of 1370 to 1470 ° C. for 1 hour, and after sintering, a tool base A made of a WC-base cemented carbide having an insert shape of JDMT140520ZDSR manufactured by Mitsubishi Materials Corp. C was produced respectively.
  • a TiAlMeCN layer was formed on the surfaces of these tool bases A to D by CVD using a CVD apparatus.
  • the CVD conditions are as follows. Formation conditions A to K shown in Tables 4 and 5, that is, from a gas group A composed of NH 3 and H 2 , TiCl 4 , AlCl 3 , MeCl x , N 2 , Al (CH 3 ) 3 , H 2
  • the reaction gas composition (capacity% with respect to the total of the gas group A and the gas group B) is set as NH 3 : 2.0 to 6.0% as the gas group A.
  • the average layer thickness, the average Al content ratio x, the Me average content ratio y, the C average content ratio z, and the Cl average content ratio s shown in Table 7 are formed.
  • Invention coated tools 1-16 were produced.
  • the lower layer and / or the upper layer shown in Table 6 were formed under the formation conditions shown in Table 3.
  • the average layer thickness ( ⁇ m) shown in Table 8 is obtained by performing chemical vapor deposition on the surfaces of the tool bases A to D under the formation conditions A ′ to J ′ shown in Tables 4 and 5.
  • Comparative coating tools 1 to 16 were manufactured by vapor-depositing a hard coating layer having at least a TiAlMeCN layer and a TiAlCN layer. Similar to the coated tools 4 to 13 of the present invention, the comparative coated tools 4 to 13 were formed with the lower layer and / or the upper layer shown in Table 6 under the forming conditions shown in Table 3.
  • the cross section (longitudinal cross section) in the direction perpendicular to the tool base of each component layer of the coated tools 1 to 16 and comparative coated tools 1 to 16 of the present invention is measured using a scanning electron microscope (magnification 5000 times).
  • the average layer thickness was obtained by measuring and averaging the five layer thicknesses in the observation field, all were the average layer thicknesses shown in Table 7 and Table 8.
  • the average Al content x, the average Me content y, and the average Cl content s of the TiAlMeCN layer and the TiAlCN layer are measured with an electron beam microanalyzer (Electron-Probe-Micro- Using an analyzer (EPMA), a sample whose surface is polished is irradiated with an electron beam from the sample surface side, and an average content ratio x, y of Al, Me, and Cl is obtained from an average of 10 points of the analysis result of the characteristic X-ray obtained. And s were determined.
  • the average content ratio z of C was determined by secondary ion mass spectrometry (Secondary-Ion-Mass-Spectroscopy: SIMS).
  • the ion beam was irradiated in the range of 70 ⁇ m ⁇ 70 ⁇ m from the sample surface side, and the concentration in the depth direction was measured for the components emitted by the sputtering action.
  • the average content ratio z of C shows the average value of the depth direction about a TiAlMeCN layer and a TiAlCN layer.
  • the content ratio of C excludes the inevitable content ratio of C that is included without intentionally using a gas containing C as a gas raw material.
  • Tables 7 and 8 show the values of x, y, z, and s obtained above (all of x, y, z, and s are atomic ratios).
  • a (111) and A (200) corresponding to the lattice constant were calculated from the following equations.
  • Tables 7 and 8 show the values of d (111), d (200), A (111), A (200) and ⁇ A determined above.
  • the surface of the tool substrate is aligned with the surface of the tool substrate in a horizontal direction using a scanning electron microscope (magnification 5000 times and 20000 times) from the cross-sectional direction perpendicular to the tool substrate.
  • Each having a cubic structure in a (Ti 1-xy Al x Me y ) (C z N 1-z ) layer constituting a composite nitride or composite carbonitride layer existing in a range of 100 ⁇ m in length Are observed from the cross section side of the film perpendicular to the surface of the tool substrate, the particle width w in the direction parallel to the substrate surface, and the particle length l in the direction perpendicular to the substrate surface are measured, and the aspect ratio of each crystal grain is measured.
  • Tables 7 and 8 show the values of W and A determined above.
  • coated tools 1 to 16 and the comparative coated tools 1 to 16 according to the present invention are clamped at the tip of a tool steel cutter having a cutter diameter of 125 mm with a fixing jig.
  • the dry high-speed face milling which is a kind of high-speed, high-feed intermittent cutting of alloy steel, shown in FIG.
  • Tool substrate WC-based cemented carbide, TiCN-based cermet, Cutting test: dry high-speed face milling, center cutting, Work material: Block material of JIS / SCM415 width 100mm, length 400mm, Rotational speed: 764 min ⁇ 1 Cutting speed: 300 m / min, Cutting depth: 2.0 mm, Single blade feed rate: 3.0 mm / tooth, (Normal single blade feed is 2.0mm / tooth) Cutting time: 8 minutes Table 9 shows the results.
  • WC powder, TiC powder, ZrC powder, TaC powder, NbC powder, Cr 3 C 2 powder, TiN powder and Co powder all having an average particle diameter of 0.1 to 3 ⁇ m are prepared as raw material powders.
  • NbC powder WC powder
  • Co powder and Ni powder all having an average particle diameter of 0.1 to 2 ⁇ m
  • These raw material powders were blended into the composition shown in Table 11, wet mixed with a ball mill for 24 hours, dried, and then pressed into a green compact at a pressure of 98 MPa.
  • reaction gas composition (capacity% relative to the total of the gas group A and the gas group B) is As gas group A, NH 3 : 2.0 to 6.0%, H 2 : 65 to 75%, as gas group B, AlCl 3 : 0.50 to 0.90%, TiCl 4 : 0.20 to 0.
  • the average layer thickness, the average Al content ratio x, the average Me content ratio y, the average C content ratio z, and the average Cl content ratio s shown in Table 13 are shown.
  • Invention coated tools 17-32 were produced.
  • the lower layer and the upper layer shown in Table 12 were formed under the formation conditions shown in Table 3.
  • Comparative coating tools 17 to 32 shown in Table 14 were produced by vapor-depositing a hard coating layer in the same manner as the coating tool of the present invention. Similar to the coated tools 20 to 29 of the present invention, the comparative coated tools 20 to 29 were formed with the lower layer and / or the upper layer shown in Table 12 under the forming conditions shown in Table 3.
  • each component layer of the inventive coated tool 17-32 and comparative coated tool 17-32 is measured using a scanning electron microscope (magnification 5000 times), and the layer thicknesses at five points in the observation field are measured and averaged. When the average layer thickness was determined, the average layer thicknesses shown in Table 13 and Table 14 were all shown.
  • the coated tools 17 to 32 of the present invention and the comparative coated tools 17 to 32 are shown below.
  • Cutting condition 1 Work material: JIS-S35C lengthwise equal length 4 round fluted round bars, Cutting speed: 300 m / min, Cutting depth: 1.5 mm, Feed: 0.5 mm / rev, Cutting time: 5 minutes, (Normal feed is 0.25mm / rev),
  • Cutting condition 2 Work material: JIS / FCD450 lengthwise equidistant round bars with 4 vertical grooves, Cutting speed: 280 m / min, Cutting depth: 1.5 mm, Feed: 0.5 mm / rev, Cutting time: 5 minutes, (Normal feed is 0.25mm / rev), Table 15 shows the results of the cutting test.
  • WC powder, TiC powder, TaC powder, NbC powder, Cr 3 C 2 powder and Co powder each having an average particle diameter of 0.1 to 3 ⁇ m were prepared. These raw material powders are shown in Table 16. Then, after adding wax, ball mill mixing in acetone for 24 hours, drying under reduced pressure, press-molding into a green compact of a predetermined shape at a pressure of 98 MPa, and this green compact in a vacuum of 5 Pa , Sintered under vacuum at a predetermined temperature within a range of 1370 to 1470 ° C. for 1 hour, and after sintering, tool bases P to R made of WC-base cemented carbide having an ISO standard SOMT120416PDER insert shape Each was manufactured.
  • reaction gas composition (volume% with respect to the total of the gas group A and the gas group B) NH 3 : 2.0 to 6.0%, H 2 : 65 to 75%, Gas Group B as AlCl 3 : 0.50 to 0.90%, TiCl 4 : 0.20 to 0.30%, MeCl x : 0.10 to 0.20%, N 2 : 3 to 12%, Al (CH 3 ) 3 : 0.00 to 0.10%, H 2 : remaining, reaction atmosphere pressure: 4.5 to 5.
  • the present invention is also applied to the surfaces of the tool bases P to R using the CVD apparatus with the formation conditions A ′ to H ′ shown in Tables 4 and 5 and the average layer thickness shown in Table 19.
  • Comparative coating tools 33 to 40 shown in Table 19 were produced by vapor-depositing a hard coating layer in the same manner as the coating tool.
  • the lower layer and / or the upper layer shown in Table 17 were formed for the comparative coated tools 35 to 38 under the formation conditions shown in Table 3.
  • each component layer of the inventive coated tool 33 to 40 and comparative coated tool 33 to 40 is measured using a scanning electron microscope (5000 times magnification), and the layer thicknesses at five points in the observation field are measured and averaged.
  • the average layer thickness was determined, the average layer thicknesses shown in Table 18 and Table 19 were all shown.
  • coated tools 33 to 40 of the present invention and the comparative coated tools 33 to 40 will be described below in a state where all the various coated tools are clamped to the tip of a cutter made of tool steel having a cutter diameter of 50 mm by a fixing jig.
  • the dry high-speed face milling which is a kind of high-speed, high-feed intermittent cutting of alloy steel, shown in FIG.
  • Tool base WC-based cemented carbide
  • Cutting test Dry high-speed face milling, center cut cutting
  • Work material Block material of JIS / SCM435 width 35mm, length 200mm, Rotational speed: 1592 min ⁇ 1
  • Cutting speed 250 m / min
  • Cutting depth 1.0 mm
  • Single blade feed rate 1.0 mm / tooth
  • Cutting time 5 minutes Table 20 shows the results.
  • the coated tool of the present invention has a predetermined Al content ratio, Me content ratio, C content ratio, and Cl content ratio in the cubic crystal grains of the TiAlMeCN layer.
  • the lattice strain satisfying 0.007 ⁇ ⁇ ⁇ A ⁇ 0.050 ⁇ is formed, the hardness is high. As a result, high heat generation occurs, and the cutting blade is subjected to intermittent / impact high loads. Even when used for high-speed, high-feed, intermittent cutting that acts, it exhibits excellent wear resistance over a long period of use without the occurrence of chipping or chipping.
  • the cubic crystal grains constituting the TiAlMeCN layer and the TiAlCN layer satisfy a predetermined Al content rate, Me content rate, C content rate, Cl content rate, 0.007 ⁇ ⁇ ⁇ A ⁇ 0.050 ⁇ . It is clear that the comparative coated tool in which no lattice strain is formed reaches the end of its life in a short time due to the occurrence of abnormal damage such as chipping or the progress of wear in high-speed and high-feed intermittent cutting.
  • the coated tool of the present invention can be used as a coated tool for various work materials as well as high-speed and high-feed intermittent cutting of alloy steel, and has excellent cutting performance over a long period of use. Therefore, it is possible to sufficiently satisfy the high performance of the cutting device, the labor saving and energy saving of the cutting process, and the cost reduction.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Inorganic Chemistry (AREA)
  • General Chemical & Material Sciences (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Chemical Vapour Deposition (AREA)
  • Cutting Tools, Boring Holders, And Turrets (AREA)

Abstract

L'invention concerne un outil de coupe à revêtement de surface présentant une excellente résistance à l'écaillage et à l'usure lorsqu'il est utilisé pour la coupe intermittente à grande vitesse et à haut débit d'aciers alliés et similaires. L'outil de coupe à revêtement de surface est un outil de coupe ayant un revêtement dur contenant (Ti1-x―yAlxMey)(CzN1-z) (Me est au moins un parmi Zr, V, et Cr, 0,60≤x＜0,95, 0,005≤y≤0,100, 0,60＜x＋y≤0,95, et 0,0000≤z≤0,0050) sur la surface d'une base d'outil, la teneur moyenne s de Cl dans la quantité totale d'atomes constituant une phase de TiAlMeCN satisfaisant à 0,0001≤s≤0,0040, et la valeur absolue ΔA de la différence entre A(111) et A(200), qui sont définies comme A(111)=31/2d(111) et A(200)=2d(200) à partir du calcul d'espacements interplanaires d(111) et d(200) de grains structurés de type NaCl dans la couche de TiAlMeCN, satisfait à 0,007Å≤ΔA≤0,050Å.
PCT/JP2018/012025 2017-03-27 2018-03-26 Outil de coupe à revêtement de surface présentant une couche de revêtement dure présentant une excellente résistance à l'écaillage et à l'usure WO2018181123A1 (fr)

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JP2018024752A JP6935058B2 (ja) 2017-03-27 2018-02-15 硬質被覆層が優れた耐チッピング性、耐摩耗性を発揮する表面被覆切削工具
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JP2012201955A (ja) * 2011-03-28 2012-10-22 Ngk Spark Plug Co Ltd 被覆焼結体、被覆焼結体の製造方法
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CN113165084A (zh) * 2018-10-11 2021-07-23 三菱综合材料株式会社 硬质包覆层发挥优异的耐熔敷性、耐塑性变形性及耐异常损伤性的表面包覆切削工具
CN113165084B (zh) * 2018-10-11 2024-04-05 三菱综合材料株式会社 硬质包覆层发挥优异的耐熔敷性、耐塑性变形性及耐异常损伤性的表面包覆切削工具

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