JP2019162709A - Surface-coated cutting tool having hard coating layer exerting excellent chipping resistance - Google Patents
Surface-coated cutting tool having hard coating layer exerting excellent chipping resistance Download PDFInfo
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- 238000005520 cutting process Methods 0.000 title claims abstract description 61
- 239000011247 coating layer Substances 0.000 title claims description 19
- 239000002131 composite material Substances 0.000 claims abstract description 69
- 150000004767 nitrides Chemical class 0.000 claims abstract description 36
- 239000000203 mixture Substances 0.000 claims abstract description 29
- 239000010410 layer Substances 0.000 claims description 126
- 239000013078 crystal Substances 0.000 claims description 57
- 239000010936 titanium Substances 0.000 claims description 47
- 229910052719 titanium Inorganic materials 0.000 claims description 29
- 229910052782 aluminium Inorganic materials 0.000 claims description 25
- 239000011195 cermet Substances 0.000 claims description 4
- 229910052582 BN Inorganic materials 0.000 claims description 3
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 claims description 3
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 3
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 claims description 3
- FAPWRFPIFSIZLT-UHFFFAOYSA-M Sodium chloride Chemical compound [Na+].[Cl-] FAPWRFPIFSIZLT-UHFFFAOYSA-M 0.000 abstract description 8
- 239000011780 sodium chloride Substances 0.000 abstract description 4
- 229910004349 Ti-Al Inorganic materials 0.000 abstract description 3
- 229910004692 Ti—Al Inorganic materials 0.000 abstract description 3
- 229910017150 AlTi Inorganic materials 0.000 abstract 2
- 230000002051 biphasic effect Effects 0.000 abstract 1
- 230000007547 defect Effects 0.000 abstract 1
- 239000007789 gas Substances 0.000 description 16
- 239000000463 material Substances 0.000 description 10
- 238000000034 method Methods 0.000 description 10
- 239000002245 particle Substances 0.000 description 9
- 239000000843 powder Substances 0.000 description 9
- 239000011248 coating agent Substances 0.000 description 8
- 238000000576 coating method Methods 0.000 description 8
- 230000006378 damage Effects 0.000 description 8
- 230000007423 decrease Effects 0.000 description 8
- 229910010037 TiAlN Inorganic materials 0.000 description 7
- 230000002159 abnormal effect Effects 0.000 description 7
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- 238000006243 chemical reaction Methods 0.000 description 4
- 238000009826 distribution Methods 0.000 description 4
- 238000000731 high angular annular dark-field scanning transmission electron microscopy Methods 0.000 description 4
- 238000005229 chemical vapour deposition Methods 0.000 description 3
- 150000001875 compounds Chemical class 0.000 description 3
- 238000010894 electron beam technology Methods 0.000 description 3
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- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 description 2
- BVKZGUZCCUSVTD-UHFFFAOYSA-L Carbonate Chemical compound [O-]C([O-])=O BVKZGUZCCUSVTD-UHFFFAOYSA-L 0.000 description 2
- 238000003917 TEM image Methods 0.000 description 2
- 229910001315 Tool steel Inorganic materials 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 229910021480 group 4 element Inorganic materials 0.000 description 2
- 229910021478 group 5 element Inorganic materials 0.000 description 2
- 229910021476 group 6 element Inorganic materials 0.000 description 2
- 230000007774 longterm Effects 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 description 2
- 239000011295 pitch Substances 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 239000012495 reaction gas Substances 0.000 description 2
- 230000001629 suppression Effects 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 238000012935 Averaging Methods 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 239000000853 adhesive Substances 0.000 description 1
- 230000001070 adhesive effect Effects 0.000 description 1
- UQZIWOQVLUASCR-UHFFFAOYSA-N alumane;titanium Chemical compound [AlH3].[Ti] UQZIWOQVLUASCR-UHFFFAOYSA-N 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
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- 238000002230 thermal chemical vapour deposition Methods 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
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Abstract
Description
本発明は、熱伝導性が悪い切削材を含む高負荷が作用する高速断続切削加工であっても、硬質被覆層が優れた耐チッピング性・耐欠損性を備えることにより、長期の使用にわたって優れた切削性能を発揮する表面被覆切削工具（以下、被覆工具ということがある）に関するものである。 The present invention is excellent over a long period of use because the hard coating layer has excellent chipping resistance and fracture resistance even in high-speed intermittent cutting where a high load including a cutting material with poor thermal conductivity acts. The present invention relates to a surface-coated cutting tool (hereinafter also referred to as a coated tool) that exhibits excellent cutting performance.
従来、炭化タングステン（以下、ＷＣで示す）基超硬合金、炭窒化チタン（以下、ＴｉＣＮで示す）基サーメットあるいは立方晶窒化ホウ素（以下、ｃＢＮで示す）基超高圧焼結体で構成された工具基体（以下、これらを総称して工具基体という）の表面に、硬質被覆層として、Ｔｉ−Ａｌ系の複合炭窒化物層を蒸着法により被覆形成した被覆工具があり、これらは、すぐれた耐摩耗性を発揮することが知られている。
ただ、前記従来のＴｉ−Ａｌ系の複合炭窒化物層を被覆形成した被覆工具は、比較的耐摩耗性に優れるものの、高速断続切削条件で用いた場合にチッピング等の異常損耗を発生しやすいことから、硬質被覆層の改善についての種々の提案がなされている。
Conventionally, tungsten carbide (hereinafter referred to as WC) based cemented carbide, titanium carbonitride (hereinafter referred to as TiCN) based cermet, or cubic boron nitride (hereinafter referred to as cBN) based super high pressure sintered body. There is a coated tool in which a Ti—Al-based composite carbonitride layer is formed on the surface of a tool substrate (hereinafter collectively referred to as a tool substrate) by a vapor deposition method as a hard coating layer. It is known to exhibit wear resistance.
However, the coated tool formed by coating the conventional Ti—Al based composite carbonitride layer is relatively excellent in wear resistance, but is likely to cause abnormal wear such as chipping when used under high-speed intermittent cutting conditions. Accordingly, various proposals have been made for improving the hard coating layer.
例えば、特許文献１には、基材と、その表面に形成された硬質被膜とを含み、
前記硬質被膜は１または２以上の層により構成され、前記層のうち少なくとも１層は、硬質粒子を含む層であり、前記硬質粒子は、第１単位層と第２単位層とが交互に積層された多層構造を含み、前記第１単位層は、周期表の４族元素、５族元素、６族元素およびＡｌからなる群より選ばれる１種以上の元素と、Ｂ、Ｃ、ＮおよびＯからなる群より選ばれる１種以上の元素とからなる第１化合物を含み、前記第２単位層は、周期表の４族元素、５族元素、６族元素およびＡｌからなる群より選ばれる１種以上の元素と、Ｂ、Ｃ、ＮおよびＯからなる群より選ばれる１種以上の元素とからなる第２化合物を含む、被覆工具により、耐摩耗性と耐溶着性を向上させることが提案されている。
For example, Patent Document 1 includes a base material and a hard coating formed on the surface thereof,
The hard coating is composed of one or more layers, and at least one of the layers is a layer containing hard particles, and the hard particles are alternately laminated with first unit layers and second unit layers. The first unit layer includes one or more elements selected from the group consisting of Group 4 elements, Group 5 elements, Group 6 elements and Al of the periodic table, and B, C, N and O Wherein the second unit layer is selected from the group consisting of Group 4 elements, Group 5 elements, Group 6 elements and Al of the periodic table. Proposed to improve wear resistance and welding resistance with a coated tool comprising a second compound comprising at least one element and at least one element selected from the group consisting of B, C, N and O Has been.
また、特許文献２には、基体上に柱状結晶組織を有する窒化チタンアルミニウム硬質皮膜を形成し、該硬質皮膜が、（Ｔｉｘ１Ａｌｙ１）Ｎ（ただし、ｘ１及びｙ１はそれぞれ原子比でｘ１＝０．００５〜０．１、及びｙ１＝０．９９５〜０．９を満たす数字である。）で表される組成を有するｆｃｃ構造の高Ａｌ含有ＴｉＡｌＮと、（Ｔｉｘ２Ａｌｙ２）Ｎ（ただし、ｘ２及びｙ２はそれぞれ原子比でｘ２＝０．５〜０．９、及びｙ２＝０．５〜０．１を満たす数字である。）で表される組成を有するｆｃｃ構造の網目状高Ｔｉ含有ＴｉＡｌＮを有するとともに、前記高Ａｌ含有ＴｉＡｌＮが前記網目状高Ｔｉ含有ＴｉＡｌＮに囲まれている被覆工具により、優れた耐摩耗性及び耐酸化性を発揮することが記載されている。 Further, in Patent Document 2, a titanium aluminum nitride hard film having a columnar crystal structure is formed on a substrate, and the hard film is (Tix 1 Aly 1 ) N (where x 1 and y 1 are atomic ratios, respectively). high Al content TiAlN having an fcc structure having a composition represented by: x 1 = 0.005 to 0.1 and y 1 = 0.995 to 0.9), and (Tix 2 Aly 2 ) N (provided that, x 2 = 0.5~0.9 x 2 and y 2 are each an atomic ratio, and a number satisfying y 2 = 0.5 to 0.1.) a composition represented by the The coated tool in which the high Al content TiAlN has a network-like high Ti content TiAlN having an fcc structure and the high Al content TiAlN is surrounded by the network high Ti content TiAlN can exhibit excellent wear resistance and oxidation resistance. Are listed.
特許文献３には、工具基体の表面に、硬質被覆層を設け、
（ａ）前記硬質被覆層は、化学蒸着法により成膜された平均層厚１〜２０μｍのＴｉとＡｌの複合窒化物層または複合炭窒化物層を少なくとも含み、前記複合窒化物層または前記複合炭窒化物層の組成を組成式：（Ｔｉ１−ｘＡｌｘ）（ＣｙＮ１−ｙ）で表した場合、前記複合窒化物層または前記複合炭窒化物層のＡｌのＴｉとＡｌの合量に占める平均含有割合Ｘａｖｇ、および前記複合窒化物層または前記複合炭窒化物層のＣのＣとＮの合量に占める平均含有割合Ｙａｖｇ（但し、Ｘａｖｇ、Ｙａｖｇはいずれも原子比）が、それぞれ、０．６０≦Ｘａｖｇ≦０．９５、０≦Ｙａｖｇ≦０．００５を満足し、
（ｂ）前記複合窒化物層または前記複合炭窒化物層は、ＮａＣｌ型の面心立方構造を有する複合窒化物または複合炭窒化物の相を少なくとも含み、
（ｃ）また、前記複合窒化物層または前記複合炭窒化物層について、電子線後方散乱回折装置を用いて、前記複合窒化物層または前記複合炭窒化物層内のＮａＣｌ型の面心立方構造を有する個々の結晶粒の結晶方位を前記複合窒化物層または前記複合炭窒化物層の縦断面方向から解析した場合、前記工具基体の表面の法線方向に対して前記結晶粒の結晶面である｛１００｝面の法線がなす傾斜角を測定し、該傾斜角のうち０〜４５度の範囲内にある傾斜角を０．２５度のピッチ毎に区分して、各区分内に存在する度数を集計して得られた傾斜角度数分布において、０〜１０度の範囲内の傾斜角区分に最高ピークが存在すると共に、前記０〜１０度の範囲内に存在する度数の合計が、前記傾斜角度数分布における度数全体の３５％以上であり、
（ｄ）また、前記工具基体の表面の前記法線方向に沿って、前記複合窒化物層または前記複合炭窒化物層における前記ＮａＣｌ型の面心立方構造を有する結晶粒内に、組成式：（Ｔｉ１−ｘＡｌｘ）（ＣｙＮ１−ｙ）におけるＴｉとＡｌの周期的な組成変化が存在し、周期的に変化するｘの極大値の平均と極小値の平均の差Δｘが０．０３〜０．２５であり、
（ｅ）さらに、前記複合窒化物層または前記複合炭窒化物層中のＴｉとＡｌの周期的な組成変化が存在するＮａＣｌ型の面心立方構造を有する結晶粒において、その前記工具基体の表面の前記法線方向に沿った周期が３〜１００ｎｍである、被覆工具が、耐摩耗性や耐チッピング性に優れていると記載されている。
In Patent Document 3, a hard coating layer is provided on the surface of a tool base,
(A) The hard coating layer includes at least a composite nitride layer or composite carbonitride layer of Ti and Al having an average layer thickness of 1 to 20 μm formed by a chemical vapor deposition method, and the composite nitride layer or the composite When the composition of the carbonitride layer is expressed by a composition formula: (Ti 1-x Al x ) (C y N 1-y ), Al of the composite nitride layer or the composite carbonitride layer of Ti and Al The average content ratio X avg occupying the total amount, and the average content ratio Y avg occupying the total amount of C and N in C of the composite nitride layer or the composite carbonitride layer (where X avg and Y avg are both Atomic ratio) satisfy 0.60 ≦ X avg ≦ 0.95 and 0 ≦ Y avg ≦ 0.005, respectively.
(B) The composite nitride layer or the composite carbonitride layer includes at least a composite nitride or composite carbonitride phase having a NaCl-type face-centered cubic structure,
(C) Further, for the composite nitride layer or the composite carbonitride layer, an NaCl-type face-centered cubic structure in the composite nitride layer or the composite carbonitride layer is obtained using an electron beam backscattering diffractometer. When the crystal orientation of each crystal grain having the above is analyzed from the longitudinal cross-sectional direction of the composite nitride layer or the composite carbonitride layer, the crystal plane of the crystal grain with respect to the normal direction of the surface of the tool base Measure the inclination angle formed by the normal of a certain {100} plane, and divide the inclination angle within the range of 0 to 45 degrees out of the inclination angle by 0.25 degree pitch, and exist in each section In the inclination angle distribution obtained by counting the frequencies to be performed, the highest peak exists in the inclination angle section within the range of 0 to 10 degrees, and the total of the frequencies existing within the range of 0 to 10 degrees is 35% or more of the entire frequency in the tilt angle number distribution,
(D) In the crystal grains having the NaCl-type face-centered cubic structure in the composite nitride layer or the composite carbonitride layer along the normal direction of the surface of the tool base, a composition formula: There is a periodic composition change of Ti and Al in (Ti 1-x Al x ) (C y N 1-y ), and the difference Δx between the average of the local maximum value and the average of the local minimum value of x that periodically changes is 0.03-0.25,
(E) Further, in the crystal grains having a NaCl-type face-centered cubic structure in which a periodic composition change of Ti and Al in the composite nitride layer or the composite carbonitride layer exists, the surface of the tool base It is described that the coated tool whose period along the normal direction is 3 to 100 nm is excellent in wear resistance and chipping resistance.
特許文献４には、工具基体の表面に、硬質被覆層を設け、
（ａ）前記硬質被覆層は、化学蒸着法により成膜された平均層厚１〜２０μｍのＴｉとＡｌの複合窒化物または複合炭窒化物層を少なくとも含み、組成式：（Ｔｉ１−ｘＡｌｘ）（ＣｙＮ１−ｙ）で表した場合、前記複合窒化物または複合炭窒化物層のＡｌのＴｉとＡｌの合量に占める平均含有割合ＸａｖｇおよびＣのＣとＮの合量に占める平均含有割合Ｙａｖｇ（但し、Ｘａｖｇ、Ｙａｖｇはいずれも原子比）が、それぞれ、０．６０≦Ｘａｖｇ≦０．９５、０≦Ｙａｖｇ≦０．００５を満足し、
（ｂ）前記複合窒化物または複合炭窒化物層は、ＮａＣｌ型の面心立方構造を有する複合窒化物または複合炭窒化物の相を少なくとも含み、
（ｃ）また、前記複合窒化物または複合炭窒化物層について、電子線後方散乱回折装置を用いて、複合窒化物または複合炭窒化物層内のＮａＣｌ型の面心立方構造を有する個々の結晶粒の結晶方位を、前記複合窒化物または複合炭窒化物層の縦断面方向から解析した場合、工具基体表面の法線方向に対する前記結晶粒の結晶面である｛１１１｝面の法線がなす傾斜角を測定し、該傾斜角のうち法線方向に対して０〜４５度の範囲内にある傾斜角を０．２５度のピッチ毎に区分して各区分内に存在する度数を集計し傾斜角度数分布を求めたとき、０〜１０度の範囲内の傾斜角区分に最高ピークが存在すると共に、前記０〜１０度の範囲内に存在する度数の合計が、前記傾斜角度数分布における度数全体の４５％以上の割合を示し、
（ｄ）前記複合窒化物または複合炭窒化物層について、該層の縦断面方向から観察した場合に、複合窒化物または複合炭窒化物層内のＮａＣｌ型の面心立方構造を有する個々の結晶粒の平均粒子幅Ｗが０．１〜２．０μｍ、平均アスペクト比Ａが２〜１０である柱状組織を有し、
（ｅ）また、前記複合窒化物または複合炭窒化物層の前記ＮａＣｌ型の面心立方構造を有する個々の結晶粒内に、組成式：（Ｔｉ１−ｘＡｌｘ）（ＣｙＮ１−ｙ）におけるＴｉとＡｌの周期的な組成変化が該結晶粒の＜００１＞で表される等価の結晶方位のうちの一つの方位に沿って存在し、周期的に変化するｘの極大値の平均と極小値の平均の差Δｘが０．０３〜０．２５である、被覆工具が、耐摩耗性、耐チッピング性、耐欠損性に優れていると記載されている。
In Patent Document 4, a hard coating layer is provided on the surface of the tool base,
(A) The hard coating layer includes at least a composite nitride or composite carbonitride layer of Ti and Al having an average layer thickness of 1 to 20 μm formed by a chemical vapor deposition method, and has a composition formula: (Ti 1-x Al x ) When expressed by (C y N 1-y ), the average content ratio Xavg in the total amount of Ti and Al in the composite nitride or composite carbonitride layer and the total amount of C and N in C The average content ratio Yavg (where Xavg and Yavg are both atomic ratios) satisfy 0.60 ≦ Xavg ≦ 0.95 and 0 ≦ Yavg ≦ 0.005, respectively.
(B) The composite nitride or composite carbonitride layer includes at least a composite nitride or composite carbonitride phase having a NaCl-type face-centered cubic structure,
(C) Further, with respect to the composite nitride or composite carbonitride layer, each crystal having an NaCl type face-centered cubic structure in the composite nitride or composite carbonitride layer using an electron beam backscattering diffractometer When the crystal orientation of the grains is analyzed from the longitudinal section direction of the composite nitride or composite carbonitride layer, the normal of the {111} plane that is the crystal plane of the crystal grains with respect to the normal direction of the surface of the tool base is formed. The inclination angle is measured, and the inclination angles within the range of 0 to 45 degrees with respect to the normal direction among the inclination angles are divided into pitches of 0.25 degrees, and the frequencies existing in each division are tabulated. When the inclination angle frequency distribution is obtained, the highest peak is present in the inclination angle section within the range of 0 to 10 degrees, and the sum of the frequencies existing within the range of 0 to 10 degrees is in the inclination angle number distribution. Shows more than 45% of the total frequency,
(D) Individual crystals having a NaCl-type face-centered cubic structure in the composite nitride or composite carbonitride layer when observed from the longitudinal section direction of the composite nitride or composite carbonitride layer Having a columnar structure having an average particle width W of 0.1 to 2.0 μm and an average aspect ratio A of 2 to 10;
(E) In each crystal grain having the NaCl-type face-centered cubic structure of the composite nitride or composite carbonitride layer, a composition formula: (Ti 1-x Al x ) (C y N 1- The periodic composition change of Ti and Al in y ) exists along one of the equivalent crystal orientations represented by <001> of the crystal grains, and the periodically changing x maximum value of x It is described that a coated tool having a difference Δx between an average and an average of a minimum value of 0.03 to 0.25 is excellent in wear resistance, chipping resistance, and fracture resistance.
近年の切削加工における省力化および省エネ化の要求は強く、これに伴い、切削加工は一段と高速化、高効率化の傾向にあり、被覆工具には、より一層、耐チッピング性、耐欠損性、耐剥離性等の耐異常損傷性が求められるとともに、長期の使用にわたって優れた耐摩耗性が求められている。
しかし、前記特許文献１に記載されている被覆工具は、耐酸化性が低く高速断続切削に供したときにはチッピングが発生しやすく、満足できる切削性能を有しているとはいえない。
In recent years, there has been a strong demand for energy saving and energy saving in cutting, and along with this, cutting tends to be faster and more efficient, and the coated tool has even more chipping resistance, chipping resistance, Abnormal damage resistance such as peel resistance is required, and excellent wear resistance is required over a long period of use.
However, the coated tool described in Patent Document 1 has low oxidation resistance and is prone to chipping when subjected to high-speed intermittent cutting, and cannot be said to have satisfactory cutting performance.
また、前記特許文献２に記載された被覆工具は、高Ａｌ含有ＴｉＡｌＮと高Ｔｉ含有ＴｉＡｌＮとのＡｌ含有割合の差が大きく、両者の界面における密着力が十分でないため高速断続切削に供した場合にはチッピングが発生しやすく、耐熱亀裂進展性も不十分であって、満足する切削性能を発揮するとは言えないという課題があった。 In addition, the coated tool described in Patent Document 2 has a large difference in the Al content ratio between high Al content TiAlN and high Ti content TiAlN, and the adhesive force at the interface between the two is not sufficient, so when subjected to high-speed intermittent cutting However, there is a problem that chipping is likely to occur and the thermal crack propagation is insufficient, and it cannot be said that satisfactory cutting performance is exhibited.
さらに、前記特許文献３および前記特許文献４に記載された被覆工具は、ＡｌとＴｉの複合窒化物のＡｌとＴｉの周期的な組成変化を有し、耐チッピング性に優れるものの、ＡｌとＴｉの周期的な組成変化の無い方向への耐亀裂伝播性には劣るため、より負荷の高い高速断続切削に供した場合にはチッピングが発生しやすく満足する切削性能を発揮し得ない場合があった。 Further, the coated tools described in Patent Document 3 and Patent Document 4 have a periodic composition change of Al and Ti of a composite nitride of Al and Ti, and have excellent chipping resistance, but Al and Ti Therefore, when subjected to high-speed intermittent cutting with higher load, chipping is likely to occur, and satisfactory cutting performance may not be exhibited. It was.
そこで、本発明は、より高負荷の高速断続切削加工に供したときであっても、優れた耐チッピング性、耐欠損性を備え、長期の使用にわって優れた切削性能を発揮する被覆工具を提供することを目的とする。 Accordingly, the present invention provides a coated tool that has excellent chipping resistance and fracture resistance and exhibits excellent cutting performance over a long period of use even when subjected to high-speed intermittent cutting with a higher load. The purpose is to provide.
本発明者らは、ＡｌとＴｉの複合窒化物または複合炭窒化物層を含む硬質被覆層（以下、「ＡｌＴｉＣＮ層」ということがある）を蒸着形成した被覆工具の組織について鋭意検討したところ、高Ａｌ含有のＡｉＴｉＣＮ領域（以下、高Ａｌ含有領域）と低Ａｌ含有のＡｌＴｉＣＮ領域（以下、低Ａｌ含有領域）とのＡｌ濃度差を所定の範囲に抑え、高Ａｌ含有領域が低Ａｌ含有領域に囲まれた二相組織とすると、高Ａｌ含有領域と低Ａｌ含有領域との３次元的な密着性が向上し、両者の界面が破壊起点となることを防止できるとの新たな知見を得た。 The inventors of the present invention have made extensive studies on the structure of a coated tool on which a hard coating layer including a composite nitride of Al and Ti or a composite carbonitride layer (hereinafter also referred to as “AlTiCN layer”) is formed by vapor deposition. The Al concentration difference between the high Al content AiTiCN region (hereinafter referred to as high Al content region) and the low Al content AlTiCN region (hereinafter referred to as low Al content region) is suppressed within a predetermined range, and the high Al content region is a low Al content region. New knowledge has been obtained that the two-phase structure surrounded by the metal improves the three-dimensional adhesion between the high Al content region and the low Al content region, and prevents the interface between the two from becoming the origin of fracture. It was.
本発明は、前記知見に基づいてなされたものであって、
「（１）炭化タングステン基超硬合金、炭窒化チタン基サーメットまたは立方晶窒化ホウ素基超高圧焼結体のいずれかで構成された工具基体の表面に、硬質被覆層が設けられた表面被覆切削工具において、
（ａ）前記硬質被覆層は、平均層厚１．０〜２０．０μｍのＴｉとＡｌの複合窒化物または複合炭窒化物層を少なくとも含み、
（ｂ）前記ＴｉとＡｌの複合窒化物または複合炭窒化物層は、ＮａＣｌ型の面心立方構造を有する複合窒化物または複合炭窒化物の相を少なくとも含み、
（ｃ）前記ＴｉとＡｌの複合窒化物または複合炭窒化物層において、該相は組成式（Ａｌｘ１Ｔｉ１−ｘ１）（Ｃｙ１Ｎ１−ｙ１）で表される高Ａｌ含有領域が組成式（Ａｌｘ２Ｔｉ１−ｘ２）（Ｃｙ２Ｎ１−ｙ２）で表される低Ａｌ含有領域に囲まれている二相組織を有し、
ＡｌのＴｉとＡｌの合量に占める平均含有割合ｘ１、ｘ２およびＣのＣとＮの合量に占める平均含有割合ｙ１、ｙ２（但し、ｘ１、ｘ２、ｙ１、ｙ２はいずれも原子比）が、それぞれ、０．７０＜ｘ１＜０．９３、０．４０＜ｘ２＜０．８５、０．００００≦ｙ１≦０．００５０、０．００００≦ｙ２≦０．００５０を満足し、高Ａｌ含有領域のＡｌのＴｉとＡｌの合量に占める含有割合ｘ１の最小値ｘ１ｍｉｎ、低Ａｌ含有領域のＡｌのＴｉとＡｌの合量に占める含有割合ｘ２の最大値ｘ２ｍａｘ（但し、ｘ１ｍｉｎ、ｘ２ｍａｘはいずれも原子比）が０．０５＜ｘ１ｍｉｎ−ｘ２ｍａｘ＜０．３０を満足することを特徴とする表面被覆切削工具。
（２）前記二相組織は、前記硬質被覆層の縦断面において４０面積％以上存在することを特徴とする（１）に記載の表面被覆切削工具。
（３）縦断面における前記高Ａｌ含有領域と前記低Ａｌ含有領域を含む８０ｎｍ×８０ｎｍの領域において、該低Ａｌ含有領域に囲まれた該高Ａｌ含有領域の個数が１０個以上１０００個未満であることを特徴とする（１）または（２）に記載の表面被覆切削工具。
である。
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 In the tool
(A) The hard coating layer includes at least a composite nitride or composite carbonitride layer of Ti and Al having an average layer thickness of 1.0 to 20.0 μm,
(B) the Ti and Al composite nitride or composite carbonitride layer includes at least a composite nitride or composite carbonitride phase having a NaCl-type face-centered cubic structure;
(C) In the composite nitride or composite carbonitride layer of Ti and Al, the phase is composed of a high Al content region represented by a composition formula (Al x1 Ti 1-x1 ) (C y1 N 1-y1 ). Having a two-phase structure surrounded by a low Al-containing region represented by the formula (Al x2 Ti 1-x2 ) (C y2 N 1-y2 ),
Average content ratios x 1 , x 2 in the total amount of Ti and Al in Al and average content ratios y 1 , y 2 in the total amount of C and N in C (where x 1 , x 2 , y 1 , y 2 are atomic ratios) of 0.70 <x 1 <0.93, 0.40 <x 2 <0.85, 0.0000 ≦ y 1 ≦ 0.0050, 0.0000 ≦ y 2, respectively. ≦ 0.0050, the content ratio x 1 min of the content ratio x 1 in the total amount of Ti and Al in the high Al content region, the content ratio in the total content of Ti and Al in the low Al content region maximum x 2max of x 2 (where, x 1min, x 2max any atomic ratio) surface-coated cutting tool, wherein a satisfies 0.05 <x 1min -x 2max <0.30 .
(2) The surface-coated cutting tool according to (1), wherein the two-phase structure is present in an area of 40% by area or more in the longitudinal section of the hard coating layer.
(3) In the 80 nm × 80 nm region including the high Al content region and the low Al content region in the longitudinal section, the number of the high Al content regions surrounded by the low Al content region is 10 or more and less than 1000 The surface-coated cutting tool according to (1) or (2), wherein
It is.
本発明の被覆工具は、低Ａｌ含有領域に囲まれる高Ａｌ含有領域が存在することにより、熱伝導性が悪い切削材を含む高速断続切削加工時であっても３次元的に存在するＡｌ組成が変化する界面において、亀裂進展が抑制され、優れた耐異常損傷性を発揮し、また、高Ａｌ含有領域と低Ａｌ含有領域とのＡｌの最小濃度差であるｘ１ｍｉｎ−ｘ２ｍａｘが、０．０５＜ｘ１ｍｉｎ−ｘ２ｍａｘ＜０．３０を満たすことにより、高Ａｌ含有領域と低Ａｌ含有領域の３次元的密着性が高まり、その界面が破壊起点となることを防止する、という優れた効果を奏する。 Since the coated tool of the present invention has a high Al content region surrounded by a low Al content region, the Al composition exists three-dimensionally even during high-speed intermittent cutting including a cutting material with poor thermal conductivity. In the interface where the change occurs, crack growth is suppressed, excellent abnormal damage resistance is exhibited, and the minimum difference in Al concentration between the high Al content region and the low Al content region is x 1min -x 2max is 0. .05 <x 1min −x 2max <0.30, the three-dimensional adhesion between the high Al-containing region and the low Al-containing region is improved, and the interface is prevented from becoming a fracture starting point. There is an effect.
次に、本発明について、より詳細に説明する。 Next, the present invention will be described in more detail.
硬質被覆層の平均層厚：
本発明の硬質被覆層は、後述するように、組成式：（ＡｌｘｉＴｉ１−ｘｉ）（ＣｙｉＮ１−ｙｉ）（ただし、ｉ＝１または２）で表されるＴｉとＡｌの複合窒化物または複合炭窒化物（ＴｉＡｌＣＮ）層を少なくとも含む。このＴｉＡｌＣＮ層は、硬さが高く、優れた耐摩耗性を有するが、特に平均層厚が１．０〜２０．０μｍのとき、その効果が際立って発揮される。その理由は、平均層厚が１．０μｍ未満では、層厚が薄いため長期の使用にわっての耐摩耗性を十分確保することができず、一方、その平均層厚が２０．０μｍを超えると、ＴｉＡｌＣＮ層の結晶粒が粗大化し易くなり、チッピングを発生しやすくなるためである。
Average thickness of hard coating layer:
As described later, the hard coating layer of the present invention is a composite of Ti and Al represented by the composition formula: (Al xi Ti 1-xi ) (C y i N 1-y i) (where i = 1 or 2). At least a nitride or composite carbonitride (TiAlCN) layer is included. This TiAlCN 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 μm. The reason is that if the average layer thickness is less than 1.0 μm, the layer thickness is so thin that sufficient wear resistance for long-term use cannot be ensured, while the average layer thickness exceeds 20.0 μm. This is because the crystal grains of the TiAlCN layer are easily coarsened and chipping is likely to occur.
ＴｉＡｌＣＮ層内のＮａＣｌ型の面心立方晶構造を有する結晶相：
前記ＴｉＡｌＣＮ層において、ＮａＣｌ型の面心立方晶構造を有する結晶粒を有する相が存在することが必要であり、その面積割合として６０面積％以上であることが好ましい。これにより、高硬度であるＮａＣｌ型の面心立方晶構造を有する結晶粒の面積比率が六方晶構造の結晶粒に比べて相対的に高くなり、硬さが向上するという効果を得ることができる。この面積率は、８５面積％以上がより好ましい。
Crystal phase having a NaCl-type face-centered cubic structure in the TiAlCN layer:
In the TiAlCN layer, a phase having crystal grains having a NaCl-type face-centered cubic structure must be present, and the area ratio is preferably 60 area% or more. As a result, the area ratio of the crystal grains having a highly hard NaCl type face centered cubic structure is relatively higher than that of the hexagonal crystal grains, and the effect of improving the hardness can be obtained. . As for this area ratio, 85 area% or more is more preferable.
ＴｉＡｌＣＮ層の組成：
図１は本発明のＴｉＡｌＣＮ層の縦断面（層厚方向断面）のＨＡＡＤＦ−ＳＴＥＭ像を表す。図２はＴｉＡｌＣＮ層の縦断面（層厚方向断面）の模式図を表し、図３は、この図２に示すＴｉＡｌＣＮ層に存在する二相組織を有する結晶粒を拡大した模式図である。この図１（図１の模式図の図３）に示すように、結晶粒は四角形の結晶相（第１相：ＨＡＡＤＦ−ＳＴＥＭ像では黒または濃い灰色）と、その周囲を取り囲む（例えば、網目状）結晶相（第２相：ＨＡＡＤＦ−ＳＴＥＭ像では白または薄い灰色）が存在する組織である。この第１相、第２相のそれぞれに対して、ＥＤＳ分析を行ったところ、第１相は高Ａｌ含有のＴｉＡｌＣＮ相であり、第２相は低Ａｌ含有のＴｉＡｌＣＮ相であることが判明した。また、図４は柱状結晶の場合の二相組織の一例を示す模式図である。
ここで、前記ＴｉＡｌＣＮ層は、第１相を組成式（Ａｌｘ１Ｔｉ１−ｘ１）（Ｃｙ１Ｎ１−ｙ１）で表わし、第２相を同じく組成式（Ａｌｘ２Ｔｉ１−ｘ２）（Ｃｙ２Ｎ１−ｙ２）で表わすと、ＡｌのＴｉとＡｌの合量に占める平均含有割合ｘ１、ｘ２およびＣのＣとＮの合量に占める平均含有割合ｙ１、ｙ２（但し、ｘ１、ｘ２、ｙ１、ｙ２はいずれも原子比）が、それぞれ、０．７０＜ｘ１＜０．９３、０．４０＜ｘ２＜０．８５、０．００００≦ｙ１≦０．００５０、０．００００≦ｙ２≦０．００５０、ｘ１の最小値をｘ１ｍｉｎ、ｘ２の最大値をｘ２ｍａｘとすると、０．０５＜ｘ１ｍｉｎ−ｘ２ｍａｘ＜０．３０にあることが必要十分である。
これらの数値範囲とする理由は、
ｘ１については、０．７０以下になると硬質被覆層全体の平均Ａｌ含有割合が低下することにより硬さが低下し、耐摩耗性が損なわれ、一方、０．９３以上になると硬さに劣る六方晶が析出しはじめ、耐摩耗性が低下し、
ｘ２については、０．４０以下になると硬さの低下に伴う耐摩耗性、耐チッピング性の低下の影響が大きくなり、一方、０．８５以上になると低Ａｌ含有領域がエネルギー的に不安定となり、切削時のように刃先に断続的な機械的・熱的衝撃が加わる環境下において低Ａｌ含有領域と高Ａｌ含有領域の界面を中心に六方晶が析出するようになり強度低下を招き、破壊起点となってチッピング等の異常損傷を生じ、
ｘ１ｍｉｎ−ｘ２ｍａｘについては、０．０５以下ではＡｌ含有割合の差が小さいため、組成変調界面における亀裂伝播抑制が不十分となり、一方、０．３０以上ではＡｌ含有割合の差が大きいため、界面に生じる歪が大きくなり過ぎ、切削時に破壊起点となってチッピング等の異常損傷を生じる。
次に、ｘ１、ｘ２、ｙ１、ｙ２、ｘ１ｍｉｎ、ｘ２ｍａｘの測定方法について説明する。
高Ａｌ含有領域と低Ａｌ含有領域のそれぞれに、ナノビーム回折を行い、ＮａＣｌ型の面心立方構造の結晶粒であることを確認するとともに、ＥＤＳ（ビーム径１ｎｍ）を用いて、膜厚方向中心の任意の２０の領域で、高Ａｌ含有領域と低Ａｌ含有領域とを有する粒子の組成を分析して、高Ａｌ含有領域の平均Ａｌ含有割合ｘ１および低Ａｌ含有領域の平均Ａｌ含有割合ｘ２を求め、各領域のＣのＣとＮの合量に占める平均含有割合ｙ１、ｙ２を測定する。そして、測定された２０点の高Ａｌ含有領域のＡｌ含有割合が１〜３番目に小さい測定値を平均し、ｘ１ｍｉｎとして算出し、同様に測定された２０点の低Ａｌ含有領域のＡｌ含有割合の１〜３番目に大きい測定値を平均し、ｘ２ｍａｘとして算出する。
また、少なくとも、前記任意の２０の領域で測定される高Ａｌ含有領域のＡｌ含有割合は全て０．７超え、０．９３未満であること、または、前記任意の２０の領域で測定される低Ａｌ含有領域のＡｌ含有割合は全て０．４０を超え０．８５未満であることが、より望ましい。
なお、高Ａｌ含有領域が低Ａｌ含有領域に囲まれているとは、縦断面において高Ａｌ含有領域の周囲長の５０％以上が低Ａｌ含有領域に接していることをいう。
Composition of TiAlCN layer:
FIG. 1 shows a HAADF-STEM image of a longitudinal section (a section in the layer thickness direction) of the TiAlCN layer of the present invention. FIG. 2 is a schematic diagram of a longitudinal section (layer thickness direction section) of the TiAlCN layer, and FIG. 3 is an enlarged schematic diagram of crystal grains having a two-phase structure existing in the TiAlCN layer shown in FIG. As shown in FIG. 1 (FIG. 3 of the schematic diagram of FIG. 1), the crystal grains surround a rectangular crystal phase (first phase: black or dark gray in the HAADF-STEM image) and its periphery (for example, mesh A structure in which a crystalline phase (second phase: white or light gray in the HAADF-STEM image) exists. When EDS analysis was performed on each of the first phase and the second phase, it was found that the first phase was a high Al content TiAlCN phase and the second phase was a low Al content TiAlCN phase. . FIG. 4 is a schematic diagram showing an example of a two-phase structure in the case of columnar crystals.
Here, in the TiAlCN layer, the first phase is represented by a composition formula (Al x1 Ti 1-x1 ) (C y1 N 1-y1 ), and the second phase is similarly represented by the composition formula (Al x2 Ti 1-x2 ) (C expressed in y2 N 1-y2), the average proportion occupied in the total amount of the average content x 1, x 2 and C of C and N to total the total amount of Ti and Al Al y 1, y 2 (where, x 1 , x 2 , y 1 and y 2 are all atomic ratios) of 0.70 <x 1 <0.93, 0.40 <x 2 <0.85, 0.0000 ≦ y 1 ≦, respectively. 0.0050,0.0000 ≦ y 2 ≦ 0.0050, the minimum value x 1min of x 1, and the maximum value of x 2 and x 2max, in 0.05 <x 1min -x 2max <0.30 It is necessary and sufficient.
The reason for these numerical ranges is
For x 1 is decreased the hardness by the average Al content of whole the hard layer becomes 0.70 or less is reduced, the wear resistance is impaired, whereas, less hardness becomes 0.93 or more Hexagonal crystals begin to precipitate, wear resistance decreases,
For x 2, wear resistance due to the decrease in the hardness becomes 0.40 or less, the influence of the decrease in chipping resistance is increased, whereas, a low Al-containing region energetically unstable 0.85 In the environment where intermittent mechanical and thermal impacts are applied to the cutting edge as in cutting, hexagonal crystals are precipitated around the interface between the low Al content region and the high Al content region, resulting in a decrease in strength. Causes abnormal damage such as chipping as a starting point of destruction,
For x 1min -x 2max , since the difference in Al content is small at 0.05 or less, crack propagation suppression at the composition modulation interface is insufficient, whereas, at 0.30 or more, the difference in Al content is large, The strain generated at the interface becomes too large, and becomes a starting point of fracture during cutting, causing abnormal damage such as chipping.
Then, x 1, x 2, y 1, y 2, x 1min, measuring method of x 2max will be described.
Nano beam diffraction is performed on each of the high Al content region and the low Al content region to confirm that it is a NaCl type face centered cubic crystal grain, and using EDS (beam diameter 1 nm), the center in the film thickness direction The composition of particles having a high Al content region and a low Al content region is analyzed in any 20 regions of the above, and the average Al content rate x 1 of the high Al content region and the average Al content rate x of the low Al content region are analyzed. 2 is obtained, and the average content ratios y 1 and y 2 in the total amount of C and N of C in each region are measured. Then, the measured value of the Al content of the 20 high Al-containing regions was averaged from the first to the third smallest, calculated as x 1 min , and the Al content of the 20 low Al-containing regions measured in the same manner The 1st to 3rd largest measured values of the ratio are averaged and calculated as x2max .
Further, at least the Al content ratios of the high Al content region measured in the 20 arbitrary regions are all greater than 0.7 and less than 0.93, or low as measured in the 20 arbitrary regions. It is more desirable that the Al content in the Al-containing region is more than 0.40 and less than 0.85.
The phrase “the high Al content region is surrounded by the low Al content region” means that 50% or more of the perimeter of the high Al content region is in contact with the low Al content region in the longitudinal section.
二相領域の縦断面における面積割合：
二相領域の縦断面における面積割合は、４０％以上とすることが好ましい。その理由は、４０％以上であれば、より確実に亀裂伝播の抑制がより一層確実になされるためである。
ここで、縦断面における二相領域の面積割合は、例えば、ＴｉＡｌＣＮ層の縦断面のＴＥＭ像（倍率：５００００倍）より幅１μｍ×１μｍの視野において求め、少なくとも５視野の平均値として算出する。
Area ratio in longitudinal section of two-phase region:
The area ratio in the longitudinal section of the two-phase region is preferably 40% or more. The reason is that the crack propagation is more reliably suppressed if it is 40% or more.
Here, the area ratio of the two-phase region in the longitudinal section is obtained, for example, from a TEM image (magnification: 50000 times) of the longitudinal section of the TiAlCN layer in a visual field having a width of 1 μm × 1 μm and calculated as an average value of at least five visual fields.
縦断面における高Ａｌ含有領域と低Ａｌ含有領域を含む８０ｎｍ×８０ｎｍの領域において、低Ａｌ含有領域に囲まれた高Ａｌ含有領域の個数：
縦断面における高Ａｌ含有領域と低Ａｌ含有領域を含む８０ｎｍ×８０ｎｍの領域において、低Ａｌ含有領域に囲まれた高Ａｌ含有領域の個数が１０個以上１０００個未満であることが好ましい。その理由は、１０個未満ではひとつの領域の大きさが大き過ぎるため組成変調界面の亀裂伝播抑制が不十分になることがあり、１０００個以上では高Ａｌ含有領域と低Ａｌ含有領域の界面数が増えることにより局所的な密着強度の低下や塑性変形を生じやすくなるため耐チッピング性あるいは耐摩耗性の低下を招くことがあるためである。
The number of high Al-containing regions surrounded by the low Al-containing region in the 80 nm × 80 nm region including the high Al-containing region and the low Al-containing region in the longitudinal section:
In the 80 nm × 80 nm region including the high Al content region and the low Al content region in the longitudinal section, the number of high Al content regions surrounded by the low Al content region is preferably 10 or more and less than 1000. The reason for this is that if the number is less than 10, the size of one region is too large and crack propagation suppression of the composition modulation interface may be insufficient, and if it is 1000 or more, the number of interfaces between the high Al content region and the low Al content region This is because a decrease in local adhesion strength and plastic deformation are liable to occur due to an increase in the thickness, which may result in a decrease in chipping resistance or wear resistance.
縦断面における高Ａｌ含有領域と前記低Ａｌ含有領域を含む８０ｎｍ×８０ｎｍの領域において、低Ａｌ含有領域に囲まれた高Ａｌ含有領域の個数は以下のように求める。本発明のＴｉＡｌＣＮ層の縦断面（層厚方向断面）のＴＥＭ像（倍率：５０００００倍）あるいはそのＥＤＳマッピング像より、８０ｎｍ×８０ｎｍの領域において組成差によるコントラストの違い等を、画像処理を行うことで高Ａｌ含有領域と低Ａｌ含有領域を特定し、色分けすることが出来る。画像認識により着色された高Ａｌ含有領域の数をカウントすることで低Ａｌ含有領域に囲まれた高Ａｌ含有領域の個数を求める。 In the 80 nm × 80 nm region including the high Al content region and the low Al content region in the longitudinal section, the number of high Al content regions surrounded by the low Al content region is determined as follows. From the TEM image (magnification: 500,000 times) of the longitudinal section (layer thickness direction section) of the TiAlCN layer of the present invention or its EDS mapping image, image processing is performed for differences in contrast due to composition differences in the 80 nm × 80 nm region. Thus, the high Al content region and the low Al content region can be specified and color-coded. By counting the number of high Al content regions colored by image recognition, the number of high Al content regions surrounded by the low Al content region is obtained.
柱状結晶組織を有し、その結晶粒の平均粒子幅Ｗが０．１０〜３．００μｍ、平均アスペクト比Ａが２．０〜１０．０：
本発明において、ＴｉＡｌＣＮ層は柱状結晶組織を有し、その結晶粒の縦断面における平均粒子幅Ｗが０．１０〜３．００μｍ、平均アスペクト比Ａが２．０〜１０．０であることが望ましい。その理由は、平均粒子幅Ｗが０．１０μｍよりも小さい微粒結晶になると粒界の増加による耐塑性変形性の低下、耐酸化性の低下により異常損傷に至りやすくなる。一方平均粒子幅Ｗが３．００μｍよりも大きくなると粗大に成長した粒子の存在により、靱性が低下しやすくなる。また、平均アスペクト比Ａが２．０よりも小さい粒状結晶になると切削時に皮膜表面に生じるせん断応力に対してその界面が破壊起点となりやすくなってしまいチッピングの原因となる。また、平均アスペクト比Ａが１０．０を超えると、切削時に刃先に微小なチッピングが生じ、隣り合う柱状組織に欠けが生じた場合に、皮膜表面に生じるせん断応力に対しての抗力が小さくなりやすく、柱状組織が破断することで一気に損傷が進行し、大きなチッピングを生じる。したがって、結晶粒の平均粒子幅Ｗが０．１０〜３．００μｍ、平均アスペクト比Ａが２．０〜１０．０であることが望ましい。
次に、結晶粒の平均粒子幅Ｗと平均アスペクト比Ａの算出方法について説明する。まず、硬質皮膜の工具基体に平行な方向の１００μｍの観察視野において結晶粒界を判定する。結晶粒界の判定方法としては、電子線後方散乱回折装置を用いて縦断面方向から０．０１μｍ間隔の解析を行い、隣接する測定点（以下、ピクセルという）の間で５度以上の方位差がある場合、そこを粒界と定義する。ここで、縦断面方向とは、工具基体表面に垂直な方向を意味する。縦断面とは、工具基体表面に垂直な断面を意味する。そして、粒界で囲まれた領域を１つの結晶粒と定義する。ただし、隣接するピクセル全てと５度以上の方位差がある単独に存在するピクセルは結晶粒とせず、２ピクセル以上が連結しているものを結晶粒として取り扱う。このようにして、粒界判定を行い、結晶粒を特定する。次に、ある結晶粒ｉの結晶粒の層厚方向の最大長さをＨｉ、結晶粒の面積をＳｉとして求めて、結晶粒ｉの粒子幅ＷｉはＷｉ＝Ｓｉ／Ｈｉとして算出する。さらに、結晶粒ｉのアスペクト比ＡｉはＡｉ＝Ｈｉ／Ｗｉとして算出する。このようにして、任意の２０の結晶粒の粒子幅Ｗ１〜Ｗ２０を平均し、前記結晶粒の平均粒子幅Ｗとする。また、同様にして前記任意の２０の結晶粒のアスペクト比Ａ１〜Ａ２０を平均し、前記結晶粒の平均アスペクト比Ａとする。
なお、本発明ではアスペクト比Ａが２．０よりも小さい結晶粒を粒状結晶、アスペクト比Ａが２．０よりも大きい結晶粒を柱状結晶と、それぞれ、定義する。
It has a columnar crystal structure, the average grain width W of the crystal grains is 0.10 to 3.00 μm, and the average aspect ratio A is 2.0 to 10.0:
In the present invention, the TiAlCN layer has a columnar crystal structure, the average grain width W in the longitudinal section of the crystal grains is 0.10 to 3.00 μm, and the average aspect ratio A is 2.0 to 10.0. desirable. The reason for this is that when the average grain width W is smaller than 0.10 μm, it becomes easy to cause abnormal damage due to a decrease in plastic deformation resistance due to an increase in grain boundaries and a decrease in oxidation resistance. On the other hand, when the average particle width W is larger than 3.00 μm, the presence of coarsely grown particles tends to reduce toughness. In addition, when the average aspect ratio A is smaller than 2.0, the crystal becomes less likely to be a starting point of fracture due to shear stress generated on the surface of the coating during cutting, which causes chipping. Also, if the average aspect ratio A exceeds 10.0, the chip edge is slightly chipped at the time of cutting, and if the adjacent columnar structure is chipped, the resistance to the shear stress generated on the coating surface becomes small. It is easy, damage is advanced at a stretch by breaking the columnar structure, and large chipping occurs. Therefore, it is desirable that the average grain width W of the crystal grains is 0.10 to 3.00 μm and the average aspect ratio A is 2.0 to 10.0.
Next, a method for calculating the average grain width W and the average aspect ratio A of the crystal grains will be described. First, a crystal grain boundary is determined in an observation visual field of 100 μm in a direction parallel to the hard-coated tool base. As a method for determining a crystal grain boundary, an electron beam backscattering diffractometer is used to analyze an interval of 0.01 μm from the longitudinal cross-sectional direction, and an orientation difference of 5 degrees or more between adjacent measurement points (hereinafter referred to as pixels). If there is, it is defined as a grain boundary. Here, the longitudinal section direction means a direction perpendicular to the tool base surface. A longitudinal section means a section perpendicular to the tool base surface. A region surrounded by the grain boundary is defined as one crystal grain. However, a single pixel that has an orientation difference of 5 degrees or more with all adjacent pixels is not a crystal grain, and a pixel having two or more pixels connected is treated as a crystal grain. In this way, grain boundary determination is performed to identify crystal grains. Next, the maximum length of a crystal grain i in the layer thickness direction is determined as H i , and the area of the crystal grain is determined as S i , and the grain width W i of the crystal grain i is expressed as W i = S i / H i. Calculate as Furthermore, the aspect ratio A i grain i is calculated as A i = H i / W i. In this way, the particle widths W 1 to W 20 of 20 arbitrary crystal grains are averaged to obtain the average particle width W of the crystal grains. Similarly, the average aspect ratios A 1 to A 20 of the 20 arbitrary crystal grains are averaged to obtain the average aspect ratio A of the crystal grains.
In the present invention, crystal grains having an aspect ratio A smaller than 2.0 are defined as granular crystals, and crystal grains having an aspect ratio A larger than 2.0 are defined as columnar crystals.
下部層および上部層：
本発明では、硬質被覆層として前記ＴｉＡｌＣＮ層を設けることによって十分な耐チッピング性、耐摩耗性を有するが、Ｔｉの炭化物層、窒化物層、炭窒化物層、炭酸化物層および炭窒酸化物層のうちの１層または２層以上からなり、０．１〜２０．０μｍの合計平均層厚を有するＴｉ化合物層を含む下部層を設けた場合、および／または、少なくとも酸化アルミニウム層を含む上部層が１．０〜２５．０μｍの合計平均層厚で設けられた場合には、これらの層が奏する効果と相俟って、一層優れた特性を発揮することができる。
Ｔｉの炭化物層、窒化物層、炭窒化物層、炭酸化物層および炭窒酸化物層のうちの１層または２層以上からなり、０．１〜２０．０μｍの合計平均層厚を有するＴｉ化合物層を含む下部層を設ける場合、下部層の合計平均層厚が０．１μｍ未満では、下部層の効果が十分に奏されず、一方、２０．０μｍを超えると結晶粒が粗大化し易くなり、チッピングを発生しやすくなる。また、酸化アルミニウム層を含む上部層の合計平均層厚が１．０μｍ未満では、上部層の効果が十分に奏されず、一方、２５．０μｍを超えると結晶粒が粗大化し易くなり、チッピングを発生しやすくなる。
Lower layer and upper layer:
In the present invention, the TiAlCN layer provided as the hard coating layer has sufficient chipping resistance and wear resistance. However, the Ti carbide layer, nitride layer, carbonitride layer, carbonate layer and carbonitride oxide 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 μm, and / or an upper portion comprising at least an aluminum oxide layer When the layers are provided with a total average layer thickness of 1.0 to 25.0 μm, combined with the effect produced 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 μm 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 μm, the effect of the lower layer is not sufficiently achieved. On the other hand, if it exceeds 20.0 μm, the crystal grains are likely to be coarsened. , Chipping is likely to occur. Further, if the total average layer thickness of the upper layer including the aluminum oxide layer is less than 1.0 μm, the effect of the upper layer is not sufficiently achieved. On the other hand, if it exceeds 25.0 μm, the crystal grains are likely to be coarsened and chipping is caused. It tends to occur.
製造方法：
本発明のＴｉＡｌＣＮ層は、例えば、次の条件におけるＴｉＡｌＣＮ層の形成の後、一例としてあげるアニール処理工程を行うことによって、作製することができる。
ＴｉＡｌＣＮ層の形成：
反応ガス組成（容量％）：
ガス群Ａ：ＮＨ３：２．００〜５．００％、Ｈ２：６０〜７５％、
ガス群Ｂ：ＡｌＣｌ３：０．６０〜１．００％、ＴｉＣｌ４：０．０７〜０．４０％、
Ｃ２Ｈ４：０．００〜０．５０、Ｎ２：０．００〜１２．００％、Ｈ２：残、
反応雰囲気圧力：４．０〜５．０ｋＰａ、反応雰囲気温度：７００〜８５０℃、
供給周期１．０００〜５．０００秒、
１周期当たりのガス供給時間０．０５０〜０．１２０秒、
ガス群Ａとガス群Ｂの供給の位相差０．０４５〜０．１１５秒
アニール処理：
アニール温度：９００〜１０００℃
アニール時間：１．０〜４．０時間
アニール雰囲気圧力：４．０〜５．０ｋＰａ
ガス組成：Ｈ２雰囲気
Production method:
The TiAlCN layer of the present invention can be produced, for example, by performing an annealing process as an example after the formation of the TiAlCN layer under the following conditions.
Formation of TiAlCN layer:
Reaction gas composition (volume%):
Gas group A: NH 3 : 2.00 to 5.00%, H 2 : 60 to 75%,
Gas group B: AlCl 3 : 0.60 to 1.00%, TiCl 4 : 0.07 to 0.40%,
C 2 H 4: 0.00~0.50, N 2: 0.00~12.00%, H 2: remainder,
Reaction atmosphere pressure: 4.0-5.0 kPa, Reaction atmosphere temperature: 700-850 ° C.,
Supply cycle 1.000-5.000 seconds,
Gas supply time per cycle 0.050 to 0.120 seconds,
Phase difference of supply of gas group A and gas group B 0.045 to 0.115 seconds Annealing treatment:
Annealing temperature: 900-1000 ° C
Annealing time: 1.0 to 4.0 hours Annealing atmosphere pressure: 4.0 to 5.0 kPa
Gas composition: H 2 atmosphere
次に、本発明の被覆工具を実施例により具体的に説明する。
なお、以下の実施例では、工具基体として、ＷＣ基超硬合金を用いた場合について説明するが、ＴｉＣＮ基サーメットおよびｃＢＮ基超高圧焼結体を工具基体として用いた場合も同様である。また、被覆工具としてはインサートに限らず、ドリル、メタルソー、リーマー、タップなどの切削工具に、本発明の被覆工具は好適に使用できることは言うまでもない。
Next, the coated tool of the present invention will be specifically described with reference to examples.
In the following examples, the case where a WC-based cemented carbide is used as the tool base will be described. However, the same applies to the case where a TiCN-based cermet and a cBN-based ultrahigh-pressure sintered body are used as the tool base. Moreover, it cannot be overemphasized that the coating tool of this invention can be used suitably for cutting tools, such as a drill, a metal saw, a reamer, a tap, as a coating tool not only an insert.
原料粉末として、いずれも０．１〜３．０μｍの平均粒径を有するＷＣ粉末、ＴｉＣ粉末、ＺｒＣ粉末、ＴａＣ粉末、ＮｂＣ粉末、Ｃｒ３Ｃ２粉末、ＴｉＮ粉末およびＣｏ粉末を用意し、これら原料粉末を、表１に示される配合組成に配合し、さらにワックスを加えてアセトン中で２４時間ボールミル混合し、減圧乾燥した後、９８ＭＰａの圧力で所定形状の圧粉体にプレス成形し、この圧粉体を５Ｐａの真空中、１３７０〜１４７０℃の範囲内の所定の温度に１時間保持の条件で真空焼結し、焼結後、ＩＳＯ規格ＳＥＥＮ１２０３ＡＦＳＮのインサート形状をもったＷＣ基超硬合金製の工具基体Ａ〜ＣおよびＩＳＯ規格ＣＮＭＧ１２０４１２のインサート形状をもったＷＣ基超硬合金製の工具基体Ｄ〜Ｆをそれぞれ製造した。 As raw material powders, WC powder, TiC powder, ZrC powder, TaC powder, NbC powder, Cr 3 C 2 powder, TiN powder and Co powder each having an average particle diameter of 0.1 to 3.0 μm are prepared. The raw material powder is blended in the blending composition shown in Table 1, added with wax, ball mill mixed in acetone for 24 hours, dried under reduced pressure, and press-molded into a green compact of a predetermined shape at a pressure of 98 MPa. WC-based cemented carbide with the insert shape of ISO standard SEEN1203AFSN after sintering the green compact in vacuum of 5 Pa at a predetermined temperature within the range of 1370 to 1470 ° C. for 1 hour. Tool bases A to C made of WC and cemented bases D to F made of a WC-base cemented carbide having an insert shape of ISO standard CNMG120212 were manufactured.
次に、これらの工具基体Ａ〜Ｆの表面に、ＣＶＤ装置を用い、ＴｉＡｌＣＮ層をＣＶＤにより形成した。
ＣＶＤ条件は、次のとおりである。
表３に示される形成条件Ａ〜Ｉ、すなわち、ＮＨ３とＨ２からなるガス群Ａと、ＴｉＣｌ４、ＡｌＣｌ３、Ｎ２、Ｈ２からなるガス群Ｂ、および、おのおのガスの供給方法として、反応ガス組成（％は、ガス群Ａおよびガス群Ｂを合わせた全体に対する容量％）を、ガス群ＡとしてＮＨ３：２．００〜５．００％、Ｈ２：６０〜７５％、ガス群ＢとしてＡｌＣｌ３：０．６０〜１．００％、ＴｉＣｌ４：０．０７〜０．４０％、Ｃ２Ｈ４：０．００〜０．５０、Ｎ２：０．００〜１２．００％、Ｈ２：残、反応雰囲気圧力：４．０〜５．０ｋＰａ、反応雰囲気温度：７００〜８５０℃、供給周期１．０００〜５．０００秒、１周期当たりのガス供給時間０．０５０〜０．１２０秒、ガス群Ａとガス群Ｂの供給の位相差０．０４５〜０．１１５秒とし、所定時間熱ＣＶＤ法による蒸着形成を行った。そして、その後、表４に示されるアニール処理条件Ｏ〜Ｗ、すなわち、温度：９００〜１０００℃、時間：１．０〜４．０時間、雰囲気圧力：４．０〜５．０ｋＰａのＨ２雰囲気で、アニール処理を行った。
前記の条件でＴｉＡｌＣＮ層を形成することにより、表６に示す平均層厚、Ａｌの平均含有割合ｘ１、ｘ２、ｘ１ｍｉｎ、ｘ２ｍａｘ、Ｃの平均含有割合ｙ１、ｙ２を有する本発明被覆工具１〜１８を製造した。
なお、本発明被覆工具１〜６、９、１１、１２、１４、１５、１８については、表２に示される形成条件で、表５に示される下部層および／または上部層を形成した。
Next, a TiAlCN layer was formed by CVD on the surface of these tool bases A to F using a CVD apparatus.
The CVD conditions are as follows.
Formation conditions A to I shown in Table 3, that is, a gas group A composed of NH 3 and H 2 , a gas group B composed of TiCl 4 , AlCl 3 , N 2 , and H 2 , and a method for supplying each gas , The reaction gas composition (% is the capacity% with respect to the total of the gas group A and the gas group B), NH 3 : 2.00 to 5.00%, H 2 : 60 to 75%, gas as the gas group A As group B, AlCl 3 : 0.60 to 1.00%, TiCl 4 : 0.07 to 0.40%, C 2 H 4 : 0.00 to 0.50, N 2 : 0.00 to 12.00 %, H 2 : remaining, reaction atmosphere pressure: 4.0 to 5.0 kPa, reaction atmosphere temperature: 700 to 850 ° C., supply cycle of 1.000 to 5.000 seconds, gas supply time per cycle of 0.050 0.120 seconds, phase difference of supply of gas group A and gas group B 0.0 It was set to 45 to 0.115 seconds, and vapor deposition was performed by a thermal CVD method for a predetermined time. And after that, annealing conditions O to W shown in Table 4, that is, temperature: 900 to 1000 ° C., time: 1.0 to 4.0 hours, atmospheric pressure: 4.0 to 5.0 kPa H 2 atmosphere Then, annealing treatment was performed.
By forming the TiAlCN layer under the above-described conditions, the average layer thickness, the average Al content ratio x 1 , x 2 , x 1 min , x 2max , and the average C content ratio y 1 , y 2 shown in Table 6 are shown. Invention coated tools 1-18 were produced.
In addition, about this invention coated tool 1-6, 9, 11, 12, 14, 15, 18, 18, the lower layer and / or the upper layer which were shown in Table 5 were formed on the formation conditions shown in Table 2.
また、比較の目的で、工具基体Ａ〜Ｆの表面に、表３に示される形成条件Ａ’〜Ｉ’で化学蒸着を行うことにより、表７に示される平均層厚（μｍ）を有し、ＴｉＡｌＣＮ層を含む硬質被覆層を蒸着形成して比較被覆工具１〜１８を製造した。
なお、本発明被覆工具と同様に、比較被覆工具１〜７、１０〜１５については、表２に示される形成条件で、表５に示される下部層および／または上部層を形成した。
For the purpose of comparison, chemical vapor deposition is performed on the surfaces of the tool bases A to F under the formation conditions A ′ to I ′ shown in Table 3, so that the average layer thickness (μm) shown in Table 7 is obtained. Comparative coating tools 1 to 18 were manufactured by vapor-depositing a hard coating layer including a TiAlCN layer.
In addition, similarly to this invention coated tool, about the comparison coated tools 1-7, 10-15, the lower layer and / or upper layer which were shown in Table 5 were formed on the formation conditions shown in Table 2.
また、本発明被覆工具１〜１８、比較被覆工具１〜１８の各構成層の工具基体に垂直な方向の断面（縦断面：層厚方向断面）を、走査型電子顕微鏡（倍率５０００倍）を用いて測定し、観察視野内の５点の層厚を測って平均して平均層厚を求めたところ、いずれも表６および表７に示される平均層厚であった。また、ｘ１、ｘ２、ｙ１、ｙ２等について、前述の方法にしたがって測定した。 Moreover, the cross section (longitudinal cross section: cross section in the layer thickness direction) perpendicular to the tool base of each constituent layer of the present coated tools 1 to 18 and comparative coated tools 1 to 18 is taken with a scanning electron microscope (5000 times magnification). When the average layer thickness was determined by measuring and averaging the five layer thicknesses within the observation field of view, both were the average layer thicknesses shown in Tables 6 and 7. Further, the x 1, x 2, y 1 , y 2 , etc., were measured according to the method described above.
次に、前記各種の被覆工具をいずれもカッタ径１２５ｍｍの工具鋼製カッタ先端部に固定治具にてクランプした状態で、本発明被覆工具１〜９、比較被覆工具１〜９について、以下に示す、合金鋼の高速断続切削の一種である乾式高速正面フライス、センターカット切削加工試験を実施し、切刃の逃げ面摩耗幅を測定した。
＜切削試験Ａ＞
本発明被覆工具１〜９、比較被覆工具１〜９に対して実施した。
カッタ径： １２５ｍｍ
被削材： ＪＩＳ・ＳＣＭ４４０幅１００ｍｍ、長さ４００ｍｍのブロック材
回転速度： １１４６ｍｉｎ−１、
切削速度： ４５０ｍ／ｍｉｎ、
切り込み： １．０ｍｍ、
一刃送り量： ０．１ｍｍ／刃、
切削時間： ６分、
（通常切削速度は、１５０−２５０ｍ／ｍｉｎ）
表８に切削試験の結果を示す。なお、比較被覆工具１〜９については、チッピング発生が原因で寿命に至ったため、寿命に至るまでの時間を示す。
Next, the present coated tools 1 to 9 and comparative coated tools 1 to 9 are as follows in the state where each of the various coated tools is clamped to a tool steel cutter tip portion having a cutter diameter of 125 mm by a fixing jig. The dry high-speed face milling, which is a kind of high-speed interrupted cutting of alloy steel, and a center-cut cutting test were performed, and the flank wear width of the cutting blade was measured.
<Cutting test A>
It implemented with respect to this invention coated tool 1-9 and comparative coated tool 1-9.
Cutter diameter: 125mm
Work material: JIS / SCM440 block material having a width of 100 mm and a length of 400 mm Rotational speed: 1146 min −1
Cutting speed: 450 m / min,
Cutting depth: 1.0mm,
Single-blade feed rate: 0.1 mm / tooth,
Cutting time: 6 minutes,
(Normal cutting speed is 150-250 m / min)
Table 8 shows the results of the cutting test. In addition, about the comparison coated tools 1-9, since it reached the lifetime due to chipping generation | occurrence | production, the time until it reaches a lifetime is shown.
次に、前記各種の被覆工具をいずれも工具鋼製バイトの先端部に固定治具にてネジ止めした状態で、本発明被覆工具１０〜１８、比較被覆工具１０〜１８について、以下に示す、Ｎｉ−１９Ｃｒ−１９Ｆｅ−３Ｍｏ−０．９Ｔｉ−０．５Ａｌ−５．１（Ｎｂ＋Ｔａ）合金の４スリット溝入り材の乾式高速断続旋削試験を実施し、いずれも切刃の逃げ面摩耗幅を測定した。
＜切削試験Ｂ＞
本発明被覆工具１０〜１８、比較被覆工具１０〜１８に対して実施した。
被削材： Ｎｉ−１９Ｃｒ−１９Ｆｅ−３Ｍｏ−０．９Ｔｉ−０．５Ａｌ−５．１（Ｎｂ＋Ｔａ）合金の長さ方向等間隔４本溝入り
切削速度： １００ｍ／ｍｉｎ、
切り込み： ０．５ｍｍ、
送り： ０．２ｍｍ／ｒｅｖ、
切削時間： ７分
（通常切削速度は、６０ｍ／ｍｉｎ）
表８に切削試験の結果を示す。なお、比較被覆工具１０〜１８については、チッピング発生が原因で寿命に至ったため、寿命に至るまでの時間を示す。
Next, in the state where each of the various coated tools is screwed to the tip of the tool steel tool with a fixing jig, the present coated tools 10-18 and comparative coated tools 10-18 are shown below. Conducted dry high-speed intermittent turning test on Ni-19Cr-19Fe-3Mo-0.9Ti-0.5Al-5.1 (Nb + Ta) alloy 4-slit grooved material and measured the flank wear width of the cutting edge in all cases did.
<Cutting test B>
It implemented with respect to this invention coated tool 10-18 and comparative coated tool 10-18.
Work material: Ni-19Cr-19Fe-3Mo-0.9Ti-0.5Al-5.1 (Nb + Ta) alloy with four grooves at regular intervals in the length direction Cutting speed: 100 m / min,
Cutting depth: 0.5mm,
Feed: 0.2mm / rev,
Cutting time: 7 minutes (normal cutting speed is 60 m / min)
Table 8 shows the results of the cutting test. In addition, about the comparison coated tools 10-18, since the lifetime was reached because of chipping, the time until the lifetime is reached is shown.
表８に示される結果から、本発明被覆工具１〜１８は、低Ａｌ含有領域に囲まれる高Ａｌ含有領域が存在することにより、亀裂進展が抑制され、優れた耐異常損傷性を発揮し、また、高Ａｌ含有領域と低Ａｌ含有領域とのＡｌの最小濃度差であるｘ１ｍｉｎ−ｘ２ｍａｘが、０．０５＜ｘ１ｍｉｎ−ｘ２ｍａｘ＜０．３０を満たすことにより、高Ａｌ含有領域と低Ａｌ含有領域の３次元的密着性が高まり、その界面が破壊起点となることを防止するため、熱伝導性が悪い切削材を含む高速断続切削加工に用いた場合であってチッピングの発生がなく、長期にわたって優れた耐摩耗性を発揮する。これに対して、本発明の被覆工具に規定される事項を一つでも満足していない比較被覆工具１〜１８は、熱伝導性が悪い切削材を含む高速断続切削加工に用いた場合にはチッピングが発生し、短時間で使用寿命に至っている。 From the results shown in Table 8, according to the present invention coated tools 1-18, the presence of a high Al-containing region surrounded by a low Al-containing region suppresses crack propagation, and exhibits excellent abnormal damage resistance. Further, when x 1min −x 2max which is the minimum concentration difference of Al between the high Al content region and the low Al content region satisfies 0.05 <x 1min −x 2max <0.30, In order to prevent three-dimensional adhesion in the low Al-containing region and the interface from becoming a starting point of fracture, chipping occurs when used for high-speed intermittent cutting including cutting materials with poor thermal conductivity. No long-term wear resistance. On the other hand, when the comparative coated tools 1 to 18 that do not satisfy even one of the matters defined in the coated tool of the present invention are used for high-speed intermittent cutting including a cutting material with poor thermal conductivity, Chipping occurs and the service life is reached in a short time.
前述のように、本発明の被覆工具は、熱伝導性が悪い被削材を含む高負荷が作用する高速断続切削加工であっても、高速断続切削加工の被覆工具として用いることができ、しかも、長期にわたって優れた耐摩耗性を発揮するから、切削装置の高性能化並びに切削加工の省力化及び省エネ化、さらには低コスト化に十分に満足できる対応ができるものである。 As described above, the coated tool of the present invention can be used as a coated tool for high-speed intermittent cutting even in high-speed intermittent cutting where a high load including a work material with poor thermal conductivity acts. Since it exhibits excellent wear resistance over a long period of time, it is possible to sufficiently satisfy the demand for higher performance of the cutting device, labor saving and energy saving of the cutting work, and further cost reduction.
Claims (4)
（ａ）前記硬質被覆層は、平均層厚１．０〜２０．０μｍのＴｉとＡｌの複合窒化物または複合炭窒化物層を少なくとも含み、
（ｂ）前記ＴｉとＡｌの複合窒化物または複合炭窒化物層は、ＮａＣｌ型の面心立方構造を有する複合窒化物または複合炭窒化物の相を少なくとも含み、
（ｃ）前記ＴｉとＡｌの複合窒化物または複合炭窒化物層において、該相は組成式（Ａｌｘ１Ｔｉ１−ｘ１）（Ｃｙ１Ｎ１−ｙ１）で表される高Ａｌ含有領域が組成式（Ａｌｘ２Ｔｉ１−ｘ２）（Ｃｙ２Ｎ１−ｙ２）で表される低Ａｌ含有領域に囲まれている二相組織を有し、
ＡｌのＴｉとＡｌの合量に占める平均含有割合ｘ１、ｘ２およびＣのＣとＮの合量に占める平均含有割合ｙ１、ｙ２（但し、ｘ１、ｘ２、ｙ１、ｙ２はいずれも原子比）が、それぞれ、０．７０＜ｘ１＜０．９３、０．４０＜ｘ２＜０．８５、０．００００≦ｙ１≦０．００５０、０．００００≦ｙ２≦０．００５０を満足し、高Ａｌ含有領域のＡｌのＴｉとＡｌの合量に占める含有割合ｘ１の最小値ｘ１ｍｉｎ、低Ａｌ含有領域のＡｌのＴｉとＡｌの合量に占める含有割合ｘ２の最大値ｘ２ｍａｘ（但し、ｘ１ｍｉｎ、ｘ２ｍａｘはいずれも原子比）が０．０５＜ｘ１ｍｉｎ−ｘ２ｍａｘ＜０．３０を満足することを特徴とする表面被覆切削工具。 In a surface-coated cutting tool in which a hard coating layer is provided on the surface of a tool base composed of any of tungsten carbide-based cemented carbide, titanium carbonitride-based cermet, or cubic boron nitride-based ultrahigh-pressure sintered body,
(A) The hard coating layer includes at least a composite nitride or composite carbonitride layer of Ti and Al having an average layer thickness of 1.0 to 20.0 μm,
(B) the Ti and Al composite nitride or composite carbonitride layer includes at least a composite nitride or composite carbonitride phase having a NaCl-type face-centered cubic structure;
(C) In the composite nitride or composite carbonitride layer of Ti and Al, the phase is composed of a high Al content region represented by a composition formula (Al x1 Ti 1-x1 ) (C y1 N 1-y1 ). Having a two-phase structure surrounded by a low Al-containing region represented by the formula (Al x2 Ti 1-x2 ) (C y2 N 1-y2 ),
Average content ratios x 1 , x 2 in the total amount of Ti and Al in Al and average content ratios y 1 , y 2 in the total amount of C and N in C (where x 1 , x 2 , y 1 , y 2 are atomic ratios) of 0.70 <x 1 <0.93, 0.40 <x 2 <0.85, 0.0000 ≦ y 1 ≦ 0.0050, 0.0000 ≦ y 2, respectively. ≦ 0.0050, the content ratio x 1 min of the content ratio x 1 in the total amount of Ti and Al in the high Al content region, the content ratio in the total content of Ti and Al in the low Al content region maximum x 2max of x 2 (where, x 1min, x 2max any atomic ratio) surface-coated cutting tool, wherein a satisfies 0.05 <x 1min -x 2max <0.30 .
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2022264196A1 (en) * | 2021-06-14 | 2022-12-22 | 住友電工ハードメタル株式会社 | Cutting tool |
| JP7325720B2 (en) | 2020-02-03 | 2023-08-15 | 三菱マテリアル株式会社 | surface coated cutting tools |
| JP7326693B2 (en) | 2020-04-13 | 2023-08-16 | 住友電工ハードメタル株式会社 | Cutting tool and its manufacturing method |
| JP7326691B2 (en) | 2020-04-13 | 2023-08-16 | 住友電工ハードメタル株式会社 | Cutting tool and its manufacturing method |
| JP7326692B2 (en) | 2020-04-13 | 2023-08-16 | 住友電工ハードメタル株式会社 | Cutting tool and its manufacturing method |
| EP4173746A4 (en) * | 2021-06-14 | 2023-08-23 | Sumitomo Electric Hardmetal Corp. | Cutting tool |
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Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2014121747A (en) * | 2012-12-20 | 2014-07-03 | Mitsubishi Materials Corp | Surface-coated cutting tool with hard coating layer exhibiting excellent chipping resistance and wear resistance |
| JP2016030319A (en) * | 2014-07-30 | 2016-03-07 | 三菱マテリアル株式会社 | Surface coated cutting tool having hard coating layer exhibiting superior chipping resistance |
| JP2016064485A (en) * | 2014-09-25 | 2016-04-28 | 三菱マテリアル株式会社 | Surface coat cutting tool having hard coat layer exhibiting superior chipping resistance |
| JP2016130343A (en) * | 2015-01-14 | 2016-07-21 | 住友電工ハードメタル株式会社 | Hard coating, cutting tool and method of manufacturing hard coating |
| JP2016137549A (en) * | 2015-01-28 | 2016-08-04 | 三菱マテリアル株式会社 | Surface-coated cutting tool with hard coating layer exerting excellent chipping resistance |
| WO2017010374A1 (en) * | 2015-07-15 | 2017-01-19 | 住友電気工業株式会社 | Coating |
| WO2017090540A1 (en) * | 2015-11-25 | 2017-06-01 | 三菱日立ツール株式会社 | Titanium aluminum nitride hard film, hard film coated tool, method for producing titanium aluminum nitride hard film, and method for producing hard film coated tool |
-
2018
- 2018-03-20 JP JP2018053449A patent/JP7191287B2/en active Active
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2014121747A (en) * | 2012-12-20 | 2014-07-03 | Mitsubishi Materials Corp | Surface-coated cutting tool with hard coating layer exhibiting excellent chipping resistance and wear resistance |
| JP2016030319A (en) * | 2014-07-30 | 2016-03-07 | 三菱マテリアル株式会社 | Surface coated cutting tool having hard coating layer exhibiting superior chipping resistance |
| JP2016064485A (en) * | 2014-09-25 | 2016-04-28 | 三菱マテリアル株式会社 | Surface coat cutting tool having hard coat layer exhibiting superior chipping resistance |
| JP2016130343A (en) * | 2015-01-14 | 2016-07-21 | 住友電工ハードメタル株式会社 | Hard coating, cutting tool and method of manufacturing hard coating |
| JP2016137549A (en) * | 2015-01-28 | 2016-08-04 | 三菱マテリアル株式会社 | Surface-coated cutting tool with hard coating layer exerting excellent chipping resistance |
| WO2017010374A1 (en) * | 2015-07-15 | 2017-01-19 | 住友電気工業株式会社 | Coating |
| WO2017090540A1 (en) * | 2015-11-25 | 2017-06-01 | 三菱日立ツール株式会社 | Titanium aluminum nitride hard film, hard film coated tool, method for producing titanium aluminum nitride hard film, and method for producing hard film coated tool |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP7325720B2 (en) | 2020-02-03 | 2023-08-15 | 三菱マテリアル株式会社 | surface coated cutting tools |
| JP7453616B2 (en) | 2020-02-03 | 2024-03-21 | 三菱マテリアル株式会社 | surface coated cutting tools |
| JP7326693B2 (en) | 2020-04-13 | 2023-08-16 | 住友電工ハードメタル株式会社 | Cutting tool and its manufacturing method |
| JP7326691B2 (en) | 2020-04-13 | 2023-08-16 | 住友電工ハードメタル株式会社 | Cutting tool and its manufacturing method |
| JP7326692B2 (en) | 2020-04-13 | 2023-08-16 | 住友電工ハードメタル株式会社 | Cutting tool and its manufacturing method |
| WO2022264196A1 (en) * | 2021-06-14 | 2022-12-22 | 住友電工ハードメタル株式会社 | Cutting tool |
| EP4173746A4 (en) * | 2021-06-14 | 2023-08-23 | Sumitomo Electric Hardmetal Corp. | Cutting tool |
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