WO2016084938A1 - Outil de coupe à revêtement de surface - Google Patents

Outil de coupe à revêtement de surface Download PDF

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Publication number
WO2016084938A1
WO2016084938A1 PCT/JP2015/083400 JP2015083400W WO2016084938A1 WO 2016084938 A1 WO2016084938 A1 WO 2016084938A1 JP 2015083400 W JP2015083400 W JP 2015083400W WO 2016084938 A1 WO2016084938 A1 WO 2016084938A1
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layer
composite
avg
average
crystal
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PCT/JP2015/083400
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English (en)
Japanese (ja)
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佐藤　賢一
翔 龍岡
健志 山口
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三菱マテリアル株式会社
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Priority claimed from JP2015229738A external-priority patent/JP6617917B2/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
Priority to US15/531,295 priority Critical patent/US20170342552A1/en
Priority to CN201580064514.6A priority patent/CN107000069A/zh
Priority to EP15863164.8A priority patent/EP3225338A4/fr
Priority to KR1020177013914A priority patent/KR20170086045A/ko
Publication of WO2016084938A1 publication Critical patent/WO2016084938A1/fr

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    • 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

Definitions

  • the present invention is a high-speed intermittent cutting process that involves high heat generation of alloy steel and the like, and an impact load is applied to the cutting edge, and the hard coating layer has excellent chipping resistance, so that it can be used for a long time.
  • the present invention relates to a surface-coated cutting tool (hereinafter referred to as a coated tool) that exhibits excellent cutting performance.
  • WC tungsten carbide
  • TiCN titanium carbonitride
  • cBN cubic boron nitride
  • a coated tool is known in which a Ti—Al-based composite nitride layer is formed by physical vapor deposition as a hard coating layer on the surface of a substrate (hereinafter collectively referred to as “substrate”). It is known that it exhibits excellent wear resistance.
  • the conventional coated tool formed with the Ti—Al composite nitride layer is relatively excellent in wear resistance, but it tends 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.
  • Patent Document 1 a TiCN layer and an Al 2 O 3 layer are used as an inner layer, and a cubic crystal structure (Ti 1-x) including a cubic crystal structure or a hexagonal crystal structure is formed thereon by chemical vapor deposition.
  • Al x ) N layer (where x is 0.65 to 0.9) is coated as an outer layer, and by applying compressive stress of 100 to 1100 MPa to the outer layer, the heat resistance and fatigue strength of the coated tool are improved. It has been proposed to do.
  • Patent Document 2 discloses a surface-coated cutting tool including a tool base and a hard coating layer formed on the base, and the hard coating layer includes one or both of Al and Cr elements.
  • a compound composed of at least one element selected from the group consisting of Group 4a, 5a, 6a group elements and Si, and at least one element selected from the group consisting of carbon, nitrogen, oxygen and boron And chlorine are disclosed to dramatically improve the wear resistance and oxidation resistance of the hard coating layer.
  • Patent Document 3 discloses that chemical vapor deposition is performed in a mixed reaction gas of TiCl 4 , AlCl 3 , and NH 3 in a temperature range of 650 to 900 ° C., so that the value of the Al content ratio x is 0.65 to Although it is described that a (Ti 1-x Al x ) N layer having a thickness of 0.95 can be formed by vapor deposition, this reference further describes an Al 2 O 3 layer on the (Ti 1-x Al x ) N layer. In order to enhance the heat insulation effect, and by forming a (Ti 1-x Al x ) N layer in which the value of x is increased from 0.65 to 0.95, cutting performance is improved. There is no disclosure up to the point of how this will be affected.
  • the coated tool described in Patent Document 2 is intended to improve wear resistance and oxidation resistance characteristics, but chipping resistance under cutting conditions involving impact such as high-speed interrupted cutting. There was a problem that was not enough.
  • the Al content ratio x can be increased, and a cubic crystal structure is formed. Therefore, although a hard coating layer having a predetermined hardness and excellent wear resistance can be obtained, there is a problem that the adhesion strength with the substrate is not sufficient and the toughness is inferior.
  • the technical problem to be solved by the present invention that is, the purpose of the present invention is to provide excellent toughness even when subjected to high-speed interrupted cutting such as alloy steel, carbon steel, cast iron, etc. It is an object of the present invention to provide a coated tool that exhibits excellent chipping resistance and wear resistance over use.
  • the present inventors have at least a composite nitride or composite carbonitride of Ti and Al (hereinafter referred to as “(Ti, Al) (C, N)” or “(Ti 1-x Al x ) ( Which may be indicated by (C y N 1-y )))
  • (Ti, Al) (C, N) or “(Ti 1-x Al x ) ( Which may be indicated by (C y N 1-y ))
  • the conventional hard coating layer including at least one (Ti 1-x Al x ) (C y N 1-y ) layer and having a predetermined average layer thickness is (Ti 1-x Al x ) (
  • the C y N 1-y ) layer When the C y N 1-y ) layer is formed in a columnar shape in the direction perpendicular to the tool base, it has high wear resistance.
  • the present inventors have conducted intensive studies on the (Ti 1-x Al x ) (C y N 1-y ) layer constituting the hard coating layer, and found that the hard coating layer had Si, Zr, B, V, Cr.
  • Cubic crystal grains are distorted by a completely new idea that is composed of crystal grains having a structure and that causes periodic concentration changes (content ratios) of Ti, Al, and Me in the cubic crystal phase.
  • the inventors have succeeded in increasing the hardness and toughness, and as a result, have found a novel finding that the chipping resistance and fracture resistance of the hard coating layer can be improved.
  • the hard coating layer is a composite nitride of Ti, Al, and Me (where Me is a kind of element selected from Si, Zr, B, V, and Cr) having an average layer thickness of 1 to 20 ⁇ m.
  • Me is a kind of element selected from Si, Zr, B, V, and Cr
  • the hard coating layer occupies the total amount of Ti of Al and Al and Me.
  • Average content ratio X avg and average content ratio Y avg in the total amount of Ti, Al, and Me in Me and average content ratio Z avg in the total amount of C and N in C (where X avg , Y avg , Z avg Are atomic ratios) of 0.60 ⁇ X avg , 0.005 ⁇ Y avg ⁇ 0.10, 0 ⁇ Z avg ⁇ 0.005, 0.605 ⁇ X avg + Y avg ⁇ 0.95, respectively.
  • said composite nitride or composite carbonitride includes grains having a NaCl-type face-centered cubic structure (or further including grains having a wurtzite-type hexagonal structure), and the NaCl-type face in the composite nitride or composite carbonitride layer.
  • the (Ti 1-xy Al x Me y ) (C z N 1-z ) layer having the above-described configuration is, for example, the following chemical vapor deposition that periodically changes the reaction gas composition on the tool base surface.
  • the film can be formed by the method.
  • the chemical vapor deposition reactor used includes a gas group A composed of NH 3 , N 2 and H 2 , TiCl 4 , Al (CH 3 ) 3 , AlCl 3 , MeCl n (Me chloride), NH 3 , N 2.
  • H 2 gas groups B are supplied into the reactor from respective separate gas supply pipes, and the gas group A and the gas group B are supplied into the reactor, for example, at regular time intervals.
  • the gas is supplied such that the gas flows for a time shorter than the period, and the gas supply of the gas group A and the gas group B causes a phase difference of a time shorter than the gas supply time so that the reaction gas composition on the tool base surface is set.
  • gas group A, II) mixed gas of gas group A and gas group B, and (III) gas group B can be changed with time.
  • it is not necessary to introduce a long exhaust process intended for strict gas replacement.
  • the reaction gas composition on the surface of the tool base is changed to (I) Gas group A
  • the reaction gas composition (volume% with respect to the total of the gas group A and the gas group B) is, for example, NH 3 : 1.0 to 1.5%, N 2 : 0 to 5 as the gas group A.
  • reaction atmosphere pressure 4.5 to 5.0 kPa
  • reaction Atmospheric temperature 700 to 900 ° C.
  • supply cycle 1 to 5 seconds gas supply time per cycle 0.15 to 0.25 seconds, phase difference between gas supply A and gas supply B 0.10 to 0.20 seconds a predetermined time, by thermal CVD method, a predetermined target layer thickness of (Ti 1-x-y Al x Me y) (C z N -Z) layer is deposited.
  • the gas group A and the gas group B are supplied so that there is a difference in the time required to reach the surface of the tool base, and NH 3 as the nitrogen source gas in the gas group A: 1.0 to 1.5%, N 2 : 0 to 5%, AlCl 3 as a metal chloride raw material or carbon raw material in gas group B: 0.6 to 0.9%, TiCl 4 : 0.2 to 0.3%, MeCl n ( Me chloride): 0.1-0.2%, Al (CH 3 ) 3 : 0-0.5%, local compositional irregularities, dislocations and point defects in the crystal grains The local distortion of the crystal lattice is formed by the introduction, and the degree of ⁇ 111 ⁇ orientation on the tool base surface side and the film surface side of the crystal grains can be changed.
  • the hard coating layer is a composite nitride of Ti, Al, and Me (where Me is a kind of element selected from Si, Zr, B, V, and Cr) having an average layer thickness of 1 to 20 ⁇ m or
  • the composite carbonitride layer is included and expressed by the composition formula: (Ti 1-xy Al x Me y ) (C z N 1-z ), the Ti of the composite nitride or the composite carbonitride layer
  • the lattice constant a of the crystal grains having the NaCl type face centered cubic structure is obtained from X-ray diffraction, and the crystal grains having the NaCl type face centered cubic structure are obtained.
  • the lattice constant a satisfies the relationship of 0.05a TiN + 0.95a AlN ⁇ a ⁇ 0.4a TiN + 0.6a AlN with respect to the lattice constant a TiN of cubic TiN and the lattice constant a AlN of cubic AlN.
  • the surface-coated cutting tool according to any one of (1) to (3), characterized in that: (5) When the composite nitride or the composite carbonitride layer is observed from the longitudinal cross-sectional direction of the layer, the composite nitride of Ti, Al, and Me having a NaCl-type face-centered cubic structure in the layer or (1) to (4) above, wherein the composite carbonitride has a columnar structure having an average grain width W of 0.1 to 2.0 ⁇ m and an average aspect ratio A of 2 to 10
  • the surface-coated cutting tool according to any one of the above.
  • the composite nitride or composite carbonitride layer has an area ratio of Ti, Al, and Me composite nitride or composite carbonitride having an NaCl type face-centered cubic structure of 70 area% or more.
  • the surface-coated cutting tool according to any one of (1) to (5), which is characterized in that (7) A tool base composed of any one of the tungsten carbide-based cemented carbide, titanium carbonitride-based cermet, or cubic boron nitride-based ultrahigh-pressure sintered body, and a composite nitride or composite carbon of Ti, Al, and Me.
  • a Ti carbide layer Between the nitride layers, one or two or more of a Ti carbide layer, a nitride layer, a carbonitride layer, a carbonate layer and a carbonitride oxide layer, and 0.1 to 20 ⁇ m
  • a lower layer including a Ti compound layer having a total average layer thickness is present.
  • an upper layer including at least an aluminum oxide layer is present on the composite nitride or composite carbonitride layer at a total average layer thickness of 1 to 25 ⁇ m.
  • the surface-coated cutting tool according to any one of the above.
  • the composite nitride or the composite carbonitride layer is formed by a chemical vapor deposition method containing at least trimethylaluminum as a reactive gas component.
  • the hard coating layer (hereinafter referred to as “hard coating layer of the present invention”) in the surface-coated cutting tool which is one embodiment of the present invention is essentially the above-described composite nitride or composite carbonitride layer.
  • the combined effect of the composite nitride or the composite carbonitride layer can be obtained by using it together with the conventionally known lower layer of (7) and the upper layer of (8). Needless to say, even better characteristics can be created.
  • Average layer thickness of the composite nitride or composite carbonitride layer 2 constituting the hard coating layer In FIG. 1, the cross-sectional schematic diagram of the composite nitride or composite carbonitride layer of Ti, Al, and Me which comprises the hard coating layer of this invention is shown.
  • the hard coating layer of the present invention is a composite nitride or composite carbonitride layer of Ti, Al, and Me represented by a composition formula: (Ti 1-xy Al x Me y ) (C z N 1-z ) 2 is included.
  • the composite nitride or composite carbonitride layer 2 has high hardness and excellent wear resistance, but the effect is particularly remarkable when the average layer thickness is 1 to 20 ⁇ m.
  • the average layer thickness is set to 1 to 20 ⁇ m. Although it is not particularly essential, a more preferable average layer thickness is 3 to 15 ⁇ m. A more preferable average layer thickness is 4 to 10 ⁇ m.
  • composition of composite nitride or composite carbonitride layer 2 constituting hard coating layer is represented by the composition formula: (Ti 1-xy Al x Me y ) (C z N 1-z ) (however, , Me is a kind of element selected from Si, Zr, B, V, and Cr), the average content ratio X avg in the total amount of Ti, Al, and Me of Al, and the combination of Ti, Al, and Me of Me.
  • the average content ratio Y avg in the amount and the average content ratio Z avg in the total amount of C and N in C are 0.60 ⁇ X, respectively.
  • Control is performed to satisfy avg , 0.005 ⁇ Y avg ⁇ 0.10, 0 ⁇ Z avg ⁇ 0.005, 0.605 ⁇ X avg + Y avg ⁇ 0.95.
  • the reason is that when the average content ratio X avg of Al is less than 0.60, the hardness of the composite nitride of Ti and Al and Me or the composite carbonitride layer 2 is inferior. When it is used, the wear resistance is not sufficient.
  • the composite nitride of Ti, Al, and Me or the composite carbonitride layer 2 is inferior in hardness, so that it is used for high-speed intermittent cutting of alloy steel and the like. In such a case, the wear resistance is not sufficient.
  • the toughness of the composite nitride of Ti, Al, and Me or the composite carbonitride layer 2 decreases due to the segregation of Me to the grain boundary, etc., and is used for high-speed intermittent cutting of alloy steel and the like. In some cases, the chipping resistance is not sufficient.
  • the average content ratio Y avg of Me was determined as 0.005 ⁇ Y avg ⁇ 0.10.
  • the composite nitride or composite carbonitride layer 2 of Ti, Al, and Me Since it is inferior in hardness, when it is subjected to high-speed interrupted cutting of alloy steel or the like, the wear resistance is not sufficient. Inviting, chipping resistance decreases.
  • the sum X avg + Y avg of the average content ratio X avg of Al and the average content ratio Y avg of Me was determined as 0.605 ⁇ X avg + Y avg ⁇ 0.95.
  • a specific component of Me a kind of element selected from Si, Zr, B, V, and Cr is used.
  • Si component or B component is used so that Y avg is 0.005 or more as Me, the hardness of the composite nitride or composite carbonitride layer 2 is improved, so that the wear resistance is improved.
  • the Zr component has the effect of strengthening the grain boundary, and the V component improves toughness, so that the chipping resistance can be further improved, and the Cr component improves oxidation resistance. Therefore, a longer tool life is expected.
  • the average content ratio Y avg exceeds 0.10
  • the average content ratios of the Al component and the Ti component are relatively decreased, so that the wear resistance or chipping resistance tends to decrease. Therefore, it must be avoided that the average content ratio is such that Y avg exceeds 0.10.
  • the composite nitride or composite carbonitride layer 2 when the average content ratio (atomic ratio) Z avg of C contained in the composite nitride or composite carbonitride layer 2 is a minute amount in the range of 0 ⁇ Z avg ⁇ 0.005, the composite nitride or composite carbon The adhesion between the nitride layer 2 and the tool base 3 or the lower layer is improved and the lubricity is improved to reduce the impact during cutting. As a result, the resistance of the composite nitride or the composite carbonitride layer 2 is improved. Defectability and chipping resistance are improved.
  • the average content ratio Z avg of C was determined as 0 ⁇ Z avg ⁇ 0.005.
  • more preferable X avg , Y avg and Z avg are 0.70 ⁇ X avg ⁇ 0.85, 0.01 ⁇ Y avg ⁇ 0.05, and 0 ⁇ Z avg ⁇ 0, respectively. 0.003, 0.7 ⁇ X avg + Y avg ⁇ 0.90.
  • each crystal grain having a NaCl-type face-centered cubic structure using an electron beam backscattering diffractometer is used.
  • the normal line of the ⁇ 111 ⁇ plane which is the crystal plane of the crystal grain with respect to the normal line 5 of the tool base surface (the direction perpendicular to the tool base surface 4 in the cross-section polished surface) Measure the tilt angle 6 (see Fig. 2A and Fig. 2B), and divide the tilt angle within the range of 0 to 45 degrees with respect to the normal direction for each pitch of 0.25 degrees
  • the frequencies existing in each section are tabulated, the highest peak is present in the tilt angle section within the range of 0 to 12 degrees, and the total of the frequencies existing in the range of 0 to 12 degrees is the slope.
  • FIG. 3A and FIG. 3B are graphs showing an example of the inclination angle number distribution obtained by measuring the crystal grains having a cubic structure, which is one embodiment of the present invention and a comparison, by the above method.
  • Crystal grains having a NaCl-type face-centered cubic structure constituting the composite nitride or composite carbonitride layer 2:
  • cubic crystal crystal grains having a NaCl-type face-centered cubic structure
  • the grain length in the direction perpendicular to the tool substrate surface 4 is l
  • the ratio l / w between w and l is the aspect ratio a of each crystal grain
  • the aspect ratio obtained for each crystal grain When the average value of a is the average aspect ratio A, and the average value of the particle width w obtained for each crystal grain is the average particle width W, the average particle width W is 0.1 to 2.0 ⁇ m and the average aspect ratio A is It is desirable to control so as to satisfy 2 to 10. When this condition is satisfied, the cubic crystal grains constituting the composite nitride or composite carbonitride layer 2 have a columnar structure and exhibit excellent wear resistance.
  • the average aspect ratio A is less than 2, it becomes difficult to form a periodic distribution (concentration change, content ratio change) of the composition, which is a feature of the present invention, in the crystal grains of the NaCl type face-centered cubic structure.
  • a columnar crystal exceeding 10 is not preferable because cracks are likely to grow along a plane along a periodic distribution of the composition in the cubic crystal phase, which is a feature of the present invention, and a plurality of grain boundaries.
  • the average particle width W is less than 0.1 ⁇ m, the wear resistance is lowered, and when it exceeds 2.0 ⁇ m, the toughness is lowered.
  • the average grain width W of the cubic crystal grains constituting the composite nitride or composite carbonitride layer 2 is preferably 0.1 to 2.0 ⁇ m.
  • the more preferable average aspect ratio and average particle width W are 4 to 7 and 0.7 to 1.5 ⁇ m, respectively.
  • FIG. 4 shows a composite nitride layer or composite carbonitride layer of Ti, Al, and Me contained in the hard coating layer of the present invention (hereinafter referred to as “composite nitride layer or composite carbonitride of Ti, Al, and Me of the present invention”).
  • composite nitride layer or composite carbonitride of Ti, Al, and Me of the present invention A crystal grain having a cubic crystal structure), and a periodic concentration change of Ti, Al, and Me is one of the equivalent crystal orientations represented by ⁇ 001> of the cubic crystal grain. It is shown as a schematic diagram that the change in the Al content ratio x is small in a plane that exists along the azimuth and is orthogonal to the azimuth.
  • FIG. 5 shows a cubic crystal structure in which a periodic concentration change of Ti, Al, and Me exists in the cross section of the composite nitride layer or composite carbonitride layer of Ti, Al, and Me of the present invention.
  • EDS energy dispersive X-ray spectroscopy
  • the X max also, if the minimum value 12a of periodically value varying x in proportion x of Al, 12b, 12c, an average value of 12d ⁇ ⁇ ⁇ and the X min, the difference of X max and X min When ⁇ x is smaller than 0.03, the above-described crystal grain distortion is small and sufficient hardness cannot be expected. On the other hand, if the difference ⁇ x between X max and X min exceeds 0.25, the distortion of the crystal grains becomes too large, lattice defects become large, and the hardness decreases. Therefore, for the change in the concentration of Ti, Al, and Me existing in the crystal grains having a cubic crystal structure, the difference between X max and X min was set to 0.03 to 0.25.
  • a more preferable difference between X max and X min is 0.05 to 0.22. Even more preferably, it is 0.08 to 0.15.
  • the periodic composition change of Ti and Al causes toughness to decrease when the period is less than 3 nm.
  • the thickness exceeds 100 nm, the effect of improving the hardness cannot be expected, so the period was set to 3 to 100 nm.
  • the more preferable period of concentration change is 15 to 80 nm. Even more preferably, it is 25 to 50 nm.
  • the crystal grains having a cubic crystal structure in which a periodic concentration change of Ti, Al, and Me in the composite nitride or composite carbonitride layer exists a periodic concentration change of Ti, Al, and Me occurs.
  • the crystal grains exist along one of the equivalent crystal orientations represented by ⁇ 001> of the cubic crystal grains lattice defects due to distortion of the crystal grains hardly occur, and the toughness is improved.
  • the Ti, Al, and Me concentrations do not substantially change in the plane orthogonal to the orientation in which the periodic concentration changes of Ti, Al, and Me exist, and the Ti Ti in the orthogonal plane is not changed.
  • the maximum value ⁇ Xo of the change amount of the content ratio x in the total amount of Al and Me is 0.01 or less.
  • the period of concentration change along one of the equivalent crystal orientations represented by ⁇ 001> of the cubic crystal grains is less than 3 nm, the toughness is lowered, and if it exceeds 100 nm, the hardness is improved. Is not fully demonstrated. Therefore, a more desirable period of the concentration change is 3 to 100 nm. Although not particularly essential, the more preferable period of concentration change is 15 to 80 nm. Even more preferably, it is 25 to 50 nm.
  • FIG. 6 shows a crystal grain having a cubic crystal structure in which a periodic concentration change of Ti, Al, and Me exists in the cross section of the composite nitride layer or composite carbonitride layer 2 of Ti, Al, and Me of the present invention.
  • the region A and the region B exist in two directions in which the periodic concentration changes of Ti, Al, and Me are orthogonal to each other, there are two directions of strain in the crystal grains. Toughness is improved.
  • the boundary 15 between the region A (13) and the region B (14) is formed on one of the equivalent crystal planes represented by ⁇ 110 ⁇ , so that the region A (13) and the region B (14) are formed.
  • a high toughness can be maintained. That is, present along the one of the orientation of the crystal orientation of the equivalent cyclic changes in the concentration of Ti and Al and Me are represented by cubic grains of ⁇ 001> was the azimuth and azimuth d A If, azimuth d cycle along the a is 3 ⁇ 30 nm, orientation d maximum DerutaXod a variation of the content x of Al in a plane perpendicular to the a is 0.01 or less area a (13 ) and periodic changes in the concentration of Ti and Al and Me is present along one of the orientation of the crystal orientation of the equivalent represented by ⁇ 001> cubic crystal grains perpendicular to the orientation d a, when the orientation thereof and azimuth d B, azimuth d cycle along the B is 3 ⁇ 30 nm, the maximum value DerutaXod B of variation of the proportion x of Al in a plane perpendicular to the direction d B 0.
  • Lattice constant a of cubic crystal grains in the composite nitride layer or composite carbonitride layer was subjected to an X-ray diffraction test using an X-ray diffractometer and Cu—K ⁇ rays as a radiation source, and the lattice constant a of cubic crystal grains was determined.
  • X-ray diffraction was performed under conditions of a measurement range of 13 ° ⁇ 2 ⁇ ⁇ 130 °, a measurement width of 0.02 °, and a measurement time of 0.5 seconds / step.
  • the peaks and crystal planes belonging to the composite nitride layer or composite carbonitride layer of Ti, Al, and Me having a cubic structure are identified, and for each peak, the wavelength and peak of the Cu-K ⁇ ray used
  • the interplanar spacing of the crystal planes was calculated from the angle, and the average value of the lattice constants calculated from the interplanar spacing values was defined as the lattice constant a.
  • Area ratio of columnar structure made of individual crystal grains having a cubic structure in composite nitride or composite carbonitride layer 2 When the area ratio of the columnar structure composed of individual crystal grains having a cubic crystal structure is less than 70% by area, the hardness is undesirably lowered. Although it is not a particularly essential configuration, the area ratio of the columnar structure composed of individual crystal grains having a preferable cubic structure is 85 area% or more. More preferably, it is 95 area% or more.
  • the composite nitride or composite carbonitride layer 2 of the present invention has one or two of a Ti carbide layer, nitride layer, carbonitride layer, carbonate layer and carbonitride oxide layer as a lower layer. Even in the case of including a Ti compound layer having a total average layer thickness of 0.1 to 20 ⁇ m and / or including an aluminum oxide layer having an average layer thickness of 1 to 25 ⁇ m as an upper layer, The combined characteristics of these layers together with the effects of these layers can be further improved by using these known lower layers and upper layers together.
  • the lower layer includes a Ti compound layer composed of one or more of Ti carbide layer, nitride layer, carbonitride layer, carbonate layer and carbonitride oxide layer
  • the total of the Ti compound layer When the average layer thickness exceeds 20 ⁇ m, the crystal grains are likely to be coarsened and chipping is likely to occur. Further, when an aluminum oxide layer is included as the upper layer, if the total average layer thickness of the aluminum oxide layer exceeds 25 ⁇ m, crystal grains are likely to be coarsened and chipping is likely to occur.
  • the lower layer is less than 0.1 ⁇ m, the effect of improving the adhesion with the lower layer of the composite nitride or composite carbonitride layer 2 of the present invention can not be expected, and if the upper layer is less than 1 ⁇ m, The effect of improving the wear resistance by forming the upper layer is not remarkable.
  • the present invention provides a surface coating in which a hard coating layer is formed 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.
  • the hard coating layer includes at least a composite nitride or composite carbonitride layer 2 of Ti, Al, and Me having an average layer thickness of 1 to 20 ⁇ m, and has a composition formula: (Ti 1-xy Al x Me y ) (C z N 1-z ), the average content X avg in the total amount of Ti, Al, and Me in Al and the average content Y avg in the total amount of Ti, Al, and Me in Me, and The average content ratio Z avg in the total amount of C and N in C (where X avg , Y avg , and Z avg are atomic ratios) is 0.60 ⁇ X avg , 0.005 ⁇ Y avg ⁇ , respectively.
  • the composite nitride or composite carbonitride layer 2 is a composite nitride having a NaCl-type face-centered cubic structure
  • the crystal orientation of Ti, Al, and Me composite nitride or composite carbonitride crystal grains containing at least the composite carbonitride phase (cubic crystal phase) and having the cubic structure is determined by electron beam backscatter diffraction.
  • the inclination angle formed by the normal line 6 of the ⁇ 111 ⁇ plane, which is the crystal plane of the crystal grain, with respect to the normal direction of the tool base surface is measured.
  • the inclination angle in the range of 0 to 45 degrees with respect to the line direction is divided into pitches of 0.25 degrees and the frequencies existing in each division are totaled to obtain the inclination angle number distribution, 0 to 12
  • the period along the normal direction of the tool base surface is 3 to 100 nm.
  • Cubic crystals of composite nitride or composite carbonitride Since distortion occurs in the crystal grains having a crystal structure, the hardness of the crystal grains is improved, and the toughness is improved while maintaining high wear resistance. As a result, the effect of improving the chipping resistance is exhibited, the cutting performance is improved over a long period of use as compared with the conventional hard coating layer, and the life of the coated tool is extended.
  • membrane structure schematic diagram which represented typically the cross section of the composite nitride of Ti, Al, and Me or the composite carbonitride layer 2 which comprises the hard coating layer 1 of this invention.
  • the horizontal stripe pattern indicates a periodic content ratio change of Al in crystal grains in the composite nitride or composite carbonitride layer made of Ti, Al, and Me.
  • An example of an inclination angle number distribution obtained for a crystal grain having a cubic structure in a cross section of a composite nitride layer or composite carbonitride layer of Ti and Al constituting a hard coating layer according to an embodiment of a comparative example is shown. It is a graph. In the cross section of the composite nitride layer of Ti, Al, and Me or the composite carbonitride layer 2 constituting the hard coating layer 1 corresponding to one embodiment of the present invention, there is a periodic concentration change of Ti, Al, and Me.
  • One of the equivalent crystal orientations represented by ⁇ 001> of the cubic crystal grains in which the periodic concentration change of Ti, Al, and Me is expressed for the crystal grains having a cubic crystal structure Is a schematic diagram schematically showing that the change in the Al content ratio x is small in a plane perpendicular to the orientation (displayed from above with a line perpendicular to the arrow). is there. Specifically, the change in the Al content ratio x in the orthogonal plane is 0.01 or less. A bright color portion indicates a region 9 having a relatively high Al content, and a dark color portion indicates a region 10 having a relatively low Al content.
  • the periodic concentration change of Ti, Al, and Me in the cross section of the composite nitride layer of Ti, Al, and Me or the composite carbonitride layer 2 constituting the hard coating layer 1 corresponding to one embodiment of the present invention.
  • the periodicity of Al with respect to the total of Ti, Al, and Me as a result of performing line analysis by energy dispersive X-ray spectroscopy (EDS) using a transmission electron microscope for the crystal grains having a cubic crystal structure
  • EDS energy dispersive X-ray spectroscopy
  • An example of the graph of density change x is shown. Specifically, it represents a periodic concentration change of Al in the crystal grains having a cubic structure in the composite nitride or composite carbonitride layer 2.
  • the present invention provides a hard tool substrate, that is, a hard surface on a tool substrate 3 composed 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 1 includes at least a composite nitride or composite carbonitride layer 2 of Ti, Al, and Me having an average layer thickness of 1 to 20 ⁇ m, and a composition formula: When expressed as (Ti 1-xy Al x Me y ) (C z N 1-z ), the average content ratio X avg and the total content of Ti, Al, and Me in the Ti, Al, and Me of Al The average content ratio Y avg in the total amount of C and the average content ratio Z avg in the total amount of C and C in C (where X avg , Y avg , and Z avg are all atomic ratios) are 0.60, respectively.
  • the grains include at least crystal grains having a cubic crystal structure, and the crystal orientation of the Ti, Al, and Me composite nitride or composite carbonitride crystal grains having the cubic crystal structure is determined using an electron beam backscatter diffraction apparatus.
  • the inclination angle formed by the normal line 6 of the ⁇ 111 ⁇ plane, which is the crystal plane of the crystal grain, with respect to the normal direction of the tool base surface is measured.
  • the inclination angle in the range of 0 to 45 degrees is divided into pitches of 0.25 degrees and the frequencies existing in each division are totaled to obtain the inclination angle number distribution,
  • There is a periodic concentration change of Ti, Al, and Me There is a periodic concentration change of Ti, Al, and Me, and the maximum value of the value x of the Al content ratio x that changes periodically.
  • WC powder, TiC powder, TaC powder, NbC powder, Cr 3 C 2 powder and Co powder all having an average particle diameter of 1 to 3 ⁇ m are prepared, and these raw material powders are blended as shown in Table 1. Blended into the composition, added with wax, mixed in a ball mill in acetone for 24 hours, dried under reduced pressure, pressed into a compact of a predetermined shape at a pressure of 98 MPa, and the compact was 1370 in a vacuum of 5 Pa.
  • Mo 2 C powder Mo 2 C powder
  • ZrC powder ZrC powder
  • NbC powder WC powder
  • Co powder all having an average particle diameter of 0.5 to 2 ⁇ m.
  • Ni powder are prepared, these raw material powders are blended in the blending composition shown in Table 2, wet mixed by a ball mill for 24 hours, dried, and then pressed into a compact at a pressure of 98 MPa.
  • the body was sintered in a nitrogen atmosphere of 1.3 kPa at a temperature of 1500 ° C. for 1 hour, and after sintering, a tool base D made of TiCN-based cermet having an ISO standard SEEN1203AFSN insert shape was produced.
  • a chemical vapor deposition apparatus is used on the surfaces of these tool bases A to D, (A) Formation conditions shown in Table 4, that is, a gas group A composed of NH 3 and H 2 , TiCl 4 , Al (CH 3 ) 3 , AlCl 3 , MeCl n (where SiCl 4 , ZrCl 4 , BCl 3 , VCl 4 , CrCl 2 ), NH 3 , N 2 , H 2 gas group B, and a method of supplying each gas, the reaction gas composition (gas group A and gas group B was combined) % As a gas group A, NH 3 : 1.0 to 1.5%, N 2 : 0 to 5%, H 2 : 55 to 60%, and as a gas group B, AlCl 3 : 0.6 to 0.9%, TiCl 4 : 0.2 to 0.3%, Al (CH 3 ) 3 : 0 to 0.5%, MeCl n (however, SiCl 4 , ZrCl 4 ,
  • Ti, Al, and Me composite nitride or composite carbonitride are formed on the surfaces of the tool bases A to D under the conditions shown in Table 5 and the target layer thickness ( ⁇ m) shown in Table 8.
  • the hard coating layer including the layer was formed by vapor deposition. At this time, a hard coating layer is formed so that the reaction gas composition on the surface of the tool base does not change with time during the film formation process of the (Ti 1-xy Al x Me y ) (C z N 1-z ) layer.
  • comparative coated tools 1 to 15 were produced. Similar to the coated tools 6 to 13 of the present invention, the lower and upper layers shown in Table 6 were formed for the comparative coated tools 6 to 13 under the forming conditions shown in Table 3.
  • the cross section of the electrode is a polished surface, it is set in a lens barrel of a field emission scanning electron microscope, and an electron beam with an acceleration voltage of 15 kV at an incident angle of 70 degrees is applied to the polished surface with an irradiation current of 1 nA.
  • each crystal grain having a cubic crystal lattice existing within the measurement range of the polished surface Irradiate each crystal grain having a cubic crystal lattice existing within the measurement range of the polished surface, and use an electron backscatter diffraction image apparatus to measure a length of 100 ⁇ m in the horizontal direction from the tool base surface and a direction perpendicular to the tool base surface.
  • the composite nitride or composite carbonitride layer of Ti, Al and Me constituting the hard coating layers of the inventive coated tools 1 to 15 and comparative coated tools 1 to 15 a scanning electron microscope (with a magnification of 5000 times and (20000 times) was observed over a plurality of visual fields.
  • An Al x Me y ) (C z N 1-z ) layer was confirmed.
  • the periodic distribution of Ti, Al, and Me exists in the cubic crystal grains, and energy dispersive X-ray spectroscopy (using a transmission electron microscope) It was confirmed by surface analysis by EDS). Further, for the coated tools 1 to 15 of the present invention and the comparative coated tools 1 to 15, cubic crystals existing in the composite nitride or composite carbonitride layer using the results of surface analysis by EDS using a transmission electron microscope.
  • the period was 3 to 100 nm, and it was confirmed that the difference ⁇ x between the average value of the maximum value of x and the average value of the minimum value was 0.03 to 0.25. .
  • the cross-sections of the constituent layers of the inventive coated tools 1 to 15 and comparative coated tools 1 to 15 in the direction perpendicular to the tool substrate were measured using a scanning electron microscope (with a magnification of 5000 times).
  • the average layer thickness was obtained by measuring and averaging the five layer thicknesses, the average layer thickness was substantially the same as the target layer thickness shown in Tables 7 and 8.
  • the average Al content and the average Me content of the composite nitride or composite carbonitride layer of the coated tools 1 to 15 of the present invention and the comparative coated tools 1 to 15 were measured using an electron beam microanalyzer (EPMA, Electron-Probe-).
  • EPMA electron beam microanalyzer
  • an electron beam was irradiated from the sample surface side, and the average Al content ratio X avg and Me average of Al was obtained from an average of 10 points of the analysis result of the characteristic X-ray obtained.
  • the content ratio Y avg was determined.
  • the average C content ratio Z avg was determined by secondary ion mass spectrometry (SIMS, Secondary-Ion-Mass-Spectroscopy).
  • 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 C content ratio Z avg indicates an average value in the depth direction of the composite nitride or composite carbonitride layer of Ti, Al, and Me.
  • 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.
  • the content ratio (atomic ratio) of the C component contained in the composite nitride or composite carbonitride layer when the supply amount of Al (CH 3 ) 3 is 0 is determined as the inevitable C content ratio.
  • the inevitable C content is subtracted from the C component content (atomic ratio) contained in the composite nitride or composite carbonitride layer obtained when Al (CH 3 ) 3 is intentionally supplied.
  • the value was determined as Z avg .
  • the coated tools 1 to 15 of the present invention and the comparative coated tools 1 to 15 using a scanning electron microscope (magnification 5000 times and 20000 times) from the cross-sectional direction perpendicular to the tool substrate, the tool substrate surface and the horizontal direction
  • a crystal which is set in a lens barrel of a field emission scanning electron microscope and is present in the measurement range of the cross-sectional polished surface with an electron beam having an acceleration voltage of 15 kV at an incident angle of 70 degrees and an irradiation current of 1 nA on the polished surface.
  • the periodicity corresponding to five periods of Al with respect to the total of Ti, Al, and Me is similarly provided for each of the regions A and B.
  • a periodic concentration change of Ti, Al, and Me in the region A exists along one of the equivalent crystal orientations represented by ⁇ 001> of the cubic crystal grains, and the orientation is defined as the orientation d. If the a, along with determining the period of the concentration variation along the direction d a, perform line analysis along a direction perpendicular to the direction d a in a section corresponding to the distance of the five cycles, Al in the section. The difference between the maximum value and the minimum value of the content ratio x of one of the equivalent crystal orientations represented by ⁇ 001> of cubic crystal grains having a periodic concentration change of Ti, Al, and Me The maximum value ⁇ Xod A of the amount of change in the orthogonal plane was obtained.
  • a periodic concentration change of Ti, Al, and Me in the region B exists along one of the equivalent crystal orientations represented by ⁇ 001> of the cubic crystal grains, and the orientation is defined as the orientation d.
  • the period of concentration change along the direction d B is obtained, and the line analysis along the direction orthogonal to the direction d B is performed in the section corresponding to the distance of the five periods, and the Al in that section is obtained.
  • the difference between the maximum value and the minimum value of the content ratio x of one of the equivalent crystal orientations represented by ⁇ 001> of cubic crystal grains having a periodic concentration change of Ti, Al, and Me The maximum value ⁇ Xod B of the amount of change within the orthogonal plane was obtained.
  • d A and d B are orthogonal to each other, and the boundary between the region A and the region B is formed on one of the equivalent crystal planes represented by ⁇ 110 ⁇ . It was confirmed. Such a period was confirmed by at least one crystal grain in the field of observation of a micro region of the composite nitride or composite carbonitride layer using a transmission electron microscope. Regarding the crystal grains in which the region A and the region B exist in the crystal grains, at least one of the crystal grains in the field of observation of the minute region of the composite nitride or composite carbonitride layer using a transmission electron microscope is used. The average of the values evaluated in each of the region A and the region B was calculated. Tables 7 and 8 show the various measurement results described above.
  • the coated tools 1 to 15 of the present invention and the comparative coated tools 1 to 15 in the state where each of the various coated tools is clamped by a fixing jig at the tip of a tool steel cutter having a cutter diameter of 125 mm is described below.
  • 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.
  • Tool substrate Tungsten carbide-based cemented carbide, titanium carbonitride-based cermet, Cutting test: dry high-speed face milling, center cutting, Work material: JIS / SCM440 block material with a width of 100 mm and a length of 400 mm, Rotational speed: 891 min ⁇ 1 Cutting speed: 350 m / min, Cutting depth: 1.5 mm, Single blade feed rate: 0.2 mm / tooth, Cutting time: 8 minutes, Table 9 shows the cutting test results.
  • 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 1 to 3 ⁇ m are prepared.
  • Compounded in the formulation shown in Table 10 added with wax, ball mill mixed in acetone for 24 hours, dried under reduced pressure, press-molded into a green compact of a predetermined shape at a pressure of 98 MPa.
  • vacuum sintering is performed at a predetermined temperature within a range of 1370 to 1470 ° C. for 1 hour, and after sintering, the cutting edge is subjected to a honing process of R: 0.07 mm.
  • Tool bases ⁇ to ⁇ made of WC-base cemented carbide having the insert shape of CNMG120212 were manufactured.
  • NbC powder NbC powder
  • WC powder Co powder
  • Ni powder Ni powder each having an average particle diameter of 0.5 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.
  • the coated tools 16 to 30 of the present invention were manufactured by forming the (Ti 1-xy Al x Me y ) (C z N 1-z ) layer shown in Table 13.
  • the lower layer and the upper layer shown in Table 12 were formed under the formation conditions shown in Table 3.
  • a chemical vapor deposition apparatus is used on the surfaces of the tool bases ⁇ to ⁇ and the tool base ⁇ , and the conditions shown in Table 5 and the target layer thickness shown in Table 14 are the same as those of the coated tool of the present invention.
  • Comparative coating tools 16 to 30 shown in Table 14 were manufactured by vapor-depositing a hard coating layer. Similar to the coated tools 19 to 28 of the present invention, the comparative coated tools 19 to 28 were formed with the lower layer and the upper layer shown in Table 12 under the forming conditions shown in Table 3.
  • each component layer of the inventive coated tool 16 to 30 and the comparative coated tool 16 to 30 is measured using a scanning electron microscope (5000 times magnification), and the layer thickness at five points in the observation field is measured.
  • the average layer thickness was obtained on average, both showed the same average layer thickness as the target layer thicknesses shown in Tables 13 and 14.
  • the average Al content ratio X avg and the average Me content ratio Y were obtained using the same method as that shown in Example 1.
  • the present coated tools 16 to 30 and the comparative coated tools 16 to 30 are shown below with all of the various coated tools screwed to the tip of the tool steel tool with a fixing jig.
  • a dry high-speed intermittent cutting test of alloy steel and a wet high-speed intermittent cutting test of cast iron were carried out, and both measured the flank wear width of the cutting edge.
  • Cutting condition 1 Work material: JIS ⁇ S45C lengthwise equal 4 round grooved round bars, Cutting speed: 380 m / min, Cutting depth: 1.5 mm, Feed: 0.2 mm / rev, Cutting time: 5 minutes, (Normal cutting speed is 220 m / min),
  • Cutting condition 2 Work material: JIS / FCD700 lengthwise equal length 4 round bar with round groove, Cutting speed: 325 m / min, Cutting depth: 1.2 mm, Feed: 0.1 mm / rev, Cutting time: 5 minutes, (Normal cutting speed is 200 m / min), Table 15 shows the results of the cutting test.
  • cBN powder, TiN powder, TiCN powder, TiC powder, Al powder, and Al 2 O 3 powder each having an average particle diameter in the range of 0.5 to 4 ⁇ m were prepared.
  • the mixture is blended in the composition shown in FIG. 1, wet mixed with a ball mill for 80 hours, dried, and then pressed into a green compact having a diameter of 50 mm ⁇ thickness: 1.5 mm under a pressure of 120 MPa.
  • the green compact is sintered in a vacuum atmosphere at a pressure of 1 Pa at a predetermined temperature in the range of 900 to 1300 ° C. for 60 minutes to obtain a presintered body for a cutting edge piece.
  • Co 8% by mass
  • WC remaining composition
  • diameter 50 mm ⁇ thickness: 2 mm
  • a certain pressure 4 GPa
  • temperature a predetermined temperature within the range of 1200 to 1400 ° C., holding at a high pressure under a condition of holding time: 0.8 hour
  • wire discharge It is divided into predetermined dimensions by a processing apparatus, and further Co: 5 mass%, TaC: 5 mass%, WC: remaining composition and shape of JIS standard CNGA12041 (thickness: 4.76 mm ⁇ inscribed circle diameter: 12.
  • the brazing part (corner part) of the WC-based cemented carbide insert body having a 7 mm 80 ° rhombus) has a composition consisting of Zr: 37.5%, Cu: 25%, Ti: the rest in mass%. After brazing using a brazing material of Ti-Zr-Cu alloy having a predetermined dimension, the cutting edge portion is subjected to honing with a width of 0.13 mm and an angle of 25 °, and further subjected to finish polishing.
  • ISO regulations Tool substrate 2A having the insert shape of CNGA120412, 2B were prepared, respectively.
  • (Ti 1-xy Al x Me y ) (C) is used on the surfaces of these tool bases 2A and 2B under the conditions shown in Table 4 by the same method as in Example 1 using a chemical vapor deposition apparatus.
  • the coated tools 31 to 40 of the present invention shown in Table 18 were manufactured by vapor-depositing a hard coating layer including a z N 1-z ) layer with a target layer thickness.
  • the inventive coated tools 34 to 39 the lower layer and the upper layer shown in Table 17 were formed under the formation conditions shown in Table 3.
  • a chemical vapor deposition apparatus was used on the surfaces of the tool bases 2A and 2B, and (Ti 1-xy Al x Me y ) (C z N 1-z ) under the conditions shown in Table 5.
  • the comparative coating tools 31 to 40 shown in Table 19 were manufactured by vapor-depositing a hard coating layer including a layer) with a target layer thickness.
  • the inventive coated tools 34 to 39 for the comparative coated tools 34 to 39, the lower layer and the upper layer shown in Table 17 were formed under the formation conditions shown in Table 3.
  • the cross-sections of the constituent layers of the inventive coated tools 31 to 40 and comparative coated tools 31 to 40 were measured using a scanning electron microscope (5000 times magnification) to measure the layer thickness at five points in the observation field.
  • the average layer thickness was obtained by averaging, and both showed an average layer thickness substantially the same as the target layer thickness shown in Tables 18 and 19.
  • the average layer thickness, the average Al content ratio X avg , the average Me content ratio Y avg , average C content ratio Z avg , inclination angle number distribution, periodic concentration change difference ⁇ x ( X max ⁇ X min ) and period, lattice constant a, average grain width W of crystal grains, average aspect
  • the ratio A and the area ratio of the cubic crystal phase in the crystal grains were determined. Tables 18 and 19 show the results.
  • WC powder, TiC powder, TaC powder, NbC powder, Cr 3 C 2 powder and Co powder each having an average particle diameter of 1 to 3 ⁇ m were prepared as raw material powders. Then, blended into the composition shown in Table 1, added with wax, ball mill mixed in acetone for 24 hours, dried under reduced pressure, and then press-molded into a green compact of a predetermined shape at a pressure of 98 MPa.
  • the thermal CVD method is performed for a predetermined time under the formation conditions shown in Table 4 in the same manner as in Example 1, so that Table 23
  • the coated tools 41 to 55 of the present invention were manufactured by forming the (Ti 1-xy Al x Me y ) (C z N 1-z ) layer shown in FIG.
  • the inventive coated tools 45 to 52 the lower layer and the upper layer shown in Table 22 were formed under the formation conditions shown in Table 3.
  • a hard coating layer is similarly applied to the surfaces of the tool bases A to C in the same manner as in the coated tool of the present invention using the chemical vapor deposition apparatus and the conditions shown in Table 21 and the target layer thickness shown in Table 24.
  • Comparative coating tools 41 to 55 shown in Table 24 were manufactured by vapor deposition.
  • the lower and upper layers shown in Table 22 were formed for the comparative coated tools 45 to 52 under the forming conditions shown in Table 3.
  • the cross-sections of the constituent layers of the inventive coated tools 41 to 55 and the comparative coated tools 41 to 55 are measured using a scanning electron microscope (5000 times magnification), and the layer thicknesses at five points in the observation field are measured.
  • the average layer thickness was obtained on average, both showed the same average layer thickness as the target layer thicknesses shown in Tables 23 and 24.
  • the average Al content ratio X avg and the average Me content ratio Y are obtained using the same method as that shown in Example 1.
  • the various coated tools are clamped on a tool steel cutter tip having a cutter diameter of 125 mm by a fixing jig.
  • a wet high-speed face milling which is a kind of high-speed intermittent cutting of carbon steel, and a center-cut cutting test were performed, and the flank wear width of the cutting edge was measured.
  • Tool base Tungsten carbide-based cemented carbide cutting test: wet high-speed face milling, center cut machining, Work material: Block material of JIS / S55C width 100mm, length 400mm, Rotational speed: 891 min ⁇ 1 Cutting speed: 350 m / min, Cutting depth: 2.0 mm, Single blade feed rate: 0.2 mm / tooth, Cutting oil: Yes Cutting time: 5 minutes Table 25 shows the cutting test results.
  • the coated tool of the present invention is a hard coating layer containing at least cubic crystal grains of a composite nitride or composite carbonitride of Ti, Al and Me.
  • the cubic crystal grains exhibit a ⁇ 111 ⁇ plane orientation and have a columnar structure, and in the crystal grains, there are changes in the concentration of Ti, Al, and Me, and the hardness due to the distortion of the crystal grains.
  • even when used for high-speed intermittent cutting where intermittent and impactful high loads act on the cutting edge, it has excellent chipping resistance and chipping resistance, resulting in excellent wear resistance over a long period of use. It is clear that it will work.
  • the hard coating layer containing at least cubic crystal grains of the composite nitride or composite carbonitride of Ti, Al and Me constituting the hard coating layer since it does not have the requirements specified in the present invention, When used for high-speed intermittent cutting with high heat generation and intermittent / impact high loads acting on the cutting edge, it is apparent that the life is shortened in a short time due to occurrence of chipping, chipping and the like.
  • the coated tool of the present invention can be used not only for high-speed intermittent cutting of alloy steel but also as a coated tool for various work materials, and has excellent chipping resistance over a long period of use. Since it exhibits wear resistance, it can sufficiently satisfy the high performance of the cutting device, the labor saving and energy saving of the cutting work, and the cost reduction.

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Cutting Tools, Boring Holders, And Turrets (AREA)
  • Chemical Vapour Deposition (AREA)

Abstract

L'invention concerne un outil de coupe à revêtement de surface comportant une couche de revêtement dure qui comprend une couche de nitrure composite ou de carbonitrure composite (2) représentée par la formule de composition : (Ti1-x-yAlxMey)(CzN1-z) (où Me représente au moins un élément choisi parmi Si, Zr, B, V et Cr), le rapport de teneur en Al moyenne Xavg, le rapport de teneur en Me moyenne Yavg et le rapport de teneur en C moyenne Zavg satisfaisant les formules : 0,60 ≤ Xavg, 0,005 ≤ Yavg ≤ 0,10, 0 ≤ Zavg ≤ 0,005, et 0,605 ≤ Xavg + Yavg ≤ 0,95, des grains de cristal comportant chacun une structure de cristal cubique sont contenus dans des grains de cristal qui constituent la couche de nitrure composite ou de carbonitrure composite (2), et un changement périodique spécifique du rapport de composition de Ti, Al et Me se produit dans les grains de cristal comportant chacun une structure de cristal cubique.
PCT/JP2015/083400 2014-11-28 2015-11-27 Outil de coupe à revêtement de surface WO2016084938A1 (fr)

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US15/531,295 US20170342552A1 (en) 2014-11-28 2015-11-27 Surface coated cutting tool
CN201580064514.6A CN107000069A (zh) 2014-11-28 2015-11-27 表面包覆切削工具
EP15863164.8A EP3225338A4 (fr) 2014-11-28 2015-11-27 Outil de coupe à revêtement de surface
KR1020177013914A KR20170086045A (ko) 2014-11-28 2015-11-27 표면 피복 절삭 공구

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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

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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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