WO2006011396A1 - 表面被覆切削工具 - Google Patents
表面被覆切削工具 Download PDFInfo
- Publication number
- WO2006011396A1 WO2006011396A1 PCT/JP2005/013278 JP2005013278W WO2006011396A1 WO 2006011396 A1 WO2006011396 A1 WO 2006011396A1 JP 2005013278 W JP2005013278 W JP 2005013278W WO 2006011396 A1 WO2006011396 A1 WO 2006011396A1
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- WIPO (PCT)
- Prior art keywords
- layer
- cutting tool
- tool according
- coated cutting
- flank
- Prior art date
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Classifications
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process
- C23C30/005—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process on hard metal substrates
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C16/00—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
- C23C16/22—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes characterised by the deposition of inorganic material, other than metallic material
- C23C16/30—Deposition of compounds, mixtures or solid solutions, e.g. borides, carbides, nitrides
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C16/00—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
- C23C16/22—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes characterised by the deposition of inorganic material, other than metallic material
- C23C16/30—Deposition of compounds, mixtures or solid solutions, e.g. borides, carbides, nitrides
- C23C16/40—Oxides
- C23C16/403—Oxides of aluminium, magnesium or beryllium
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
- C23C28/04—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings of inorganic non-metallic material
- C23C28/044—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings of inorganic non-metallic material coatings specially adapted for cutting tools or wear applications
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T407/00—Cutters, for shaping
- Y10T407/27—Cutters, for shaping comprising tool of specific chemical composition
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T408/00—Cutting by use of rotating axially moving tool
- Y10T408/03—Processes
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/26—Web or sheet containing structurally defined element or component, the element or component having a specified physical dimension
- Y10T428/263—Coating layer not in excess of 5 mils thick or equivalent
- Y10T428/264—Up to 3 mils
- Y10T428/265—1 mil or less
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/31—Surface property or characteristic of web, sheet or block
Definitions
- the present invention relates to a cutting tool having excellent cutting properties such as fracture resistance and wear resistance by forming a hard coating layer on a surface.
- a surface-coated cutting tool in which a hard coating layer is formed on the surface of a substrate, a TiC layer, a TiN layer, a TiCN layer, an AlC on the surface of a hard substrate such as cemented carbide, cermet, or ceramics.
- a TiC layer a TiC layer, a TiN layer, a TiCN layer, an AlC on the surface of a hard substrate such as cemented carbide, cermet, or ceramics.
- Single or multiple layers of hard coating layers such as O layer and TiAIN layer
- Patent Document 1 the grain size and layer thickness of the aluminum oxide layer are optimized, and the texture coefficient (Texture Coefficient: orientation coefficient) on the (012) plane is set to 1.3 or more. Thus, it is described that a dense, high fracture-resistant, acid-aluminum layer is obtained.
- Patent Document 2 the residual stress of the acid aluminum layer is released by setting the organization coefficient (orientation coefficient) in the (012) plane of the acid aluminum layer to 2.5 or more. It is described that the chipping resistance of the aluminum oxide layer is improved because it becomes easier.
- Patent Document 3 in order to improve the adhesion of the aluminum oxide layer, the X-ray peak of the X-ray diffraction analysis of the acidic aluminum layer shows the (110) plane. It describes that the peak intensity is the strongest.
- Patent Document 4 in the X-ray peak of the X-ray diffraction analysis of the aluminum oxide layer,
- defect resistance of the aluminum oxide layer is improved by optimizing the peak intensities of the (012) plane, (104) plane, (110) plane, and (116) plane.
- Patent Document 1 Japanese Patent No. 3325987
- Patent Document 2 JP 2003-025114 A
- Patent Document 3 Japanese Patent Laid-Open No. 10-156606
- Patent Document 4 Japanese Patent Laid-Open No. 2002-370105
- the main object of the present invention is to provide a surface-coated cutting tool having a long life by optimizing the balance of properties of the hard coating layer to provide a surface-coated cutting tool having excellent wear resistance and fracture resistance. It is.
- Another object of the present invention is to provide a long-life surface-coated cutting tool by preventing the welding of the work material on the flank face while preventing the large chipping that occurs suddenly by improving the impact resistance of the rake face. Is to provide.
- Still another object of the present invention is to provide a method for manufacturing a cut product that can stably obtain a cut product having a good processed surface. Means for solving the problem
- (HKL) plane One type selected from (012), (104), (110), (113), (024), (116) plane I (HKL): X-ray diffraction peak intensity measurement on (HKL) plane value
- the surface roughness at the interface between the acid / aluminum layer and the bonding layer is a rake face.
- the surface-coated cutting tool according to (5) above which is 0.08 / zm or less and 0.1 to 0.8 m on the flank face.
- the film hardness of the aluminum oxide layer measured with a micro Vickers hardness tester is 20 GPa or more on the rake face, and the film hardness force of the aluminum oxide layer on the flank face rake face
- the surface-coated cutting tool according to the above (2) which is 0.5 GPa or more larger than the film hardness in the above.
- Orientation coefficient TC on the rake face is 1.3 to 5.0, and the flank face is arranged on the flank face.
- the surface roughness at the interface between the acid-aluminum layer and the bonding layer is 0.2 to 0.5 / ⁇ ⁇ on the rake face, and the relief surface is 0.
- Adhesive force of the acid-aluminum film measured by a scratch test with a diamond indenter is in the range of 40N to 120N and on the flank.
- the orientation coefficient TC at the rake face is 0.4 to 1.0, and the orientation at the flank face is
- the orientation coefficient of the (012) plane of the aluminum oxide layer formed on the surface of the substrate is defined as the orientation coefficient TC on the rake face and the orientation coefficient TC on the flank face.
- Adjust / TC so that it is in the range of 0.3 to 0.95. This makes it possible to work with the work material during cutting.
- the bonding strength between the crystals of the acid-aluminum layer can be increased to sufficiently increase the hardness of the film, and rubbing wear on the flank face is suppressed. be able to. Furthermore, on the rake face, it is possible to increase the toughness of the acid-aluminum layer by weakening the bonding force between the crystals of the acid-aluminum layer, and to suppress chipping and sudden defects on the rake face. Both chipping and wear resistance can be improved.
- the orientation coefficient of the rake face and the flank face can be easily adjusted within a predetermined range, and both the wear resistance and fracture resistance of the surface-coated cutting tool can be improved.
- the orientation coefficient of the acid aluminum layer can be easily controlled.
- the ratio of the orientation coefficient of the acid-aluminum layer on the rake face and the flank face can be easily adjusted to a predetermined range, and a surface-coated cutting tool with no variation in performance can be obtained. Can do.
- the wear resistance of the acid-aluminum layer on the flank surface is increased, the flank wear can be suppressed, and the toughness of the acid-aluminum layer on the rake surface is maintained, thereby providing an impact resistance. Can increase the sex.
- the orientation coefficient of the (110) plane of the aluminum oxide layer deposited on the surface of the substrate is the ratio TC / TC between the orientation coefficient TC on the rake face and the orientation coefficient TC on the flank face. Adjust so that it is within the range of 3 to 0.95. This allows collisions with the workpiece during cutting.
- the orientation coefficients of the rake face and the flank face can be easily adjusted within a predetermined range, and both the wear resistance and fracture resistance of the surface-coated cutting tool can be improved.
- the adhesion of the aluminum oxide layer can be increased to suppress film peeling during the cutting process, and the orientation coefficient of the aluminum oxide layer can be easily adjusted to a predetermined range. I'll do it.
- the ratio of the orientation coefficient of the acid-aluminum layer between the rake face and the flank face can be easily adjusted to a predetermined range, and the surface-covered cutting without performance variation. It can be a tool.
- film peeling does not occur during continuous cutting that requires wear resistance, and the lower layer of the acid-aluminum layer is involved during intermittent cutting where strong impact is applied. Appropriate adhesion without causing peeling can be maintained.
- the rake face is slightly altered than the flank face, whereby the grain size of the acid aluminum layer on the rake face can be made fine and the hardness is improved. This improves the wear resistance on the rake face and also improves the acid-aluminum layer.
- By improving the toughness it is possible to increase the fracture resistance of the rake face with a large impact force and to suppress the occurrence of large chipping and defects.
- by reducing the interfacial energy of the flank wetting of the flank can be reduced and welding of the work material to the flank can be prevented.
- the crystal structure of the acid / aluminum layer can be controlled to the ⁇ -type acid / aluminum structure.
- the orientation coefficient of the acid aluminum layer can be easily controlled.
- film peeling can be suppressed while maintaining wear resistance.
- the rake face has more microcracks than the flank face, so it is easier to apply a larger impact in interrupted cutting, preventing fracture resistance on the rake face. In addition, it is possible to prevent welding on the flank.
- the rake face is more easily altered than the flank face, the grain size of the acid-aluminum layer becomes finer on the rake face, so the hardness and toughness are reduced. improves.
- the welding force can also be prevented by reducing the interfacial energy force of the aluminum oxide layer on the flank. Therefore, crater wear on the rake face, which is likely to be a problem in high-speed continuous cutting with a cutting speed of 200 m or more. And the welding of the work material to the flank can be improved.
- FIG. 1 is a schematic perspective view showing the appearance of a surface-coated cutting tool according to the present invention.
- FIG. 2 is a schematic sectional view showing an example of a film configuration of the surface-coated cutting tool of the present invention.
- FIG. 3 is an enlarged view of a portion A in FIG. 2 and a schematic diagram for explaining a method for measuring surface roughness in the present invention.
- FIG. 1 is a schematic perspective view showing a tool that works on the present embodiment
- FIG. 2 is a schematic sectional view showing a tool that works on the embodiment.
- the tool 1 has a rake face 2 on the main surface and a flank face 3 on the side surface, and a base 5 having a cutting edge 4 on the intersecting ridge line between the rake face 2 and the flank face 3.
- Hard coating layer on the surface of 6 This is a covered structure.
- Layer 7 and at least one layer of (HKL) surface of the aluminum oxide layer 7 has a (012) plane pin.
- the "JCPDS card” is a powder X-ray diffraction data file of a chemical substance published by "Joint Committee on Powder Diffraction Standards”.
- the rake face 2 of the tool 1 has the effect of increasing the strength against impact. For this reason, it is possible to prevent sudden chipping due to film peeling and breakage due to impact during cutting and tool life reduction due to abnormal wear.
- the orientation coefficient in the (012) crystal plane of the acid / aluminum layer 7 is reduced, the bond strength between the crystal grains of the acid / aluminum layer 7 is increased and the hardness of the acid / aluminum layer 7 is increased. Therefore, the wear resistance on the flank 3 of the tool 1 is improved. As a result, the entire tool can exhibit an excellent tool life in cutting. Desirable range of ratio TC / TC is 0.3-0.8, and more
- the crystal structure of the acid aluminum layer 7 is less likely to react with a work material having high acid resistance and wear resistance, and the life as a cutting tool is increased. To improve Therefore, it is desirable to have an aluminium-acid power that forms an a-type crystal structure.
- the acid-aluminum layer 7 has a ⁇ -type, in addition to the crystal structure of the ⁇ -type acid-aluminum layer.
- Another crystal structure such as ⁇ type and ⁇ type may be mixed at an intensity ratio lower than the strongest peak intensity of the X-ray diffraction peak of the ex type aluminum oxide layer. Even in this case, in measuring the orientation coefficient TC of the aluminum oxide layer 7, the orientation coefficient of the (012) plane is calculated only by the peak strength of the ⁇ -type aluminum oxide layer.
- the orientation coefficient TC of the aluminum oxide layer 7 on the rake face 2 is 1.2 to 2.5.
- the orientation coefficient TC of the aluminum oxide layer 7 on the flank 3 is 0.5 to 1.1.
- the orientation coefficient of the (012) plane in the cutting edge 4 TC to TC ratio, TC / TC is 0.2 to 0
- the layer thickness of the aluminum oxide layer 7 By setting the layer thickness of the aluminum oxide layer 7 to 1 to 6 ⁇ m, particularly 2 to 4 ⁇ m, it is possible to suppress film peeling while maintaining the wear resistance, and to set the orientation coefficient in this embodiment. This is desirable because it is easy to adjust to the setting range.
- the surface roughness force of the interface 9b between the substrate 5 and the hard coating layer 6 is 0.1 ⁇ m or less at the rake face 2, escapes to the face 3, and is 0.2 to 1.
- O / zm, preferably 0.2 to 0.5 m, and the orientation coefficient of the acid-aluminum layer 7 on the surface 2 and the flank 3 can be easily adjusted to a specified range, and the tool This is desirable because it is possible to obtain a tool 1 with no variation in performance by suppressing variations in the orientation coefficient in each part of 1.
- FIG. 3 is an enlarged view of a portion A in FIG. 2 and a schematic diagram for explaining the surface roughness measuring method in the present invention.
- the cutting surface or fracture surface of tool 1 is 5000 to 200 Observe with a scanning electron microscope (SEM) at a magnification of 00x.
- SEM scanning electron microscope
- a straight line substantially parallel to 5 is designated as B, and a straight line passing through the midpoint of the shortest distance h between these two straight lines and parallel to the substrate 5 is defined as a reference line.
- a straight line passing through the midpoint of the shortest distance h between these two straight lines and parallel to the substrate 5 is defined as a reference line.
- those protruding above the reference line C are defined as convex portions
- those concaved below the reference line C are defined as concave portions.
- the shortest distance to the apex is measured, and the average distance is calculated as the surface roughness.
- the orientation coefficient of the acid-aluminum layer 7 can be adjusted by adjusting the conditions of the bonding layer 8. Is desirable because it can be easily adjusted. Further, the adhesion of the aluminum oxide layer 7 can be increased to suppress film peeling.
- the oxygen concentration in the bonding layer 8 is preferably 2 to 10 atomic%. Thereby, the ratio of the orientation coefficients of the aluminum oxide layer 7 can be easily adjusted to a predetermined range, and the tool 1 without variation in performance can be obtained.
- the surface roughness force at the interface 9c between the aluminum oxide layer 7 and the bonding layer 8 is 0.08 ⁇ m or less for the rake face 2 and 0.1 ⁇ m to 0.8 for the flank face 3. m, especially 0.2 ⁇ m to 0.8 m, the ratio of the orientation coefficients of the aluminum oxide layer 7 can be easily adjusted to the above range, and the tool 1 without performance variations can be obtained. This is desirable because it can be done.
- the surface roughness of the interface 9c is measured by the same method as the method for measuring the interface 9b between the substrate 5 and the hard coating layer 6 described above.
- the lower layer 10 below the bonding layer 8 is a carbide or nitride of a group 4a, 5a, 6a metal, Si, Al, or two or more intermetallic compounds in the periodic table.
- a hard film composed of at least one selected from oxide, carbonitride, carbonate, nitride oxide, and oxynitride can be used.
- a titanium carbonitride layer having excellent film hardness and strength because both wear resistance and fracture resistance can be improved.
- the outermost layer 11 of the tool 1 by forming a gold-colored titanium nitride layer having a layer thickness of 0.1 to 2 m, the cutting edge 4 used when the tool 1 is used is worn. This is desirable because it can be easily discolored when the cutting blade 4 is used or not, because it discolors due to film peeling.
- the substrate 5 used in the present invention includes tungsten carbide (WC), titanium carbide (TiC), or titanium carbonitride (TiCN), and if desired, carbides of metals in groups 4a, 5a, and 6a of the periodic table, Nitride and carbonitride group strength Cemented carbide with at least one selected hard phase bonded with a binding phase composed of cobalt (Co) and Z or nickel (Ni) iron group metal. Or sintered ceramics of silicon nitride (Si N) or oxyaluminum (Al 2 O 3)
- Hard materials such as ultra-hard sintered bodies mainly composed of tetragonal boron nitride (cBN) and diamond, or high-hardness materials such as metals such as carbon steel, high-speed steel, and alloy steel are used. It is composed of a cemented carbide composed of a hard phase mainly composed of tungsten carbide (WC) and a binder phase having a cobalt (Co) force.
- cBN tetragonal boron nitride
- Co cobalt
- the film hardness of the acid aluminum layer 7 on the rake face 2 measured by a micro Vickers hardness meter is 20 GPa or more, and the film hardness of the acid aluminum layer 7 on the flank face 3 However, it is preferably 0.5 GPa or more higher than the film hardness of the aluminum oxide layer 7 on the rake face 2.
- the wear resistance of the aluminum oxide layer 7 on the flank face 3 can be increased, and the impact resistance on the rake face 2 can be increased to maintain the wear resistance, and the wear resistance of the rake face 2 can be reduced. This is desirable because it can be prevented.
- metal powder, carbon powder, etc. are appropriately added to and mixed with inorganic powders such as metal carbides, nitrides, carbonitrides, and oxides, which can be formed by firing the hard alloy described above, and press molding and filling are performed.
- the surface of the rake face 2 of the base body 5 is made of elastic turret, brush, wrap, blast.
- the surface roughness observed in the cross section of the substrate of the rake face 2 is smoothed to 0. or less and the flank 3 has a surface roughness of 0.2 to 1 m. It is controlled by polishing separately depending on the method.
- the hard coating layer 6 is formed on the surface of the substrate 5 by, for example, a chemical vapor deposition (CVD) method.
- the lower layer 10 is formed.
- the salt gas of titanium (TiCl) gas is set to 0.1 to LO volume%, nitrogen ( N) Gas
- Adjust the reaction gas by sequentially adjusting the gas mixture with 0 to 60% by volume of 4 2 and the remaining hydrogen (H) gas power.
- titanium carbonitride layer as the lower layer 10, for example, as a reaction gas composition, Shioi ⁇ titanium (TiCl) gas from 0.1 to 10 volume 0/0, the nitrogen (N) gas 0-60 volume 0/0, methane (
- a mixed gas consisting of hydrogen (H) gas is adjusted and introduced into the reaction chamber.
- the reaction gas composition is TiCl gas.
- the bonding layer 8 described above is formed on the surface of the lower layer 10, that is, immediately below the aluminum oxide layer 7.
- TiCNO titanium carbonate nitride
- TiCl titanium chloride
- CH methane
- N nitrogen
- 4 4 2 is adjusted by sequentially adjusting a mixed gas consisting of 0 to 60% by volume, CO gas, and the remaining hydrogen (H) gas.
- the CO gas among the reaction gases for forming the bonding layer 8 is formed. Concentration from 0.3 to 1.2
- the volume% is particularly effective.
- an aluminum oxide layer 7 is formed on the surface of the bonding layer 8.
- a TiN film may be formed on the outermost surface using the above film formation conditions in order to make it easy to determine whether the blade edge is used or not.
- an acid aluminum Al 2 O 3
- Layer 7 and at least one (HKL) surface of the aluminum oxide layer 7 has a (110) surface pin.
- the ratio of the orientation factor TC on the rake face 2 to the orientation factor TC on the flank 3 TC / TC is 0.3.
- the (110) face peak is set high to facilitate the generation of microcracks and release residual stress. Further, it is possible to suppress the occurrence of a large sudden defect by improving the impact resistance.
- the (110) plane peak of the acid-aluminum layer 7 is set low, and microcracks are generated in the acid-aluminum layer 7 This prevents the work material from entering and welding into the microcracks. As a result, the tool 1 can exhibit stable and reliable performance capable of stable cutting.
- the oxide-aluminum layer 7 on the rake face 2 side is configured to have a strong (110) crystal orientation, thereby generating microcracks in the acid-aluminum layer 7.
- the residual stress in the aluminum oxide layer 7 can be released to improve the toughness of the film, and the tool life can be prevented from being shortened due to a suddenly large defect on the rake face 2 of the tool 1.
- the orientation coefficient TC in the (110) crystal plane of the acid-aluminum layer 7 is reduced to increase the bond strength between the crystal grains of the acid-aluminum layer 7.
- a particularly desirable range of the ratio of orientation coefficients TC / TC is 0.5 to 0.85.
- the crystal structure of the acid-aluminum layer 7 is excellent in resistance to abrasion due to a chemical reaction that hardly reacts with a work material having high acid-resistance.
- the a-type acid / aluminum layer is used for measuring the orientation coefficient in the (110) plane of the acid / aluminum layer 7 in the present embodiment.
- the acid-aluminum layer 7 has ⁇ -type, in addition to the crystal structure of the ⁇ -type acid-aluminum layer
- Another crystal structure such as ⁇ type and ⁇ type may be mixed at an intensity ratio lower than the strongest peak intensity of the X-ray diffraction peak of the ex type aluminum oxide layer. Even in this case, in the measurement of the orientation coefficient TC of the aluminum oxide layer 7, the (110) plane orientation coefficient is calculated only by the peak strength of the ⁇ -type aluminum oxide layer.
- the orientation coefficient TC of the aluminum oxide layer 7 on the rake face 2 is 1.3 to 5.0, preferably
- the orientation coefficient of the (110) plane in the cutting edge 4 is the ratio of TC to TC, and TC / TC is 0.2 to 0.
- the layer thickness of the aluminum oxide layer 7 By setting the layer thickness of the aluminum oxide layer 7 to 1 to 6 ⁇ m, particularly 2 to 4 ⁇ m, it is possible to suppress film peeling while maintaining wear resistance, and to set the orientation coefficient in this embodiment. This is desirable because it is easy to adjust to the setting range.
- the surface roughness force of the interface 9b between the substrate 5 and the hard coating layer 6 is 0.2 to 1 / ⁇ ⁇ at the rake face 2, and 0.6 to 2 m at the flank face 3. desirable.
- the orientation coefficient of the acid-aluminum layer 7 on the rake face 2 and the flank face 3 can be easily adjusted to a predetermined range, and variations in the orientation coefficient in each part of the tool 1 are suppressed. You can get a tool 1 with no variation.
- the method for measuring the surface roughness at the interface 9b can be measured in the same manner as the measurement method described in the above embodiment.
- the bonding layer 8 having a compound strength containing at least titanium and oxygen immediately below the acid-aluminum layer 7, adjusting the conditions of the bonding layer 8, the orientation coefficient of the acid-aluminum layer 7 can be adjusted. It is desirable because it becomes easy to adjust the value. Further, the adhesion of the aluminum oxide layer 7 can be increased to suppress film peeling.
- the ratio of the orientation coefficient of the aluminum oxide layer 7 can be easily adjusted to the above range, Desirable because tool 1 can be made without any variation in performance!
- the surface roughness force at the interface 9c between the acid-aluminum layer 7 and the bonding layer 8 is 0.2 to 0.5 m for the rake face 2, and 0.6 ⁇ m to 2 for the flank face 3. It is desirable that the thickness is ⁇ m because the ratio of the orientation coefficients of the aluminum oxide layer 7 can be easily adjusted within the above range and the tool 1 can be obtained without variation in performance.
- the surface roughness of the interface 9c is measured by the same method as the measurement method of the interface 9b between the substrate 5 and the hard covering layer 6 described above.
- a lower layer 10 similar to that of the first embodiment is formed below the bonding layer 8. It is preferable that the outermost layer 11 similar to that of the first embodiment is formed on the outermost surface of the tool 1 that is preferably applied.
- examples of the substrate 5 of the present embodiment include the same ones as exemplified in the first embodiment.
- the adhesion force of the acid aluminum layer 7 on the rake face 2 is in the range of 40N to 120N, and the adhesion force 30N of the aluminum oxide layer 7 on the flank face 3 is: LOON Within the range, the acid / aluminum layer 7 does not peel off during continuous cutting, and only the acid / aluminum layer 7 peels off during intermittent cutting. Since the lower layer remains, it is desirable because sufficient wear resistance can be maintained even during intermittent cutting.
- the peel load of the acid aluminum 7 can be measured, for example, by measuring the adhesion force of the acid aluminum layer 7 by a scratch test. Specifically, the scratch test is measured by pulling the surface of the acid aluminum layer 7 of the tool 1 with a diamond indenter under the following conditions.
- the boundary position between the region where the oxide aluminum layer 7 is exposed and the lower layer 10 different from the aluminum oxide layer 7 or the region where the substrate 5 is exposed is identified in the scratch mark, and at this position.
- the peel load (F) at which the aluminum oxide layer 7 starts to peel can be obtained.
- the element component exposed on the surface is confirmed by X-ray spectroscopic analysis (EPMA) or X-ray photoelectron spectroscopic analysis (XPS).
- EPMA X-ray spectroscopic analysis
- XPS X-ray photoelectron spectroscopic analysis
- the base 2 is produced in the same manner as in the first embodiment described above.
- the orientation coefficient in the (110) plane of the aluminum oxide layer 7 it is necessary to adjust the surface roughness immediately below the oxidized aluminum layer 7.
- the surface of the rake face 2 of the base body 5 is polished by an elastic mortar, brush, wrap, blast, barrel processing or the like.
- the surface roughness observed in the cross section of the base body 5 of the rake face 2 should be within the range of 0.2 to 1111, and the flank 3 should have a surface roughness force SO. 6 to 2 m. It is controlled by polishing separately according to the above method.
- the hard coating layer 6 is formed on the surface of the substrate 2 by, eg, chemical vapor deposition (CVD).
- the lower layer 10 is formed.
- the lower layer 10 may be formed in the same manner as in the first embodiment described above.
- the above-described bonding layer 8 is formed on the surface of the lower layer 10, that is, immediately below the aluminum oxide layer 7.
- TiCNO titanium carbonate nitride
- TiCl titanium chloride emissions
- CH methane
- the volume% is particularly effective.
- an aluminum oxide layer 7 is formed on the surface of the bonding layer 8.
- the aluminum oxide layer 7 may be formed in the same manner as in the first embodiment described above. That is, even if the film formation conditions of the aluminum oxide layer 7 are similar, the film formation conditions such as the bonding layer directly under the aluminum oxide layer and the formation conditions such as the surface roughness are changed. Thus, the properties of the oxidized aluminum layer 7 can be changed.
- TiN titanium nitride
- a third embodiment of the surface-coated cutting tool according to the present invention will be described.
- the same or equivalent parts as those in the first and second embodiments described above are denoted by the same reference numerals and description thereof is omitted.
- Layer 7 at least one layer, and the (HKL) surface of this aluminum oxide layer 7 has a (113) surface pin.
- the ratio of the orientation factor TC on the rake face 2 to the orientation factor TC on the flank 3 TC / TC is 0.3.
- the grain size of the acid film layer on the rake face can be made finer, the hardness is improved, and the wear resistance on the rake face is increased.
- the toughness of the aluminum oxide layer it is possible to improve the fracture resistance of the rake face with a large impact force and to suppress the occurrence of large chipping and defects.
- wetting of the flank surface can be reduced and work material can be prevented from welding to the flank surface. It is possible to prevent crater wear and degradation of machined surface quality due to welding of work material on the flank.
- a particularly desirable range of the ratio TC ZTC is 0.
- orientation coefficient TC of the (113) plane of the aluminum oxide layer 7 on the rake face 2 is 0 ⁇ 4.
- ⁇ L 0, preferably ⁇ or 0.4 to 0.7, clearance, self-direction coefficient of surface 3 TC force 0.2 to 0.7, preferably ⁇ or 0
- orientation coefficient of the (113) plane at the cutting edge 4 TC to TC ratio, TC / TC is 0.2 to 0
- the layer thickness of the aluminum oxide layer 7 By setting the layer thickness of the aluminum oxide layer 7 to 1 to 6 ⁇ m, particularly 2 to 4 ⁇ m, it is possible to suppress film peeling while maintaining wear resistance, and to set the orientation coefficient in the present embodiment. This is desirable because it is easy to adjust to the setting range.
- a bonding layer 8 having a compound strength containing at least titanium and oxygen immediately below the aluminum oxide layer 7.
- the crystal structure of the aluminum oxide layer 7 can be controlled to an ⁇ -type aluminum oxide structure.
- the adhesion of the aluminum oxide layer 7 can be enhanced to suppress film peeling.
- the ratio of the orientation coefficient of the aluminum oxide layer 7 can be easily adjusted to the above range, Desirable because tool 1 can be made without any variation in performance!
- the lowermost surface 10 similar to that in the above embodiment is preferably formed below the bonding layer 8, and the outermost surface of the tool 1 is preferably the same as in the above embodiment.
- the outermost layer 11 is preferably formed.
- examples of the substrate 5 of the present embodiment include those similar to those exemplified in the above embodiment.
- the base 2 is produced in the same manner as in the first embodiment described above.
- the orientation coefficient in the (113) plane of the aluminum oxide layer 7 it is necessary to adjust the surface roughness immediately below the oxidized aluminum layer 7.
- the method first, the surface of the rake face 2 of the base 5 is polished with an elastic mortar, brush, wrap, blast, ballet, etc., and observed on the cross section of the base 5 of the rake face 2. The surface roughness is controlled within the range of 0.05-0. And the flank 3 is polished and controlled separately by the above method so that the surface roughness is 0.4-1.
- the hard coating layer 6 is formed on the surface of the substrate 2 by, for example, chemical vapor deposition (CVD).
- the lower layer 10 is formed.
- the lower layer 10 may be formed in the same manner as in the first embodiment described above.
- the above-described bonding layer 8 is formed on the surface of the lower layer 10, that is, immediately below the aluminum oxide layer 7.
- TiCNO titanium carbonate nitride
- TiCl titanium chloride emissions
- CH methane
- the volume% is particularly effective.
- an aluminum oxide layer 7 is formed on the surface of the bonding layer 8.
- a method for forming the aluminum oxide layer 7 it may be formed in the same manner as in the first embodiment described above.
- a titanium nitride (TiN) film may be formed on the outermost surface using the above film formation conditions in order to make it easy to determine whether the blade edge is used or not.
- the manufacturing method of the cut material of this invention is demonstrated.
- the method of manufacturing the cut object of the present invention applies the cutting edge formed on the crossed ridge line portion between the rake face and the flank face of the surface-coated cutting tool according to the present invention to the cut object. Processing is performed. Thereby, it is possible to obtain a cut object having a stable and excellent machining surface.
- the cutting process includes a high-speed continuous cutting process.
- a tool that uses the (HKL) surface of the aluminum oxide layer as the (113) surface that is, a tool that works on the third embodiment described above. .
- the particles forming the acid-aluminum layer become weak, and thus the mechanical properties such as the hardness and toughness of the acid-aluminum layer are improved. It is possible to improve the property and suppress damage such as micro-chipping.
- the (113) orientation is weaker than the rake face, so that the interface energy of the acid-aluminum layer on the flank face is lowered and reaction with the work material is less likely to occur. Prevents welding of cutting materials Therefore, it is possible to suppress the deterioration of the work quality of the work material.
- the tool that works in the third embodiment is likely to cause problems in high-speed continuous cutting with a cutting speed of 200 m or more, crater wear and micro-chipping on the rake face, and welding of the work material to the flank face. Can be improved.
- the cutting may include an intermittent cutting process.
- the tool to be used is one in which the (HKL) surface of the aluminum oxide layer is the (110) surface, that is, a tool that works well in the second embodiment described above. preferable.
- the rake face has a configuration with more microcracks than the flank face, so it is easy to receive a larger impact in interrupted cutting, and it can prevent fracture resistance on the rake face and prevent welding on the flank face. be able to.
- the cutting may include a continuous cutting process and an intermittent cutting process.
- a tool in which the (HKL) surface of the aluminum oxide layer is the (012) surface that is, a tool that works on the first embodiment described above. Yes.
- the force described in the case where the (HKL) plane of the aluminum oxide layer is the (012) plane, the (110) plane, and the (113) plane is the aluminum oxide of the present invention.
- the (HKL) plane of the layer is not limited to this, and any (012), (104), (110), (113), (024), (116) plane force may be selected.
- the hard coating layer 6 including the acid-aluminum layer 7 is formed by a chemical vapor deposition (CVD) method, but the present invention is limited to this.
- the hard coating layer 6 may be formed by other film forming methods such as physical vapor deposition (PVD).
- PVD physical vapor deposition
- TiC Titanium carbide
- WC tungsten carbide
- CNMA120412 tungsten carbide
- a cemented carbide was prepared by firing at 1500 ° C for 1 hour. Further, the manufactured carbide was subjected to cutting edge treatment (Hounging R) from the rake face so as to have the substrate surface roughness shown in Table 2 with a brush cage. The flank 3 was also controlled so that the surface roughness in the cross-sectional observation of the tool was within the range shown in Table 2.
- the interface between the substrate and the hard coating layer on the fracture surface of the obtained tool was observed with a scanning electron microscope (SEM) at a magnification of 15000 to measure the surface roughness of the substrate.
- SEM scanning electron microscope
- a straight line that passes through the highest convex portion H where the base protrudes most and is substantially parallel to the base is A, and the base is the most concave.
- a straight line passing through the deepest recess L and substantially parallel to the base was defined as B.
- a straight line passing through the midpoint of the shortest distance h between the two straight lines A and B and substantially parallel to the substrate was defined as a reference line C.
- the shortest distance between the highest part of the undulation peak at the interface between the base and the hard coating layer and the deepest part of the valley and the reference line is measured for each peak and valley, and the average value of the distances is measured.
- the surface was rough.
- the surface roughness of the substrate was measured on the rake face and flank face by the above method, and the average was calculated for each sample. The results are shown in Table 2.
- FCD700 Ductile pig iron 4 grooved sleeve material
- Evaluation item Observe the cutting edge with a microscope and measure the amount of flank wear and tip wear.
- FCD700 Ductile pig iron 4 grooved sleeve material
- Feeding speed 0.3 to 0.5 (feed amount fluctuation) mmZrev
- TC / TC is from 0.3
- Sample No. 1-8 which had a small tool life, had abnormal wear from the rake face and a short tool life.
- sample Nos. 1 to 1-6 with TC / TC in the range of 0.3 to 0.95 are resistant to
- a cemented carbide was prepared in the same manner as in Example I, and a blade edge treatment (Hounging R) was applied from the rake face so that the substrate surface roughness shown in Table 5 was obtained by brushing.
- the flank 3 was also controlled so that the surface roughness in the cross-sectional observation of the tool was in the range shown in Table 5.
- TiN Surface layer
- the direction coefficient TC was calculated as the average of three locations, and the ratio TC ZTC was calculated.
- the result is a table
- the obtained tool was subjected to a scratch test on the rake face and flank face of the tool under the following conditions, and the peeling state was observed and the delamination state and the load at which the coating layer began to peel from the substrate Then, the adhesive strength of the acid aluminum layer was calculated.
- FCD700 Ductile pig iron sleeve material
- Evaluation item Observe the cutting edge with a microscope and measure the amount of flank wear and tip wear.
- FCD700 Ductile pig iron 4 grooved sleeve material
- Feeding speed 0.3 to 0.5 (feed amount fluctuation) mmZrev
- sample Nos. 11-1 to 6 with TC / TC in the range of 0.3 to 0.95 are resistant to
- a cemented carbide was prepared in the same manner as in Example I, and a blade edge treatment (Hounging R) was applied from the rake face so as to have the substrate surface roughness shown in Table 8 by brushing.
- flank 3 was also controlled so that the surface roughness in the cross-sectional observation of the tool was within the range shown in Table 8.
- the orientation coefficient TC was calculated as the average of three locations, and the ratio TC ZTC was calculated. Result
- Evaluation item Observe the cutting edge with a microscope and measure the amount of flank wear and tip wear.
- Feeding speed 0.3 to 0.5 (feed amount fluctuation) mmZrev
- TC / TC is from 0.3
- sample No. Ill-8 which had a small tool life, had abnormal wear from the rake face.
- Sample Nos. Ill — 1 to 6 in the range of F R ⁇ 0.95 were excellent in both wear resistance and fracture resistance, and the edge of the blade was almost completely damaged.
Description
Claims
Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US11/571,813 US8007929B2 (en) | 2004-07-29 | 2005-07-20 | Surface coated cutting tool |
JP2006529232A JP4658939B2 (ja) | 2004-07-29 | 2005-07-20 | 表面被覆切削工具 |
EP05766413A EP1772217B1 (en) | 2004-07-29 | 2005-07-20 | Surface coated cutting tool |
Applications Claiming Priority (4)
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JP2004-221181 | 2004-07-29 | ||
JP2004221181 | 2004-07-29 | ||
JP2004-249293 | 2004-08-27 | ||
JP2004249293 | 2004-08-27 |
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WO2006011396A1 true WO2006011396A1 (ja) | 2006-02-02 |
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PCT/JP2005/013278 WO2006011396A1 (ja) | 2004-07-29 | 2005-07-20 | 表面被覆切削工具 |
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US (1) | US8007929B2 (ja) |
EP (1) | EP1772217B1 (ja) |
JP (1) | JP4658939B2 (ja) |
KR (1) | KR100983551B1 (ja) |
WO (1) | WO2006011396A1 (ja) |
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JP2008173737A (ja) * | 2007-01-22 | 2008-07-31 | Hitachi Tool Engineering Ltd | 酸化アルミニウム被覆工具 |
WO2011105420A1 (ja) * | 2010-02-24 | 2011-09-01 | 京セラ株式会社 | 切削工具 |
JP2012101336A (ja) * | 2010-11-12 | 2012-05-31 | Mitsubishi Materials Corp | 耐摩耗性と切屑排出性に優れた表面被覆ドリル |
WO2017204141A1 (ja) * | 2016-05-24 | 2017-11-30 | 株式会社タンガロイ | 被覆切削工具 |
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EP1736307A4 (en) * | 2004-03-29 | 2011-10-05 | Kyocera Corp | SURFACE COATING AND CUTTING TOOL |
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US8129040B2 (en) * | 2007-05-16 | 2012-03-06 | Oerlikon Trading Ag, Truebbach | Cutting tool |
AT12293U1 (de) * | 2009-10-05 | 2012-03-15 | Ceratizit Austria Gmbh | Schneidwerkzeug zur bearbeitung metallischer werkstoffe |
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JP5890594B2 (ja) * | 2013-12-17 | 2016-03-22 | 京セラ株式会社 | 被覆工具 |
US9405990B2 (en) * | 2014-08-19 | 2016-08-02 | Morpho Detection, Llc | X-ray diffraction imaging system with signal aggregation across voxels containing objects and method of operating the same |
EP3195960B1 (en) * | 2014-08-28 | 2020-01-15 | Kyocera Corporation | Coated tool |
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JP6419220B2 (ja) * | 2015-01-28 | 2018-11-07 | 京セラ株式会社 | 被覆工具 |
KR102089996B1 (ko) * | 2015-11-28 | 2020-03-17 | 쿄세라 코포레이션 | 절삭 공구 |
CN108430681B (zh) * | 2016-11-15 | 2020-06-23 | 住友电工硬质合金株式会社 | 切削工具 |
JP6519935B1 (ja) | 2018-03-16 | 2019-05-29 | 住友電工ハードメタル株式会社 | 表面被覆切削工具及びその製造方法 |
US11219952B2 (en) | 2018-03-16 | 2022-01-11 | Sumitomo Electric Hardmetal Corp. | Surface-coated cutting tool and method of manufacturing the same |
US11167375B2 (en) | 2018-08-10 | 2021-11-09 | The Research Foundation For The State University Of New York | Additive manufacturing processes and additively manufactured products |
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CN113664295A (zh) * | 2021-09-08 | 2021-11-19 | 南京航空航天大学 | 一种加工蠕墨铸铁用表面织构刀具及其制备方法 |
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Also Published As
Publication number | Publication date |
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JPWO2006011396A1 (ja) | 2008-05-01 |
EP1772217B1 (en) | 2013-04-03 |
EP1772217A4 (en) | 2011-12-28 |
US8007929B2 (en) | 2011-08-30 |
JP4658939B2 (ja) | 2011-03-23 |
KR100983551B1 (ko) | 2010-09-24 |
US20090214857A1 (en) | 2009-08-27 |
KR20070038159A (ko) | 2007-04-09 |
EP1772217A1 (en) | 2007-04-11 |
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