USRE41111E1 - Cutting tool - Google Patents

Cutting tool Download PDF

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USRE41111E1
USRE41111E1 US12/211,244 US21124408A USRE41111E US RE41111 E1 USRE41111 E1 US RE41111E1 US 21124408 A US21124408 A US 21124408A US RE41111 E USRE41111 E US RE41111E
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layer
cutting
hard coating
tin
ticn
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US12/211,244
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Takatoshi Oshika
Toshiaki Ueda
Takuya Hayahi
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Mitsubishi Materials Corp
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Mitsubishi Materials Corp
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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
    • 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
    • C23C16/02—Pretreatment of the material to be coated
    • C23C16/0272—Deposition of sub-layers, e.g. to promote the adhesion of the main coating
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16B—DEVICES FOR FASTENING OR SECURING CONSTRUCTIONAL ELEMENTS OR MACHINE PARTS TOGETHER, e.g. NAILS, BOLTS, CIRCLIPS, CLAMPS, CLIPS OR WEDGES; JOINTS OR JOINTING
    • F16B2/00—Friction-grip releasable fastenings
    • F16B2/02—Clamps, i.e. with gripping action effected by positive means other than the inherent resistance to deformation of the material of the fastening
    • F16B2/06—Clamps, i.e. with gripping action effected by positive means other than the inherent resistance to deformation of the material of the fastening external, i.e. with contracting action
    • F16B2/065—Clamps, i.e. with gripping action effected by positive means other than the inherent resistance to deformation of the material of the fastening external, i.e. with contracting action using screw-thread elements
    • 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
    • C23C16/34—Nitrides
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C16/00—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
    • C23C16/22—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes characterised by the deposition of inorganic material, other than metallic material
    • C23C16/30—Deposition of compounds, mixtures or solid solutions, e.g. borides, carbides, nitrides
    • C23C16/36—Carbonitrides
    • 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
    • C23C28/042—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 including a refractory ceramic layer, e.g. refractory metal oxides, ZrO2, rare earth oxides
    • 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
    • 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
    • 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
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16B—DEVICES FOR FASTENING OR SECURING CONSTRUCTIONAL ELEMENTS OR MACHINE PARTS TOGETHER, e.g. NAILS, BOLTS, CIRCLIPS, CLAMPS, CLIPS OR WEDGES; JOINTS OR JOINTING
    • F16B5/00—Joining sheets or plates, e.g. panels, to one another or to strips or bars parallel to them
    • F16B5/06—Joining sheets or plates, e.g. panels, to one another or to strips or bars parallel to them by means of clamps or clips
    • F16B5/0685—Joining sheets or plates to strips or bars
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16L—PIPES; JOINTS OR FITTINGS FOR PIPES; SUPPORTS FOR PIPES, CABLES OR PROTECTIVE TUBING; MEANS FOR THERMAL INSULATION IN GENERAL
    • F16L3/00—Supports for pipes, cables or protective tubing, e.g. hangers, holders, clamps, cleats, clips, brackets
    • F16L3/08—Supports for pipes, cables or protective tubing, e.g. hangers, holders, clamps, cleats, clips, brackets substantially surrounding the pipe, cable or protective tubing
    • F16L3/10—Supports for pipes, cables or protective tubing, e.g. hangers, holders, clamps, cleats, clips, brackets substantially surrounding the pipe, cable or protective tubing divided, i.e. with two or more members engaging the pipe, cable or protective tubing
    • F16L3/1008—Supports for pipes, cables or protective tubing, e.g. hangers, holders, clamps, cleats, clips, brackets substantially surrounding the pipe, cable or protective tubing divided, i.e. with two or more members engaging the pipe, cable or protective tubing with two members engaging the pipe, cable or tubing, both being made of thin band material completely surrounding the pipe
    • F16L3/1016—Supports for pipes, cables or protective tubing, e.g. hangers, holders, clamps, cleats, clips, brackets substantially surrounding the pipe, cable or protective tubing divided, i.e. with two or more members engaging the pipe, cable or protective tubing with two members engaging the pipe, cable or tubing, both being made of thin band material completely surrounding the pipe the members being joined by means of two screws
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23B—TURNING; BORING
    • B23B2228/00—Properties of materials of tools or workpieces, materials of tools or workpieces applied in a specific manner
    • B23B2228/10—Coatings
    • 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
    • Y10T428/24—Structurally defined web or sheet [e.g., overall dimension, etc.]
    • Y10T428/24942—Structurally defined web or sheet [e.g., overall dimension, etc.] including components having same physical characteristic in differing degree
    • Y10T428/2495—Thickness [relative or absolute]
    • Y10T428/24967—Absolute thicknesses specified
    • Y10T428/24975—No layer or component greater than 5 mils thick
    • 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
    • Y10T428/30—Self-sustaining carbon mass or layer with impregnant or other layer

Definitions

  • the present invention relates to a Cermet cutting tool having a coated surface (to be referred to as a coated Cermet cutting tool) used for high-speed, intermittent cutting of various types of steel, cast iron and so forth, and its hard coating layer in particular demonstrates superior chipping resistance.
  • coated Cermet cutting tools comprise a base (to be generically referred to as the tool base) made of tungsten carbide (WC)-based cemented carbide or titanium carbide (TiC)-based Cermet, and a hard coating layer.
  • This hard coating layer comprises:
  • coated Cermet cutting tools are widely known to be used for continuous and intermittent cutting of various types of steel, cast iron and so forth.
  • Japanese Unexamined Patent Application, First Publication No. Hei 6-31503 discloses that the Ti compound layer and the ⁇ -Al 2 O 3 layer, which compose a hard coating layer, have a particulate crystal structure.
  • Japanese Unexamined Patent Application, First Publication No. Hei 6-8010 discloses a technology for improving the strength of a TiCN layer comprising the Ti compound layer in which the TiCN layer is made to contain a longitudinally growing crystal structure by vapor deposition with an ordinary chemical vapor deposition device in an intermediate temperature range of 700-950° C. using a mixed gas containing organic carbonitride as the reactive gas.
  • Cutting devices have recently come to be required to offer higher performance, and there are also strong needs for saving of labor, saving of energy and reduced costs with respect to cutting processing. Accompanying these needs, the speed of cutting processing is tending to become even faster, resulting in the unavoidable circumstances of cutting processing under heavy-duty cutting conditions including greater cutting depth and faster feeding.
  • the inventors of the present invention conducted research to improve chipping resistance by focusing on a Cermet cutting tool comprising an ⁇ -Al 2 O 3 layer as the hard coating layer. As a result, the following research results were obtained.
  • an ⁇ -Al 2 O 3 layer is formed under ordinary conditions on the Al 2 O 3 core thin film which is heat treated under conditions in which the reaction atmosphere is changed to a hydrogen atmosphere at a pressure of 3-13 kPa and the reaction atmosphere temperature is raised to 1100-1200° C.
  • the ⁇ -Al 2 O 3 layer obtained in this manner was confirmed to demonstrate a pole plot graph in which the highest peak of the inclination section appears within a narrow range.
  • the inclination of the normal of the (0001) plane of crystal grains relative to the normal of the surface polishing plane is measured by emitting an electron beam onto individual ⁇ -Al 2 O 3 crystal grains having a hexagonal crystal lattice present within the measuring range of the surface polishing plane using a field emission scanning electron microscope.
  • the measured inclinations within the range of 0-45 degrees indicated by the individual crystal grains are divided for each pitch of 0.25 degrees, and a pole plot graph is prepared in which the measured inclination present in each section are tabulated for each section.
  • the pole plot graph is shown in which the highest peak of the inclination division appears within a narrow range of 0-10 degrees.
  • a conventional ⁇ -Al 2 O 3 layer was confirmed to have a pole plot graph in which a gradual highest pitch of the inclination section appears over a wide range of 25-35 degrees.
  • the present invention is based on these research results.
  • the present invention provides a cutting tool provided with a tool base composed with WC-based cemented carbide or TiCN-based Cermet, and a hard coating layer; wherein the hard coating layer comprises:
  • the ⁇ -Al 2 O 3 layer which composes the hard coating layer, exhibits a pole plot graph in which the highest peak appears in the inclination section within a range of 0-10 degrees as shown in FIG. 2 , and demonstrates superior chipping resistance.
  • the cutting tool of the present invention exhibits superior wear resistance and cutting performance over a long period of time even during high-speed intermittent cutting of various types of steel and cast iron that is accompanied by extremely high levels of mechanical and thermal shock as well as the generation of a large amount of heat.
  • the hard coating layer it is preferable for the hard coating layer to have an aluminum oxide core thin layer containing an aluminum oxide core between the lower layer and the upper layer.
  • the mean layer thickness of the aluminum oxide core thin layer prefferably be in a range of 20-200 nm.
  • the hard coating layer is obtained by forming the Ti compound and/or Zr compound layer; forming the aluminum oxide core thin layer on the surface of the Ti compound and/or Zr compound layer under conditions of a reaction gas composition, in % by volume, of AlCl 3 : 3-10%, CO 2 : 0.5-3%, C 2 H 4 : 0.01-0.3% and H 2 : remainder, a reaction atmosphere temperature of 750-900° C. and a reaction atmosphere pressure of 3-13 kPa; and heating the aluminum oxide core thin layer to 1100-1200° C. under conditions in which the reaction atmosphere is hydrogen and the reaction pressure is 3-13 kPa; and forming the aluminum oxide layer having an ⁇ crystal structure on the heated aluminum oxide core thin layer.
  • a reaction gas composition in % by volume, of AlCl 3 : 3-10%, CO 2 : 0.5-3%, C 2 H 4 : 0.01-0.3% and H 2 : remainder, a reaction atmosphere temperature of 750-900° C. and a reaction atmosphere pressure of 3-13
  • FIGS. 1A and 1B are sketch drawings showing the measuring range of inclination of the normal of the (0001) plane of crystal grains in an ⁇ -Al 2 O 3 layer which comprises a hard coating layer.
  • FIG. 2 is a pole plot graph of the (0001) plane of an ⁇ -Al 2 O 3 layer which comprises a hard coating layer of the cutting tool of the present invention.
  • FIG. 3 is a pole plot graph of the (0001) plane of an ⁇ -Al 2 O 3 layer which comprises a hard coating layer of a cutting tool of the prior art.
  • the cutting tool of the present invention is provided with a tool base composed with WC-based cemented carbide or TiCN-based Cermet, and a hard coating layer.
  • the hard coating layer further comprises a Ti compound and/or Zr compound layer, which is a lower layer, and an ⁇ -Al 2 O 3 layer, which is an upper layer.
  • the Ti compound and/or Zr compound layer is basically present as the lower layer of the ⁇ -Al 2 O 3 layer. Since it has superior strength, the hard coating layer comprising it also has superior strength. In addition, since it is securely adhered to both the tool base and the ⁇ -Al 2 O 3 layer, it contributes to improved adhesion of the hard coating layer to the tool base. If the mean layer thickness is less than 0.5 ⁇ m, the actions are unable to be fully demonstrated. On the other hand, if the mean layer thickness exceeds 20 ⁇ m, the thermoplastic deformation occurs easily during high-speed intermittent cutting accompanying the generation of high levels of heat, in particular, thereby causing uneven wear. Consequently, the mean layer thickness of the Ti compound and/or Zr compound layer is defined to be 0.5-20 ⁇ m.
  • the ⁇ -Al 2 O 3 layer improves wear resistance of the hard coating layer because Al 2 O 3 itself has high hardness and superior heat resistance.
  • the ⁇ -Al 2 O 3 layer of the present invention since the ⁇ -Al 2 O 3 layer of the present invention has superior strength as compared with conventional ⁇ -Al 2 O 3 layers, it acts to further improve the chipping resistance of the hard coating layer.
  • the effects are unable to be adequately demonstrated if its mean layer thickness is less than 1 ⁇ m.
  • it is thicker than 30 ⁇ m, chipping occurs easily. Consequently, the mean layer thickness of the ⁇ -Al 2 O 3 layer is defined to be 1 30 ⁇ m.
  • Its mean layer thickness is preferably 20 nm or more, and more preferably 30 nm or more.
  • its mean layer thickness is preferably 200 nm or less, and more preferably 150 nm or less.
  • the mean layer thickness of the Al 2 O 3 core thin film formed on the Ti compound and/or Zr compound layer prior to formation by vapor deposition of the ⁇ -Al 2 O 3 layer is preferably 20-200 nm, and more preferably 30-150 nm.
  • a TiN layer having a gold color tone may also be formed by vapor deposition as necessary as the uppermost surface layer of the hard coating layer for the purpose of discriminating before and after use of the coated Cermet cutting tool.
  • the mean layer thickness of the TiN layer having a gold color tone is preferably 0.1-1 ⁇ m. If the mean layer thickness is less than 0.1 ⁇ m, adequate discrimination effects are unable to be obtained. In addition, a mean layer thickness of up to 1 ⁇ m is adequate for the TiN layer to demonstrate a discrimination effect.
  • Mo 2 C powder Mo 2 C powder
  • ZrC powder ZrC powder
  • NbC powder NbC powder
  • TaC powder WC powder
  • the Ti compound and/or Zr compound layers having the target layer thicknesses shown in Table 4 were first formed by vapor deposition as the lower layer of the hard coating layer under the conditions shown in Table 3 (the 1-TiCN in Table 3 indicates the formation conditions of a TiCN layer having a longitudinally growing crystal structure described in Japanese Unexamined Patent Application, First Publication No. Hei 6-8010, while others indicate the formation conditions of an ordinary particulate crystal structure) using an ordinary chemical vapor deposition device on the surfaces of these tool bases A through F and a through f.
  • Al 2 O 3 core thin films of the target layer thicknesses shown in Table 4 were formed under low-temperature conditions in which a reaction gas composition comprising, in % by volume, AlCl 3 : 6.5%, CO 2 : 1.6%, C 2 H 4 : 0.13%, and H 2 : reminder; a reaction atmosphere temperature: 820° C.; a reaction atmosphere pressure: 8 kPa; and a reaction time: 5-80 minutes (the relationship between the layer thickness of the Al 2 O 3 core thin film and a reaction time was assessed in advance by an experiment, similar to the case of the Ti compound layer).
  • the Al 2 O 3 core thin film was heat treated under conditions of changing the reaction atmosphere pressure to a hydrogen atmosphere at 8 kPa and raising the reaction atmosphere temperature to 1135° C.
  • cutting tools of Examples 1, 3-6 and 8-11, 14, 16-19 were produced by forming by vapor deposition the ⁇ -Al 2 O 3 layers of the target layer thicknesses shown in Table 4 for the upper layer of the hard coating layer under the conditions shown in the Table 3.
  • cutting tools of Examples 2, 7, 12, 13, 15 and 20 were produced by forming by vapor deposition the TiN layers of the target layer thicknesses shown in Table 4 for the uppermost surface layer of the hard coating layer under the conditions shown in the Table 3 on the resulting ⁇ -Al 2 O 3 layers.
  • comparative cutting tools 1 through 20 were respectively produced under the same conditions with the exception of not forming the Al 2 O 3 core thin film and not performing heat treatment prior to forming the ⁇ -Al 2 O 3 layer of the hard coating layer as shown in Table 5.
  • Pole plot graphs were respectively produced using a field emission scanning electron microscope for the ⁇ -Al 2 O 3 layers that compose the hard coating layer with the resulting coated Cermet cutting tools of Examples 1-20 and coated Cermet cutting tools of Comparative Examples 1-20.
  • the surface of the ⁇ -Al 2 O 3 layer was placed inside the barrel of a field emission scanning electron microscope as the polishing plane.
  • an electron beam having an acceleration voltage of 15 kV was emitted onto individual crystal grains having a hexagonal crystal lattice present within the measuring range of the surface polishing plane at an emission current of 1 nA and incident angle of 70 degrees relative to the polishing plane.
  • Inclination of the (0001) plane which is the crystal plane of the crystal grains, was measured relative to the normal of the surface polishing plane in intervals of 0.1 ⁇ m/step for a region measuring 30 ⁇ 50 ⁇ m using an electron backscattering diffraction imaging device.
  • the measured inclination within the range of 0-45 degrees indicated by each crystal grain was divided for each pitch of 0.25 degrees based on the measurement results, and the measured inclinations present in each section were tabulated for each section to prepare pole plot graphs.
  • the thickness of each layer of the hard coating layers of the resulting coated Cermet cutting tools of Examples 1-20 and Comparative Examples 1-20 was measured using a scanning electron microscope (measurement of longitudinal cross-section). As a result, all of the mean layer thicknesses (average of five measuring points) were confirmed to be substantially the same as the target layer thickness. Furthermore, measurement of the layer thickness of the heat-treated Al 2 O 3 core thin film in the coated Cermet cutting tools of Examples 1-20 was extremely difficult.
  • coated Cermet cutting tools of Examples 1-7 and 14-17 and coated Cermet coating tools of Comparative Examples 1-7 and 14-17 were bolted onto the end of a tool steel cutting bit followed by performing the cutting tests described below.
  • Cut material Round bar composed of JIS-SCM440 in which four longitudinal grooves are formed at equal intervals in the direction of length
  • Cut material Round bar composed of JIS-S45C in which four longitudinal grooves are formed at equal intervals in the direction of length
  • Cut material Round bar composed of JIS-FC300 in which four longitudinal grooves are formed at equal intervals in the direction of length
  • coated Cermet cutting tools of Examples 8-13 and 18-20 and the coated Cermet cutting tools of Comparative Examples 8-13 and 18-20 were bolted to the end of the tool steel cutting bit followed by performing the cutting tests described below.
  • Cut material Round bar composed of JIS-SCM440 in which four longitudinal grooves are formed at equal intervals in the direction of length
  • Cut material Round bar composed of JIS-S45C in which four longitudinal grooves are formed at equal intervals in the direction of length
  • Cut material Round bar composed of JIS-FC300 in which four longitudinal grooves are formed at equal intervals in the direction of length
  • the (0001) plane of the ⁇ -Al 2 O 3 layer indicated the highest peak in the inclination section within the range of 0-10 degrees in the pole plot graphs. Consequently, these cutting tools demonstrated extremely high resistance to mechanical and thermal shock, and superior chipping resistance even during high-speed intermittent cutting of steel or cast iron accompanied by the generation of a large amount of heat.
  • the cutting tools significantly suppressed the occurrence of chipping of the cutting edge, and exhibited superior wear resistance.
  • the cutting tool of the present invention is naturally capable of continuous and intermittent cutting of various types of steel and cast iron under normal conditions, is extremely resistant to mechanical and thermal shock, exhibits superior chipping resistance even during the most severe high-speed intermittent cutting accompanied the generation of a large amount of heat, and demonstrates superior cutting performance over a long period of time.
  • the cutting tool of the present invention is capable of satisfactorily accommodating increased performance of cutting devices, labor and energy savings in cutting processing, as well as reductions in costs.

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Abstract

The present invention provides a cutting tool in which the hard coating layer demonstrates superior chipping resistance. The cutting tool has a tool base composed with tungsten carbide-based cemented carbide or titanium carbonitride-based Cermet, and a hard coating layer provided on the surface thereof; wherein the hard coating layer includes: (a) a Ti compound and/or Zr compound layer, which is a lower layer, comprising one or more layers of a TiC layer, TiN layer, TiCN layer, TiCO layer, TiCNO layer, ZrC layer, ZrN layer, ZrCN layer, ZrCO layer, ZrCNO layer and (b) an aluminum oxide layer having an α crystal structure which is an upper layer, including the highest peak in the inclination section within a range of 0-10.

Description

BACKGROUND OF THE INVENTION
1. Incorporation by Reference
The present application claims priority under 35 U.S.C. §119 to Japanese Patent Application Nos. 2003-053059 filed on Feb. 28, 2003 and 2003-056639 filed on Mar. 4, 2003. The contents of the applications are incorporated herein by reference in their entirety.
2. Field of the Invention
The present invention relates to a Cermet cutting tool having a coated surface (to be referred to as a coated Cermet cutting tool) used for high-speed, intermittent cutting of various types of steel, cast iron and so forth, and its hard coating layer in particular demonstrates superior chipping resistance.
3. Description of the Related Art
Known examples of coated Cermet cutting tools comprise a base (to be generically referred to as the tool base) made of tungsten carbide (WC)-based cemented carbide or titanium carbide (TiC)-based Cermet, and a hard coating layer. This hard coating layer comprises:
  • (a) a Ti compound and/or Zr compound layer, which is a lower layer, comprising one or more layers of a Ti carbide (TiC) layer, Ti nitride (TiN) layer, Ti carbonitride (TiCN) layer, Ti oxicarbide (TiCO) layer, Ti oxicarbonitride (TiCNO) layer, Zr carbide (ZrC) layer, Zr nitride (ZrN) layer, Zr carbonitride (ZrCN) layer, Zr oxicarbide (ZrCO) layer and Zr oxicarbonitride (ZrCNO) layer formed by chemical vapor deposition (to be simply referred to as vapor deposition formation), and having an overall mean layer thickness of 0.5-2.0 μm, and
  • (b) an aluminum oxide layer having an α crystal structure in the vapor deposited state (to be referred to as an α-Al2O3 layer), which is an upper layer, and having a mean layer thickness of 1-30 μm.
These coated Cermet cutting tools are widely known to be used for continuous and intermittent cutting of various types of steel, cast iron and so forth.
In addition, Japanese Unexamined Patent Application, First Publication No. Hei 6-31503 discloses that the Ti compound layer and the α-Al2O3 layer, which compose a hard coating layer, have a particulate crystal structure.
Moreover, Japanese Unexamined Patent Application, First Publication No. Hei 6-8010 discloses a technology for improving the strength of a TiCN layer comprising the Ti compound layer in which the TiCN layer is made to contain a longitudinally growing crystal structure by vapor deposition with an ordinary chemical vapor deposition device in an intermediate temperature range of 700-950° C. using a mixed gas containing organic carbonitride as the reactive gas.
Cutting devices have recently come to be required to offer higher performance, and there are also strong needs for saving of labor, saving of energy and reduced costs with respect to cutting processing. Accompanying these needs, the speed of cutting processing is tending to become even faster, resulting in the unavoidable circumstances of cutting processing under heavy-duty cutting conditions including greater cutting depth and faster feeding.
There are no problems with the use of the conventional coated Cermet cutting tools in the case of continuous or intermittent cutting of steel or cast iron and so forth under ordinary conditions. However, although the α-Al2O3 layer that composes the hard coating layer has superior heat resistance, since it is not provided with adequate strength, when used for high-speed intermittent cutting under severe cutting conditions, namely high-speed intermittent cutting in which thermal shock is repeatedly applied at an extremely short pitch to the cutting edge, chipping occurs easily in the hard coating layer. As a result, the cutting tool reaches the end of its service life in a comparatively short period of time.
SUMMARY OF THE INVENTION
Therefore, the inventors of the present invention conducted research to improve chipping resistance by focusing on a Cermet cutting tool comprising an α-Al2O3 layer as the hard coating layer. As a result, the following research results were obtained.
  • (1) When an α-Al2O3 layer, which comprises a hard coating layer, is formed on the surface of a cutting tool by vapor deposition, prior to this formation by vapor deposition, an Al2O3 core (the Al2O3 core is preferably an Al2O3 core thin film having a mean layer thickness of 20-200 nm, to be referred to as an Al2O3 core thin film) is formed on the surface of the Ti compound and/or Zr compound layer, which is a lower layer, using an ordinary chemical vapor deposition device under low-temperature conditions of a reactive gas composition, in % by volume, of AlCl3: 3-10%, CO2: 0.5-3%, C2H4: 0.01-0.3% and H2: remainder, reaction atmosphere temperature of 750-900° C., and reaction atmosphere pressure of 3-13 kPa.
Next, an α-Al2O3 layer is formed under ordinary conditions on the Al2O3 core thin film which is heat treated under conditions in which the reaction atmosphere is changed to a hydrogen atmosphere at a pressure of 3-13 kPa and the reaction atmosphere temperature is raised to 1100-1200° C. The α-Al2O3 layer obtained in this manner was confirmed to demonstrate a pole plot graph in which the highest peak of the inclination section appears within a narrow range.
Specifically, as shown in the sketch drawings in FIG. 1, the inclination of the normal of the (0001) plane of crystal grains relative to the normal of the surface polishing plane is measured by emitting an electron beam onto individual α-Al2O3 crystal grains having a hexagonal crystal lattice present within the measuring range of the surface polishing plane using a field emission scanning electron microscope. Next, the measured inclinations within the range of 0-45 degrees indicated by the individual crystal grains are divided for each pitch of 0.25 degrees, and a pole plot graph is prepared in which the measured inclination present in each section are tabulated for each section. In this case, as shown in FIG. 2, the pole plot graph is shown in which the highest peak of the inclination division appears within a narrow range of 0-10 degrees.
Furthermore, as shown in FIG. 3, a conventional α-Al2O3 layer was confirmed to have a pole plot graph in which a gradual highest pitch of the inclination section appears over a wide range of 25-35 degrees.
  • (2) An α-Al2O3 layer formed by vapor deposition on the heat-treated Al2O3 core thin film has significantly improved strength as compared with a conventional α-Al2O3 layer. Thus, a coated Cermet cutting tool in which a hard coating layer was formed by vapor deposition as the upper layer was confirmed to demonstrate superior chipping resistance as compared with a conventional Cermet cutting tool in which a conventional α-Al2O3 layer was formed by vapor deposition.
The present invention is based on these research results. In order to solve these problems, the present invention provides a cutting tool provided with a tool base composed with WC-based cemented carbide or TiCN-based Cermet, and a hard coating layer; wherein the hard coating layer comprises:
  • (a) a Ti compound and/or Zr compound layer, which is a lower layer, comprising one or more layers of a TiC layer, TiN layer, TiCN layer, TiCO layer, TiCNO layer, ZrC layer, ZrN layer, ZrCN layer, ZrCO layer and ZrCNO layer, which are formed by vapor deposition, and having an overall mean layer thickness of 0.5-20 μm, and
  • (b) an aluminum oxide layer having an α crystal structure in the state of being formed by vapor deposition (α-Al2O3 layer), which is an upper layer, comprising the highest peak in the inclination section within a range of 0-10 degrees in the case of emitting an electron beam onto individual crystal grains having a hexagonal crystal lattice present within the measuring range of the surface polishing plane, measuring the inclination of the normal of the (0001) crystal plane of the crystal grains relative to the normal of the surface polishing plane using a field emission scanning electron microscope, dividing the measured inclinations within a range of 0-45 degrees indicated by the individual crystal grains for each pitch of 0.25 degrees, and preparing a pole plot graph by tabulating the measured inclinations present in each section for each section, and having a mean layer thickness in a range of 1-30 μm.
In the cutting tool of the present invention, the α-Al2O3 layer, which composes the hard coating layer, exhibits a pole plot graph in which the highest peak appears in the inclination section within a range of 0-10 degrees as shown in FIG. 2, and demonstrates superior chipping resistance. Thus, the cutting tool of the present invention exhibits superior wear resistance and cutting performance over a long period of time even during high-speed intermittent cutting of various types of steel and cast iron that is accompanied by extremely high levels of mechanical and thermal shock as well as the generation of a large amount of heat.
In the cutting tool, it is preferable for the hard coating layer to have an aluminum oxide core thin layer containing an aluminum oxide core between the lower layer and the upper layer.
In the cutting tool, it is preferable for the mean layer thickness of the aluminum oxide core thin layer to be in a range of 20-200 nm.
In the cutting tool, it is preferable that the hard coating layer is obtained by forming the Ti compound and/or Zr compound layer; forming the aluminum oxide core thin layer on the surface of the Ti compound and/or Zr compound layer under conditions of a reaction gas composition, in % by volume, of AlCl3: 3-10%, CO2: 0.5-3%, C2H4: 0.01-0.3% and H2: remainder, a reaction atmosphere temperature of 750-900° C. and a reaction atmosphere pressure of 3-13 kPa; and heating the aluminum oxide core thin layer to 1100-1200° C. under conditions in which the reaction atmosphere is hydrogen and the reaction pressure is 3-13 kPa; and forming the aluminum oxide layer having an α crystal structure on the heated aluminum oxide core thin layer.
BRIEF DESCRIPTION OF THE DRAWINGS
FIGS. 1A and 1B are sketch drawings showing the measuring range of inclination of the normal of the (0001) plane of crystal grains in an α-Al2O3 layer which comprises a hard coating layer.
FIG. 2 is a pole plot graph of the (0001) plane of an α-Al2O3 layer which comprises a hard coating layer of the cutting tool of the present invention.
FIG. 3 is a pole plot graph of the (0001) plane of an α-Al2O3 layer which comprises a hard coating layer of a cutting tool of the prior art.
 DETAILED DESCRIPTION OF THE INVENTION
As was previously explained, the cutting tool of the present invention is provided with a tool base composed with WC-based cemented carbide or TiCN-based Cermet, and a hard coating layer. The hard coating layer further comprises a Ti compound and/or Zr compound layer, which is a lower layer, and an α-Al2O3 layer, which is an upper layer.
The reasons for limiting the mean layer thicknesses of the upper and lower layers of the hard coating layer in the manner previously described are as indicated below.
(a) Ti Compound and/or Zr Compound Layer
The Ti compound and/or Zr compound layer is basically present as the lower layer of the α-Al2O3 layer. Since it has superior strength, the hard coating layer comprising it also has superior strength. In addition, since it is securely adhered to both the tool base and the α-Al2O3 layer, it contributes to improved adhesion of the hard coating layer to the tool base. If the mean layer thickness is less than 0.5 μm, the actions are unable to be fully demonstrated. On the other hand, if the mean layer thickness exceeds 20 μm, the thermoplastic deformation occurs easily during high-speed intermittent cutting accompanying the generation of high levels of heat, in particular, thereby causing uneven wear. Consequently, the mean layer thickness of the Ti compound and/or Zr compound layer is defined to be 0.5-20 μm.
(b) α-Al2O3 Layer
The α-Al2O3 layer improves wear resistance of the hard coating layer because Al2O3 itself has high hardness and superior heat resistance. At the same time, since the α-Al2O3 layer of the present invention has superior strength as compared with conventional α-Al2O3 layers, it acts to further improve the chipping resistance of the hard coating layer. However, the effects are unable to be adequately demonstrated if its mean layer thickness is less than 1 μm. On the other hand, if it is thicker than 30 μm, chipping occurs easily. Consequently, the mean layer thickness of the α-Al2O3 layer is defined to be 1 30 μm.
(c) Heat-Treated Al2O3 Core Thin Film
There is a close relationship between the inclination section indicating the highest peak and the ratio of the heat-treated Al2O3 core thin film, in a pole plot graph of the α-Al2O3 layer. If the ratio of the heat-treated Al2O3 core thin film is too low, it becomes difficult to adjust the inclination section where the highest peak appears to within the range of 0-10 degrees, and it also becomes difficult to impart a satisfactory level of strength to the α-Al2O3 layer formed by vapor deposition thereon. Consequently, the effect of improving chipping resistance is unavoidably inadequate. Thus, it is preferable to provide an Al2O3 core thin film, and particularly a heat-treated Al2O3 core thin film. Its mean layer thickness is preferably 20 nm or more, and more preferably 30 nm or more. On the other hand, since it becomes difficult to make the inclination section where the highest peak appears to be within the range of 0-10 degrees if its ratio becomes excessively large. Therefore, its mean layer thickness is preferably 200 nm or less, and more preferably 150 nm or less.
Thus, the mean layer thickness of the Al2O3 core thin film formed on the Ti compound and/or Zr compound layer prior to formation by vapor deposition of the α-Al2O3 layer is preferably 20-200 nm, and more preferably 30-150 nm.
A TiN layer having a gold color tone may also be formed by vapor deposition as necessary as the uppermost surface layer of the hard coating layer for the purpose of discriminating before and after use of the coated Cermet cutting tool. In this case, the mean layer thickness of the TiN layer having a gold color tone is preferably 0.1-1 μm. If the mean layer thickness is less than 0.1 μm, adequate discrimination effects are unable to be obtained. In addition, a mean layer thickness of up to 1 μm is adequate for the TiN layer to demonstrate a discrimination effect.
EXAMPLES
The following provides a more detailed explanation of the cutting tool of the present invention by referring to Examples and Comparative Examples.
As raw material powders, WC powder, TiC powder, ZrC powder, VC powder, TaC powder, NbC powder, Cr3C2 powder, TiN powder, TaN powder and Co powder having a mean particle diameter of 1-3 μm were prepared. These raw material powders were blended to the blending compositions shown in Table 1, wax was added to them, and they were then mixed using a ball mill for 24 hours in acetone. After drying under reduced pressure, the dried mixtures were pressed formed into green compacts of a predetermined shape at a pressure of 98 MPa. Next, the green compacts were vacuum sintered for 1 hour in a vacuum at 5 Pa at a predetermined temperature within the range of 1370-1470° C. After sintering, the cutting edges were subjected to honing of R=0.07 mm to produce tool bases A through F made of WC-based cemented carbide having the indexable insert shape defined in ISO-CNMG 120408.
TABLE 1
Blending Composition (% by mass)
Type Co TiC ZrC VC TaC NbC Cr3C2 TiN TaN WC
Tool A 7 — — — — — — — — Rem.
Base B 5.7 — — — 1.5 0.5 — — — Rem.
C 5.7 — — — — — 1   — — Rem.
D 8.5 — 0.5 — — — 0.5 — — Rem.
E 12.5 2 — — — — — 1 2 Rem.
F 14 — — 0.2 — — 0.8 — — Rem.
In addition, as raw material powders, TiCN (mass ratio of TiC/TiN=50/50) powder, Mo2C powder, ZrC powder, NbC powder, TaC powder, WC powder, Co powder and Ni powder having a mean particle diameter of 0.5-2 μm were prepared. These powders were mixed to the blending compositions shown in Table 2, they were then wet-mixed for 24 hours with a ball mill. After drying, they were press formed into green compacts at a pressure of 98 MPa. Next, the green compacts were sintered for 1 hour at a nitrogen atmosphere at 1.3 kPa, at a temperature of 1540° C. After sintering, the cutting edges were subjected to honing of R=0.07 mm to produce tool bases a through f made of TiCN-based Cermet having the insert shape of ISO standard CNMG 120412.
TABLE 2
Blending Composition (% by mass)
Type Co Ni ZrC TaC NbC Mo2C WC TiCN
Tool a 13 5 — 10 — 10 16 Rem.
Base b 8 7 — 5 — 7.5 — Rem.
c 5 — — — — 6 10 Rem.
d 10 5 — 11 2 — — Rem.
e 9 4 1 8 — 10 10 Rem.
f 12 5.5 — 10 — 9.5 14.5 Rem.
The Ti compound and/or Zr compound layers having the target layer thicknesses shown in Table 4 were first formed by vapor deposition as the lower layer of the hard coating layer under the conditions shown in Table 3 (the 1-TiCN in Table 3 indicates the formation conditions of a TiCN layer having a longitudinally growing crystal structure described in Japanese Unexamined Patent Application, First Publication No. Hei 6-8010, while others indicate the formation conditions of an ordinary particulate crystal structure) using an ordinary chemical vapor deposition device on the surfaces of these tool bases A through F and a through f.
TABLE 3
Formation Conditions
Layers of Hard
Coating Layer Reaction Atmosphere
(numbers indicate Reaction Gas Composition Pressure Temperature
atomic ratios) (% by volume) (kPa) (° C.)
TiC TiCl4: 4.2%, CH4: 8.5%, 7 1020
H2: rem.
TiN (first layer) TiCl4: 4.2%, N2: 30%, 30 900
H2: rem.
TiN (other layer) TiCl4: 4.2%, N2: 35%, 50 1040
H2: rem.
1-TiC0.5N0.5 TiCl4: 4.2%, N2: 20%, 7 1000
CH3CN: 0.6%, H2: rem.
TiC0.5N0.5 TiCl4: 4.2%, N2: 20%, 12 1020
CH4: 4%, H2: rem.
TiC0.5O0.5 TiCl4: 4.2%, CO: 4%, 7 1020
H2: rem.
TiC0.3N0.3O0.4 TiCl4: 4.2%, CO: 3%, 20 1020
CH4: 3%, N2: 20%, H2: rem.
ZrC ZrCl4: 4.2%, CH4: 8.5%, 7 1040
H2: rem.
ZrN ZrCl4: 4.2%, N2: 30%, 30 960
H2: rem.
ZrC0.5N0.5 ZrCl4: 4.2%, N2: 20%, 7 960
CH3CN: 0.8%, H2: rem.
ZrC0.5O0.5 ZrCl4: 4.2%, CO: 4%, 7 1040
H2: rem.
ZrC0.3N0.3O0.4 ZrCl4: 4.2%, CO: 3%, 20 1040
CH4: 3%, N2: 20%, H2: rem.
α-Al2O3 AlCl3: 2.2%, CO2: 5.5%, 7 1000
HCl: 2.2%, H2S: 0.2%,
H2: rem.
TABLE 4-1
Tool Hard Coating Layer (parentheses: target layer thickness: μm unless indicated in nm)
base 1st 2nd 3rd 4th 5th 6th 7th
Type symbol layer layer layer layer layer layer layer
Coated 1 A TiN 1-TiCN TiN TiCNO Al2O3 core thin film α-Al2O3 —
Cermet (1) (17.5) (1) (0.5) (50 nm) (3)
Cutting 2 B TiN 1-TiCN TiC TiCNO Al2O3 core thin film α-Al2O3 TiN
Tool of (1) (4) (4) (1) (80 nm) (8) (0.3)
Examples 3 C TiN 1-TiCN TiCNO Al2O3 core thin film α-Al2O3 — —
(1) (4.5) (0.5) (50 nm) (15)
4 D TiN 1-TiCN TiC TiCNO Al2O3 core thin film α-Al2O3 —
(0.5) (10) (2) (0.3) (100 nm) (3)
5 D TiC 1-TiCN TiCNO Al2O3 core thin film α-Al2O3 — —
(1) (4) (1) (20 nm) (15)
6 E TiC 1-TiCN TiCO Al2O3 core thin film α-Al2O3 — —
(0.5) 9 (0.5) (50 nm) (8)
7 F TiN TiC 1-TiCN Al2O3 core thin film α-Al2O3 TiN —
(1) (1) (8) (150 nm) (5) (0.1)
8 a TiCN 1-TiCN TiCO Al2O3 core thin film α-Al2O3 — —
(1) (8.5) (0.5) (200 nm) (10)
9 b TiC 1-TiCN Al2O3 core thin film α-Al2O3 TiN — —
(1) (9) (100 nm) (5) (1)
10 c TiN 1-TiCN TiC TiCNO Al2O3 core thin film α-Al2O3 —
(0.5) (1.5) (0.5) (0.5) (80 nm) (20)
11 d TiN TiCN Al2O3 core thin film α-Al2O3 — — —
(1) (19) (100 nm) (1)
12 e TiN TiC TiCN TiCO Al2O3 core thin film α-Al2O3 TiN
(1) (1) (7) (1) (30 nm) (10) (0.1)
13 f TiCN TiC TiCNO Al2O3 core thin film α-Al2O3 TiN —
(0.5) (2) (0.5) (80 nm) (30) (0.3)
TABLE 4-2
Tool Hard Coating Layer (parentheses: target layer thickness: μm unless indicated in nm)
base 1st 2nd 3rd 4th 5th 6th 7th
Type symbol layer layer layer layer layer layer layer
Coated 14 A ZrN ZrCN ZrN ZrCO Al2O3 core thin film α-Al2O3 —
Cermet (1) (7.5) (1) (0.5) (50 nm) (6)
Cutting 15 B ZrN ZrCN ZrC ZrCNO Al2O3 core thin film α-Al2O3 TiN
Tool of (1) (4) (4) (1) (80 nm) (8) (0.3)
Examples 16 C ZrN ZrCN ZrCNO Al2O3 core thin film α-Al2O3 — —
(1) (16.5) (0.5) (200 nm) (3)
17 D TiN 1-TiCN ZrC ZrCNO Al2O3 core thin film α-Al2O3 —
(0.5) (6) (2) (0.3) (100 nm) (12)
18 d ZrC ZrCN TiCNO Al2O3 core thin film α-Al2O3 — —
(1) (2) (0.5) (20 nm) (20)
19 e ZrC ZrCN ZrCO Al2O3 core thin film α-Al2O3 — —
(0.5) (9) (0.5) (50 nm) (10)
20 f ZrN ZrCO ZrCN Al2O3 core thin film α-Al2O3 TiN —
(1) (1) (8) (150 nm) (15) (0.1)
Next, Al2O3 core thin films of the target layer thicknesses shown in Table 4 were formed under low-temperature conditions in which a reaction gas composition comprising, in % by volume, AlCl3: 6.5%, CO2: 1.6%, C2H4: 0.13%, and H2: reminder; a reaction atmosphere temperature: 820° C.; a reaction atmosphere pressure: 8 kPa; and a reaction time: 5-80 minutes (the relationship between the layer thickness of the Al2O3 core thin film and a reaction time was assessed in advance by an experiment, similar to the case of the Ti compound layer). Next, the Al2O3 core thin film was heat treated under conditions of changing the reaction atmosphere pressure to a hydrogen atmosphere at 8 kPa and raising the reaction atmosphere temperature to 1135° C. Subsequently, cutting tools of Examples 1, 3-6 and 8-11, 14, 16-19 were produced by forming by vapor deposition the α-Al2O3 layers of the target layer thicknesses shown in Table 4 for the upper layer of the hard coating layer under the conditions shown in the Table 3.
Moreover, cutting tools of Examples 2, 7, 12, 13, 15 and 20 were produced by forming by vapor deposition the TiN layers of the target layer thicknesses shown in Table 4 for the uppermost surface layer of the hard coating layer under the conditions shown in the Table 3 on the resulting α-Al2O3 layers.
In addition, for the sake of comparison, comparative cutting tools 1 through 20 were respectively produced under the same conditions with the exception of not forming the Al2O3 core thin film and not performing heat treatment prior to forming the α-Al2O3 layer of the hard coating layer as shown in Table 5.
TABLE 5
Hard Coating Layer (parentheses: target
Tool layer thickness: μm)
Base 1st 2nd 3rd 4th 5th 6th
Symbol layer layer layer layer layer layer
Coated 1 A TiN 1-TiCN TiN TiCNO α-Al2O3 —
Cermet (1) (17.5) (1) (0.5) (3)
Cutting 2 B TiN 1-TiCN TiC TiCNO α-Al2O3 TiN
Tools of (1) (4) (4) (1) (8) (0.3)
Compara- 3 C TiN 1-TiCN TiCNO α-Al2O3 — —
tive (1) (4.5) (0.5) (15)
Examples 4 D TiN 1-TiCN TiC TiCNO α-Al2O3 —
(0.5) (10) (2) (0.3) (3)
5 D TiC 1-TiCN TiCNO α-Al2O3 — —
(1) (4) (1) (15)
6 E TiC 1-TiCN TiCO α-Al2O3 — —
(0.5) 9 (0.5) (8)
7 F TiN TiC 1-TiCN α-Al2O3 TiN —
(1) (1) (8) (5) (0.1)
8 a TiCN 1-TiCN TiCO α-Al2O3 — —
(1) (8.5) (0.5) (10)
9 b TiC 1-TiCN α-Al2O3 TiN — —
(1) (9) (5) (1)
10 c TiN 1-TiCN TiC TiCNO α-Al2O3 —
(0.5) (1.5) (0.5) (0.5) (20)
11 d TiN TiCN α-Al2O3 — — —
(1) (19) (1)
12 e TiN TiC TiCN TiCO α-Al2O3 TiN
(1) (1) (7) (1) (10) (0.1)
13 f TiCN TiC TiCNO α-Al2O3 TiN —
(0.5) (2) (0.5) (10) (0.3)
14 A ZrN ZrCN ZrN ZrCO α-Al2O3 —
(1) (7.5) (1) (0.5) (6)
15 B ZrN ZrCN ZrC ZrCNO α-Al2O3 TiN
(1) (4) (4) (1) (8) (0.3)
16 C ZrN ZrCN ZrCNO α-Al2O3 — —
(1) (16.5) (0.5) (3)
17 D TiN 1-TiCN ZrC ZrCNO α-Al2O3 —
(0.5) (6) (2) (0.3) (12)
18 d ZrC ZrCN TiCNO α-Al2O3 — —
(0.5) (2) (0.5) (20)
19 e ZrC ZrCN ZrCO α-Al2O3 — —
(0.5) (9) (0.5) (10)
20 f ZrN ZrCO ZrCN α-Al2O3 TiN —
(1) (1) (8) (15) (0.1)

Production of Pole Plot Graphs
Pole plot graphs were respectively produced using a field emission scanning electron microscope for the α-Al2O3 layers that compose the hard coating layer with the resulting coated Cermet cutting tools of Examples 1-20 and coated Cermet cutting tools of Comparative Examples 1-20.
Namely, the surface of the α-Al2O3 layer was placed inside the barrel of a field emission scanning electron microscope as the polishing plane. Next, an electron beam having an acceleration voltage of 15 kV was emitted onto individual crystal grains having a hexagonal crystal lattice present within the measuring range of the surface polishing plane at an emission current of 1 nA and incident angle of 70 degrees relative to the polishing plane. Inclination of the (0001) plane, which is the crystal plane of the crystal grains, was measured relative to the normal of the surface polishing plane in intervals of 0.1 μm/step for a region measuring 30×50 μm using an electron backscattering diffraction imaging device. The measured inclination within the range of 0-45 degrees indicated by each crystal grain was divided for each pitch of 0.25 degrees based on the measurement results, and the measured inclinations present in each section were tabulated for each section to prepare pole plot graphs.
The inclination sections in which the (0001) plane exhibits the highest peak are respectively shown in Tables 6-1 and 6-2 in the resulting pole plot graphs of the α-Al2O3 layer.
TABLE 6-1
Inclination section in which Amount of flank
(0001) plane of α-Al2O3 layer wear (mm)
indicates highest peak Alloy Carbon Cast
(degrees) steel steel iron
Coated 1 3.25-3.50 0.31 0.30 0.33
Cermet 2 1.00-1.25 0.23 0.24 0.25
Cutting 3 1.50-1.75 0.26 0.25 0.24
Tool of 4 2.75-3.00 0.32 0.31 0.34
Examples 5 8.00-8.25 0.38 0.36 0.35
6 2.00-2.25 0.28 0.28 0.29
7 5.25-5.50 0.33 0.34 0.37
8  9.75-10.00 0.37 0.36 0.36
9 2.25-2.50 0.29 0.29 0.31
10 0.50-0.75 0.23 0.21 0.21
11 3.50-3.75 0.38 0.39 0.45
12 4.25-4.50 0.34 0.33 0.33
13 0.00-0.25 0.25 0.20 0.19
14 3.00-3.25 0.30 0.32 0.31
15 1.50-1.75 0.24 0.25 0.26
16 1.00-1.25 0.26 0.24 0.26
17 2.75-3.00 0.32 0.30 0.33
18 8.50-8.75 0.39 0.38 0.36
19 1.50-1.75 0.25 0.26 0.27
20 5.00-5.25 0.34 0.32 0.35
TABLE 6-2
Inclination section in Cutting test results
which (0001) plane of (time to reach service life)
α-Al2O3 layer indicates Alloy Carbon Cast
highest peak (degrees) steel steel iron
Coated 1 25.75-26.00 2.8 min. 2.7 min. 2.9 min.
Cermet 2 29.50-29.75 1.7 min. 1.5 min. 1.0 min.
Cutting 3 33.50-33.75 0.5 min. 0.3 min. 0.3 min.
Tools of 4 26.50-26.75 2.7 min. 2.9 min. 3.0 min.
Comparative 5 32.25-32.50 0.5 min. 0.4 min. 0.5 min.
Examples 6 29.50-29.75 1.5 min. 1.8 min. 1.9 min.
7 27.50-27.75 2.0 min. 2.1 min. 1.6 min.
8 31.00-31.25 0.9 min. 0.7 min. 0.6 min.
9 26.25-26.50 2.2 min. 1.9 min. 1.9 min.
10 33.25-33.50 0.3 min. 0.3 min. 0.5 min.
11 25.00-25.25 3.1 min. 2.6 min. 1.5 min.
12 31.50-31.75 1.1 min. 0.8 min. 0.8 min.
13 34.75-35.00 0.2 min. 0.3 min. 0.5 min.
14 25.75-26.00 2.9 min. 2.8 min. 2.7 min.
15 29.00-29.25 1.8 min. 1.7 min. 1.2 min.
16 32.50-32.75 0.8 min. 0.5 min. 0.9 min.
17 28.50-28.75 2.5 min. 2.8 min. 3.0 min.
18 34.25-34.50 0.5 min. 0.3 min. 0.7 min.
19 29.25-29.50 1.7 min. 1.8 min. 2.0 min.
20 27.75-28.00 2.2 min. 1.9 min. 1.8 min.

Thickness of Each Layer of Hard Coating Layer
The thickness of each layer of the hard coating layers of the resulting coated Cermet cutting tools of Examples 1-20 and Comparative Examples 1-20 was measured using a scanning electron microscope (measurement of longitudinal cross-section). As a result, all of the mean layer thicknesses (average of five measuring points) were confirmed to be substantially the same as the target layer thickness. Furthermore, measurement of the layer thickness of the heat-treated Al2O3 core thin film in the coated Cermet cutting tools of Examples 1-20 was extremely difficult.
Next, coated Cermet cutting tools of Examples 1-7 and 14-17 and coated Cermet coating tools of Comparative Examples 1-7 and 14-17 were bolted onto the end of a tool steel cutting bit followed by performing the cutting tests described below.
Dry High-Speed Intermittent Cutting Test Using Alloy Steel
The amount of flank wear of the cutting edge, or when that was unable to be measured, the service life of the cutting edge, namely the amount of time until chipping occurred in the hard coating layer, was measured. The cut material and test conditions used are indicated below. The test results are shown in Table 6.
Cut material: Round bar composed of JIS-SCM440 in which four longitudinal grooves are formed at equal intervals in the direction of length
Cutting speed: 350 m/min (normal cutting speed: 250 m/min)
Cutting depth: 1 mm
Feed: 0.25 mm/rev.
Cutting time: 5 min.
Dry High-Speed Intermittent Cutting Test Using Carbon Steel
Similar to the Dry High-Speed Intermittent Cutting Test Using Alloy Steel, the amount of wear of the flank of the cutting edge or the service life of the cutting edge was measured. The cut material and test conditions used are indicated below. The results are shown in Table 6.
Cut material: Round bar composed of JIS-S45C in which four longitudinal grooves are formed at equal intervals in the direction of length
Cutting speed: 400 m/min (normal cutting speed: 300 m/min)
Cutting depth: 1 mm
Feed: 0.25 mm/rev.
Cutting time: 5 min.
Dry High-Speed Intermittent Cutting Test Using Cast Iron
Similar to these tests, the amount of wear of the flank of the cutting edge or the service life of the cutting edge was measured. The cut material and test conditions used are indicated below. The results are shown in Table 6.
Cut material: Round bar composed of JIS-FC300 in which four longitudinal grooves are formed at equal intervals in the direction of length
Cutting speed: 450 m/min (normal cutting speed: 300 m/min)
Cutting depth: 1.5 mm
Feed: 0.25 mm/rev.
Cutting time: 5 min.
Moreover, the coated Cermet cutting tools of Examples 8-13 and 18-20 and the coated Cermet cutting tools of Comparative Examples 8-13 and 18-20 were bolted to the end of the tool steel cutting bit followed by performing the cutting tests described below.
Dry High-Speed Intermittent Cutting Test Using Alloy Steel
Similar to these tests, the amount of wear of the flank of the cutting edge or the service life of the cutting edge was measured. The cut material and test conditions used are indicated below. The results are shown in Table 6.
Cut material: Round bar composed of JIS-SCM440 in which four longitudinal grooves are formed at equal intervals in the direction of length
Cutting speed: 400 m/min (normal cutting speed: 250 m/min)
Cutting depth: 0.7 mm
Feed: 0.15 mm/rev.
Cutting time: 5 min.
Dry High-Speed Intermittent Cutting Test Using Carbon Steel
Similar to these tests, the amount of wear of the flank of the cutting edge or the service life of the cutting edge was measured. The cut material and test conditions used are indicated below. The results are shown in Table 6.
Cut material: Round bar composed of JIS-S45C in which four longitudinal grooves are formed at equal intervals in the direction of length
Cutting speed: 400 m/min (normal cutting speed: 300 m/min)
Cutting depth: 0.7 mm
Feed: 0.15 mm/rev.
Cutting time: 5 min.
Dry High-Speed Intermittent Cutting Test Using Cast Iron
Similar to these tests, the amount of wear of the flank of the cutting edge or the service life of the cutting edge was measured. The cut material and test conditions used are indicated below. The results are shown in Table 6.
Cut material: Round bar composed of JIS-FC300 in which four longitudinal grooves are formed at equal intervals in the direction of length
Cutting speed: 450 m/min (normal cutting speed: 300 m/min)
Cutting depth: 0.7 mm
Feed: 0.15 mm/rev.
Cutting time: 5 min.
As shown in Tables 4 through 6, in the coated Cermet cutting tools of the Examples 1-20, the (0001) plane of the α-Al2O3 layer indicated the highest peak in the inclination section within the range of 0-10 degrees in the pole plot graphs. Consequently, these cutting tools demonstrated extremely high resistance to mechanical and thermal shock, and superior chipping resistance even during high-speed intermittent cutting of steel or cast iron accompanied by the generation of a large amount of heat. The cutting tools significantly suppressed the occurrence of chipping of the cutting edge, and exhibited superior wear resistance.
In contrast, in the case of the Cermet cutting tools of Comparative Examples 1 to 20, the (0001) plane of the α-Al2O3 layer, which is the upper layer of the hard coating layer, indicated the highest peak in the inclination section within the range of 25-35 degrees in the pole plot graphs. Consequently, these cutting tools were unable to withstand the severe mechanical and thermal shock during high-speed intermittent cutting, chipping occurred in the cutting edge, and the cutting tools reached the end of their service life in a comparatively short period of time.
As has been described above, the cutting tool of the present invention is naturally capable of continuous and intermittent cutting of various types of steel and cast iron under normal conditions, is extremely resistant to mechanical and thermal shock, exhibits superior chipping resistance even during the most severe high-speed intermittent cutting accompanied the generation of a large amount of heat, and demonstrates superior cutting performance over a long period of time. Thus, the cutting tool of the present invention is capable of satisfactorily accommodating increased performance of cutting devices, labor and energy savings in cutting processing, as well as reductions in costs.

Claims (3)

1. A cutting tool provided with a tool base composed with tungsten carbide-based cemented carbide or titanium carbonitride-based Cermet, and a hard coating layer provided on the surface of the tool base; wherein the hard coating layer comprises:
(a) at least one of a Ti compound and a Zr compound layer, which is a lower layer, comprising at least one layer of a Ti carbide layer, Ti nitride layer, Ti carbonitride layer, Ti oxicarbide layer, Ti oxicarbonitride layer, Zr carbide layer, Zr nitride layer, Zr carbonitride layer, Zr oxicarbide layer and Zr oxicarbonitride layer formed by chemical vapor deposition, and having an overall mean layer thickness of 0.5-20 μm, and
(b) an aluminum oxide layer having an α crystal structure in the state of being formed by chemical vapor deposition, which is an upper layer, comprising the highest peak in the inclination section within a range of 0-10 degrees in the case of emitting an electron beam onto individual crystal grains having a hexagonal crystal lattice present within the measuring range of the surface polishing plane, measuring the inclination of the normal of the (0001) crystal plane of the crystal grains relative to the normal of the surface polishing plane using a field emission scanning electron microscope, dividing the measured inclinations within a range of 0-45 degrees indicated by the individual crystal grains for each pitch of 0.25 degrees, and preparing a pole plot graph by tabulating the measured inclinations present in each section for each section, and having the mean layer thickness is 1-30 μm.
2. A cutting tool according to claim 1, wherein the hard coating layer has an aluminum oxide core thin layer containing an aluminum oxide core between the lower layer and the upper layer.
3. A cutting tool according to claim 2, wherein the mean layer thickness of the aluminum oxide core thin layer is 20-200 nm.
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US20040224159A1 (en) 2004-11-11
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ATE385266T1 (en) 2008-02-15
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DE602004011582T2 (en) 2008-05-21
US7201956B2 (en) 2007-04-10
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DE602004011582D1 (en) 2008-03-20
KR100993152B1 (en) 2010-11-09

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