WO2014156448A1 - 表面被覆窒化硼素焼結体工具 - Google Patents
表面被覆窒化硼素焼結体工具 Download PDFInfo
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- WO2014156448A1 WO2014156448A1 PCT/JP2014/054687 JP2014054687W WO2014156448A1 WO 2014156448 A1 WO2014156448 A1 WO 2014156448A1 JP 2014054687 W JP2014054687 W JP 2014054687W WO 2014156448 A1 WO2014156448 A1 WO 2014156448A1
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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
- C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
- C23C14/06—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the coating material
- C23C14/0641—Nitrides
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- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
- C04B41/009—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone characterised by the material treated
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- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
- C04B41/45—Coating or impregnating, e.g. injection in masonry, partial coating of green or fired ceramics, organic coating compositions for adhering together two concrete elements
- C04B41/52—Multiple coating or impregnating multiple coating or impregnating with the same composition or with compositions only differing in the concentration of the constituents, is classified as single coating or impregnation
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- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
- C04B41/80—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone of only ceramics
- C04B41/81—Coating or impregnation
- C04B41/89—Coating or impregnation for obtaining at least two superposed coatings having different compositions
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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
- C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
- C23C14/06—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the coating material
- C23C14/0664—Carbonitrides
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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
- 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
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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
- 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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- 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
- C23C28/40—Coatings including alternating layers following a pattern, a periodic or defined repetition
- C23C28/42—Coatings including alternating layers following a pattern, a periodic or defined repetition characterized by the composition of the alternating layers
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23C—MILLING
- B23C2226/00—Materials of tools or workpieces not comprising a metal
- B23C2226/12—Boron nitride
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23C—MILLING
- B23C2228/00—Properties of materials of tools or workpieces, materials of tools or workpieces applied in a specific manner
- B23C2228/10—Coating
Definitions
- the present invention relates to a surface-coated boron nitride sintered body tool in which at least the cutting edge portion includes a cubic boron nitride sintered body and a coating film formed on the surface of the cubic boron nitride sintered body.
- a tool in which the surface of a cubic boron nitride sintered body is coated with a coating film such as ceramics is used as a cutting tool for cutting hardened steel because it exhibits excellent wear resistance. Recently, high precision is required in such cutting, and it is required to improve the surface roughness of the surface of the work material.
- Patent Document 1 WO 2010/150335 pamphlet (Patent Document 1) and WO 2012/005275 pamphlet (Patent Document 2) specify the surface of a cubic boron nitride sintered body.
- Patent Document 2 A tool coated with a coating film composed of a lower layer composed of multiple layers of ceramic composition and an upper layer composed of a compound layer has been proposed.
- a base material for such a multilayer coated tool not only a cubic boron nitride sintered body but also a cemented carbide, for example, is used (Japanese Patent Laid-Open No. 2008-188689 (Patent Document 3)). And Japanese translations of PCT publication No. 2008-534297 (patent document 4)).
- the present invention has been made in view of such a situation, and the object of the present invention is to cut at least in the case of processing hardened steel, etc., particularly when processing hardened steel at a low speed.
- the blade portion is to improve the wear resistance of a tool including a base material made of a cubic boron nitride sintered body.
- the present inventor has examined in detail the state of tool wear that occurs when machining hardened steel.
- boundary wear occurs at the boundary of the front cutting edge, which is one end of the wear part, and this boundary wear has the greatest impact on the tool life. Turned out to be giving.
- Such boundary wear is considered to occur even when hardened steel is processed at a low speed.
- the chip thickness becomes infinitely small at the boundary of the front cutting edge, so tensile stress is generated, resulting in mechanical wear of the tool coating layer. It is possible.
- the surface-coated boron nitride sintered body tool of the present invention includes a cubic boron nitride sintered body and at least a coating layer formed on the surface of the cubic boron nitride sintered body.
- the cubic boron nitride sintered body contains not less than 30% by volume and not more than 80% by volume of cubic boron nitride, and nitrides, carbides, borons of Group 4 elements, Group 5 elements and Group 6 elements of the periodic table of elements. It further includes a binder phase containing at least one compound selected from the group consisting of compounds, oxides, and solid solutions thereof, an aluminum compound, and inevitable impurities.
- the coating layer includes an A layer and a B layer.
- the A layer is MLa za1 (M represents one or more of Group 4 element, Group 5 element and Group 6 element of the periodic table of elements, Al and Si, and La represents 1 of B, C, N and O) And za1 is 0.85 or more and 1.0 or less.
- the B layer is formed by alternately laminating one or more thin film layers having different compositions. The thickness of each thin film layer is greater than 30 nm and less than 200 nm.
- the B1 thin film layer which is one of the thin film layers, is composed of (Ti 1 -xb1-yb1 Si xb1 M1 yb1 ) (C 1 -zb1 N zb1 ) (M1 is a group 4 element in the periodic table of elements excluding Ti, Represents one or more of group elements, group 6 elements and Al, xb1 is 0.01 or more and 0.25 or less, yb1 is 0 or more and 0.7 or less, and zb1 is 0.4 or more and 1 or less. ).
- the B2 thin film layer which is a kind of thin film layer and different from the B1 thin film layer, is formed by alternately laminating one or more compound layers having different compositions.
- the B2a compound layer which is one of the compound layers, is composed of (Ti 1 -xb2-yb2 Si xb2 M2 yb2 ) (C 1 -zb2 N zb2 ) (M2 is a group 4 element in the periodic table of elements other than Ti, Represents one or more of group elements, group 6 elements and Al, xb2 is 0.01 or more and 0.25 or less, yb2 is 0 or more and 0.7 or less, and zb2 is 0.4 or more and 1 or less. ).
- the B2b compound layer which is one of the compound layers and is different from the B2a compound layer, is (Al 1 -xb3 M3 xb3 ) (C 1 -zb3 N zb3 ) (M3 is a group 4 element in the periodic table of elements, the fifth Group element, Group 6 element, and one or more of Si, xb3 is 0.2 or more and 0.77 or less, and zb3 is 0.4 or more and 1 or less.
- the thickness of the A layer is 0.2 ⁇ m or more and 10 ⁇ m or less.
- the thickness of B layer is 0.05 micrometer or more and 5 micrometers or less.
- the total thickness of the coating layer is 0.25 ⁇ m or more and 15 ⁇ m or less.
- wear processing of hardened steel, etc., particularly when hardened steel is processed at low speed, wear resistance of a tool including a base material in which at least the cutting edge portion is made of a cubic boron nitride sintered body can be improved.
- ⁇ Configuration of surface coated boron nitride sintered body tool> At least the cutting edge portion of the surface-coated boron nitride sintered body tool according to the present invention is described as a cubic boron nitride sintered body (hereinafter referred to as “cBN sintered body”. “CBN” is an abbreviation of “cubic Boron Nitride”. And a coating layer formed on the surface of the cBN sintered body.
- the surface-coated boron nitride sintered body tool having such a basic configuration can be used particularly effectively in the machining of sintered alloys and hard-to-cut cast iron (for example, cutting) or hardened steel. It can be suitably used in various types of processing of general metals other than the above.
- the cBN sintered body constitutes the base material of the tool among the cutting edge portions of the surface-coated boron nitride sintered body tool, and is 30% by volume to 80% by volume of cubic boron nitride (hereinafter referred to as “cBN”).
- a binder phase was selected from the group consisting of nitrides, carbides, borides, oxides, and solid solutions of Group 4 elements, Group 5 elements and Group 6 elements of the periodic table of elements. It contains at least one compound, an aluminum compound, and inevitable impurities, and binds cBN to each other.
- the cBN sintered body contains 30% by volume or more of cBN, it is possible to prevent a decrease in wear resistance of the base material of the surface-coated boron nitride sintered body tool. Moreover, since cBN can be disperse
- the content volume ratio of cBN is determined according to the following method. The cBN sintered body is mirror-polished, and a backscattered electron image of the cBN sintered body structure in an arbitrary region is photographed at 2000 times with an electron microscope.
- cBN particles particles made of cBN
- the binder phase is a gray region or a white region.
- the cBN sintered body region and the binder phase region are binarized by image processing to determine the occupied area of the cBN particles.
- the content volume ratio of cBN can be obtained.
- the cBN sintered body contains 50% by volume or more and 65% by volume or less of cBN. If the cBN sintered body contains 50% by volume or more of cBN, it is possible to provide a base material for a surface-coated boron nitride sintered body tool having an excellent balance between wear resistance and fracture resistance. Moreover, if the cBN sintered body contains 65% by volume or less of cBN, the bonding strength between the cBNs by the binder phase can be increased.
- the cBN particles protrude from the binder phase toward the coating layer.
- the adhesiveness of a cBN sintered compact and a coating layer can be improved.
- the step between the cBN particles and the binder phase is 0.05 ⁇ m or more and 1.0 ⁇ m or less. If this level difference is 0.05 ⁇ m or more, an anchor effect can be obtained. Moreover, if this level
- the step between the cBN particles and the binder phase is 0.1 ⁇ m or more and 0.5 ⁇ m or less. If this level difference is 0.1 ⁇ m or more, the anchor effect can be obtained effectively. Moreover, if this level
- the volume content of cBN in the cBN sintered body is higher from the interface between the cBN sintered body and the coating layer toward the inside of the cBN sintered body.
- the volume content rate of a binder phase is higher than the volume content rate of cBN in the interface of a cBN sintered compact and a coating layer, the adhesiveness of a cBN sintered compact and a coating layer can be improved.
- the volume content of cBN is higher than the volume content of the binder phase inside the cBN sintered body, the fracture resistance of the cBN sintered body can be improved.
- the volume content of cBN is 40% by volume on the interface side with the coating layer (region separated from 0 ⁇ m to 20 ⁇ m from the interface between the cBN sintered body and the coating layer toward the inside of the cBN sintered body).
- the volume is 60% by volume.
- the particle size of the cBN particles contained in the cBN sintered body increases from the interface between the cBN sintered body and the coating layer toward the inside of the cBN sintered body.
- the particle size of the cBN particles is small at the interface between the cBN sintered body and the coating layer, the adhesion between the cBN sintered body and the coating layer can be enhanced.
- the particle size of the cBN particles is large inside the cBN sintered body, the toughness can be increased.
- the particle size of cBN particles is 0.1 ⁇ m or more and 1 ⁇ m or less in a region away from 0 ⁇ m to 20 ⁇ m toward the inside of the cBN sintered body from the interface between the cBN sintered body and the coating layer. And 2 ⁇ m or more and 10 ⁇ m or less in a region exceeding 20 ⁇ m and 300 ⁇ m or less from the interface between the coating layer and the cBN sintered body.
- the particle size of cBN particles is determined according to the following method. The diameter of the circle circumscribing the cBN particles in the backscattered electron image of the cBN sintered body structure obtained when obtaining the volume fraction of cBN is measured, and the measured diameter is taken as the particle size of the cBN particles.
- the cBN sintered body should just be provided in the cutting-blade part of the surface covering boron nitride sintered compact tool.
- the base material of the surface-coated boron nitride sintered body tool includes a cutting edge portion made of a cBN sintered body and a base body made of a material different from the cBN sintered body (for example, a cemented carbide). Also good.
- the cutting blade portion made of the cBN sintered body is preferably bonded to the base body through a brazing material or the like, and the brazing material can be selected in consideration of the bonding strength or the melting point. it can.
- the cBN sintered body may constitute the entire base material of the surface-coated boron nitride sintered body tool.
- the coating layer includes an A layer and a B layer.
- the coating layer of the present invention may contain other layers in addition to the A layer and the B layer as long as it includes the A layer and the B layer. Examples of such other layers include, but are not limited to, the C layer provided between the A layer and the B layer as described later or the D layer which is the lowermost layer. .
- the thickness of the coating layer is 0.25 ⁇ m or more and 15 ⁇ m or less.
- the thickness of the coating layer is 0.25 ⁇ m or more, it is possible to prevent the wear resistance of the surface-coated boron nitride sintered body tool from being lowered due to the thin thickness of the coating layer.
- the thickness of the coating layer is 15 ⁇ m or less, the chipping resistance of the coating layer at the initial stage of cutting can be improved.
- the thickness of the coating layer is 0.7 ⁇ m or more and 4 ⁇ m or less.
- the total thickness of the coating layer and the thickness of each layer and the number of layers to be described later are all cut from the surface-coated boron nitride sintered body tool, and the cross-section thereof is SEM (scanning electron microscope) or TEM It is calculated
- the composition of each layer as described later constituting the coating layer was measured using an EDX analyzer (energy dispersive X-ray analyzer) attached to the SEM or TEM.
- the coating layer may be provided only on the cutting edge portion of the surface-coated boron nitride sintered body tool, but it may cover the entire surface of the substrate of the surface-coated boron nitride sintered body tool, or may be cut. It may not be provided in a part of the portion different from the blade portion. Further, in a portion different from the cutting edge portion, a part of the laminated structure of the coating layer may be partially different.
- the A layer is MLa za1 (M represents one or more of Group 4 element, Group 5 element and Group 6 element of the periodic table of elements, Al and Si, and La represents 1 of B, C, N and O) And za1 is 0.85 or more and 1.0 or less.
- M represents one or more of Group 4 element, Group 5 element and Group 6 element of the periodic table of elements, Al and Si, and La represents 1 of B, C, N and O
- za1 is 0.85 or more and 1.0 or less.
- a layer (Ti 1-xa Ma xa ) (C 1-za2 N za2) (Ma fourth group elements of the periodic table of elements other than Ti, group 5 element and a group 6 element, Al And xa is 0 or more and 0.7 or less, and za2 is 0 or more and 1 or less. If the A layer contains Ti, peeling, cracking, or chipping of the A layer during wear can be further prevented. More preferably, the composition xa of Ma is 0 or more and 0.3 or less. Thereby, peeling of A layer at the time of abrasion, a crack, chipping, etc. can be prevented further.
- xa (Ti 1-xa (1) -xa (2) Ma (1) xa (1) Ma (2) xa (2) ) (C 1-za2 N za2 )
- xa The sum of (1) and xa (2) is preferably 0 or more and 0.7 or less, and more preferably 0 or more and 0.3 or less. This is also true for the B layer, C layer, and D layer shown below.
- the composition of N changes in a stepped or inclined manner from the cBN sintered body side toward the surface side of the A layer.
- the composition of N is large on the cBN sintered body side of the A layer, the fracture resistance and peel resistance can be improved.
- the composition of N is small on the surface side of the A layer, peeling, cracking, chipping, etc. of the A layer during wear can be further prevented.
- the composition of N changes stepwise from the cBN sintered body side toward the surface side of the A layer means that the N composition is discontinuously from the cBN sintered body side toward the surface side of the A layer.
- the composition of N changes in an inclined manner from the cBN sintered body side to the surface side of the A layer
- the N composition continuously decreases from the cBN sintered body side to the surface side of the A layer or
- it is a configuration obtained by continuously changing the flow rate ratio between the N source gas and the C source gas.
- the A layer has a region having a higher C composition than the cBN sintered body side on the surface side of the A layer. This also improves the fracture resistance and peel resistance on the cBN sintered body side of the A layer, and further prevents the A layer from peeling, cracking, or chipping during wear on the surface side of the A layer. Can do.
- the cBN sintered body side of the A layer means a region separated from 0 ⁇ m to 0.1 ⁇ m from the surface of the A layer located closest to the cBN sintered body toward the inside of the A layer.
- the surface side of the A layer means the side opposite to the cBN sintered body side of the A layer, and 0 ⁇ m or more from the surface of the A layer located farthest from the cBN sintered body toward the inside of the A layer. It means a region separated by 0.1 ⁇ m or less.
- the thickness of the A layer is 0.2 ⁇ m or more and 10 ⁇ m or less.
- a surface-coated boron nitride sintered body tool excellent in crater wear resistance or flank wear resistance can be provided.
- the thickness of the A layer exceeds 10 ⁇ m, it may be difficult to further improve the crater wear resistance or flank wear resistance of the surface-coated boron nitride sintered body tool.
- the A layer is provided more on the surface side of the surface-coated boron nitride sintered body tool than the B layer.
- a layer can wear
- the B layer can prevent propagation of the generated crack to the base material side.
- the B layer is formed by alternately laminating one or more thin film layers having different compositions.
- the B layer a structure in which one or more B1 thin film layers and one or more B2 thin film layers are alternately laminated is described, but the B layer of the present invention includes the B1 thin film layer and the B2 thin film layer. As long as other layers are included in addition to the B1 thin film layer and the B2 thin film layer, there is no problem.
- the thickness of B layer is 0.05 micrometer or more and 5 micrometers or less.
- the average value of the Si composition in the entire B layer is 0.003 or more and 0.25 or less.
- the average value of the Si composition in the entire B layer is more preferably 0.005 or more and 0.2 or less, and further preferably 0.005 or more and 0.15 or less.
- the B1 thin film layer is composed of (Ti 1-xb1-yb1 Si xb1 M1 yb1 ) (C 1-zb1 N zb1 ) (M1 is a group 4 element, group 5 element and group 6 element in the periodic table of elements other than Ti) And xb1 is 0.01 or more and 0.25 or less, yb1 is 0 or more and 0.7 or less, and zb1 is 0.4 or more and 1 or less.
- M1 represents at least one of Cr, Nb and W.
- the composition yb1 of M1 is preferably 0 or more and 0.4 or less, and more preferably 0.05 or more and 0.15 or less.
- the thickness of the B1 thin film layer is greater than 30 nm and less than 200 nm.
- the B2 thin film layer is formed by alternately laminating one or more compound layers having different compositions.
- the B2 thin film layer a structure in which one or more B2a compound layers and one or more B2b compound layers are alternately laminated is described.
- the B2 thin film layer of the present invention includes the B2a compound layer and the B2b compound layer.
- other layers may be included.
- the thickness of the B2 thin film layer is greater than 30 nm and less than 200 nm.
- the B2a compound layer is composed of (Ti 1 -xb2-yb2 Si xb2 M2 yb2 ) (C 1 -zb2 N zb2 ) (M2 is a group 4 element, group 5 element and group 6 element in the periodic table of elements other than Ti) And xb2 is 0.01 or more and 0.25 or less, yb2 is 0 or more and 0.7 or less, and zb2 is 0.4 or more and 1 or less. M2 preferably represents at least one of Cr, Nb and W, and more preferably represents the same element as M1.
- the composition yb2 of M2 is preferably 0 or more and 0.4 or less, more preferably 0.05 or more and 0.15 or less. More preferably, it shows the same value as the composition yb1 of M1.
- the thickness of the B2a compound layer is 0.5 nm or more and less than 30 nm.
- the B2b compound layer is composed of (Al 1 -xb 3 M 3 xb 3 ) (C 1 -zb 3 N zb 3 ) (M 3 is a group 4 element, a group 5 element and a group 6 element in the periodic table of elements and one or more of Si Xb3 is 0.2 or more and 0.77 or less, and zb3 is 0.4 or more and 1 or less.
- M3 represents at least one of Ti and Cr.
- the composition xb3 of M3 is preferably 0.25 or more and 0.5 or less, more preferably 0.25 or more and 0.4 or less.
- the thickness of the B2b compound layer is 0.5 nm or more and less than 30 nm.
- the lowermost layer of the B layer may be a B1 thin film layer or a B2 thin film layer.
- the uppermost layer of the B layer may be a B1 thin film layer or a B2 thin film layer.
- the lowermost layer of the B2 thin film layer may be a B2a compound layer or a B2b compound layer.
- the uppermost layer of the B2 thin film layer may be a B2a compound layer or a B2b compound layer.
- t2 / t1 which is a ratio of the average thickness t1 of the B1 thin film layer and the average thickness t2 of the B2 thin film layer, satisfies 0.5 ⁇ t2 / t1 ⁇ 10.0.
- the boundary wear resistance of the surface-coated boron nitride sintered body tool (particularly the boundary wear resistance of the surface-coated boron nitride sintered body tool during low-speed cutting) can be further improved.
- t2 / t1 satisfies 1.5 ⁇ t2 / t1 ⁇ 5.0.
- the boundary wear resistance of the surface-coated boron nitride sintered body tool (particularly the boundary wear resistance of the surface-coated boron nitride sintered body tool at the time of low-speed cutting) can be further improved. Therefore, it is possible to provide a surface-coated boron nitride sintered body tool having excellent wear resistance against repeated impacts or vibrations. More preferably, t2 / t1 satisfies 2.0 ⁇ t2 / t1 ⁇ 4.5.
- t2 / t1 when the A layer is provided on the surface side of the B layer, t2 / t1 satisfies 1.5 ⁇ t2 / t1 ⁇ 5.0 on the cBN sintered body side, and on the A layer side. It becomes smaller as it goes, and the layer A side satisfies 1.2 ⁇ t2 / t1 ⁇ 2.
- production of a crack can be prevented in the A layer side of B layer, and it can prevent that a crack propagates to the cBN sintered compact side in the cBN sintered compact side of B layer.
- the A layer side of the B layer means the B1 thin film layer and the B2 thin film layer located closest to the A layer.
- the cBN sintered compact side of B layer means the B1 thin film layer and B2 thin film layer which are located nearest to a cBN sintered compact.
- the coating layer further includes a C layer provided between the A layer and the B layer, and the C layer is McLc zc (Mc is a group 4 element, a group 5 element, and an element of the periodic table of elements) It represents one or more of Group 6 elements, Al and Si, Lc represents one or more of B, C, N and O, and zc is 0 or more and 0.85 or less.
- McLc zc Mc is a group 4 element, a group 5 element, and an element of the periodic table of elements
- It represents one or more of Group 6 elements
- Al and Si Lc represents one or more of B, C, N and O
- zc is 0 or more and 0.85 or less.
- the thickness of the C layer is 0.005 ⁇ m or more and 0.5 ⁇ m or less. If the thickness of the C layer is 0.005 ⁇ m or more, the effects obtained by providing the C layer can be sufficiently obtained. If the thickness of C layer is 0.5 micrometer or less, it can prevent that the thickness of a coating layer becomes large too much by providing C layer. More preferably, the thickness of the C layer is 0.01 ⁇ m or more and 0.2 ⁇ m or less.
- the composition zc of Lc is greater than 0 and less than 0.7. If the composition zc of Lc is larger than 0, the heat resistance and chemical wear resistance of the C layer can be improved, and thus the propagation of cracks generated in the A layer to the substrate side is effectively stopped in the C layer. be able to. More preferably, the composition zc of Lc is 0.2 or more and 0.5 or less.
- the C layer includes at least one element constituting the A layer and the B layer. If the C layer contains at least one element constituting the A layer, the adhesion between the A layer and the C layer can be improved. If the C layer contains at least one element constituting the B layer, the adhesion between the B layer and the C layer can be improved. More preferably, the C layer includes at least one element constituting a portion located on the C layer side of each of the A layer and the B layer.
- the coating layer further includes a D layer provided between the base material and the B layer, and the D layer is MdLd zd (Md is a Group 4 element, a Group 5 element and a Group 5 element in the periodic table of elements) It represents one or more of group 6 elements, Al and Si, Ld represents one or more of B, C, N and O, and zd is 0.85 or more and 1.0 or less.
- MdLd zd MdLd zd
- Md is a Group 4 element, a Group 5 element and a Group 5 element in the periodic table of elements
- Ld represents one or more of B, C, N and O
- zd is 0.85 or more and 1.0 or less.
- Such D layer is excellent in adhesiveness with a cBN sintered body. Therefore, if the coating layer further includes a D layer, the adhesion between the cBN sintered body and the coating layer can be enhanced. More preferably, in MdLd zd constituting the D layer, Ld is
- the D layer represents (Al 1 -xd Md2 xd ) Ld zd (Md2 represents one or more of Group 4 element, Group 5 element and Group 6 element of the periodic table of elements and Si, and xd Is 0.25 or more and 0.45 or less). If D layer contains Al, the adhesiveness of a cBN sintered compact and a coating layer can be improved more. More preferably, in (Al 1-xd Md2 xd ) Ld zd constituting the D layer, Md2 is at least one of Ti, Cr and V.
- the thickness of the D layer is 0.05 ⁇ m or more and 1.0 ⁇ m or less. If the thickness of D layer is 0.05 micrometer or more, the effect acquired by providing D layer can fully be acquired. If the thickness of D layer is 1.0 micrometer or less, it can prevent that the thickness of a coating layer becomes large too much by providing D layer. More preferably, the thickness of the D layer is 0.1 ⁇ m or more and 0.5 ⁇ m or less.
- the method of manufacturing a surface-coated boron nitride sintered body tool according to the present invention includes, for example, a step of preparing a base material having a cBN sintered body at least at a cutting edge portion, and a coating layer on at least the surface of the cBN sintered body. Forming.
- the step of preparing the base material preferably includes a step of forming a cBN sintered body, and the step of forming the cBN sintered body includes sintering a mixture of cBN particles and a raw material powder of a binder phase under high temperature and high pressure. It is preferable to include the process to make. More preferably, the method for preparing the base material further includes the step of joining the cBN sintered body to the base body having a predetermined shape.
- the step of forming the coating layer preferably includes a step of forming the coating layer by an arc ion plating method (ion plating method in which a solid material is evaporated using vacuum arc discharge) or a sputtering method.
- a coating layer can be formed by using a metal evaporation source containing a metal species that constitutes the coating layer and a reaction gas such as CH 4 , N 2, or O 2 .
- a reaction gas such as CH 4 , N 2, or O 2 .
- conditions for forming the coating layer known conditions can be employed.
- a coating layer is formed by using a metal evaporation source including a metal species constituting the coating layer, a reactive gas such as CH 4 , N 2, or O 2 and a sputtering gas such as Ar, Kr, or Xe. Can be formed.
- a metal evaporation source including a metal species constituting the coating layer, a reactive gas such as CH 4 , N 2, or O 2 and a sputtering gas such as Ar, Kr, or Xe.
- a reactive gas such as CH 4 , N 2, or O 2
- a sputtering gas such as Ar, Kr, or Xe.
- FIG. 1 is a cross-sectional view showing an example of the configuration of a surface-coated boron nitride sintered body tool in an example.
- FIG. 2 is a cross-sectional view illustrating an example of a configuration of a main part of the surface-coated boron nitride sintered body tool in the embodiment.
- the resulting mixture was heat treated in a vacuum at 1000 ° C. for 30 minutes.
- the compound obtained by the heat treatment was uniformly pulverized by a ball mill pulverizing method using a cemented carbide ball media having a diameter of 6 mm. This obtained the raw material powder of the binder phase.
- a boron nitride ball medium having a diameter of 3 mm is prepared by blending cBN particles having an average particle diameter of 1.5 ⁇ m and a raw material powder of a binder phase so that the content of cBN in the cBN sintered body is 30% by volume.
- the obtained mixed powder was laminated on a cemented carbide support plate and then filled into Mo capsules. After that, using an ultrahigh pressure apparatus, sintering was performed at a pressure of 5.5 GPa and a temperature of 1300 ° C. for 30 minutes. Thereby, cBN sintered compact A was obtained.
- a base body made of a cemented carbide material (equivalent to K10) having an ISO standard DNGA150408 shape was prepared.
- the above-mentioned cBN sintered body A shape: apex angle is 55 ° and both sides sandwiching the apex angle are 2 mm each on the bottom surface of the prepared base body (corner portion) is the bottom surface, and the thickness is 2 mm. Of a triangular prism).
- a mouthpiece made of Ti—Zr—Cu was used for joining.
- the outer peripheral surface, upper surface, and lower surface of the joined body were ground to form a negative land shape (a negative land width of 150 ⁇ m and a negative land angle of 25 °) at the cutting edge. In this way, a base material 3 having a cutting edge portion made of the cBN sintered body A was obtained.
- the obtained base material 3 was put in a film forming apparatus and evacuated. After that, after heating to 500 ° C., Ar gas was introduced (pressure 1 Pa), a bias voltage ( ⁇ 500 V) was applied to the substrate 3, and etching was performed with Ar ions. After that, Ar gas was exhausted from the film forming apparatus.
- the D layer 20 was formed on the substrate 3 in the film forming apparatus. Specifically, a D layer having a thickness of 0.5 ⁇ m was formed by vapor deposition under the following conditions.
- Target Introduced gas containing 66 atomic% Al and 34 atomic% Cr: N 2 Deposition pressure: 5Pa Arc discharge current: 150A Substrate bias voltage: -35V Table rotation speed: 3 rpm.
- the B layer 30 was formed on the D layer 20 in the film forming apparatus. Specifically, first, a B1 thin film layer 31 having an overall thickness of 35 nm was formed by vapor deposition under the following conditions.
- Target B1 Introduced gas containing 90 atomic% Ti and 10 atomic% Si: N 2 Deposition pressure: 3Pa Arc discharge current: 150A Substrate bias voltage: -40V Table rotation speed: 4 rpm.
- a B2 thin film layer 32 having an overall thickness of 165 nm was formed by vapor deposition under the following conditions.
- the rotary table in which the arc currents of the targets B2a and B2b and the base material are set so that the thickness of the B2a compound layer 32A is 2.5 nm and the thickness of the B2b compound layer 32B is 3 nm.
- the rotation speed was adjusted.
- Target B2a Target containing 90 atomic% Ti and 10 atomic% Si
- Target B2b Introducing gas containing 66 atomic% Al and 34 atomic% Cr: N 2 Deposition pressure: 3Pa
- the B1 thin film layers 31 and the B2 thin film layers 32 were alternately laminated to form five layers each.
- the B layer 30 having an overall thickness of 1 ⁇ m was formed.
- the A layer 50 was formed on the C layer 40 in the film forming apparatus. Specifically, an A layer having a thickness of 0.1 ⁇ m was formed by vapor deposition under the following conditions.
- Target: Ti Introduced gas: N 2 , CH 4 (the flow rate is adjusted so that the film to be formed has an atomic ratio of C: N 1: 4)
- the coating layer 10 in which the D layer 20, the B layer 30, and the A layer 50 were sequentially laminated was formed on the base material 3, and thus the sample 1 was manufactured.
- Samples 2 to 7 were produced according to the production method of Sample 1 except that the thickness of the A layer was changed to the numerical value shown in Table 1.
- cBN sintered body A According to the method for forming cBN sintered body A, cBN sintering was performed except that the cBN particles and the binder phase raw material powder were blended so that the cBN content in the cBN sintered body was a numerical value shown in Table 3. Body D was obtained. Using the obtained cBN sintered body D, a base material of Sample 8 was formed according to the method of manufacturing a base material of Sample 1 described above.
- a D layer having a thickness of 0.02 ⁇ m was formed by vapor deposition under the following conditions.
- a B layer was formed according to the production method of Sample 1.
- the arc thickness of the targets B2a and B2b and the rotation speed of the rotary table on which the base material is set are adjusted so that the thicknesses of the B2a compound layer and the B2b compound layer are 1.5 nm, respectively,
- a B2 thin film layer having a thickness of 12 nm was formed by vapor deposition.
- the N 2 flow rate and the CH 4 flow rate are adjusted so that the composition of the film to be formed is TiC 0.4 N 0.6 under the conditions shown below, and an A layer having a thickness of 0.1 ⁇ m is deposited by vapor deposition. Formed. In this way, Sample 8 was manufactured.
- the target was prepared, and the type of the introduced gas and its supply amount were adjusted so that a layer having the composition shown in Tables 1 and 2 was obtained.
- Ar, N 2, CH 4 or the like was appropriately used as the introduced gas.
- the film forming pressure is adjusted as appropriate within the range of 0.1 Pa to 7 Pa
- the arc discharge current is adjusted as appropriate within the range of 60 A to 200 A
- the substrate bias voltage is adjusted as appropriate within the range of ⁇ 25 V to ⁇ 700 V.
- the table rotation speed was appropriately adjusted within the range of 0.5 to 10 rpm. The same applies to Samples 15 to 56 shown below.
- Samples 16 to 20 were manufactured according to the method for manufacturing Sample 15 except that the C layer was formed according to the method described below.
- Target Ti Introduced gas: Ar Deposition pressure: 2Pa Arc discharge current: 150A Substrate bias voltage: -70V Table rotation speed: 3 rpm.
- a cBN sintered body F was obtained according to the method of forming the cBN sintered body D except that cBN particles having an average particle diameter of 0.5 ⁇ m and a raw material powder of a binder phase were blended.
- the base materials of Samples 32-36 were formed according to the base material manufacturing method of Sample 1 described above.
- a D layer, a B layer, and an A layer were formed in order. This produced Samples 32-36.
- a cBN sintered body G was obtained according to the method for forming the cBN sintered body D except that cBN particles having an average particle diameter of 3 ⁇ m and a raw material powder for a binder phase were blended.
- the base materials of Samples 37 to 40 were formed in accordance with the above-described manufacturing method of the base material of Sample 1.
- the resulting mixture was heat treated in a vacuum at 1000 ° C. for 30 minutes.
- the compound obtained by the heat treatment was uniformly pulverized by a ball mill pulverizing method using a cemented carbide ball media having a diameter of 6 mm. This obtained the raw material powder of the binder phase.
- a cBN sintered body H was obtained.
- base materials of samples 41 to 45 were formed according to the base material manufacturing method of sample 1 described above.
- the resulting mixture was heat treated in a vacuum at 1000 ° C. for 30 minutes.
- the compound obtained by the heat treatment was uniformly pulverized by a ball mill pulverizing method using a cemented carbide ball media having a diameter of 6 mm. This obtained the raw material powder of the binder phase.
- cBN sintered body I was obtained according to the method of forming cBN sintered body D.
- a base material of Sample 54 was formed according to the base material manufacturing method of Sample 1 described above.
- Sample 55 was manufactured according to the manufacturing method of Sample 1 except that the B layer, the C layer, and the D layer were not formed.
- Sample 56 was manufactured according to the manufacturing method of Sample 1 except that the A layer and the C layer were not formed.
- TiCN * 01 to TiCN * 08 in Table 1 are as shown in Table 4.
- the number of layers * 21 is the sum of the number of B2a compound layers and the number of B2b compound layers
- the number of layers * 22 is the number of B1 thin film layers and the number of B2 thin film layers. And the sum.
- flank wear amount VB and surface roughness Rz Using the manufactured samples 1 to 56, cutting (cutting distance: 4 km) was performed according to the following cutting conditions. After that, the flank wear amount VB was measured using an optical microscope, and the surface roughness Rz of the work material surface was measured in accordance with JIS standards. The measurement result of the flank wear amount VB is shown in the column “VB (mm)” in Table 5, and the measurement result of the surface roughness Rz of the work surface is shown in the column “Rz ( ⁇ m)” in Table 5. The smaller the VB, the more excellent the flank wear resistance of the surface-coated boron nitride sintered body tool. The smaller the Rz, the better the surface-coated boron nitride sintered body tool has excellent flank wear resistance, crater wear resistance, and boundary wear resistance. In the present embodiment, it is assumed that Rz is 3 ⁇ m or less.
- a specific numerical value of the surface roughness Rz of the work material when the surface roughness Rz of the work material exceeds 3.2 ⁇ m, a cutting distance at that time, and a surface roughness Rz of the work material are 3 Using a specific numerical value of the surface roughness Rz of the work material just before exceeding 2 ⁇ m and the cutting distance at that time, the relationship between the cutting distance and the surface roughness Rz of the work material is approximated by a straight line, The cutting distance when the surface roughness Rz of the work material reached 3.2 ⁇ m was measured. The result is shown in the column of “Cutting distance (km)” in Table 5.
- the surface-coated boron nitride sintered body tool is more excellent in flank wear resistance, crater wear resistance, and boundary wear resistance. In the present embodiment, it is said that the cutting distance is 7 km or more, which is good.
- Samples 2 to 6, 9 to 13, 15 to 20, 22 to 25, 28 to 30, 33 to 35, 38, 39, 42 to 44, and 46 to 54 have small VB, Rz of 3 ⁇ m or less, and cutting The distance was 7 km or more. Therefore, these samples were found to be excellent in flank wear resistance, crater wear resistance, and boundary wear resistance during low-speed cutting.
- sample 11 and the sample 56 are considered.
- the composition of the B layer, the thickness of the B layer, the composition of the D layer, and the thickness of the D layer are very similar between the sample 11 and the sample 56, but the A layer is provided in the sample 11. In contrast, the sample 56 is not provided.
- Rz is 3 ⁇ m or less and the cutting distance is 9 km or more
- VB is more than twice that of sample 11
- Rz is greater than 3 ⁇ m and the cutting distance is less than 3 km. It was.
- the sample 55 will be considered.
- the A layer is provided, but the B layer is not provided.
- Rz was larger than 3 micrometers and the cutting distance was about 3 km.
- the surface-coated boron nitride sintered body tool that does not include either the A layer or the B layer is not excellent in flank wear resistance, crater wear resistance, and boundary wear resistance during low-speed cutting.
- the surface-coated boron nitride sintered body tool having both the A layer and the B layer is surprisingly excellent in all of flank wear resistance, crater wear resistance, and boundary wear resistance during low speed cutting. I understood. This was first discovered by the present inventors.
- Samples 1 to 7 have different thicknesses of the A layer. In Samples 1 and 7, Rz was larger than 3 ⁇ m and the cutting distance was about 3 km. On the other hand, in Samples 2 to 6, Rz was 3 ⁇ m or less, and the cutting distance was 7 km or more. From these facts, if the thickness of the layer A is 0.2 ⁇ m or more and 10 ⁇ m or less, the flank wear resistance, crater wear resistance, and boundary wear resistance of the surface-coated boron nitride sintered body tool at the time of low speed cutting will be improved. I found it to increase.
- the thickness of the A layer is preferably 0.5 ⁇ m or more and 5 ⁇ m or less, and more preferably 1 ⁇ m or more and 5 ⁇ m or less.
- Samples 8 to 14 since the thicknesses of the A layer and the entire B layer are different from each other, the thicknesses of the coating layers are different from each other. In samples 8 and 14, Rz was larger than 3 ⁇ m and the cutting distance was about 3 km. On the other hand, in Samples 9 to 13, Rz was 3 ⁇ m or less, and the cutting distance was 8 km or more. From these facts, if the thickness of the coating layer is 0.25 ⁇ m or more and 15 ⁇ m or less, the flank wear resistance, crater wear resistance, and boundary wear resistance of the surface-coated boron nitride sintered body tool at the time of low speed cutting will be improved. I found it to increase.
- the thickness of the coating layer is preferably 0.5 ⁇ m or more and 10 ⁇ m or less, and more preferably 0.5 ⁇ m or more and 5 ⁇ m or less.
- Samples 15 to 20> Although the thickness of the C layer was different from each other, Rz was 3 ⁇ m or less, and the cutting distance was 8 km or more. In Samples 16 to 19, Rz was 2.5 ⁇ m or less, and the cutting distance was 8.5 km or more. Accordingly, the thickness of the C layer is preferably 0.005 ⁇ m or more and 0.5 ⁇ m or less, more preferably 0.01 ⁇ m or more and 0.5 ⁇ m or less, and 0.01 ⁇ m or more and 0.2 ⁇ m or less. It turns out that it is even more preferable.
- Samples 21 to 26 the compositions of the B1 thin film layer and the B2a compound layer are different from each other.
- Rz was larger than 3 ⁇ m and the cutting distance was about 3 to 4 km.
- Rz was 2.7 ⁇ m or less, and the cutting distance was 7.5 km or more.
- the Si composition is preferably 0.05 or more and 0.25 or less, and more preferably 0.05 or more and 0.2 or less.
- Samples 27 to 31 the thicknesses of the B1 thin film layer and the B2 thin film layer are different from each other.
- Rz was larger than 3 ⁇ m and the cutting distance was about 3 to 3.5 km.
- Rz was 3 ⁇ m or less and the cutting distance was 7.5 km or more. From these facts, if the thickness of each of the B1 thin film layer and the B2 thin film layer is greater than 30 nm and less than 200 nm, the flank wear resistance and crater wear resistance of the surface-coated boron nitride sintered tool during low-speed cutting. And increased resistance to boundary wear.
- each of the B1 thin film layer and the B2 thin film layer is preferably 40 nm or more and 180 nm or less.
- Samples 32 to 36 the thicknesses of the B2a compound layers are different from each other.
- Rz was larger than 3 ⁇ m and the cutting distance was 3.5 km.
- Rz was 3 ⁇ m or less, and the cutting distance was 7.5 km or more. From these facts, if the thickness of the B2a compound layer is 0.5 nm or more and less than 30 nm, the flank wear resistance, crater wear resistance, and boundary wear resistance of the surface-coated boron nitride sintered body tool during low-speed cutting. was found to increase.
- the B2a compound layer is preferably 1 nm to 25 nm, more preferably 1 nm to 20 nm, and even more preferably 1 nm to 10 nm.
- Samples 37 to 40 the compositions of the B2b compound layers are different from each other.
- Rz was about 4 ⁇ m and the cutting distance was about 3 km.
- Rz was 2.6 ⁇ m or less, and the cutting distance was 8 km or more. Therefore, if the Al composition of the B2b compound layer is 0.23 or more and 0.8 or less, the flank wear resistance, crater wear resistance, and boundary resistance of the surface-coated boron nitride sintered body tool at the time of low-speed cutting. It was found that the wear resistance was increased.
- the Al composition of the B2b compound layer is preferably 0.5 or more and 0.75 or less, and more preferably 0.6 or more and 0.75 or less.
- Samples 41 to 45 the thicknesses of the B2b compound layers are different from each other.
- Rz was larger than 3.5 ⁇ m and the cutting distance was about 3 km.
- Rz was 2.5 ⁇ m or less, and the cutting distance was 8 km or more. From these facts, if the thickness of the B2b compound layer is 0.5 nm or more and less than 30 nm, the flank wear resistance, crater wear resistance, and boundary wear resistance of the surface-coated boron nitride sintered body tool during low-speed cutting. was found to increase.
- the thickness of the B2b compound layer is preferably 1 nm or more and 25 nm or less, more preferably 3 nm or more and 20 nm or less, and further preferably 5 nm or more and 20 nm or less.
- samples 46 to 54 the compositions of the cBN sintered bodies were different from each other, but Rz was 3 ⁇ m or less and the cutting distance was 7 km or more. In samples 48 to 54, Rz was 2.4 ⁇ m or less, and the cutting distance was about 9 km. Therefore, the volume content of cubic boron nitride in the cubic boron nitride sintered body is preferably 30% by volume to 85% by volume, and more preferably 50% by volume to 65% by volume. I found it preferable.
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Abstract
Description
本発明にかかる表面被覆窒化硼素焼結体工具の少なくとも切れ刃部分は、立方晶窒化硼素焼結体(以下では「cBN焼結体」と記す。「cBN」は「cubic Boron Nitride」の略語である。)と、cBN焼結体の表面上に形成された被覆層とを含む。このような基本的構成を有する表面被覆窒化硼素焼結体工具は、焼結合金や難削鋳鉄の機械加工(たとえば切削加工)または焼入鋼の加工において特に有効に用いることができる他、これら以外の一般的な金属の各種加工においても好適に用いることができる。
cBN焼結体は、表面被覆窒化硼素焼結体工具の切れ刃部分のうち当該工具の基材を構成するものであり、30体積%以上80体積%以下の立方晶窒化硼素(以下では「cBN」と記す)を含み、結合相をさらに含む。ここで、結合相は、元素の周期表の第4族元素、第5族元素および第6族元素の窒化物、炭化物、硼化物、酸化物ならびにこれらの固溶体からなる群の中から選択された少なくとも1種の化合物とアルミニウム化合物と不可避不純物とを含み、cBN同士を互いに結合する。cBN焼結体が30体積%以上のcBNを含んでいれば、表面被覆窒化硼素焼結体工具の基材の耐摩耗性の低下を防止できる。また、cBN焼結体が80体積%以下のcBNを含んでいれば、cBN焼結体においてcBNを分散させることができるので、結合相によるcBN同士の接合強度を確保することができる。本明細書では、cBNの含有体積率は次に示す方法にしたがって求められたものである。cBN焼結体を鏡面研磨し、任意の領域のcBN焼結体組織の反射電子像を電子顕微鏡にて2000倍で写真撮影する。このとき、cBNからなる粒子(以下では「cBN粒子」と記す。)は黒色領域となり、結合相は灰色領域または白色領域となる。撮影されたcBN焼結体組織の写真からcBN焼結体領域と結合相領域とを画像処理により2値化し、cBN粒子の占有面積を求める。求められたcBN粒子の占有面積を以下に示す式に代入すれば、cBNの含有体積率が求まる。
(cBNの含有体積率)=(cBN粒子の占有面積)÷(撮影されたcBN焼結体組織の面積)×100。
被覆層は、A層とB層とを含む。本発明の被覆層は、A層とB層とを含む限り、A層およびB層以外に他の層を含んでいても差し支えない。このような他の層としては、たとえば後述のようなA層とB層との間に設けられるC層または最下層であるD層などを挙げることができるが、これらのみに限られるものではない。
A層は、MLaza1(Mは元素の周期表の第4族元素、第5族元素および第6族元素、AlならびにSiの1種以上を表わし、LaはB、C、NおよびOの1種以上を表わし、za1は0.85以上1.0以下である)からなる。これにより、A層は、滑らかに摩耗する。別の言い方をすると、A層は、剥離、割れ、または、チッピングなどを伴うことなく摩耗する。よって、表面被覆窒化硼素焼結体工具の耐クレータ摩耗性または耐逃げ面摩耗性などを高めることができる。
B層は、組成の異なる2種以上の薄膜層が交互にそれぞれ1つ以上積層されてなる。以下では、B層として、B1薄膜層とB2薄膜層とが交互にそれぞれ1つ以上積層されて構成されたものを挙げるが、本発明のB層は、B1薄膜層とB2薄膜層とを含む限り、B1薄膜層およびB2薄膜層以外に他の層を含んでいても差し支えない。B層の厚さは、0.05μm以上5μm以下である。
(B層全体におけるSi組成の平均値)=[{(B層を構成する各層のSi組成)×(当該各層の厚さ)}の総和]÷(B層全体の厚さ)。
(B1薄膜層の平均厚さt1)=(B1薄膜層の厚さの合計)÷(B1薄膜層の層数)。
好ましくは、被覆層がA層とB層との間に設けられたC層をさらに含むことであり、C層がMcLczc(Mcは元素の周期表の第4族元素、第5族元素および第6族元素、AlならびにSiの1種以上を表わし、LcはB、C、NおよびOの1種以上を表わし、zcは0以上0.85以下である)からなることである。これにより、A層とB層との密着性を高めることができる。また、A層がB層よりも表面側に設けられている場合には、A層で発生したクラックの基材側への伝搬をC層で止めることができる。
好ましくは、被覆層が基材とB層との間に設けられたD層をさらに含むことであり、D層がMdLdzd(Mdは元素の周期表の第4族元素、第5族元素および第6族元素、AlならびにSiの1種以上を表わし、LdはB、C、NおよびOの1種以上を表わし、zdは0.85以上1.0以下である)からなることである。このようなD層はcBN焼結体との密着性に優れる。よって、被覆層がD層をさらに含むのであれば、cBN焼結体と被覆層との密着性を高めることができる。より好ましくは、D層を構成するMdLdzdでは、LdがNであることである。
本発明にかかる表面被覆窒化硼素焼結体工具の製造方法は、たとえば、cBN焼結体を少なくとも切れ刃部分に有する基材を準備する工程と、少なくともcBN焼結体の表面上に被覆層を形成する工程とを含む。基材を準備する工程は、cBN焼結体を形成する工程を含むことが好ましく、cBN焼結体を形成する工程は、cBN粒子と結合相の原料粉末との混合物を高温高圧下で焼結させる工程を含むことが好ましい。基材を準備する方法は、所定の形状を有する基材本体にcBN焼結体を接合させる工程をさらに含むことがより好ましい。
図1は、実施例における表面被覆窒化硼素焼結体工具の構成の一例を示す断面図である。図2は、実施例における表面被覆窒化硼素焼結体工具の要部の構成の一例を示す断面図である。
<cBN焼結体Aの形成>
まず、原子比でTi:N=1:0.6となるように、平均粒子径が1μmのTiN粉末と平均粒子径が3μmのTi粉末とを混合した。得られた混合物を真空中で1200℃で30分間、熱処理してから、粉砕した。これにより、TiN0.6からなる金属間化合物粉末を得た。
形状がISO規格のDNGA150408であり、超硬合金材料(K10相当)からなる基材本体を準備した。準備した基材本体の刃先(コーナ部分)に上記cBN焼結体A(形状:頂角が55°であり当該頂角を挟む両辺がそれぞれ2mmである二等辺三角形を底面とし、厚さが2mmの三角柱状のもの)を接合した。接合には、Ti-Zr-Cuからなる口ウ材を用いた。接合体の外周面、上面および下面を研削し、刃先にネガランド形状(ネガランド幅が150μmであり、ネガランド角が25°)を形成した。このようにして、切れ刃部分がcBN焼結体Aからなる基材3を得た。
<D層の形成>
上記成膜装置内でD層20を基材3上に形成した。具体的には、以下に示す条件で、厚さが0.5μmであるD層を蒸着により形成した。
ターゲット:Alを66原子%、Crを34原子%含む
導入ガス:N2
成膜圧力:5Pa
アーク放電電流:150A
基板バイアス電圧:-35V
テーブル回転速度:3rpm。
上記成膜装置内でB層30をD層20上に形成した。具体的には、まず、以下に示す条件で、全体の厚さが35nmであるB1薄膜層31を蒸着により形成した。
ターゲットB1:Tiを90原子%、Siを10原子%含む
導入ガス:N2
成膜圧力:3Pa
アーク放電電流:150A
基板バイアス電圧:-40V
テーブル回転速度:4rpm。
ターゲットB2a:Tiを90原子%、Siを10原子%含む
ターゲットB2b:Alを66原子%、Crを34原子%含む
導入ガス:N2
成膜圧力:3Pa
基板バイアス電圧:-50V。
上記成膜装置内でA層50をC層40上に形成した。具体的には、以下に示す条件で、厚さが0.1μmであるA層を蒸着により形成した。
ターゲット:Ti
導入ガス:N2、CH4(形成する膜が原子比でC:N=1:4となるように流量を調整)
成膜圧力:1Pa
アーク放電電流:160A
基板バイアス電圧:-400V
テーブル回転速度:3rpm。
A層の厚さを表1に示す数値となるように変更したことを除いては上記試料1の製造方法にしたがって、試料2~7を製造した。
cBN焼結体におけるcBN含有率が表3に示す数値となるようにcBN粒子と結合相の原料粉末とを配合したことを除いては上記cBN焼結体Aの形成方法にしたがって、cBN焼結体Dを得た。得られたcBN焼結体Dを用いて、上記試料1の基材の製造方法にしたがって、試料8の基材を形成した。
ターゲット:Alを60原子%、Crを40原子%含む
導入ガス:N2
成膜圧力:0.7Pa
アーク放電電流:130A
基板バイアス電圧:-35V
テーブル回転速度:3rpm。
ターゲット:Ti
導入ガス:N2、CH4
成膜圧力:2Pa
アーク放電電流:140A
基板バイアス電圧:-600V
テーブル回転速度:4rpm。
B2a化合物層およびB2b化合物層のそれぞれの層数を変更し、且つ、B1薄膜層およびB2薄膜層のそれぞれの層数を変更して、B層の全体の厚さを変更したこと、および、A層の厚さを表1に示す厚さとしたことを除いては上記試料8の製造方法にしたがって、試料9~10を製造した。
B2a化合物層およびB2b化合物層のそれぞれの層数を変更し、且つ、B1薄膜層およびB2薄膜層のそれぞれの層数を変更して、B層の全体の厚さを変更したこと、および、以下に示す条件でA層を形成したことを除いては上記試料8の製造方法にしたがって、試料11を製造した。具体的には、A層の形成開始時からA層の厚さが1μmとなるまでの間は、N2のみを導入して成膜圧力を2Paとした。そののち、CH4を徐々に増やしながらN2を徐々に減らして、A層をさらに0.6μm形成した。このとき、組成がTiC0.4N0.6となるまで、CH4を徐々に増やしながらN2を徐々に減らした。このようにして試料11を製造した。試料12~14も同様に製造した。
ターゲット:Ti
導入ガス:N2、CH4
アーク放電電流:140A
基板バイアス電圧:-600V
テーブル回転速度:4rpm。
cBN焼結体におけるcBN含有率が表3に示す数値となるようにcBN粒子と結合相の原料粉末とを配合したことを除いては上記cBN焼結体Aの形成方法にしたがって、cBN焼結体Bを得た。得られたcBN焼結体Bを用いて、上記試料1の基材の製造方法にしたがって、試料15~20の基材を形成した。
以下に示す方法にしたがってC層を形成したことを除いては上記試料15の製造方法にしたがって、試料16~20を製造した。
ターゲット:Ti
導入ガス:Ar
成膜圧力:2Pa
アーク放電電流:150A
基板バイアス電圧:-70V
テーブル回転速度:3rpm。
cBN焼結体におけるcBN含有率が表3に示す数値となるようにcBN粒子と結合相の原料粉末とを配合したことを除いては上記cBN焼結体Aの形成方法にしたがって、cBN焼結体Cを得た。得られたcBN焼結体Cを用いて、上記試料1の基材の製造方法にしたがって、試料21~26の基材を形成した。
cBN焼結体におけるcBN含有率が表3に示す数値となるようにcBN粒子と結合相の原料粉末とを配合したことを除いては上記cBN焼結体Aの形成方法にしたがって、cBN焼結体Eを得た。得られたcBN焼結体Eを用いて、上記試料1の基材の製造方法にしたがって、試料27の基材を形成した。
平均粒径が0.5μmのcBN粒子と結合相の原料粉末とを配合したことを除いては上記cBN焼結体Dの形成方法にしたがって、cBN焼結体Fを得た。得られたcBN焼結体Fを用いて、上記試料1の基材の製造方法にしたがって、試料32~36の基材を形成した。次に、上記試料1の製造方法にしたがって、D層、B層およびA層を順に形成した。これにより、試料32~36を製造した。
平均粒径が3μmのcBN粒子と結合相の原料粉末とを配合したことを除いては上記cBN焼結体Dの形成方法にしたがって、cBN焼結体Gを得た。得られたcBN焼結体Gを用いて、上記試料1の基材の製造方法にしたがって、試料37~40の基材を形成した。
まず、原子比でTi:C:N=1:0.3:0.3となるように、平均粒子径が1μmのTiCN粉末と平均粒子径が3μmのTi粉末とを混合した。得られた混合物を真空中で1200℃で30分間、熱処理してから、粉砕した。これにより、TiC0.3N0.3からなる金属間化合物粉末を得た。
表1に示すcBN焼結体を用いて、上記試料1の基材の製造方法にしたがって、試料46~53の基材を形成した。次に、上記試料1、11、16の製造方法にしたがって、D層、B層、C層およびA層を順に形成した。これにより、試料46~53を製造した。
まず、原子比でTi:C=1:0.6となるように、平均粒子径が1μmのTiC粉末と平均粒子径が3μmのTi粉末とを混合した。得られた混合物を真空中で1200℃で30分間、熱処理してから、粉砕した。これにより、TiC0.6からなる金属間化合物粉末を得た。
B層、C層およびD層を形成しなかったことを除いては上記試料1の製造方法にしたがって、試料55を製造した。
A層およびC層を形成しなかったことを除いては上記試料1の製造方法にしたがって、試料56を製造した。
製造された試料1~56を用いて、以下に示す切削条件にしたがって切削加工(切削距離:4km)を行った。そののち、光学顕微鏡を用いて逃げ面摩耗量VBを測定し、JIS規格にしたがって被削材表面の面粗度Rzを測定した。逃げ面摩耗量VBの測定結果を表5の「VB(mm)」の欄に示し、被削材表面の面粗度Rzの測定結果を表5の「Rz(μm)」の欄に示す。VBが小さいほど、表面被覆窒化硼素焼結体工具は耐逃げ面摩耗性に優れる。Rzが小さいほど、表面被覆窒化硼素焼結体工具は耐逃げ面摩耗性、耐クレータ摩耗性および耐境界摩耗性に優れる。本実施例では、Rzが3μm以下であれば良好であるとしている。
被削材:高硬度鋼(SCM415H/HRC60)
切削速度:100m/min(低速)
送り:f=0.1mm/rev
切り込み:ap=0.1mm
切削油:エマルジョン(日本フルードシステム製造の商品名「システムカット96」)を20倍希釈したもの(wet状態)。
製造された試料1~56を用いて、上記切削条件にしたがって切削加工を行った。具体的には、一定の切削間隔だけ切削加工を行った後に表面粗さ計を用いて被削材の面粗度Rzを測定するということを繰り返し行った。被削材の面粗度Rzが3.2μmを超えると、切削加工を停止し、そのときの切削距離{(一定の切削間隔)×(被削材の面粗度Rzが3.2μmを超えたときの切削回数n)}を求めた。また、被削材の面粗度Rzが3.2μmを超える直前の切削距離{(一定の切削間隔)×(n-1)}も求めた。そして、被削材の面粗度Rzが3.2μmを超えたときの被削材の面粗度Rzの具体的な数値およびそのときの切削距離と、被削材の面粗度Rzが3.2μmを超える直前の被削材の面粗度Rzの具体的な数値およびそのときの切削距離とを用い、切削距離と被削材の面粗度Rzとの関係を直線で近似して、被削材の面粗度Rzが3.2μmとなった時点の切削距離を測定した。その結果を表5の「切削距離(km)」の欄に示す。切削距離が長いほど、表面被覆窒化硼素焼結体工具は耐逃げ面摩耗性、耐クレータ摩耗性および耐境界摩耗性に優れる。本実施例では、切削距離が7km以上であれば良好であるとしている。
結果を表5に示す。
まず、試料11と試料56とについて考察する。B層の組成、B層の厚さ、D層の組成およびD層の厚さは、試料11と試料56とで互いに酷似しているが、A層は、試料11では設けられているのに対して試料56では設けられていない。そして、試料11では、Rzは3μm以下であり切削距離は9km以上であるのに対し、試料56では、VBは試料11の2倍超でありRzは3μmよりも大きく切削距離は3km未満であった。
試料1~7では、A層の厚さが互いに異なる。試料1、7では、Rzは3μmよりも大きく、切削距離は3km程度であった。一方、試料2~6では、Rzは3μm以下であり、切削距離は7km以上であった。これらのことから、A層の厚さが0.2μm以上10μm以下であれば、低速切削時、表面被覆窒化硼素焼結体工具の耐逃げ面摩耗性、耐クレータ摩耗性および耐境界摩耗性が高まることが分かった。
試料8~14では、A層の厚さおよびB層全体の厚さのそれぞれが互いに異なるので、被覆層の厚さが互いに異なる。試料8、14では、Rzは3μmよりも大きく、切削距離は3km程度であった。一方、試料9~13では、Rzは3μm以下であり、切削距離は8km以上であった。これらのことから、被覆層の厚さが0.25μm以上15μm以下であれば、低速切削時、表面被覆窒化硼素焼結体工具の耐逃げ面摩耗性、耐クレータ摩耗性および耐境界摩耗性が高まることが分かった。
試料15~20では、C層の厚さが互いに異なるが、Rzは3μm以下であり、切削距離は8km以上であった。また、試料16~19では、Rzは2.5μm以下であり、切削距離は8.5km以上であった。これらのことから、C層の厚さは、0.005μm以上0.5μm以下であることが好ましく、0.01μm以上0.5μm以下であることがより好ましく、0.01μm以上0.2μm以下であることがさらに好ましいということが分かった。
試料21~26では、B1薄膜層およびB2a化合物層のそれぞれの組成が互いに異なる。試料21、26では、Rzは3μmよりも大きく、切削距離は3~4km程度であった。一方、試料22~25では、Rzは2.7μm以下であり、切削距離は7.5km以上であった。これらのことから、B1薄膜層およびB2a化合物層のそれぞれでは、Si組成が0.01以上0.25以下であれば、低速切削時、表面被覆窒化硼素焼結体工具の耐逃げ面摩耗性、耐クレータ摩耗性および耐境界摩耗性が高まることが分かった。
試料27~31では、B1薄膜層およびB2薄膜層のそれぞれの厚さが互いに異なる。試料27、31では、Rzは3μmよりも大きく、切削距離は3~3.5km程度であった。一方、試料28~30では、Rzは3μm以下であり、切削距離は7.5km以上であった。これらのことから、B1薄膜層およびB2薄膜層のそれぞれの厚さが30nmよりも大きく200nm未満であれば、低速切削時、表面被覆窒化硼素焼結体工具の耐逃げ面摩耗性、耐クレータ摩耗性および耐境界摩耗性が高まることが分かった。
試料32~36では、B2a化合物層の厚さが互いに異なる。試料32、36では、Rzは3μmよりも大きく、切削距離は3.5kmであった。一方、試料33~35では、Rzは3μm以下であり、切削距離は7.5km以上であった。これらのことから、B2a化合物層の厚さが0.5nm以上30nm未満であれば、低速切削時、表面被覆窒化硼素焼結体工具の耐逃げ面摩耗性、耐クレータ摩耗性および耐境界摩耗性が高まることが分かった。
試料37~40では、B2b化合物層の組成が互いに異なる。試料37、40では、Rzは4μm程度であり、切削距離は3km程度であった。一方、試料38、39では、Rzは2.6μm以下であり、切削距離は8km以上であった。これらのことから、B2b化合物層のAl組成が0.23以上0.8以下であれば、低速切削時、表面被覆窒化硼素焼結体工具の耐逃げ面摩耗性、耐クレータ摩耗性および耐境界摩耗性が高まることが分かった。
試料41~45では、B2b化合物層の厚さが互いに異なる。試料41、45では、Rzは3.5μmよりも大きく、切削距離は3km程度であった。一方、試料42~44では、Rzは2.5μm以下であり、切削距離は8km以上であった。これらのことから、B2b化合物層の厚さが0.5nm以上30nm未満であれば、低速切削時、表面被覆窒化硼素焼結体工具の耐逃げ面摩耗性、耐クレータ摩耗性および耐境界摩耗性が高まることが分かった。
試料46~54では、cBN焼結体の組成が互いに異なるが、Rzは3μm以下であり、切削距離は7km以上であった。また、試料48~54では、Rzは2.4μm以下であり、切削距離は9km程度であった。これらのことから、立方晶窒化硼素焼結体における立方晶窒化硼素の体積含有率は、30体積%以上85体積%以下であることが好ましく、50体積%以上65体積%以下であることがより好ましいということが分かった。
Claims (21)
- 少なくとも切れ刃部分が立方晶窒化硼素焼結体と前記立方晶窒化硼素焼結体の表面上に形成された被覆層とを含む表面被覆窒化硼素焼結体工具であって、
前記立方晶窒化硼素焼結体は、立方晶窒化硼素を30体積%以上80体積%以下含み、元素の周期表の第4族元素、第5族元素および第6族元素の窒化物、炭化物、硼化物、酸化物ならびにこれらの固溶体からなる群の中から選択された少なくとも1種の化合物とアルミニウム化合物と不可避不純物とを含む結合相をさらに含み、
前記被覆層は、A層とB層とを含み、
前記A層は、MLaza1(Mは元素の周期表の第4族元素、第5族元素および第6族元素、AlならびにSiの1種以上を表わし、LaはB、C、NおよびOの1種以上を表わし、za1は0.85以上1.0以下である)からなり、
前記B層は、組成の異なる2種以上の薄膜層が交互にそれぞれ1つ以上積層されてなり、
前記薄膜層のそれぞれの厚さは、30nmよりも大きく200nm未満であり、
前記薄膜層の1種であるB1薄膜層は、(Ti1-xb1-yb1Sixb1M1yb1)(C1-zb1Nzb1)(M1はTiを除く元素の周期表の第4族元素、第5族元素および第6族元素ならびにAlの1種以上を表わし、xb1は0.01以上0.25以下であり、yb1は0以上0.7以下であり、zb1は0.4以上1以下である)からなり、
前記薄膜層の1種であって前記B1薄膜層とは異なるB2薄膜層は、組成の異なる2種以上の化合物層が交互にそれぞれ1つ以上積層されてなり、
前記化合物層のそれぞれの厚さは、0.5nm以上30nm未満であり、
前記化合物層の1種であるB2a化合物層は、(Ti1-xb2-yb2Sixb2M2yb2)(C1-zb2Nzb2)(M2はTiを除く元素の周期表の第4族元素、第5族元素および第6族元素ならびにAlの1種以上を表わし、xb2は0.01以上0.25以下であり、yb2は0以上0.7以下であり、zb2は0.4以上1以下である)からなり、
前記化合物層の1種であって前記B2a化合物層とは異なるB2b化合物層は、(Al1-xb3M3xb3)(C1-zb3Nzb3)(M3は元素の周期表の第4族元素、第5族元素および第6族元素ならびにSiの1種以上を表わし、xb3は0.2以上0.77以下であり、zb3は0.4以上1以下である)からなり、
前記A層の厚さは、0.2μm以上10μm以下であり、
前記B層の厚さは、0.05μm以上5μm以下であり、
前記被覆層全体の厚さは、0.25μm以上15μm以下である表面被覆窒化硼素焼結体工具。 - 前記A層は、(Ti1-xaMaxa)(C1-za2Nza2)(MaはTiを除く元素の周期表の第4族元素、第5族元素および第6族元素、AlならびにSiの1種以上を表わし、xaは0以上0.7以下であり、za2は0以上1以下である)からなる請求項1に記載の表面被覆窒化硼素焼結体工具。
- 前記A層では、Nの組成za2が、前記立方晶窒化硼素焼結体側から当該A層の表面側へ向かってステップ状または傾斜状に変化する請求項2に記載の表面被覆窒化硼素焼結体工具。
- 前記A層は、当該A層の表面側に、前記立方晶窒化硼素焼結体側よりもCの組成の高い領域を有する請求項2または3に記載の表面被覆窒化硼素焼結体工具。
- 前記M1は、Cr、NbおよびWの少なくとも1つを表わし、
前記M1の組成yb1は、0以上0.4以下であり、
前記M2は、Cr、NbおよびWの少なくとも1つを表わし、
前記M2の組成yb2は、0以上0.4以下である請求項1~4のいずれか1項に記載の表面被覆窒化硼素焼結体工具。 - 前記M2は前記M1と同一の元素を表わし、前記M2の組成yb2は前記M1の組成yb1と同一の値である請求項5に記載の表面被覆窒化硼素焼結体工具。
- 前記M3はTiおよびCrの少なくとも1つを表わし、前記M3の組成xb3は0.25以上0.5以下である請求項1~6のいずれか1項に記載の表面被覆窒化硼素焼結体工具。
- 前記B1薄膜層の平均厚さt1と前記B2薄膜層の平均厚さt2との比であるt2/t1が、0.5<t2/t1≦10.0を満たす請求項1~7のいずれか1項に記載の表面被覆窒化硼素焼結体工具。
- 前記t2/t1は、1.5<t2/t1≦5.0を満たす請求項8に記載の表面被覆窒化硼素焼結体工具。
- 前記B層は、前記A層よりも前記立方晶窒化硼素焼結体側に設けられており、
前記t2/t1は、前記立方晶窒化硼素焼結体側では1.5<t2/t1≦5.0を満たし、前記A層側に向かうにつれて小さくなり、前記A層側では1.2<t2/t1<2を満たす請求項8または9に記載の表面被覆窒化硼素焼結体工具。 - 前記B層全体におけるSi組成の平均値は、0.003以上0.25以下である請求項1~10のいずれか1項に記載の表面被覆窒化硼素焼結体工具。
- 前記B層全体におけるSi組成の平均値は、0.02以上0.2以下である請求項11に記載の表面被覆窒化硼素焼結体工具。
- 前記A層は、前記B層よりも前記表面被覆窒化硼素焼結体工具の表面側に設けられている請求項1~12のいずれか1項に記載の表面被覆窒化硼素焼結体工具。
- 前記被覆層は、前記A層と前記B層との間に設けられたC層をさらに含み、
前記C層は、McLczc(Mcは元素の周期表の第4族元素、第5族元素および第6族元素、AlならびにSiの1種以上を表わし、LcはB、C、NおよびOの1種以上を表わし、zcは0以上0.85以下である)からなり、
前記C層の厚さは、0.005μm以上0.5μm以下である請求項1~13のいずれか1項に記載の表面被覆窒化硼素焼結体工具。 - 前記Lcの組成zcは0よりも大きく0.7未満である請求項14に記載の表面被覆窒化硼素焼結体工具。
- 前記C層は、前記A層および前記B層を構成する元素の少なくとも1種以上を含む請求項14または15に記載の表面被覆窒化硼素焼結体工具。
- 前記被覆層は、前記立方晶窒化硼素焼結体と前記B層との間に設けられたD層をさらに含み、
前記D層は、MdLdzd(Mdは元素の周期表の第4族元素、第5族元素および第6族元素、AlならびにSiの1種以上を表わし、LdはB、C、NおよびOの1種以上を表わし、zdは0.85以上1.0以下である)からなる請求項1~16のいずれか1項に記載の表面被覆窒化硼素焼結体工具。 - 前記立方晶窒化硼素焼結体は、前記立方晶窒化硼素を50体積%以上65体積%以下含む請求項1~17のいずれか1項に記載の表面被覆窒化硼素焼結体工具。
- 前記立方晶窒化硼素焼結体と前記被覆層との界面では、
前記立方晶窒化硼素からなる粒子が前記結合相よりも前記被覆層側に突出しており、
前記立方晶窒化硼素からなる粒子と前記結合相との段差が0.05μm以上1.0μm以下である請求項1~18のいずれか1項に記載の表面被覆窒化硼素焼結体工具。 - 前記立方晶窒化硼素焼結体における前記立方晶窒化硼素の体積含有率は、前記立方晶窒化硼素焼結体と前記被覆層との界面から前記立方晶窒化硼素焼結体の内部に向かって高くなる請求項1~19のいずれか1項に記載の表面被覆窒化硼素焼結体工具。
- 前記立方晶窒化硼素焼結体に含まれる前記立方晶窒化硼素の粒径は、前記立方晶窒化硼素焼結体と前記被覆層との界面から前記立方晶窒化硼素焼結体の内部に向かって大きくなる請求項1~20のいずれか1項に記載の表面被覆窒化硼素焼結体工具。
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CN201480018897.9A CN105073311B9 (zh) | 2013-03-29 | 2014-02-26 | 表面被覆氮化硼烧结体工具 |
US14/780,201 US20160047031A1 (en) | 2013-03-29 | 2014-02-26 | Surface-coated boron nitride sintered body tool |
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KR20150133816A (ko) | 2015-11-30 |
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US20160047031A1 (en) | 2016-02-18 |
CN105073311B9 (zh) | 2017-06-20 |
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