WO2014084389A1 - 総形刃物および木材用総形工具 - Google Patents
総形刃物および木材用総形工具 Download PDFInfo
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- WO2014084389A1 WO2014084389A1 PCT/JP2013/082296 JP2013082296W WO2014084389A1 WO 2014084389 A1 WO2014084389 A1 WO 2014084389A1 JP 2013082296 W JP2013082296 W JP 2013082296W WO 2014084389 A1 WO2014084389 A1 WO 2014084389A1
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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
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
- C04B35/58—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides
- C04B35/58007—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on refractory metal nitrides
- C04B35/58014—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on refractory metal nitrides based on titanium nitrides, e.g. TiAlON
- C04B35/58021—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on refractory metal nitrides based on titanium nitrides, e.g. TiAlON based on titanium carbonitrides
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B27—WORKING OR PRESERVING WOOD OR SIMILAR MATERIAL; NAILING OR STAPLING MACHINES IN GENERAL
- B27G—ACCESSORY MACHINES OR APPARATUS FOR WORKING WOOD OR SIMILAR MATERIALS; TOOLS FOR WORKING WOOD OR SIMILAR MATERIALS; SAFETY DEVICES FOR WOOD WORKING MACHINES OR TOOLS
- B27G13/00—Cutter blocks; Other rotary cutting tools
- B27G13/12—Cutter blocks; Other rotary cutting tools for profile cutting
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23C—MILLING
- B23C5/00—Milling-cutters
- B23C5/02—Milling-cutters characterised by the shape of the cutter
- B23C5/12—Cutters specially designed for producing particular profiles
- B23C5/14—Cutters specially designed for producing particular profiles essentially comprising curves
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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
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
- C04B35/56—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbides or oxycarbides
- C04B35/5607—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbides or oxycarbides based on refractory metal carbides
- C04B35/5611—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbides or oxycarbides based on refractory metal carbides based on titanium carbides
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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
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
- C04B35/58—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides
- C04B35/58007—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on refractory metal nitrides
- C04B35/58014—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on refractory metal nitrides based on titanium nitrides, e.g. TiAlON
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
- C22C29/04—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbonitrides
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
- B22F2005/001—Cutting tools, earth boring or grinding tool other than table ware
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2207/00—Aspects of the compositions, gradients
- B22F2207/01—Composition gradients
- B22F2207/03—Composition gradients of the metallic binder phase in cermets
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2207/00—Aspects of the compositions, gradients
- B22F2207/11—Gradients other than composition gradients, e.g. size gradients
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2207/00—Aspects of the compositions, gradients
- B22F2207/11—Gradients other than composition gradients, e.g. size gradients
- B22F2207/13—Size gradients
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2302/00—Metal Compound, non-Metallic compound or non-metal composition of the powder or its coating
- B22F2302/10—Carbide
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2302/00—Metal Compound, non-Metallic compound or non-metal composition of the powder or its coating
- B22F2302/15—Carbonitride
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2303/00—Functional details of metal or compound in the powder or product
- B22F2303/40—Layer in a composite stack of layers, workpiece or article
Definitions
- the present invention relates to, for example, a total shape cutter used for cutting of wood and a total shape tool for wood formed by mounting it.
- Wood which is a workpiece, covers a wide range of miscellaneous raw wood and waste wood, and MDF material containing a large amount of adhesive (of fiberboard manufactured by dry process using plant fiber such as wood as a raw material, The density of 0.35-0.80 g / cm 3 )) and the processing of natural wood that contains a lot of water, the cutting edge part of the overall shape tool corrodes and causes chipping. Therefore, there is a need for a complete cutter that can be used over a long period of time.
- the present invention has been devised to meet the above requirements, and is a lightweight cutter with high fracture resistance, wear resistance, and corrosion resistance, and a plurality of these cutters in a rotary holder.
- An object of the present invention is to provide a total shape tool for wood that is mounted.
- the overall shape cutter of the present invention is an integral plate-like body having a cutting edge portion, and this plate-like body is composed of a cermet containing a hard phase and a binder phase.
- the total shape tool for wood according to the present invention is formed by mounting a plurality of the above-described total shape cutters on the rotary holder.
- the overall cutting tool of the present invention can withstand long-term use because it is lightweight and has high fracture resistance, wear resistance, and corrosion resistance.
- the number of rotations can be increased without requiring a large amount of power, so that the processing efficiency can be further increased.
- cutting can be performed at high speed rotation, swaying of the machined surface is suppressed, and thus good machined surface properties can be obtained over a long period of time.
- FIG. 6B is a distribution diagram of Co by wavelength dispersion X-ray spectroscopy (WDS) in FIG. 6A.
- FIG. 6B is a distribution diagram of N (nitrogen) by wavelength dispersive X-ray spectroscopy (WDS) in FIG. 6A.
- EBSD electron beam backscattering diffraction
- FIG. 1 is a front view illustrating an example of a total shape tool for wood according to the present embodiment
- FIG. 2 is a front view illustrating an example of a total shape cutter according to the present embodiment.
- a total shape tool 1 for wood shown in FIG. 1 is formed by mounting a plurality of total shape cutters 2 on a rotary holder 3, and the total shape cutter 2 is inserted into a mounting port 4 provided on the rotary holder 3. It is installed by.
- the overall cutting tool 2 is composed of a base 2a and a cutting edge part 2b, and the shape of the cutting edge part 2b in contact with the wood that is the workpiece has a curved portion in FIG. Note that the overall cutter 2 is not formed by joining the cutting edge 2b to the base 2a by brazing or the like, but is made of a single plate, and the cutting edge 2b is a blade including the cutting edge 2c. It is a part that has been subjected to a pasting process.
- the material of the plate-like body constituting the total cutting tool 2 is made of cermet including a hard phase and a binder phase.
- the cermet in the present invention is defined as one in which the hard phase has the highest area ratio in the structure in which the proportion of cubic crystals containing TiC, TiN or TiCN. That is, the cemented carbide containing the most tungsten carbide (WC) is not included in the cermet of the present invention.
- the total shape cutter 2 of this embodiment is not limited to the shape shown in figure.
- the overall cutting tool 2 of the present embodiment is a unitary plate-like body in which a base 2a and a cutting blade portion 2b along a post-cutting shape of wood as a workpiece are joined by brazing or the like. Therefore, there is no possibility that the cutting edge 2b is peeled off from the base 2a even at high speed rotation.
- it consists of a cermet containing a hard phase and a binder phase, so it has high fracture resistance, corrosion resistance, and wear resistance. It can process MDF materials that contain a large amount of adhesive and natural wood that contains a large amount of moisture. However, there is little wear due to chipping and chipping.
- the specific gravity is lighter than cemented carbide and high-speed steel (SKH material), it is possible to increase the number of revolutions of the overall tool 1 for wood, thereby increasing the processing efficiency and suppressing the unevenness of the processing surface.
- the properties of the processed surface can be improved. Specifically, 18000 r. p. It is possible to cope with a rotational speed of m or more.
- specific dimensions of the total shape cutter 2 are, for example, a thickness of 1.5 to 3.5 mm, and an outer dimension of 15 to 60 mm ⁇ 15 to 60 mm when regarded as a rectangular shape.
- the mass ratio of the hard phase to the binder phase in the cermet constituting the overall cutter 2 is 70 to 95% by mass for the hard phase and 5 to 30% by mass for the binder phase.
- the specific gravity is 8.0 g / cm 3 or less
- the fracture toughness K IC is 8.5 MPa ⁇ m 1/2 or more
- the Vickers hardness Hv in the internal region of the cermet is 1500 or more. It is.
- the fracture toughness K IC may be determined according to JIS R 1607 (1995). Moreover, what is necessary is just to obtain
- the inner region of the cermet means a region on the inner side of 100 ⁇ m or more from the surface of the cermet.
- a Ti-based cermet having the highest Ti mass content ratio among metals is used as the cermet constituting the overall cutter 2.
- Co and Ni are included as the binder phase, and the content ratio of Ni with respect to the content of Co and Ni is 25 to 45 mass%.
- the content ratio of Ni to the content of Co and Ni is determined by crushing a part of the overall blade 2 and dissolving the obtained powder in hydrochloric acid, and then an ICP emission spectroscopic analyzer (manufactured by Shimadzu Corporation: ICPS- 8100) for Co and Ni and dividing the Ni content by the sum of the Co and Ni contents.
- the Ni content ratio relative to the Co and Ni contents in the cutting edge portion 2b is greater on the surface than on the inside. This makes it possible to further suppress chipping when cutting an MDF material containing a large amount of adhesive or a natural tree containing a large amount of water, and a MDF material containing a large amount of adhesive or a natural material containing a large amount of water.
- the corrosion resistance of the cutting edge portion 2b in contact with the wood can be further improved.
- the surface in the cutting blade part 2b is a surface which has comprised the outer side of the cutting blade part 2b, and the inside in the cutting blade part 2b means an area
- the Ni content in the cutting edge portion 2b is prepared by preparing a sample whose surface and inside can be observed, observing with a SEM (scanning electron microscope), and using an attached EDS (energy dispersive X-ray analyzer). What is necessary is just to compare the obtained count value. In addition, when there is a difference of 10% or more in the obtained count value, it is considered that there is a significant difference.
- the cermet 10 of FIG. 3 includes a bonded phase (white in the photograph of FIG. 3) 14 mainly composed of at least one of Co and Ni, and one or more carbonitrids of Group 4, 5, and 6 metals of the periodic table.
- the hard phase 12 is composed of a first hard phase 12A (black in the photograph of FIG. 3) composed of TiCN, and the periodic tables 4, 5, and 6 other than Ti and Ti.
- the outer peripheral portion is gray).
- the first hard phase 12A has an average particle diameter of 0.05 to 1 ⁇ m
- the second hard phase 12B has an average particle diameter of 0.2 to 3 ⁇ m and larger than the average particle diameter of the first hard phase 12A.
- the second hard phase 12B forms an agglomerated portion 15 having a particle size of three times or more of the average particle size of the second hard phase 12B, and the agglomerated portion 15 is 20 to 20 in the structure of the cermet 10. It exists at a ratio of 60 area%.
- the carbon content in the cermet 10 is 6.00 to 6.50% by mass.
- the fracture resistance of the cermet 10 is improved. That is, since the cermet 10 has a carbon content of 6.00 to 6.50% by mass, which is lower than that of the conventional cermet, it is difficult to exhibit the properties of carbide with high hardness, and the toughness of the cermet 10 is improved. Therefore, it is possible to suppress chipping of the cutting edge 2c in the cutting process of the cutting edge portion 2b, and it is possible to form a sharp cutting edge. As a result, when wood is machined with a general shape tool provided with an overall shape cutter, the machined surface of the wood is smooth and the generation of flaking can be suppressed.
- the first hard phase 12A has an average particle diameter of 0.05 to 1 ⁇ m, and by dispersing with such a particle diameter, it is possible to suppress a decrease in the hardness of the cermet 10. As a result, the fracture resistance is improved without reducing the wear resistance of the cermet 10.
- the second hard phase 12B is composed of a composite carbonitride with Ti and one or more of the Group 4, 5 and 6 metals of the periodic table other than Ti, and the content ratio of W in the central portion is in the outer peripheral portion. Since the content ratio of W is higher, the toughness of the second hard phase 12B is high.
- the second hard phase 12B has aggregate portions 15 larger than a predetermined size independently of the first hard phase 12A in the structure of the cermet 10 at a ratio of 20 to 60 area%.
- the agglomeration part 15 has an effect of suppressing the progress of cracks. That is, the agglomeration part 15 has an interface between the core part and the peripheral part like a cored structure particle of a black core part made of TiCN and a gray peripheral part made of a composite carbonitride of Ti and W or the like. It does not exist and cracks propagate along this interface.
- the agglomeration portion 15 has a higher effect of weakening the progress energy of cracks by developing the cracks in a complicated manner as compared with a hard phase having a simple uniform structure. Therefore, it is possible to suppress the chipping of the blade edge 2c and achieve a sharp state.
- the second hard phase is excellent in toughness, the fracture resistance of the cermet 10 can be further increased.
- the hard phase 12 consists of composite carbonitride with 1 type or more of periodic table 4th, 5th, and 6th metals other than Ti and Ti, the content rate of W in center part, and W in outer peripheral part
- the second hard phase 12B higher than the content ratio of W
- the fourth hard phase 12D in which the central portion is made of TiCN
- the distribution state of the W element in the hard phase can be confirmed by electron microanalyzer (EPMA) or Auger analysis.
- the first hard phase 12A can also be confirmed with an electron beam microanalyzer (EPMA).
- the second hard phase 12 ⁇ / b> B forms the agglomerated portion 15 independently of the first hard phase 12 ⁇ / b> A. That is, the second hard phase 12B exists in the agglomerated portion 15, but the first hard phase 12A does not exist.
- the average particle diameter of the first hard phase 12A is 0.05 ⁇ m or more
- the first hard phase 12A is not aggregated and the dispersed state is good in the cermet 10, and the hardness of the cermet 10 is high.
- the hardness of the cermet 10 is high in the average particle diameter of the 1st hard phase 12A being 1 micrometer or less.
- the average particle size of the second hard phase 12B is 0.2 ⁇ m or more and the average particle size of the first hard phase 12A or more, the toughness of the cermet 10 is high, and the average particle size of the second hard phase 12B. Is 3 ⁇ m or less, the hardness of the cermet 10 is high.
- the second hard phase 12B independently forms the first hard phase 12A and forms an agglomerated portion 15 having a particle size of three times or more with respect to the average particle size of the second hard phase 12B.
- the agglomerated portion 15 having a particle size of 3 times or more with respect to the average particle size of 12B is present in the structure of the cermet 10 in a ratio of 20 to 60 area%, the cermet 10 has high fracture resistance.
- a desirable range of the area ratio of the agglomerated portion 15 is 30 to 50 area%.
- the 2nd hard phase 12B may exist independently.
- the carbon content ratio in the cermet 10 is 6.00% by mass or more, the hardness of the cermet 10 is high, and when the carbon content ratio in the cermet 10 is 6.50% by mass or less, the fracture resistance of the cermet 10 High nature.
- the agglomerated portion 15 is composed of composite carbonitride with Ti and one or more of Group 4, 5, and 6 metals of the periodic table other than Ti, and the content ratio of W in the central portion is in the outer peripheral portion.
- the third hard phase having the same W content ratio may be present together with the second hard phase in which the W content ratio in the central portion is higher than the W content ratio in the outer peripheral portion.
- the area ratio of the third hard phase 12C existing in the cermet 10 is 0 to 40 area% in the structure of the cermet 10.
- the portion other than the agglomerated portion 15 includes a core portion made of TiCN and a peripheral portion made of a composite carbonitride of one or more of the periodic table groups 4, 5 and 6 metals other than Ti and Ti.
- a fourth hard phase may be present.
- the area ratio of the fourth hard phase 12D present in the cermet 10 is 0 to 30% by area in the structure of the cermet 10.
- the ratio of SA and SB (SB / SA). Is 1.0 to 2.5. Within this range, the fracture resistance can be improved without reducing the wear resistance of the cermet 10.
- the ratio (d B / d A ) is 3 0-10. This has the effect of improving the wear resistance of the cermet 10.
- the particle size of the hard phase 12 in the present invention is measured in accordance with the measuring method of the average particle size of the cemented carbide specified in CIS-019D-2005. At this time, in the case where the hard phase 12 has a cored structure, the outer edge of the peripheral part including the core part and the peripheral part is measured as one hard phase 12.
- the cermet 10 contains 70 to 95 area% of the hard phase 12 and 5 to 30 area% of the binder phase.
- the total content of the nitrides or carbonitrides of the periodic tables 4, 5 and 6 metals mainly composed of Ti forming the hard phase 12 is 70 to 90% by mass. 80 to 90% by mass in terms of improvement.
- the content of the binder phase 14 is 10 to 30% by mass, the cermet 10 has an excellent balance of hardness and toughness.
- a desirable range of the binder phase is 10 to 25% by mass.
- the ratio of each metal element to the total amount of metal elements of the cermet 10 is as follows: Ti is 40 to 70% by mass, W is 10 to 30% by mass, Nb is 0 to 20% by mass, and Mo is 0 to 10% by mass. %, Ta is 0 to 10% by mass, V is 0 to 5% by mass, Zr is 0 to 5% by mass, Co is 5 to 15% by mass, and Ni is 5 to 15% by mass.
- the cermet 10 has high wear resistance and fracture resistance.
- FIG. 6 is a diagram showing Vickers hardness Hv in the vicinity;
- FIG. 6A is a scanning electron micrograph of FIG. 5A, and
- FIG. 6B is a distribution diagram of Co by wavelength dispersive X-ray spectroscopic analysis (WDS);
- WDS wavelength dispersive X-ray spectroscopic analysis
- FIG. 7 which is electron backscatter diffraction (EBSD) data in the vicinity of the surface of the cermet 20 of FIGS. 5A and 6A. explain.
- the cermet 20 of FIGS. 5A to 5C includes a TiCN phase, 40-60% by volume of a hard phase composed of cubic crystals containing Ti and other metal elements, and 30-50% by volume of a WC phase as another hard phase. And a binder phase in the range of 8 to 15% by volume.
- the composition of the cermet 20 is 50 to 70% by mass of WC, 15 to 30% by mass of TiCN, and one or more carbides of Group 4, 5, and 6 metals in the periodic table other than W and Ti,
- the entire composition contains at least one of nitride and carbonitride in a ratio of 0 to 10% by mass and at least one of Co and Ni in a ratio of 6 to 12% by mass.
- the cermet 20 is made of carbide, nitride, and carbonitride containing one or more of W, Ti, and other metals in Group 4, 5, and 6 of the periodic table.
- a composite hard phase comprising at least one kind (observed in gray in the figure, also referred to as ⁇ phase) 22, a WC phase 23 (observed in white in the figure), and at least one of Co and Ni And a binder phase 24 (observed in black in the figure).
- a part of the periodic table Group 4, 5 and 6 metals other than WC can also exist as carbides or nitrides.
- the surface region 26 in which the content ratio of the WC phase 23 is higher than the inner region of the cermet 20 exists on the surface side of the cermet 20. Yes.
- the content ratio of at least one of carbides, nitrides, and carbonitrides of Group 4, 5, and 6 metals of the periodic table other than WC is lower than that in the inner region 27 of the cermet 20.
- the average particle size of the WC phase in the surface region 26 is larger than the average particle size of the WC phase 23 in the internal region 27.
- the mean free path between the WC phases 23, 23 corresponding to the thickness of the binder phase 24 surrounding the WC phase 23 in the surface region 26 is lengthened (thickened), and degration of the WC phase 23 is suppressed.
- the fracture resistance on the surface of 20 can be improved.
- the fourth, fifth, and sixth group metals other than WC can be partly present as carbide or nitride in addition to the carbonitride.
- a high hardness region 28 having a higher hardness than the inner region 27 of the cermet 20 exists immediately below the surface region 26. Thereby, the plastic deformation of the cermet 20 can be suppressed, and the effect of increasing the wear resistance is remarkable.
- the cermet 20 has three regions from the surface, that is, the surface region 26, the high hardness region 28, and the internal region 27.
- the surface region 26 and the high hardness region 28 have clearly different structures, and their boundaries are clear. If the boundary between the surface region 26 and the high hardness region 28 is unclear, the region where the ratio of the WC phase in the total amount of the hard phase is 80 area% or more is the surface region 26 and the WC in the total amount of the hard phase. A region having a phase ratio of less than 80 area% is divided as a high hardness region 28. Even when the high hardness region 28 does not exist, the surface region 26 and the internal region 27 clearly have different structures, and their boundaries are clear.
- the region where the proportion of the WC phase in the total amount of the hard phase is 80 area% or more is the surface region 26 and the WC phase in the total amount of the hard phase. Can be clearly divided as the internal region 27.
- the boundary between the high hardness region 28 and the inner region 27 continuously changes as the whole cermet 20, and therefore it is difficult to clearly determine the boundary visually.
- the boundary is determined from the result of the hardness distribution obtained by connecting the hardness at each measurement point in FIG. 5C. That is, the internal region 27 indicates a region in which the hardness does not change within the range of variation in the hardness distribution, and the boundary between the high hardness region 28 and the internal region 27 is an intermediate value of the range of hardness variation in the internal region 27. It is assumed that the hardness curve of the high hardness region 28 intersects.
- the analysis is performed at a depth of 1000 ⁇ m from the surface of the cermet 20 far from the boundary between the internal region 27 and the high hardness region 28.
- the average particle size of the WC phase 23 in the surface region 26 is 1.1 to 1.5 times the average particle size of the WC phase 23 in the internal region 27, the fracture resistance and resistance to cermet 20 are reduced. Abrasion can be maintained in a more balanced manner.
- the average particle size of the WC phase 23 in the internal region 27 is 1.5 to 4.0 ⁇ m, and the particularly desirable average particle size is 2.7 to 3.5 ⁇ m.
- the content ratio of N is high at the portion where the Co content ratio is high, that is, at the position of the binder phase 24 (FIG. 6C). It can be seen that the content ratio is high at the position of the composite hard phase 22, and the content ratio is low at the position of the WC phase 23 (the white ratio is low in the figure).
- the content ratio of the binder phase contained in the surface region 26 is larger than the content ratio of the binder phase contained in the internal region 27 and is contained in the binder phase 24 in the surface region 26.
- the nitrogen content ratio is greater than the nitrogen content ratio contained in the WC phase 23. Therefore, the nitrogen content ratio contained in the binder phase 24 in the surface region 6 is higher than the nitrogen content ratio contained in the binder phase 24 in the inner region 27.
- the plastic deformation resistance of the binder phase 24 surrounding the WC phase 23 in the surface region 26 is improved and the WC phase 23 is prevented from being shattered.
- the chipping at the cutting edge 2c of the cutting edge portion 2b during chipping is performed. It can be suppressed and a sharp cutting edge can be obtained.
- the fracture resistance on the surface of the cermet 20 can be improved.
- the inner region 27 has the same composition as the entire composition of the cermet 20.
- the surface region 26 has a composition in which the content ratio of the WC phase 23 is high with respect to the internal region 27 and the content ratio of the composite hard phase 22 is low.
- the high hardness region 28 has a composition with a high content ratio of the composite hard phase 22 and a low content ratio of the WC phase 23, Co, and nitrogen as compared with the internal region 27 and the surface region 26.
- the nitrogen content ratio in the surface region 26 is 1.1 times or more than the nitrogen content ratio in the internal region 27.
- both the fracture resistance and wear resistance of the cermet 20 can be maintained in a well-balanced manner.
- a preferable range of the nitrogen content ratio in the surface region 26 in the internal region 27 is 1.08 to 1.10.
- the thickness of the surface region 26 is 5 to 20 ⁇ m.
- the toughness of the cutting edge 2c can be increased and plastic deformation on the surface of the cermet 20 can be suppressed.
- the surface region 26 has this thickness, even if a component in the cermet 20 forms a chemical vapor deposition (CVD) film, which will be described later, on the surface of the cermet 20, a part of the crystals constituting the structure grows abnormally. It is possible to suppress the formation of a good CVD film on the surface of the cermet 20.
- a particularly desirable thickness of the surface region 26 is 10 to 20 ⁇ m.
- the thickness of the high hardness region 28 is 30 to 200 ⁇ m, and particularly desirably 50 to 150 ⁇ m, so that the plastic deformation resistance of the cermet 20 can be improved and the wear resistance can be increased.
- the Vickers hardness Hvd at the center in the thickness direction of the surface region 26 is in the range of 0.8 to 1.0 times the average Vickers hardness Hvi in the inner region 7, and the high hardness region 28
- the maximum value Hvh of the Vickers hardness is in the range of 1.2 to 1.3 times the average Vickers hardness Hvi in the inner region 27. Within this range, both the wear resistance and fracture resistance of the cermet 20 can be improved.
- the average particle size of the composite hard phase 22 in the high hardness region 28 immediately below the surface region 26 Decreases from the surface toward the inner region 27 (not shown in FIG. 7), and exhibits an effect of increasing the hardness of the surface of the high hardness region 28 and having excellent wear resistance.
- the high hardness region 28 has a low content ratio of the WC phase 23 with respect to the internal region 27, and the high hardness region 28 has a high hardness.
- the composite hard phase 22 is expressed by white to grayish white, the WC phase 23 is dark gray, and the binder phase 24 is black.
- a coating layer may be formed on the surface of the cermet 20 by a chemical vapor deposition (CVD) method or a physical vapor deposition (PVD) method such as an ion plating method or a sputtering method, if desired.
- CVD chemical vapor deposition
- PVD physical vapor deposition
- the presence of the surface region 26 can suppress the chipping of the coating layer immediately, and the adhesiveness is also good.
- the CVD film is excellent in wear resistance against high-speed cutting, but the presence of the surface region 26 makes it possible to produce a coating layer made of normal particles without causing the CVD film to grow abnormally. Can do.
- cermet that combines at least two of the features of the first to third embodiments may be employed as the overall cutting tool 2.
- the total shape tool 1 for wood according to the present embodiment is formed by mounting a plurality of the total shape cutters 2 according to the present embodiment on the rotary holder 3, the plurality of total shape tools 2 to be mounted are conventional cemented carbide or Since it is lighter than the SKH material, the rotational speed can be increased without requiring a large amount of power, so that the processing efficiency can be further increased. In addition, since cutting can be performed at high speed rotation, swaying of the machined surface is suppressed, and thus good machined surface properties can be obtained over a long period of time.
- the manufacturing method of the cermet of the 1st embodiment is demonstrated. At least one powder selected from TiC, TiN and TiCN, and at least one powder of carbide, nitride and carbonitride containing one or more of W, Mo, Ta, V, Zr and Nb; Co powder and Ni powder are prepared, and a predetermined amount is weighed and then mixed. In order to make the Ni content ratio in the binder phase Co and Ni 25% or more and 45% or less, the mass ratio of Ni powder in the Co powder and Ni powder at the time of weighing is 25% or more and 45% or less. do it.
- a binder is added to the mixed powder to form a molding raw material.
- this forming raw material it is formed into a predetermined plate shape by a known method such as press molding, extrusion molding or injection molding, and fired at a maximum temperature of 1400 to 1600 ° C.
- the overall blade 2 can be obtained by forming the cutting edge portion 2b by grinding using a grinder.
- what is necessary is just to heat-process, after immersing the cutting blade part 2b in Ni solution, in order to increase the content rate of Ni in the cutting blade part 2b on the surface from the inside.
- Method for producing cermet of second embodiment A method for producing the cermet according to the second embodiment will be described.
- TiCN powder having an average particle size of 0.1 to 1.2 ⁇ m, particularly 0.3 to 0.9 ⁇ m, and carbide powder, nitride powder, and carbonitride powder of Group 4, 5, and 6 metals of the periodic table other than TiCN
- a mixed powder is prepared by adding and mixing carbon powder, if desired, with at least one of the above.
- TiN powder and WC powder having an average particle size of 0.1 to 3 ⁇ m as at least one of carbide powder, nitride powder, and carbonitride powder of periodic tables 4, 5, and 6 metals other than TiCN NbC powder, MoC, TaC powder, VC powder and ZrC powder are applicable.
- the mixed powder is prepared by adding a binder, a solvent, or the like to the above-mentioned weighed raw material powder and mixing by a known mixing method such as a ball mill, a vibration mill, a jet mill, or an attritor mill.
- a known mixing method such as a ball mill, a vibration mill, a jet mill, or an attritor mill.
- an attritor mill is employed.
- the raw material powder is pulverized and the particle size is reduced by powder mixing by an attritor mill, at least one of the metal W powder and WC 1-x (0 ⁇ x ⁇ 1) powder, the metal Co powder and the metal Ni powder are ductile. Therefore, it tends to agglomerate by pulverization.
- the mixed powder is molded into a predetermined shape by a known molding method such as press molding.
- the above-mentioned cemented carbide with a predetermined structure can be produced by firing under the following conditions.
- specific firing conditions (a) the temperature is raised from room temperature to 1200 ° C., and (b) the temperature is raised from 1200 ° C. to a firing temperature T 1 of 1330 to 1380 ° C. by 0.1 to 2 ° C./min.
- the temperature is increased at a temperature rate a, and (c) the rate of temperature increase is 4 to 15 ° C./min from a firing temperature T 1 to a firing temperature T 2 of 1500 to 1600 ° C. in vacuum or in an inert gas atmosphere of 30 to 2000 Pa.
- the temperature is raised at b, and (d) is held at a firing temperature T 2 for 0.5 to 2 hours in a vacuum or an inert gas atmosphere of 30 to 2000 Pa, and then fired under conditions for lowering the temperature.
- the metal W powder and WC 1-x (0 ⁇ x ⁇ 1) powder aggregated in the mixed powder By controlling the temperature rising pattern during the firing and the timing of introducing a predetermined amount of inert gas, at least one of the metal W powder and WC 1-x (0 ⁇ x ⁇ 1) powder aggregated in the mixed powder.
- the seeds are agglomerated by being carbonized and nitrided while other Group 4, 5, and 6 elements are in solid solution. Further, the Co powder and the Ni powder are dissolved while being dissolved in each other, wrap around the hard phase, and bond between the hard phases. As a result, the cermet 10 having the above-described structure can be produced.
- step (b) if the rate of temperature increase in step (b) is slower than 0.1 ° C./min, the firing time is too long to be realistic, and if the rate of temperature increase in step (b) is higher than 2 ° C./min, The sintered Co metal powder and Ni metal powder do not sufficiently sinter, and the sinterability of the metal W powder is inferior. Moreover, when the rate of temperature increase in the step (c) is slower than 4 ° C./min, it is difficult to form the second hard phase having a high W content ratio in the central portion. (C) When the temperature increase rate in a process is faster than 15 degree-C / min, the sinterability of metal W powder will become high too much and the aggregation part 15 will be hard to be formed.
- the firing temperature T 2 is less than 1500 ° C.
- the second hard phase is difficult to be formed, and when the firing temperature T 2 is higher than 1600 ° C., the sinterability in the agglomerated portion 15 becomes active, and the agglomerated portion 15 is one uniform. It becomes a hard phase.
- a mixed raw material powder in which at least one of Ni powder of 3 to 0.8 ⁇ m is mixed is prepared.
- TiC powder and TiN powder may be added to the mixed raw material powder together with the TiCN powder. However, these raw material powders are dissolved during firing and
- the mixed raw material powder is molded into a predetermined shape by a known molding method such as press molding.
- tissue mentioned above can be produced by baking the said molded object on the following conditions.
- specific firing conditions (A) The temperature is raised to 1050 to 1250 ° C.
- the temperature is raised to a firing temperature T of 1500 to 1600 ° C.
- step (b) if the atmosphere in step (b) is an inert gas atmosphere such as nitrogen (N), a large amount of gas is generated in the inner region of the alloy and remains as voids, so that a dense alloy cannot be obtained. There is a possibility that the toughness of the alloy is lowered, and when the rate of temperature increase in the step (b) is slower than 5 ° C./min, the decomposition of TiCN proceeds to the inner region of the alloy and the surface region is not formed and is faster than 10 ° C./min. In addition, since a large amount of gas generated by decomposition of TiCN is generated in the inner region of the alloy and voids remain, a dense sintered body cannot be obtained.
- N inert gas atmosphere
- the decomposition of TiCN proceeds excessively, oversintering occurs, abnormal grain growth occurs, and it is difficult to control the particle size of the WC phase 3, and the rise in the step (c) is difficult. It is not realistic that the temperature rate is lower than 0.1 ° C./min. If the temperature rate is higher than 5 ° C./min, the thickness of the surface region becomes thin and the WC phase grain growth in the surface region becomes insufficient.
- the nitrogen content ratio of the binder phase in the surface region is larger than the nitrogen content ratio of the binder phase in the inner region, and the nitrogen content ratio contained in the binder phase in the surface region is more than the nitrogen content ratio contained in the composite hard phase.
- the nitrogen content ratio of the binder phase in the surface region tends to be significantly smaller than the nitrogen content ratio of the binder phase in the inner region.
- the cooling rate after firing to 5 to 12 ° C./min, the average particle size of the composite hard phase can be reduced from the surface toward the internal region in the high hardness region.
- a complete cutter made of a cermet, cemented carbide and SKH material was produced from the outer shape shown in FIG.
- the sharpness of the blade edge was confirmed by observation with a metal microscope with respect to the entire blade after the blade processing.
- the number of chippings was confirmed for a field of view having an enlargement magnification of 300 times, the number of chippings was confirmed for 5 fields of view and the total number of chippings having a depth of 3 ⁇ m or more was evaluated, there were 20 chippings.
- a composition of a cermet it is TiCN: 40 mass%, TiN: 10 mass%, WC: 20 mass%, NbC: 10 mass%, Co: 12 mass%, Ni: 8 mass%. Then, a total shape tool for wood was obtained by attaching eight total shape blades to each rotary holder.
- the processed surface of the MDF material cut by using the cermet general shape cutter was less peeled and very good processed surface properties than the cemented carbide and SKH materials.
- the chipping state of the cutting edge that determines the processed surface state of the MDF material was confirmed by the same evaluation method using a metal microscope after cutting, the total number of chippings after the completion of processing was 40.
- Samples with Ni content ratios of Co and Ni of 20%, 25%, 35%, 45% and 50% were prepared. This content ratio was measured for Co and Ni using an ICP emission spectrometer (ICPS-8100, manufactured by Shimadzu Corporation) after pulverizing a part of the sample and dissolving the obtained powder in hydrochloric acid. , Obtained by dividing the Ni content by the sum of the Co and Ni contents.
- the specific gravity of the cermet was 8.0 g / cm 3 or less, and the fracture toughness K IC was 8.5 MPa ⁇ m 1/2 or more.
- the Ni content range in which the Vickers hardness in the inner region of the cermet is 1500 or more, that is, the Ni content ratio that is excellent in high fracture resistance and wear resistance is 25 to 45% by mass. .
- the sample was the same up to the step of forming the cutting edge part.
- One sample was directly subjected to heat treatment after the cutting edge was immersed in the Ni solution as it was for the other sample. Then, for each sample, an observation sample of the surface and the inside is prepared and observed using an SEM (scanning electron microscope), and the count values obtained by the attached EDS (energy dispersive X-ray analyzer) are compared. As a result, there was no significant difference between the surface and the inside of one sample, and the surface of the other sample contained more Ni than the inside.
- the total number of chippings after the blade processing was 15, and the total number of chippings after the cutting processing was 30.
- TiCN powder having an average particle size of 0.6 ⁇ m, 7% by mass of WC powder having an average particle size of 1.1 ⁇ m, 10% by mass of TiN powder having an average particle size of 1.5 ⁇ m, and NbC having an average particle size of 1.5 ⁇ m 11% by mass of powder, 1% by mass of ZrC powder with an average particle size of 1.8 ⁇ m, 2% by mass of VC powder with an average particle size of 1.0 ⁇ m, 6% by mass of W powder with an average particle size of 6 ⁇ m, and an average particle size of 2
- a mixed powder prepared by adjusting a ratio of 10% by mass of Ni powder of 4 ⁇ m and 10% by mass of Co powder having an average particle diameter of 1.9 ⁇ m to isopropyl alcohol (IPA) using a stainless steel ball mill and carbide balls.
- IPA isopropyl alcohol
- the obtained overall shape knife was observed with a scanning electron microscope (SEM), and observed at five arbitrary positions in the cross section of the cermet with a 5000 ⁇ photograph, and each hard phase was observed with an electron beam microanalyzer (EPMA).
- SEM scanning electron microscope
- EPMA electron beam microanalyzer
- the average particle size of the first hard phase is 0.35 ⁇ m
- the average particle size of the second hard phase is 1.1 ⁇ m
- the area ratio of the first hard phase (SA) in the field of view is 33 area%
- the area ratio of the second hard phase (SB) is 34 area%
- the area ratio of the third hard phase (SC) is 16 area%
- SD area ratio of 4 hard phases
- SD area ratio of the binder phase was 14 area%.
- the ratio (SB / SA) was 1.03.
- the carbon content in the cermet was measured using a carbon analysis method using a cemented carbide with a known carbon content as a standard sample, and it was 6.15% by mass. Furthermore, the specific gravity of the cermet was 6.4 g / cm 3 , the fracture toughness K IC was 15.0 MPa ⁇ m 1/2 , and the Vickers hardness in the inner region of the cermet was 1500.
- this compact was put into a firing furnace, (a) heated to 1200 ° C. at a heating rate of 10 ° C./min, (b) 1400 at a heating rate r 1 of 6 ° C./min in a vacuum atmosphere. (C) In an atmosphere filled with nitrogen (N 2 ) gas 2500 Pa, the temperature was raised to 1550 ° C. at a heating rate r 2 of 1.0 ° C./min, and in that state for 1 hour And (d) calcination was performed under the calcination conditions of calcination in the step of cooling at a cooling rate of 10 ° C./min.
- the obtained cermet was subjected to scanning electron microscope (SEM) observation and electron beam backscatter diffraction (EBSD) measurement in the vicinity of the surface.
- Image analysis was performed in an area of 8 ⁇ m ⁇ 8 ⁇ m using analysis software, and the presence state of the hard phase and the presence of the surface area were confirmed, and the area ratio and average particle diameter were calculated.
- image data in one field of view is converted to gray scale, and a frequency graph of brightness is created based on the brightness at each dot.
- the set with the highest brightness is the WC phase, and the next highest set is combined.
- the aggregate having the lowest particle and lightness was identified as the binder phase, and the ratio of the number of dots was calculated as the area ratio.
- the lightness in the middle was calculated as a threshold value.
- cubic area particles composed of a composite hard phase of W and Ti and carbonitride containing Ta, Nb, and Zr are 50 area%, WC particles are 35 area%, and the average particle diameter of WC particles is It was 2.8 ⁇ m and the binder phase was 15 area%.
- the cubic particles were 2 area%, the WC particles were 83 area%, the average particle diameter of the WC particles was 2.1 ⁇ m, and the binder phase was 15 area%.
- the cubic particles were 60 area%, the WC particles were 30 area%, the average particle diameter of the WC particles was 2.7 ⁇ m, and the binder phase was 10 area%.
- the composite hard phase on the surface region side and the internal region side When the average particle diameter of (cubic grains) was measured, it was 2.0 ⁇ m on the surface region side of the high hardness region and 1.0 ⁇ m on the inner region side of the high hardness region.
- the average particle diameter is obtained by specifying cubic particles and WC particles in the SEM photograph with respect to the surface region, the high hardness region and the internal region of the cermet, calculating the area thereof, obtaining the average value, and calculating the average area. The diameter of the circle when converted to a circle was estimated and used as the average particle diameter of cubic grains and WC grains.
- the composition in the cermet after firing was the same as the composition described in the mixed raw material powder in Table 1 except that TiN changed to TiCN during firing. That is, the content of WC was the same as the content of WC in the mixed raw material powder described above, and the content of TiCN was the same as the content of TiCN in the mixed raw material powder described above. In addition, the content of one or more carbonitrides of the periodic tables 4, 5 and 6 metals other than W and Ti is the same as the total metal content of the other compounds in the mixed raw material powder described above. But everything was carbonitride. Furthermore, the content of Co and Ni was the same as the total content of Co and Ni in the mixed raw material powder described above.
- the Vickers hardness was measured at a load corresponding to the distance from the cermet surface with a load of 50 g, and the distribution of the Vickers hardness was shown in a graph as shown in FIG. 5C.
- the Vickers hardness Hvd 1420 at the center in the thickness direction of the surface region
- the average Vickers hardness Hvi 1550 in the inner region
- the maximum value Vvh hardness Hvh 2000 GPa in the high hardness region.
- the average Vickers hardness Hvi in the inner region was determined by determining the boundary position at the beginning of the inner region from the distribution of Vickers hardness and measuring three points every 20 ⁇ m from this boundary position.
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Abstract
Description
(第1の実施態様)
総形刃物2を構成するサーメットとしては、金属のうちでTiの質量の含有比率が最も高いTi基サーメットを用いる。このとき、本実施態様では、結合相としてCoおよびNiを含み、CoおよびNiの含有量に対するNiの含有比率が25~45質量%である。この範囲であることにより、高い耐蝕性と耐摩耗性を併せ持つことから、接着剤を多く含有するMDF材や水分を多く含有する自然木であっても長期間にわたって切削加工できる総形刃物2となる。
(第2の実施態様)
総形刃物2を構成するサーメットの第2の実施態様として、図3のサーメットの断面についての走査型電子顕微鏡(SEM)写真および図4の模式図を基に説明する。
(第3の実施態様)
総形刃物2を構成するサーメットの第3の実施態様について、図5Aの表面付近における断面についての走査型電子顕微鏡写真、図5Bの内部領域における断面についての走査型電子顕微鏡写真、図5Cの表面付近におけるビッカース硬度Hvを示す図、図5Aのサーメットの表面付近の一部において、図6Aの走査型電子顕微鏡写真、図6Bの波長分散型X線分光分析(WDS)によるCoの分布図、図6Cの波長分散型X線分光分析(WDS)によるN(窒素)の分布図、および図5A、図6Aのサーメット20の表面付近における電子線後方散乱回折(EBSD)データである図7を基に説明する。
本実施形態の木材用総形工具1は、本実施形態の総形刃物2を回転ホルダ3に複数装着してなるものであることから、複数装着する総形刃物2が従来の超硬合金やSKH材に比べて軽量であることにより、大きな動力を必要とすることなく回転数を上げることができるため、加工効率をより高めることができる。また、高速回転で切削できることから、加工面のむしれが抑制されるため、良好な加工面性状を長期間にわたって得ることができる。
第1の実施態様のサーメットの製造方法について説明する。TiC、TiNおよびTiCNから選ばれる少なくとも1種の粉末と、W、Mo、Ta、V、ZrおよびNbのうちの1種以上を含有する炭化物、窒化物、炭窒化物の少なくとも1種の粉末と、Co粉末と、Ni粉末とを準備し、所定量秤量した後、混合する。なお、結合相であるCoとNiとにおけるNiの含有比率を25%以上45%以下とするには、秤量時におけるCo粉末とNi粉末とにおけるNi粉末の質量比率を25%以上45%以下とすればよい。
第2の実施態様のサーメットの製造方法について説明する。まず、平均粒径0.1~1.2μm、特に0.3~0.9μmのTiCN粉末と、TiCN以外の周期表4、5、6族金属の炭化物粉末、窒化物粉末、炭窒化物粉末の少なくとも1種と、平均粒径0.5~5μmの所定量の金属Co粉末や金属Ni粉末と、平均粒径2~10μmの金属W粉末およびWC1-x(0<x≦1)粉末の少なくとも1種と、所望により炭素粉末を添加して混合し混合粉末を調整する。
第3の実施態様のサーメットの製造方法について説明する。まず、平均粒径0.5~2.0μm、望ましくは0.6~1.5μmのTiCN粉末と、平均粒径0.5~5μmのWC粉末と、平均粒径0.1~2μmの上述した他の周期表第4、5および6族金属の炭化物粉末、窒化物粉末または炭窒化物粉末のいずれか1種と、平均粒径1.0~3.0μmのCo粉末と平均粒径0.3~0.8μmのNi粉末との少なくとも1種と、を混合した混合原料粉末を作製する。なお、この混合原料粉末中にTiCN粉末ととともにTiC粉末やTiN粉末を添加することもあるが、これらの原料粉末は焼成中に固溶して、焼成後の複合硬質相においてともにTiCNを構成する。
(a)1050~1250℃まで昇温し、
(b)真空雰囲気で5~10℃/分の昇温速度r1で1300~1400℃まで昇温し、(c)窒素(N)を1000~3000Pa充填した雰囲気で0.1~5℃/分の昇温速度r2で1500~1600℃の焼成温度Tまで昇温するとともに、
(d)真空雰囲気、または不活性ガスを充填した雰囲気で0.5~1時間維持し、(e)3~15℃/分の冷却速度で冷却する工程にて焼成する。
また、本実施形態の木材用総形工具は、複数の装着口4を設けた回転ホルダを作製し、それぞれの装着口4に総形刃物2を挿入して装着すればよい。
2 :総形刃物
2a:基体
2b:切刃部
3 :回転ホルダ
4 :装着口
Claims (14)
- 切刃部を有する一体物の板状体であり、硬質相と結合相とを含むサーメットからなる総形刃物。
- 前記結合相としてCoおよびNiを含み、CoおよびNiの含有量に対するNiの含有比率が25~45質量%である請求項1に記載の総形刃物。
- 前記切刃部におけるCoおよびNiの含有量に対するNiの含有比率が、内部より表面で多い請求項1または請求項2に記載の総形刃物。
- 前記サーメットが、CoおよびNiの少なくとも1種を主とする結合相と、周期表第4、5および6族金属のうちの1種以上の炭窒化物からなる硬質相とからなり、前記硬質相が、TiCNからなる第1硬質相、およびTiとTi以外の周期表第4、5および6族金属のうちの1種以上との複合炭窒化物からなり、かつ中心部におけるWの含有比率が外周部におけるWの含有比率よりも高い第2硬質相を含み、前記第1硬質相は平均粒径が0.05~1μmであり、前記第2硬質相は平均粒径が0.2~3μmでかつ前記第1硬質相の平均粒径よりも大きく、前記第2硬質相は、当該第2硬質相の平均粒径に対して3倍以上の粒径からなる凝集部を構成してなり、該凝集部はサーメットの組織中に20~60面積%の比率で存在し、サーメット中の炭素の含有比率が6.00~6.50質量%である請求項1乃至3のいずれかに記載の総形刃物。
- 前記凝集部中には、TiとTi以外の周期表第4、5および6族金属のうちの1種以上との複合炭窒化物からなり、かつ中心部におけるWの含有比率が外周部におけるWの含有比率と同じ第3硬質相がさらに存在する請求項4に記載の総形刃物。
- 前記凝集部以外の部分には、TiCNからなる芯部およびTiとTi以外の周期表第4、5および6族金属のうちの1種以上との複合炭窒化物からなる周辺部からなる第4硬質相がさらに存在する請求項4または5に記載の総形刃物。
- 前記サーメットには、WC以外の周期表第4、5および6族金属の炭化物、窒化物および炭窒化物の含有比率が前記サーメットの内部に比べて低い表面領域が存在するとともに、該表面領域におけるWC相の平均粒径が前記内部におけるWC相の平均粒径に対して大きい請求項1乃至6のいずれかに記載の総形刃物。
- 前記表面領域におけるWC相の平均粒径が、前記内部におけるWC相の平均粒径に対して1.1~1.5倍である請求項7に記載の総形刃物。
- 前記表面領域の厚みが5~20μmである請求項7または8に記載の総形刃物。
- 前記表面領域の直下に、前記サーメットの内部に対して硬度が高い高硬度領域が存在する請求項7乃至9のいずれかに記載の総形刃物。
- 前記高硬度領域中の前記WC相の含有比率が前記内部よりも低い請求項10に記載の総形刃物。
- 前記表面領域の厚み方向の中央におけるビッカース硬度が、前記内部における平均ビッカース硬度に対して0.8~1.0倍である請求項7乃至11のいずれかに記載の総形刃物。
- 前記高硬度領域中のビッカース硬度の極大値が、前記内部における平均ビッカース硬度に対して1.2~1.3倍である請求項10乃至13のいずれかに記載の総形刃物。
- 請求項1乃至請求項13のいずれかに記載の総形刃物を回転ホルダに複数装着してなる木材用総形工具。
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JP2014549938A JP5956609B2 (ja) | 2012-11-29 | 2013-11-29 | 総形刃物および木材用総形工具 |
EP13858854.6A EP2926964A4 (en) | 2012-11-29 | 2013-11-29 | STRAWBERRY SHAPE AND TOOL FOR WOOD SHAPE |
US14/648,184 US20150299051A1 (en) | 2012-11-29 | 2013-11-29 | Formed cutter and formed tool for wood |
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JP2012-261178 | 2012-11-29 |
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EP (1) | EP2926964A4 (ja) |
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Cited By (2)
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WO2014208447A1 (ja) * | 2013-06-28 | 2014-12-31 | 京セラ株式会社 | サーメットおよびその製造方法並びに切削工具 |
US20190176240A1 (en) * | 2016-04-13 | 2019-06-13 | Kyocera Corporation | Cutting insert and cutting tool |
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CN105562801A (zh) * | 2014-10-17 | 2016-05-11 | 基准精密工业(惠州)有限公司 | 铣刀 |
US20170203465A1 (en) * | 2016-01-19 | 2017-07-20 | II Phillip C. Crabtree | Router bit |
US10940606B2 (en) * | 2018-04-20 | 2021-03-09 | Micro Jig, Inc. | Router bit with a flared cutting edge |
US11491682B2 (en) | 2018-04-20 | 2022-11-08 | Henry Wang | Router bit with a flared cutting edge |
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US10570486B2 (en) | 2013-06-28 | 2020-02-25 | Kyocera Corporation | Cermet, and method for manufacturing same, as well as cutting tool |
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Also Published As
Publication number | Publication date |
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EP2926964A1 (en) | 2015-10-07 |
JPWO2014084389A1 (ja) | 2017-01-05 |
US20150299051A1 (en) | 2015-10-22 |
EP2926964A4 (en) | 2016-07-13 |
JP5956609B2 (ja) | 2016-07-27 |
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