WO2011002008A1 - サーメットおよび被覆サーメット - Google Patents
サーメットおよび被覆サーメット Download PDFInfo
- Publication number
- WO2011002008A1 WO2011002008A1 PCT/JP2010/061122 JP2010061122W WO2011002008A1 WO 2011002008 A1 WO2011002008 A1 WO 2011002008A1 JP 2010061122 W JP2010061122 W JP 2010061122W WO 2011002008 A1 WO2011002008 A1 WO 2011002008A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- cermet
- area
- hard phase
- phase
- hard
- Prior art date
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/05—Mixtures of metal powder with non-metallic powder
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process
- C23C30/005—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process on hard metal substrates
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23B—TURNING; BORING
- B23B27/00—Tools for turning or boring machines; Tools of a similar kind in general; Accessories therefor
- B23B27/14—Cutting tools of which the bits or tips or cutting inserts are of special material
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/05—Mixtures of metal powder with non-metallic powder
- C22C1/051—Making hard metals based on borides, carbides, nitrides, oxides or silicides; Preparation of the powder mixture used as the starting material therefor
-
- 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
- C22C29/06—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 carbides, but not containing other metal compounds
- C22C29/08—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 carbides, but not containing other metal compounds based on tungsten carbide
-
- 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
-
- 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
- B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12014—All metal or with adjacent metals having metal particles
- Y10T428/12028—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, etc.]
- Y10T428/12146—Nonmetal particles in a component
Definitions
- the present invention relates to a cermet and a coated cermet used for cutting tools and the like.
- Cermet has moderate toughness and wear resistance, and is used as a cutting tool for finishing cutting because a smooth and beautiful finished surface can be obtained by cutting the work material.
- a conventional technique related to cermet there is a method for producing a cermet in which the hardness of the cermet surface portion is increased to improve the wear resistance (see, for example, Patent Document 1). Further, there is a cermet whose structure is controlled inside and near the surface of the alloy to improve the performance (see, for example, Patent Document 2).
- an object of the present invention is to provide a cermet and a coated cermet which are more excellent in wear resistance and fracture resistance than conventional ones.
- the present inventors have made various studies for improving the fracture resistance of a cermet having excellent wear resistance.
- the present inventors include a cermet carbonitride phase and a tungsten carbide phase so as to have a predetermined ratio, and further, by sintering in a nitrogen atmosphere while changing the pressure in the sintering furnace, wear resistance is increased. It is possible to form a surface region with high toughness on the surface of the cermet having excellent properties, and when a surface region with high toughness is formed on the surface of the cermet, the strength and fracture resistance of the cermet are thereby improved. It has been found that the addition of V improves the high temperature strength and fracture resistance of the cermet, and the present invention has been completed.
- the cermet of the present invention includes a first hard phase composed of WC and a periodic table 4 (Ti, Zr, Hf, etc.), 5 (V, Nb, Ta, etc.) and 6 (Cr, Mo, W, etc.) containing titanium.
- a cermet comprising a second hard phase composed of at least one of group element carbides, nitrides, carbonitrides and their mutual solid solutions, and a binder phase mainly composed of an iron group metal.
- the ratio of the area ratio of the first hard phase to the area ratio of the second hard phase in the cross-sectional structure of the inner region of the cermet is 0.15 to 4.
- the cermet of the present invention is excellent in wear resistance and fracture resistance by providing a surface region having higher toughness than the internal region together with an internal region having excellent wear resistance and toughness.
- the coated cermet obtained by coating the cermet of the present invention with a hard film is further excellent in wear resistance.
- the surface region composed of the first hard phase and the binder phase is formed with an average thickness of 5 to 100 ⁇ m in the depth direction from the cermet surface.
- the average thickness of the surface region is less than 5 ⁇ m, the effect of increasing the toughness is not exhibited, and when the average thickness of the surface region exceeds 100 ⁇ m, the wear resistance is reduced.
- the average thickness was 5 to 100 ⁇ m.
- the average thickness of the surface region is preferably 10 to 50 ⁇ m, and more preferably 20 to 35 ⁇ m.
- the surface region is composed of a first hard phase and a binder phase, and has high toughness.
- the first hard phase of the present invention is made of WC.
- WC has a high thermal conductivity and has the effect of making it difficult for thermal cracks to occur in the cermet. Furthermore, since WC easily plastically deforms even at room temperature, an alloy containing WC has high toughness.
- the 2nd hard phase of this invention consists of at least 1 sort (s) chosen from the carbide
- the second hard phase include Ti carbonitride and carbonitride of a combination of Ti and at least one selected from the group consisting of W, Ta, Nb, Mo, V, Cr, Zr and Hf.
- the second hard phase has the effect of improving the wear resistance of the cermet.
- the structure structure of the second hard phase for example, Ti (C, N), (Ti, W) (C, N), (Ti, W, Ta) (C, N), (Ti, W, Nb) ( (C, N), (Ti, W, Ta, Nb) (C, N), (Ti, W, Nb, Mo, V) (C, N), (Ti, W, Cr, V) (C, N ), (Ti, W, Nb, Cr, V) (C, N), (Ti, W, Ta, Nb, Cr, V) (C, N), (Ti, W, Nb, Cr, Zr) ( C, N), (Ti, W, Cr) (C, N), (Ti, W, Nb, Cr, Hf) (C, N), (Ti, W, Ta, Cr) (C, N), A single phase made of carbonitride such as (Ti, W, Ta, Nb, Cr)
- C C C T -0.0653 ⁇ C W
- C N / C C the ratio of the amount of nitrogen C N (% by weight) contained in the whole cermet to C C (% by weight) obtained in the above.
- C C is an amount regarded as the carbon amount of the second hard phase
- 0.0653 is a coefficient for obtaining the carbon amount contained in WC, as will be described in detail below.
- the amount of carbon dissolved in the cermet binder phase is very small, and most of the carbon contained in the entire cermet is contained in the first hard phase and the second hard phase.
- W contained in the entire cermet is contained in the first hard phase and the second hard phase, but the amount of W contained in the first hard phase is large, and the amount of W contained in the second hard phase is very small. Therefore, (1) W included in the entire cermet is considered to form the first hard phase (WC), and (2) the value obtained by subtracting the carbon amount of WC from the carbon amount of the entire cermet is the carbon amount of the second hard phase. I saw it.
- WC is composed of W with 183.85 atoms and C (carbon) with 12.01 atoms, so the weight ratio of C contained in WC is 0.0613 and included in WC The weight ratio of W is 0.9387.
- the carbon content contained in WC is obtained by (0.0613 / 0.9387) ⁇ C W , that is, (0.0653 ⁇ C W ).
- the carbon amount (0.0653 ⁇ C W ) contained in WC By subtracting the carbon amount (0.0653 ⁇ C W ) contained in WC from the carbon amount C T (% by weight) of the entire cermet, the amount of carbon contained in the binder phase and the second hard phase can be obtained. . Since the amount of carbon dissolved in the binder phase is very small compared to the amount of carbon contained in the second hard phase, the carbon amount C C (wt%) of the second hard phase is (C T ⁇ 0.0653). • C W )
- nitrogen does not dissolve in the WC of the first hard phase.
- the amount of nitrogen dissolved in the binder phase is very small compared to the amount of nitrogen contained in the second hard phase. Most of the nitrogen is contained in the second hard phase. Therefore, it can be considered that the nitrogen amount of the whole cermet is proportional to the nitrogen amount of the second hard phase.
- the (C N / C C ) ratio that is, the ratio of the carbon amount to the nitrogen amount in the second hard phase
- the cermet of the present invention is obtained. 0.25 ⁇ (C N / C C ) ⁇ 6 is satisfied.
- the second hard in the raw powder composition This is achieved by adjusting the carbon content and the nitrogen content of the phase raw material powder. More specifically, the weight ratio of the nitrogen amount and the carbon amount of the second hard phase raw material powder in the raw material powder composition may be 1: 4 to 9: 1, preferably 1: 3.57 to 5: 1. More preferably, it is 1: 3.33 to 4.6: 1.
- the carbon content C T (% by weight) of the entire cermet can be measured by a high-frequency combustion-infrared absorption method.
- the nitrogen content C N (% by weight) of the entire cermet was measured by an inert gas melting-thermal conductivity method.
- the tungsten amount C W (% by weight) of the entire cermet can be measured by a fluorescent X-ray analyzer.
- the area% of each phase in the cross-sectional structure of the alloy corresponds to the volume% of each phase.
- the area ratio of the binder phase is 3 to 30 area%, and the sum of the area ratio of the first hard phase and the area ratio of the second hard phase is 70 to 97 area%.
- the total of these is preferably 100% by area.
- the reason for this is that when the binder phase is less than 3 area% and the sum of the first hard phase and the second hard phase is more than 97 area%, the toughness of the cermet decreases, conversely, This is because the wear resistance of the cermet is reduced when the binder phase is more than 30 area% and the total of the first hard phase and the second hard phase is less than 70 area%.
- the area ratio in the cross-sectional structure of the inner region of the cermet of the present invention is such that the area ratio of the binder phase is 4 to 25% by area, and the sum of the area ratio of the first hard phase and the area ratio of the second hard phase is The area ratio of the binder phase is 5 to 20 area%, and the total of the area ratio of the first hard phase and the area ratio of the second hard phase is preferably 80 to 95 area%.
- the internal region of the cermet of the present invention refers to a region other than the surface region. In order to make the internal region of the cermet of the present invention have the above-mentioned area ratio, it can be achieved by sintering at a densifying temperature.
- the area ratio of the binder phase is 3 to 30 area%
- the area ratio of the first hard phase is 70 to 97 area%
- the total of these is 100 area%. preferable.
- the reason for this is that when the binder phase is less than 3 area% and the first hard phase is more than 97 area%, the toughness of the cermet decreases, and conversely, the binder phase exceeds 30 area%. If the first hard phase is less than 70 area%, the wear resistance of the cermet is reduced.
- the second hard phase is contained in the surface region so as to be 0.1 to 10% by area of the cross-sectional structure of the surface region by substituting the first hard phase in the surface region, the toughness is not deteriorated. This is preferable because the wear resistance is improved.
- the area ratio of the binder phase in the inner region and the area ratio of the binder phase in the surface region are approximately the same. More preferably, the area ratio in the cross-sectional structure of the surface region of the cermet of the present invention is such that the area ratio of the binder phase is 4 to 25 area%, and the area ratio of the first hard phase is 75 to 96 area%.
- the area ratio of the binder phase is 5 to 20 area%, and the area ratio of the first hard phase is 80 to 95 area%.
- the surface region of the cermet of the present invention refers to a region having an average thickness of 5 to 100 ⁇ m in the depth direction from the surface of the cermet. In order to make the surface area of the cermet of the present invention have the above-mentioned area ratio, it can be achieved by setting the surface area portion to a low nitrogen state during sintering.
- the ratio of the area% of the first hard phase to the area% of the second hard phase in the cross-sectional structure of the inner region of the cermet of the present invention is 0.15 or more, the toughness is improved and the area% of the second hard phase is increased.
- the ratio of the area% of the first hard phase exceeds 4, the wear resistance is lowered. Therefore, the ratio of the area% of the first hard phase to the area% of the second hard phase was set to 0.15 to 4.
- the ratio of the area% of the first hard phase to the area% of the second hard phase is more preferably 0.20 to 3.8, and further preferably 0.25. ⁇ 3.5.
- it in order to make the ratio of the area% of the first hard phase to the area% of the second hard phase within the above range, it can be achieved by sintering under the condition of not denitrifying.
- the amount of Cr 3 C 2 obtained when the Cr element contained in the entire cermet of the present invention is converted into carbide (in this case, Cr element is converted into Cr 3 C 2 ), and the weight of the entire cermet is 100% by weight.
- Cr element is added to the cermet of the present invention so as to be 0.1 to 10% by weight, the high temperature strength of the cermet, particularly the high temperature strength of the surface region is improved. If the Cr 3 C 2 content when the Cr element is converted to carbide is less than 0.1% by weight, no effect is observed, and if it exceeds 10% by weight, the toughness decreases and the fracture resistance decreases.
- Cr element it is preferable to add Cr element to the cermet of the present invention so that the amount of Cr 3 C 2 when converted to carbide is 0.1 to 10% by weight.
- the amount of Cr 3 C 2 is more preferably 0.15 to 8% by weight, still more preferably 0.2 to 6% by weight.
- it in order to make the Cr 3 C 2 amount within the above range, it can be achieved by adding a predetermined amount of Cr 3 C 2 at the time of powder blending.
- the amount of VC when the V element contained in the entire cermet of the present invention is converted to carbide is 0.1 to 5% when the total weight of the cermet is 100% by weight.
- the element V is added to the cermet of the present invention so as to be%, the grain growth of WC is suppressed, the structure becomes uniform, and the fracture resistance is improved.
- the amount of VC is less than 0.1% by weight, the effect of homogenizing the structure and the effect of improving the fracture resistance cannot be obtained sufficiently, and when it exceeds 5% by weight, the toughness is lowered and the fracture resistance is lowered. To do.
- the V element to the cermet of the present invention so that the VC amount in terms of carbide is 0.1 to 5% by weight.
- the VC amount is more preferably 0.2 to 4% by weight, still more preferably 0.3 to 3% by weight.
- it in order to make VC amount into the said range, it can achieve by adding predetermined amount of VC at the time of powder blending.
- the bonded phase of the present invention has an effect of increasing the strength of the cermet by firmly bonding the first hard phase and the second hard phase.
- the binder phase containing an iron group metal as a main component is an iron group metal or an iron group metal and at least one of elements of the periodic tables 4, 5, and 6, Si, Al, Zn, Cu, Ru, Rh, and Re.
- the seed is a solid solution of less than 50% by weight when the total weight of the binder phase is 100% by weight.
- the iron group metal represents Co, Ni, or Fe.
- the binder phase is composed of one or two of Co and Ni because the mechanical strength is improved, and among them, the bond phase is more preferable because adhesion between the cermet and the hard film is improved.
- the elements of the periodic table 4, 5, and 6 are added to the iron group metal of the binder phase, and the total weight of the binder phase is 100% by weight. When it is less than 50% by weight, it is preferable.
- the binder phase is contained in an amount of less than 50 wt% because the sinterability is improved. Further, when the total weight of the binder phase is 100% by weight, it is preferable to add 30% by weight or less to the iron group metal of the binder phase because the wear resistance is improved. In this invention, in order to make the quantity of each component into the said range, it can achieve by adding the predetermined quantity of each component at the time of powder blending.
- the surface of the cermet of the present invention is coated with a hard film such as periodic table 4, 5, 6 element, Al, Si oxide, carbide, nitride and their mutual solid solution, hard carbon film by CVD method or PVD method.
- the coated cermet is excellent in wear resistance.
- Specific examples of the hard film include TiN, TiC, TiCN, TiAlN, TiSiN, AlCrN, Al 2 O 3 , diamond, diamond-like carbon (DLC), and the like.
- the average total film thickness of the hard film is 0.1 ⁇ m or more, the wear resistance is improved, and when it exceeds 30 ⁇ m, the chipping resistance is lowered, so 0.1-30 ⁇ m is preferable.
- the average total film thickness of the hard film is more preferably 1 to 20 ⁇ m, and further preferably 2.5 to 15 ⁇ m.
- the average total film thickness of the hard film can be increased by increasing the coating processing time.
- the cermet according to the present invention includes, for example, TiCN powder, WC powder, periodic table 4, 5, 6 elemental carbide, nitride, carbonitride and their mutual solid solution powder, and iron group metal powder.
- step (C) holding in a nitrogen atmosphere at a pressure of 10 Torr or higher at a second heating temperature of 1420 to 1600 ° C .;
- step (D) holding at a second heating temperature of 1420 to 1600 ° C. in a nitrogen atmosphere at a lower pressure than in step (C);
- step (E) A method of producing a cermet comprising a step of cooling from a second heating temperature of 1420 to 1600 ° C. to room temperature in a nitrogen atmosphere at a lower pressure than in step (D).
- step (A) the mixture is heated in a non-oxidizing atmosphere to prevent oxidation of the mixture.
- the non-oxidizing atmosphere include a vacuum, a nitrogen atmosphere, an inert gas atmosphere, and a hydrogen atmosphere.
- the pressure of the nitrogen atmosphere in the steps (B) and (C) is preferably 10 Torr or more. Note that when the pressure in the nitrogen atmosphere is higher than 100 Torr, the sinterability of the cermet is lowered. Therefore, the pressure in the nitrogen atmosphere is preferably 10 to 100 Torr.
- a TiCN powder, a WC powder, carbides, nitrides, carbonitrides and their mutual solid solution powders of periodic table 4, 5, and 6 elements, and iron group metal powders are prepared. These powders are commercially available or prepared by solution heat treatment at high temperatures, and the average particle size and the like are not particularly limited.
- the Fisher method Fisher method described in American Society for Testing and Materials (ASTM) standard B330
- the average particle size measured by Sub-Sieve® Sizer (FSSS) is preferably 0.1 to 10 ⁇ m, more preferably 0.5 to 8 ⁇ m.
- the powders are weighed to a predetermined weight ratio, mixed with a solvent in a wet ball mill, and after mixing, the solvent is evaporated to dry the mixture.
- a molding wax such as paraffin is added to the obtained mixture to form a predetermined shape.
- the molding method include press molding, extrusion molding, and injection molding.
- the molded mixture is put in a sintering furnace and heated to 350 to 450 ° C. in vacuum to remove the wax, and then the first heating temperature of 450 to 1200 to 1400 ° C. in vacuum or nitrogen atmosphere, preferably Is raised to 1200-1350 ° C.
- the rate of temperature increase is not particularly limited, but is preferably 1 to 20 ° C./min.
- the mixture is heated from a first heating temperature of 1200 to 1400 ° C. to a second heating temperature of 1420 to 1600 ° C., preferably 1450 to 1550 ° C., in a nitrogen atmosphere at a pressure of 10 Torr or more, preferably 10 to 300 Torr, and a nitrogen atmosphere At a second heating temperature of 1420 to 1600 ° C. for 10 to 60 minutes, preferably 20 to 50 minutes.
- the temperature raising rate at this time is not particularly limited, but is preferably 0.5 to 15 ° C./min.
- the cooling rate is not particularly limited, but is preferably 0.1 to 100 ° C./min.
- the coated cermet of the present invention can be obtained by coating the surface of the cermet of the present invention with a hard film by a conventional CVD method or PVD method.
- the cermet and coated cermet of the present invention are excellent in wear resistance and fracture resistance, and therefore exhibit excellent cutting performance when used as a cutting tool. Therefore, when the cermet and the coated cermet of the present invention are used as a cutting tool, the tool life can be improved as compared with the conventional case.
- Example 1 As raw material powder of cermet, average particle size 1.5 [mu] m of Ti (C 0.7 N 0.3) powder, average particle size 1.4 ⁇ m of Ti (C 0.5 N 0.5) powder, an average particle diameter of 1.5 ⁇ m Ti (C 0.3 N 0.7 ) Powder, TiN powder with an average particle diameter of 1.5 ⁇ m, (Ti 0.92 Nb 0.03 W 0.05 ) (C 0.5 N 0.5 ) powder with an average particle diameter of 1.7 ⁇ m, (Ti 0.89 Nb 0.03 Ta with an average particle diameter of 1.6 ⁇ m) 0.03 W 0.05 ) (C 0.5 N 0.5 ) powder, (Ti 0.8 Nb 0.1 W 0.1 ) (C 0.5 N 0.5 ) powder having an average particle diameter of 1.5 ⁇ m, TiC powder having an average particle diameter of 1.5 ⁇ m, average particle diameter 5 ⁇ m TaC powder, NbC powder with an average particle size of 1.5 ⁇ m, ZrC powder with an average particle size of 1.5 ⁇ m, WC
- the weighed mixed powder was mixed and pulverized with a wet ball mill, and then the solvent was evaporated to dry the mixture.
- Paraffin was added to the dried mixture and press molded.
- the press-molded mixture was put in a sintering furnace, and the temperature was gradually raised from room temperature to 450 ° C. in a vacuum to evaporate paraffin, and then from 450 ° C. in vacuum.
- the temperature was raised to a first heating temperature of 1220 ° C. at a heating rate of 10 to 12 ° C./min. Further, the mixture was heated from a first heating temperature of 1220 ° C. to a second heating temperature of 1540 ° C.
- the temperature was raised to 10 ° C. at a heating rate of 10 ° C./min. Furthermore, the temperature was raised from 1280 ° C. to 1540 ° C. at a rate of temperature rise of 5 ° C./min in vacuum, and held at 1540 ° C. in vacuum for 50 minutes. Then, it cooled in the vacuum from 1540 degreeC to normal temperature with the cooling rate of 100 degree-C / min.
- the surface structure of the obtained cermet and the cross-sectional structure of the internal region were observed with a scanning electron microscope, and the composition of the binder phase, the first hard phase, the second hard phase, the Cr amount and V using an EDS attached to the scanning electron microscope.
- the amount was measured.
- Cr content wt%) is converted to Cr 3 C 2 (wt%)
- V % by weight was converted to VC (% by weight). Since the amount of Cr 3 C 2 and the amount of VC show the same value in the surface region and the internal region, the amount is included in the entire cermet.
- the iron group elements are used as the main component if the total of iron group elements is 50% by weight or more with respect to the whole binder phase.
- the average thickness of the surface region was measured from the cross-sectional structure of the cermet using a scanning electron microscope. From a photograph obtained by using a scanning electron microscope photograph the cross-sectional structure of the surface region and the interior region of the cermet, in the surface region and the inner region, the area ratio S b of the binder phase, the area ratio of the first hard phase S 1, the second hard The area ratio S 2 of the phase was measured. Also it was determined S 1 / S 2 ratio of S 1 and S 2. These values are shown in Table 3. Incidentally, Comparative Product 5 because there pores are a number due to a decrease in sinterability, the total area ratio of S b and S 1 and S 2 does not become 100% by area.
- the nitrogen content C N (% by weight) of the entire cermet was measured by an inert gas melting-thermal conductivity method.
- the carbon content C T (% by weight) of the entire cermet was measured by a high frequency combustion-infrared absorption method.
- the amount of tungsten C W (% by weight) of the entire cermet was measured with a fluorescent X-ray analyzer.
- C N / (C T ⁇ 0.0653 ⁇ C W ) was calculated from these values, and the results are also shown in Table 3.
- the cermet was ground and honed and processed into an ISO standard TNMG160408 shape. Further, the film structure is (substrate side) average film thickness 1.0 ⁇ mTiN ⁇ average film thickness 8.0 ⁇ mTi (C, N) ⁇ average film thickness 0.5 ⁇ mTi (C, N, O) ⁇ average film thickness 1.5 ⁇ m Al 2 O 3—A hard film having an average film thickness of 0.2 ⁇ m TiN (outermost surface side) (average total film thickness of 11.2 ⁇ m) was coated by a CVD method. Cutting tests 1 to 3 were performed using a coated cermet obtained by CVD coating.
- Table 4 shows the results of the cutting test 1.
- Abrasion resistance evaluation test sample shape TNMG160408 Work material: S40C (shape: cylinder) Cutting speed: 200 m / min Cutting depth: 2.0mm Feed amount: 0.25mm / rev Atmosphere: Criteria for wet cutting life: Life is defined as when it is missing or when the maximum flank wear amount V Bmax is 0.3 mm or more.
- Table 5 shows the results of the cutting test 2.
- Abrasion resistance evaluation test sample shape TNMG160408 Work material: SCM440 (shape: cylinder) Cutting speed: 200 m / min Cutting depth: 2.0mm Feed amount: 0.25mm / rev Atmosphere: Criteria for wet cutting life: Life is defined as when it is missing or when the maximum flank wear amount V Bmax is 0.3 mm or more.
- Table 6 shows the results of the cutting test 3.
- the inventive product has a machining length of 4.2 km or more and is superior to the comparative product in cutting performance.
- the comparative product had a processing length of 3.1 km or less.
- the thermal conductivity is high and thermal cracks do not occur.
- the comparative product 3 was easy to react with the work material and was inferior in wear resistance and had a short life.
- the inventive product has a machining length of 3.8 km or more, and the cutting performance is superior to the comparative product.
- the comparative product was 2.8 km or less.
- the results of cutting tests 1 to 3 were scored. That is, with respect to the number of impacts of the cutting test 1, 3 points are 25,000 times or more, 2 points are 20000 times or more and less than 25000 times, 1 point is 15000 times or more and less than 20000 times, and 0 point is less than 15000 times. The results were averaged. Also, regarding the machining length of the cutting test 2, 4.5 points or more is 3 points, 3.0 km or more and less than 4.5 km is 2 points, 1.5 km or more and less than 3.0 km is 1 point, and less than 1.5 km is 0 point.
- the cutting length of the cutting test 3 is 4.0 km or more, 3 points, 2.5 km or more and less than 4.0 km, 2 points, 1.0 km or more and less than 2.5 km, 1 point, and less than 1.0 km as 0 point. .
- the average value of the scores of the cutting test 1 and the scores of the cutting test 2 and the cutting test 3 were totaled, and the value was used as a result of the comprehensive evaluation. The larger the score, the better the cutting performance.
- the obtained comprehensive evaluation results are shown in Table 7.
- the average value of the cutting test 1 of the invention product is 1.7 to 3 points, and it can be seen that it has excellent fracture resistance.
- the results of the cutting test 2 and the cutting test 3 of the invention product are 2 to 3 points, indicating that the wear resistance is excellent.
- Comparative products have lower overall evaluation scores than invention products. This indicates that the overall cutting performance is inferior to that of the invention.
- the comparative product 2 shows excellent wear resistance with 2 points in each of the cutting test 2 and the cutting test 3, but the average value of the cutting test 1 is 1 point, and the overall evaluation is 5 points. .
- Comparative product 3 showed 3 points in cutting test 1 and excellent chipping resistance. However, since it was 1 point each in cutting test 2 and cutting test 3, it was 5 in overall evaluation.
- Abrasion resistance evaluation test sample shape VNMG160408 Work material: S40C (shape: cylindrical) Cutting speed: 140 m / min Cutting depth: 2.0mm Feed amount: 0.25mm / rev Atmosphere: Criteria for dry cutting life: 10 corners are cut for a maximum of 15 minutes and broken, or the maximum flank wear amount V Bmax is 0.3 mm or more.
- Table 9 shows the results of cutting test 4.
- Example 2 As raw material powder of cermet, Ti (C 0.5 N 0.5 ) powder with an average particle size of 1.4 ⁇ m, TaC powder with an average particle size of 1.5 ⁇ m, NbC powder with an average particle size of 1.5 ⁇ m, HfC with an average particle size of 1.6 ⁇ m Powder, WC powder having an average particle diameter of 1.5 ⁇ m, Cr 3 C 2 powder having an average particle diameter of 1.1 ⁇ m, and Co powder having an average particle diameter of 1.3 ⁇ m were prepared. Using these, the blending composition shown in Table 10 was weighed.
- a mixed powder was produced by the same method as in Example 1, and press molded.
- the press-molded mixture is put in a sintering furnace and gradually heated to 450 ° C. in a vacuum to evaporate paraffin, and then heated in a vacuum to a first heating temperature of 1240 ° C. at a rate of temperature increase of 10-12 ° C. /
- the temperature was raised in minutes. Further, the temperature is increased from a first heating temperature of 1240 ° C. to a second heating temperature of 1520 ° C. in a nitrogen atmosphere at a pressure of 30 Torr at a rate of temperature increase of 2.0 ° C./min, and the first heating temperature of 1520 ° C. in a nitrogen atmosphere at a pressure of 30 Torr.
- the cross-sectional structure of the surface region and internal region of the cermet was observed with a scanning electron microscope, and the composition of the binder phase, the first hard phase, and the second hard phase was measured using EDS attached to the scanning electron microscope. These results are shown in Table 11. Note that, among the elements contained in the binder phase, 50% by weight or more of the elements as the main component was used as the main component, and less than 50% by weight of the elements as the trace component was used as the minor component.
- the average thickness of the surface region was measured from the cross-sectional structure of the cermet using a scanning electron microscope. From a photograph obtained by using a scanning electron microscope photograph the cross-sectional structure of the surface region and the interior region of the cermet, in the surface region and the inner region, the area ratio S b of the binder phase, the area ratio of the first hard phase S 1, the second hard The area ratio S 2 of the phase was measured. Also it was determined S 1 / S 2 ratio of S 1 and S 2. These values are shown in Table 12.
- the obtained cermet was ground and honed and processed into an ISO standard TNMG160408 shape. Further, the film structure is (substrate side) average film thickness 1.0 ⁇ mTiN ⁇ average film thickness 8.0 ⁇ mTi (C, N) ⁇ average film thickness 0.5 ⁇ mTi (C, N, O) ⁇ average film thickness 1.5 ⁇ m Al 2 O 3—A hard film having an average film thickness of 0.2 ⁇ m TiN (outermost surface side) (average total film thickness of 11.2 ⁇ m) was coated by a CVD method. Cutting test 5 was performed using the coated cermets of Invention Products 11 and 12 obtained by CVD coating and the coated cermets of Comparative Products 3 and 4 of Example 1.
- Abrasion resistance evaluation test sample shape TNMG160408 Work material: S40C (shape: cylinder) Cutting speed: 200 m / min Cutting depth: 2.0mm Feed amount: 0.25mm / rev Atmosphere: Criteria for wet cutting life: Life is defined as when it is missing or when the maximum flank wear amount V Bmax is 0.3 mm or more.
- Table 13 shows the results of the cutting test 5.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Cutting Tools, Boring Holders, And Turrets (AREA)
- Powder Metallurgy (AREA)
Abstract
Description
0.25<(CN/(CT-0.0653・CW))<6
を満足し、第1硬質相と結合相とからなる平均厚さ5~100μmの表面領域、および表面領域よりも内部に存在する第1硬質相と第2硬質相と結合相とからなる内部領域によって形成され、サーメットの内部領域の断面組織における、第2硬質相の面積率に対する第1硬質相の面積率の比が0.15~4であるものである。
CC=CT-0.0653・CW
で求めたCC(重量%)に対する、サーメット全体に含有される窒素量CN(重量%)の比(CN/CC)により、本発明のサーメットの特徴の一つを規定した。ここで、CCは以下に詳述するように、第2硬質相の炭素量とみなされる量であり、0.0653はWCに含まれる炭素量を求めるための係数である。
(A)非酸化雰囲気で常温から1200~1400℃の第1加熱温度まで昇温させる工程と、
(B)1200~1400℃の第1加熱温度から1420~1600℃の第2加熱温度まで圧力10Torr以上の窒素雰囲気で昇温させる工程と、
(C)1420~1600℃の第2加熱温度にて圧力10Torr以上の窒素雰囲気で保持する工程と、
(D)1420~1600℃の第2加熱温度にて工程(C)よりも低い圧力の窒素雰囲気で保持する工程と、
(E)1420~1600℃の第2加熱温度から常温まで工程(D)よりも低い圧力の窒素雰囲気で冷却する工程と
を含むサーメットの製造方法により得ることができる。
サーメットの原料粉末として、平均粒径1.5μmのTi(C0.7N0.3)粉、平均粒径1.4μmのTi(C0.5N0.5)粉、平均粒径1.5μmのTi(C0.3N0.7)粉、平均粒径1.5μmのTiN粉、平均粒径1.7μmの(Ti0.92Nb0.03W0.05)(C0.5N0.5)粉、平均粒径1.6μmの(Ti0.89Nb0.03Ta0.03W0.05)(C0.5N0.5)粉、平均粒径1.5μmの(Ti0.8Nb0.1W0.1)(C0.5N0.5)粉、平均粒径1.5μmのTiC粉、平均粒径1.5μmのTaC粉、 平均粒径1.5μmのNbC粉、平均粒径1.5μmのZrC粉、 平均粒径1.5μmのWC粉、平均粒径1.6μmのMo2C粉、平均粒径1.1μmのCr3C2粉、平均粒径1.0μmのVC粉、平均粒径1.3μmのCo粉、平均粒径1.6μmのNi粉を用意した。これらを用いて、表1に示す配合組成に秤量した。
耐欠損性評価試験
試料形状:TNMG160408
被削材:S40C(形状:円柱に4本の溝を入れた略円柱状)
切削速度:160m/min
切り込み:2.0mm
送り量:0.25mm/rev
雰囲気:湿式切削
試験回数:3回
寿命の判定基準:欠損するまでの衝撃回数を寿命とする。なお、衝撃回数が25000回になるまでに欠損しない場合は、その時点で試験を終了する。
耐摩耗性評価試験
試料形状:TNMG160408
被削材:S40C(形状:円柱)
切削速度:200m/min
切り込み:2.0mm
送り量:0.25mm/rev
雰囲気:湿式切削
寿命の判定基準:欠損したとき、または、最大逃げ面摩耗量VBmaxが0.3mm以上になったときを寿命とする。
耐摩耗性評価試験
試料形状:TNMG160408
被削材:SCM440(形状:円柱)
切削速度:200m/min
切り込み:2.0mm
送り量:0.25mm/rev
雰囲気:湿式切削
寿命の判定基準:欠損したとき、または、最大逃げ面摩耗量VBmaxが0.3mm以上になったときを寿命とする。
耐摩耗性評価試験
試料形状:VNMG160408
被削材:S40C(形状:円柱状)
切削速度:140m/min
切り込み:2.0mm
送り量:0.25mm/rev
雰囲気:乾式切削
寿命の判定基準:10コーナを最大15分間切削して、欠損したとき、または、最大逃げ面摩耗量VBmaxが0.3mm以上になったときを寿命とする。
サーメットの原料粉末として、平均粒径1.4μmのTi(C0.5N0.5)粉、平均粒径1.5μmのTaC粉、 平均粒径1.5μmのNbC粉、平均粒径1.6μmのHfC粉、 平均粒径1.5μmのWC粉、平均粒径1.1μmのCr3C2粉、平均粒径1.3μmのCo粉を用意した。これらを用いて、表10に示す配合組成に秤量した。
耐摩耗性評価試験
試料形状:TNMG160408
被削材:S40C(形状:円柱)
切削速度:200m/min
切り込み:2.0mm
送り量:0.25mm/rev
雰囲気:湿式切削
寿命の判定基準:欠損したとき、または、最大逃げ面摩耗量VBmaxが0.3mm以上になったときを寿命とする。
Claims (21)
- WCからなる第1硬質相と、チタン元素を含む周期表4,5および6族元素の炭化物、窒化物、炭窒化物およびこれらの相互固溶体の少なくとも1種からなる第2硬質相と、鉄族金属を主成分とする結合相とから構成されたサーメットであって、サーメット全体に含有される炭素量CT(重量%)、サーメット全体に含有されるタングステン量CW(重量%)、サーメット全体に含有される窒素量CN(重量%)が、
0.25<(CN/(CT-0.0653・CW))<6
を満足し、
サーメットは、第1硬質相と結合相とからなる平均厚さ5~100μmの表面領域、および表面領域よりも内部に存在する第1硬質相と第2硬質相と結合相とからなる内部領域によって形成され、
サーメットの内部領域の断面組織における、第2硬質相の面積率に対する第1硬質相の面積率の比が0.15~4であることを特徴とするサーメット。 - サーメットの内部領域の断面組織における、結合相の面積率が3~30面積%、第1硬質相の面積率と第2硬質相の面積率との合計が70~97面積%であり、これらの合計が100面積%である請求項1に記載のサーメット。
- サーメットの表面領域の断面組織における、結合相の面積率が3~30面積%、第1硬質相の面積率が70~97面積%であり、これらの合計が100面積%である請求項1または2に記載のサーメット。
- サーメット全体に含まれるCr元素をCr3C2に換算したときのCr3C2量が0.1~10重量%である請求項1~3のいずれか1項に記載のサーメット。
- サーメット全体に含まれるV元素をVCに換算したときのVC量が0.1~5重量%である請求項1~4のいずれか1項に記載のサーメット。
- 第2硬質相が、Ti(C,N)、(Ti,W)(C,N)、(Ti,W,Ta)(C,N)、(Ti,W,Nb)(C,N)、(Ti,W,Ta,Nb)(C,N)、(Ti,W,Nb,Mo,V)(C,N)、(Ti,W,Cr,V)(C,N)、(Ti,W,Nb,Cr,V)(C,N)、(Ti,W,Ta,Nb,Cr,V)(C,N)、(Ti,W,Nb,Cr,Zr)(C,N)、(Ti,W,Cr)(C,N)、(Ti,W,Nb,Cr,Hf)(C,N)、(Ti,W,Ta,Cr)(C,N)及び(Ti,W,Ta,Nb,Cr)(C,N)から選択される少なくとも1種からなる請求項1~5のいずれか1項に記載のサーメット。
- 第2硬質相が、
Ti(C,N)、(Ti,W)(C,N)、(Ti,W,Ta)(C,N)、(Ti,W,Nb)(C,N)、(Ti,W,Ta,Nb)(C,N)、(Ti,W,Nb,Mo,V)(C,N)、(Ti,W,Cr,V)(C,N)、(Ti,W,Nb,Cr,V)(C,N)、(Ti,W,Ta,Nb,Cr,V)(C,N)、(Ti,W,Nb,Cr,Zr)(C,N)、(Ti,W,Cr)(C,N)、(Ti,W,Nb,Cr,Hf)(C,N)、(Ti,W,Ta,Cr)(C,N)、(Ti,W,Ta,Nb,Cr)(C,N)の炭窒化物の少なくとも1種からなる単一相、及び、
Ti(C,N)、(Ti,W)(C,N)、(Ti,W,Ta)(C,N)、(Ti,W,Nb)(C,N)、(Ti,W,Ta,Nb)(C,N)、(Ti,W,Nb,Mo,V)(C,N)、(Ti,W,Cr,V)(C,N)、(Ti,W,Nb,Cr,V)(C,N)、(Ti,W,Ta,Nb,Cr,V)(C,N)、(Ti,W,Nb,Cr,Zr)(C,N)、(Ti,W,Cr)(C,N)、(Ti,W,Nb,Cr,Hf)(C,N)、(Ti,W,Ta,Cr)(C,N)及び(Ti,W,Ta,Nb,Cr)(C,N)の炭窒化物の少なくとも1種からなる芯部(コア)を(Ti,W)(C,N)、(Ti,W,Ta)(C,N)、(Ti,W,Nb)(C,N)、(Ti,W,Ta,Nb)(C,N)、(Ti,W,Nb,Mo,V)(C,N)、(Ti,W,Cr,V)(C,N)、(Ti,W,Nb,Cr,V)(C,N)、(Ti,W,Ta,Nb,Cr,V)(C,N)、(Ti,W,Nb,Cr,Zr)(C,N)、(Ti,W,Cr)(C,N)、(Ti,W,Nb,Cr,Hf)(C,N)、(Ti,W,Ta,Cr)(C,N)及び(Ti,W,Ta,Nb,Cr)(C,N)の炭窒化物の少なくとも1種からなり芯部(コア)とは異なる組成の周辺部(リム)が取り囲む組織構造のコアリム相、
から選択される少なくとも1種からなる請求項1~6のいずれか1項に記載のサーメット。 - CT、CW及びCNが、0.28<(CN/CC)<5
ここで、CC=CT-0.0653・CWである
を満足する請求項1~7のいずれか1項に記載のサーメット。 - CT、CW及びCNが、0.3<(CN/CC)<4.6
ここで、CC=CT-0.0653・CWである
を満足する請求項1~7のいずれか1項に記載のサーメット。 - サーメットの内部領域の断面組織における、結合相の面積率が4~25面積%、第1硬質相の面積率と第2硬質相の面積率との合計が75~96面積%であり、これらの合計が100面積%である請求項1~9のいずれか1項に記載のサーメット。
- サーメットの内部領域の断面組織における、結合相の面積率が5~20面積%、第1硬質相の面積率と第2硬質相の面積率との合計が80~95面積%であり、これらの合計が100面積%である請求項1~9のいずれか1項に記載のサーメット。
- サーメットの表面領域の断面組織における、結合相の面積率が4~25面積%、第1硬質相の面積率が75~96面積%であり、これらの合計が100面積%である請求項1~11のいずれか1項に記載のサーメット。
- サーメットの表面領域の断面組織における、結合相の面積率が5~20面積%、第1硬質相の面積率が80~95面積%であり、これらの合計が100面積%である請求項1~11のいずれか1項に記載のサーメット。
- 第2硬質相の面積%に対する第1硬質相の面積%の比が、0.20~3.8である請求項1~13のいずれか1項に記載のサーメット。
- 第2硬質相の面積%に対する第1硬質相の面積%の比が、0.25~3.5である請求項1~13のいずれか1項に記載のサーメット。
- サーメット全体に含まれるCr元素をCr3C2に換算したときのCr3C2量が、0.15~8重量%である請求項1~15のいずれか1項に記載のサーメット。
- サーメット全体に含まれるV元素をVCに換算したときのVC量が、0.2~4重量%である請求項1~16のいずれか1項に記載のサーメット。
- TiCN粉と、WC粉と、周期表4、5、6族元素の炭化物、窒化物、炭窒化物およびこれらの相互固溶体の粉末と、鉄族金属の粉末とを所定の配合組成となるように混合した混合物を、
(A)非酸化雰囲気で常温から1200~1400℃の第1加熱温度まで昇温させる工程と、
(B)1200~1400℃の第1加熱温度から1420~1600℃の第2加熱温度まで圧力10Torr以上の窒素雰囲気で昇温させる工程と、
(C)1420~1600℃の第2加熱温度にて圧力10Torr以上の窒素雰囲気で保持する工程と、
(D)1420~1600℃の第2加熱温度にて工程(C)よりも低い圧力の窒素雰囲気で保持する工程と、
(E)1420~1600℃の第2加熱温度から常温まで工程(D)よりも低い圧力の窒素雰囲気で冷却する工程と
からなる工程により製造される請求項1~17のいずれか1項に記載のサーメット。 - 請求項1~18のいずれか1項に記載のサーメットの表面に硬質膜を被覆した被覆サーメット。
- 硬質膜が、周期表4、5、6族元素、Al,Siの酸化物、炭化物、窒化物およびこれらの相互固溶体、及び硬質炭素膜からなる群より選択される少なくとも1種の硬質膜からなる請求項19に記載の被覆サーメット。
- 硬質膜が、TiN、TiC、TiCN、TiAlN、TiSiN、AlCrN、Al2O3、ダイヤモンド及びダイヤモンドライクカーボン(DLC)からなる群より選択される少なくとも1種の硬質膜からなる請求項19又は20に記載の被覆サーメット。
Priority Applications (7)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
RU2012103012/02A RU2012103012A (ru) | 2009-06-30 | 2010-06-30 | Металлокерамика и металлокерамика с покрытием |
EP10794176A EP2450136A1 (en) | 2009-06-30 | 2010-06-30 | Cermet and coated cermet |
CN2010800298646A CN102470446A (zh) | 2009-06-30 | 2010-06-30 | 金属陶瓷和被覆金属陶瓷 |
US13/381,316 US20120114960A1 (en) | 2009-06-30 | 2010-06-30 | Cermet and Coated Cermet |
BRPI1011920A BRPI1011920A2 (pt) | 2009-06-30 | 2010-06-30 | cermet e cermet revestido. |
JP2011520946A JPWO2011002008A1 (ja) | 2009-06-30 | 2010-06-30 | サーメットおよび被覆サーメット |
CA2766894A CA2766894A1 (en) | 2009-06-30 | 2010-06-30 | Cermet and coated cermet |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2009155236 | 2009-06-30 | ||
JP2009-155236 | 2009-06-30 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2011002008A1 true WO2011002008A1 (ja) | 2011-01-06 |
Family
ID=43411079
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2010/061122 WO2011002008A1 (ja) | 2009-06-30 | 2010-06-30 | サーメットおよび被覆サーメット |
Country Status (9)
Country | Link |
---|---|
US (1) | US20120114960A1 (ja) |
EP (1) | EP2450136A1 (ja) |
JP (1) | JPWO2011002008A1 (ja) |
KR (1) | KR20120023179A (ja) |
CN (1) | CN102470446A (ja) |
BR (1) | BRPI1011920A2 (ja) |
CA (1) | CA2766894A1 (ja) |
RU (1) | RU2012103012A (ja) |
WO (1) | WO2011002008A1 (ja) |
Cited By (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2013002270A1 (ja) * | 2011-06-27 | 2013-01-03 | 京セラ株式会社 | 硬質合金および切削工具 |
WO2013150603A1 (ja) * | 2012-04-02 | 2013-10-10 | オーエスジー株式会社 | 切削工具用硬質被膜及び硬質被膜被覆切削工具 |
JP2015107525A (ja) * | 2014-12-18 | 2015-06-11 | 住友電気工業株式会社 | 回転ツール |
US9409238B2 (en) | 2012-04-09 | 2016-08-09 | Osg Corporation | Hard coating for cutting tool, and cutting tool coated with hard coating |
JP2019116674A (ja) * | 2017-12-27 | 2019-07-18 | 株式会社タンガロイ | 超硬合金及び被覆超硬合金 |
JP2019151875A (ja) * | 2018-03-01 | 2019-09-12 | 住友電気工業株式会社 | 基材および切削工具 |
JPWO2019138599A1 (ja) * | 2018-01-09 | 2020-10-01 | 住友電工ハードメタル株式会社 | 超硬合金及び切削工具 |
JP7157887B1 (ja) | 2022-03-08 | 2022-10-20 | 日本タングステン株式会社 | 粉砕・撹拌・混合・混練機部材 |
Families Citing this family (30)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20110117368A1 (en) * | 2008-07-16 | 2011-05-19 | Hideaki Matsubara | Hard Powder, Process for Preparing Hard Powder and Sintered Hard Alloy |
JP5559575B2 (ja) | 2009-03-10 | 2014-07-23 | 株式会社タンガロイ | サーメットおよび被覆サーメット |
US8784977B2 (en) | 2009-06-22 | 2014-07-22 | Tungaloy Corporation | Coated cubic boron nitride sintered body tool |
US9279187B2 (en) * | 2009-11-11 | 2016-03-08 | Southwest Research Institute | Method for applying a diffusion barrier interlayer for high temperature components |
US8999531B2 (en) | 2010-04-16 | 2015-04-07 | Tungaloy Corporation | Coated CBN sintered body |
US8673435B2 (en) | 2010-07-06 | 2014-03-18 | Tungaloy Corporation | Coated cBN sintered body tool |
CN102719720B (zh) * | 2011-03-29 | 2015-08-05 | 厦门钨业股份有限公司 | 一种(Ti,Mo,W(Ta,Nb))(C,N)固溶体粉末的制备方法 |
US9511572B2 (en) | 2011-05-25 | 2016-12-06 | Southwest Research Institute | Nanocrystalline interlayer coating for increasing service life of thermal barrier coating on high temperature components |
CN102534335A (zh) * | 2012-01-17 | 2012-07-04 | 四川大学 | 稀土合金粉末改性的Ti(C,N)基金属陶瓷及其制备方法 |
CN103521770B (zh) * | 2013-09-22 | 2015-10-28 | 成都工具研究所有限公司 | TiCN基金属陶瓷 |
EP3120956B1 (en) * | 2014-03-19 | 2018-10-03 | Tungaloy Corporation | Cermet tool |
CN104018017B (zh) * | 2014-05-27 | 2016-02-24 | 南京航空航天大学 | 废旧Ti(C,N)基金属陶瓷材料的回收与再生方法 |
CN104164594A (zh) * | 2014-07-07 | 2014-11-26 | 马鞍山市万鑫铸造有限公司 | 一种led灯具用耐温防吸胀铝基复合散热材料 |
GB2528272B (en) * | 2014-07-15 | 2017-06-21 | Tokamak Energy Ltd | Shielding materials for fusion reactors |
JP5989930B1 (ja) * | 2014-11-27 | 2016-09-07 | 京セラ株式会社 | サーメットおよび切削工具 |
JP6439975B2 (ja) * | 2015-01-16 | 2018-12-19 | 住友電気工業株式会社 | サーメットの製造方法 |
JP6090685B1 (ja) * | 2015-06-12 | 2017-03-08 | 株式会社タンガロイ | 超硬合金および被覆超硬合金 |
WO2017147510A1 (en) * | 2016-02-24 | 2017-08-31 | Saint-Gobain Abrasives, Inc. | Abrasive articles including a coating and methods for forming the same |
AT15139U1 (de) * | 2016-03-11 | 2017-01-15 | Ceratizit Austria Gmbh | Zerspanungswerkzeug |
US20180010219A1 (en) * | 2016-04-21 | 2018-01-11 | Jeong-su Song | Method of manufacturing hard metal composition for precious metal |
CN107923006B (zh) * | 2016-05-02 | 2019-08-30 | 住友电气工业株式会社 | 硬质合金和切削工具 |
WO2020070978A1 (ja) * | 2018-10-04 | 2020-04-09 | 住友電工ハードメタル株式会社 | 超硬合金、それを含む切削工具および超硬合金の製造方法 |
CN112877578A (zh) * | 2019-11-29 | 2021-06-01 | 株洲钻石切削刀具股份有限公司 | 超细晶粒硬质合金及其制备方法 |
CN114901846B (zh) * | 2020-04-15 | 2023-06-30 | 住友电工硬质合金株式会社 | 硬质合金以及包含该硬质合金的切削工具 |
CN111663093B (zh) * | 2020-06-05 | 2022-07-26 | 广东电网有限责任公司 | 一种金属陶瓷材料、一种金属陶瓷涂层及其制备方法 |
CN112247142B (zh) * | 2020-10-21 | 2022-07-26 | 九江学院 | 一种具有核壳结构的双硬质相双粘结相金属碳化物陶瓷粉末及其制备方法 |
CN112680646B (zh) * | 2020-12-03 | 2022-05-06 | 三峡大学 | 具有高熵合金粘结相的TiC基金属陶瓷的制备方法 |
CN112962008A (zh) * | 2021-01-29 | 2021-06-15 | 嘉兴鸷锐新材料科技有限公司 | 一种Ti(C,N)基金属陶瓷工具及其制备方法 |
CN113232380B (zh) * | 2021-04-30 | 2023-03-28 | 咸阳职业技术学院 | 一种高强高韧层状互通结构钢结硬质合金及其制备方法 |
CN114150198A (zh) * | 2021-11-19 | 2022-03-08 | 四川一然新材料科技有限公司 | 低密度金属陶瓷材料制备方法及低密度金属陶瓷零件 |
Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS62193731A (ja) * | 1986-02-18 | 1987-08-25 | Mitsubishi Metal Corp | 耐摩耗性のすぐれたサ−メツト製切削工具の製造法 |
JPH0215139A (ja) * | 1988-03-11 | 1990-01-18 | Kyocera Corp | TiCN基サーメットおよびその製法 |
JPH07316716A (ja) * | 1994-05-19 | 1995-12-05 | Sumitomo Electric Ind Ltd | 窒素含有焼結硬質合金 |
JP2001502249A (ja) * | 1996-10-11 | 2001-02-20 | サンドビック アクティエボラーグ | 結合相富化した表面領域を有する超硬合金の製造方法 |
Family Cites Families (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS61195950A (ja) * | 1985-02-25 | 1986-08-30 | Mitsubishi Metal Corp | 高硬度および高靭性を有する切削工具用サ−メツト |
JPS62265107A (ja) * | 1985-10-14 | 1987-11-18 | Sumitomo Electric Ind Ltd | 硬質合金用複炭窒化物の製造法 |
US6057046A (en) * | 1994-05-19 | 2000-05-02 | Sumitomo Electric Industries, Ltd. | Nitrogen-containing sintered alloy containing a hard phase |
KR100792190B1 (ko) * | 2005-04-19 | 2008-01-07 | 재단법인서울대학교산학협력재단 | 유심구조가 없는 고용체 분말, 그 제조 방법, 상기 고용체분말을 포함하는 서멧트용 분말, 그 제조 방법, 상기고용체 분말 및 서멧트용 분말을 이용한 유심구조가 없는세라믹스 소결체 및 서멧트 |
-
2010
- 2010-06-30 RU RU2012103012/02A patent/RU2012103012A/ru not_active Application Discontinuation
- 2010-06-30 CA CA2766894A patent/CA2766894A1/en not_active Abandoned
- 2010-06-30 KR KR1020127000455A patent/KR20120023179A/ko not_active Application Discontinuation
- 2010-06-30 WO PCT/JP2010/061122 patent/WO2011002008A1/ja active Application Filing
- 2010-06-30 CN CN2010800298646A patent/CN102470446A/zh active Pending
- 2010-06-30 BR BRPI1011920A patent/BRPI1011920A2/pt not_active IP Right Cessation
- 2010-06-30 JP JP2011520946A patent/JPWO2011002008A1/ja active Pending
- 2010-06-30 US US13/381,316 patent/US20120114960A1/en not_active Abandoned
- 2010-06-30 EP EP10794176A patent/EP2450136A1/en not_active Withdrawn
Patent Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS62193731A (ja) * | 1986-02-18 | 1987-08-25 | Mitsubishi Metal Corp | 耐摩耗性のすぐれたサ−メツト製切削工具の製造法 |
JPH0215139A (ja) * | 1988-03-11 | 1990-01-18 | Kyocera Corp | TiCN基サーメットおよびその製法 |
JPH07316716A (ja) * | 1994-05-19 | 1995-12-05 | Sumitomo Electric Ind Ltd | 窒素含有焼結硬質合金 |
JP2001502249A (ja) * | 1996-10-11 | 2001-02-20 | サンドビック アクティエボラーグ | 結合相富化した表面領域を有する超硬合金の製造方法 |
Cited By (16)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US9228252B2 (en) | 2011-06-27 | 2016-01-05 | Kyocera Corporation | Hard alloy and cutting tool |
EP2725111A4 (en) * | 2011-06-27 | 2015-07-22 | Kyocera Corp | HARD ALLOY AND CUTTING TOOL |
CN103635599A (zh) * | 2011-06-27 | 2014-03-12 | 京瓷株式会社 | 硬质合金及切削工具 |
JPWO2013002270A1 (ja) * | 2011-06-27 | 2015-02-23 | 京セラ株式会社 | 硬質合金および切削工具 |
WO2013002270A1 (ja) * | 2011-06-27 | 2013-01-03 | 京セラ株式会社 | 硬質合金および切削工具 |
WO2013150603A1 (ja) * | 2012-04-02 | 2013-10-10 | オーエスジー株式会社 | 切削工具用硬質被膜及び硬質被膜被覆切削工具 |
JPWO2013150603A1 (ja) * | 2012-04-02 | 2015-12-14 | オーエスジー株式会社 | 切削工具用硬質被膜及び硬質被膜被覆切削工具 |
CN104203466A (zh) * | 2012-04-02 | 2014-12-10 | Osg株式会社 | 切削工具用硬质被膜及硬质被膜被覆切削工具 |
US9409238B2 (en) | 2012-04-09 | 2016-08-09 | Osg Corporation | Hard coating for cutting tool, and cutting tool coated with hard coating |
JP2015107525A (ja) * | 2014-12-18 | 2015-06-11 | 住友電気工業株式会社 | 回転ツール |
JP2019116674A (ja) * | 2017-12-27 | 2019-07-18 | 株式会社タンガロイ | 超硬合金及び被覆超硬合金 |
JPWO2019138599A1 (ja) * | 2018-01-09 | 2020-10-01 | 住友電工ハードメタル株式会社 | 超硬合金及び切削工具 |
JP2019151875A (ja) * | 2018-03-01 | 2019-09-12 | 住友電気工業株式会社 | 基材および切削工具 |
JP7013948B2 (ja) | 2018-03-01 | 2022-02-01 | 住友電気工業株式会社 | 基材および切削工具 |
JP7157887B1 (ja) | 2022-03-08 | 2022-10-20 | 日本タングステン株式会社 | 粉砕・撹拌・混合・混練機部材 |
JP2023130938A (ja) * | 2022-03-08 | 2023-09-21 | 日本タングステン株式会社 | 粉砕・撹拌・混合・混練機部材 |
Also Published As
Publication number | Publication date |
---|---|
US20120114960A1 (en) | 2012-05-10 |
JPWO2011002008A1 (ja) | 2012-12-13 |
RU2012103012A (ru) | 2013-08-10 |
CA2766894A1 (en) | 2011-01-06 |
KR20120023179A (ko) | 2012-03-12 |
CN102470446A (zh) | 2012-05-23 |
EP2450136A1 (en) | 2012-05-09 |
BRPI1011920A2 (pt) | 2016-04-19 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
WO2011002008A1 (ja) | サーメットおよび被覆サーメット | |
JP6703757B2 (ja) | サーメット、及び切削工具 | |
JP5454678B2 (ja) | サーメットおよび被覆サーメット | |
JP5652113B2 (ja) | 耐熱合金の切削加工で優れた耐欠損性を発揮するwc基超硬合金製切削工具および表面被覆wc基超硬合金製切削工具 | |
JP5559575B2 (ja) | サーメットおよび被覆サーメット | |
JP2010517792A (ja) | Ti基サーメット | |
JP7272353B2 (ja) | 超硬合金、切削工具および超硬合金の製造方法 | |
JP2011235410A (ja) | 耐熱合金の切削加工で優れた耐欠損性を発揮するwc基超硬合金製切削工具および表面被覆wc基超硬合金製切削工具 | |
WO2011065468A1 (ja) | 回転工具 | |
JP2012086297A (ja) | 高速断続切削加工ですぐれた耐チッピング性と耐摩耗性を発揮するwc基超硬合金製切削工具 | |
JP5381616B2 (ja) | サーメットおよび被覆サーメット | |
JP5063129B2 (ja) | サーメット | |
JP4069749B2 (ja) | 荒加工用切削工具 | |
JP7035820B2 (ja) | 基材および切削工具 | |
JP2010253607A (ja) | 切削工具 | |
JP2011088253A (ja) | 耐熱塑性変形性に優れたwc基超硬合金製切削工具および表面被覆wc基超硬合金製切削工具 | |
JP5644388B2 (ja) | サーメットおよび被覆サーメット | |
JP5233124B2 (ja) | 超硬合金および被覆超硬合金 | |
JP6380016B2 (ja) | サーメット工具および被覆サーメット工具 | |
WO2015141757A1 (ja) | サーメット工具 | |
JP4126451B2 (ja) | 超硬合金 | |
JP3762278B2 (ja) | 超硬合金およびその製造方法 | |
JP7170965B2 (ja) | 超硬合金及び被覆超硬合金 | |
JP2014077178A (ja) | サーメットおよび被覆サーメット | |
JP7473871B2 (ja) | 耐摩耗性および耐欠損性にすぐれたwc基超硬合金製切削工具および表面被覆wc基超硬合金製切削工具 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
WWE | Wipo information: entry into national phase |
Ref document number: 201080029864.6 Country of ref document: CN |
|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 10794176 Country of ref document: EP Kind code of ref document: A1 |
|
ENP | Entry into the national phase |
Ref document number: 2011520946 Country of ref document: JP Kind code of ref document: A |
|
WWE | Wipo information: entry into national phase |
Ref document number: 10263/DELNP/2011 Country of ref document: IN |
|
WWE | Wipo information: entry into national phase |
Ref document number: 13381316 Country of ref document: US Ref document number: 2766894 Country of ref document: CA |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
ENP | Entry into the national phase |
Ref document number: 20127000455 Country of ref document: KR Kind code of ref document: A |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2012103012 Country of ref document: RU Ref document number: 2010794176 Country of ref document: EP |
|
REG | Reference to national code |
Ref country code: BR Ref legal event code: B01A Ref document number: PI1011920 Country of ref document: BR |
|
ENP | Entry into the national phase |
Ref document number: PI1011920 Country of ref document: BR Kind code of ref document: A2 Effective date: 20111228 |