CN111455206B - Method for manufacturing hard alloy by rapid semi-solid hot pressing - Google Patents
Method for manufacturing hard alloy by rapid semi-solid hot pressing Download PDFInfo
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- 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
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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
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
- B22F3/14—Both compacting and sintering simultaneously
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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
- C22C29/06—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
- C22C29/067—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 comprising a particular metallic binder
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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
- C22C29/06—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
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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
- C22C29/06—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
- C22C29/10—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 titanium carbide
Abstract
The invention relates to a method for manufacturing hard alloy by rapid semi-solid hot pressing. Firstly, accurately calculating the thickness of the hard alloy powder when the hard alloy powder is completely compact; then, placing the hard alloy powder into an inner cavity of a hot-pressing die, inserting a pressure head into the inner cavity of the hot-pressing die, vacuumizing a working chamber of a hot-pressing machine or filling inert protective gas after vacuumizing, and quickly heating the hard alloy powder in the hot-pressing die to a high temperature corresponding to a certain liquid phase; and finally, the pressing head descends rapidly to axially press the hard alloy powder, when the thickness of the hard alloy powder is slightly smaller than the calculated thickness when the hard alloy powder is completely compact, the descending of the pressing head is immediately stopped, the pressing of the pressing head is stopped, and the heating of the hard alloy powder is stopped at the same time, so that the manufacture of the hard alloy is completed. The hard alloy manufactured by the invention has fine hard phase, high density, high hardness, wear resistance and toughness, and avoids the contact between the hard phases; the production process has short time, saves energy and reduces production cost.
Description
Technical Field
The invention relates to the field of hard alloy manufacturing, in particular to a method for manufacturing hard alloy by rapid semi-solid hot pressing.
Background
The hard alloy is a cermet material formed by using metal or alloy as a binder (binder phase) and combining hard compounds (hard phase) of refractory metals, has the outstanding advantages of high hardness and high wear resistance, is widely used for manufacturing cutting tools, impact tools and wear-resistant and corrosion-resistant parts, and becomes an indispensable tool and die material in the fields of machining, geological exploration, mining, oil drilling, die manufacturing and the like. Although the hard phases and binder phases that make up cemented carbides vary, liquid phase sintering by powder metallurgy is used industrially to make cemented carbides: the method comprises the following steps of heating a pressed blank of a mixture of hard phase powder and binder phase powder (hard alloy powder) to a temperature at which a part of liquid phase appears, preserving heat for a certain time, rotating and rearranging the rest solid phase to the most compact arrangement under the action of capillary force of the liquid phase, and filling the rest pores with the liquid phase to achieve complete densification. The heat preservation is carried out for a long time at the temperature of the existence of the liquid phase, the hard phase grows up obviously, and the hardness, the wear resistance and the toughness of the hard alloy are reduced. To solve this problem, studies are currently being conducted on solid state hot pressing or solid state hot isostatic pressing for consolidating cemented carbide powders. Solid hot pressing or solid hot isostatic pressing reduces the consolidation temperature and thus the growth of hard phases, and although no liquid phase is present, the application of pressure allows the cemented carbide powder to be fully densified, while the absence of liquid phase also allows direct contact between hard phases in some areas, which are difficult to form a metallurgical bond, resulting in a reduction in the toughness of the cemented carbide. In recent years, much research has been conducted on spark plasma sintering of cemented carbide powders. Compared with solid hot pressing or solid hot isostatic pressing, the combined action of the discharge plasma and the axial pressure in the discharge plasma sintering process further reduces the consolidation temperature, shortens the consolidation time to several minutes to dozens of minutes, further weakens the growth of a hard phase, and although the thin layer on the surface of the powder of the binder phase is instantaneously melted due to the high temperature generated by spark discharge among the powder in the discharge plasma sintering process, the instantaneously existing trace liquid phase cannot infiltrate the whole surface of the hard phase, so that some direct contact among the hard phases still exists, and the toughness of the hard alloy is reduced.
Disclosure of Invention
Aiming at the problems in the prior art, the invention provides a method for manufacturing hard alloy by rapid semi-solid hot pressing.
The method for manufacturing the hard alloy by rapid semi-solid hot pressing comprises the following steps:
a precise calculation of the thickness of the cemented carbide powder when fully densified:
accurately calculating the thickness of the hard alloy powder when the hard alloy powder is completely compact according to the geometric shape of the inner cavity of the hot pressing die, the weight of the hard alloy powder and the theoretical density of the hard alloy;
b, axially hot-pressing hard alloy powder:
b, placing the hard alloy powder with the weight in the step a into an inner cavity of a hot-pressing die, inserting a pressing head into the inner cavity, and placing a combined body formed by the hot-pressing die, the hard alloy powder and the pressing head into a working chamber of a hot press; vacuumizing the working chamber of the hot press or filling inert protective gas after vacuumizing, and then quickly heating the hard alloy powder to a preset high temperature, wherein the temperature range of the high temperature is the temperature corresponding to a liquid phase containing a certain volume fraction in the hard alloy powder; and c, after the hard alloy powder is heated to a preset high temperature, enabling a pressure head to descend to axially press the hard alloy powder, gradually increasing the relative density of a hard alloy powder consolidation body under the combined action of the axial pressure and the lateral pressure of the inner cavity wall of the hot-pressing die, and immediately stopping descending the pressure head and pressurizing the pressure head when the thickness of the hard alloy powder is slightly less than the thickness of the hard alloy powder when the hard alloy powder is completely compacted, namely the actual descending distance of the pressure head is slightly greater than the corresponding descending distance of the pressure head when the hard alloy powder is completely compacted, and simultaneously stopping heating the hard alloy powder to finish the manufacture of the hard alloy. The purpose of the slightly larger downward distance of the pressure head is to ensure the complete compactness of the hard alloy powder, and the hard alloy powder extruded by the slightly larger downward distance of the pressure head is discharged from a gap between the inner cavity wall of the hot-pressing die and the pressure head.
Preferably, the hard phase of the cemented carbide powder is WC, or a mixture of WC and TiC, or a mixture of TaC and NbC, or a mixture of TiC, TaC and NbC, and the binder phase is Co, or Ni, or a mixture of Ni and Fe.
Preferably, the hard alloy powder is steel bonded hard alloy powder, and the hard phase is TiC, WC, VC, TiN, TiCN, or TiB2Or TiC and Al2O3Mixtures, or TiB2The bonding phase of the TiC-containing alloy is chromium-molybdenum steel with 0.5-1.5% of Cr, 0.2-2.5% of Mo and 0.2-0.5% of C, or high-manganese steel with more than or equal to 7% of Mn and more than or equal to 0.6% of C, or high-chromium steel with more than or equal to 6% of Cr and more than or equal to 0.4% of C, or high-speed steel or stainless steel, and the Cr, Mo, C and Mn contents are in percentage by weight.
Preferably, the high temperature is in a temperature range corresponding to 5-30% volume fraction of liquid phase in the cemented carbide powder.
Preferably, the heating rate is 20-30 ℃/min.
Preferably, the descending speed is 1-4 mm/s.
Preferably, the width of the gap between the inner cavity wall of the hot-pressing die and the pressure head is 0.05-0.1 mm.
Preferably, the system pressure of the vacuumizing is 1X 10-2-9×10-2Pa; the inert protective gas is nitrogen, argon or helium, and the pressure is 0.05-0.1 MPa.
Preferably, the downward movement of the pressure head is stopped and the pressure head is stopped when the thickness of the hard alloy powder is 2-5% less than the thickness of the hard alloy powder when the hard alloy powder is fully dense, which is accurately calculated in the step a.
The method comprises the steps of quickly heating the hard alloy powder to a preset high temperature, then quickly descending a pressure head in a working chamber of a hot press, applying axial pressure to the hard alloy powder heated to the semi-solid temperature in a hot press die until the hard alloy powder is completely compact, immediately stopping heating and pressurizing, and carrying out quick semi-solid hot pressing to manufacture the hard alloy. Compared with the prior art, the method has the following advantages:
1. in the invention, the existence of the liquid phase and the combined action of the pressure promote the complete densification of the hard alloy, and the relative density higher than that of liquid phase sintering can be obtained. Furthermore, the characteristics of fine hard phase and high relative density of the invention result in that the hard alloy prepared by the invention has higher hardness, wear resistance and toughness than the hard alloy prepared by the liquid phase sintering method.
2. Compared with solid state hot pressing, solid state hot isostatic pressing and spark plasma sintering, the hard alloy of the present invention has no direct contact between hard phases and thus greatly raised toughness.
3. Compared with liquid phase sintering, solid state hot pressing and solid state hot isostatic pressing, the time of the manufacturing process is greatly shortened (from several hours to dozens of minutes), and the energy consumption and the production cost of the manufacturing are reduced.
Drawings
FIG. 1 is an optical microscope photograph of WC-8Co (weight percent) cemented carbide made with the present invention in example 1;
FIG. 2 is the hardness test results for WC-8Co (weight percent) cemented carbide made according to the invention in example 1;
FIG. 3 is the results of a three-point flexural strength test of WC-8Co (weight percent) cemented carbide made in accordance with the present invention in example 1;
FIG. 4 is an optical microscope photograph of WC-8Co (weight percent) cemented carbide made by liquid phase sintering as a comparison in example 1;
example 1
The present example was aimed at producing WC-8Co (weight percent) cemented carbide with a hard phase of WC and a binder phase of Co using the method of the present invention. The inner cavity of the hot-pressing die is a cylinder with the diameter of 43.5 mm, and the gap between the corresponding cylindrical pressure head and the wall of the inner cavity of the hot-pressing die is 0.08 mm. The weight of WC-8Co (weight percent) cemented carbide powder obtained by mixing WC powder and Co powder was 515.6 g, which was 14.7 g/cm based on the theoretical density of WC-8Co (weight percent) cemented carbide3The thickness of the cemented carbide powder when fully densified was accurately calculated to be 23.6 mm. After 515.6 g of WC-8Co (weight percent) hard alloy powder is placed in an inner cavity of a hot-pressing die, a pressure head is inserted into the inner cavity of the hot-pressing die, the pressure head freely falls to contact the hard alloy powder, and the thickness of the hard alloy powder, namely the distance from the lower surface of the pressure head to the bottom of the hot-pressing die (the height of a cavity of the hot-pressing die, the length of the pressure head exposed out of the hot-pressing die and the total length of the pressure head) is 67.5 mm. Putting a combined body consisting of a hot-pressing die, hard alloy powder and a pressing head into a working chamber of a hot press; vacuumizing the working chamber of the hot press to 5 x 10-2Pa, followed by rapid heating of the cemented carbide powder from room temperature about 25 ℃ to 13 ℃ at a rate of 30 ℃/minAnd at the temperature of 40 ℃, the volume fraction of the liquid phase is about 17%, a pressure head is enabled to move downwards at 3 mm/s to axially press the hard alloy powder, and the relative density of the hard alloy powder solidified body is gradually increased under the combined action of the axial pressure and the lateral pressure of the inner cavity wall of the hot-pressing die. When the pressing head descends 44.6 mm, namely the thickness of the hard alloy powder is 22.9 mm and is less than 23.6 mm of the thickness of the hard alloy powder when the hard alloy powder is completely dense by about 3%, the hard alloy powder with the diameter of 43.5 mm and the thickness of 0.7 mm is extruded out from a gap between the inner cavity wall of the hot pressing die and the pressing head, and then the descending of the pressing head is immediately stopped, the pressing of the pressing head is stopped, and meanwhile, the heating of the hard alloy powder is stopped, so that the manufacture of the hard alloy is completed. The heating and pressurization were stopped for about 44 minutes from the start of the temperature rise.
The WC-8Co (weight percent) cemented carbide produced according to the invention was subjected to a density test and found to be 14.688 g/cm3And the relative density is 99.92%. Optical microscopy of the microstructure see fig. 1, the mean size of the hard phase WC particles is about 6 μm. The hardness of the test is shown in FIG. 2, and the average hardness HRA87.9 is calculated. According to a three-point bending stress-bending displacement graph tested by the national standard GB/T232-2010 shown in figure 3, when the bending displacement is maximum, namely when the bending is broken, the corresponding bending stress is the three-point bending strength, and the average value of the three-point bending strength of the three tests is calculated to be about 1100 MPa.
For comparison, WC-8Co (weight percent) cemented carbide was made by liquid phase sintering from the same cemented carbide powder. The experimental results show that the sintering temperature capable of achieving the highest relative density is 1550 ℃, and the shortest holding time is 3 hours. Vacuumizing the working chamber of the vacuum sintering furnace to 5 x 10-2Pa, heating the cemented carbide powder from room temperature of 25 ℃ to 1550 ℃ at a rate of 30 ℃/min, keeping the temperature for 3 hours, and stopping heating to finish the manufacture of the cemented carbide. In this case, the liquid phase sintering was carried out for about 3 hours and 51 minutes from the start of the temperature rise to the stop of the heating; according to the above description, in the production method of the present invention, the heating and pressurizing are stopped for about 44 minutes from the start of the temperature rise; the manufacturing method of the invention and the liquid phase sintering have about the same vacuumizing time before heating, and the manufacturing is completedThe time for cooling down to room temperature in the manufacturing method of the present invention is shorter than that in liquid phase sintering (the cooling start temperature 1340 c of the manufacturing method of the present invention is lower than that in liquid phase sintering 1550 c), so that the manufacturing method of the present invention greatly shortens the manufacturing time according to the above analysis.
The WC-8Co (weight percent) cemented carbide produced by liquid phase sintering as described above was subjected to a density test and the result was 14.5927 g/cm3The relative density is 99.27%, which is the highest density achievable by liquid phase sintering, and is less than 99.92% of the inventive process. Optical microscopy of the microstructure see fig. 4, with the mean size of the hard phase WC particles being about 9 μm. The average hardness of the test is about HRA85.8, and the average three-point bending strength is about 990MPa, which is lower than that of the hard alloy prepared by the method.
Example 2
The object of this example is to produce a 50TiC-50Cr12MoV (weight percent) steel cemented carbide with TiC as the hard phase and high chromium steel Cr12MoV (Fe-1.6C-12Cr-0.5Mo-0.2V, weight percent) as the binder phase by the method of the invention. The inner cavity of the hot-pressing die is a prism, the size of the cross section is a square with a 90-degree fillet, the radius of the fillet is 5 mm, the length of each side without a circular arc is 40 mm, and the cross section area can be calculated to be 2479 square mm; the gap between the corresponding prismatic pressure head and the inner cavity wall of the hot-pressing die is 0.05 mm. The weight of 50TiC-50Cr12MoV (weight percent) steel bond hard alloy powder obtained by mixing the Cr12MoV powder and the TiC powder is 600 g, and the theoretical density of the 50TiC-50Cr12MoV (weight percent) steel bond hard alloy is 6.06 g/cm3And accurately calculating the thickness of the steel bonded hard alloy powder when the powder is completely compact to be 39.9 mm. After 600 g of 50TiC-50Cr12MoV (weight percentage) steel bond hard alloy powder is placed in an inner cavity of a hot-pressing die, a pressure head is inserted into the inner cavity of the hot-pressing die, the pressure head freely falls to contact the steel bond hard alloy powder, and the thickness of the steel bond hard alloy powder, namely the distance from the lower surface of the pressure head to the bottom of the hot-pressing die (the height of a cavity of the hot-pressing die, the length of the pressure head exposed out of the hot-pressing die and the total length of the pressure head) is 99.8 mm. The hot-pressing die, the steel bond hard alloy powder and the pressure head are formedThe assembly of (1) is placed in a working chamber of a hot press; vacuumizing the working chamber of the hot press to 1 × 10-2And (2) filling argon gas to a pressure of 0.07MPa after Pa, then rapidly heating the steel bond hard alloy powder to 1265 ℃ from room temperature of 25 ℃ at a speed of 25 ℃/min, wherein the steel bond hard alloy powder contains about 10% of liquid phase by volume fraction, enabling a pressure head to descend at 4 mm/s to axially press the steel bond hard alloy powder, and gradually increasing the relative density of a steel bond hard alloy powder solidified body under the combined action of axial pressure and lateral pressure of the inner cavity wall of a hot-pressing die. And when the pressing head descends 61.9 mm, namely the thickness of the steel bond hard alloy powder is 37.9 mm and is less than about 5% of the thickness of the steel bond hard alloy powder when the steel bond hard alloy powder is fully compacted by 39.9 mm, immediately stopping descending the pressing head and pressurizing the pressing head, and simultaneously stopping heating the steel bond hard alloy powder to finish the manufacturing of the steel bond hard alloy. Steel bond cemented carbide powder having a thickness of about 2 mm and a weight of about 30 g was extruded from the gap between the inner cavity wall of the hot press die and the ram. The heating and pressurization were stopped for about 50 minutes from the start of the temperature rise.
The 50TiC-50Cr12MoV (weight percentage) steel bonded hard alloy manufactured by the invention is subjected to a density test, and the result is 6.0425 g/cm3And the relative density is 99.71 percent. The average size of the TiC particles of the hard phase was observed by optical microscopy to be about 3 μm. After the steel bonded hard alloy is quenched at 1030 ℃ and tempered at 530 ℃, the tested average hardness is about HRA73.3, and the average three-point bending strength is 1400 MPa.
For comparison, steel bonded cemented carbide was manufactured by liquid phase sintering using the same steel bonded cemented carbide powder. The experimental result shows that the sintering process capable of obtaining the highest relative density is that the sintering temperature is 1350 ℃ and the heat preservation time is 2 hours. Vacuumizing the working chamber of the vacuum sintering furnace to 1 x 10-2And (3) introducing argon to the pressure of 0.07MPa after Pa, then heating the steel bond hard alloy powder from the room temperature of 25 ℃ to the sintering temperature of 1350 ℃ at the speed of 25 ℃/min, preserving the heat for 2 hours, and stopping heating to finish the manufacture of the steel bond hard alloy. In this case, the liquid phase sintering was carried out for about 2 hours and 53 minutes from the start of the temperature rise to the stop of the heating; in light of the foregoing description, forThe manufacturing method of the present invention comprises heating and pressurizing for about 50 minutes from the start of temperature rise to the stop of heating and pressurizing; the time for vacuumizing and argon filling before heating is about the same as the time for liquid phase sintering, and the time for cooling to room temperature after completion of the manufacturing method of the present invention is shorter than that for liquid phase sintering (the cooling start temperature 1265 ℃ of the manufacturing method of the present invention is lower than the cooling start temperature 1350 ℃ of the liquid phase sintering), so the manufacturing method of the present invention greatly shortens the manufacturing time according to the above analysis.
The above 50TiC-50Cr12MoV (weight percent) steel bonded cemented carbide manufactured by liquid phase sintering was subjected to density test and the result was 5.96 g/cm3The relative density is 98.35%, which is the highest density achievable by liquid phase sintering, and is less than 99.71% of the method of the present invention. The average size of the TiC particles of the hard phase was observed by optical microscopy to be about 5.5 μm. After the steel bonded hard alloy is quenched at 1030 ℃ and tempered at 530 ℃, the tested average hardness is about HRA71.2, and the average three-point bending strength is 1200MPa, which is lower than the average hardness and the average three-point bending strength of the steel bonded hard alloy.
Claims (3)
1. A method for manufacturing hard alloy by rapid semi-solid hot pressing is characterized in that: the method comprises the following steps:
a precise calculation of the thickness of the cemented carbide powder when fully densified:
accurately calculating the thickness of the hard alloy powder when the hard alloy powder is completely compact according to the geometric shape of the inner cavity of the hot pressing die, the weight of the hard alloy powder and the theoretical density of the hard alloy;
b, axially hot-pressing hard alloy powder:
b, placing the hard alloy powder with the weight in the step a into an inner cavity of a hot-pressing die, inserting a pressing head into the inner cavity, and placing a combined body formed by the hot-pressing die, the hard alloy powder and the pressing head into a working chamber of a hot press; vacuumizing the working chamber of the hot press or filling inert protective gas after vacuumizing, and then quickly heating the hard alloy powder to a preset high temperature, wherein the temperature range of the high temperature is corresponding to a liquid phase containing 5-30% of volume fraction in the hard alloy powder; b, after the hard alloy powder is heated to a preset high temperature, enabling a pressure head to descend to axially press the hard alloy powder, and when the thickness of the hard alloy powder is slightly smaller than the thickness of the hard alloy powder which is accurately calculated in the step a and is completely compact, immediately stopping descending the pressure head and pressurizing the pressure head, and simultaneously stopping heating the hard alloy powder to finish the manufacture of the hard alloy;
the heating rate is 20-30 ℃/min;
the descending speed is 1-4 mm/s;
when the thickness of the hard alloy powder descends to a position 2% -5% less than the thickness of the hard alloy powder when the hard alloy powder is completely compact, which is accurately calculated in the step a, the descending of the pressure head is stopped, and the pressure head is stopped to be pressurized;
the hard phase of the hard alloy powder is WC, or a mixture of WC and TiC, or a mixture of TaC and NbC, or a mixture of TiC, TaC and NbC, and the binding phase is Co, or Ni, or a mixture of Ni and Fe;
or the hard alloy powder is steel bonded hard alloy powder, and the hard phase is TiC, WC, VC, TiN, TiCN, or TiB2Or TiC and Al2O3Mixtures, or TiB2The bonding phase of the TiC-containing alloy is chromium-molybdenum steel with 0.5-1.5% of Cr, 0.2-2.5% of Mo and 0.2-0.5% of C, or high-manganese steel with more than or equal to 7% of Mn and more than or equal to 0.6% of C, or high-chromium steel with more than or equal to 6% of Cr and more than or equal to 0.4% of C, or high-speed steel or stainless steel, and the Cr, Mo, C and Mn contents are in percentage by weight.
2. The method of claim 1, wherein: the width of a gap between the inner cavity wall of the hot-pressing die and the pressure head is 0.05-0.1 mm.
3. The method of claim 1, wherein: the pressure of the vacuumized system is 1 x 10-2-9×10- 2Pa, the inert protective gas is nitrogen, argon or helium,the pressure is 0.05-0.1 MPa.
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