CN110923535A - Hard alloy and preparation method and application thereof - Google Patents
Hard alloy and preparation method and application thereof Download PDFInfo
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- CN110923535A CN110923535A CN201911289350.3A CN201911289350A CN110923535A CN 110923535 A CN110923535 A CN 110923535A CN 201911289350 A CN201911289350 A CN 201911289350A CN 110923535 A CN110923535 A CN 110923535A
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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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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23B—TURNING; BORING
- B23B51/00—Tools for drilling machines
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23C—MILLING
- B23C5/00—Milling-cutters
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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
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
Abstract
The invention provides a hard alloy which comprises the following components or consists of the following components: 12-15 wt% of cobalt; 0 wt% -0.5 wt% of vanadium carbide; 0.8 to 2.0 weight percent of chromium carbide; 82.5 wt% -87.2 wt% of tungsten carbide. The invention adopts high content Co and proper amount Cr3C2And VC is used as a grain growth inhibitor, so that the stability of a WC/Co interface of the alloy is ensured to obtain good toughness and strength, and the granularity of WC grains can be controlled within a certain range to ensure sufficient wear resistance. The end mill and the drill made of the submicron fine grain hard alloy bar have the advantages of wear resistance, obdurability, high efficiency and high strength stainless steel used in the field of cutting aviation titanium alloy and 3cThe service life of the device can especially meet the requirement of modern high-efficiency processing on large-feed working conditions.
Description
Technical Field
The invention relates to the field of hard alloy, in particular to hard alloy and a preparation method and application thereof.
Background
The WC-Co hard alloy with submicron grain and superfine grain has high hardness, toughness and strength, and may be used widely in metal machining, metal forming tool and wear-resisting part. In practice, hardness, strength and toughness must be reasonably matched to maximize the life of cemented carbide tools. Particularly, for the cutting processing of some metal materials which are difficult to process, such as titanium alloy, high-temperature alloy and stainless steel, the hard alloy bar which is used as the material of the solid milling cutter needs to have excellent hardness, strength and toughness at the same time, and the excellent hardness, the strength and the toughness are mainly realized by means of adjusting the grain size of WC (wolfram carbide) in the hard alloy, the content of Co (cobalt) in the hard alloy, optimizing a WC/Co interface and the like.
Titanium alloy and stainless steel which are used in a large amount in modern aviation industry have the characteristics of high strength, work hardening and the like, and cutting machining of the titanium alloy and the stainless steel needs cutter materials to have good strength and toughness on the premise of ensuring certain wear resistance so as to ensure the integrity of a cutting edge. At present, the cutting tool for processing titanium alloy in the markets at home and abroad is mainly made of hard alloy with the cobalt content of 9-12%, the hardness of the hard alloy is 1650-1800 HV30, the bending strength is more than 4000MPa, and the fracture toughness is 9.5-12 MPam1/2In the meantime.
CN 101812621A discloses a submicron crystal hard alloy, which comprises the components of, by mass, Co 7% -9%, VC 0.1% -0.4%, Cr3C20.2 to 0.5 percent of WC with the balance of 0.7 to 0.9 mu m. The hardness is high (1730-1860 HV3), but the bending strength is low (not less than 4000 MPa). Therefore, the cutting tool is not suitable for cutting high-strength metals such as titanium alloy and the like, and is only suitable for processing cast iron and aluminum alloy.
CN 103710604A mentions a submicron cemented carbide comprising 6.0-13.2 wt% cobalt and 86.3-93.5 wt% tungsten carbide, the average grain size of the cemented carbide is 0.6-1.0 μm. The technical proposal in the patent does not relate to inhibitor Cr3C2And the use of VC. Meanwhile, the preparation method adopts a WC-Co composite powder process, and the process is complex.
JP 2000105395 discloses a submicron grained cemented carbide, but it is used for stainless steel machining applications, has poor strength and toughness, is suitable for cutting inserts, and is not suitable for making solid tools.
Disclosure of Invention
In view of the problems in the prior art, an object of the present invention is to provide a high strength and high toughness cemented carbide, which has improved bending strength and fracture toughness by adjusting the content of each component in the cemented carbide, and is suitable for manufacturing a solid cutting tool.
The second object of the present invention is to provide a method for producing a cemented carbide corresponding to the first object.
A third object of the present invention is to provide a cemented carbide for use in the above-mentioned objects.
In order to achieve one of the above purposes, the technical scheme adopted by the invention is as follows:
a cemented carbide comprising or consisting of:
according to the invention, the cemented carbide comprises cobalt, the content of cobalt being 12-15 wt%.
According to the invention, the cobalt content may be enumerated as 12 wt%, 12.1 wt%, 12.2 wt%, 12.3 wt%, 12.4 wt%, 12.5 wt%, 12.6 wt%, 12.7 wt%, 12.8 wt%, 12.9 wt%, 13 wt%, 13.1 wt%, 13.2 wt%, 13.3 wt%, 13.4 wt%, 13.5 wt%, 13.6 wt%, 13.7 wt%, 13.8 wt%, 13.9 wt%, 14 wt%, 14.1 wt%, 14.2 wt%, 14.3 wt%, 14.4 wt%, 14.5 wt%, 14.6 wt%, 14.7 wt%, 14.8 wt%, 14.9 wt%, 15 wt% and any value therebetween.
According to the invention, the hard alloy comprises vanadium carbide, and the content of the vanadium carbide is 0 wt% -0.5 wt%.
According to the invention, the vanadium carbide content may be cited as 0 wt%, 0.1 wt%, 0.2 wt%, 0.3 wt%, 0.4 wt%, 0.5 wt% and any value in between.
According to the invention, the hard alloy comprises chromium carbide, and the content of the chromium carbide is 0.8-2.0 wt%
According to the invention, the content of chromium carbide may be cited as 0.8 wt%, 0.9 wt%, 1.0 wt%, 1.1 wt%, 1.2 wt%, 1.3 wt%, 1.4 wt%, 1.5 wt%, 1.6 wt%, 1.7 wt%, 1.8 wt%, 1.9 wt%, 2.0 wt% and any value in between.
According to the invention, the cemented carbide comprises tungsten carbide, the content of tungsten carbide being 82.5 wt% to 87.2 wt% or the balance.
According to the invention, the content of tungsten carbide may be enumerated as 82.5 wt%, 83.0 wt%, 83.5 wt%, 84.0 wt%, 84.5 wt%, 85.0 wt%, 85.5 wt%, 86.0 wt%, 86.5 wt%, 87.0 wt%, 87.2 wt% and any value in between.
In some preferred embodiments of the invention, the tungsten carbide has a fisher's particle size of 0.4 to 0.9 μm, preferably 0.4 to 0.8 μm, more preferably 0.5 to 0.8 μm.
According to the invention, the Fisher-size of the tungsten carbide can be cited as 0.4 μm, 0.45 μm, 0.5 μm, 0.55 μm, 0.6 μm, 0.65 μm, 0.7 μm, 0.75 μm, 0.8 μm, 0.85 μm and 0.9 μm and any value in between.
In some preferred embodiments of the invention, the cobalt has a fisher particle size of 1.5 μm or less, preferably 0.8 to 1.2 μm; and/or the Freund's particle size of the vanadium carbide is less than 1.5 μm, preferably 0.8 μm to 1.2 μm; and/or the Freund's particle size of the chromium carbide is 1.5 μm or less, preferably 0.8 to 1.2 μm.
According to the invention, the Fischer-Tropsch particle sizes of the cobalt, vanadium carbide and chromium carbide may be the same or different, preferably the Fischer-Tropsch particle sizes of the three differ from each other by less than 0.5 μm, more preferably by less than 0.3 μm.
In order to achieve the second purpose, the invention adopts the following technical scheme:
the preparation method of the hard alloy sequentially comprises the steps of mixing, wet grinding, drying, press forming and sintering.
In some preferred embodiments of the present invention, the mixing comprises providing raw materials for preparing the cemented carbide, and mixing the raw materials; wherein the raw materials comprise cobalt, vanadium carbide, chromium carbide, tungsten carbide and a forming agent.
In some preferred embodiments of the present invention, the forming agent is polyethylene glycol and/or paraffin.
In some preferred embodiments of the present invention, the cobalt is present in an amount of 12 wt% to 15 wt%, the vanadium carbide is present in an amount of 0 wt% to 0.5 wt%, the chromium carbide is present in an amount of 0.8 wt% to 2.0 wt%, the tungsten carbide is present in an amount of 82.5 wt% to 87.2 wt%, and the forming agent is present in an amount of 0.5 wt% to 3.0 wt%, based on the total weight of cobalt, vanadium carbide, chromium carbide and tungsten carbide.
In some preferred embodiments of the present invention, the carbon balance of the feedstock is controlled to be + 0.06% + 0.21%.
According to the invention, the above-mentioned carbon balance values are listed as + 0.06%, + 0.07%, + 0.08%, + 0.09%, + 0.10%, + 0.11%, + 0.12%, + 0.13%, + 0.14%, + 0.15%, + 0.16%, + 0.17%, + 0.18%, + 0.19%, + 0.20% and + 0.21%.
According to the invention, when polyethylene glycol is adopted as a forming agent, the dosage of the polyethylene glycol is 1.5-3.0 wt%; when paraffin is used as the forming agent, the dosage of the paraffin is 0.5 wt% -1.5 wt%.
In some preferred embodiments of the invention, the wet grinding is performed in a ball mill, the ball milling medium is alcohol, the ball-to-material ratio is (5-10): 1, the rotation speed of the ball mill is 30-40 rpm, and the ball milling time is 50-80 h.
According to the invention, the material of the grinding rods used in the ball milling can be cemented carbide, and the specifications of the grinding rods (diameter, length, unit: mm) can be 5.5, 14.0(25 wt%), 8.6, 16.3(50 wt%) and 10.5, 17(25 wt%), respectively.
According to the present invention, the solid-to-liquid ratio in the ball mill may be 300mL/kg to 700 mL/kg.
In some preferred embodiments of the present invention, the drying is spray drying, preferably, the drying temperature is 80 ℃ to 100 ℃, and the drying time is 0.5h to 2 h.
According to the invention, the compression molding mode is compression molding, extrusion molding or isostatic pressing.
In some preferred embodiments of the present invention, the sintering is performed by low pressure sintering, and the sintering conditions include: the sintering pressure is 45 bar-100 bar, the sintering temperature is 1350 ℃ to 1450 ℃, and the sintering time is 0.5 h-1.0 h.
In order to achieve the third purpose, the invention adopts the following technical scheme:
the hard alloy or the hard alloy prepared by the preparation method is applied to the field of titanium alloy and stainless steel processing.
In some preferred embodiments the present invention relates to the use of a cemented carbide as described above or a cemented carbide made according to the above-described method of preparation in the field of solid-state tool machining.
The invention adopts high content Co and proper amount Cr3C2And VC is used as a grain growth inhibitor, and a proper wet grinding medium and a forming agent are adopted at the same time, and a proper low-pressure sintering temperature and time are matched, so that WC grains grow properly, the stability of a WC/Co interface of the alloy is ensured to obtain good toughness and strength, and the granularity of the WC grains can be controlled within a certain range to ensure sufficient wear resistance. The end mill and the drill made of the submicron fine grain hard alloy bar have the advantages of wear resistance and obdurability, have high efficiency and service life in the field of cutting aviation titanium alloy and 3c high-strength stainless steel, and particularly can meet the requirement of modern high-efficiency processing on large-feed working conditions.
Drawings
FIG. 1 is a scanning electron micrograph of a cemented carbide produced in example 1 of the present invention.
Fig. 2 is a comparison of the cutting edge of the cemented carbide of example 1 of the present invention and the cutting edge of a milling cutter made of titanium alloy of a standard grade (comparative example 1) for processing titanium alloy at a foreign country after milling the TC21 titanium alloy for 24m, wherein the upper graph is a graph showing the results of example 1, and the lower graph is a graph showing the results of comparative example 1.
FIG. 3 is a SEM photograph of a cemented carbide produced in example 2 of the present invention.
Fig. 4 is a comparison of the cutting edge of the cemented carbide of example 2 of the present invention and the cutting edge of a milling cutter made of a titanium alloy processing common trademark (comparative example 2) in foreign countries after milling TC4 titanium alloy for 5 hours, wherein the upper graph is a graph of the results of example 2, and the lower graph is a graph of the results of comparative example 2.
FIG. 5 is a SEM photograph of a cemented carbide produced in example 3 of the present invention.
Fig. 6 is a comparison of the cutting edge of the hard alloy of example 3 of the present invention and the cutting edge of a milling cutter made of a standard grade (comparative example 3) for stainless steel processing at abroad after milling 316L stainless steel for 7 hours, wherein the upper graph shows the results of example 3, and the lower graph shows the results of comparative example 3.
Detailed Description
The present invention will be described in detail below with reference to examples, but the scope of the present invention is not limited to the following description.
Example 1
Co powder with the Fisher particle size of 1.0um and Cr with the Fisher particle size of 1.2um are selected during mixing3C2And VC and WC powder with a fisher particle size of 0.7 um. Wherein the Co powder and the Cr powder3C2VC and WC in weight percentages of 12%, 1.0%, 0.25% and the balance, respectively. Controlling the carbon balance to be + 0.09%, taking polyethylene glycol as a forming agent (the total weight of cobalt, vanadium carbide, chromium carbide and tungsten carbide is taken as a calculation reference, the dosage of the polyethylene glycol is 2 wt%), taking alcohol as a ball milling medium, enabling the liquid-solid ratio to be 500mL/kg, the ball-material ratio to be 7:1, and enabling the ball mill to rotate at the rotating speed of 36 r/min, and carrying out ball milling for 60 hours. Then spray drying to obtain a mixture, carrying out compression molding, sintering at 1410 ℃ in a gas pressure sintering furnace, keeping the temperature for 1 hour, keeping the sintering pressure at 100MPa, and carrying out coarse grinding to obtain the phi 3.25 x 38.5mm and phi 20 x 150 bars.
A bar with the diameter of 3.25mm is used for physical property test, the hardness of the bar is 1480HV30, the bending strength is 4612MPa on average, and the fracture toughness is 13.2MPam1/2And the WC average grain size is 0.83 um. The scanning electron micrograph is shown in FIG. 1.
As shown in FIG. 1, the WC crystal grains in the prepared alloy are uniformly distributed, and the boundary grows clearly and completely.
A20 mm diameter bar was milled into a TC21 titanium alloy milling test using a mill having the same inlet gauge as that of comparative example 1. The cutting edge of the tool made of two materials is shown in fig. 2 by cutting comparison of a 24m slotting mill under the same conditions.
As shown in FIG. 2, the cutting edge of the comparison mark is damaged and cannot be processed continuously; the cutting edge of the submicron fine-grain hard alloy is intact, and the submicron fine-grain hard alloy can be continuously processed until the submicron fine-grain hard alloy fails to work, and is improved by 25 percent compared with a comparative mark.
Example 2
Co powder with the Fisher particle size of 0.8um and Cr with the Fisher particle size of 1.2um are selected during mixing3C2And WC powder with a fisher particle size of 0.4 um. Wherein the Co powder and the Cr powder3C2And WC 13%, 1.6% by weight, and the balance. Controlling the carbon balance to be + 0.12%, taking polyethylene glycol as a forming agent (the total weight of cobalt, vanadium carbide, chromium carbide and tungsten carbide is taken as a calculation reference, the dosage of the polyethylene glycol is 2 wt%), taking alcohol as a ball milling medium, enabling the liquid-solid ratio to be 500mL/kg, the ball-material ratio to be 8:1, and enabling the ball mill to rotate at the rotating speed of 36 r/min, and carrying out ball milling for 70 hours. Then spray drying to obtain a mixture, compression molding, sintering in a gas pressure sintering furnace at 1450 ℃, keeping the temperature for 0.75 hour, keeping the sintering pressure at 100MPa, and coarsely grinding to obtain the phi 3.25 x 38.5mm and phi 16 x 330 bars.
A bar with the diameter of 3.25mm is used for physical property test, the hardness of the bar is 1500HV30, the bending strength is 4812MPa on average, and the fracture toughness is 13.7MPam1/2And the WC average grain size is 0.85 um. The scanning electron micrograph thereof is shown in FIG. 3.
As shown in FIG. 3, the WC grains in the alloy have complete growth, uniform grain size distribution and no obvious coarse grains.
A bar with the diameter of 16mm is cut into a length of 100mm and processed into a milling cutter with the same specification as that of a certain inlet of the comparative example 2 to carry out TC4 titanium alloy side milling test. After 5 hours of cutting comparison, the cutting edges of the two materials made into the cutter are shown in fig. 4.
It is seen from fig. 4 that the cutting edge integrity of the submicron cemented carbide of the present invention is significantly better than the comparative grade. The alloy of the invention is continuously processed until the cutting edge is invalid within 6 hours, which is improved by 20 percent compared with the comparative mark.
Example 3
Co powder with the Fisher particle size of 0.8um and Cr with the Fisher particle size of 1.5um are selected during mixing3C2VC with a Fisher size of 1.2um and WC powder with a Fisher size of 0.5 um. Wherein the Co powder and the Cr powder3C2VC and WC in the weight percentages of 15%, 1.2%, 0.4% and the rest. Controlling the carbon balance to be + 0.15%, taking paraffin as a forming agent (the total weight of cobalt, vanadium carbide, chromium carbide and tungsten carbide is taken as a calculation reference, the dosage of the paraffin is 1.1 wt%), taking alcohol as a ball milling medium, enabling the liquid-solid ratio to be 500mL/kg, the ball-material ratio to be 8:1, and the rotating speed of a ball mill to be 36 r/min, and carrying out ball milling for 80 hours. Then spray drying to obtain a mixture, compression molding, sintering in a gas pressure sintering furnace at 1450 ℃, keeping the temperature for 0.5 hour, keeping the sintering pressure at 100MPa, and coarsely grinding to obtain phi 4.0 x 310 mm.
Through physical property test, the hardness is 1400HV30, the bending strength is mean 4912MPa, and the fracture toughness is 14.2MPam1/2And the WC average grain size is 0.6 um. The scanning electron micrograph thereof is shown in FIG. 5.
As shown in FIG. 5, the WC grains in the alloy have complete growth, uniform grain size distribution and no obvious coarse grains.
The steel bar material is processed into a milling cutter with the same import specification as that of the comparative example 3 to carry out 316L stainless steel side milling test. The cutting edges of the two materials made into the cutter after 4 hours of cutting comparison are shown in fig. 6.
It is seen from fig. 6 that the cutting edge integrity of the submicron cemented carbide of the present invention is significantly better than the comparative grade.
Example 4
Submicron cemented carbide was prepared as in example 1 except that the WC powder used in example 4 had a fisher grain size of 0.6 um.
Physical property tests show that the hardness of the material is 1560HV30, the bending strength is 4752MPa on average, and the fracture toughness is 12.8MPam1/2And the WC average grain size is 0.67 um.
Example 5
Submicron grained cemented carbide was prepared as in example 1, except that Co powder, Cr powder, etc. were used in example 53C2The Fisher particle size of VC was 1.2. mu.m.
The physical property test shows that the hardness is 1480HV30, the bending strength is averagely 4600MPa, and the fracture toughness is 13.5MPam1/2And the WC average grain size is 0.8 um.
Example 6
A submicron cemented carbide was prepared as in example 1, except that the carbon balance was controlled to + 0.06% in example 6.
The physical property test shows that the hardness is 1500HV30, the bending strength is 4681MPa on average, and the fracture toughness is 13.0MPam1/2And the WC average grain size is 0.8 um.
Comparative example 1
Comparative example 1 is an alloy grade produced by a foreign company, in which the amount of Co powder is 10 wt% and the WC average grain size is 0.8 um. The physical property test shows that the hardness is 1600HV30, the bending strength is 4200MPa on average, and the fracture toughness is 10.8MPam1/2。
Comparative example 2
Comparative example 2 is an alloy grade produced by a foreign company, in which the amount of Co powder used is 12 wt% and the grain size is 0.4 um. The physical property test shows that the hardness is 1700HV30, the bending strength is on average 4275MPa, and the fracture toughness is 9.8MPam1/2。
Comparative example 3
Comparative example 3 is an alloy grade produced by a foreign company, in which the amount of Co powder is 12 wt% and the WC average grain size is 0.5 um.
Physical property tests show that the hardness is 1680HV30, the bending strength is 4524MPa on average, and the fracture toughness is 10.0MPam1/2。
For comparison, the results of the above embodiment are summarized in table 1 below.
It should be noted that the above-mentioned embodiments are only for explaining the present invention, and do not constitute any limitation to the present invention. The present invention has been described with reference to exemplary embodiments, but the words which have been used herein are words of description and illustration, rather than words of limitation. The invention can be modified, as prescribed, within the scope of the claims and without departing from the scope and spirit of the invention. Although the invention has been described herein with reference to particular means, materials and embodiments, the invention is not intended to be limited to the particulars disclosed herein, but rather extends to all other methods and applications having the same functionality.
Claims (10)
1. A cemented carbide comprising or consisting of:
2. cemented carbide according to claim 1, characterized in that the tungsten carbide has a fisher's grain size of 0.4-0.9 μm, preferably 0.4-0.8 μm, more preferably 0.5-0.8 μm.
3. Cemented carbide according to claim 1 or 2, characterized in that the cobalt has a fisher's grain size below 1.5 μm, preferably 0.8 to 1.2 μm; and/or the Freund's particle size of the vanadium carbide is less than 1.5 μm, preferably 0.8 μm to 1.2 μm; and/or the Freund's particle size of the chromium carbide is 1.5 μm or less, preferably 0.8 to 1.2 μm.
4. A method of making a cemented carbide according to any one of claims 1-3 comprising the steps of mixing, wet milling, drying, press forming and sintering in sequence.
5. A method of manufacturing as claimed in claim 4, wherein said mixing comprises providing raw materials for manufacturing said cemented carbide, and mixing said raw materials; the raw materials comprise cobalt, vanadium carbide, chromium carbide, tungsten carbide and a forming agent, and preferably, the forming agent is polyethylene glycol and/or paraffin.
6. The method according to claim 4 or 5, wherein the cobalt content is 12 wt% to 15 wt%, the vanadium carbide content is 0 wt% to 0.5 wt%, the chromium carbide content is 0.8 wt% to 2.0 wt%, the tungsten carbide content is 82.5 wt% to 87.2 wt%, and the forming agent content is 0.5 wt% to 3.0 wt%, based on the total weight of cobalt, vanadium carbide, chromium carbide, and tungsten carbide, and preferably the carbon balance of the raw material is controlled to + 0.06% to + 0.21%.
7. The preparation method according to any one of claims 4 to 6, wherein the wet grinding is carried out in a ball mill, the ball milling medium is alcohol, the ball-to-material ratio is (5-10): 1, the rotation speed of the ball mill is 30-40 rpm, and the ball milling time is 50-80 h.
8. The preparation method according to any one of claims 4 to 7, wherein the drying temperature is 80 ℃ to 100 ℃ and the drying time is 0.5h to 2h, preferably the drying manner is spray drying.
9. The production method according to any one of claims 4 to 8, wherein the conditions of the sintering include: the sintering pressure is 45 bar-100 bar, the sintering temperature is 1350 ℃ to 1450 ℃, and the sintering time is 0.5 h-1.0 h.
10. Use of a cemented carbide according to any one of claims 1-3 or a cemented carbide produced according to the method of any one of claims 4-9 in the field of titanium alloy and stainless steel machining, in particular in the field of solid tool machining.
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN112195387A (en) * | 2020-09-30 | 2021-01-08 | 昆山长鹰硬质材料科技股份有限公司 | Hard alloy, die-cutting knife roll hard alloy blank and preparation method of die-cutting knife roll hard alloy blank |
| CN113943873A (en) * | 2021-10-14 | 2022-01-18 | 九江金鹭硬质合金有限公司 | Preparation method of hard alloy for progressive stamping |
| CN115053004A (en) * | 2021-10-15 | 2022-09-13 | 住友电工硬质合金株式会社 | Cemented carbide and cutting tool using the same |
| CN115821099A (en) * | 2022-11-28 | 2023-03-21 | 攀钢集团攀枝花钢铁研究院有限公司 | Preparation method of hard alloy |
| CN115896578A (en) * | 2022-10-28 | 2023-04-04 | 株洲硬质合金集团有限公司 | Ultrafine hard alloy cutter material and preparation method and application thereof |
| CN116121615A (en) * | 2022-12-02 | 2023-05-16 | 株洲硬质合金集团有限公司 | Superfine ultrafine particle hard alloy and preparation method and application thereof |
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