CN115138849A - Preparation method of binderless hard alloy cutter material - Google Patents
Preparation method of binderless hard alloy cutter material Download PDFInfo
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- 239000000463 material Substances 0.000 title claims abstract description 44
- 239000000956 alloy Substances 0.000 title claims abstract description 36
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 30
- 238000002360 preparation method Methods 0.000 title claims abstract description 10
- 238000005245 sintering Methods 0.000 claims abstract description 62
- 239000000843 powder Substances 0.000 claims abstract description 37
- 238000000034 method Methods 0.000 claims abstract description 29
- 238000002156 mixing Methods 0.000 claims abstract description 18
- 239000002131 composite material Substances 0.000 claims abstract description 16
- 238000005303 weighing Methods 0.000 claims abstract description 8
- 229910018072 Al 2 O 3 Inorganic materials 0.000 claims description 13
- 239000011230 binding agent Substances 0.000 claims description 11
- 238000000498 ball milling Methods 0.000 claims description 8
- 238000005520 cutting process Methods 0.000 claims description 8
- 238000010438 heat treatment Methods 0.000 claims description 8
- 238000001816 cooling Methods 0.000 claims description 4
- 238000000227 grinding Methods 0.000 claims description 2
- 230000003247 decreasing effect Effects 0.000 claims 3
- 238000003825 pressing Methods 0.000 claims 1
- 238000005452 bending Methods 0.000 abstract description 11
- 238000000280 densification Methods 0.000 abstract description 3
- 239000013078 crystal Substances 0.000 abstract description 2
- 239000011651 chromium Substances 0.000 description 14
- 238000001035 drying Methods 0.000 description 10
- 238000012360 testing method Methods 0.000 description 7
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 6
- 229910002804 graphite Inorganic materials 0.000 description 6
- 239000010439 graphite Substances 0.000 description 6
- 239000003112 inhibitor Substances 0.000 description 4
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 description 4
- 238000002441 X-ray diffraction Methods 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 238000011160 research Methods 0.000 description 3
- 239000011882 ultra-fine particle Substances 0.000 description 3
- 229910001069 Ti alloy Inorganic materials 0.000 description 2
- 239000000654 additive Substances 0.000 description 2
- 230000000996 additive effect Effects 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- UFGZSIPAQKLCGR-UHFFFAOYSA-N chromium carbide Chemical compound [Cr]#C[Cr]C#[Cr] UFGZSIPAQKLCGR-UHFFFAOYSA-N 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 238000005553 drilling Methods 0.000 description 2
- 239000003966 growth inhibitor Substances 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 238000004321 preservation Methods 0.000 description 2
- 229910052761 rare earth metal Inorganic materials 0.000 description 2
- 150000002910 rare earth metals Chemical class 0.000 description 2
- 239000003870 refractory metal Substances 0.000 description 2
- 238000002490 spark plasma sintering Methods 0.000 description 2
- 229910003470 tongbaite Inorganic materials 0.000 description 2
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- UUJDYXCAZMFYTK-UHFFFAOYSA-N [Co].[Ta].[W] Chemical compound [Co].[Ta].[W] UUJDYXCAZMFYTK-UHFFFAOYSA-N 0.000 description 1
- YWJQGSHYTRHJJH-UHFFFAOYSA-N [Co].[Ti].[W] Chemical compound [Co].[Ti].[W] YWJQGSHYTRHJJH-UHFFFAOYSA-N 0.000 description 1
- ZTJWUVMPZRLXAB-UHFFFAOYSA-N [Ta].[Ti].[W] Chemical compound [Ta].[Ti].[W] ZTJWUVMPZRLXAB-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000003763 carbonization Methods 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000000975 co-precipitation Methods 0.000 description 1
- JPNWDVUTVSTKMV-UHFFFAOYSA-N cobalt tungsten Chemical compound [Co].[W] JPNWDVUTVSTKMV-UHFFFAOYSA-N 0.000 description 1
- 238000004891 communication Methods 0.000 description 1
- 238000007731 hot pressing Methods 0.000 description 1
- 238000012994 industrial processing Methods 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 230000005764 inhibitory process Effects 0.000 description 1
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- 238000005551 mechanical alloying Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000005272 metallurgy Methods 0.000 description 1
- 238000009768 microwave sintering Methods 0.000 description 1
- 238000005065 mining Methods 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 239000010955 niobium Substances 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 238000005457 optimization Methods 0.000 description 1
- SIWVEOZUMHYXCS-UHFFFAOYSA-N oxo(oxoyttriooxy)yttrium Chemical compound O=[Y]O[Y]=O SIWVEOZUMHYXCS-UHFFFAOYSA-N 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
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- 229910001404 rare earth metal oxide Inorganic materials 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 238000003756 stirring Methods 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
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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
- B22F3/10—Sintering only
- B22F3/105—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding
-
- 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
- C22C29/005—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides comprising a particular metallic binder
-
- 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
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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
- B22F3/10—Sintering only
- B22F3/105—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding
- B22F2003/1051—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding by electric discharge
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
- B22F2005/001—Cutting tools, earth boring or grinding tool other than table ware
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- Mechanical Engineering (AREA)
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- Metallurgy (AREA)
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Abstract
The invention provides a preparation method of a binderless hard alloy cutter material, which comprises the steps of mixing superfine WC with Al, wherein the grain diameter of the superfine WC is 0.2 mu m 2 O 3 、Y 2 O 3 、Cr 3 C 2 Weighing and mixing the components with the mass fractions of 92.5wt%, 4wt%, 3wt% and 0.5wt% to obtain uniform composite powder, and performing plasma sintering at the temperature of 1550 ℃ and the pressure of 25MPa for 10min to obtain the material with the optimal comprehensive mechanical properties, wherein the relative density, the microhardness HV30 and the bending strength are respectively 98.2%, 2250 and 1282MPa. The process obtains a block material with excellent comprehensive performance, solves the problems of difficult sintering densification, large crystal grains and poor comprehensive mechanical property of the binderless hard alloy, effectively improves the frictional wear performance and high temperature resistance of the cutter material, and prolongs the service life of the cutter material.
Description
Technical Field
The invention relates to a preparation method of a binderless hard alloy cutter material.
Background
Cemented carbide is an alloy material made from a hard compound of refractory metals and a binder metal by a powder metallurgy process. The hard alloy has high hardness, strength, wear resistance and corrosion resistance, is known as 'industrial teeth', is used for manufacturing cutting tools, cutters, drilling tools and wear-resistant parts, and is widely applied to the fields of war industry, aerospace, machining, metallurgy, oil drilling, mining tools, electronic communication, buildings and the like. WC is widely used as a refractory metal hard compound in hard alloy materials, and particularly in the field of tool manufacturing, WC-based hard alloys are the most typical and most widely used. The traditional WC-based hard alloy refers to hard alloy containing Co and other binder phases, has high hardness, high strength and density and good toughness, and has important application in the field of industrial processing and production as a cutter. The traditional hard alloy cutter contains binder phase Co and the like, so that when the traditional hard alloy cutter is used for high-speed cutting, particularly when difficult-to-machine materials such as titanium alloy and the like are machined, the phenomena of large cutting force, high cutting temperature, easy adhesion, softening, material loss and the like occur, the quality and the precision of the machined materials are seriously influenced, meanwhile, the service life of the cutter is greatly shortened, and the application of the cutter in the industrial field is limited. The common conventional WC-based hard alloy is divided into four types, namely tungsten cobalt, tungsten tantalum cobalt, tungsten titanium cobalt and tungsten titanium tantalum (niobium). In recent years, much research on cemented tungsten carbide has been focused on cemented tungsten carbide with binder phase, and few studies have been made on non-binder phase WC-based cemented tungsten carbide. The WC-based hard alloy without the binding phase is a WC-based alloy material without the binding phase or with the content of the binding phase less than 0.5 percent, has high hardness, high strength, good wear resistance and corrosion resistance and certain toughness, and is used in the fields of cutter cutting, drill bits, medical parts and the like. The WC-based hard alloy without the binding phase does not contain the binding phase, so that the WC-based hard alloy serving as a cutter is not easy to soften and run off at high temperature, and has the advantages of good wear resistance and corrosion resistance, longer service life and wider application field. But no binding phase, the sintering temperature of the alloy is higher, and the densification is difficultThe degree is large, and the toughness is reduced to a certain extent. The traditional hard alloy is prepared by adopting a mechanical alloying method, a coprecipitation method, a spray conversion method, a reduction carbonization method and other methods, and then is sintered in an atmosphere sintering mode, a microwave sintering mode, a hot-pressing sintering mode and other sintering modes to obtain the hard alloy material with excellent performance. The research is mainly on the sintering process, the material component ratio, the powder preparation method and the refined grains. The non-binding phase hard alloy is mainly added with carbide such as TiC or Al in a plasma sintering mode 2 O 3 、ZrO 2 Adding rare earth oxide or VC and Cr into the second phase 3 C 2 And the like to enhance toughening. Cr (chromium) component 3 C 2 Inhibition of grain growth, al 2 O 3 And yttrium oxide can be used as a sintering aid additive to reduce the sintering temperature of the alloy, purify the crystal boundary and improve the mechanical property. The WC-based hard alloy without the binding phase has more advantages than the traditional hard alloy when processing some difficult-to-process materials such as titanium alloy. Therefore, the preparation of the binderless WC-based cutter material with excellent comprehensive performance is a hotspot of cutting cutter research, and the optimization of the sintering process is the key of preparation.
Disclosure of Invention
The invention aims to provide a preparation method of a binderless hard alloy cutter material, so as to obtain a cutter material with excellent high-temperature friction wear and comprehensive performance and solve the problems in the background art.
In order to achieve the above objects, the present invention provides the following technical routes and schemes.
A preparation method of a binderless hard alloy cutter material comprises the following steps:
(1) Mixing superfine mWC powder with grain size of 0.2 μ 5363 and Cr as grain growth inhibitor 3 C 2 、Al 2 O 3 And rare earth Y 2 O 3 Weighing proper mass according to proper component proportion, and sintering additive Al 2 O 3 And Y 2 O 3 The contents of (A) are respectively fixed to 4wt% and 3wt%, the amounts of chromium carbide added (wt%) are respectively set to 0%, 0.25%, 0.5%, 0.75%, 1%, 1.5% and 2%, and the contents of tungsten carbide are respectively 93%, 92.75%, 92.5%, 9%2.25%, 92%, 91.5% and 91%. And ball-milling, stirring and mixing the powder to obtain uniform composite powder for storage.
(2) 22g of composite powder with different components are respectively taken and sintered in plasma sintering equipment, the sintering temperature is 1550 ℃, the sintering pressure is 45MPa, the heat preservation time is 10min, and the diameter of a sample is 20mm.
(3) Removing graphite paper from the block material obtained by sintering, drying the block material in a drying oven to constant weight, measuring the density of the material by using an Archimedes drainage method, and calculating the density. Then, mechanical property tests such as Vickers hardness, bending strength, fracture toughness and the like are carried out, XRD analysis, metallographic phase and scanning electron microscope observation are combined, the chromium carbide component is optimized to be 0.5wt%, and WC/Al is determined 2 O 3 /Y 2 O 3 /Cr 3 C 2 The component composition of the alloy is 92.5WC4Al 2 O 3 3Y 2 O 3 0.5Cr 3 C 2 。
(4) Weighing and mixing the composite powder uniformly according to the optimized components, changing the plasma sintering temperature, setting the temperature gradient to be 1500 ℃, 1550 ℃, 1600 ℃, 1650 ℃ and 1700 ℃, setting the sintering pressure to be 45MPa, and setting the heat preservation time to be 10min.
(5) And (3) performing mechanical property test, XRD analysis and structure observation on samples obtained by sintering at different temperatures, and determining that the comprehensive mechanical property of the material is optimal at the sintering temperature of 1550 ℃.
(6) According to 0.5wt% Cr 3 C 2 And (3) sintering the uniformly mixed composite powder at the sintering temperature of 1550 ℃ under the pressures of 15MPa, 25MPa, 35MPa and 45MPa, and keeping the temperature for 10min.
(7) And (3) carrying out mechanical property test, XRD analysis and structure observation on samples obtained by sintering under different pressures, and determining that the comprehensive mechanical property of the material under the sintering pressure of 25MPa is optimal.
(8)WC/Al 2 O 3 /Y 2 O 3 /Cr 3 C 2 The optimal composition ratio of the alloy is 92.5WC4Al 2 O 3 3Y 2 O 3 0.5Cr 3 C 2 The sintering process is at 1550 deg.C and 25MPa.
As a further scheme of the invention: WC powder and a grain growth inhibitor Cr in the step (1) 3 C 2 Sintering aid Al 2 O 3 And rare earth Y 2 O 3 Selecting powder with finer granularity, and grinding and mixing for 15-50 h by adopting a mechanical ball milling method or a wet ball milling method.
As a further scheme of the invention: the specific sintering process in the step (2) is as follows: the powder is firstly put into a graphite die, the pressure is pre-increased to 15MPa before sintering, the temperature is increased to 600 ℃ at the heating rate of 100 ℃/min, then the pressure is increased to the set pressure, the heating rate is gradually reduced when the powder is rapidly heated to be close to the sintering temperature at the heating rate of 160 ℃/min, and finally the temperature is increased to the sintering temperature at 0.2 ℃/min, so that the heating temperature can be accurately controlled. And after the temperature reaches the sintering temperature, reducing the temperature to 600 ℃ at the cooling speed of 300 ℃/min, cooling the temperature to 250 ℃ along with the furnace, reducing the pressure to 0MPa, and taking out the sample after the temperature is reduced to the room temperature.
Compared with the prior art, the invention has the beneficial effects that: optimize WC/Al 2 O 3 /Y 2 O 3 /Cr 3 C 2 The component proportion of the alloy material optimizes the optimal sintering temperature and pressure of the plasma sintering process, and the block material with excellent comprehensive mechanical properties is obtained. Spark plasma sintering and sintering aid Al 2 O 3 And Y 2 O 3 The sintering temperature of the non-binding phase hard alloy is greatly reduced, the performance of the material is improved by optimizing alloy components and a sintering process, and the problems of difficult sintering densification, high sintering temperature and grain growth of the non-binding phase hard alloy are solved, so that the frictional wear performance of the material is improved, the high-temperature performance of a cutter is effectively improved, and the service life of the cutter is prolonged.
Drawings
FIG. 1 is a non-binding phase WC/Al alloy prepared according to example 1 of the present invention 2 O 3 /Y 2 O 3 /Cr 3 C 2 The hard alloy material has SEM fracture morphology, wherein (a) is 93WC4Al 2 O 3 3Y 2 O 3 1500 ℃ sintered sample, and (b) 92.5WC4Al 2 O 3 3Y 2 O 3 0.5Cr 3 C 2 Sintered sample at 1550 DEG CAnd (5) preparing the product.
Detailed Description
The technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all of the embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Example 1
In embodiment 1 of the present invention, a method for preparing a cemented carbide tool material without a binder phase comprises the steps of:
mixing the ultrafine powder of 0.2 mu mWC and sintering aid Al 2 O 3 And Y 2 O 3 According to 93WC4Al 2 O 3 3Y 2 O 3 The powder is weighed according to the component proportion, and the powder is ball-milled and mixed to obtain uniform composite powder for standby.
And (3) taking 22g of composite powder, and performing discharge plasma sintering for 10min at the sintering temperature of 1550 ℃ and the sintering pressure of 45MPa, wherein the diameter of a sample is 20mm.
Removing graphite paper from the sintered sample, drying the sintered sample in a drying oven to constant weight, measuring the density of the material by an Archimedes drainage method, and calculating the density. And then, testing mechanical properties such as bending strength, vickers hardness, fracture toughness and the like, and observing by combining XRD, metallographic phase and scanning electron microscope to characterize the comprehensive mechanical properties and microstructure of the sample, wherein the relative density, microhardness HV30 and bending strength of the material are respectively 95.5%, 1323 and 684.2MPa.
Example 2
In embodiment 2 of the present invention, a method for preparing a cemented carbide tool material without a binder phase comprises the steps of:
mixing superfine powder of 0.2 μmWC and grain inhibitor Cr 3 C 2 Sintering aid Al 2 O 3 And Y 2 O 3 According to 92.5WC4Al 2 O 3 3Y 2 O 3 0.5Cr 3 C 2 Weighing the powder according to the component ratio, and ball-milling and mixing the powder to obtain the mixtureAnd mixing the powder uniformly for later use.
And (3) taking 22g of composite powder, and performing discharge plasma sintering for 10min at the sintering temperature of 1550 ℃ and the sintering pressure of 45MPa, wherein the diameter of a sample is 20mm.
Removing graphite paper from the sintered sample, drying the sintered sample in a drying oven to constant weight, measuring the density of the material by an Archimedes drainage method, and calculating the density. And then, testing mechanical properties such as bending strength, vickers hardness, fracture toughness and the like, and observing by combining XRD, metallographic phase and scanning electron microscope to represent comprehensive mechanical properties and microstructures of the sample, wherein the relative density, the microhardness HV30 and the bending strength of the material are respectively 98.3%, 1536 and 1004MPa.
Example 3
In embodiment 3 of the present invention, a method for preparing a cemented carbide tool material without a binder phase comprises the steps of:
mixing the powder with the ultrafine particle size of 0.2 mu mWC and the grain inhibitor Cr 3 C 2 Sintering aid Al 2 O 3 And Y 2 O 3 According to 92.25WC4Al 2 O 3 3Y 2 O 3 0.75Cr 3 C 2 Weighing the powder according to the component ratio, and performing ball milling and mixing on the powder to obtain uniform composite powder for later use.
And (3) taking 22g of composite powder, and performing discharge plasma sintering for 10min at the sintering temperature of 1550 ℃ and the sintering pressure of 45MPa, wherein the diameter of a sample is 20mm.
And removing graphite paper from the sintered sample, drying the sintered sample in a drying box to constant weight, measuring the density of the material by using an Archimedes drainage method, and calculating the density. And then, testing mechanical properties such as bending strength, vickers hardness, fracture toughness and the like, and then, observing by combining XRD, metallographic phase and a scanning electron microscope, and characterizing the comprehensive mechanical properties and microstructure of the sample, wherein the relative density, the microhardness HV30 and the bending strength of the material are respectively 88.2%, 1982 and 792.5MPa.
Example 4
In embodiment 4 of the present invention, a method for preparing a cemented carbide tool material without a binder phase comprises the steps of:
mixing the powder with the ultrafine particle size of 0.2 mu mWC and the grain inhibitor Cr 3 C 2 Sintering aid Al 2 O 3 And Y 2 O 3 According to 92.5WC4Al 2 O 3 3Y 2 O 3 0.5Cr 3 C 2 Weighing the powder according to the component ratio, and carrying out ball milling and mixing on the powder to obtain uniform composite powder for later use.
And (3) taking 22g of composite powder, and performing discharge plasma sintering for 10min at the sintering temperature of 1550 ℃ and the sintering pressure of 25MPa, wherein the diameter of a sample is 20mm.
And removing graphite paper from the sintered sample, drying the sintered sample in a drying box to constant weight, measuring the density of the material by using an Archimedes drainage method, and calculating the density. And then, testing mechanical properties such as bending strength, vickers hardness, fracture toughness and the like, and then, observing by combining XRD, metallographic phase and a scanning electron microscope, and characterizing the comprehensive mechanical properties and microstructure of the sample, wherein the relative density, the microhardness HV30 and the bending strength of the material are respectively 98.2%, 2250 and 1282MPa.
In conclusion, the ultrafine particle size of 0.2 mu mWC powder and the grain inhibitor Cr are mixed 3 C 2 Sintering aid Al 2 O 3 And Y 2 O 3 According to 92.5WC4Al 2 O 3 3Y 2 O 3 0.5Cr 3 C 2 The composite powder with the component ratio is subjected to spark plasma sintering for 10min at the sintering temperature of 1550 ℃ and the sintering pressure of 25MPa, the comprehensive mechanical property of the material is optimal, and the relative density, the microhardness HV30 and the bending strength of the material are respectively 98.2%, 2250 and 1282MPa.
Claims (4)
1. The preparation method of the binderless hard alloy cutter material is characterized by comprising the following steps of:
mixing WC with Al 2 O 3 、Y 2 O 3 、Cr 3 C 2 Weighing and mixing the components with the mass fractions of 92.5wt%, 4wt%, 3wt% and 0.5wt% to obtain uniform composite powder;
performing plasma sintering at 1550 deg.C and 25MPa for 10min to obtain 92.5WC4Al 2 O 3 3Y 2 O 3 0.5Cr 3 C 2 The hard alloy cutter material.
2. The method for preparing a cemented carbide tool material without binder phase according to claim 1 wherein the WC grain size before the composite powder is mixed is 0.2 μm.
3. The method for preparing the cemented carbide cutting tool material without the binding phase according to claim 2, wherein the composite powder is prepared by mixing WC and Al 2 O 3 、Y 2 O 3 And Cr 3 C 2 Weighing, mixing and grinding for 15-50 h by adopting a mechanical ball milling method or a wet ball milling method.
4. The method for preparing the cemented carbide cutting tool material without the binder phase according to claim 1, wherein the pre-pressing is 15MPa before the plasma sintering, the temperature is raised to 600 ℃ at a heating rate of 100 ℃/min, then the pressure is increased to 25MPa, the heating rate is gradually decreased when the rapid heating is carried out to approach the sintering temperature at a heating rate of 160 ℃/min, finally the temperature is raised to the sintering temperature at 0.2 ℃/min, the temperature is decreased to 600 ℃ at a cooling rate of 300 ℃/min after the temperature reaches the sintering temperature, and the pressure is decreased to 0 after the furnace cooling to 250 ℃.
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| CN115652166A (en) * | 2022-11-04 | 2023-01-31 | 安徽尚欣晶工新材料科技有限公司 | Superhard alloy material for ultrahigh-pressure water jet cutter and preparation method thereof |
Citations (15)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1995005497A1 (en) * | 1993-08-16 | 1995-02-23 | Sumitomo Electric Industries, Ltd. | Cemented carbide alloy for cutting tool and coated cemented carbide alloy |
| JPH11124650A (en) * | 1997-10-20 | 1999-05-11 | Toshiba Tungaloy Co Ltd | Wc-containing cemented carbide subjected to transgranular dispersion strengthening by oxide, and its production |
| WO2009119682A1 (en) * | 2008-03-26 | 2009-10-01 | 京セラ株式会社 | Cutting tool |
| CN102151834A (en) * | 2011-03-08 | 2011-08-17 | 深圳市格林美高新技术股份有限公司 | Al2O3-cobalt-based adhesive phase-containing ultrafine hard alloy powder and preparation method and use thereof |
| CN102220534A (en) * | 2011-07-20 | 2011-10-19 | 中南大学 | Method for reinforcing binder phase of hard alloy |
| CN102628138A (en) * | 2012-03-23 | 2012-08-08 | 华南理工大学 | Trace cobalt-containing tungsten carbide without bonding phase and preparation method thereof |
| CN103834824A (en) * | 2014-03-20 | 2014-06-04 | 中国科学院长春应用化学研究所 | Binding-phase-free tungsten carbide hard alloy and preparation method thereof |
| CN103898387A (en) * | 2014-04-29 | 2014-07-02 | 东南大学 | Binding-phase TiC/WC composite hard alloy and preparation method thereof |
| CN103924144A (en) * | 2014-04-09 | 2014-07-16 | 中南大学 | Preparation method of unbonded-phase ultrafine WC hard alloy |
| CN108165791A (en) * | 2017-12-06 | 2018-06-15 | 台州学院 | A kind of preparation method of soap-free emulsion polymeization phase ultrafine tungsten carbide hard alloy |
| CN109852862A (en) * | 2019-01-11 | 2019-06-07 | 广东技术师范学院 | A kind of high rigidity composite hard alloy and the preparation method and application thereof |
| CN111056852A (en) * | 2019-12-19 | 2020-04-24 | 西安交通大学 | Binding phase-free WC-based hard alloy cutter material and preparation method thereof |
| CN111172443A (en) * | 2020-02-24 | 2020-05-19 | 山东大学 | High-comprehensive-performance hard alloy cutter material and preparation method thereof |
| CN111663068A (en) * | 2020-07-01 | 2020-09-15 | 南京佑天金属科技有限公司 | HfC modified WC-Co composite material with nearly equal particle size, and preparation method and application thereof |
| CN113336554A (en) * | 2021-07-02 | 2021-09-03 | 阳江职业技术学院 | Water jet sand pipe raw material, water jet sand pipe preparation method and water jet sand pipe |
-
2022
- 2022-06-02 CN CN202210629300.0A patent/CN115138849B/en active Active
Patent Citations (15)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1995005497A1 (en) * | 1993-08-16 | 1995-02-23 | Sumitomo Electric Industries, Ltd. | Cemented carbide alloy for cutting tool and coated cemented carbide alloy |
| JPH11124650A (en) * | 1997-10-20 | 1999-05-11 | Toshiba Tungaloy Co Ltd | Wc-containing cemented carbide subjected to transgranular dispersion strengthening by oxide, and its production |
| WO2009119682A1 (en) * | 2008-03-26 | 2009-10-01 | 京セラ株式会社 | Cutting tool |
| CN102151834A (en) * | 2011-03-08 | 2011-08-17 | 深圳市格林美高新技术股份有限公司 | Al2O3-cobalt-based adhesive phase-containing ultrafine hard alloy powder and preparation method and use thereof |
| CN102220534A (en) * | 2011-07-20 | 2011-10-19 | 中南大学 | Method for reinforcing binder phase of hard alloy |
| CN102628138A (en) * | 2012-03-23 | 2012-08-08 | 华南理工大学 | Trace cobalt-containing tungsten carbide without bonding phase and preparation method thereof |
| CN103834824A (en) * | 2014-03-20 | 2014-06-04 | 中国科学院长春应用化学研究所 | Binding-phase-free tungsten carbide hard alloy and preparation method thereof |
| CN103924144A (en) * | 2014-04-09 | 2014-07-16 | 中南大学 | Preparation method of unbonded-phase ultrafine WC hard alloy |
| CN103898387A (en) * | 2014-04-29 | 2014-07-02 | 东南大学 | Binding-phase TiC/WC composite hard alloy and preparation method thereof |
| CN108165791A (en) * | 2017-12-06 | 2018-06-15 | 台州学院 | A kind of preparation method of soap-free emulsion polymeization phase ultrafine tungsten carbide hard alloy |
| CN109852862A (en) * | 2019-01-11 | 2019-06-07 | 广东技术师范学院 | A kind of high rigidity composite hard alloy and the preparation method and application thereof |
| CN111056852A (en) * | 2019-12-19 | 2020-04-24 | 西安交通大学 | Binding phase-free WC-based hard alloy cutter material and preparation method thereof |
| CN111172443A (en) * | 2020-02-24 | 2020-05-19 | 山东大学 | High-comprehensive-performance hard alloy cutter material and preparation method thereof |
| CN111663068A (en) * | 2020-07-01 | 2020-09-15 | 南京佑天金属科技有限公司 | HfC modified WC-Co composite material with nearly equal particle size, and preparation method and application thereof |
| CN113336554A (en) * | 2021-07-02 | 2021-09-03 | 阳江职业技术学院 | Water jet sand pipe raw material, water jet sand pipe preparation method and water jet sand pipe |
Non-Patent Citations (1)
| Title |
|---|
| 胡涛等: "无粘结相 WC 基硬质合金刀具材料的研究现状与前景", 《工具技术》, vol. 53, pages 7 - 11 * |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115652166A (en) * | 2022-11-04 | 2023-01-31 | 安徽尚欣晶工新材料科技有限公司 | Superhard alloy material for ultrahigh-pressure water jet cutter and preparation method thereof |
| CN115652166B (en) * | 2022-11-04 | 2024-03-08 | 安徽尚欣晶工新材料科技有限公司 | Superhard hard alloy material for ultrahigh-pressure water jet knife and preparation method thereof |
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