CN115971477A - High-hardness and high-toughness hard alloy and preparation method thereof - Google Patents
High-hardness and high-toughness hard alloy and preparation method thereof Download PDFInfo
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- CN115971477A CN115971477A CN202211662732.8A CN202211662732A CN115971477A CN 115971477 A CN115971477 A CN 115971477A CN 202211662732 A CN202211662732 A CN 202211662732A CN 115971477 A CN115971477 A CN 115971477A
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- 239000000956 alloy Substances 0.000 title claims abstract description 94
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 90
- 238000002360 preparation method Methods 0.000 title claims abstract description 17
- 238000005245 sintering Methods 0.000 claims abstract description 44
- 238000000498 ball milling Methods 0.000 claims abstract description 28
- 239000002994 raw material Substances 0.000 claims abstract description 28
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 claims abstract description 23
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims abstract description 22
- 238000001816 cooling Methods 0.000 claims abstract description 22
- 238000000034 method Methods 0.000 claims abstract description 22
- 238000001035 drying Methods 0.000 claims abstract description 19
- 238000002156 mixing Methods 0.000 claims abstract description 19
- 229910020517 Co—Ti Inorganic materials 0.000 claims abstract description 16
- 239000011812 mixed powder Substances 0.000 claims abstract description 15
- 239000003795 chemical substances by application Substances 0.000 claims abstract description 11
- 238000003825 pressing Methods 0.000 claims abstract description 11
- 238000004321 preservation Methods 0.000 claims abstract description 10
- 238000005238 degreasing Methods 0.000 claims abstract description 5
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 24
- 239000000463 material Substances 0.000 claims description 19
- 238000010438 heat treatment Methods 0.000 claims description 16
- 229910052786 argon Inorganic materials 0.000 claims description 12
- 238000004519 manufacturing process Methods 0.000 claims description 6
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical group CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 5
- 239000002202 Polyethylene glycol Substances 0.000 claims description 5
- 229920001223 polyethylene glycol Polymers 0.000 claims description 5
- 239000007791 liquid phase Substances 0.000 claims description 4
- 238000001694 spray drying Methods 0.000 claims description 3
- 238000001291 vacuum drying Methods 0.000 claims description 3
- 239000012188 paraffin wax Substances 0.000 claims 1
- 239000000843 powder Substances 0.000 description 16
- 229910009043 WC-Co Inorganic materials 0.000 description 7
- 239000002245 particle Substances 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 4
- 238000000354 decomposition reaction Methods 0.000 description 4
- 239000007789 gas Substances 0.000 description 4
- 239000013078 crystal Substances 0.000 description 3
- 238000005553 drilling Methods 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 239000012300 argon atmosphere Substances 0.000 description 2
- 239000012298 atmosphere Substances 0.000 description 2
- 239000011230 binding agent Substances 0.000 description 2
- 239000002131 composite material Substances 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 239000012071 phase Substances 0.000 description 2
- 238000006467 substitution reaction Methods 0.000 description 2
- AFCARXCZXQIEQB-UHFFFAOYSA-N N-[3-oxo-3-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)propyl]-2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidine-5-carboxamide Chemical compound O=C(CCNC(=O)C=1C=NC(=NC=1)NCC1=CC(=CC=C1)OC(F)(F)F)N1CC2=C(CC1)NN=N2 AFCARXCZXQIEQB-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000000919 ceramic Substances 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000007542 hardness measurement Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000003801 milling Methods 0.000 description 1
- 239000003870 refractory metal Substances 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
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Abstract
The invention discloses a high-hardness high-toughness hard alloy and a preparation method thereof, and relates to the technical field of hard alloy materials. The preparation method of the high-hardness high-toughness hard alloy comprises the following steps: s1, mixing Ti 2 Mixing AlC, tungsten carbide and cobalt powder to obtain a hard alloy raw material, wherein the hard alloy raw material comprises the following components in percentage by mass: 75-93.8% of tungsten carbide, 6-15% of cobalt powder and Ti 2 0.2 to 10 percent of AlC; s2, mixing the hard alloy raw material with a forming agent, performing ball milling, and drying to obtain hard alloy mixed powder; s3, pressing the obtained hard alloy mixed powder to obtain a formed green body; s4, low-pressure sintering is carried out on the molded green body in the step S3Obtaining the WC-Co-Ti with high hardness and high toughness 2 AlC hard alloy, wherein the sintering process comprises the following steps: degreasing, sintering, heat preservation and cooling; thereby solving the problem that the hardness and the fracture toughness of the hard alloy can not be improved simultaneously in the prior art.
Description
Technical Field
The invention relates to the technical field of hard alloy materials, in particular to a high-hardness high-toughness hard alloy and a preparation method thereof.
Background
Cemented carbide is a multiphase composite material composed of one or more high hardness, high modulus refractory metal carbides as the matrix and transition group metals or other alloys as the binder phase. The composite structure material has the advantages of high hardness, high wear resistance and red hardness of ceramics, and higher strength and toughness of metal; the specific double high performance is the goal pursued by the scientific researchers of the materials. The WC-Co hard alloy has the advantages of high strength, high hardness, good wear resistance and the like, and is widely applied to the fields of cutting, drilling, impact and the like.
At present, in order to meet the higher requirements of the fields of high-precision metal cutting, micro-processing of electronic instruments and the like on the hardness and strength of WC-Co hard alloy, WC crystal grains are often refined to superfine grade, so that the superfine WC-Co hard alloy with high hardness and high strength is obtained. However, WC grain refinement will significantly reduce the mean free path of Co, which in turn reduces the fracture toughness of the cemented carbide.
Therefore, how to solve the problem that the hardness and the fracture toughness of the cemented carbide cannot be simultaneously improved in the prior art becomes an important technical problem to be solved by those skilled in the art.
Disclosure of Invention
The invention aims to provide a high-hardness high-toughness hard alloy and a preparation method thereof so as to solve the technical problem that the hardness and the fracture toughness of the hard alloy cannot be simultaneously improved in the prior art. The technical effects that can be produced by the preferred technical scheme in the technical schemes provided by the invention are described in detail in the following.
In order to achieve the purpose, the invention provides the following technical scheme:
the invention provides a preparation method of a high-hardness high-toughness hard alloy, which is characterized by comprising the following steps of:
s1, mixing Ti 2 Mixing AlC, tungsten carbide and cobalt powder to obtain a hard alloy raw material, wherein the hard alloy raw material comprises the following components in percentage by mass: 75-93.8% of tungsten carbide, 6-15% of cobalt powder and Ti 2 AlC 0.2～10％；
S2, mixing the hard alloy raw material with a forming agent, performing ball milling, and drying to obtain hard alloy mixed powder;
s3, pressing the obtained hard alloy mixed powder to obtain a formed green body;
s4, sintering the molded green body in the step S3 at low pressure to obtain the WC-Co-Ti with high hardness and high toughness 2 AlC hard alloy, wherein the sintering process comprises the following steps: degreasing, sintering, heat preservation and cooling.
On the basis of the technical scheme, the invention can be improved as follows.
Further, the grain diameters of the tungsten carbide, the cobalt powder and the Ti2AlC in the hard alloy raw material are respectively 0.2-2.0 μm, 0.5-2.0 μm and 3.0-5.0 μm.
Furthermore, the forming agent is polyethylene glycol, and the mass ratio of the hard alloy raw material to the forming agent is 1 (0.01-0.03).
Furthermore, the ball milling medium is absolute ethyl alcohol, the ball milling time is 24-72 h, the ball milling rotating speed is 250-500 r/min, and the ball-to-material ratio of the ball milling is (5-10): 1.
Further, the drying is vacuum drying or spray drying, the drying temperature is 75-90 ℃, and the drying time is 6-8 h.
Further, the pressing pressure is 150-350 MPa, and the pressure maintaining time is 0.5-5 min.
Further, under the condition that the vacuum degree is 1.0-5.0 multiplied by 10 < -3 > Pa, the molded green body is heated to 1200 ℃ from room temperature, argon gas is introduced, the pressure is 1-10 MPa, the temperature is continuously raised to the sintering temperature, low-pressure sintering is carried out, then the temperature is reduced to 1200 ℃, and the introduction of the argon gas is stopped.
Furthermore, the temperature of the low-pressure sintering is 1320-1510 ℃, and the pressure is 1-10 Mpa.
Further, the sintering stage is high liquid phase sintering, the heat preservation time of the heat preservation stage is 0.5-2 h, and the cooling mode of the cooling stage is furnace cooling.
High-hardness and high-toughness WC-Co-Ti 2 The AlC hard alloy is prepared by a preparation method of a hard alloy with high hardness and high toughness.
The technical scheme provided by the application comprises the following beneficial effects:
in the technical scheme provided by the invention, the preparation method of the high-hardness high-toughness hard alloy comprises the following steps: s1, mixing Ti 2 Mixing AlC, tungsten carbide and cobalt powder to obtain a hard alloy raw material, wherein the hard alloy raw material comprises the following components in percentage by mass: 75-93.8% of tungsten carbide, 6-15% of cobalt powder and Ti 2 0.2 to 10 percent of AlC; s2, mixing the hard alloy raw material with a forming agent, performing ball milling, and drying to obtain hard alloy mixed powder; s3, pressing the obtained hard alloy mixed powder to obtain a formed green body S4, and sintering the formed green body in the S3 at low pressure in an argon atmosphere to obtain WC-Co-Ti with high hardness and high toughness 2 AlC hard alloy, wherein the sintering process comprises the following steps: degreasing, sintering, heat preservation and cooling. So configured, the present invention utilizes Ti 2 The layered structure of AlC is controlled by Ti 2 The mass percentage of AlC and the sintering temperature and pressure can ensure that the hard alloy has high hardness and keeps better toughness; control of Ti 2 The addition amount of AlC and the temperature and pressure in the sintering process realize Ti 2 Controllable decomposition of AlC material at high temperature and high pressure to partially decompose Ti 2 Decomposition product T of AlCThe iC can effectively refine WC crystal grains, thereby improving the hardness of the material. With non-decomposed Ti 2 The advantages of the layered structure of the AlC are fully exerted, crack branching and deflection are induced, and the hard alloy has excellent toughness; WC-Co-Ti prepared by the invention 2 The hardness of AlC hard alloy is 19-22 GPa, and the fracture toughness is 9-13 MPa.m 1/2 The method can be widely applied to the fields of wear-resistant parts, cutters, drilling tools and the like; the invention mixes tungsten carbide, cobalt powder and Ti 2 The hard alloy is prepared by mixing and ball-milling AlC powder and sintering at low pressure, the process stability and the repeatability are strong, the preparation of raw materials, the process and equipment are relatively simple, and the manufacturing cost is low; thereby solving the problem that the hardness and the fracture toughness of the hard alloy can not be improved simultaneously in the prior art.
Detailed Description
In order to make the objects, technical solutions and advantages of the present invention more apparent, the technical solutions of the present invention will be described in detail below. It is to be understood that the described embodiments are merely exemplary of the invention, and not restrictive of the full scope of the invention. All other embodiments, which can be derived by a person skilled in the art from the examples given herein without any inventive step, are within the scope of the present invention.
The purpose of the present embodiment is to provide a method for preparing a hard alloy with high hardness and high toughness; thereby solving the problem that the hardness and the fracture toughness of the hard alloy can not be improved simultaneously in the prior art.
The embodiments shown below do not limit the inventive content described in the claims. The entire contents of the configurations shown in the following embodiments are not limited to those required as solutions of the inventions described in the claims.
The embodiment provides a preparation method of a high-hardness high-toughness hard alloy, which comprises the following steps: s1, mixing Ti 2 Mixing AlC, tungsten carbide and cobalt powder to obtain a hard alloy raw material, wherein the hard alloy raw material comprises the following components in percentage by mass: 75 to 93.8 percent of tungsten carbide and 6 to 15 percent of cobalt powder, andthe above Ti 2 0.2 to 10 percent of AlC; s2, mixing the hard alloy raw material with a forming agent, performing ball milling, and drying to obtain hard alloy mixed powder; s3, pressing the obtained hard alloy mixed powder to obtain a formed green body; s4, sintering the molded green body in the S3 in an argon atmosphere at low pressure to obtain WC-Co-Ti with high hardness and high toughness 2 AlC hard alloy, wherein the sintering process comprises the following steps: degreasing, sintering, heat preservation and cooling.
So configured, the present invention utilizes Ti 2 The increase structure of AlC is controlled by Ti 2 The mass percentage of AlC and the sintering temperature and pressure can ensure that the hard alloy has high hardness and keeps better toughness; control of Ti 2 The addition amount of AlC and the temperature and pressure in the sintering process realize Ti 2 Controllable decomposition of AlC material at high temperature and high pressure to partially decompose Ti 2 TiC which is a decomposition product of AlC can effectively refine WC crystal grains, so that the hardness of the material is improved. With non-decomposed Ti 2 The advantages of the layered structure of the AlC are fully exerted, and crack branching and deflection are induced, so that the hard alloy has excellent toughness; WC-Co-Ti prepared by the invention 2 The hardness of AlC hard alloy is 19-22 GPa, and the fracture toughness is 9-13 MPa.m 1/2 The wear-resistant material can be widely applied to the fields of wear-resistant parts, cutters, drilling tools and the like; the invention mixes tungsten carbide, cobalt powder and Ti 2 The hard alloy is prepared by mixing and ball-milling AlC powder and sintering at low pressure, the process stability and the repeatability are strong, the preparation of raw materials, the process and equipment are relatively simple, and the manufacturing cost is low; thereby solving the problem that the hardness and the fracture toughness of the hard alloy can not be improved simultaneously in the prior art.
The hard alloy comprises the following components in percentage by mass: 77-93.8% of tungsten carbide, 6-15% of cobalt powder and Ti 2 0.2 to 8 percent of AlC powder. In this embodiment, the cemented carbide raw material includes, by mass percentage, 77 to 93.8% of tungsten carbide, preferably 83 to 91%, and more preferably 88 to 90%. In the examples, tungsten carbide is preferably used in the form of powder, and the particle size of tungsten carbide is preferably 0.2 to 5.0. Mu.m. The invention uses tungsten carbide as the base of the hard alloyThe basic raw materials. In this embodiment, the cemented carbide raw material includes, by mass percentage, 6 to 15% of cobalt powder, preferably 8 to 12%, and more preferably 8.0 to 10%. In the present embodiment, the particle size of the cobalt powder is preferably 0.2 to 5.0. Mu.m. Cobalt was used as the binder phase in this example. In this embodiment, the cemented carbide material includes Ti in percentage by mass 2 0.2 to 8 percent of AlC powder, preferably 0.5 to 5 percent of AlC powder. In this example, ti 2 AlC is preferably used in the form of a powder, ti 2 The particle size of AlC is preferably 1.0 to 5.0. Mu.m.
As an alternative embodiment, the tungsten carbide, cobalt powder and Ti in the cemented carbide feedstock 2 The grain sizes of AlC are 0.2-2.0 μm, 0.5-2.0 μm and 3.0-5.0 μm respectively.
In an alternative embodiment, the forming agent is polyethylene glycol, and the mass ratio of the cemented carbide raw material to the forming agent is 1 (0.01-0.03).
As an optional implementation mode, the medium for ball milling in the embodiment is preferably absolute ethyl alcohol, the ball milling time is 24-72 h, the rotation speed of the ball milling is 250-500 r/min, and the ball-to-material ratio of the ball milling is (5-10): 1. The ball-to-material ratio of the ball mill in this example is preferably 10. In this embodiment, the ball milling equipment is not particularly limited, and any ball milling equipment known in the art and capable of achieving the above parameters may be used, such as a ball mill. The powder materials are uniformly mixed by a ball milling process.
As an alternative embodiment, the drying is vacuum drying or spray drying, the drying temperature is 75-90 ℃, and the drying time is 6-8 h. After the ball milling is finished, preferably drying the materials obtained by the ball milling to obtain mixed powder; the temperature for drying in this embodiment is preferably 75 ℃, the time for drying is preferably 6 to 7 hours, and the drying is preferably carried out in a vacuum rotary evaporator. This example evaporates the milling media by drying.
As an alternative embodiment, the pressing pressure is 150-350 MPa, and the dwell time is 0.5-5 min. The pressing pressure in the embodiment is preferably 250 to 300MPa; the dwell time for pressing is preferably 0.5 to 5min. The apparatus for compacting the green compact according to the present invention is not particularly limited, and may be any apparatus known in the art. The invention obtains a shaped green body by pressing.
As an alternative embodiment, the shaped green body is brought to a vacuum of 1.0 to 5.0X 10 -3 And under the Pa condition, heating from room temperature to 1200 ℃, starting to introduce argon under the pressure of 1-10 MPa, continuously heating to the sintering temperature, performing low-pressure sintering, then cooling to 1200 ℃, and stopping introducing argon. The process of high-temperature sintering in the present embodiment preferably includes: at a vacuum degree of 10 -2 ～10 -3 And under the condition of Pa, heating from room temperature to 1200 ℃ at a heating rate of 5 ℃/min, starting introducing argon, continuously heating to the high-temperature sintering temperature at a heating rate of 3 ℃/min, carrying out liquid-phase sintering, then cooling to 1100 ℃ along with the furnace, stopping introducing the argon, and then cooling to room temperature to obtain the high-hardness and high-toughness WC-Co-Ti2AlC hard alloy.
More specifically, the low-pressure sintering is carried out at a holding temperature of 1320-1510 ℃ and a pressure of 1-10 MPa. In the embodiment, the pressure is preferably 2-5 MPa, the sintering temperature is preferably 1360-1400 ℃, and the heat preservation time is preferably 0.5-2 h.
As an optional embodiment, the sintering stage is high liquid phase sintering, the heat preservation time of the heat preservation stage is 0.5 to 2 hours, and the cooling manner of the cooling stage in this embodiment is preferably furnace cooling.
The invention provides WC-Co-Ti prepared by the preparation method in the technical scheme 2 And AlC hard alloy. WC-Co-Ti in the invention 2 The Vickers microhardness of AlC hard alloy is 19-22 GPa, and the fracture toughness is 9-13 MPa.m 1 /2 。
Example 1
The hard alloy comprises the following raw materials in percentage by weight: ti 2 1.0% of AlC powder, 89.5% of tungsten carbide powder and 10.0% of cobalt powder; the particle diameters of the components are respectively 3 μm, 0.2 μm and 0.5 μm;
mixing a hard alloy raw material with 1.0wt% of polyethylene glycol, and carrying out ball milling for 72 hours, wherein the ball milling medium is absolute ethyl alcohol, and the ball-to-material ratio is 10:1, the rotating speed of a main shaft of the ball mill is 350r/min, the obtained ball-milled material is dried for 8 hours at 90 ℃ in a vacuum rotary evaporator to obtain mixed powder, and the mixed powder isPressing under the pressure of 250MPa for 1.5min to obtain a molded green body; placing the formed green body into a high temperature atmosphere furnace at a vacuum degree of 10 -2 ～10 -3 Heating from room temperature to 1200 ℃ at the heating rate of 5 ℃/min under the Pa condition, introducing argon gas with the pressure of 2MPa, continuously heating at the heating rate of 3 ℃/min to the sintering temperature of 1360 ℃, performing high-temperature sintering for 1h, then cooling to 1100 ℃, stopping introducing the argon gas, and continuously cooling to the room temperature along with the furnace to obtain WC-Co-Ti 2 AlC cemented carbide, denoted WC-Co-1.0Ti 2 AlC。
Example 2
The present example differs from example 1 in that: the hard alloy comprises the following raw materials in percentage by weight: ti 2 2.0% of AlC powder, 88% of tungsten carbide powder and 10% of cobalt powder; the grain diameters of all the components are respectively 3 mu m, 1 mu m and 1 mu m, and the prepared wear-resistant WC-Co-Ti 2 The AlC hard alloy is marked as WC-Co-2.0Ti 2 AlC。
Example 3
The hard alloy comprises the following raw materials in percentage by weight: ti 2 4.0% of AlC powder, 86.0% of tungsten carbide powder and 10.0% of cobalt powder; the particle diameters of the components are respectively 3 μm, 1 μm and 1 μm; mixing a hard alloy raw material with 1wt% of polyethylene glycol, and carrying out ball milling for 72 hours, wherein the ball milling medium is absolute ethyl alcohol, and the ball-to-material ratio is 10:1, the rotating speed of a main shaft of a ball mill is 275r/min, the obtained ball-milled material is dried for 8 hours at 80 ℃ in a vacuum rotary evaporator to obtain mixed powder, and the mixed powder is pressed under the pressure of 250MPa for 1min to obtain a formed green body; placing the formed green body into a high-temperature atmosphere furnace at a vacuum degree of 10E -2 ～10E -3 Heating from room temperature to 1200 ℃ at the heating rate of 5 ℃/min under the Pa condition, introducing argon, continuously heating at the heating rate of 3 ℃/min until the sintering temperature is 1400 ℃, sintering at high temperature for 1h, then cooling to 1100 ℃, stopping introducing argon, and cooling to room temperature along with the furnace to obtain the wear-resistant WC-Co-Ti alloy material 2 AlC cemented carbide, denoted WC-Co-4.0Ti 2 AlC。
Comparative example 1
Ti in example 1 2 Total replacement of AlC powder with WC powder, other parameters andthe procedure is as in example 1, and WC-Co cemented carbide material, denoted as WC-Co, is prepared.
Performance testing
1) The mechanical properties of the cemented carbides prepared in examples 1 to 3 and comparative example 1 were measured by vickers hardness measurement, and the results are shown in table 1.
Table 1 performance parameters of cemented carbides prepared in examples 1 to 3 and comparative example 1
As can be seen from Table 1, WC-Co-Ti prepared according to the invention 2 The hardness of the AlC hard alloy is obviously higher than that of the WC-Co hard alloy in the comparative example 1, and the fracture toughness of the AlC hard alloy is still maintained to be 9.5 MPa.m 1/2 The above.
As can be seen from the above examples, the invention provides a high-hardness high-toughness hard alloy and a preparation method thereof, and WC-Co-Ti prepared by the invention 2 The hardness of AlC hard alloy is 19-22 GPa, and the fracture toughness is 9-13 MPa.m 1/2 . With no addition of Ti 2 Compared with WC-Co hard alloy of AlC, the hardness of the alloy is obviously improved, and the excellent toughness is kept. Therefore, the hard alloy prepared by the invention has the advantages of high hardness, good toughness and the like. The invention has the advantages of relatively simple raw material preparation, process and equipment and low manufacturing cost.
The above description is only for the specific embodiments of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art can easily conceive of the changes or substitutions within the technical scope of the present invention, and all the changes or substitutions should be covered within the scope of the present invention. Therefore, the protection scope of the present invention should be protected by the following claims.
Claims (10)
1. The preparation method of the high-hardness high-toughness hard alloy is characterized by comprising the following steps of:
s1, mixing Ti 2 Mixing AlC with tungsten carbide and cobalt powder to obtain hard alloy raw materialThe hard alloy comprises the following components in percentage by mass: 75-93.8% of tungsten carbide, 6-15% of cobalt powder and Ti 2 AlC 0.2～10％；
S2, mixing the hard alloy raw material with a forming agent, performing ball milling, and drying to obtain hard alloy mixed powder;
s3, pressing the obtained hard alloy mixed powder to obtain a formed green body;
s4, sintering the molded green body in the S3 at low pressure to obtain WC-Co-Ti with high hardness and high toughness 2 AlC hard alloy, wherein the sintering process comprises the following steps: degreasing, sintering, heat preservation and cooling.
2. The method for producing a hard alloy having high hardness and high toughness according to claim 1, wherein the tungsten carbide, the cobalt powder, and the Ti in the hard alloy raw material 2 The grain sizes of AlC are 0.2-2.0 μm, 0.5-2.0 μm and 3.0-5.0 μm respectively.
3. The method for producing a hard alloy having high hardness and high toughness according to claim 1, wherein the forming agent is paraffin wax or polyethylene glycol, and the mass ratio of the hard alloy material to the forming agent is 1 (0.01 to 0.03).
4. The preparation method of the hard alloy with high hardness and high toughness according to claim 1, wherein the ball milling medium is absolute ethyl alcohol, the ball milling time is 24-72 hours, the ball milling rotation speed is 250-500 r/min, and the ball-to-material ratio of the ball milling is (5-10): 1.
5. The method for preparing a hard alloy having high hardness and high toughness according to claim 1, wherein the drying is vacuum drying or spray drying, the drying temperature is 75 to 90 ℃, and the drying time is 6 to 8 hours.
6. The method for preparing a hard alloy having high hardness and high toughness according to claim 1, wherein the pressing pressure is 150 to 350MPa, and the dwell time is 0.5 to 5min.
7. The method for producing a hard alloy having high hardness and high toughness according to claim 1, wherein the green compact is formed under a vacuum of 1.0 to 5.0 x 10 -3 And under the Pa condition, heating from room temperature to 1200 ℃, starting to introduce argon under the pressure of 1-10 MPa, continuously heating to the sintering temperature, performing low-pressure sintering, then cooling to 1200 ℃, and stopping introducing argon.
8. The method for preparing a hard alloy with high hardness and high toughness according to claim 7, wherein the low pressure sintering is carried out at a temperature of 1320-1510 ℃ under a pressure of 1-10 MPa.
9. The method for preparing a hard alloy with high hardness and high toughness according to claim 1, wherein the sintering stage is high liquid phase sintering, the holding time of the holding stage is 0.5-2 h, and the cooling mode of the cooling stage is furnace cooling.
10. High-hardness high-toughness WC-Co-Ti prepared in the method for preparing the high-hardness high-toughness cemented carbide according to any one of claims 1 to 9 2 And AlC hard alloy.
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Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2003104507A1 (en) * | 2002-06-10 | 2003-12-18 | Kennametal Widia Gmbh & Co. Kg | Hard metal substrate body and method for producing the same |
| US20090041609A1 (en) * | 2007-08-07 | 2009-02-12 | Duz Volodymyr A | High-strength discontinuously-reinforced titanium matrix composites and method for manufacturing the same |
| JP2009120902A (en) * | 2007-11-14 | 2009-06-04 | Sumitomo Electric Ind Ltd | Laminated structure type cemented carbide, its manufacturing method, and tool made of the cemented carbide |
| CN105200252A (en) * | 2014-06-24 | 2015-12-30 | 江苏朗亿新材料有限公司 | Novel high-conductivity and high-abrasion-resistance aluminum matrix composite |
| US20190071792A1 (en) * | 2016-04-14 | 2019-03-07 | Sumitomo Electric Hardmetal Corp. | Surface-coated cutting tool and method of producing the same |
| CN112430769A (en) * | 2020-10-15 | 2021-03-02 | 岭南师范学院 | Wear-resistant WC-Co-Ti3SiC2Hard alloy and preparation method thereof |
| CN114672712A (en) * | 2022-04-13 | 2022-06-28 | 西安理工大学 | Layered Mo2TiAlC2Toughened molybdenum-silicon-boron alloy and preparation method thereof |
| CN115353395A (en) * | 2022-09-23 | 2022-11-18 | 哈尔滨新干线轨道交通科技有限公司 | Preparation of Ti 2 AlC/B 4 Method for preparing C complex phase ceramic |
-
2022
- 2022-12-23 CN CN202211662732.8A patent/CN115971477A/en active Pending
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2003104507A1 (en) * | 2002-06-10 | 2003-12-18 | Kennametal Widia Gmbh & Co. Kg | Hard metal substrate body and method for producing the same |
| US20090041609A1 (en) * | 2007-08-07 | 2009-02-12 | Duz Volodymyr A | High-strength discontinuously-reinforced titanium matrix composites and method for manufacturing the same |
| JP2009120902A (en) * | 2007-11-14 | 2009-06-04 | Sumitomo Electric Ind Ltd | Laminated structure type cemented carbide, its manufacturing method, and tool made of the cemented carbide |
| CN105200252A (en) * | 2014-06-24 | 2015-12-30 | 江苏朗亿新材料有限公司 | Novel high-conductivity and high-abrasion-resistance aluminum matrix composite |
| US20190071792A1 (en) * | 2016-04-14 | 2019-03-07 | Sumitomo Electric Hardmetal Corp. | Surface-coated cutting tool and method of producing the same |
| CN112430769A (en) * | 2020-10-15 | 2021-03-02 | 岭南师范学院 | Wear-resistant WC-Co-Ti3SiC2Hard alloy and preparation method thereof |
| CN114672712A (en) * | 2022-04-13 | 2022-06-28 | 西安理工大学 | Layered Mo2TiAlC2Toughened molybdenum-silicon-boron alloy and preparation method thereof |
| CN115353395A (en) * | 2022-09-23 | 2022-11-18 | 哈尔滨新干线轨道交通科技有限公司 | Preparation of Ti 2 AlC/B 4 Method for preparing C complex phase ceramic |
Non-Patent Citations (3)
| Title |
|---|
| SHTANSKY. D. V: "Comparative investigation of TiAlC(N), and CrAlC(N) coatings deposited by sputtering of MAX-phase Ti2-xCrxAlC targets", 《SURFACE & COATINGS TECHNOLOGY》, 15 December 2009 (2009-12-15), pages 3595 - 3609 * |
| 李云明: "原位合成Ti2AlC/TiAl复合材料的显微组织与性能", 《特种铸造及有色合金》, 29 February 2008 (2008-02-29), pages 145 - 147 * |
| 李萌: "烧结温度对WC-Co-Ti3SiC2硬质合金微观组织与力学性能的影响", 《稀有金属材料与工程》, 31 July 2023 (2023-07-31), pages 2653 - 2657 * |
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