CN114635069A - High-strength-toughness medium-entropy alloy binding phase Ti (C, N) -based metal ceramic and preparation method thereof - Google Patents
High-strength-toughness medium-entropy alloy binding phase Ti (C, N) -based metal ceramic and preparation method thereof Download PDFInfo
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- 238000002360 preparation method Methods 0.000 title claims abstract description 17
- 229910052751 metal Inorganic materials 0.000 title claims description 27
- 239000002184 metal Substances 0.000 title claims description 27
- 239000000919 ceramic Substances 0.000 title claims description 21
- 239000011195 cermet Substances 0.000 claims abstract description 24
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 12
- 239000000654 additive Substances 0.000 claims abstract description 10
- 230000000996 additive effect Effects 0.000 claims abstract description 10
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 10
- 229910003178 Mo2C Inorganic materials 0.000 claims abstract description 3
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- 229910010293 ceramic material Inorganic materials 0.000 claims description 5
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- 238000011049 filling Methods 0.000 claims description 5
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- 238000002490 spark plasma sintering Methods 0.000 claims description 3
- 239000003973 paint Substances 0.000 claims 1
- 238000004663 powder metallurgy Methods 0.000 abstract description 3
- 238000009776 industrial production Methods 0.000 abstract description 2
- 239000011230 binding agent Substances 0.000 abstract 2
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 9
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- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
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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
- C22C29/04—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 carbonitrides
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- B—PERFORMING OPERATIONS; TRANSPORTING
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- 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
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- 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
- B22F3/24—After-treatment of workpieces or articles
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- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
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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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- 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
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- 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
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- 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
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- B22F2003/248—Thermal after-treatment
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- B22F9/00—Making metallic powder or suspensions thereof
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- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
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Abstract
The invention discloses a high strength and toughness medium entropy alloy bonding phase Ti (C, N)-based cermet and a preparation method thereof, which relates to the technical field of powder metallurgy. It comprises the following components by mass: hard phase 47-80, binder phase 12-33 and additive phase 8-20; The hard phase is one or more of Ti (C0.4, N0.6), Ti (C0.5, N0.5) and Ti (C0.6, N0.4); The binder phase is a CoCrNi medium entropy alloy, wherein the molar percentage of Co, Cr and Ni is 1: 1: 1; The added phase is one or more of WC, Mo2C, NbC, TaC, VC, AlN and C. The invention has the advantages of high strength and toughness, high wear resistance, excellent high temperature performance, simple preparation process, good reproducibility, suitability for large-scale industrial production and the like, and has great industrial application value and broad application prospect in the fields of numerical control machine tools, high temperature resistant dies and the like.
Description
Technical Field
The invention relates to the technical field of powder metallurgy, in particular to high-strength and high-toughness medium-entropy alloy binding phase Ti (C, N) -based metal ceramic and a preparation method thereof.
Background
The Ti (C, N) -based cermet is a composite material prepared by a powder metallurgy method by using Ti (C, N) as a hard phase and nickel and molybdenum as metal bonding phases. Compared with the traditional hard alloy, the Ti (C, N) -based metal ceramic has the excellent performances of high hardness, wear resistance, corrosion resistance, high-temperature oxidation resistance and the like, and the cost is much lower than that of the hard alloy. Therefore, Ti (C, N) cermet can be used as an upgraded substitute product of hard alloy in many fields, and is currently applied to machining, mold manufacturing and petrochemical industry.
In the chinese patent 201810611621.1, CrNiFeCoAlCuZrMoRe high-entropy alloy pre-alloyed powder is used as a bonding phase of Ti (C, N) cermet instead of Ni or Co, and the toughness of the cermet is improved by using the high hardness and high toughness of the high-entropy alloy. However, the crnifecoalcuzrmorey multi-principal element high-entropy alloy has more element types, obvious solid solution strengthening effect, difficult dislocation movement and crystal face slippage and larger brittleness, so that the wettability between the high-entropy alloy pre-alloyed powder and a Ti (C, N) hard phase is poorer in the sintering process of the metal ceramic, the defects of holes and the like are easy to occur in the sintering process of the metal ceramic, the sintering is difficult to compact, and the brittleness is larger. In addition, the pre-synthesized high-entropy alloy powder can experience high temperature again in the sintering process of the metal ceramic, so that the diffusion of multi-principal element elements is more sufficient, the lattice distortion is reduced, and the performance of the high-entropy alloy matrix is deteriorated. Generally speaking, the greater brittleness of the high-entropy alloy and the higher sintering temperature of the cermet are the keys for limiting the performance of the cermet of the binding phase of the high-entropy alloy.
Compared with high-entropy alloy, the medium-entropy alloy has better shaping and fracture toughness, and the CoCrNi medium-entropy alloy is a typical FCC structure medium-entropy alloy which has excellent toughness at room temperature and low temperature. The invention takes CoCrNi medium entropy alloy as a binding phase, and prepares Ti (C, N) -based cermet with high obdurability in situ by rapid sintering and rapid cooling of spark plasma sintering.
Disclosure of Invention
The invention aims to provide a high-strength-toughness medium-entropy alloy binding phase Ti (C, N) -based metal ceramic and a preparation method thereof, aiming at the defects in the prior art.
In order to achieve the purpose, the invention adopts the following technical scheme: a high-strength toughness medium-entropy alloy binding phase Ti (C, N) -based metal ceramic and a preparation method thereof comprise the following components in parts by mass: 47-80 hard phase, 12-33 binding phase and 8-20 additive phase; the hard phase is one or more of Ti (C0.4, N0.6), Ti (C0.5, N0.5) and Ti (C0.6, N0.4); the binding phase is CoCrNi medium entropy alloy, wherein the mole percentage of Co, Cr and Ni is 1: 1: 1; the additive phase is one or more of WC, Mo2C, NbC, TaC, VC, AlN and C.
The preparation method of the high-strength-toughness medium-entropy alloy binding phase Ti (C, N) -based metal ceramic comprises the following steps: pre-preparing CoCrNi intermediate entropy alloy powder: weighing and mixing Co, Cr and Ni powder according to the component requirements, placing the mixed powder in a stainless steel ball milling tank, and preparing CoCrNi intermediate entropy alloy prefabricated powder through mechanical alloying; material mixing and ball milling: weighing and mixing the prepared medium-entropy alloy powder, the hard phase and the additive phase powder according to the component requirements, and then putting the mixture into a planetary ball mill for wet milling; sintering the metal ceramic: drying the ball-milled slurry by a spray drying method, then filling the dried powder into a graphite die, and preparing the metal ceramic material by adopting a discharge plasma sintering mode; high-temperature annealing post-treatment: the cermet material is placed in a box-type heat treatment furnace for high-temperature annealing post-treatment, so that the strength and the shape of the medium-entropy alloy binding phase and the interface binding force between the medium-entropy alloy and the hard phase are further improved.
More optimally, the granularity of Co, Cr and Ni powder in the CoCrNi intermediate entropy alloy powder prefabrication is 2-5 mu m, and the purity is more than or equal to 99.5%.
More preferably, the mechanical alloying process parameters in the CoCrNi intermediate entropy alloy powder prefabrication are as follows: the ball material ratio is 20: 1, the rotation speed of the ball mill is 350rpm, the ball milling tank is filled with Ar gas protective atmosphere, the total ball milling time is 12 hours, and cooling is stopped for 10 minutes every 60 minutes.
More preferably, the wet milling process parameters in the material mixing and ball milling are as follows: the ball material ratio is 8:1, the rotation speed of the ball mill is 250rpm, and the ball milling medium is absolute ethyl alcohol.
More preferably, the discharge plasma sintering process parameters in the cermet sintering are as follows: the vacuum degree is 10 < -3 > to 10 < -5 > Pa, the sintering temperature is 1250 ℃ to 1450 ℃, the heating rate is 100 ℃/min, the heat preservation time is 30min, and the sintering pressure is 30MPa to 45 MPa.
More preferably, the process parameters of the high-temperature annealing in the high-temperature annealing post-treatment are as follows: 900-950 ℃, the annealing time is 1-3 hours, and the cooling mode is furnace cooling.
After the technical scheme is adopted, the invention has the beneficial effects that:
1. the CoCrNi intermediate entropy alloy prefabricated powder prepared by mechanical alloying has fine and uniform grain diameter, average grain size of 0.5-1.5 mu m and lower surface oxygen content, and is beneficial to subsequent sintering of cermet materials;
2. the method adopts a spark plasma sintering method to prepare the metal ceramic, and the sintering process can ensure high temperature rise rate and cooling rate, on one hand, can ensure that the entropy alloy binding phase in CoCrNi keeps higher lattice distortion and improves the toughness of the binding phase, on the other hand, is beneficial to obtaining the metal ceramic with ultra-fine grains and can also improve the strength and the hardness of the material;
3. ti, Al and other elements can be dissolved in the CoCrNi medium-entropy alloy bonding phase in a solid solution mode, and an uneven precipitated phase can be generated in the bonding phase after high-temperature annealing, so that the strength and the shape of the medium-entropy alloy bonding phase can be further improved;
4. the Ti (C, N) -based metal ceramic prepared by the invention takes CoCrNi intermediate entropy alloy as a binding phase, and the intermediate entropy alloy has good obdurability, high-temperature oxidation resistance and wear resistance, so that the metal ceramic has higher obdurability, high-temperature performance and wear resistance, and the application range of the material is expanded;
5. the medium-entropy alloy binding phase Ti (C, N) -based metal ceramic has the advantages of high strength and toughness, high wear resistance, excellent high-temperature performance, simple preparation process, good reproducibility, suitability for large-scale industrial production and the like, and has great industrial application value and wide application prospect in the fields of numerical control machine tools, high-temperature-resistant dies and the like.
Detailed Description
The invention is further described below. The following examples are only for illustrating the technical solutions of the present invention more clearly, and the protection scope of the present invention is not limited thereby.
Table 1 is a blend of 7 ingredient formulations. Different process parameters are adopted to prepare the medium-entropy alloy binding phase Ti (C, N) -based cermet, and the hardness, the bending strength and the fracture toughness of the cermet are respectively measured.
Table 1 cermet compositions of the four component formulations
TABLE 2 composition formula (mol%) of CoCrNi mid-entropy alloy
| Composition (I) | Co | Cr | Ni |
| CoCrNi medium entropy alloy | 33.34 | 33.33 | 33.33 |
Example one
(1) Pre-preparing CoCrNi intermediate entropy alloy powder: weighing and mixing high-purity Co, Cr and Ni powder (the granularity is 2-5 mu m, the purity is more than or equal to 99.5%) according to the component requirements, placing the mixed powder into a stainless steel ball milling tank, and preparing CoCrNi intermediate entropy alloy prefabricated powder through mechanical alloying, wherein the mechanical alloying process parameters are as follows: the ball material ratio is 20: 1, the rotating speed of the ball mill is 350rpm, Ar gas protective atmosphere is filled in a ball milling tank, the total ball milling time is 12 hours, and cooling is stopped for 10 minutes every 60 minutes;
(2) material mixing and ball milling: weighing and mixing the prepared intermediate entropy alloy powder, hard phase and additive phase powder according to component requirements, and then placing the mixture into a planetary ball mill for wet milling, wherein the technological parameters of the wet milling are as follows: the ball-material ratio is 8:1, the rotation speed of the ball mill is 250rpm, and the ball milling medium is absolute ethyl alcohol;
(3) sintering the metal ceramic: drying the ball-milled slurry by a spray drying method, then filling the dried powder into a graphite die, and preparing the metal ceramic material by adopting a discharge plasma sintering mode, wherein the sintering process parameters are as follows: the vacuum degree is 10-5Pa, the sintering temperature is 1350 ℃, the heating rate is 100 ℃/min, the heat preservation time is 30min, and the sintering pressure is 30 MPa.
(4) High-temperature annealing post-treatment: and (3) placing the cermet material in a box-type heat treatment furnace, and carrying out high-temperature annealing post-treatment at 900 ℃ for 3 hours, wherein the cooling mode is furnace cooling so as to improve the strength and the plasticity of the CoCrNi medium-entropy alloy binding phase and improve the interface bonding between the medium-entropy alloy and the hard phase.
The material obtained in this example was subjected to performance testing, and the results are shown in table 3.
TABLE 3 mechanical Properties of the different cermets prepared in example 1
| Composition (I) | 1# | 2# | 3# | 4# | 5# |
| Bending Strength σ b (MPa) | 1955 | 2150 | 2275 | 2505 | 2660 |
| Hardness (HRA) | 93.3 | 92.5 | 92.2 | 91.6 | 90.9 |
| Fracture toughness (MN. m-3/2) | 8.5 | 8.8 | 9.8 | 11.8 | 13.8 |
Example two
(1) Pre-preparing CoCrNi intermediate entropy alloy powder: weighing and mixing high-purity Co, Cr and Ni powder (the granularity is 2-5 mu m, the purity is more than or equal to 99.5%) according to the component requirements, placing the mixed powder into a stainless steel ball milling tank, and preparing CoCrNi intermediate entropy alloy prefabricated powder through mechanical alloying, wherein the mechanical alloying process parameters are as follows: the ball material ratio is 20: 1, the rotating speed of the ball mill is 350rpm, Ar gas protective atmosphere is filled in a ball milling tank, the total ball milling time is 12 hours, and cooling is stopped for 10 minutes every 60 minutes;
(2) material mixing and ball milling: weighing and mixing the prepared intermediate entropy alloy powder, hard phase and additive phase powder according to component requirements, and then placing the mixture into a planetary ball mill for wet milling, wherein the technological parameters of the wet milling are as follows: the ball-material ratio is 8:1, the rotation speed of the ball mill is 250rpm, and the ball milling medium is absolute ethyl alcohol;
(3) sintering the metal ceramic: drying the ball-milled slurry by a spray drying method, then filling the dried powder into a graphite die, and preparing the metal ceramic material by adopting a discharge plasma sintering mode, wherein the sintering process parameters are as follows: the vacuum degree is 10-5Pa, the sintering temperature is 1300 ℃, the heating rate is 100 ℃/min, the heat preservation time is 45min, and the sintering pressure is 40 MPa.
(4) High-temperature annealing post-treatment: and (3) placing the cermet material in a box-type heat treatment furnace, and carrying out high-temperature annealing post-treatment at 950 ℃ for 2 hours, wherein the cooling mode is furnace cooling so as to improve the strength and the plasticity of the CoCrNi intermediate entropy alloy binding phase and improve the interface bonding between the intermediate entropy alloy and the hard phase.
The material obtained in this example was subjected to performance testing, and the results are shown in table 3.
TABLE 4 mechanical Properties of the different cermets prepared in example 1
| Composition (I) | 1# | 2# | 3# | 4# | 5# |
| Bending Strength σ b (MPa) | 1880 | 2070 | 2250 | 2570 | 2710 |
| Hardness (HRA) | 93.5 | 92.8 | 92.5 | 91.3 | 90.5 |
| Fracture toughness (MN. m-3/2) | 8.6 | 9.2 | 10.3 | 11.5 | 13.6 |
EXAMPLE III
(1) Pre-preparing CoCrNi intermediate entropy alloy powder: weighing and mixing high-purity Co, Cr and Ni powder (the granularity is 2-5 mu m, the purity is more than or equal to 99.5%) according to the component requirements, placing the mixed powder into a stainless steel ball milling tank, and preparing CoCrNi intermediate entropy alloy prefabricated powder through mechanical alloying, wherein the mechanical alloying process parameters are as follows: the ball material ratio is 20: 1, the rotating speed of the ball mill is 400rpm, Ar gas protective atmosphere is filled in a ball milling tank, the total ball milling time is 12 hours, and cooling is stopped for 10 minutes every 60 minutes;
(2) material mixing and ball milling: weighing and mixing the prepared intermediate entropy alloy powder, hard phase and additive phase powder according to component requirements, and then placing the mixture into a planetary ball mill for wet milling, wherein the technological parameters of the wet milling are as follows: the ball-material ratio is 8:1, the rotation speed of the ball mill is 300rpm, and the ball milling medium is absolute ethyl alcohol;
(3) sintering the metal ceramic: drying the ball-milled slurry by a spray drying method, then filling the dried powder into a graphite die, and preparing the metal ceramic material by adopting a discharge plasma sintering mode, wherein the sintering process parameters are as follows: the vacuum degree is 10-3Pa, the sintering temperature is 1200 ℃, the heating rate is 100 ℃/min, the heat preservation time is 60min, and the sintering pressure is 45 MPa.
(4) High-temperature annealing post-treatment: and (3) placing the cermet material in a box-type heat treatment furnace, and carrying out high-temperature annealing post-treatment at 950 ℃ for 1 hour, wherein the cooling mode is furnace cooling so as to improve the strength and the plasticity of the CoCrNi intermediate entropy alloy binding phase and improve the interface bonding between the intermediate entropy alloy and the hard phase.
The material obtained in this example was subjected to performance testing, and the results are shown in table 3.
TABLE 5 mechanical Properties of the different cermets prepared in example 1
| Composition (I) | 1# | 2# | 3# | 4# | 5# |
| Bending Strength σ b (MPa) | 1820 | 2100 | 2210 | 2475 | 2810 |
| Hardness (HRA) | 93.1 | 92.2 | 92.8 | 91.8 | 90.3 |
| Fracture toughness (MN. m-3/2) | 7.8 | 8.5 | 10.3 | 11.0 | 14.5 |
。
The above description is only for the purpose of illustrating the technical solutions of the present invention and not for the purpose of limiting the same, and other modifications or equivalent substitutions made by those skilled in the art to the technical solutions of the present invention should be covered within the scope of the claims of the present invention without departing from the spirit and scope of the technical solutions of the present invention.
Claims (7)
1. A high-strength toughness medium-entropy alloy binding phase Ti (C, N) -based cermet is characterized in that: the paint comprises the following components in parts by weight: 47-80 hard phase, 12-33 binding phase and 8-20 additive phase; the hard phase is one or more of Ti (C0.4, N0.6), Ti (C0.5, N0.5) and Ti (C0.6, N0.4); the binding phase is CoCrNi medium entropy alloy, wherein the mole percentage of Co, Cr and Ni is 1: 1: 1; the additive phase is one or more of WC, Mo2C, NbC, TaC, VC, AlN and C.
2. A preparation method of high-strength-toughness medium-entropy alloy binding phase Ti (C, N) -based metal ceramic is characterized by comprising the following steps: the preparation method comprises the following steps:
1) pre-preparing CoCrNi intermediate entropy alloy powder: weighing and mixing Co, Cr and Ni powder according to the component requirements, placing the mixed powder in a stainless steel ball milling tank, and preparing CoCrNi intermediate entropy alloy prefabricated powder through mechanical alloying;
2) material preparation and ball milling: weighing and mixing the prepared medium-entropy alloy powder, the hard phase and the additive phase powder according to the component requirements, and then putting the mixture into a planetary ball mill for wet milling;
3) sintering the metal ceramic: drying the ball-milled slurry by a spray drying method, then filling the dried powder into a graphite die, and preparing the metal ceramic material by adopting a discharge plasma sintering mode;
4) and (3) high-temperature annealing post-treatment: the cermet material is placed in a box-type heat treatment furnace for high-temperature annealing post-treatment, so that the strength and the shape of the medium-entropy alloy binding phase and the interface binding force between the medium-entropy alloy and the hard phase are further improved.
3. The preparation method of the high-toughness medium-entropy alloy binding phase Ti (C, N) -based cermet according to claim 2, is characterized in that: in the step 1, the granularity of Co, Cr and Ni powder is 2-5 mu m, and the purity is more than or equal to 99.5%.
4. The preparation method of the high-toughness medium-entropy alloy binding phase Ti (C, N) -based cermet according to claim 2, is characterized in that: the mechanical alloying in the step 1 comprises the following process parameters: the ball material ratio is 20: 1, the rotating speed of the ball mill is 350rpm, the ball milling tank is filled with Ar gas protective atmosphere, the total ball milling time is 12 hours, and cooling is stopped for 10 minutes every 60 minutes.
5. The preparation method of the high-toughness medium-entropy alloy binding phase Ti (C, N) -based cermet according to claim 2, is characterized in that: the wet grinding process parameters in the step 2 are as follows: the ball-material ratio is 8:1, the rotation speed of the ball mill is 250rpm, and the ball milling medium is absolute ethyl alcohol.
6. The preparation method of the high-toughness medium-entropy alloy binding phase Ti (C, N) -based cermet according to claim 2, is characterized in that: the technological parameters of the spark plasma sintering in the step 3 are as follows: the vacuum degree is 10 < -3 > to 10 < -5 > Pa, the sintering temperature is 1250 ℃ to 1450 ℃, the heating rate is 100 ℃/min, the heat preservation time is 30min, and the sintering pressure is 30MPa to 45 MPa.
7. The preparation method of the high-toughness medium-entropy alloy binding phase Ti (C, N) -based cermet according to claim 2, is characterized in that: the process parameters of the high-temperature annealing in the step 4 are as follows: 900-950 ℃, the annealing time is 1-3 hours, and the cooling mode is furnace cooling.
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| CN115198159A (en) * | 2022-06-19 | 2022-10-18 | 西北工业大学 | Graphite-reinforced CoCrNi intermediate entropy alloy solid self-lubricating material and in-situ preparation method |
| CN115418542A (en) * | 2022-07-12 | 2022-12-02 | 杭州巨星科技股份有限公司 | Nano modified metal ceramic cutter material and preparation method thereof |
| WO2023232158A1 (en) * | 2022-11-24 | 2023-12-07 | 常州大学 | Medical degradable znmgca medium-entropy alloy, and preparation method therefor and use thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN115198159A (en) * | 2022-06-19 | 2022-10-18 | 西北工业大学 | Graphite-reinforced CoCrNi intermediate entropy alloy solid self-lubricating material and in-situ preparation method |
| CN115198159B (en) * | 2022-06-19 | 2023-08-25 | 西北工业大学 | Graphite reinforced CoCrNi medium entropy alloy solid self-lubricating material and in-situ preparation method thereof |
| CN115418542A (en) * | 2022-07-12 | 2022-12-02 | 杭州巨星科技股份有限公司 | Nano modified metal ceramic cutter material and preparation method thereof |
| WO2023232158A1 (en) * | 2022-11-24 | 2023-12-07 | 常州大学 | Medical degradable znmgca medium-entropy alloy, and preparation method therefor and use thereof |
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