CN111485155A - (Ti, W) C-based metal ceramic cutting tool material added with alumina coated cubic boron nitride composite powder and preparation method thereof - Google Patents
(Ti, W) C-based metal ceramic cutting tool material added with alumina coated cubic boron nitride composite powder and preparation method thereof Download PDFInfo
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- 239000000843 powder Substances 0.000 title claims abstract description 97
- 229910052582 BN Inorganic materials 0.000 title claims abstract description 87
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 title claims abstract description 87
- 239000002131 composite material Substances 0.000 title claims abstract description 82
- 229910052719 titanium Inorganic materials 0.000 title claims abstract description 80
- 239000000463 material Substances 0.000 title claims abstract description 76
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 title claims abstract description 72
- 229910052721 tungsten Inorganic materials 0.000 title claims abstract description 71
- 239000000919 ceramic Substances 0.000 title claims abstract description 44
- 238000005520 cutting process Methods 0.000 title claims abstract description 42
- 229910052751 metal Inorganic materials 0.000 title claims abstract description 36
- 239000002184 metal Substances 0.000 title claims abstract description 36
- 238000002360 preparation method Methods 0.000 title abstract description 14
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims abstract description 63
- 238000005245 sintering Methods 0.000 claims abstract description 40
- 238000007731 hot pressing Methods 0.000 claims abstract description 35
- 239000010941 cobalt Substances 0.000 claims abstract description 29
- 229910017052 cobalt Inorganic materials 0.000 claims abstract description 29
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims abstract description 29
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 29
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims abstract description 27
- 239000011733 molybdenum Substances 0.000 claims abstract description 27
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 27
- 239000002994 raw material Substances 0.000 claims abstract description 14
- 238000000034 method Methods 0.000 claims abstract description 11
- 239000011259 mixed solution Substances 0.000 claims description 55
- 239000007788 liquid Substances 0.000 claims description 52
- 239000006185 dispersion Substances 0.000 claims description 51
- 239000002202 Polyethylene glycol Substances 0.000 claims description 47
- 229920001223 polyethylene glycol Polymers 0.000 claims description 47
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 45
- 238000000498 ball milling Methods 0.000 claims description 45
- 239000011195 cermet Substances 0.000 claims description 26
- 239000000243 solution Substances 0.000 claims description 23
- 239000004698 Polyethylene Substances 0.000 claims description 21
- -1 polyethylene Polymers 0.000 claims description 21
- 229920000573 polyethylene Polymers 0.000 claims description 21
- 238000002156 mixing Methods 0.000 claims description 20
- 238000001035 drying Methods 0.000 claims description 17
- CTQNGGLPUBDAKN-UHFFFAOYSA-N O-Xylene Chemical compound CC1=CC=CC=C1C CTQNGGLPUBDAKN-UHFFFAOYSA-N 0.000 claims description 16
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 16
- 239000008096 xylene Substances 0.000 claims description 16
- 239000002245 particle Substances 0.000 claims description 14
- 238000005406 washing Methods 0.000 claims description 14
- 239000000956 alloy Substances 0.000 claims description 13
- DBMJMQXJHONAFJ-UHFFFAOYSA-M Sodium laurylsulphate Chemical compound [Na+].CCCCCCCCCCCCOS([O-])(=O)=O DBMJMQXJHONAFJ-UHFFFAOYSA-M 0.000 claims description 12
- 239000011812 mixed powder Substances 0.000 claims description 10
- 238000000926 separation method Methods 0.000 claims description 10
- VHUUQVKOLVNVRT-UHFFFAOYSA-N Ammonium hydroxide Chemical compound [NH4+].[OH-] VHUUQVKOLVNVRT-UHFFFAOYSA-N 0.000 claims description 9
- 235000011114 ammonium hydroxide Nutrition 0.000 claims description 9
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 8
- 229910045601 alloy Inorganic materials 0.000 claims description 8
- 229910002804 graphite Inorganic materials 0.000 claims description 8
- 239000010439 graphite Substances 0.000 claims description 8
- 238000004321 preservation Methods 0.000 claims description 8
- 238000001354 calcination Methods 0.000 claims description 7
- 238000001816 cooling Methods 0.000 claims description 7
- 238000007873 sieving Methods 0.000 claims description 7
- 239000011261 inert gas Substances 0.000 claims description 6
- IDGUHHHQCWSQLU-UHFFFAOYSA-N ethanol;hydrate Chemical compound O.CCO IDGUHHHQCWSQLU-UHFFFAOYSA-N 0.000 claims description 4
- 238000004519 manufacturing process Methods 0.000 claims 1
- 238000005452 bending Methods 0.000 abstract description 11
- 239000011258 core-shell material Substances 0.000 abstract description 9
- 230000002159 abnormal effect Effects 0.000 abstract description 3
- 239000011159 matrix material Substances 0.000 abstract description 2
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 abstract 1
- 239000010931 gold Substances 0.000 abstract 1
- 229910052737 gold Inorganic materials 0.000 abstract 1
- 230000009466 transformation Effects 0.000 abstract 1
- 239000010936 titanium Substances 0.000 description 61
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 18
- 239000012071 phase Substances 0.000 description 16
- 238000000227 grinding Methods 0.000 description 15
- 238000003756 stirring Methods 0.000 description 13
- 238000005303 weighing Methods 0.000 description 13
- 229910052757 nitrogen Inorganic materials 0.000 description 11
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 9
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 description 9
- 230000000052 comparative effect Effects 0.000 description 6
- 238000010438 heat treatment Methods 0.000 description 6
- 238000010907 mechanical stirring Methods 0.000 description 6
- 238000005498 polishing Methods 0.000 description 6
- 238000001132 ultrasonic dispersion Methods 0.000 description 6
- 239000011230 binding agent Substances 0.000 description 5
- 229910052593 corundum Inorganic materials 0.000 description 5
- 239000010410 layer Substances 0.000 description 5
- MAKDTFFYCIMFQP-UHFFFAOYSA-N titanium tungsten Chemical compound [Ti].[W] MAKDTFFYCIMFQP-UHFFFAOYSA-N 0.000 description 5
- 229910001845 yogo sapphire Inorganic materials 0.000 description 5
- 239000000203 mixture Substances 0.000 description 4
- 238000001878 scanning electron micrograph Methods 0.000 description 4
- 229910009043 WC-Co Inorganic materials 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 238000001291 vacuum drying Methods 0.000 description 3
- 238000009736 wetting Methods 0.000 description 3
- 229910052799 carbon Inorganic materials 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 239000011248 coating agent Substances 0.000 description 2
- 238000000576 coating method Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 238000010183 spectrum analysis Methods 0.000 description 2
- 239000000853 adhesive Substances 0.000 description 1
- 230000001070 adhesive effect Effects 0.000 description 1
- WNROFYMDJYEPJX-UHFFFAOYSA-K aluminium hydroxide Chemical compound [OH-].[OH-].[OH-].[Al+3] WNROFYMDJYEPJX-UHFFFAOYSA-K 0.000 description 1
- 229910021502 aluminium hydroxide Inorganic materials 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000003153 chemical reaction reagent Substances 0.000 description 1
- 238000005253 cladding Methods 0.000 description 1
- 239000011247 coating layer Substances 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 229910001679 gibbsite Inorganic materials 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 238000001000 micrograph Methods 0.000 description 1
- 239000002105 nanoparticle Substances 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 239000003870 refractory metal Substances 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
Images
Classifications
-
- 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
-
- B22F1/0003—
-
- 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
-
- 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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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Cutting Tools, Boring Holders, And Turrets (AREA)
- Powder Metallurgy (AREA)
- Ceramic Products (AREA)
Abstract
The invention relates to a (Ti, W) C-based metal ceramic cutting tool material added with alumina coated cubic boron nitride composite powder and a preparation method thereof, wherein the cutting tool material is prepared by hot-pressing and sintering the following main raw materials in percentage by mass: 2-8% of cobalt, 1-5% of nickel, 5-10% of molybdenum, 1-20% of alumina-coated cubic boron nitride composite powder and the balance of (Ti, W) C; the sum of the mass percentages of the components is 100 percent. The cutting tool material of the invention forms Al with (Ti, W) C as a ceramic matrix, C-BN as a core2O3A multi-layer core-shell microstructure with an intermediate layer and a metal phase as a shell; effectively improves the compactness of the cutter material, relieves the stress concentration and gold of the internal interface of the cutterThe method belongs to the problem of abnormal growth of ceramic grains, solves the problem of reduced mechanical property caused by the transformation of c-BN to h-BN at high temperature, and the obtained cutter material has better mechanical property, particularly greatly improved bending strength and fracture toughness.
Description
Background
The (Ti, W) C-based cermet material is a novel solid solution-based cermet developed on the basis of WC-Co series hard alloy and TiC-Ni series cermet; it is a kind of composite material which uses (Ti, W) C as hard phase, at the same time adds WC, TaC and other refractory metal carbide or nitride, and uses cobalt, nickel and other as adhesive. Compared with the traditional WC-Co-based hard alloy, the (Ti, W) C-based metal ceramic cutter has good red hardness, wear resistance, thermal stability, oxidation resistance and adhesion resistance at the high temperature of 700-1100 ℃, has high cutting temperature, improves the cutting speed and the service life by 3-10 times and 2-5 times respectively, has rich main raw material resources and low cost, and is an ideal upgraded substitute product of the WC-Co-based hard alloy high-speed high-efficiency cutter. The presence of WC in (Ti, W) C solid solution makes the wetting of the hard particles with the binder phase better (wetting angle of TiC and Ni at 1450 ℃ under vacuum conditions is 30 °, whereas wetting angle of WC and Ni under the same conditions is 0 °) compared to TiC-Ni based cermet materials. Compared with the Ti (C, N) -based cermet material, the (Ti, W) C does not contain N element, so that the problems of increased pores and reduced strength caused by denitrification during high-temperature sintering of the Ti (C, N) -based cermet material do not exist. Therefore, (Ti, W) C-based cermets are considered as hard composite materials with great potential for development.
Chinese patent document CN106316398A discloses a tungsten carbide titanium-based ceramic cutting tool material added with cubic boron nitride and a preparation method thereof. The cutter material comprises the following raw materials in percentage by mass: 80-84% of micron tungsten titanium carbide, 1-5% of nano cubic boron nitride and 15% of nano cobalt; the invention takes cubic boron nitride as a reinforcing phase, and achieves the effect of particle dispersion reinforcement. However, at high temperature, cubic boron nitride is easy to change phase to hexagonal boron nitride, so that the problem of reduced mechanical property is caused; due to thermal expansion mismatch, the direct addition of cubic boron nitride easily results in large internal stress of the cutter material and low mechanical property. Chinese patent document CN106904947AA self-lubricating ceramic cutting tool material added with h-BN @ Ni core-shell structure composite powder and a preparation method thereof are provided, wherein the raw material components comprise α -Al in percentage by mass2O325-45 percent of (W, Ti) C50-70 percent, 2-10 percent of nickel-coated hexagonal boron nitride composite powder according to the mass of h-BN, and 0.4-1.5 percent of MgO. The invention can greatly improve the fracture toughness of the self-lubricating ceramic cutter material and reduce the sintering temperature of the ceramic cutter material; however, the mechanical property of hexagonal boron nitride is poor, the hardness of a metal phase is low, and the good fracture toughness of the metal can be utilized to improve the overall fracture toughness of the cutter material by coating h-BN with the metal Ni, but the problems of low bending strength and hardness are not solved, and the service performance of the cutter is poor.
Disclosure of Invention
Aiming at the defects in the prior art, the invention provides a (Ti, W) C-based metal ceramic cutting tool material added with alumina coated cubic boron nitride composite powder and a preparation method thereof. The invention is formed by adding alumina coated cubic boron nitride composite powder and metal binding phase molybdenum, nickel and cobalt, wherein (Ti, W) C is used as a ceramic matrix, C-BN is used as a core, and Al2O3A multi-layer core-shell microstructure with an intermediate layer and a metal binder phase as a shell; the obtained multilayer core-shell microstructure improves the compactness of the cutter material, relieves the problems of interface stress concentration inside the (Ti, W) C-based cermet cutter and abnormal growth of cermet grains, and successfully solves the problem of mechanical property reduction caused by phase change of C-BN to h-BN at higher temperature. Compared with the method without coating (namely directly adding c-BN and Al)2O3And metal binder phase), the mechanical properties of the obtained cutter material are improved, and especially the bending strength and the fracture toughness are greatly improved.
Description of terms:
c-BN@Al(OH)3: is the abbreviation of aluminum hydroxide coated cubic boron nitride composite powder;
c-BN@Al2O3: it is a abbreviation of alumina coated cubic boron nitride composite powder.
The technical scheme of the invention is as follows:
a (Ti, W) C-based metal ceramic cutting tool material added with alumina coated cubic boron nitride composite powder is prepared by hot-pressing and sintering the following main raw materials in percentage by mass:
2-8% of cobalt, 1-5% of nickel, 5-10% of molybdenum, 1-20% of alumina-coated cubic boron nitride composite powder and the balance of (Ti, W) C; the sum of the mass percentages of the components is 100 percent;
the alumina-coated cubic boron nitride composite powder is prepared by the following method:
dispersing the c-BN in an absolute ethyl alcohol solution to obtain a mixed solution 1; dispersing sodium dodecyl sulfate and polyethylene glycol in absolute ethyl alcohol to obtain a mixed solution 2; fully and uniformly mixing the mixed solution 1 and the mixed solution 2, reacting for 50-60 min at 70-80 ℃, and cooling, centrifugally separating, washing and drying to obtain modified c-BN powder;
dispersing the modified c-BN powder in absolute ethyl alcohol to obtain c-BN dispersion liquid; mixing Al (NO)3)3And polyethylene glycol dispersed in a mixed solution containing water, xylene and anhydrous ethanol to obtain Al (NO)3)3A solution; mixing Al (NO)3)3Adding the solution into the c-BN dispersion liquid, uniformly mixing, dropwise adding ammonia water to adjust the pH value to 7, reacting for 20-40 min at 70-80 ℃, and obtaining c-BN @ Al (OH) through centrifugal separation, washing and drying3(ii) a Then calcining at the temperature of 900-1200 ℃ under the protection of inert gas to obtain the alumina-coated cubic boron nitride composite powder.
According to the invention, the (Ti, W) C-based metal ceramic cutter material is preferably prepared by hot-pressing and sintering the following main raw materials in percentage by weight: 3-6% of cobalt, 2-4% of nickel, 5-8% of molybdenum, 5-15% of alumina-coated cubic boron nitride composite powder and the balance of (Ti, W) C; the sum of the weight percentages of the components is 100 percent.
According to the invention, the average grain diameter of the alumina coated cubic boron nitride composite powder is 0.3-1.5 μm, the average grain diameter of (Ti, W) C is 2-5 μm, and the average grain diameters of molybdenum, cobalt and nickel are 1-3 μm.
The preparation method of the (Ti, W) C-based metal ceramic cutting tool material added with the alumina coated cubic boron nitride composite powder comprises the following steps:
(1) dispersing polyethylene glycol in absolute ethyl alcohol to form polyethylene glycol-absolute ethyl alcohol dispersion liquid; sequentially dispersing (Ti, W) C, molybdenum, cobalt and nickel in polyethylene glycol-absolute ethyl alcohol dispersion liquid, and then carrying out ball milling for 40-80h under the protection of inert gas to prepare composite powder dispersion liquid;
(2) dispersing the c-BN in an absolute ethyl alcohol solution to obtain a mixed solution 1; dispersing sodium dodecyl sulfate and polyethylene glycol in absolute ethyl alcohol to obtain a mixed solution 2; fully and uniformly mixing the mixed solution 1 and the mixed solution 2, reacting for 50-60 min at 70-80 ℃, and cooling, centrifugally separating, washing and drying to obtain modified c-BN powder;
(3) dispersing the modified c-BN powder in absolute ethyl alcohol to obtain c-BN dispersion liquid; mixing Al (NO)3)3And polyethylene glycol dispersed in a mixed solution containing water, xylene and anhydrous ethanol to obtain Al (NO)3)3A solution; mixing Al (NO)3)3Adding the solution into the c-BN dispersion liquid, uniformly mixing, dropwise adding ammonia water to adjust the pH value to 7, reacting for 20-40 min at 70-80 ℃, and obtaining c-BN @ Al (OH) through centrifugal separation, washing and drying3(ii) a Then calcining for 1-3h at the temperature of 900-;
(4) dispersing the alumina coated cubic boron nitride composite powder in a polyethylene glycol-absolute ethyl alcohol solution to obtain a mixed solution; adding the mixed solution into the composite powder dispersion liquid obtained in the step (1), and continuing ball milling for 1-3 hours under the protection of inert gas; drying and sieving to obtain mixed powder;
(5) and carrying out hot-pressing sintering on the obtained mixed powder in a graphite mold to obtain the (Ti, W) C-based metal ceramic cutter material.
Preferably, in steps (1) to (4), the weight average molecular weight of the polyethylene glycol is 2000-8000; preferably, the weight average molecular weight of the polyethylene glycol is 4000-6000.
According to the invention, the concentration of polyethylene glycol in the polyethylene glycol-absolute ethyl alcohol dispersion liquid in the step (1) is 1-5 g/L, preferably 2-4 g/L.
According to the present invention, in the step (1), the mass content of (Ti, W) C in the composite powder dispersion liquid is preferably 0.2 to 1g/m L.
According to the invention, in the step (1), the ball milling time is 48-60h, the ball milling is performed by using hard alloy ball milling balls, and the mass ratio of the ball milling balls to the materials is 5-15: 1.
According to the invention, in the mixed liquid 1 in the step (2), the mass concentration of c-BN is 0.006-0.009g/m L, the mass ratio of c-BN, sodium dodecyl sulfate and polyethylene glycol is 2-4:1-2:1, and in the mixed liquid 2, the mass concentration of polyethylene glycol is 0.006-0.008 g/ml.
Preferably, according to the invention, in step (2), the c-BN average particle size is from 0.1 to 0.3. mu.m.
According to the present invention, the mass concentration of the modified c-BN powder in the c-BN dispersion liquid in the step (3) is preferably 0.01 to 0.04g/m L.
According to the present invention, in the step (3), the volume ratio of water, xylene and absolute ethyl alcohol in the mixed solution containing water, xylene and absolute ethyl alcohol is 1:2: 7; the Al (NO)3The volume ratio of the mass of the mixed solution to the mixed solution containing water, xylene and absolute ethyl alcohol is 0.01-0.03g/m L, and the mass of the polyethylene glycol is Al (NO)33-8% of the mass.
According to a preferred embodiment of the present invention, in step (3), the c-BN and Al (NO)3The mass ratio of (A) to (B) is 1:1.1-1: 1.5.
Preferably, in step (3), the concentration of the ammonia water is 0.2-0.4 mol/L.
According to the invention, the mass ratio of the alumina-coated cubic boron nitride composite powder to the polyethylene glycol in the step (4) is preferably 15:1-20:1, and the mass concentration of the alumina-coated cubic boron nitride composite powder in the mixed solution is preferably 0.05-0.20g/m L.
According to the invention, in the step (4), the ball milling is performed by using hard alloy ball milling balls, and the mass ratio of the ball milling balls to the materials is 10-20: 1.
According to the invention, in the step (4), the sieving screen is 200-300 meshes.
According to the invention, in the step (4), the drying is preferably carried out for 24-36 h under the condition of 100-110 ℃ in vacuum.
According to the preferable selection of the invention, in the step (5), the hot-pressing sintering conditions comprise that the sintering temperature is 1450-1550 ℃, the hot-pressing pressure is 25-35 MPa, the heat preservation time is 20-40 min, the temperature rise rate is 10-25 ℃/min, and the vacuum degree range is 5-7 × 10-2Pa。
The invention has the technical characteristics and beneficial effects that:
1. the invention provides a novel (Ti, W) C-based metal ceramic cutting tool material with a multilayer core-shell microstructure and excellent mechanical properties. The cutting tool material of the invention forms Al with c-BN as a core2O3The multilayer core-shell microstructure with the intermediate layer and the metal binder phase as the shell improves the compactness of the cutter material. Residual compressive stress is formed inside the c-BN particles by utilizing the characteristics of low thermal expansion coefficient and high elastic modulus of the c-BN core, so that stress concentration at an interface is relieved; by using Al2O3The intermediate layer coats the c-BN particles, so that the phase change effect of the c-BN to the h-BN at a higher temperature can be inhibited, and the high mechanical property of the cubic boron nitride is ensured; may also be assisted by Al2O3The excellent sintering property improves the sintering property of c-BN. The shell metal phase can be used as the bonding phase of the cutter and can inhibit the nano Al through the heterogeneous cladding effect2O3Abnormal growth of ceramic particles; under the action of high-temperature liquid phase diffusion, a shell with a multilayer core-shell microstructure is formed, the combination and growth of crystal grains are prevented, and the problem of abnormal growth of metal ceramic crystal grains is solved. In addition, Al2O3The intermediate layer and the metal bonding phase are taken as the shell, and simultaneously the problems of thermal expansion mismatch and tool internal interface stress concentration caused by directly adding cubic boron nitride are alleviated, so that the mechanical property is improved.
2. The cutter material obtained by the invention has excellent mechanical properties, the hardness can reach 21.68GPa, and the fracture toughness can reach 13.25 MPa.m1/2The bending strength can reach 1021 MPa; phase (C)The mixture is not coated (namely, c-BN and Al are directly added)2O3And metal binder phase), the mechanical properties of the obtained cutter material are improved, and particularly, the bending strength and the fracture toughness are greatly improved by about 41 percent and 81 percent respectively. The cutter material is used for cutting, has good cutter service life, and has low surface roughness of a processed workpiece.
Drawings
FIG. 1 is a scanning electron micrograph of an alumina-coated cubic boron nitride composite powder prepared in example 1;
FIG. 2 is a photograph showing the spectral analysis of the alumina-coated cubic boron nitride composite powder prepared in example 1;
FIG. 3 is a scanning electron micrograph of fractures of the (Ti, W) C-based cermet cutting tool material prepared in example 1.
Detailed Description
The present invention will be further described with reference to specific examples, but the present invention is not limited to the following examples.
The method is a conventional method unless otherwise specified, and the reagent is commercially available without further specified.
Example 1
A (Ti, W) C-based metal ceramic cutting tool material added with alumina coated cubic boron nitride composite powder is prepared by hot-pressing and sintering the following main raw materials in percentage by mass:
10% of cubic boron nitride composite powder coated by alumina, 3.5% of nickel, 6.5% of molybdenum, 5% of cobalt and the balance of (Ti, W) C; the sum of the mass percentages of the components is 100 percent;
the preparation steps are as follows:
(1) dispersing 0.4g of polyethylene glycol (with the weight-average molecular weight of 4000) in 200m L absolute ethyl alcohol, mechanically stirring and ultrasonically dispersing for 30min to prepare 2 g/L polyethylene glycol-absolute ethyl alcohol dispersion liquid, then weighing tungsten carbide titanium, nickel, molybdenum and cobalt in sequence according to the proportion, adding the tungsten carbide titanium, nickel, molybdenum and cobalt into the polyethylene glycol-absolute ethyl alcohol dispersion liquid, mechanically stirring and ultrasonically dispersing for 30min, then ball-milling for 60h at room temperature under the protection of nitrogen (the ball-milling adopts ball-milling balls made of hard alloy materials, the mass ratio of the ball-milling balls to the materials is 15:1) to prepare composite powder dispersion liquid, wherein the mass content of (Ti, W) C in the composite powder dispersion liquid is 0.3g/m L, and storing the composite powder dispersion liquid in a ball-milling tank for later use.
(2) Under the conditions of mechanical stirring and ultrasonic dispersion, 4g of cubic boron nitride c-BN (with the average particle size of 0.2 mu m) is weighed and dispersed in 500m L absolute ethyl alcohol solution to obtain mixed solution 1, sodium dodecyl sulfate and polyethylene glycol (with the weight-average molecular weight of 4000) are sequentially dispersed in 200m L absolute ethyl alcohol according to the mass ratio of 3:1.5:1 of the c-BN, the sodium dodecyl sulfate and the polyethylene glycol to obtain mixed solution 2, the mixed solution 1 and the mixed solution 2 are fully mixed, the reaction is carried out for 60min at 75 ℃, and modified c-BN powder is obtained through cooling, centrifugal separation, washing and drying;
(3) under the conditions of mechanical stirring and ultrasonic dispersion, 4g of modified c-BN powder is dispersed in 200m L of absolute ethyl alcohol to obtain c-BN dispersion liquid according to the formula of c-BN and Al (NO)3)3Weighing Al (NO) at a mass ratio of 1:1.53)3And dispersing the Al and polyethylene glycol in 300m L mixed solution containing water, xylene and absolute ethyl alcohol (the volume ratio of the water to the xylene to the absolute ethyl alcohol is 1:2:7) to obtain Al (NO)3)3Solution of polyethylene glycol having a weight average molecular weight of 4000 and a mass of Al (NO)3)35% of the mass; and adding Al (NO)3)3Slowly adding the solution into the c-BN dispersion liquid, uniformly mixing, dropwise adding ammonia water with the mass concentration of 0.3 mol/L to adjust the pH value to 7, reacting for 30min at 75 ℃, and obtaining c-BN @ Al (OH) through centrifugal separation, washing and drying3(ii) a Calcining the mixture for 2 hours at 1100 ℃ under the protection of nitrogen to obtain alumina coated cubic boron nitride composite powder;
(4) weighing and dispersing the alumina-coated cubic boron nitride composite powder in 100m L polyethylene glycol (weight average molecular weight is 4000) -absolute ethyl alcohol according to a ratio to obtain a mixed solution, wherein the mass ratio of the alumina-coated cubic boron nitride composite powder to the polyethylene glycol is 15:1, and the mass concentration of the alumina-coated cubic boron nitride composite powder in the mixed solution is 0.08g/m L;
(5) carrying out hot-pressing sintering on the obtained mixed powder in a graphite mold to obtain the (Ti, W) C-based metal ceramic cutter material, wherein the hot-pressing sintering conditions are that the sintering temperature is 1500 ℃, the hot-pressing pressure is 30MPa, the heat preservation time is 30min, the heating rate is 20 ℃/min, and the vacuum degree is 6 × 10-2Pa。
The (Ti, W) C-based cermet cutter material green body obtained in the example was subjected to cutting, rough grinding, finish grinding, grinding and polishing to prepare a ceramic sample strip of 3mm × 4mm × 30mm, and mechanical properties of the ceramic sample strip were measured to be 21.68GPa in hardness and 13.25 MPa.m.in fracture toughness1/2And bending strength 1021 MPa.
The scanning electron micrograph of the alumina-coated cubic boron nitride composite powder prepared in this example is shown in fig. 1, and it can be seen from the micrograph that a uniform nanoparticle coating layer is formed on the surface of the cubic boron nitride powder;
the energy spectrum analysis photograph of the alumina-coated cubic boron nitride composite powder prepared in the embodiment is shown in fig. 2, and it can be known from the drawing that the composite powder only contains elements of alumina and cubic boron nitride, and no other impurity elements are introduced;
the scanning electron micrograph of the fracture of the (Ti, W) -based cermet cutting tool material prepared in this example is shown in fig. 3, which shows that the alumina-coated cubic boron nitride composite powder with the core-shell structure still has the core-shell structure after sintering, and the cubic boron nitride is located inside the alumina crystal grains.
Example 2
A (Ti, W) C-based metal ceramic cutting tool material added with alumina coated cubic boron nitride composite powder is prepared by hot-pressing and sintering the following main raw materials in percentage by mass:
5% of alumina-coated cubic boron nitride composite powder, 4% of nickel, 6% of molybdenum, 5% of cobalt and the balance of (Ti, W) C; the sum of the mass percentages of the components is 100 percent;
the preparation steps are as follows:
(1) dispersing 0.4g of polyethylene glycol (with the weight-average molecular weight of 4000) in 200m L absolute ethyl alcohol, mechanically stirring and ultrasonically dispersing for 30min to prepare 2 g/L polyethylene glycol-absolute ethyl alcohol dispersion liquid, then weighing tungsten carbide titanium, nickel, molybdenum and cobalt in sequence according to the proportion, adding the tungsten carbide titanium, nickel, molybdenum and cobalt into the polyethylene glycol-absolute ethyl alcohol dispersion liquid, mechanically stirring and ultrasonically dispersing for 40min, then ball-milling for 50h at room temperature under the protection of nitrogen (the ball-milling adopts ball-milling balls made of hard alloy materials, the mass ratio of the ball-milling balls to the materials is 15:1) to prepare composite powder dispersion liquid, wherein the mass content of (Ti, W) C in the composite powder dispersion liquid is 0.48g/m L, and storing the composite powder dispersion liquid in a ball-milling tank for later use.
(2) Under the conditions of mechanical stirring and ultrasonic dispersion, 3g of cubic boron nitride c-BN (the average particle size is 0.2 mu m) is weighed and dispersed in 500m L absolute ethyl alcohol solution to obtain mixed solution 1, sodium dodecyl sulfate and polyethylene glycol are sequentially dispersed in 200m L absolute ethyl alcohol according to the mass ratio of 3:2:1 of the c-BN, the sodium dodecyl sulfate and the polyethylene glycol (the weight average molecular weight is 4000) to obtain mixed solution 2, the mixed solution 1 and the mixed solution 2 are fully mixed, the reaction is carried out for 50min at the temperature of 80 ℃, and modified c-BN powder is obtained through cooling, centrifugal separation, washing and drying;
(3) under the conditions of mechanical stirring and ultrasonic dispersion, 3g of modified c-BN powder is dispersed in 200m L of absolute ethyl alcohol to obtain c-BN dispersion liquid according to the formula of c-BN and Al (NO)3)3Weighing Al (NO) according to the mass ratio of 1:1.23)3And dispersing the Al and polyethylene glycol in 300m L mixed solution containing water, xylene and absolute ethyl alcohol (the volume ratio of the water to the xylene to the absolute ethyl alcohol is 1:2:7) to obtain Al (NO)3)3Solution of polyethylene glycol having a weight average molecular weight of 4000 and a mass of Al (NO)3)36% of the mass; and adding Al (NO)3)3Slowly adding the solution into the c-BN dispersion liquid, uniformly mixing, dropwise adding ammonia water with the mass concentration of 0.3 mol/L to adjust the pH value to 7, reacting for 20min at the temperature of 80 ℃, and obtaining c-BN @ Al (OH) through centrifugal separation, washing and drying3(ii) a Calcining the mixture for 2 hours at 1100 ℃ under the protection of nitrogen to obtain alumina coated cubic boron nitride composite powder;
(4) weighing and dispersing the alumina-coated cubic boron nitride composite powder in 100m L polyethylene glycol (weight average molecular weight is 4000) -absolute ethyl alcohol according to a ratio to obtain a mixed solution, wherein the mass ratio of the alumina-coated cubic boron nitride composite powder to the polyethylene glycol is 15:1, and the mass concentration of the alumina-coated cubic boron nitride composite powder in the mixed solution is 0.08g/m L;
(5) carrying out hot-pressing sintering on the obtained mixed powder in a graphite mold to obtain the (Ti, W) C-based metal ceramic cutter material, wherein the hot-pressing sintering conditions are that the sintering temperature is 1450 ℃, the hot-pressing pressure is 35MPa, the heat preservation time is 30min, the heating rate is 15 ℃/min, and the vacuum degree is 6 × 10-2Pa。
The (Ti, W) C-based cermet cutting tool material green body obtained in this example was subjected to cutting, rough grinding, finish grinding, grinding and polishing to prepare a ceramic sample bar of 3mm × 4mm × 30mm, and mechanical properties of the ceramic sample bar were measured as hardness 20.31GPa and fracture toughness 12.46 MPa.m1/2And bending strength 977 MPa.
Example 3
A (Ti, W) C-based metal ceramic cutting tool material added with alumina coated cubic boron nitride composite powder is prepared by hot-pressing and sintering the following main raw materials in percentage by mass:
15% of alumina-coated cubic boron nitride composite powder, 3% of nickel, 6% of molybdenum, 6% of cobalt and the balance of (Ti, W) C; the sum of the mass percentages of the components is 100 percent;
the preparation steps are as follows:
(1) dispersing 0.8g of polyethylene glycol (with the weight-average molecular weight of 4000) in 200m L absolute ethyl alcohol, mechanically stirring and ultrasonically dispersing for 30min to prepare 2 g/L polyethylene glycol-absolute ethyl alcohol dispersion liquid, then weighing tungsten carbide titanium, nickel, molybdenum and cobalt in sequence according to the proportion, adding the tungsten carbide titanium, nickel, molybdenum and cobalt into the polyethylene glycol-absolute ethyl alcohol dispersion liquid, mechanically stirring and ultrasonically dispersing for 30min, then ball-milling for 70h at room temperature under the protection of nitrogen (the ball-milling adopts ball-milling balls made of hard alloy materials, and the mass ratio of the ball-milling balls to the materials is 15:1) to prepare composite powder dispersion liquid, wherein the mass content of (Ti, W) C in the composite powder dispersion liquid is 0.35g/m L, and storing the composite powder dispersion liquid in a ball-milling tank for later use.
(2) Under the conditions of mechanical stirring and ultrasonic dispersion, 4.5g of cubic boron nitride c-BN (with the average particle size of 0.2 mu m) is weighed and dispersed in 500m L anhydrous ethanol solution to obtain mixed solution 1, sodium dodecyl sulfate and polyethylene glycol are sequentially dispersed in 200m L anhydrous ethanol according to the mass ratio of 2.5:1.5:1 of the c-BN, the sodium dodecyl sulfate and the polyethylene glycol (with the weight average molecular weight of 4000) to obtain mixed solution 2, the mixed solution 1 and the mixed solution 2 are fully and uniformly mixed, react for 60min at 70 ℃, and modified c-BN powder is obtained through cooling, centrifugal separation, washing and drying;
(3) under the conditions of mechanical stirring and ultrasonic dispersion, 4.5g of modified c-BN powder is dispersed in 200m L of absolute ethyl alcohol to obtain c-BN dispersion liquid according to the ratio of c-BN to Al (NO)3)3Weighing Al (NO) according to the mass ratio of 1:1.13)3And dispersing the Al and polyethylene glycol in 250m L mixed solution containing water, xylene and absolute ethyl alcohol (the volume ratio of the water to the xylene to the absolute ethyl alcohol is 1:2:7) to obtain Al (NO)3)3Solution of polyethylene glycol having a weight average molecular weight of 4000 and a mass of Al (NO)3)35% of the mass; and mixing Al (NO)3Slowly adding the solution into the c-BN dispersion liquid, uniformly mixing, dropwise adding ammonia water with the mass concentration of 0.3 mol/L to adjust the pH value to 7, reacting for 30min at 70 ℃, and obtaining c-BN @ Al (OH) through centrifugal separation, washing and drying3(ii) a Calcining the mixture for 2 hours at 1100 ℃ under the protection of nitrogen to obtain alumina coated cubic boron nitride composite powder;
(4) weighing and dispersing the alumina-coated cubic boron nitride composite powder in 100m L polyethylene glycol (weight average molecular weight is 4000) -absolute ethyl alcohol according to a ratio to obtain a mixed solution, wherein the mass ratio of the alumina-coated cubic boron nitride composite powder to the polyethylene glycol is 15:1, and the mass concentration of the alumina-coated cubic boron nitride composite powder in the mixed solution is 0.15g/m L;
(5) carrying out hot-pressing sintering on the obtained mixed powder in a graphite mold to obtain the (Ti, W) C-based metal ceramic cutter material, wherein the hot-pressing sintering conditions comprise the sintering temperature of 1500 ℃, the hot-pressing pressure of 35MPa, the heat preservation time of 25min, the heating rate of 20 ℃/min and the vacuum degree of 6 × 10-2Pa。
The (Ti, W) C-based cermet cutting tool material green body obtained in the example was subjected to cutting, rough grinding, finish grinding, grinding and polishing to prepare a ceramic sample strip of 3mm × 4mm × 30mm, and mechanical properties of the ceramic sample strip were measured to be 20.93GPa in hardness and 11.72 MPa.m.in fracture toughness1/2And a bending strength of 993 MPa.
Comparative example 1
A (Ti, W) C-based metal ceramic cutter material is prepared by hot-pressing and sintering the following main raw materials in percentage by mass:
10% of cubic boron nitride, 3.5% of nickel, 6.5% of molybdenum, 5% of cobalt and the balance of (Ti, W) C; the sum of the mass percentages of the components is 100 percent;
the preparation steps are as follows:
(1) dispersing 0.6g of polyethylene glycol (with the weight-average molecular weight of 4000) in 300m L absolute ethyl alcohol, mechanically stirring and ultrasonically dispersing for 30min to prepare a polyethylene glycol-absolute ethyl alcohol dispersion liquid with the concentration of 2 g/L, then weighing tungsten carbide titanium, nickel, molybdenum, cobalt and cubic boron nitride in sequence according to the proportion, adding the tungsten carbide titanium, the nickel, the molybdenum, the cobalt and the cubic boron nitride into the polyethylene glycol-absolute ethyl alcohol dispersion liquid, mechanically stirring and ultrasonically dispersing for 30min, then ball-milling for 60h at room temperature under the protection of nitrogen (the ball-milling adopts ball-milling balls made of hard alloy, the mass ratio of the ball-milling balls to materials is 15:1), and finally carrying out vacuum drying for 24h under the condition of 110 ℃ and sieving by a 200-mesh sieve;
(2) carrying out hot-pressing sintering on the obtained mixed powder in a graphite mold to obtain the (Ti, W) C-based metal ceramic cutter material, wherein the hot-pressing sintering conditions are that the sintering temperature is 1500 ℃, the hot-pressing pressure is 30MPa, the heat preservation time is 30min, the heating rate is 20 ℃/min, and the vacuum degree is 6 × 10-2Pa。
The (Ti, W) C-based cermet cutting tool material green body obtained in this comparative example was subjected to cutting-rough grinding-finish grinding-polishing steps to prepare a ceramic sample bar of 3mm × 4mm × 30mm, and measuredThe mechanical properties are as follows: 19.14GPa and fracture toughness of 8.83 MPa.m1/2And bending strength 874 MPa. From the above, the alumina-coated cubic boron nitride composite powder of the present invention has an important influence on the mechanical properties of the cutting tool material.
Comparative example 2
A (Ti, W) C-based metal ceramic cutter material is prepared by hot-pressing and sintering the following main raw materials in percentage by mass:
5% of cubic boron nitride, 5% of nano-alumina (the particle size is 20nm), 3.5% of nickel, 6.5% of molybdenum, 5% of cobalt and the balance of (Ti, W) C; the sum of the mass percentages of the components is 100 percent;
the preparation steps are as follows:
(1) dispersing 0.6g of polyethylene glycol (with the weight-average molecular weight of 4000) in 300m L absolute ethyl alcohol, mechanically stirring and ultrasonically dispersing for 30min to prepare a polyethylene glycol-absolute ethyl alcohol dispersion liquid with the concentration of 2 g/L, then weighing aluminum oxide, tungsten titanium carbide, nickel, molybdenum, cobalt and cubic boron nitride in sequence according to the proportion, adding the weighed aluminum oxide, tungsten titanium carbide, nickel, molybdenum, cobalt and cubic boron nitride into the polyethylene glycol-absolute ethyl alcohol dispersion liquid, mechanically stirring and ultrasonically dispersing for 30min, then ball-milling for 60h at room temperature under the protection of nitrogen (the ball-milling adopts ball-milling balls made of hard alloy, the mass ratio of the ball-milling balls to materials is 15:1), and finally carrying out vacuum drying for 24h at the temperature of 110 ℃ and sieving by a 200-mesh sieve;
(2) carrying out hot-pressing sintering on the obtained mixed powder in a graphite mold to obtain the (Ti, W) C-based metal ceramic cutter material, wherein the hot-pressing sintering conditions are that the sintering temperature is 1500 ℃, the hot-pressing pressure is 30MPa, the heat preservation time is 30min, the heating rate is 20 ℃/min, and the vacuum degree is 6 × 10-2Pa。
The (Ti, W) C-based cermet cutter material blank obtained in the comparative example is subjected to cutting, rough grinding, fine grinding, grinding and polishing to prepare a ceramic sample strip of 3mm × 4mm × 30mm, and the mechanical properties of the ceramic sample strip are measured to be 18.55GPa and the fracture toughness to be 7.32 MPa.m.1/2And a bending strength of 722 MPa. From the above, the alumina-coated cubic boron nitride composite powder of the present invention has an important influence on the mechanical properties of the cutting tool material.
Comparative example 3
A preparation method of a (Ti, W) C-based metal ceramic cutter material is formed by hot-pressing and sintering the following main raw materials in percentage by mass:
2.5 percent of cubic boron nitride, 2.5 percent of nano-alumina (the grain diameter is 20nm), 3.5 percent of nickel, 6.5 percent of molybdenum, 5 percent of cobalt and the balance of (Ti, W) C; the sum of the mass percentages of the components is 100 percent;
the preparation steps are as follows:
(1) dispersing 0.6g of polyethylene glycol (with the weight-average molecular weight of 4000) in 300m L absolute ethyl alcohol, mechanically stirring and ultrasonically dispersing for 30min to prepare a polyethylene glycol-absolute ethyl alcohol dispersion liquid with the concentration of 2 g/L, then weighing nano aluminum oxide and cubic boron nitride according to the proportion, adding the nano aluminum oxide and the cubic boron nitride into the polyethylene glycol-absolute ethyl alcohol dispersion liquid, mechanically stirring and ultrasonically dispersing for 30min, then sequentially weighing tungsten titanium carbide, nickel, molybdenum and cobalt, adding the tungsten titanium carbide, the nickel, the molybdenum and the cobalt into the dispersion liquid, mechanically stirring and ultrasonically dispersing for 30min, then ball-milling for 60h at room temperature under the protection of nitrogen (the ball-milling adopts ball-milling balls made of hard alloy materials, the mass ratio of the ball-milling balls to materials is 10:1), and finally, carrying out vacuum drying for 24h under the condition of 110 ℃, and sieving;
(2) carrying out hot-pressing sintering on the obtained mixed powder in a graphite mold to obtain the (Ti, W) C-based metal ceramic cutter material, wherein the hot-pressing sintering conditions are that the sintering temperature is 1500 ℃, the hot-pressing pressure is 30MPa, the heat preservation time is 30min, the heating rate is 20 ℃/min, and the vacuum degree is 6 × 10-2Pa。
The (Ti, W) C-based cermet cutter material blank obtained in the comparative example is subjected to cutting, rough grinding, fine grinding, grinding and polishing to prepare a ceramic sample strip of 3mm × 4mm × 30mm, and the mechanical properties of the ceramic sample strip are measured to be 19.06GPa and the fracture toughness to be 9.86 MPa.m1/2And a bending strength of 738 MPa. From the above, the alumina-coated cubic boron nitride composite powder of the present invention has an important influence on the mechanical properties of the cutting tool material.
Claims (10)
1. A (Ti, W) C-based metal ceramic cutting tool material added with alumina coated cubic boron nitride composite powder is characterized by being prepared by hot-pressing and sintering the following main raw materials in percentage by mass:
2-8% of cobalt, 1-5% of nickel, 5-10% of molybdenum, 1-20% of alumina-coated cubic boron nitride composite powder and the balance of (Ti, W) C; the sum of the mass percentages of the components is 100 percent;
the alumina-coated cubic boron nitride composite powder is prepared by the following method:
dispersing the c-BN in an absolute ethyl alcohol solution to obtain a mixed solution 1; dispersing sodium dodecyl sulfate and polyethylene glycol in absolute ethyl alcohol to obtain a mixed solution 2; fully and uniformly mixing the mixed solution 1 and the mixed solution 2, reacting for 50-60 min at 70-80 ℃, and cooling, centrifugally separating, washing and drying to obtain modified c-BN powder;
dispersing the modified c-BN powder in absolute ethyl alcohol to obtain c-BN dispersion liquid; mixing Al (NO)3)3And polyethylene glycol dispersed in a mixed solution containing water, xylene and anhydrous ethanol to obtain Al (NO)3)3A solution; mixing Al (NO)3)3Adding the solution into the c-BN dispersion liquid, uniformly mixing, dropwise adding ammonia water to adjust the pH value to 7, reacting for 20-40 min at 70-80 ℃, and obtaining c-BN @ Al (OH) through centrifugal separation, washing and drying3(ii) a Then calcining at the temperature of 900-1200 ℃ under the protection of inert gas to obtain the alumina-coated cubic boron nitride composite powder.
2. The (Ti, W) -based cermet cutting tool material with an added alumina-coated cubic boron nitride composite powder of claim 1, wherein the (Ti, W) -based cermet cutting tool material is prepared by hot-pressing and sintering the following main raw materials in percentage by weight: 3-6% of cobalt, 2-4% of nickel, 5-8% of molybdenum, 5-15% of alumina-coated cubic boron nitride composite powder and the balance of (Ti, W) C; the sum of the weight percentages of the components is 100 percent.
3. The (Ti, W) -based cermet cutting tool material with the addition of the alumina-coated cubic boron nitride composite powder according to claim 1, wherein the average particle size of the alumina-coated cubic boron nitride composite powder is 0.3 to 1.5 μm, the average particle size of (Ti, W) C is 2 to 5 μm, and the average particle sizes of mo, co and ni are all 1 to 3 μm.
4. The method for producing a (Ti, W) -based cermet cutting tool material with addition of alumina-coated cubic boron nitride composite powder as set forth in any one of claims 1 to 3, comprising the steps of:
(1) dispersing polyethylene glycol in absolute ethyl alcohol to form polyethylene glycol-absolute ethyl alcohol dispersion liquid; sequentially dispersing (Ti, W) C, molybdenum, cobalt and nickel in polyethylene glycol-absolute ethyl alcohol dispersion liquid, and then carrying out ball milling for 40-80h under the protection of inert gas to prepare composite powder dispersion liquid;
(2) dispersing the c-BN in an absolute ethyl alcohol solution to obtain a mixed solution 1; dispersing sodium dodecyl sulfate and polyethylene glycol in absolute ethyl alcohol to obtain a mixed solution 2; fully and uniformly mixing the mixed solution 1 and the mixed solution 2, reacting for 50-60 min at 70-80 ℃, and cooling, centrifugally separating, washing and drying to obtain modified c-BN powder;
(3) dispersing the modified c-BN powder in absolute ethyl alcohol to obtain c-BN dispersion liquid; mixing Al (NO)3)3And polyethylene glycol dispersed in a mixed solution containing water, xylene and anhydrous ethanol to obtain Al (NO)3)3A solution; mixing Al (NO)3)3Adding the solution into the c-BN dispersion liquid, uniformly mixing, dropwise adding ammonia water to adjust the pH value to 7, reacting for 20-40 min at 70-80 ℃, and obtaining c-BN @ Al (OH) through centrifugal separation, washing and drying3(ii) a Then calcining for 1-3h at the temperature of 900-;
(4) dispersing the alumina coated cubic boron nitride composite powder in a polyethylene glycol-absolute ethyl alcohol solution to obtain a mixed solution; adding the mixed solution into the composite powder dispersion liquid obtained in the step (1), and continuing ball milling for 1-3 hours under the protection of inert gas; drying and sieving to obtain mixed powder;
(5) and carrying out hot-pressing sintering on the obtained mixed powder in a graphite mold to obtain the (Ti, W) C-based metal ceramic cutter material.
5. The method for preparing a (Ti, W) C-based cermet cutting tool material with alumina-coated cubic boron nitride composite powder added as recited in claim 4 wherein in steps (1) - (4), the weight average molecular weight of the polyethylene glycol is all 2000-8000; preferably, the weight average molecular weight of the polyethylene glycol is 4000-6000.
6. The method for preparing the (Ti, W) C-based cermet cutting tool material with the addition of the alumina-coated cubic boron nitride composite powder according to claim 4, wherein the step (1) comprises one or more of the following conditions:
a. in the polyethylene glycol-absolute ethyl alcohol dispersion liquid, the concentration of polyethylene glycol is 1-5 g/L, preferably 2-4 g/L;
b. the mass content of (Ti, W) C in the composite powder dispersion liquid is 0.2-1g/m L;
c. the ball milling time is 48-60h, the ball milling is performed by adopting hard alloy ball milling balls, and the mass ratio of the ball milling balls to the materials is 5-15: 1.
7. The method for preparing the (Ti, W) C-based cermet cutting tool material with the addition of the alumina-coated cubic boron nitride composite powder according to claim 4, wherein the step (2) comprises one or more of the following conditions:
a. in the mixed solution 1, the mass concentration of c-BN is 0.006-0.009g/m L, the mass ratio of c-BN, sodium dodecyl sulfate and polyethylene glycol is 2-4:1-2:1, and in the mixed solution 2, the mass concentration of polyethylene glycol is 0.006-0.008 g/ml;
b. the c-BN average particle size is 0.1 to 0.3 mu m.
8. The method for preparing a (Ti, W) C-based cermet cutting tool material with the addition of alumina-coated cubic boron nitride composite powder according to claim 4, wherein the step (3) comprises one or more of the following conditions:
a. in the c-BN dispersion liquid, the mass concentration of the modified c-BN powder is 0.01-0.04g/m L;
b. the volume ratio of water, xylene and absolute ethyl alcohol in the mixed solution containing water, xylene and absolute ethyl alcohol is 1:2: 7; the Al (NO)3The volume ratio of the mass of the mixed solution to the mixed solution containing water, xylene and absolute ethyl alcohol is 0.01-0.03g/m L, and the mass of polyethylene glycolIn an amount of Al (NO)33-8% of the mass;
c. the c-BN and Al (NO)3The mass ratio of (1: 1.1) - (1: 1.5);
d. the concentration of the ammonia water is 0.2-0.4 mol/L.
9. The method for preparing the (Ti, W) C-based cermet cutting tool material with the addition of the alumina-coated cubic boron nitride composite powder according to claim 4, wherein the step (4) comprises one or more of the following conditions:
a. the mass ratio of the alumina-coated cubic boron nitride composite powder to the polyethylene glycol is 15:1-20:1, and the mass concentration of the alumina-coated cubic boron nitride composite powder in the mixed solution is 0.05-0.20g/m L;
b. the ball milling is performed by using ball milling balls made of hard alloy materials, and the mass ratio of the ball milling balls to the materials is 10-20: 1;
c. the sieving screen is 200-300 meshes.
10. The method for preparing a (Ti, W) C-based cermet cutting tool material with an alumina-coated cubic boron nitride composite powder added according to claim 4, wherein in the step (5), the hot-pressing sintering conditions include a sintering temperature of 1450-1550 ℃, a hot-pressing pressure of 25-35 MPa, a heat preservation time of 20-40 min, a temperature rise rate of 10-25 ℃/min, and a vacuum degree range of 5-7 × 10-2Pa。
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