CN112795861A - A kind of tungsten carbide-chromium carbide-nickel composite powder and preparation method thereof and cermet coating and preparation method thereof - Google Patents
A kind of tungsten carbide-chromium carbide-nickel composite powder and preparation method thereof and cermet coating and preparation method thereof Download PDFInfo
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- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 title claims abstract description 182
- 239000000843 powder Substances 0.000 title claims abstract description 136
- 239000011651 chromium Substances 0.000 title claims abstract description 110
- 239000002131 composite material Substances 0.000 title claims abstract description 95
- 229910052759 nickel Inorganic materials 0.000 title claims abstract description 87
- 238000000576 coating method Methods 0.000 title claims abstract description 64
- 239000011248 coating agent Substances 0.000 title claims abstract description 63
- 229910052804 chromium Inorganic materials 0.000 title claims abstract description 55
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 title claims abstract description 55
- 239000010937 tungsten Substances 0.000 title claims abstract description 55
- 229910052721 tungsten Inorganic materials 0.000 title claims abstract description 55
- 238000002360 preparation method Methods 0.000 title claims abstract description 30
- 239000011195 cermet Substances 0.000 title claims abstract description 28
- 239000002245 particle Substances 0.000 claims abstract description 124
- 229910003470 tongbaite Inorganic materials 0.000 claims abstract description 57
- 238000010285 flame spraying Methods 0.000 claims abstract description 41
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 claims abstract description 28
- UFGZSIPAQKLCGR-UHFFFAOYSA-N chromium carbide Chemical compound [Cr]#C[Cr]C#[Cr] UFGZSIPAQKLCGR-UHFFFAOYSA-N 0.000 claims abstract description 27
- 239000011812 mixed powder Substances 0.000 claims abstract description 21
- 238000009826 distribution Methods 0.000 claims abstract description 13
- 238000005245 sintering Methods 0.000 claims description 25
- ATUOYWHBWRKTHZ-UHFFFAOYSA-N Propane Chemical compound CCC ATUOYWHBWRKTHZ-UHFFFAOYSA-N 0.000 claims description 24
- 239000000203 mixture Substances 0.000 claims description 23
- 239000007921 spray Substances 0.000 claims description 21
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 18
- 238000002156 mixing Methods 0.000 claims description 17
- 238000005469 granulation Methods 0.000 claims description 15
- 238000000034 method Methods 0.000 claims description 15
- 230000003179 granulation Effects 0.000 claims description 12
- 239000001294 propane Substances 0.000 claims description 12
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 11
- 239000001301 oxygen Substances 0.000 claims description 11
- 229910052760 oxygen Inorganic materials 0.000 claims description 11
- 238000005507 spraying Methods 0.000 claims description 11
- 238000000498 ball milling Methods 0.000 claims description 8
- 229910052757 nitrogen Inorganic materials 0.000 claims description 8
- 239000000463 material Substances 0.000 claims description 7
- 238000001035 drying Methods 0.000 claims description 6
- 239000002002 slurry Substances 0.000 claims description 6
- QGZKDVFQNNGYKY-UHFFFAOYSA-O Ammonium Chemical compound [NH4+] QGZKDVFQNNGYKY-UHFFFAOYSA-O 0.000 claims description 4
- 229920002538 Polyethylene Glycol 20000 Polymers 0.000 claims description 4
- 239000008367 deionised water Substances 0.000 claims description 4
- 229910021641 deionized water Inorganic materials 0.000 claims description 4
- 229920000058 polyacrylate Polymers 0.000 claims description 4
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Chemical compound O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 4
- 239000008187 granular material Substances 0.000 claims description 2
- 238000004519 manufacturing process Methods 0.000 claims 1
- 229910052751 metal Inorganic materials 0.000 description 43
- 239000002184 metal Substances 0.000 description 43
- 238000005524 ceramic coating Methods 0.000 description 40
- 239000012071 phase Substances 0.000 description 32
- 230000000052 comparative effect Effects 0.000 description 16
- 238000001878 scanning electron micrograph Methods 0.000 description 16
- 238000005979 thermal decomposition reaction Methods 0.000 description 15
- 239000002994 raw material Substances 0.000 description 12
- 238000002441 X-ray diffraction Methods 0.000 description 11
- 238000002844 melting Methods 0.000 description 10
- 230000008018 melting Effects 0.000 description 10
- 230000003647 oxidation Effects 0.000 description 9
- 238000007254 oxidation reaction Methods 0.000 description 9
- 238000005516 engineering process Methods 0.000 description 7
- 239000000758 substrate Substances 0.000 description 7
- 238000012360 testing method Methods 0.000 description 7
- 239000000243 solution Substances 0.000 description 6
- 238000001228 spectrum Methods 0.000 description 6
- 238000007751 thermal spraying Methods 0.000 description 6
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 5
- 239000011159 matrix material Substances 0.000 description 5
- 238000012512 characterization method Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 238000012216 screening Methods 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- 239000011230 binding agent Substances 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 230000001788 irregular Effects 0.000 description 3
- 239000007791 liquid phase Substances 0.000 description 3
- 239000000919 ceramic Substances 0.000 description 2
- QDOXWKRWXJOMAK-UHFFFAOYSA-N chromium(III) oxide Inorganic materials O=[Cr]O[Cr]=O QDOXWKRWXJOMAK-UHFFFAOYSA-N 0.000 description 2
- 239000011247 coating layer Substances 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 238000005034 decoration Methods 0.000 description 2
- 230000008021 deposition Effects 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 229910001873 dinitrogen Inorganic materials 0.000 description 2
- 230000002349 favourable effect Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 239000012798 spherical particle Substances 0.000 description 2
- 229910000599 Cr alloy Inorganic materials 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 238000009825 accumulation Methods 0.000 description 1
- 239000003570 air Substances 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- QNHZQZQTTIYAQM-UHFFFAOYSA-N chromium tungsten Chemical compound [Cr][W] QNHZQZQTTIYAQM-UHFFFAOYSA-N 0.000 description 1
- 239000003086 colorant Substances 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 230000001627 detrimental effect Effects 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 239000003350 kerosene Substances 0.000 description 1
- 239000010410 layer Substances 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 238000007873 sieving Methods 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
- C23C4/12—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the method of spraying
- C23C4/129—Flame spraying
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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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
- C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
- C22C29/067—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds comprising a particular metallic binder
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
- C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
- C22C29/08—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds based on tungsten carbide
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
- C23C4/04—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the coating material
- C23C4/06—Metallic material
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- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Plasma & Fusion (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Coating By Spraying Or Casting (AREA)
- Powder Metallurgy (AREA)
Abstract
本发明涉及复合粉末技术领域，提供了一种碳化钨‑碳化铬‑镍复合粉末的制备方法，包括以下步骤：按质量含量计，将多尺度碳化钨58～78％、多尺度碳化铬10～30％和多尺度镍6～20％进行混料，得到混合粉体；其中，多尺度碳化钨的粒径分布于0.6～6μm之间，多尺度碳化铬的粒径分布于0.5～3μm之间，多尺度镍的粒径分布于0.9～5μm之间；将所述混合粉体进行造粒，得到混合物颗粒；将所述混合物颗粒进行真空烧结，得到碳化钨‑碳化铬‑镍复合粉末。本发明制备方法得到的碳化钨‑碳化铬‑镍复合粉末在超音速火焰喷涂制备金属陶瓷涂层时，能够使得所制备的金属陶瓷涂层相结构与粉末基本一致，提高金属陶瓷涂层的力学性能。
The invention relates to the technical field of composite powders, and provides a preparation method of tungsten carbide-chromium carbide-nickel composite powder, comprising the following steps: by mass content, 58-78% of multi-scale tungsten carbide and 10-78% of multi-scale chromium carbide 30% and 6-20% of multi-scale nickel are mixed to obtain mixed powder; wherein, the particle size distribution of multi-scale tungsten carbide is between 0.6 and 6 μm, and the particle size distribution of multi-scale chromium carbide is between 0.5 and 3 μm. , the particle size distribution of multi-scale nickel is between 0.9 and 5 μm; the mixed powder is granulated to obtain mixed particles; the mixed particles are vacuum sintered to obtain tungsten carbide-chromium carbide-nickel composite powder. When the tungsten carbide-chromium carbide-nickel composite powder obtained by the preparation method of the present invention is used to prepare the cermet coating by supersonic flame spraying, the phase structure of the prepared cermet coating can be basically consistent with the powder, and the mechanical properties of the cermet coating can be improved. performance.
Description
Technical Field
The invention relates to the technical field of composite powder, in particular to tungsten carbide-chromium carbide-nickel composite powder and a preparation method thereof, and a metal ceramic coating and a preparation method thereof.
Background
The tungsten carbide-chromium carbide-nickel is prepared from Ni as binder phase, tungsten carbide (WC) and chromium carbide (Cr)3C2) Cermet of hard phase, combining WC and Cr3C2The Ni-based wear-resistant and corrosion-resistant coating has the advantages of high hardness, good wettability of Ni and carbide ceramic and high toughness, and can be widely used for wear-resistant and corrosion-resistant coatings on the surfaces of mechanical parts. The supersonic flame spraying technology is that propane or aviation kerosene is used as fuel, oxygen or air is used as combustion-supporting gas, solid powder is fed into high-speed flame, and after heating and melting, the solid powder collides with the surface of a substrate to form a coating layer by accumulation. The supersonic flame spraying technology has the characteristics of high particle speed and low temperature, becomes a common preparation technology of the metal ceramic coating, and the prepared metal ceramic coating has the advantages of compact coating structure, high bonding strength and wear resistance. However, carbide hard phases WC, Cr3C2Easily generate thermal decomposition or oxidation in the flame sprayed by the supersonic flame to form W2C、W、Cr7C3、Cr26C7Or Cr2O3An isothermal decomposition phase and an oxidation phase. These thermally decomposed or oxidized phases, while enhancing the microhardness of the coating, are detrimental to the toughness of the coating and reduce the wear and corrosion resistance of the coating.
The strategy for improving the microstructure and the performance of the supersonic flame spraying metal ceramic coating mainly comprises two aspects: the method comprises the following steps of optimizing the components, the grain sizes and the structures of the metal ceramic powder, and optimizing the technological parameters of the supersonic flame spraying thermal spraying. However, for WC and Cr3C2Co-existing cermet systems, supersonic flame spray carbonisationThe tungsten-chromium carbide-nickel cermet coating still inevitably produces WC, Cr3C2The thermal decomposition or oxidation phenomenon of the coating reduces the mechanical property of the coating.
Therefore, it is desirable to provide a tungsten carbide-chromium carbide-nickel composite powder that avoids the WC, Cr effects of supersonic flame spraying3C2The obtained coating has good mechanical property due to the thermal decomposition or oxidation phenomenon.
Disclosure of Invention
The invention aims to provide tungsten carbide-chromium carbide-nickel composite powder, a preparation method and application thereof, which realize that the phase composition of a supersonic flame sprayed tungsten carbide-chromium carbide-nickel metal ceramic coating is basically consistent with that of the original powder and has good mechanical properties.
In order to achieve the above object, the present invention provides the following technical solutions:
the invention provides a preparation method of tungsten carbide-chromium carbide-nickel composite powder, which comprises the following steps:
mixing 58-78% of multi-scale tungsten carbide, 10-30% of multi-scale chromium carbide and 6-20% of multi-scale nickel according to mass content to obtain mixed powder; the grain size of the multi-scale tungsten carbide is distributed between 0.6 and 6 mu m; the multi-scale chromium carbide is multi-scale Cr3C2Said multi-scale Cr3C2The particle size of the particles is distributed between 0.5 and 3 mu m; the grain size of the multi-scale nickel is distributed between 0.9 and 5 mu m.
Preferably, the grain size of the multi-scale tungsten carbide is distributed between 0.6 and 5 mu m; the multi-scale Cr3C2The particle size of the particles is distributed between 0.5 and 1.5 mu m; the particle size of the multi-scale nickel is distributed between 1 and 4 mu m.
Preferably, the granulation is spray granulation.
Preferably, the spray granulation comprises: and mixing the mixed powder with deionized water, ammonium polyacrylate and PEG-20000 solution to prepare slurry, then ball-milling for 8-10 h in a ball mill at a rotating speed of 50-300 r/min, setting the drying temperature to be 250-550 ℃, and drying and agglomerating the slurry to obtain mixture particles.
Preferably, the temperature of the vacuum sintering is 900-1250 ℃.
Preferably, the sintering time of the vacuum sintering is 0.5-3 h.
Preferably, the particle size of the spherical mixture particles is 5-75 μm.
The invention also provides the tungsten carbide-chromium carbide-nickel composite powder obtained by the preparation method in the technical scheme, wherein the particle size of the tungsten carbide-chromium carbide-nickel composite powder is 5-75 micrometers.
The invention also provides a preparation method of the metal ceramic coating, the tungsten carbide-chromium carbide-nickel composite powder in the technical scheme is obtained by supersonic flame spraying, and the parameters of the supersonic flame spraying comprise: the flow rate of oxygen is 241.2-804.1 slpm, the flow rate of propane is 15.9-53.3 slpm, the flow rate of nitrogen is 20.6-82.6 slpm, the distance between the outlet end of a spray gun for supersonic flame spraying and the surface of a base material is 80-250 mm, the speed of the spray gun moving parallel to the base body is 50-500 mm/s, and the powder feeding speed is 5-40 g/min.
The invention also provides the metal ceramic coating prepared by the preparation method of the technical scheme.
The invention provides a preparation method of tungsten carbide-chromium carbide-nickel composite powder, which comprises the following steps: mixing 58-78% of multi-scale tungsten carbide, 10-30% of multi-scale chromium carbide and 6-20% of multi-scale nickel to obtain mixed powder; the grain size of the multi-scale tungsten carbide is distributed between 0.6 and 6 mu m; the multi-scale chromium carbide is multi-scale Cr3C2Said multi-scale Cr3C2The particle size of the particles is distributed between 0.5 and 3 mu m; the grain size of the multi-scale nickel is distributed between 0.9 and 5 mu m. According to the invention, multi-scale tungsten carbide, chromium carbide and nickel are used as raw materials, and the particles in the obtained composite powder are multi-scale carbide particles and nickel particles through mixing, granulating and vacuum sintering. When the tungsten carbide-chromium carbide-nickel composite powder obtained by the preparation method provided by the invention is applied to the preparation of the metal ceramic coating by supersonic flame spraying, the coarse-grained carbide is not melted in the process of supersonic flame sprayingThe thermal decomposition, the melting of the fine grain carbide and the melting of the metal nickel, the melting of the fine grain carbide and the liquid phase nickel as the binding phase, the coarse grain carbide as the hard phase can effectively inhibit the carbide from decomposing or oxidizing, so that the thermal decomposition or oxidation degree of the carbide in the supersonic flame spraying tungsten carbide-chromium carbide-nickel metal ceramic coating is extremely low, and the coating phase structure is basically consistent with the powder. Experimental results show that when the tungsten carbide-chromium carbide-nickel composite powder prepared by the preparation method is applied to preparing a metal ceramic coating by supersonic flame spraying, the microhardness of the obtained tungsten carbide-chromium carbide-nickel metal ceramic coating is 500-1150 HV0.3An elastic modulus of 72 to 372GPa and a fracture toughness of 1.5 to 5.3MPa x m1/2The wear rate of the dry pin disc is 0.0087-0.031 mg/N/m.
Drawings
FIG. 1 is a diagram of WC-Cr prepared in example 13C2-SEM image of Ni composite powder;
FIG. 2 shows WC-Cr prepared in example 13C2-cross-sectional SEM image of Ni composite powder;
FIG. 3 shows WC-Cr prepared in example 13C2-a particle size distribution map of the Ni composite powder;
FIG. 4 shows WC-Cr prepared in example 13C2-XRD patterns of Ni composite powder and cermet coating prepared in example 2;
FIG. 5 is a SEM image of a cross-section of a cermet coating prepared in example 2;
FIG. 6 shows WC-Cr prepared in example 13C2-XRD patterns of Ni composite powder and cermet coating prepared in example 3;
FIG. 7 is a SEM image of a cross-section of a cermet coating prepared in example 3;
FIG. 8 is a WC-Cr alloy prepared in example 43C2-SEM image of Ni composite powder;
FIG. 9 shows WC-Cr prepared in example 43C2-SEM image of Ni composite powder cross section;
FIG. 10 shows WC-Cr prepared in example 43C2-a particle size distribution map of the Ni composite powder;
FIG. 11 is WC-Cr prepared in example 43C2-XRD patterns of Ni composite powder and cermet coating prepared in example 5;
FIG. 12 is a cross-sectional SEM image of a cermet coating prepared according to example 5;
FIG. 13 is a view showing WC-Cr prepared in comparative example 13C2-SEM image of Ni composite powder;
FIG. 14 shows WC-Cr prepared in comparative example 13C2-cross-sectional SEM image of Ni composite powder;
FIG. 15 shows WC-Cr prepared in comparative example 13C2-a particle size distribution map of the Ni composite powder;
FIG. 16 shows WC-Cr prepared in comparative example 13C2-XRD patterns of Ni composite powder and cermet coating prepared in comparative example 2;
FIG. 17 shows WC-Cr prepared in comparative example 23C2-cross-sectional SEM image of Ni composite coating.
Detailed Description
The invention provides a preparation method of tungsten carbide-chromium carbide-nickel composite powder, which comprises the following steps:
(1) mixing 58-78% of multi-scale tungsten carbide, 10-30% of multi-scale chromium carbide and 6-20% of multi-scale nickel according to mass content to obtain mixed powder; the grain size of the multi-scale tungsten carbide is distributed between 0.6 and 6 mu m; the multi-scale chromium carbide is multi-scale Cr3C2Said multi-scale Cr3C2The particle size of the particles is distributed between 0.5 and 3 mu m; the grain size of the multi-scale nickel is distributed between 0.9 and 5 mu m;
(2) granulating the mixed powder obtained in the step (1) to obtain mixture granules;
(3) and (3) sintering the mixture particles obtained in the step (2) in vacuum to obtain tungsten carbide-chromium carbide-nickel composite powder.
According to the invention, 58-78% of multi-scale tungsten carbide, 10-30% of multi-scale chromium carbide and 6-20% of multi-scale nickel are mixed according to mass content to obtain mixed powder.
In the invention, the mass content of the multi-scale tungsten carbide in the raw materials for preparing the tungsten carbide-chromium carbide-nickel composite powder is 58-78%, preferably 60-75%, and more preferably 65-73%. In the invention, the grain size of the multi-scale tungsten carbide is preferably distributed between 0.6 and 6 microns, more preferably distributed between 0.6 and 5 microns, and most preferably distributed between 0.8 and 2.5 microns. The particle size distribution of the multi-scale tungsten carbide is not particularly limited, and the multi-scale tungsten carbide can be distributed in the particle size range. The source of the tungsten carbide is not particularly limited in the present invention, and the above particle size range can be achieved by using commercially available products known to those skilled in the art. In the invention, when the grain size of the multi-scale tungsten carbide is distributed between the ranges, the multi-scale effect is more obvious.
In the invention, the raw material for preparing the tungsten carbide-chromium carbide-nickel composite powder comprises 10-30% of multi-scale chromium carbide, preferably 20-30% by mass. In the invention, the grain size of the multi-scale chromium carbide is preferably distributed between 0.5 and 3 mu m, and more preferably distributed between 0.5 and 1.5 mu m. The grain size distribution of the multi-scale chromium carbide is not particularly limited, and the multi-scale chromium carbide can be distributed in the grain size range. The source of the multi-scale chromium carbide is not particularly limited in the present invention, and the above particle size range can be achieved by using commercially available products well known to those skilled in the art. In the present invention, when the grain size of the multi-scale chromium carbide is distributed between the above ranges, a more significant multi-scale effect is obtained.
In the invention, the raw material for preparing the tungsten carbide-chromium carbide-nickel composite powder comprises 6-20% of multi-scale nickel, preferably 8-12% of multi-scale nickel by mass. In the invention, the particle size of the multi-scale nickel is preferably distributed between 0.9 and 5 μm, more preferably distributed between 1 and 4 μm, and most preferably distributed between 1 and 3 μm. The grain size distribution of the multi-scale chromium carbide is not particularly limited, and the multi-scale chromium carbide can be distributed in the grain size range. The source of the multi-scale nickel is not particularly limited in the present invention, and the above particle size range can be achieved by using commercially available products well known to those skilled in the art. When the grain size of the multi-scale nickel is distributed between the ranges, the multi-scale effect is more obvious.
In the invention, by adopting multi-scale tungsten carbide, chromium carbide and nickel as raw materials, when preparing the tungsten carbide-chromium carbide-nickel composite powder, the prepared tungsten carbide-chromium carbide-nickel composite powder still has multi-scale particles.
The method for mixing the multi-scale tungsten carbide, the multi-scale chromium carbide and the multi-scale nickel is not particularly limited, and the mixing method known to those skilled in the art can be adopted. In the invention, the mixing mode is preferably ball milling. In the invention, the rotation speed of the ball milling is preferably 50-200 r/min, and more preferably 80-150 r/min; the ball-to-feed ratio of the ball mill is preferably 10: 1. In the invention, the ball milling can fully and uniformly mix multi-scale tungsten carbide, multi-scale chromium carbide and multi-scale nickel particles; when the ball milling parameters are preferably in the above ranges, the multi-scale tungsten carbide, the multi-scale chromium carbide and the multi-scale nickel particles are more fully mixed.
After the mixed powder is obtained, the mixed powder is granulated to obtain mixture particles.
In the present invention, the granulation is preferably spray granulation. In the present invention, the spray granulation includes: mixing the mixed powder with deionized water, ammonium polyacrylate and PEG-20000 solution to prepare slurry, then ball-milling the slurry in a ball mill at a rotation speed of 50-300 r/min for 8-10 h, and setting the drying temperature to 900-1250 ℃. The mixing mode of the mixed powder and the solution of deionized water, ammonium polyacrylate and PEG-20000 is not particularly limited, and the mixing mode known to those skilled in the art can be adopted.
In the invention, the rotation speed of the ball mill is preferably 80-250 r/min, and more preferably 100-150 r/min.
In the invention, the ball milling time is preferably 9-10 h.
In the invention, the drying temperature is preferably 250-550 ℃, and more preferably 400 ℃.
In the present invention, when the spray granulation parameter is preferably in the above range, the obtained mixture particles are nearly spherical, have good fluidity, and can further promote the deposition of the supersonic flame sprayed coating of the tungsten carbide-chromium carbide-nickel composite powder.
In the present invention, the particle size of the mixture particles is preferably 5 to 75 μm, and more preferably 15 to 53 μm. In the present invention, when the particle size of the mixture particles is preferably in the above range, the particle size of the mixture particles is matched with the particle size of the supersonic flame spraying powder feeding, so that it is possible to prevent the powder from being difficult to effectively feed due to too small particle size, and the mechanical properties of the obtained cermet coating can be further improved due to poor particle melting and low speed caused by too large particle size.
In the present invention, when the particle diameter of the granulated product is not in the above range, the granulated product is preferably post-treated to obtain a mixture particle. In the present invention, the post-treatment preferably comprises crushing and sieving, which are carried out sequentially. The crushing and screening operations are not particularly limited in the present invention, and the particle size of the mixture particles can be within the above range by using technical solutions well known to those skilled in the art.
After the mixture particles are obtained, the mixture particles are sintered in vacuum to obtain the tungsten carbide-chromium carbide-nickel composite powder. In the present invention, the vacuum sintering can ablate the organic binder used in the spray granulation process, and can also melt a very small amount of the mixed particles to increase the strength of the powder and promote the effective bonding of the particles. The vacuum sintering apparatus of the present invention is not particularly limited, and a vacuum sintering apparatus known to those skilled in the art may be used. In the present invention, the vacuum sintering apparatus is preferably a vacuum sintering furnace.
In the invention, the temperature of the vacuum sintering is preferably 900-1250 ℃, more preferably 950-1200 ℃, and most preferably 1000-1150 ℃. In the present invention, when the temperature of the vacuum sintering is in the above range, the organic binder in the decomposed mixture particles can be further increased, and the effective bonding of the respective particles can be promoted, thereby further improving the strength of the tungsten carbide-chromium carbide-nickel composite powder.
In the invention, the time for vacuum sintering is preferably 0.5-3 h, and more preferably 1-2 h. In the present invention, when the vacuum sintering time is preferably within the above range, abnormal growth of powder particles can be further prevented, and effective bonding of particles can be further promoted, which is more advantageous for obtaining a tungsten carbide-chromium carbide-nickel composite powder having high strength.
The preparation method of the tungsten carbide-chromium carbide-nickel composite powder provided by the invention adopts multi-scale tungsten carbide, multi-scale chromium carbide and multi-scale nickel as raw materials, and obtains particles still with multi-scale inside the tungsten carbide-chromium carbide-nickel composite powder through mixing, spray granulation and vacuum sintering; the multi-scale carbide composition can avoid the problems of increase of brittle phase of a coating and low microhardness of coarse-crystal carbide particles caused by high-temperature thermal decomposition or oxidation of the fine-crystal carbide during supersonic flame spraying of the tungsten carbide-chromium carbide-nickel composite powder.
The invention also provides the tungsten carbide-chromium carbide-nickel composite powder prepared by the technical scheme. In the present invention, the tungsten carbide-chromium carbide-nickel composite powder has multi-scale particles inside.
In the invention, the particle size of the tungsten carbide-chromium carbide-nickel composite powder is 5-75 μm, and preferably 15-53 μm. In the present invention, the particle size of the tungsten carbide-chromium carbide-nickel composite powder needs to be matched with the particle size required for supersonic flame spraying, and when the particle size of the tungsten carbide-chromium carbide-nickel composite powder is within the above range, the particle size can be better matched with the particle size required for supersonic flame spraying.
The invention also provides a preparation method of the metal ceramic coating, wherein the metal ceramic coating is prepared by spraying tungsten carbide-chromium carbide-nickel composite powder through supersonic flame; the parameters of the supersonic flame spraying comprise: the flow rate of oxygen is 241.2-804.1 slpm, the flow rate of propane is 15.9-53.3 slpm, the flow rate of nitrogen is 20.6-82.6 slpm, the distance between the outlet end of a spray gun for supersonic flame spraying and the surface of a base material is 80-250 mm, the speed of the spray gun moving parallel to the base body is 50-500 mm/s, and the powder feeding speed is 5-40 g/min.
In the invention, the flow rate of oxygen in the supersonic flame spraying is 241.2-804.1 slpm, preferably 300-723.7 slpm, and more preferably 321.6-603.1 slpm. In the present invention, when the oxygen flow rate is in the above range, it is possible to prevent the supersonic flame temperature from being lowered due to an excessively high oxygen flow rate, so that the powder is hard to melt or soften; the flame combustion is unstable due to too low flame, and the mechanical property of the metal ceramic coating can be further improved.
In the invention, the flow rate of propane in the supersonic flame spraying is 15.9-53.3 slpm, preferably 32-53.3 slpm. In the present invention, when the propane flow rate is in the above range, it is possible to prevent the supersonic flame temperature from being extremely high due to an excessively high propane flow rate, which is likely to cause thermal decomposition of carbide, and to prevent the powder from being melted or softened with difficulty due to an excessively low propane flow rate, thereby further improving the mechanical properties of the cermet coating layer.
In the invention, the flow rate of nitrogen in the supersonic flame spraying is 20.6-82.6 slpm, preferably 23.9-60 slpm, and more preferably 23.9-37.1 slpm. In the present invention, when the nitrogen gas flow rate is preferably in the above range, it is possible to prevent the entire flame temperature from being lowered due to an excessively high nitrogen gas flow rate and a large amount of powder from being not melted due to an excessively high powder feed rate; the powder feeding rate is low due to over-low condition, the deposition efficiency of the coating is low, and the mechanical property of the metal ceramic coating can be further improved.
In the invention, the distance between the outlet end of the spray gun for supersonic flame spraying and the surface of the base material is 80-250 mm, preferably 170-250 mm.
In the invention, the speed of the spray gun for supersonic flame spraying moving parallel to the substrate is 50-500 mm/s, preferably 500 mm/s.
In the invention, the powder feeding speed of the supersonic flame spraying is 5-40 g/min, preferably 20-30 g/min.
In the invention, when the parameter of the supersonic flame spraying is preferably in the range, the supersonic flame spraying is more favorable for forming a small amount of bonding phase for melting the fine crystalline carbide and the liquid phase nickel and hard phase for melting the coarse crystalline carbide in the spraying process, and obtaining the metal ceramic coating with the multi-scale fine crystalline carbide and coarse crystalline carbide distributed in the nickel matrix, thereby being more favorable for improving the mechanical property of the metal ceramic coating.
In the present invention, the cermet coating is preferably formed by spraying tungsten carbide-chromium carbide-nickel composite powder onto a substrate by a supersonic flame. The substrate of the present invention is not particularly limited, and a substrate known to those skilled in the art may be used. In the present invention, the substrate preferably comprises a coarsened low carbon steel substrate.
The invention adopts tungsten carbide-chromium carbide-nickel composite powder with a multi-scale carbide structure as a raw material, adopts supersonic flame spraying to prepare the metal ceramic coating, wherein the coarse-grain carbide does not undergo melting thermal decomposition in the supersonic flame spraying process, the fine-grain carbide undergoes little melting and the metal nickel undergoes melting, a small amount of molten fine-grain carbide and liquid-phase nickel are used as binding phases, and the coarse-grain carbide is used as a hard phase, so that the thermal decomposition or oxidation degree of the carbide in the prepared supersonic flame spraying tungsten carbide-chromium carbide-nickel metal ceramic coating is extremely low, the phase structure of the coating is basically consistent with that of the powder, and the mechanical property of the metal ceramic coating can be further improved.
The invention also provides the metal ceramic coating prepared by the preparation method of the technical scheme.
The metal ceramic coating provided by the invention has extremely low thermal decomposition or oxidation degree of carbide, and the coating phase structure is basically consistent with that of powder, so that the metal ceramic coating has excellent mechanical properties.
The technical solution of the present invention will be clearly and completely described below with reference to the embodiments of the present invention. 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 embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Example 1
Raw materials: multi-scale WC particles with a particle size of 0.8-2.5 μm, and multi-scale Cr particles with a particle size of 0.5-1.5 μm3C2Particles and multi-scale Ni particles with the particle size of 1-3 mu m.
Powder preparation: according to the mass content, 58 percent of multi-scale WC particles and 30 percent of multi-scale Cr are mixed3C2Mixing the particles and multi-scale Ni particles with the mass fraction of 12% by a ball mill at a ball-to-material ratio of 10:1 and a rotating speed of 120r/min for 10 hours; preparation of WC-Cr by spray granulation3C2-Ni mixed powder, and screening to obtain powder with the particle size of 15-53 μm; for WC-Cr3C2-sintering the Ni mixed powder in a vacuum sintering furnace at 1150 ℃ for 2 hours; obtaining WC-Cr3C2-Ni composite powder.
WC-Cr obtained in this example3C2SEM image of Ni composite powder as in fig. 1;
WC-Cr obtained in this example3C2A cross-sectional SEM image of the Ni composite powder is shown in fig. 2;
WC-Cr obtained in this example3C2The particle size distribution diagram of the-Ni composite powder is shown in fig. 3;
WC-Cr obtained in this example3C2The XRD pattern of the-Ni composite powder is shown in FIG. 4.
As can be seen from FIG. 1, WC-Cr3C2the-Ni composite powder has a nearly spherical structure and a partially irregular structure.
As can be seen from FIG. 2, WC particles in bright color, Ni particles in gray color and Cr particles in dark gray color3C2Particles; WC-Cr3C2-the Ni composite powder size is 15-53 microns; the powder is composed of WC and Cr3C2And a Ni phase.
Example 2
Preparing a metal ceramic coating: WC-Cr prepared as in example 13C2And the-Ni composite powder is spraying powder serving as a raw material, and a coating is deposited on the surface of the coarsened low-carbon steel matrix by adopting a supersonic flame spraying technology to obtain the metal ceramic coating. The supersonic flame spraying parameters are as follows: the oxygen flow was 482.5slpm, propane flow was 40slpm, nitrogen flow was 41.3slpm, the spraying distance was 170mm, the scanning speed was 500m/s, and the powder feeding rate was 20 g/min.
Cermet coatingTesting the mechanical properties of the layers: the characterization and the test of GB T37421 and 2019 thermal spraying coating are adopted to obtain that the microhardness of the coating is 641 +/-110 HV0.3The elastic modulus is 226 +/-47 GPa, and the fracture toughness is 3.7 +/-1.1 MPa multiplied by m1/2The wear rate of the dry pin disc is 0.016 plus or minus 0.004 mg/N/m.
The XRD pattern of the cermet coating obtained in this example is shown in FIG. 4;
the SEM spectrum of the cross section of the cermet coating obtained in this example is shown in FIG. 5.
As can be seen from FIG. 4, the coating is made of WC and Cr3C2Mainly phase-dominated and containing only a very small amount of Cr7C3And WC1-xThe thermal decomposition phase of (A) shows that the carbide of the coating has only low thermal decomposition phenomenon, and the composition of the metal ceramic coating and WC-Cr3C2the-Ni composite powder was almost uniform.
As can be seen from FIG. 5, the bright nearly spherical particles are WC, the gray region is Ni-Cr-W solid solution phase, and the dark gray random region is Cr3C2。
Example 3
Preparing a metal ceramic coating: WC-Cr prepared as described in example 13C2the-Ni composite powder is thermal spraying powder, and a coating is deposited on the surface of the coarsened low-carbon steel matrix by adopting a supersonic flame spraying technology to obtain the metal ceramic coating. The supersonic flame spraying parameters are as follows: the oxygen flow was 321.7slpm, the propane flow was 40slpm, the nitrogen flow was 41.3slpm, the spraying distance was 170mm, the scanning speed was 500m/s, and the powder feeding rate was 20 g/min.
Testing the mechanical properties of the metal ceramic coating: the characterization and the test of GB T37421 and 2019 thermal spraying coating are adopted to obtain that the microhardness of the coating is 904 +/-257 HV0.3The elastic modulus is 166 +/-24 GPa, and the fracture toughness is 4.3 +/-0.9 MPa multiplied by m1/2The wear rate of the dry pin disc is 0.016 +/-0.003 mg/N/m.
WC-Cr obtained in this example3C2The XRD pattern of the Ni composite powder and the XRD pattern of the cermet coating are shown in FIG. 6;
the SEM spectrum of the cross section of the cermet coating obtained in this example is shown in FIG. 7.
As can be seen from FIG. 6, the coating was divided by WC and Cr3C2Besides the main phase, the alloy also contains a very small amount of thermally decomposed phase WC1-x、Cr7C3And an oxidized phase Cr2O3But without the presence of a thermally decomposed phase W2C. Shows that the degree of thermal decomposition of carbide in the coating is lower, and the composition of the metal ceramic coating and WC-Cr3C2the-Ni composite powder was almost uniform.
As can be seen from FIG. 7, the bright nearly spherical particles are WC, the gray region is Ni-Cr-W solid solution phase, and the dark gray random region is Cr3C2。
Example 4
Raw materials: multi-scale WC particles with a particle size of 0.8-2.5 μm, Cr particles with a particle size of 0.5-1.5 μm3C2Particles and multi-scale Ni particles with the particle size of 1-3 mu m.
Powder preparation: according to the mass content, 72 percent of multi-scale WC particles and 20 percent of multi-scale Cr are mixed3C2Mixing the particles and 8 mass percent of multi-scale Ni particles by a ball mill at a ball-to-material ratio of 10:1 and a rotating speed of 120r/min for 10 hours; preparation of WC-Cr by spray granulation3C2-Ni mixed powder, and screening to obtain powder with the particle size of 15-53 μm; for WC-Cr3C2-sintering the Ni mixed powder in a vacuum sintering furnace at 1150 ℃ for 2 hours; obtaining WC-Cr3C2-Ni composite powder.
WC-Cr obtained in this example3C2The SEM spectrum of the-Ni composite powder is shown in fig. 8;
WC-Cr obtained in this example3C2The SEM spectrum of the cross section of the Ni composite powder is shown in FIG. 9;
WC-Cr obtained in this example3C2The particle size distribution of the-Ni composite powder is shown in fig. 10;
WC-Cr obtained in this example3C2The XRD pattern of the-Ni composite powder is shown in FIG. 11.
As can be seen from FIG. 8, WC-Cr3C2the-Ni composite powder has a nearly spherical structure and a partially irregular structure.
As can be seen from FIG. 9, WC grains in bright color, Ni grains in gray color, and Cr grains in dark gray color3C2Particles; the powder size is 15-53 microns; the powder is composed of WC and Cr3C2And a Ni phase.
Example 5
Preparing a metal ceramic coating: WC-Cr prepared as in example 43C2And the-Ni composite powder is spraying powder serving as a raw material, and a coating is deposited on the surface of the coarsened low-carbon steel matrix by adopting a supersonic flame spraying technology to obtain the metal ceramic coating. The supersonic flame spraying parameters are as follows: the oxygen flow rate was 321.6slpm, the propane flow rate was 40slpm, the nitrogen flow rate was 61.9slpm, the spraying distance was 170mm, the scanning speed was 500m/s, and the powder feeding rate was 20 g/min.
Testing the mechanical properties of the metal ceramic coating: the characterization and the test of GB T37421 and 2019 thermal spraying coating are adopted to obtain that the microhardness of the coating is 797 +/-236 HV0.3Elastic modulus of 147 +/-57 GPa and fracture toughness of 2.6 +/-0.2 MPa x m1/2The wear rate of the dry pin disc is 0.033 +/-0.009 mg/N/m.
The XRD pattern of the cermet coating obtained in this example is shown in FIG. 11;
the SEM spectrum of the cross section of the cermet coating obtained in this example is shown in FIG. 12.
As can be seen from FIG. 11, the coating is made of WC and Cr3C2And Ni phase as main component, which is basically consistent with the original powder phase structure.
As can be seen from FIG. 12, in the SEM image of the cross section of the cermet coating, the bright particles are WC, the gray areas are rich in Ni-Cr-W solid solution, and the dark gray areas are Cr3C2The coating contains a small number of pores.
Comparative example 1
Raw materials: tungsten carbide particles having a particle size of 0.2 to 0.5 μm, chromium carbide particles having a particle size of 0.1 to 0.3 μm, and Ni particles having a particle size of 0.4 to 0.8 μm.
Powder preparation: according to the mass content, 58 percent of WC particles by mass are mixed30% of Cr3C2Mixing the particles and Ni particles with the mass fraction of 12% by a ball mill at a ball-to-material ratio of 10:1 and a rotating speed of 120r/min for 10 hours; preparation of WC-Cr by spray granulation3C2-Ni mixed powder, and screening to obtain powder with the particle size of 15-53 μm; for WC-Cr3C2-sintering the Ni mixed powder in a vacuum sintering furnace at 1150 ℃ for 2 hours; obtaining WC-Cr3C2-Ni composite powder.
FIG. 13 is a view showing WC-Cr prepared in comparative example 13C2-SEM image of Ni composite powder;
FIG. 14 shows WC-Cr prepared in comparative example 13C2-cross-sectional SEM image of Ni composite powder;
FIG. 15 shows WC-Cr prepared in comparative example 13C2-particle size distribution of Ni composite powder.
As can be seen from FIG. 13, WC-Cr3C2the-Ni composite powder has a nearly spherical structure and a partially irregular structure.
As can be seen from FIGS. 13-14, the bright colors are WC particles, gray Ni particles and dark gray Cr particles3C2The particles are difficult to distinguish on the powder section because of the small original particle size; WC-Cr3C2-the Ni composite powder size is 15-53 microns; the powder is composed of WC and Cr3C2And a Ni phase.
Comparative example 2
Preparing a metal ceramic coating: WC-Cr prepared as in comparative example 13C2And the-Ni composite powder is spraying powder, and a coating is deposited on the surface of the coarsened low-carbon steel matrix by adopting a supersonic flame spraying technology to obtain the metal ceramic coating. The supersonic flame spraying parameters are as follows: the oxygen flow was 482.5slpm, propane flow was 40slpm, nitrogen flow was 41.3slpm, the spraying distance was 170mm, the scanning speed was 500m/s, and the powder feeding rate was 20 g/min.
FIG. 16 shows WC-Cr prepared in comparative example 13C2-XRD patterns of Ni composite powder and cermet coating prepared in comparative example 2;
FIG. 17 shows WC-Cr prepared in comparative example 23C2SEM image of cross section of-Ni composite coating。
As can be seen from FIG. 15, the coating contains WC and Cr3C2And besides Ni, WC is remarkably generated by remarkable thermal decomposition2And WC1-XPhase, the structure is obviously different from the original powder phase.
As can be seen from the SEM spectrum of the cross section of the coating in FIG. 17, the bright particles are mainly WC, the gray areas are Ni-Cr-W-rich solid solution areas, and a large number of holes are formed in the coating.
Testing the mechanical properties of the metal ceramic coating: the characterization and the test of GB T37421 and 2019 thermal spraying coating are adopted to obtain that the microhardness of the coating is 610 +/-220 HV0.3The elastic modulus is 171 +/-49 GPa, and the fracture toughness is 3.2 +/-1.3 MPa multiplied by m1/2The wear rate of the dry pin disc is 0.02 +/-0.003 mg/N/m.
From the above examples 1 to 5, it can be seen that when the tungsten carbide-chromium carbide-nickel composite powder obtained by the preparation method of the tungsten carbide-chromium carbide-nickel composite powder provided by the invention is applied to a metal ceramic coating prepared by supersonic flame spraying, the thermal decomposition or oxidation degree of carbide in the metal ceramic coating is extremely low, the phase structure of the coating is basically consistent with that of the powder, the coating has excellent mechanical properties, and the mechanical properties are higher than those of the metal ceramic coating prepared in the comparative example 2.
The foregoing is only a preferred embodiment of the present invention, and it should be noted that, for those skilled in the art, various modifications and decorations can be made without departing from the principle of the present invention, and these modifications and decorations should also be regarded as the protection scope of the present invention.
Claims (10)
1. A preparation method of tungsten carbide-chromium carbide-nickel composite powder comprises the following steps:
(1) mixing 58-78% of multi-scale tungsten carbide, 10-30% of multi-scale chromium carbide and 6-20% of multi-scale nickel according to mass content to obtain mixed powder; the grain size of the multi-scale tungsten carbide is distributed between 0.6 and 6 mu m; the multi-scale chromium carbide is multi-scale Cr3C2Said multi-scale Cr3C2Particle size distribution of0.5-3 μm; the grain size of the multi-scale nickel is distributed between 0.9 and 5 mu m;
(2) granulating the mixed powder obtained in the step (1) to obtain mixture granules;
(3) and (3) sintering the mixture particles obtained in the step (2) in vacuum to obtain tungsten carbide-chromium carbide-nickel composite powder.
2. The method for preparing the tungsten carbide-chromium carbide-nickel composite powder according to claim 1, wherein the grain size of the multi-scale tungsten carbide is distributed between 0.6 and 5 μm; the multi-scale Cr3C2The particle size of the particles is distributed between 0.5 and 1.5 mu m; the particle size of the multi-scale nickel is distributed between 1 and 4 mu m.
3. The method for preparing a tungsten carbide-chromium carbide-nickel composite powder according to claim 1, wherein the granulation in the step (2) is spray granulation.
4. The method of preparing a tungsten carbide-chromium carbide-nickel composite powder according to claim 3, wherein the spray granulation comprises: and mixing the mixed powder with deionized water, ammonium polyacrylate and PEG-20000 solution to prepare slurry, then ball-milling for 8-10 h in a ball mill at a rotating speed of 50-300 r/min, setting the drying temperature to be 250-550 ℃, and drying and agglomerating the slurry to obtain mixture particles.
5. The method for preparing the tungsten carbide-chromium carbide-nickel composite powder according to claim 1, wherein the temperature of the vacuum sintering in the step (3) is 900 to 1250 ℃.
6. The method for preparing the tungsten carbide-chromium carbide-nickel composite powder according to claim 1 or 5, wherein the sintering time of the vacuum sintering is 0.5 to 3 hours.
7. The method for preparing a tungsten carbide-chromium carbide-nickel composite powder according to claim 1, wherein the particle diameter of the mixture particles is 5 to 75 μm.
8. The tungsten carbide-chromium carbide-nickel composite powder obtained by the production method according to any one of claims 1 to 7, wherein the particle size of the tungsten carbide-chromium carbide-nickel composite powder is 5 to 75 μm.
9. A method for preparing a cermet coating, which is obtained by spraying the tungsten carbide-chromium carbide-nickel composite powder of claim 7 through supersonic flame spraying; the parameters of the supersonic flame spraying comprise: the flow rate of oxygen is 241.2-804.1 slpm, the flow rate of propane is 15.9-53.3 slpm, the flow rate of nitrogen is 20.6-82.6 slpm, the distance between the outlet end of a spray gun for supersonic flame spraying and the surface of a base material is 80-250 mm, the speed of the spray gun moving parallel to the base body is 50-500 mm/s, and the powder feeding speed is 5-40 g/min.
10. The cermet coating produced by the method of claim 9.
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| CN114042911A (en) * | 2021-11-22 | 2022-02-15 | 河北京津冀再制造产业技术研究有限公司 | Composite powder, composite coating, preparation method and application thereof |
| CN114042911B (en) * | 2021-11-22 | 2023-11-24 | 河北京津冀再制造产业技术研究有限公司 | Composite powder, composite coating, preparation method and application thereof |
| CN117904572A (en) * | 2024-01-15 | 2024-04-19 | 东北大学 | A method for improving the wear resistance of hydrophobic coating by turning |
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