CN115007870A - Preparation method of powder for generating high-entropy alloy coating through laser aluminothermic reduction - Google Patents
Preparation method of powder for generating high-entropy alloy coating through laser aluminothermic reduction Download PDFInfo
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- 239000000843 powder Substances 0.000 title claims abstract description 141
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 58
- 239000000956 alloy Substances 0.000 title claims abstract description 58
- 238000000576 coating method Methods 0.000 title claims abstract description 46
- 239000011248 coating agent Substances 0.000 title claims abstract description 43
- 230000009467 reduction Effects 0.000 title claims abstract description 21
- 238000002360 preparation method Methods 0.000 title claims abstract description 15
- 238000000498 ball milling Methods 0.000 claims abstract description 69
- 239000002131 composite material Substances 0.000 claims abstract description 29
- 239000000919 ceramic Substances 0.000 claims abstract description 13
- 238000002156 mixing Methods 0.000 claims abstract description 12
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims abstract description 9
- 239000002245 particle Substances 0.000 claims abstract description 9
- 238000001291 vacuum drying Methods 0.000 claims abstract description 9
- 229910010413 TiO 2 Inorganic materials 0.000 claims abstract description 8
- 238000001035 drying Methods 0.000 claims abstract description 7
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 5
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 3
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 3
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 3
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 3
- 239000000463 material Substances 0.000 claims description 18
- 238000000034 method Methods 0.000 claims description 11
- 238000000227 grinding Methods 0.000 claims description 10
- 238000001238 wet grinding Methods 0.000 claims description 4
- 238000004321 preservation Methods 0.000 claims description 3
- 238000004372 laser cladding Methods 0.000 abstract description 13
- 238000010521 absorption reaction Methods 0.000 abstract description 8
- 230000003746 surface roughness Effects 0.000 abstract description 6
- 239000000126 substance Substances 0.000 abstract description 4
- 230000006872 improvement Effects 0.000 abstract description 3
- 238000002310 reflectometry Methods 0.000 abstract description 3
- 230000002787 reinforcement Effects 0.000 abstract 1
- 238000006722 reduction reaction Methods 0.000 description 14
- 230000000694 effects Effects 0.000 description 8
- OGIDPMRJRNCKJF-UHFFFAOYSA-N titanium oxide Inorganic materials [Ti]=O OGIDPMRJRNCKJF-UHFFFAOYSA-N 0.000 description 7
- 230000009286 beneficial effect Effects 0.000 description 5
- 230000003647 oxidation Effects 0.000 description 5
- 238000007254 oxidation reaction Methods 0.000 description 5
- 238000001179 sorption measurement Methods 0.000 description 5
- 239000010935 stainless steel Substances 0.000 description 4
- 229910001220 stainless steel Inorganic materials 0.000 description 4
- 238000009826 distribution Methods 0.000 description 3
- 230000003014 reinforcing effect Effects 0.000 description 3
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N Titan oxide Chemical compound O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 229910001234 light alloy Inorganic materials 0.000 description 2
- 239000011858 nanopowder Substances 0.000 description 2
- 230000008569 process Effects 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- 229910052581 Si3N4 Inorganic materials 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000005253 cladding Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 229910052593 corundum Inorganic materials 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000003912 environmental pollution Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000011065 in-situ storage Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- HQVNEWCFYHHQES-UHFFFAOYSA-N silicon nitride Chemical compound N12[Si]34N5[Si]62N3[Si]51N64 HQVNEWCFYHHQES-UHFFFAOYSA-N 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 229910001845 yogo sapphire Inorganic materials 0.000 description 1
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/16—Making metallic powder or suspensions thereof using chemical processes
- B22F9/18—Making metallic powder or suspensions thereof using chemical processes with reduction of metal compounds
- B22F9/20—Making metallic powder or suspensions thereof using chemical processes with reduction of metal compounds starting from solid metal compounds
- B22F9/22—Making metallic powder or suspensions thereof using chemical processes with reduction of metal compounds starting from solid metal compounds using gaseous reductors
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/001—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides
- C22C32/0015—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides with only single oxides as main non-metallic constituents
- C22C32/0031—Matrix based on refractory metals, W, Mo, Nb, Hf, Ta, Zr, Ti, V or alloys thereof
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
- B22F2009/043—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling by ball milling
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
Abstract
A preparation method of powder for generating a high-entropy alloy coating by laser aluminothermic reduction is characterized by comprising the following steps: mixing nanometer TiO 2 Mixing the powder with Al, Nb, Ti, V and Cr powder, adding absolute ethyl alcohol, and performing ball milling in a planetary ball mill to obtain composite powder; keeping the temperature of the ball-milled composite powder in a vacuum drying oven for drying; then, ball milling and crushing are fully carried out, and the light high-entropy alloy coating composite powder for generating ceramic phase reinforcement by laser aluminothermic reduction is prepared; the nanometer powder has small particle size, large specific surface area and high specific surface energy, and can be adsorbed on the surface of micron-sized powder, and the nanometer TiO powder is prepared by mixing the nanometer powder and the nanometer powder 2 When the powder is adsorbed on the surface of other micron-sized powder, the powder is changed into the powderThe surface chemical components and the surface roughness of the micron-sized powder are changed, the light reflection form is more prone to diffuse reflection due to the improvement of the surface roughness, and the reflectivity of laser is reduced, so that the laser absorption coefficient of the composite powder is improved, and the preparation of the light high-entropy alloy coating by laser cladding is facilitated.
Description
Technical Field
The invention belongs to the field of high-entropy alloy coating powder preparation, and particularly relates to a powder preparation method for generating a high-entropy alloy coating by laser aluminothermic reduction.
Background
In 2004, the concept of high entropy alloy was first proposed by professor yearn of scholars in all over the world. The high-entropy alloy generally comprises five or more main elements, and the elements are composed according to equal atomic ratio or nearly equal atomic ratio. Different from the traditional alloy, the high-entropy alloy is easy to form a single solid solution phase due to high mixing entropy, and has four remarkable effects: thermodynamic high entropy effect, kinetic slow diffusion effect, structural lattice distortion effect, and performance "cocktail effect". The unique crystal structure and four effects enable the high-entropy alloy to have excellent wear resistance, corrosion resistance and high-temperature oxidation resistance. The light alloy can save energy and reduce environmental pollution while reducing the weight of the component, and is widely applied to the fields of automobile traffic, aerospace, electronic parts and the like. The proposal of the high-entropy alloy concept provides a new direction for the development of light alloys.
Laser cladding is used as a technology for preparing the coating and has the characteristics of fast heating and fast cooling. The heat input amount is uniform, the heat affected zone is small, a coating with higher density can be obtained, and the size and the shape can be accurately controlled.
When the light high-entropy alloy coating is prepared by laser cladding, metal ceramic powder can be added into the light high-entropy alloy powder to generate an in-situ self-generated reaction to generate a ceramic reinforcing phase, so that the performance of the light high-entropy alloy coating is further improved.
However, the high-entropy alloy coating prepared by the laser cladding technology at present has the following defects:
1. the composite powder for preparing the high-entropy alloy coating has low laser absorption coefficient, so that the comprehensive performance and the efficiency of the preparation process of the alloy coating are low in the laser cladding preparation process;
2. the heat input amount in the process of preparing the high-entropy alloy coating by the traditional laser cladding is small, so that the temperature field distribution of a molten pool is uneven, the organization structure of the finally prepared coating is sparse, and the quality of the whole coating is poor;
3. the high-entropy alloy coating prepared by the traditional laser cladding has low oxidation resistance.
Disclosure of Invention
In order to solve the technical problems, the invention provides a powder preparation method for generating a high-entropy alloy coating by laser aluminothermic reduction, which aims to solve the problems that the laser absorption coefficient of composite powder is low, the heat input is small and the finally prepared alloy coating is not strong in oxidation resistance in the process of preparing the high-entropy alloy coating by laser cladding.
In order to achieve the technical effect of solving the technical problems, the invention is realized by the following technical scheme: a preparation method of powder for generating a high-entropy alloy coating by laser aluminothermic reduction is characterized by comprising the following steps:
s1 mixing nano TiO 2 Mixing the powder with Al, Nb, Ti, V and Cr powder, adding absolute ethyl alcohol, and performing ball milling in a planetary ball mill to obtain composite powder;
s2, drying the ball-milled composite powder in a vacuum drying oven under the condition of heat preservation;
s3, performing ball milling and crushing to prepare composite powder for generating the ceramic phase reinforced light high-entropy alloy coating by laser aluminothermic reduction;
further, all the powder in the S1 is spherical powder, the purity is not lower than 99.99%, the mass fraction of the absolute ethyl alcohol is 16.24-16.46 wt%, and the particle size and the content of the powder are represented as follows:
further, the ball milling mode in the S2 is wet milling, the ball milling rotation speed is 120-150 rpm, the ball material ratio is 4:1, and the ball milling time is 2-8 h;
further, in the S2, heat preservation is carried out for 8-10 hours at 70 ℃ in a vacuum drying oven;
further, in the S2, the ball grinding time is 2-3 h, the rotating speed is 120-150 rpm, and the ball material ratio is 4: 1.
The invention has the beneficial effects that:
1. the nanometer powder has small particle size, large specific surface area, high specific surface energy and good adsorption performance, and can be adsorbed on the surface of micron-sized powder, and the nanometer TiO powder has the advantages of high adsorption performance and low cost 2 When the composite powder is adsorbed on the surface of other micron-sized powder, the surface chemical components and the surface roughness of the micron-sized powder are changed, the improvement of the surface roughness enables the light reflection form to be more prone to diffuse reflection, and the reflectivity of laser is reduced, so that the laser absorption coefficient of the composite powder is improved, and the preparation of the light high-entropy alloy coating by laser cladding is facilitated;
2. second, nano TiO 2 The aluminum reduction reaction can be carried out with Al powder, so that the heat input during cladding is improved, the temperature field distribution of a molten pool is more uniform, and the coating structure is more compact; the Al2O3 ceramic reinforcing phase generated by the method is beneficial to improving the high-temperature oxidation resistance of the light high-entropy alloy coating.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings used in the description of the embodiments will be briefly introduced below, and it is obvious that the drawings in the following description are only some embodiments of the present invention, and it is obvious for those skilled in the art that other drawings can be obtained according to the drawings without creative efforts.
FIG. 1 is an SEM morphology of a light high-entropy alloy composite powder prepared in example 1;
FIG. 2 is an SEM morphology of a light high-entropy alloy composite powder prepared in example 1;
FIG. 3 is an SEM morphology of a light high-entropy alloy composite powder prepared in example 2;
FIG. 4 is an SEM morphology of a light high-entropy alloy composite powder prepared in example 3;
fig. 5 shows the laser absorption coefficients of the powders prepared in example 1 and comparative example 1.
Detailed Description
The technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the drawings in the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all of the embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Example 1
Referring to fig. 1 to 2, a method for preparing powder for generating a high-entropy alloy coating by laser aluminothermic reduction specifically comprises the following steps:
(1) weigh 0.60 wt% of the nano TiO with an electronic balance with an accuracy of + -0.1 mg 2 Powder, 8.25 wt% of Al powder, 28.49 wt% of Nb powder, 14.64 wt% of Ti powder, 15.67 wt% of V powder and 15.89 wt% of Cr powder; wherein all the powders are spherical powders and nano TiO 2 The grain size of the Al powder is 100-200 nm, the grain size of the Al powder is 10-12 mu m, and the grain sizes of the rest powders are 13-52 mu m;
(2) putting all the powder into a ball milling tank, adding 16.46 wt% of absolute ethyl alcohol, fully mixing, and then adding grinding balls to enable the ball material ratio to be 4:1, wherein the ball milling tank and the grinding balls are made of stainless steel materials. The ball milling can is filled in a star-type ball mill for ball milling, the ball milling speed is 120rpm, and the ball milling time is 8 hours; wherein, the ball milling is stopped after the ball milling is repeatedly circulated for 16 times by pausing for 5min every 15min of forward rotation, then pausing for 5min after 15min of reverse rotation and receiving the forward rotation for 15 min;
(3) drying the ball-milled light high-entropy alloy composite powder in a vacuum drying oven for 8 hours at 70 ℃;
(4) putting the dried light high-entropy alloy composite powder into a planetary ball mill to be crushed for 2 hours, wherein the ball milling speed is 120rpm, and the ball-to-material ratio is 4: 1; wherein, the ball milling is stopped after the reciprocating circulation is carried out for 4 times after the ball milling is stopped for 5min when the ball milling is carried out for 15min each time when the ball milling is carried out; finally, the powder for generating the ceramic phase reinforced light high-entropy alloy coating by laser aluminothermic reduction is prepared.
Example 2
Referring to fig. 3, a method for preparing powder for producing a ceramic phase reinforced lightweight high-entropy alloy coating by laser aluminothermic reduction specifically comprises the following steps:
(1) weigh 0.60 wt% of the nano TiO with an electronic balance with an accuracy of + -0.1 mg 2 Powder, 8.25 wt% of Al powder, 28.49 wt% of Nb powder, 14.64 wt% of Ti powder, 15.67 wt% of V powder and 15.89 wt% of Cr powder; wherein all the powders are spherical powders and nano TiO 2 The grain size of the Al powder is 100-200 nm, the grain size of the Al powder is 10-12 mu m, and the grain sizes of the rest powders are 13-52 mu m;
(2) putting all the powder into a ball milling tank, adding 16.46 wt% of absolute ethyl alcohol, mixing, and then adding grinding balls to enable the ball-material ratio to be 4:1, wherein the ball milling tank and the grinding balls are made of stainless steel materials; the ball milling can is filled in a star type ball mill for full ball milling, the ball milling speed is 120rpm, and the ball milling time is 2 hours; wherein, the ball milling is stopped after the reciprocating circulation is carried out for 4 times after the ball milling is stopped for 5min when the ball milling is carried out for 15min each time when the ball milling is carried out;
(3) drying the ball-milled light high-entropy alloy composite powder in a vacuum drying oven for 8 hours at 70 ℃;
(4) putting the dried light high-entropy alloy composite powder into a planetary ball mill to be crushed for 2 hours, wherein the ball milling speed is 120rpm, and the ball-to-material ratio is 4: 1; wherein, the ball milling is stopped after the reciprocating circulation is carried out for 4 times after the ball milling is stopped for 5min when the ball milling is carried out for 15min each time when the ball milling is carried out; finally, the powder for generating the ceramic phase reinforced light high-entropy alloy coating by laser aluminothermic reduction is prepared.
Example 3
Referring to fig. 4, a method for preparing powder for producing a ceramic phase reinforced lightweight high-entropy alloy coating by laser aluminothermic reduction specifically comprises the following steps:
(1) weigh 0.60 wt% of the nano TiO with an electronic balance with an accuracy of + -0.1 mg 2 Powder, 8.25 wt% of Al powder, 28.49 wt% of Nb powder, 14.64 wt% of Ti powder, 15.67 wt% of V powder15.89 wt% of Cr powder; wherein all the powder is spherical powder, the particle size of the nano TiO2 is 100-200 nm, the particle size of the Al powder is 10-12 mu m, and the particle sizes of the rest powder are 13-52 mu m;
(2) putting all the powder into a ball milling tank, adding 16.46 wt% of absolute ethyl alcohol, mixing, and then adding grinding balls to enable the ball-material ratio to be 4:1, wherein the ball milling tank and the grinding balls are made of stainless steel materials; the ball milling can is canned and fully ball milled in a star-type ball mill, the ball milling rotating speed is 120rpm, and the ball milling time is 4 hours; wherein, the ball milling is stopped after the reciprocating circulation is carried out for 8 times after the ball milling is stopped for 5min when the ball milling is carried out for 15min each time when the ball milling is carried out;
(3) drying the ball-milled light high-entropy alloy composite powder in a vacuum drying oven for 8 hours at 70 ℃;
(4) putting the dried light high-entropy alloy composite powder into a planetary ball mill to be crushed for 2 hours, wherein the ball milling speed is 120rpm, and the ball-to-material ratio is 4: 1; wherein, the ball milling is stopped after the reciprocating circulation is carried out for 4 times after the ball milling is stopped for 5min when the ball milling is carried out for 15min each time when the ball milling is carried out; finally, the powder for generating the ceramic phase reinforced light high-entropy alloy coating by laser aluminothermic reduction is prepared.
Example 4
This example is a comparative experiment of the above example 1, and as shown in fig. 5, a method for preparing a powder for laser cladding of a light high-entropy alloy coating specifically includes the following steps:
(1) 8.33 wt% of Al powder, 28.67 wt% of Nb powder, 14.77 wt% of Ti powder, 15.72 wt% of V powder, 16.04 wt% of Cr powder were weighed out with an electronic balance having a measurement accuracy of. + -. 0.1 mg; wherein all the powder is spherical powder, the grain diameter of the Al powder is 10-12 mu m, and the grain diameters of the rest powder are 13-52 mu m;
(2) putting all the powder into a ball milling tank, adding 16.46 wt% of absolute ethyl alcohol, fully mixing, and then adding grinding balls to enable the ball-material ratio to be 4:1, wherein the ball milling tank and the grinding balls are made of stainless steel materials; the ball milling can is filled in a star type ball mill for ball milling, the ball milling speed is 120rpm, and the ball milling time is 4 hours; wherein, the ball milling is stopped after the reciprocating circulation is carried out for 8 times after the ball milling is stopped for 5min when the ball milling is carried out for 15min each time when the ball milling is carried out;
(3) drying the ball-milled light high-entropy alloy composite powder in a vacuum drying oven for 8 hours at 70 ℃;
(4) putting the dried light high-entropy alloy composite powder into a planetary ball mill to be crushed for 2 hours, wherein the ball milling speed is 120rpm, and the ball-to-material ratio is 4: 1; wherein, the ball milling is stopped after the ball milling is repeatedly circulated for 4 times after the ball milling is stopped for 5min when the ball milling is stopped for 15min every 15min of positive rotation and then for 15min of negative rotation and 5min of pause and 15min of positive rotation; finally, the powder for laser cladding of the light high-entropy alloy coating is prepared.
As shown in figures 1-4, when the wet milling time is 2-8 h, the nano TiO is 2 Can be well adsorbed on micron-sized powder. Because the grain diameter of the Al powder is smaller than that of other micron-sized powder, and the powder has strong viscosity, the nano TiO powder 2 The particles of the @ Al powder are easily bonded to each other to form a large cluster, as shown in FIG. 2. In addition, as the time of wet milling increases, the surface morphology of some powders changes to varying degrees and the sphericity of the powder decreases. The adsorption effect and the sphericity are considered comprehensively, and the beneficial influence of the adsorption behavior of the nano powder on the preparation of the light high-entropy alloy coating by laser is greater than the influence of the sphericity of the powder to a certain extent. In examples 1 to 3, the two aspects are combined to obtain the optimal powder for generating the ceramic phase reinforced light-weight high-entropy alloy coating by laser aluminothermic reduction. FIG. 5 shows the laser absorption coefficient of the powder, and it can be seen that the nano TiO 2 The laser energy can be better coupled into the powder by adding the silicon nitride powder, which is beneficial to the preparation of the coating.
In summary, 1, the nano-powder has small particle size, large specific surface area, high specific surface energy and good adsorption performance, and can be adsorbed on the surface of micron-sized powder, and the nano-TiO thereof 2 The laser absorption coefficient of the composite powder is larger than that of other simple substance powder, the surface chemical components and the surface roughness of the micron-sized powder are changed when the composite powder is adsorbed on the surface of other micron-sized powder, the light reflection form is more prone to diffuse reflection due to the improvement of the surface roughness, the reflectivity of laser is reduced, the laser absorption coefficient of the composite powder is improved, and the preparation of the light high-entropy alloy coating by laser cladding is facilitated;
2. it is provided withSub, nano TiO 2 The aluminum reduction reaction can be carried out with Al powder, so that the heat input during laser cladding is improved, the temperature field distribution of a laser melting pool is more uniform, and the coating structure is more compact; al produced thereby 2 O 3 The ceramic reinforcing phase is beneficial to improving the high-temperature oxidation resistance of the light high-entropy alloy coating.
In the description herein, references to the description of "one embodiment," "an example," "a specific example" or the like are intended to mean that a particular feature, structure, material, or characteristic described in connection with the embodiment or example is included in at least one embodiment or example of the invention. In this specification, the schematic representations of the terms used above do not necessarily refer to the same embodiment or example. Furthermore, the particular features, structures, materials, or characteristics described may be combined in any suitable manner in any one or more embodiments or examples.
The preferred embodiments of the invention disclosed above are intended to be illustrative only. The preferred embodiments are not intended to be exhaustive or to limit the invention to the precise embodiments disclosed. Obviously, many modifications and variations are possible in light of the above teaching. The embodiments were chosen and described in order to best explain the principles of the invention and the practical application, to thereby enable others skilled in the art to best utilize the invention. The invention is limited only by the claims and their full scope and equivalents.
Claims (5)
1. A preparation method of powder for generating a high-entropy alloy coating by laser aluminothermic reduction is characterized by comprising the following steps:
s1 mixing nano TiO 2 Mixing the powder with Al, Nb, Ti, V and Cr powder, adding absolute ethyl alcohol, and performing ball milling in a planetary ball mill to obtain composite powder;
s2, drying the ball-milled composite powder in a vacuum drying oven under the condition of heat preservation;
and S3, performing ball milling and crushing to obtain the composite powder for generating the ceramic phase reinforced light high-entropy alloy coating by laser aluminothermic reduction.
2. The method for preparing powder for laser aluminothermic reduction to produce high entropy alloy coatings of claim 1, wherein; all the powder in the S1 is spherical powder, the purity is not lower than 99.99%, the mass fraction of the absolute ethyl alcohol is 16.24-16.46 wt%, and the particle size and the content of the powder are shown in the table.
3. A method for preparing powder for generating a high-entropy alloy coating through laser aluminothermic reduction according to claim 1, wherein; the ball milling mode in the S2 is wet milling, the ball milling rotating speed is 120-150 rpm, the ball material ratio is 4:1, and the ball milling time is 2-8 h.
4. The method for preparing powder for laser aluminothermic reduction to produce high entropy alloy coatings of claim 1, wherein; and in the S2, the vacuum drying oven is kept at 70 ℃ for 8-10 h.
5. The method for preparing powder for laser aluminothermic reduction to produce high entropy alloy coatings of claim 1, wherein; and in the S2, the ball grinding time is 2-3 h, the rotating speed is 120-150 rpm, and the ball-material ratio is 4: 1.
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| Publication number | Priority date | Publication date | Assignee | Title |
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