CN114672802A - Preparation method of nano Si modified WC/MoFeCrTiW high-entropy alloy composite cladding layer - Google Patents
Preparation method of nano Si modified WC/MoFeCrTiW high-entropy alloy composite cladding layer Download PDFInfo
- Publication number
- CN114672802A CN114672802A CN202210337861.3A CN202210337861A CN114672802A CN 114672802 A CN114672802 A CN 114672802A CN 202210337861 A CN202210337861 A CN 202210337861A CN 114672802 A CN114672802 A CN 114672802A
- Authority
- CN
- China
- Prior art keywords
- cladding layer
- entropy alloy
- powder
- nano
- laser
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 238000005253 cladding Methods 0.000 title claims abstract description 106
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 68
- 239000000956 alloy Substances 0.000 title claims abstract description 68
- 239000002131 composite material Substances 0.000 title claims abstract description 32
- 238000002360 preparation method Methods 0.000 title claims abstract description 10
- 239000000843 powder Substances 0.000 claims abstract description 50
- 238000004372 laser cladding Methods 0.000 claims abstract description 37
- 238000000576 coating method Methods 0.000 claims abstract description 33
- 239000011248 coating agent Substances 0.000 claims abstract description 32
- 238000000034 method Methods 0.000 claims abstract description 20
- 239000005543 nano-size silicon particle Substances 0.000 claims abstract description 18
- 239000002245 particle Substances 0.000 claims abstract description 13
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 10
- 239000011230 binding agent Substances 0.000 claims abstract description 10
- 239000010959 steel Substances 0.000 claims abstract description 10
- 239000000463 material Substances 0.000 claims abstract description 9
- 238000002156 mixing Methods 0.000 claims abstract description 9
- 230000003014 reinforcing effect Effects 0.000 claims abstract description 4
- 238000001035 drying Methods 0.000 claims description 13
- 239000000203 mixture Substances 0.000 claims description 8
- 229920003086 cellulose ether Polymers 0.000 claims description 7
- 239000000758 substrate Substances 0.000 claims description 7
- 229910052804 chromium Inorganic materials 0.000 claims description 5
- 229910052719 titanium Inorganic materials 0.000 claims description 5
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 4
- 229910052742 iron Inorganic materials 0.000 claims description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims description 4
- 238000003756 stirring Methods 0.000 claims description 4
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 3
- 238000004140 cleaning Methods 0.000 claims description 3
- 238000000227 grinding Methods 0.000 claims description 3
- 239000004570 mortar (masonry) Substances 0.000 claims description 3
- 238000005498 polishing Methods 0.000 claims description 3
- 238000005303 weighing Methods 0.000 claims description 3
- 229910052786 argon Inorganic materials 0.000 claims description 2
- 239000007789 gas Substances 0.000 claims description 2
- 229910052721 tungsten Inorganic materials 0.000 claims description 2
- 238000004519 manufacturing process Methods 0.000 claims 2
- 238000005260 corrosion Methods 0.000 abstract description 40
- 230000007797 corrosion Effects 0.000 abstract description 29
- 229910001567 cementite Inorganic materials 0.000 abstract description 10
- 238000005204 segregation Methods 0.000 abstract description 10
- 230000007547 defect Effects 0.000 abstract description 8
- 239000010410 layer Substances 0.000 description 91
- 239000013078 crystal Substances 0.000 description 13
- 238000005299 abrasion Methods 0.000 description 10
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 8
- 238000009826 distribution Methods 0.000 description 8
- 229910017384 Fe3Si Inorganic materials 0.000 description 6
- 210000001787 dendrite Anatomy 0.000 description 5
- 238000006056 electrooxidation reaction Methods 0.000 description 5
- 238000011056 performance test Methods 0.000 description 5
- 238000012360 testing method Methods 0.000 description 5
- 230000004580 weight loss Effects 0.000 description 5
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 2
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N Titan oxide Chemical compound O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical group [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- QDOXWKRWXJOMAK-UHFFFAOYSA-N dichromium trioxide Chemical compound O=[Cr]O[Cr]=O QDOXWKRWXJOMAK-UHFFFAOYSA-N 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 238000011160 research Methods 0.000 description 2
- 239000011856 silicon-based particle Substances 0.000 description 2
- 239000002344 surface layer Substances 0.000 description 2
- 229910003470 tongbaite Inorganic materials 0.000 description 2
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 description 2
- RZVAJINKPMORJF-UHFFFAOYSA-N Acetaminophen Chemical compound CC(=O)NC1=CC=C(O)C=C1 RZVAJINKPMORJF-UHFFFAOYSA-N 0.000 description 1
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- 229910000599 Cr alloy Inorganic materials 0.000 description 1
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- 241000282414 Homo sapiens Species 0.000 description 1
- 229910001182 Mo alloy Inorganic materials 0.000 description 1
- BPQQTUXANYXVAA-UHFFFAOYSA-N Orthosilicate Chemical compound [O-][Si]([O-])([O-])[O-] BPQQTUXANYXVAA-UHFFFAOYSA-N 0.000 description 1
- 229910000978 Pb alloy Inorganic materials 0.000 description 1
- 229910001069 Ti alloy Inorganic materials 0.000 description 1
- 229910001080 W alloy Inorganic materials 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000000919 ceramic Substances 0.000 description 1
- 229910052681 coesite Inorganic materials 0.000 description 1
- 229910052906 cristobalite Inorganic materials 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000010790 dilution Methods 0.000 description 1
- 239000012895 dilution Substances 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000003292 glue Substances 0.000 description 1
- 238000007542 hardness measurement Methods 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- VJPLIHZPOJDHLB-UHFFFAOYSA-N lead titanium Chemical compound [Ti].[Pb] VJPLIHZPOJDHLB-UHFFFAOYSA-N 0.000 description 1
- 239000011159 matrix material Substances 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
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 235000019353 potassium silicate Nutrition 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000005855 radiation Effects 0.000 description 1
- 239000000377 silicon dioxide Substances 0.000 description 1
- 235000012239 silicon dioxide Nutrition 0.000 description 1
- 239000011863 silicon-based powder Substances 0.000 description 1
- NTHWMYGWWRZVTN-UHFFFAOYSA-N sodium silicate Chemical compound [Na+].[Na+].[O-][Si]([O-])=O NTHWMYGWWRZVTN-UHFFFAOYSA-N 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 229910052682 stishovite Inorganic materials 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 229910052905 tridymite Inorganic materials 0.000 description 1
Classifications
-
- 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
- C23C24/00—Coating starting from inorganic powder
- C23C24/08—Coating starting from inorganic powder by application of heat or pressure and heat
- C23C24/10—Coating starting from inorganic powder by application of heat or pressure and heat with intermediate formation of a liquid phase in the layer
- C23C24/103—Coating with metallic material, i.e. metals or metal alloys, optionally comprising hard particles, e.g. oxides, carbides or nitrides
-
- 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
-
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Other Surface Treatments For Metallic Materials (AREA)
- Powder Metallurgy (AREA)
Abstract
The invention discloses a preparation method of a nano Si modified WC/MoFeCrTiW high-entropy alloy composite cladding layer, which comprises the steps of selecting Q235 steel as a cladding layer base material, selecting MoFeCrTiW high-entropy alloy powder as a cladding layer binder material, selecting spherical WC powder as a reinforcing phase, mixing with the high-entropy alloy powder, carrying out laser cladding in a preset powder feeding mode, prefabricating a nano Si particle coating, and carrying out laser remelting on the nano Si particle coating and the cladding layer. The invention overcomes the defects of air holes, cracks and component segregation generated in the process of cladding the WC/MoFeCrTiW high-entropy alloy cladding layer by laser and the defects of Cr7C3 and Fe3C and the like, improves the structure of the cladding layer, solves the problem that WC particles cannot be uniformly distributed in the cladding layer, obtains few air holes and cracks by modifying nano Si, improves the component segregation phenomenon in the cladding layer, and obtains the cladding layer with high hardness, high wear resistance and high corrosion resistance.
Description
Technical Field
The invention relates to a preparation method of a nano Si modified WC/MoFeCrTiW high-entropy alloy composite cladding layer.
Background
The alloy systems mainly developed by human beings include iron and steel materials mainly containing iron, aluminum alloys mainly containing aluminum, titanium-lead alloys, and the like. The high-entropy alloy is a novel alloy series, and has great scientific research significance and industrial development potential. The mechanical property, the chemical property and the physical property of the high-entropy alloy are greatly improved compared with those of the traditional alloy, such as high strength, high hardness, excellent wear resistance, excellent corrosion resistance and the like. With the demand of people for higher-performance composite coatings, research on high-entropy alloys is also becoming a hot spot. The traditional high-entropy alloy coating often only has certain specific performance, the current coating pursues more comprehensive performance, and the corresponding performance is customized according to different requirements and use environments. Although the MoFeCrTiW high-entropy alloy has higher strength, the structure of the MoFeCrTiW high-entropy alloy contains more intermetallic compounds and coarse dendritic crystals, so that the MoFeCrTiW high-entropy alloy has increased brittleness and lower wear resistance, and cannot be used in severe environments. Because tungsten carbide (WC) ceramic particles have the advantages of high melting point, high hardness, good stability, good wettability with a metal matrix and the like, WC is used as a reinforcing phase of the MoFeCrTiW high-entropy alloy to improve the wear resistance of the MoFeCrTiW high-entropy alloy.
In order to obtain the WC reinforced MoFeCrTiW high-entropy alloy composite cladding layer, a laser cladding method is commonly used. However, laser cladding has short heating time, high heating speed and high cooling speed, WC particles cannot be uniformly distributed in a cladding layer, the strengthening effect of WC cannot be fully exerted, and cracks and pores are generated. In addition, although the hardness and wear resistance of the WC/MoFeCrTiW high-entropy alloy composite cladding layer prepared by laser cladding are improved, the addition of WC particles can generate a Cr7C3 phase and a Fe3C phase, and generate component segregation, so that the corrosion resistance of the coating is further reduced. The laser cladding WC/MoFeCrTiW high-entropy alloy composite cladding layer is composed of dendrites and equiaxed crystals, but the proportion of the dendrites is still high, and the corrosion resistance of the laser cladding WC/MoFeCrTiW high-entropy alloy composite cladding layer is reduced due to the occurrence of dendrite segregation. Due to the defects, the laser cladding WC/MoFeCrTiW high-entropy alloy composite cladding layer has high hardness and high wear resistance, and simultaneously the corrosion resistance is greatly reduced, so that the use of the laser cladding WC/MoFeCrTiW high-entropy alloy composite cladding layer in a severe environment is limited.
Disclosure of Invention
In order to solve the problems, the invention provides a preparation method of a nano Si modified WC/MoFeCrTiW high-entropy alloy composite cladding layer. The invention overcomes the defects of air holes, cracks and component segregation generated in the process of cladding the WC/MoFeCrTiW high-entropy alloy cladding layer by laser and the defects of Cr7C3 and Fe3C and the like, improves the structure of the cladding layer, solves the problem that WC particles cannot be uniformly distributed in the cladding layer, obtains few air holes and cracks by modifying nano Si, improves the component segregation phenomenon in the cladding layer, and obtains the cladding layer with high hardness, high wear resistance and better corrosion resistance.
The invention relates to a preparation method of a nano Si modified WC/MoFeCrTiW high-entropy alloy composite cladding layer, which takes Q235 steel as a cladding layer base material, takes MoFeCrTiW high-entropy alloy powder as a cladding layer binder material, takes spherical WC powder as a reinforcing phase, mixes with the MoFeCrTiW high-entropy alloy powder, carries out laser cladding by adopting a preset powder feeding mode, then prefabricates a nano Si particle coating and carries out laser remelting on the coating and the cladding layer.
The method specifically comprises the following steps:
step 1: pretreatment of
1a, weighing Fe, Mo, Cr, Ti and W high-entropy alloy powder and spherical WC powder according to the proportion, placing the powder in a mortar, grinding the powder for more than 2 hours to uniformly mix the powder, and then drying the powder to remove moisture, wherein the drying temperature is 120 ℃, and the drying time is 2 hours;
1b, polishing, derusting and deburring the surface to be clad of the Q235 steel substrate by using a grinder and metallographic abrasive paper, and then cleaning and drying by using alcohol.
Step 2: laser cladding
Uniformly mixing the pretreated high-entropy alloy powder and spherical WC powder, adding cellulose ether, fully stirring and mixing, presetting the mixture on the surface of a Q235 steel substrate, wherein the preset thickness is 1.2mm, fully drying, carrying out preheating treatment, and carrying out laser cladding to form a cladding layer of the WC composite high-entropy alloy.
And step 3: laser remelting
Uniformly covering the surface of the WC/MoFeCrTiW high-entropy alloy composite cladding layer obtained after laser cladding with a 1.2-1.5mm nano Si particle coating, and then carrying out laser remelting with the laser remelting power of 0.6-0.7Kw and the scanning speed of 3-5 mm/s.
In the step 1, the high-entropy alloy powder comprises the following components in percentage by mass: fe 12-17%, Mo 20-24%, Cr 20-26%, Ti 20-26%, and W12-15%.
In the step 1, the granularity of the spherical WC powder is 300 meshes, and the mass of the spherical WC powder is 30% of the total mass of the high-entropy alloy powder.
In the step 2, the addition mass of the cellulose ether is 30% of the total mass of the high-entropy alloy powder and the spherical WC powder.
In the step 2, in the laser cladding process, the laser power is 1.8kW, the laser scanning speed is 3mm/s, the spot diameter is 3.0mm, the focal length is 140mm, the defocusing amount is +/-5 mm, argon with the purity of 99.9% is adopted for protection in the cladding process, the gas flow is 12-25L/min, and the temperature is naturally cooled to the room temperature.
In the step 3, the nano Si particle coating is obtained by fully stirring and mixing nano Si particles and a binder; wherein the purity of the nano Si particles is 99.9%, and the particle size is 200 meshes; the binder is cellulose ether, and the addition mass of the binder is 30% of the mass of the nano Si particles.
The nano Si coating covered during laser remelting and Fe3C in the WC/MoFeCrTiW high-entropy alloy composite cladding layer react to generate Fe3Si, because the potential of Fe3Si is low, the Fe3Si phase is firstly dissolved and corroded as an anode during corrosion reaction, the high-activity Fe element is dissolved preferentially, the inactive Si element is enriched, the potential of the Fe3Si phase is promoted to be shifted positively and converted into a cathode, so that the corrosion current is reduced, the added nano Si forms SiC gradient distribution in the cladding layer, and the corrosion resistance is improved while the hardness and the wear resistance are maintained.
The scanning speed adopted in the preparation of the coating is 3-5mm/s, and the performance of the cladding layer after laser remelting is optimal when the scanning speed is 5 mm/s. When the scanning speed is low, the energy absorbed by the coating is large, unnecessary loss is caused, and the performance is reduced; when the scanning speed is too high, the cladding layer and the surface of the base material cannot form good metallurgical bonding, so that the performance of the cladding layer is rapidly reduced.
The laser remelting power adopted in the preparation of the cladding layer is 0.6-0.7KW, and if the laser power is too low, the added Si cannot be fully combined with the cladding layer, so that the quality of the cladding layer is reduced; when the laser power is higher, the depth of a remelted layer is larger, the dilution rate of a cladding layer is high, the gradient distribution of structures such as reaction generated phases, equiaxed crystals and the like cannot be ensured, elements of the cladding layer are burnt, and the quality of the cladding layer is reduced; experiments prove that the cladding layer with uniform components and excellent performance can be obtained when the laser remelting power is 0.7 KW.
Through tests, the hardness of the cladding layer prepared by the invention is at least improved by 20 percent compared with that of a laser cladding WC/MoFeCrTiW high-entropy alloy cladding layer, and the highest hardness is up to 825HV 0.2; the wear resistance is improved by 30 percent, and the wear rate is as low as 7.35 multiplied by 10-7g/s is less than or equal to; the corrosion resistance is improved by more than two times, and the self-corrosion potential is improved to EcorrHigher than-378.622 mV, from corrosion current density reduction to Icorr3.741 μ a or less.
The invention has the beneficial effects that:
1. the shape of the WC powder used by the cladding layer is spherical, the contact area of the spherical WC particles in the process of solidification of a molten pool is large, the growth of crystal grains can be hindered, the crystal grains are refined, the performance of the cladding layer is improved, and the corrosion resistance of the cladding layer can be improved by the spherical WC particles.
2. Because 20-26% of Cr and 20-26% of Ti are added into the components of the high-entropy alloy powder, more TiC and Cr3C2 phases are generated in the laser cladding process, and the hardness and the wear resistance of the high-entropy alloy powder are improved; and higher Cr and Ti can form Cr2O3 and TiO2 passive films in a corrosive environment, so that the corrosion can be effectively prevented from continuing, the corrosion rate is slowed down, and the corrosion resistance of the steel is improved.
3. The binder adopted in the preparation of the nano Si particle covering layer is oxygen-containing cellulose ether, so that the peeling between the coating and the substrate caused by the expansion of silicate glue and water glass is avoided, the oxygen-containing cellulose ether can also ensure the good absorption rate of the coating to radiation laser, and the quality of the cladding layer is improved.
4. The nanometer Si coating laser remelting generates a large amount of SiC which is in gradient distribution along the depth direction as a heterogeneous nucleation core to promote the formation of equiaxed crystals, the equiaxed crystal proportion is also in gradient distribution along the depth direction under the control of remelting parameters such as laser power, the tissue distribution is favorable for the high hardness, high wear resistance and corrosion resistance of a surface layer and a subsurface layer, the sinking of WC particles can be prevented, and the distribution of the WC particles in a cladding layer is improved, so that the hardness and wear resistance of the cladding layer are further improved. The hardness of the coating is improved by 168HV0.2 compared with the coating without secondary remelting, and the wear resistance is improved by 30 percent.
5. The nano Si coating is remelted for the second time by laser, so that bubbles and oxide impurities in a cladding layer obtained by the first laser cladding are further removed, the defects of inclusions, air holes and the like of the cladding layer are obviously reduced, the components of the cladding layer are more uniform, the component segregation phenomenon is reduced, and the micro corrosion primary battery is difficult to form; and Si added in the laser remelting process can also react with Fe3C to generate SiC and Fe3Si intermediate phase when the cladding layer is remelted, promote the decomposition of Cr7C3, react to generate Cr3C2 and SiC, reduce the content of Fe3C, Cr7C3 and the like, and improve the corrosion resistance by two times compared with the coating without secondary remelting.
6. Si particles adopted in the laser remelting process are in a nanometer size, the diffusion speed of the Si particles into a laser cladding layer is high during remelting, gradient distribution is formed in the cladding layer, and because Si can form an SiO2 passive film in a corrosive environment, the closer to the surface layer of the cladding layer, the more the Si content is, the better the corrosion resistance is; compared with micron Si, the added nano Si is easier to enter a crystal structure, the density of the crystal structure is improved, the proportion of dendrites is greatly reduced, the formation of equiaxed crystals is promoted, and the dendrite segregation is reduced, so that the corrosion resistance is improved.
7. In the laser remelting process, Si powder in the pre-coated Si coating reacts with Fe3C in the laser cladding layer to generate a corrosion-resistant phase Fe3Si, so that the corrosion potential of the cladding layer is increased, the corrosion current density is reduced, the corrosion tendency is reduced, the corrosion rate is slowed down, the corrosion resistance of the cladding layer is further improved, and the cladding layer has high strength, high wear resistance and excellent corrosion resistance.
Detailed Description
Example 1:
step 1: pretreatment of materials
The high-entropy alloy powder comprises the following components in percentage by mass: 13% of Fe, 22% of Mo, 26% of Cr, 26% of Ti and 13% of W, weighing the required Fe, Mo, Cr, Ti and W alloy powder and spherical WC (30%) powder, putting the weighed alloy powder into a mortar, grinding for more than 2 hours to uniformly mix the alloy powder and the spherical WC powder, drying the uniformly mixed alloy powder and the spherical WC powder to remove moisture, wherein the drying temperature is 60-100 ℃, and the drying time is 3-5 hours;
and (3) polishing, derusting and deburring the surface to be clad of the Q235 steel substrate by using a grinder and metallographic abrasive paper, and then cleaning and drying by using alcohol.
Step 2: laser cladding
Uniformly mixing the pretreated alloy powder and spherical WC powder, presetting the mixture on the surface of a treated substrate, wherein the preset thickness is 1.2mm, fully drying, carrying out preheating treatment, carrying out laser cladding, and naturally cooling to room temperature to form a cladding layer of the WC composite high-entropy alloy.
And step 3: laser remelting
And carrying out laser remelting on the WC/MoFeCrTiW high-entropy alloy composite cladding layer obtained by laser cladding, wherein nano Si particles with the thickness of 1.2mm are uniformly covered on the surface of the cladding layer during remelting, the laser remelting power is 0.7Kw, and the scanning speed is 3 mm/s.
Examples 2-5 used the same procedure as in example 1, except that the parameters were selected differently.
| Examples | Thickness of Si coating applied during reflow | Scanning speed |
| 2 | 1.35mm | 3mm/s |
| 3 | 1.5mm | 3mm/s |
| 4 | 1.2mm | 4mm/s |
| 5 | 1.2mm | 5mm/s |
The observation of the embodiment 1 shows that the equiaxed crystal structure in the cladding layer structure is increased, the average grain size is smaller than that of the common laser cladding WC/MoFeCrTiW high-entropy alloy composite cladding layer, the defects such as bubbles and inclusions in the cladding layer are reduced, the composition segregation phenomenon is improved, the quantity of Fe3C and Cr7C3 phases is obviously reduced, and the WC particles are uniformly distributed in the cladding layer. The average hardness of the coating of example 1 was 787HV0.2 by the hardness test. When the rotating speed is 200r/min, the load is 200N and the abrasion time is 1h, the weight loss of the cladding layer subjected to laser remelting is 0.34 times of that of the common laser cladding WC/MoFeCrTiW high-entropy alloy composite cladding layer, and the abrasion rate is 6.89 multiplied by 10-7g/s. Through electrochemical corrosion performance tests, the self-corrosion potential of the cladding layer is increased by 89% compared with that of the common laser cladding WC/MoFeCrTiW high-entropy alloy composite cladding layer, and Ecorr-346.756 mV; the self-corrosion current density is reduced by 92 percent, Icorr＝3.435μA。
Example 2 the thickness of the nano Si cladding layer increased upon laser remelting compared to example 1. Observation of the structure of example 2 revealed that the equiaxed crystal structure in the cladding layer was further increased, the average grain size was reduced, no significant bubble and composition segregation phenomena were observed, the WC particles were uniformly distributed, and the observed Fe3C and Cr7C3 phases of the cladding layer were reduced, indicating that the Fe3C and Cr7C3 phases were reduced with the increase in Si content. The average hardness of the coating of example 2 was 812HV0.2 by the hardness test. At a rotational speed of200r/min, 200N load and 1h abrasion time, the weight loss of the cladding layer subjected to laser remelting is 0.28 times of that of the common laser cladding WC/MoFeCrTiW high-entropy alloy composite cladding layer, and the abrasion rate is 6.32 multiplied by 10-7g/s. Through electrochemical corrosion performance tests, the self-corrosion potential of the cladding layer is increased by 92 percent compared with that of the common laser cladding WC/MoFeCrTiW high-entropy alloy composite cladding layer, and Ecorr-315.231 mV; the self-corrosion current density is reduced by 94 percent, Icorr＝3.257μA。
Example 3 increases the thickness of the nano Si cladding layer upon laser remelting compared to example 2. The crack of the cladding layer can be seen by observing the structure. The average hardness of the coating of example 3 was 795HV0.2 as measured by the hardness test. When the rotating speed is 200r/min, the load is 200N and the abrasion time is 1h, the weight loss of the cladding layer subjected to laser remelting is 0.31 time of that of the common laser cladding WC/MoFeCrTiW high-entropy alloy composite cladding layer, and the abrasion rate is 6.64 multiplied by 10-7g/s. Through electrochemical corrosion performance tests, the self-corrosion potential of the cladding layer is increased by 87% compared with that of the common laser cladding WC/MoFeCrTiW high-entropy alloy composite cladding layer, and Ecorr-358.465 mV; the self-corrosion current density is reduced by 89 percent, Icorr3.954 μ a. This indicates that as the Si content increases, the improvement in the properties of the cladding layer is not significant, and the performance is degraded due to the occurrence of cracks, and the corrosion resistance is degraded due to excessive precipitation of the second phase.
The scanning speed in the embodiment 4 is 4mm/s, obvious defects such as cracks, air holes and the like do not appear in the cladding layer, the smoothness of the surface of the coating is improved, the element distribution is more uniform, and the crystal grains are refined. The average hardness of the coating of example 4 was 798HV0.2 by hardness testing. When the rotating speed is 200r/min, the load is 200N and the abrasion time is 1h, the weight loss of the cladding layer subjected to laser remelting is 0.30 times of that of the common laser cladding WC/MoFeCrTiW high-entropy alloy composite cladding layer, and the abrasion rate is 6.52 multiplied by 10-7g/s. Through electrochemical corrosion performance tests, the self-corrosion potential of the cladding layer is increased by 95 percent compared with that of the common laser cladding WC/MoFeCrTiW high-entropy alloy composite cladding layer, and Ecorr-284.743 mV; the self-corrosion current density is reduced by 96 percent, Icorr＝3.015μA。
The scan speed in example 5 was 5mm/s and the microstructure observed for the cladding layer was reduced from the average grain size of example 4. The average hardness of the coating of example 5 was 825HV0.2 by the hardness test. When the rotating speed is 200r/min, the load is 200N and the abrasion time is 1h, the weight loss of the cladding layer subjected to laser remelting is 0.29 times of that of the common laser cladding WC/MoFeCrTiW high-entropy alloy composite cladding layer, and the abrasion rate is 6.39 multiplied by 10-7g/s. Through electrochemical corrosion performance tests, the self-corrosion potential of the cladding layer is increased by 97 percent compared with the common laser cladding WC/MoFeCrTiW high-entropy alloy composite cladding layer,
Ecorr-268.359 mV; the self-corrosion current density is reduced by 98 percent, Icorr2.854 μ a. Further improving the corrosion resistance of the cladding layer.
Claims (8)
1. A preparation method of a nano Si modified WC/MoFeCrTiW high-entropy alloy composite cladding layer is characterized by comprising the following steps:
the method comprises the steps of taking Q235 steel as a cladding layer base material, taking MoFeCrTiW high-entropy alloy powder as a cladding layer binder material, taking spherical WC powder as a reinforcing phase, mixing the spherical WC powder with the MoFeCrTiW high-entropy alloy powder, carrying out laser cladding in a preset powder feeding mode, prefabricating a nano Si particle coating, and carrying out laser remelting on the nano Si particle coating and the cladding layer.
2. The method of claim 1, comprising the steps of:
step 1: pretreatment of
1a, weighing Fe, Mo, Cr, Ti and W high-entropy alloy powder and spherical WC powder according to the proportion, placing the powder in a mortar for grinding to uniformly mix the powder, and then drying to remove moisture;
1b, polishing, derusting and deburring the surface to be clad of the Q235 steel substrate by using a grinder and metallographic abrasive paper, and then cleaning and drying by using alcohol;
step 2: laser cladding
Uniformly mixing the pretreated high-entropy alloy powder and spherical WC powder, adding cellulose ether, fully stirring and mixing, presetting the mixture on the surface of a Q235 steel substrate, wherein the preset thickness is 1.2mm, fully drying, carrying out preheating treatment, and carrying out laser cladding to form a cladding layer of the WC composite high-entropy alloy;
and step 3: laser remelting
Uniformly covering the surface of the WC/MoFeCrTiW high-entropy alloy composite cladding layer obtained after laser cladding with a nano Si particle coating, and then carrying out laser remelting with the laser remelting power of 0.6-0.7Kw and the scanning speed of 3-5 mm/s.
3. The method of claim 2, wherein:
in the step 1, the high-entropy alloy powder comprises the following components in percentage by mass: fe 12-17%, Mo 20-24%, Cr 20-26%, Ti 20-26%, and W12-15%.
4. The method of claim 2, wherein:
in the step 1, the granularity of the spherical WC powder is 300 meshes, and the mass of the spherical WC powder is 30% of the total mass of the high-entropy alloy powder.
5. The method of claim 2, wherein:
in the step 2, in the laser cladding process, the laser power is 1.8kW, the laser scanning speed is 3mm/s, the spot diameter is 3.0mm, the focal length is 140mm, the defocusing amount is +/-5 mm, argon with the purity of 99.9% is adopted for protection in the cladding process, the gas flow is 12-25L/min, and the temperature is naturally cooled to the room temperature.
6. The method of claim 2, wherein:
in the step 3, the nano Si particle coating is obtained by fully stirring and mixing nano Si particles and a binder.
7. The method of manufacturing according to claim 6, characterized in that:
the purity of the nano Si particles is 99.9%, and the particle size is 200 meshes; the binder is cellulose ether, and the addition mass of the binder is 30% of the mass of the nano Si particles.
8. The production method according to claim 2, 6 or 7, characterized in that:
the thickness of the nano Si particle coating is controlled to be 1.2-1.5 mm.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210337861.3A CN114672802B (en) | 2022-03-31 | 2022-03-31 | Preparation method of nano Si modified WC/MoFeCrTiW high-entropy alloy composite cladding layer |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210337861.3A CN114672802B (en) | 2022-03-31 | 2022-03-31 | Preparation method of nano Si modified WC/MoFeCrTiW high-entropy alloy composite cladding layer |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN114672802A true CN114672802A (en) | 2022-06-28 |
| CN114672802B CN114672802B (en) | 2023-11-03 |
Family
ID=82076842
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202210337861.3A Active CN114672802B (en) | 2022-03-31 | 2022-03-31 | Preparation method of nano Si modified WC/MoFeCrTiW high-entropy alloy composite cladding layer |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN114672802B (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115338410A (en) * | 2022-09-19 | 2022-11-15 | 江苏大学 | High-entropy alloy and aluminum alloy composite material with high wear resistance and preparation method thereof |
| CN115449790A (en) * | 2022-10-14 | 2022-12-09 | 长沙理工大学 | Wear-resistant corrosion-resistant high-entropy alloy cladding layer for propeller remanufacturing and preparation method |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20110200838A1 (en) * | 2010-02-18 | 2011-08-18 | Clover Industries, Inc. | Laser clad metal matrix composite compositions and methods |
| CN103305843A (en) * | 2013-07-09 | 2013-09-18 | 铜陵学院 | Embossed laser beam implementation method and device for reducing cracks on cladding layer |
| CN108866544A (en) * | 2018-07-20 | 2018-11-23 | 合肥工业大学 | A kind of WC enhancing Fe base coating and preparation method thereof |
| CN110331398A (en) * | 2019-07-22 | 2019-10-15 | 中南大学 | A kind of composite coating and its preparation method and application of the compound bulky grain tungsten carbide of high-entropy alloy |
| CN110438487A (en) * | 2019-07-16 | 2019-11-12 | 华电电力科学研究院有限公司 | Wear-resistant corrosion-resistant laser cladding layer of a kind of micro-nano granules enhancing and preparation method thereof |
| CN112680690A (en) * | 2020-12-18 | 2021-04-20 | 安徽省特种设备检测院 | Preparation method of nano beta-SiC modified WC/Fe-based composite cladding layer |
-
2022
- 2022-03-31 CN CN202210337861.3A patent/CN114672802B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20110200838A1 (en) * | 2010-02-18 | 2011-08-18 | Clover Industries, Inc. | Laser clad metal matrix composite compositions and methods |
| CN103305843A (en) * | 2013-07-09 | 2013-09-18 | 铜陵学院 | Embossed laser beam implementation method and device for reducing cracks on cladding layer |
| CN108866544A (en) * | 2018-07-20 | 2018-11-23 | 合肥工业大学 | A kind of WC enhancing Fe base coating and preparation method thereof |
| CN110438487A (en) * | 2019-07-16 | 2019-11-12 | 华电电力科学研究院有限公司 | Wear-resistant corrosion-resistant laser cladding layer of a kind of micro-nano granules enhancing and preparation method thereof |
| CN110331398A (en) * | 2019-07-22 | 2019-10-15 | 中南大学 | A kind of composite coating and its preparation method and application of the compound bulky grain tungsten carbide of high-entropy alloy |
| CN112680690A (en) * | 2020-12-18 | 2021-04-20 | 安徽省特种设备检测院 | Preparation method of nano beta-SiC modified WC/Fe-based composite cladding layer |
Non-Patent Citations (1)
| Title |
|---|
| 陈磊: "《硬质相WC和TiC对激光熔覆高熵合金MoFeCrTiW涂层组织与性能的影响》", 《中国优秀硕士学位论文全文数据库 工程科技Ⅰ辑》, pages 1 * |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115338410A (en) * | 2022-09-19 | 2022-11-15 | 江苏大学 | High-entropy alloy and aluminum alloy composite material with high wear resistance and preparation method thereof |
| CN115338410B (en) * | 2022-09-19 | 2024-01-26 | 江苏大学 | High-entropy alloy and aluminum alloy composite material with high wear resistance and preparation method thereof |
| CN115449790A (en) * | 2022-10-14 | 2022-12-09 | 长沙理工大学 | Wear-resistant corrosion-resistant high-entropy alloy cladding layer for propeller remanufacturing and preparation method |
| CN115449790B (en) * | 2022-10-14 | 2024-01-19 | 长沙理工大学 | Wear-resistant corrosion-resistant high-entropy alloy cladding layer for remanufacturing of propeller and preparation method |
Also Published As
| Publication number | Publication date |
|---|---|
| CN114672802B (en) | 2023-11-03 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN114672802B (en) | Preparation method of nano Si modified WC/MoFeCrTiW high-entropy alloy composite cladding layer | |
| CN105112909B (en) | One kind addition CeO2Iron-based Cr3C2Laser cladding coating and preparation method thereof | |
| CN109763125B (en) | High-entropy alloy coating resistant to high-temperature abrasion and preparation process and application thereof | |
| Wang et al. | Effect of Ni-coated WC reinforced particles on microstructure and mechanical properties of laser cladding Fe-Co duplex coating | |
| Min et al. | Microstructure, microhardness and corrosion resistance of laser cladding Ni–WC coating on AlSi5Cu1Mg alloy | |
| CN101144159A (en) | Method for preparing nano/submicron TiB-TiC enhanced titanium-base composite material (TiB+TiC)/Ti | |
| CN108315733A (en) | Powder and preparation method used in a kind of laser melting coating aluminium bronze gradient coating | |
| CN112063951A (en) | Magnesium-aluminum alloy surface laser cladding self-lubricating coating and construction method thereof | |
| CN112779532A (en) | Method for preparing zirconium-based amorphous/nanocrystalline composite coating on surface of zirconium alloy | |
| CN110358943A (en) | A kind of alterant and carbon nanomaterial coordinate system for aluminum matrix composite method | |
| CN112708805A (en) | Aluminum alloy mixed powder, method for improving density of aluminum alloy product and product | |
| CN111020557B (en) | Ceramic-based buffer thermal insulation layer assisted magnesium alloy surface laser cladding composite coating and preparation method thereof | |
| Zhang et al. | Effect of Er on the characteristics of an oxide coating prepared by micro-arc oxidation on a 7075 aluminum alloy | |
| CN112626515B (en) | Method for improving performance of Inconel625 nickel-based powder laser cladding layer | |
| Saini et al. | Microstructural, mechanical and machining studies of Al-4032 alloy based hybrid composite | |
| CN1600891A (en) | Composite material layer melted and coated on surface of titanium alloy through laser | |
| CN112680690A (en) | Preparation method of nano beta-SiC modified WC/Fe-based composite cladding layer | |
| CN115283693B (en) | Preparation method of nickel-based composite coating with excellent wear resistance and high hardness | |
| CN110819980B (en) | In situ generation of ZrB2ZrC-based cladding material, composite coating and preparation method | |
| CN114250496A (en) | Composite metal material with stable mechanical property | |
| Liu et al. | Study on Melting–Precipitation Evolution of WC in Ni/WC-12Co Coating during Laser Cladding and Tribological Properties | |
| Gangadharappa et al. | Corrosion behavior of Al6061 hybrid composites reinforced with red mud particles and E-glass fiber | |
| CN110863196B (en) | AlSi/h-BN modified cladding material, metal-based composite coating and preparation method thereof | |
| CN111020559B (en) | Titanium alloy surface high-temperature-resistant self-lubricating coating and preparation method thereof | |
| Zhang et al. | Al-WC composite coating on AZ91D Mg alloy by low power pulsed laser cladding. |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |