NL2030063B1 - High-entropy alloy coating layer and preparation method thereof - Google Patents
High-entropy alloy coating layer and preparation method thereof Download PDFInfo
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- 239000000956 alloy Substances 0.000 title claims abstract description 64
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 59
- 239000011247 coating layer Substances 0.000 title claims abstract description 17
- 238000002360 preparation method Methods 0.000 title abstract description 11
- 239000010410 layer Substances 0.000 claims abstract description 51
- 238000005253 cladding Methods 0.000 claims abstract description 38
- 239000000843 powder Substances 0.000 claims abstract description 24
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 21
- 229910052742 iron Inorganic materials 0.000 claims abstract description 20
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 20
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 17
- 229910052751 metal Inorganic materials 0.000 claims abstract description 11
- 239000002184 metal Substances 0.000 claims abstract description 11
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims abstract description 9
- 229910052796 boron Inorganic materials 0.000 claims abstract description 9
- 238000000227 grinding Methods 0.000 claims abstract description 8
- 238000002156 mixing Methods 0.000 claims abstract description 3
- 238000000034 method Methods 0.000 claims description 16
- 229910000831 Steel Inorganic materials 0.000 claims description 12
- 239000000463 material Substances 0.000 claims description 12
- 239000010959 steel Substances 0.000 claims description 12
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 10
- 239000007789 gas Substances 0.000 claims description 10
- 239000011248 coating agent Substances 0.000 claims description 6
- 238000000576 coating method Methods 0.000 claims description 6
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 5
- 229910052786 argon Inorganic materials 0.000 claims description 5
- 230000001681 protective effect Effects 0.000 claims description 5
- 238000005259 measurement Methods 0.000 claims description 3
- 239000002245 particle Substances 0.000 claims description 2
- 238000005303 weighing Methods 0.000 claims description 2
- 238000004506 ultrasonic cleaning Methods 0.000 claims 1
- 238000004372 laser cladding Methods 0.000 abstract description 22
- 238000012986 modification Methods 0.000 abstract description 2
- 230000004048 modification Effects 0.000 abstract description 2
- 238000003754 machining Methods 0.000 abstract 1
- 238000007254 oxidation reaction Methods 0.000 abstract 1
- 239000011651 chromium Substances 0.000 description 17
- 235000019589 hardness Nutrition 0.000 description 14
- 238000002441 X-ray diffraction Methods 0.000 description 7
- 230000000694 effects Effects 0.000 description 7
- 238000010586 diagram Methods 0.000 description 5
- 230000009286 beneficial effect Effects 0.000 description 4
- 238000007751 thermal spraying Methods 0.000 description 4
- 230000008569 process Effects 0.000 description 3
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 210000001787 dendrite Anatomy 0.000 description 2
- 238000009792 diffusion process Methods 0.000 description 2
- 238000010790 dilution Methods 0.000 description 2
- 239000012895 dilution Substances 0.000 description 2
- 238000009713 electroplating Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 238000005551 mechanical alloying Methods 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000001228 spectrum Methods 0.000 description 2
- 238000004544 sputter deposition Methods 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 238000003723 Smelting Methods 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 235000019628 coolness Nutrition 0.000 description 1
- 230000003111 delayed effect Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 229910001325 element alloy Inorganic materials 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 238000012827 research and development Methods 0.000 description 1
- 230000000452 restraining effect Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 238000004611 spectroscopical analysis Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000004381 surface treatment Methods 0.000 description 1
- 239000010409 thin film Substances 0.000 description 1
- 230000003245 working effect Effects 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
- C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process
-
- 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
- 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
-
- 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
- C23C24/106—Coating with metal alloys or metal elements only
-
- 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
- C23C26/00—Coating not provided for in groups C23C2/00 - C23C24/00
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- 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)
Abstract
The present invention discloses a high—entropy alloy coating layer and a preparation method thereof, and belongs to the technical field of laser surface modification. The high—entropy alloy powder of the present invention is prepared from Co, Cr, Fe, Mn, Ni, and ferroboron powder, wherein a mole ratio of Co, Cr, Fe, Mn, Ni, and boron is l:l:l:l:l:0.8. The preparation method includes: uniformly mixing Co, Cr, Fe, Mn, Mi, and ferroboron metal powder according to ratios, performing vacuum ball grinding for 3 h or longer time to obtain CoCrFeMnNiBO.8 high—entropy alloy powder; presetting the CoCrFeMnNiBO.8 high—entropy alloy powder on a surface of the pretreated base body to form a prefabricated layer; and performing laser cladding machining to obtain a high—entropy alloy cladding layer. The cladding layer obtained by the laser cladding in the present invention has a good macroscopic feature, is well metallurgically bonded with the base body, and has the characteristics of high hardness, high high—temperature— oxidization resistance, and the like.
Description
P861/NLpd
HIGH-ENTROPY ALLOY COATING LAYER AND PREPARATION METHOD THEREOF
The present invention relates to a high-entropy alloy coating layer and a preparation method thereof, and belongs to the field of laser surface modification for H13 steel.
Laser cladding is a new application of laser in the technical field of surfaces. Compared with other treatment technologies, la- ser cladding used to treat a surface has many unique advantages.
For example, the chemical uniformity of a structure formed after laser melting is extremely high, and crystalline grains are very fine, thus strengthening the alloy and greatly improving the wear resistance. Due to a low thermal input, a workpiece deforms a lit- tle, and the bonding strength of a coating layer and a base body is high. The thickness of the coating layer is adjustable, which has a little thermal impact on the base body. Therefore, in the field of surface treatment, research and development activities for laser cladding are quite active.
Different from traditional materials which contains one prin- cipal element and a few of auxiliary elements, high-entropy alloy is a newly developed multi-principal-element alloy. Generally, the number of principal elements of the high-entropy alloy is n25, and the content of each metal element is between 5% and 35%. Novel al- loy is configured by this kind of elements according to an equal atomic ratio or a ratio close to the equal atomic ratio. Its high entropy value can enhance the mutual dissolution between elements, thus restraining generation of a complex phase and a large number of intermetallic compounds. Furthermore, the performance of the high-entropy alloy is determined by the combined action of the various principal elements.
The current preparation methods for the high-entropy alloy include: vacuum arc smelting, mechanical alloying, sputtering, thermal spraying, and laser cladding. The vacuum arc melting meth-
od requires simple equipment. However, due to a non-uniform cool- ing rate, relatively large crystalline grains may appear in some areas of a casting, a structure is crystallized in a fixed direc- tion, and components are difficultly mixed uniformly. A product prepared by the mechanical alloying method is powered and needs to be treated in the later stage, so as to further consolidate it in- to a block sample. The process is relatively cumbersome and com- plicated, and the production cycle is long. The thickness of a high-entropy alloy thin film prepared by the sputtering method and the thermal spraying method is relatively small, generally in the order of micrometers, which is more restrictive in practical ap- plications.
As a perforated piercing head, H13 steel is one of the most consumed key materials in the production of steel pipes. In the process of pipe piercing, H13 steel is simultaneously subjected to high temperature, high pressure, violent friction, rapid cooling, and rapid heating, and the working conditions are extremely harsh.
When the wear size reaches 1 mm or more, a piercing needle will be scrapped, bringing huge loss to an enterprise. However, the H13 steel has relatively low hardness (about HV300) and relatively poor wear resistance. Although the chromium electroplating method and the thermal spraying method can improve the wear resistance of the H13 steel, the chromium electroplating method has the disad- vantage of a thin coating layer, and the thermal spraying method has the disadvantage of a low bonding force between a coating lay- er and a base body. Therefore, these methods cannot meet the work- ing requirements under harsh conditions. For this purpose, the present invention adopts the laser cladding to prepare a high- entropy alloy coating layer on the surface of the H13 steel.
The present invention aims to provide a CoCrFeMnNiB 0.8 high- entropy alloy coating layer which is prepared from Co, Cr, Fe, Mn,
Ni, and ferroboron metal powder. A mole ratio of Co, Cr, Fe, Mn,
Ni, and boron is 1:1:1:1:1:0.8.
Another objective of the present invention is to provide a preparation method for the CoCrFeMnNiB 0.8 high-entropy alloy coating layer. In the method, a high-entropy alloy material is preset on a surface of a base body, and the high-entropy alloy ma- terial and the surface of the base body are simultaneously melted via laser cladding and are rapidly solidified into a high-entropy alloy coating layer that has a low dilution rate, is in metallur- gical bonding with the base body, and has a low diffusion rate and relatively weak segregation of principal elements of the high- entropy alloy. The method specifically includes the following steps: {1) grinding a base material to remove an oxide layer, and ultrasonically cleaning the base material with alcohol; (2) weighing Co, Cr, Fe, Mn, Ni, and ferroboron metal powder according to ratios, uniformly mixing the metal powder, andper- forming vacuum ball grinding for 3 h or more to obtain CoCrFeMnNiB 0.8 high-entropy alloy powder having a particle size of 150 to 300 meshes; and (3) presetting the CoCrFeMnNiB 0.8 high-entropy alloy powder prepared at the step (2) on a surface of the pretreated base body to form a prefabricated layer, placing the prefabricated layer at 60-100°C for constant-temperature treatment for 6 to 10 h, and performing laser cladding to obtain the high-entropy alloy clad- ding layer.
Preferably, the pretreated base body at the step (1) is H13 steel (4Cr5MoSiVl).
Preferably, the thickness of the prefabricated layer at the step (3) of the present invention is 0.5-1.0 mm.
Preferably, parameters of the laser cladding in the present invention: the laser power of the laser cladding is 3700-4200 W, the scanning speed is 350-500 mm/min, the spot diameter is 3.0-5.0 mm, and the defocusing amount is 15-30 mm, the protective gas is argon, and the gas flow rate is 6-10 L/min.
The purities of the raw materials used in the present inven- tion are all greater than or equal to 99.9%.
The principle of the present invention: the design of high- entropy alloy is mainly based on five characteristics of the high- entropy alloy: high-entropy effect in thermodynamics; delayed dif- fusion effect in kinetics; lattice distortion effect in structure;
“cocktail” effect in performance; and high structural stability.
The high-entropy alloy materials Co, Cr, Fe, Mn, and Ni used in the present invention are beneficial to form a single-phase FCC structure and are beneficial to improve the strength, hardness and wear resistance of the alloy.
On the basis of Co, Cr, Fe, Mn, and Ni, an appropriate amount of boron element (that is added in the form of ferroboron). The boron element has a strong slagging effect in the laser cladding process, which is beneficial to enhance the metallurgical bonding between the cladding layer and the base body and improve the clad- ding effect. In addition, the boron element can improve the high- temperature compressibility and wear resistance of the alloy.
The present invention has the beneficial effects. (1) The CoCrFeMnNiB 0.8 high-entropy alloy material in the present invention is metallurgically bonded with the base body through the laser cladding, so that the bonding strength of the base body and the cladding layer is greatly improved. Furthermore, the base body has a small thermal deformation, the dilution rate is low, and the scrap rate of parts is also relatively low. (2) For the CoCrFeMnNiB 0.8 high-entropy alloy material in the present invention, different components are regulated on pur- pose in order to obtain expected performance to face different working conditions. (3) The cladding layer formed by performing the laser clad- ding on the CoCrFeMnNiB 0.8 high-entropy alloy material of the present invention contains dendrites with a uniform organizational structure, and the cladding layer has high hardness. (4) By the adoption of the laser cladding method, the present invention has the characteristics of high preparation efficiency (fast heating and fast solidification). The prepared coating layer has an adjustable thickness that can reach the millimeter level, and instruments are relatively easy to operate.
FIG. 1 is a diagram of a high-entropy alloy cladding organi- zation of Embodiment 1;
FIG. 2 is a diagram of a high-entropy alloy cladding organi-
zation of Embodiment 1;
FIG. 3 is an X-ray diffraction (XRD) spectrogram of a high- entropy alloy cladding layer of Embodiment 1;
FIG. 4 is a diagram of a high-entropy alloy cladding organi- 5 zation of Embodiment 1; and
FIG. 5 is a hardness comparison diagram of a high-entropy al- loy cladding layer of Embodiment 1.
The present invention is further described in detail below in combination with the specific implementation modes. However, the protection scope of the present invention is not limited to the contents.
Chemical components of the base body material H13 steel (4Cr5MoSivVl) in the embodiment of the present invention are as shown in the following table:
Mass frac- | 0.32- 4.75 1.1 oLa- 5.8 ¢.2-
Embodiment 1
A preparation method for a CoCrFeMnNiB 0.8 high-entropy alloy coating layer specifically includes the following steps. (1) A base material is ground to remove an oxide layer and then is ultrasonically cleaned with alcohol. (2) Weighed Co, Cr, Fe, Mn, Ni, and ferroboron metal powder are uniformly mixed according to a mole ratio of the Co, Cr, Fe,
Mn, Ni, and boron of 1:1:1:1:1:0.8 and subjected to vacuum ball grinding for 3 h or longer time to obtain CoCrFeMnNiB 0.8 high- entropy alloy powder. {3) The CoCrFeMnNiB 0.8 high-entropy alloy powder of the step (2) is placed on a surface of the pretreated base body to form a prefabricated layer; the prefabricated layer is then placed at 80°C for constant-temperature treatment for 8 h; and laser clad- ding is performed to obtain a high-entropy alloy cladding layer.
The laser power of the laser cladding is 4000 W, the scanning speed is 450 mm/min, the spot diameter is 4.0 mm, the defocusing amount is 20 mm, the protective gas is argon, and the gas flow is 8 L/min.
In this example, the high-entropy alloy cladding layer after the laser cladding was polished with high-magnification sandpaper to meet the metallographic requirements and photographed and ob- served with an SEM. Structural diagrams obtained are shown in FIG. 1 and FIG. 2. It can be seen from FIG. 1 and FIG. 2 that the clad- ding layer and the base body are well bonded, and the cladding layer has a dense structure without an obvious hole defect.
An X-ray diffractometer (XRD) was used to perform X-ray dif- fraction on the cladding layer, thus obtaining a diffraction pat- tern of the cladding layer, as shown in FIG. 3. The XRD spectrum shows that the phase structure of the cladding layer is FCC, and there is a second phase of boride MB (M is Cr, Fe, Co, Mn, Ni).
An energy disperse spectroscopy (ESD) was used to analyze the components at A, B, and C in FIG. 4 and FIG. 5, and results are as shown in the following table: composition position A
It can be seen from the table that there are primary phases
FCC mainly including Co, Mn, Ni, and Fe and a little of M:B at the intercrystalline position A; the number of Cr detected at the den- drite B is obviously increased, which is possibly because that precipitated phases mainly including Cr;B are generated; and a flake-like precipitated phase is generated at C.
The microhardness of the high-entropy alloy cladding layer was measured by a microhardness tester. The measurement was car- ried out at different distances from the surface of the cladding layer. Comparison was performed to the CoCrFeMnNiB 0.8 high- entropy alloy cladding layer and the base body material H13 steel.
Results were as shown in FIG 5. FIG. 5 shows that the average hardness value of the CoCrFeMnNiB 0.8 high-entropy alloy cladding layer is 638.1HV0.2, which is significantly higher than the aver- age hardness value 318.4HV0.2 of its base body.
Embodiment 2
A preparation method for a CoCrFeMnNiB 0.8 high-entropy alloy coating layer specifically includes the following steps. (1) A base material is ground to remove an oxide layer and then is ultrasonically cleaned with alcohol. {2) Weighed Co, Cr, Fe, Mn, Ni, and ferroboron metal powder are uniformly mixed according to a mole ratio of the Co, Cr, Fe,
Mn, Ni, and boron of 1:1:1:1:1:0.8 and subjected to vacuum ball grinding for 3 h or longer time to obtain CoCrFeMnNiB 0.8 high- entropy alloy powder. (3) The CoCrFeMnNiB 0.8 high-entropy alloy powder of the step (2) is placed on a surface of the pretreated base body to form a prefabricated layer; the prefabricated layer is then placed at 60°C for constant-temperature treatment for 6 h; and laser clad- ding is performed to obtain a high-entropy alloy cladding layer.
The laser power of the laser cladding is 3700W, the scanning speed is 350mm/min, the spot diameter is 5.0mm, the defocusing amount is 15mm, the protective gas is argon, and the gas flow is 10 L/min.
Embodiment 3
A preparation method for a CoCrFeMnNiB 0.8 high-entropy alloy coating layer specifically includes the following steps. (1) A base material is ground to remove an oxide layer and then is ultrasonically cleaned with alcohol. (2) Weighed Co, Cr, Fe, Mn, Ni, and ferroboron metal powder are uniformly mixed according to a mole ratio of the Co, Cr, Fe,
Mn, Ni, and boron of 1:1:1:1:1:0.8 and subjected to vacuum ball grinding for 3 h or longer time to obtain CoCrFeMnNiB 0.8 high- entropy alloy powder. (3) The CoCrFeMnNiB 0.8 high-entropy alloy powder of the step (2) is placed on a surface of the pretreated base body to form a prefabricated layer; the prefabricated layer is then placed at 100°C for constant-temperature treatment for 10 h; and laser clad- ding is performed to obtain a high-entropy alloy cladding layer.
The laser power of the laser cladding is 4200W, the scanning speed is 500mm/min, the spot diameter is 3.0mm, the defocusing amount is 30mm, the protective gas is argon, and the gas flow is 6 L/min.
The high-entropy alloy cladding layers prepared in Embodi- ments 2 and 3 after the laser cladding were polished with high- magnification sandpaper to meet the metallographic requirements and photographed and observed with an SEM. Their structures are similar to that of Embodiment 1. The cladding layer and the base body are well bonded, and the cladding layer has a dense structure without an obvious hole defect. An XRD was used to perform X-ray diffraction on the cladding layer. The XRD spectrum shows that the phase structure of the cladding layer is FCC, and there is a sec- ond phase of boride M;B (M is Cr, Fe, Co, Mn, Ni).
The microhardness of the high-entropy alloy cladding layer was measured by a microhardness tester. The measurement was car- ried out at different distances from the surface of the cladding layer. Comparison was performed to the CoCrFeMnNiB 0.8 high- entropy alloy cladding layer and the base body material H13 steel.
It can be seen that in Embodiment 1, the hardness of the
CoCrFeMnNiB 0.8 high-entropy alloy cladding layer (with the aver- age hardness of 638.1HV0.2) is significantly higher than the hard- ness of its base body (with the average hardness of 318.4HV0.2).
In Embodiment 1, the hardness of the CoCrFeMnNiB 0.8 high-entropy alloy cladding layer (with the average hardness of 638.1HV0.2) is significantly higher than the hardness of its base body (with the average hardness of 318.4HV0.2).
Claims (5)
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| NL2030063A NL2030063B1 (en) | 2021-12-07 | 2021-12-07 | High-entropy alloy coating layer and preparation method thereof |
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