CN114457311A - High-entropy alloy nanocrystalline coating for bipolar plate of proton exchange membrane fuel cell and preparation method thereof - Google Patents
High-entropy alloy nanocrystalline coating for bipolar plate of proton exchange membrane fuel cell and preparation method thereof Download PDFInfo
- Publication number
- CN114457311A CN114457311A CN202111680633.8A CN202111680633A CN114457311A CN 114457311 A CN114457311 A CN 114457311A CN 202111680633 A CN202111680633 A CN 202111680633A CN 114457311 A CN114457311 A CN 114457311A
- Authority
- CN
- China
- Prior art keywords
- entropy alloy
- bipolar plate
- fuel cell
- coating
- exchange membrane
- 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.)
- Pending
Links
- 238000000576 coating method Methods 0.000 title claims abstract description 59
- 239000011248 coating agent Substances 0.000 title claims abstract description 58
- 239000000956 alloy Substances 0.000 title claims abstract description 44
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 44
- 239000000446 fuel Substances 0.000 title claims abstract description 20
- 239000012528 membrane Substances 0.000 title claims abstract description 18
- 238000002360 preparation method Methods 0.000 title claims abstract description 12
- 239000010936 titanium Substances 0.000 claims abstract description 41
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 39
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims abstract description 30
- 238000005260 corrosion Methods 0.000 claims abstract description 20
- 238000000151 deposition Methods 0.000 claims abstract description 19
- 230000007797 corrosion Effects 0.000 claims abstract description 16
- 230000008021 deposition Effects 0.000 claims abstract description 16
- 238000002294 plasma sputter deposition Methods 0.000 claims abstract description 11
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims abstract description 10
- 239000013078 crystal Substances 0.000 claims abstract description 10
- 229910052751 metal Inorganic materials 0.000 claims abstract description 7
- 239000002184 metal Substances 0.000 claims abstract description 7
- 238000005516 engineering process Methods 0.000 claims abstract description 6
- 239000013077 target material Substances 0.000 claims abstract description 6
- 229910052786 argon Inorganic materials 0.000 claims abstract description 5
- 238000000034 method Methods 0.000 claims description 10
- 229910052721 tungsten Inorganic materials 0.000 claims description 10
- 229910052735 hafnium Inorganic materials 0.000 claims description 9
- 229910052750 molybdenum Inorganic materials 0.000 claims description 9
- 229910052726 zirconium Inorganic materials 0.000 claims description 9
- 238000002156 mixing Methods 0.000 claims description 5
- 239000000843 powder Substances 0.000 claims description 3
- 238000007731 hot pressing Methods 0.000 claims description 2
- 238000005245 sintering Methods 0.000 claims description 2
- 239000006104 solid solution Substances 0.000 abstract description 5
- 230000002378 acidificating effect Effects 0.000 abstract description 2
- 229910052731 fluorine Inorganic materials 0.000 abstract description 2
- 239000011737 fluorine Substances 0.000 abstract description 2
- 239000007789 gas Substances 0.000 abstract description 2
- 230000007774 longterm Effects 0.000 abstract description 2
- YCKRFDGAMUMZLT-UHFFFAOYSA-N Fluorine atom Chemical compound [F] YCKRFDGAMUMZLT-UHFFFAOYSA-N 0.000 abstract 1
- 239000000758 substrate Substances 0.000 abstract 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 6
- 239000001257 hydrogen Substances 0.000 description 6
- 229910052739 hydrogen Inorganic materials 0.000 description 6
- 230000010287 polarization Effects 0.000 description 6
- 239000000243 solution Substances 0.000 description 6
- 239000000463 material Substances 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 3
- 239000007769 metal material Substances 0.000 description 3
- 238000003917 TEM image Methods 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- -1 fluorine ions Chemical class 0.000 description 2
- 238000013507 mapping Methods 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 238000001878 scanning electron micrograph Methods 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000003054 catalyst Substances 0.000 description 1
- 239000007795 chemical reaction product Substances 0.000 description 1
- 239000002826 coolant Substances 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000006073 displacement reaction Methods 0.000 description 1
- 239000007770 graphite material Substances 0.000 description 1
- 238000007373 indentation Methods 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 230000035800 maturation Effects 0.000 description 1
- 239000002105 nanoparticle Substances 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 239000012429 reaction media Substances 0.000 description 1
- 238000005477 sputtering target Methods 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 229910052723 transition metal Inorganic materials 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Images
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
- C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
- C23C14/22—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the process of coating
- C23C14/34—Sputtering
- C23C14/3464—Sputtering using more than one target
-
- 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
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
- B22F3/14—Both compacting and sintering simultaneously
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/045—Alloys based on refractory metals
-
- 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
- C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
- C23C14/06—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the coating material
- C23C14/14—Metallic material, boron or silicon
- C23C14/16—Metallic material, boron or silicon on metallic substrates or on substrates of boron or silicon
- C23C14/165—Metallic material, boron or silicon on metallic substrates or on substrates of boron or silicon by cathodic sputtering
-
- 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
- C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
- C23C14/22—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the process of coating
- C23C14/34—Sputtering
- C23C14/3407—Cathode assembly for sputtering apparatus, e.g. Target
- C23C14/3414—Metallurgical or chemical aspects of target preparation, e.g. casting, powder metallurgy
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M8/00—Fuel cells; Manufacture thereof
- H01M8/02—Details
- H01M8/0202—Collectors; Separators, e.g. bipolar separators; Interconnectors
- H01M8/0204—Non-porous and characterised by the material
- H01M8/0206—Metals or alloys
- H01M8/0208—Alloys
Abstract
The invention relates to a high-entropy alloy nanocrystalline coating for a bipolar plate of a proton exchange membrane fuel cell and a preparation method thereof. And forming the TiZrHfMoW high-entropy alloy coating with the nano isometric crystal structure on the surface of the pure titanium by using a double-cathode plasma sputtering deposition technology. The adjustable technological parameters of the double-cathode plasma sputtering deposition are target material voltage, workpiece voltage, the distance between the workpiece and the target material, argon gas pressure, deposition time and the like. The coating is formed by a single-phase BCC structure high-entropy alloy solid solution phase, has a nanoscale isometric crystal structure, is well combined with a titanium substrate, improves the surface hardness of the bipolar plate, has a low corrosion rate and good pitting corrosion resistance in a fluorine-containing ion acidic medium, and can meet the requirements of high performance and long-term use of the metal bipolar plate of the fuel cell.
Description
Technical Field
The invention relates to a high-entropy alloy coating and a preparation method thereof, in particular to a high-entropy alloy nanocrystalline coating for a bipolar plate of a proton exchange membrane fuel cell and a preparation method thereof.
Background
With the maturation of hydrogen production technology and alloy hydrogen storage technology, clean, efficient and renewable hydrogen energy can be used as green energy to enter the society on a large scale. The fuel cell can directly convert chemical energy stored in hydrogen into electric energy, the conversion efficiency is not limited by Carnot cycle, and the fuel cell is a hydrogen energy conversion device widely used at present. Among the fuel cells, Proton Exchange Membrane Fuel Cells (PEMFCs) have high energy density, short start-up time, and low operation noise, and are often used as stable power supply devices for mobile devices such as automobiles and unmanned aerial vehicles. The basic structure of a PEMFC stack may be divided into a proton exchange membrane, a catalyst layer, a diffusion layer, and a bipolar plate (current collector layer). The bipolar plates have the main functions of providing gas and coolant flow channels, separating hydrogen and oxygen, uniformly distributing reaction media, establishing a current path between a cathode and an anode connected in series, conducting heat, dissipating heat, removing water as a reaction product and the like. Currently, the most widely used bipolar plate material is a metallic material. Compared with graphite materials, metal materials have the advantages of good mechanical strength, electric conduction and heat conduction performance, air tightness and easiness in processing into thin plates. The high corrosion resistance and low density of pure titanium (CP-Ti) makes it of greater interest than other metallic materials, given the acidic and humid working environment in PEMFCs and the high fraction of bipolar plates in the total stack weight. However, due to the gradual deterioration of the proton exchange membrane during the operation of the cell, the fluorine ions released by the proton exchange membrane can react with the passive film on the surface of the titanium, and the corrosion resistance of the titanium bipolar plate is reduced. In order to further improve the corrosion resistance of the pure titanium bipolar plate, the preparation of the coating on the bipolar plate is an effective protection scheme. The high-entropy alloy has higher corrosion resistance and mechanical property than the traditional alloy due to the unique high mixed entropy characteristic. Meanwhile, compared with transition metal nitride and carbide coatings, the modulus difference of the high-entropy alloy coating and a pure titanium matrix is smaller. Therefore, the high-entropy alloy coating is a potential corrosion-resistant coating of the bipolar plate.
Disclosure of Invention
The purpose of the invention is as follows: the invention aims to provide a high-entropy alloy nanocrystalline coating for a bipolar plate of a proton exchange membrane fuel cell.
The invention also aims to provide a preparation method of the high-entropy alloy nanocrystalline coating.
The technical scheme is as follows: the invention relates to a preparation method of a high-entropy alloy nanocrystalline coating for a bipolar plate of a proton exchange membrane fuel cell, which is characterized in that a TiZrHfMoW high-entropy alloy coating with a nano isometric crystal structure is formed on the surface of pure titanium (CP-Ti) by utilizing a double-cathode plasma sputtering deposition technology.
Furthermore, the target material is prepared by mixing high-purity metal powder of Ti, Zr, Hf, Mo and W with the purity of more than or equal to 99.9 percent and the grain diameter of 300 meshes and then performing vacuum hot-pressing sintering, and the component ratio of the high-purity metal powder is 8.01 wt.% of Ti, 15.27 wt.% of Zr, 29.88 wt.% of Hf, 16.06 wt.% of Mo and 30.78 percent of W. Target voltage 900-. The workpiece voltage is 300-350V. The pole pitch is 10 mm. The pressure of argon is 35-40 Pa. The deposition time is 3-3.5 h. The deposition temperature is 700 ℃ and 800 ℃. The corrosion-resistant TiZrHfMoW high-entropy alloy nanocrystalline coating of the PEMFC metal bipolar plate is prepared by the method.
The TiZrHfMoW high-entropy alloy coating prepared by the double-cathode plasma sputtering deposition technology has good corrosion resistance. As shown in fig. 1, the tizhfmow high-entropy alloy coating is composed of nano-sized equiaxed crystals, and Ti, Zr, Hf, Mo and W elements are uniformly distributed in the coating. As shown in fig. 2, at 0.5M H2SO4The potentiodynamic polarization test in +6ppm HF solution shows that the coating has lower self-corrosion current density and more positive self-corrosion potential than pure titanium and shows excellent corrosion resistance.
The TiZrHfMoW high-entropy alloy coating can improve the surface hardness of pure titanium. As shown in FIG. 3, the coating can improve the hardness of pure titanium from 5.4 +/-0.3 GPa to 9.6 +/-0.5 GPa, so that the scratch damage suffered by the surface of the double-hit plate can be reduced. Meanwhile, the elastic modulus of the coating is 152.9 +/-6.2 GPa, and the elastic modulus matching degree is better than that of the elastic modulus of 130.5 +/-4.1 GPa of pure titanium, so that the coating and the matrix have better bonding capability.
The TiZrHfMoW high-entropy alloy coating can improve the pitting corrosion resistance of pure titanium. As shown in fig. 4, at 0.5M H2SO4After constant potential polarization in +6ppm HF solution for 48 hours, obvious pitting pits appear on the surface of pure titanium, and the coating has almost no corrosion signs and shows better pitting resistance.
Has the advantages that: compared with the prior art, the invention has the following advantages:
the invention is composed of a single-phase BCC structure high-entropy alloy solid solution phase and has a nanoscale isometric crystal structure. Compared with pure titanium, the coating has higher hardness, lower corrosion rate and better pitting resistance, improves the service time of the titanium bipolar plate in the PEMFC environment, and can meet the requirements of high performance and long-term use of the metal bipolar plate of the fuel cell.
Drawings
FIG. 1 is a TEM image of a TiZrHfMoW high-entropy alloy coating and mapping pictures of Ti, Zr, Hf, Mo, W and N elements;
FIG. 2 shows that the high-entropy alloy coating and pure titanium are 0.5M H2SO4Potentiodynamic polarization curve in +6ppm HF solution;
FIG. 3 is a load displacement curve of the high-entropy alloy coating and pure titanium in a nanometer indentation test with a maximum load of 40 mN;
FIG. 4 shows that the high-entropy alloy coating and pure titanium are 0.5M H2SO4SEM image of surface appearance after constant potential polarization for 48 hours in +6ppm HF solution;
fig. 5 is a cross-sectional SEM image of the tizhfmow high entropy alloy coating.
Detailed Description
Example 1:
the preparation process of the TiZrHfMoW high-entropy alloy coating utilizes a double-cathode plasma sputtering deposition method, and the coating formed on the surface of pure titanium consists of a single-phase BCC high-entropy alloy solid solution phase and has a nano isometric crystal structure. Wherein
a. Parameters of the double-cathode plasma sputtering process:
b. sputtering target material: mixing a Ti-Zr-Hf-Mo-W target, wherein the component ratio (mass fraction percent): 8.01 wt.% Ti, 15.27 wt.% Zr, 29.88 wt.% Hf, 16.06 wt.% Mo, 30.78% W;
c. kind of workpiece material: pure titanium (CP-Ti).
FIG. 1 is a TEM image of a TiZrHfMoW high entropy alloy nitride coating and mapping pictures of Ti, Zr, Hf, Mo, W and N elements. TEM pictures show that the coating is composed of nano equiaxed crystals, and Ti, Zr, Hf, Mo and W are uniformly distributed in the coating. In a nanometer press-in test with the maximum load of 40N, the coating obviously improves the surface hardness of pure titanium, and meanwhile, the elastic modulus of the coating is equivalent to that of the pure titanium, thereby being beneficial to improving the bonding capacity of the coating and a matrix. At 0.5M H2SO4The potentiodynamic polarization test in +6ppm HF solution shows that the coating has lower self-corrosion current density and more positive self-corrosion potential than pure titanium and shows excellent corrosion resistance. At 0.5M H2SO4After constant potential polarization in +6ppm HF solution for 48 hours, obvious pitting pits appear on the surface of pure titanium, and the coating has almost no corrosion signs and shows better pitting resistance.
Example 2:
a preparation process of a high-entropy alloy nanocrystalline coating utilizes a double-cathode plasma sputtering deposition method, and the coating formed on the surface of pure titanium consists of a single-phase BCC high-entropy alloy solid solution phase and has a nano isometric crystal structure. The technological parameters of the double-cathode plasma sputtering deposition are as follows: the target voltage is 900V, the workpiece voltage is 350V, the inter-polar distance is 10mm, the argon pressure is 40Pa, the deposition temperature is 700-800 ℃, and the deposition time is 3.5 h. b. Mixing a Ti-Zr-Hf-Mo-W target, wherein the component ratio (mass fraction percent): 8.01 wt.% Ti, 15.27 wt.% Zr, 29.88 wt.% Hf, 16.06 wt.% Mo, 30.78% W; c. kind of workpiece material: pure titanium (CP-Ti). The overall properties of the resulting coating are slightly lower than in example 1.
Example 3:
a preparation process of a high-entropy alloy nanocrystalline coating utilizes a double-cathode plasma sputtering deposition method, and the coating formed on the surface of pure titanium consists of a single-phase BCC high-entropy alloy solid solution phase and has a nano isometric crystal structure. The technological parameters of the double-cathode plasma sputtering deposition are as follows: the target voltage is 950V, the workpiece voltage is 350V, the inter-polar distance is 10mm, the argon pressure is 35Pa, the deposition temperature is 700-800 ℃, and the deposition time is 3 h. b. Mixing a Ti-Zr-Hf-Mo-W target, wherein the component ratio (mass fraction percent): 8.01 wt.% Ti, 15.27 wt.% Zr, 29.88 wt.% Hf, 16.06 wt.% Mo, 30.78% W; c, type of workpiece material: pure titanium (CP-Ti). The overall properties of the resulting coating are slightly lower than in example 1.
Claims (9)
1. A preparation method of a high-entropy alloy nanocrystalline coating for a bipolar plate of a proton exchange membrane fuel cell is characterized by comprising the following steps: and forming the TiZrHfMoW high-entropy alloy coating with the nano isometric crystal structure on the surface of pure titanium (CP-Ti) by utilizing a double-cathode plasma sputtering deposition technology.
2. The method for preparing a high-entropy alloy nanocrystalline coating for a proton exchange membrane fuel cell bipolar plate according to claim 1, is characterized in that: the target material is prepared by mixing high-purity metal powder of Ti, Zr, Hf, Mo and W with the purity of more than or equal to 99.9 percent and the grain size of 300 meshes and then performing vacuum hot-pressing sintering, and the component ratio of the target material is 8.01 wt.% of Ti, 15.27 wt.% of Zr, 29.88 wt.% of Hf, 16.06 wt.% of Mo and 30.78 percent W.
3. The method for preparing a high-entropy alloy nanocrystalline coating for a proton exchange membrane fuel cell bipolar plate according to claim 1, is characterized in that: target voltage 900-.
4. The method for preparing a high-entropy alloy nanocrystalline coating for a proton exchange membrane fuel cell bipolar plate according to claim 1, is characterized in that: the workpiece voltage is 300-350V.
5. The method for preparing a high-entropy alloy nanocrystalline coating for a proton exchange membrane fuel cell bipolar plate according to claim 1, is characterized in that: the pole pitch is 10 mm.
6. The method for preparing a high-entropy alloy nanocrystalline coating for a proton exchange membrane fuel cell bipolar plate according to claim 1, is characterized in that: the pressure of argon is 35-40 Pa.
7. The method for preparing a high-entropy alloy nanocrystalline coating for a proton exchange membrane fuel cell bipolar plate according to claim 1, is characterized in that: the deposition time is 3-3.5 h.
8. The method for preparing a high-entropy alloy nanocrystalline coating for a proton exchange membrane fuel cell bipolar plate according to claim 1, is characterized in that: the deposition temperature is 700 ℃ and 800 ℃.
9. A corrosion-resistant tizhfmow high-entropy alloy nanocrystalline coating of a PEMFC metal bipolar plate, prepared by the method of any one of claims 1 to 8.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202111680633.8A CN114457311A (en) | 2021-12-30 | 2021-12-30 | High-entropy alloy nanocrystalline coating for bipolar plate of proton exchange membrane fuel cell and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202111680633.8A CN114457311A (en) | 2021-12-30 | 2021-12-30 | High-entropy alloy nanocrystalline coating for bipolar plate of proton exchange membrane fuel cell and preparation method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN114457311A true CN114457311A (en) | 2022-05-10 |
Family
ID=81408591
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202111680633.8A Pending CN114457311A (en) | 2021-12-30 | 2021-12-30 | High-entropy alloy nanocrystalline coating for bipolar plate of proton exchange membrane fuel cell and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN114457311A (en) |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106374116A (en) * | 2016-12-01 | 2017-02-01 | 上海电机学院 | High-entropy alloy composite coating on metal bipolar plate of fuel cell and process |
| US20170314097A1 (en) * | 2016-05-02 | 2017-11-02 | Korea Advanced Institute Of Science And Technology | High-strength and ultra heat-resistant high entropy alloy (hea) matrix composites and method of preparing the same |
| CN110137525A (en) * | 2019-05-17 | 2019-08-16 | 北京中氢绿能科技有限公司 | A kind of fuel battery metal double polar plate coating and technology of preparing |
| CN110453131A (en) * | 2019-09-09 | 2019-11-15 | 沈阳工业大学 | A kind of high-entropy alloy and preparation method thereof with good thermal processability energy |
-
2021
- 2021-12-30 CN CN202111680633.8A patent/CN114457311A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20170314097A1 (en) * | 2016-05-02 | 2017-11-02 | Korea Advanced Institute Of Science And Technology | High-strength and ultra heat-resistant high entropy alloy (hea) matrix composites and method of preparing the same |
| CN106374116A (en) * | 2016-12-01 | 2017-02-01 | 上海电机学院 | High-entropy alloy composite coating on metal bipolar plate of fuel cell and process |
| CN110137525A (en) * | 2019-05-17 | 2019-08-16 | 北京中氢绿能科技有限公司 | A kind of fuel battery metal double polar plate coating and technology of preparing |
| CN110453131A (en) * | 2019-09-09 | 2019-11-15 | 沈阳工业大学 | A kind of high-entropy alloy and preparation method thereof with good thermal processability energy |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101800318B (en) | Metal bipolar plate for proton exchange membrane fuel cell and preparation method thereof | |
| CN112885997B (en) | Preparation method and application of novel silicon-based composite porous negative electrode material of lithium ion battery | |
| CN112421048A (en) | Method for preparing graphite-coated nano-silicon lithium battery negative electrode material at low cost | |
| US8841045B2 (en) | Method for fabricating bi-polar plate of fuel cell | |
| CN110767891B (en) | Preparation method of porous spherical silicon-based composite anode material | |
| JP4206058B2 (en) | Method for producing catalyst layer for fuel cell | |
| JPH10255823A (en) | Solid high polymer fuel cell | |
| CN105185988A (en) | Preparation method of three-dimensional foamed MoS2/graphene | |
| CN114481048B (en) | High-conductivity corrosion-resistant amorphous/nanocrystalline composite coexisting coating and preparation method and application thereof | |
| CN112820847A (en) | Silicon-based negative electrode material and preparation method thereof, lithium ion battery and electric appliance | |
| CN109671958B (en) | Solid oxide fuel cell and preparation method thereof | |
| CN112234186B (en) | MXene nanodot coated modified lithium ion battery cathode material and preparation method thereof | |
| CN1667859A (en) | Process for preparing solid oxide fuel battery connectors | |
| JP2005150014A (en) | Fuel cell and separator for cooling used for it | |
| CN114457311A (en) | High-entropy alloy nanocrystalline coating for bipolar plate of proton exchange membrane fuel cell and preparation method thereof | |
| CN201717318U (en) | Metal bipolar plate for proton exchange membrane fuel cell | |
| CN113151790B (en) | Ion/electron common conductor film, preparation method thereof, solid-state battery and electric vehicle | |
| JP3404363B2 (en) | Fuel cell separator | |
| CN109888265B (en) | Hydrogel-derived silicon-titanium alloy interconnection network material and preparation method and application thereof | |
| CN112221892A (en) | Novel metal bipolar plate surface modification method | |
| CN111769293A (en) | Fuel cell stack with low contact resistance and fuel cell using same | |
| CN112687892B (en) | Self-assembled high-performance core-shell structure cathode of solid oxide fuel cell and preparation method thereof | |
| CN112952131B (en) | Fe-Mn-based alloy bipolar plate with nanocrystalline AlN modified layer and preparation method thereof | |
| CN210657123U (en) | Four-cavity deposition system for metal carbide coating of fuel cell pole plate | |
| CN116694972A (en) | A cermet material (Nb) for bipolar plates of proton exchange membrane fuel cells 1-x Ta x ) 2 AlC and preparation method thereof |
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 | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20220510 |
|
| RJ01 | Rejection of invention patent application after publication |