WO2024046324A1 - 多主元多孔合金及制备方法和用于电解海水的多孔电极 - Google Patents

多主元多孔合金及制备方法和用于电解海水的多孔电极 Download PDF

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WO2024046324A1
WO2024046324A1 PCT/CN2023/115551 CN2023115551W WO2024046324A1 WO 2024046324 A1 WO2024046324 A1 WO 2024046324A1 CN 2023115551 W CN2023115551 W CN 2023115551W WO 2024046324 A1 WO2024046324 A1 WO 2024046324A1
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porous
alloy
principal
electrode
seawater
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刘雄军
李志斌
王辉
吴渊
吕昭平
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北京科技大学
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/08—Alloys with open or closed pores
    • 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
    • C22C30/02—Alloys containing less than 50% by weight of each constituent containing copper
    • 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
    • C23F—NON-MECHANICAL REMOVAL OF METALLIC MATERIAL FROM SURFACE; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL; MULTI-STEP PROCESSES FOR SURFACE TREATMENT OF METALLIC MATERIAL INVOLVING AT LEAST ONE PROCESS PROVIDED FOR IN CLASS C23 AND AT LEAST ONE PROCESS COVERED BY SUBCLASS C21D OR C22F OR CLASS C25
    • C23F1/00—Etching metallic material by chemical means
    • C23F1/02—Local etching
    • 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
    • C23F—NON-MECHANICAL REMOVAL OF METALLIC MATERIAL FROM SURFACE; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL; MULTI-STEP PROCESSES FOR SURFACE TREATMENT OF METALLIC MATERIAL INVOLVING AT LEAST ONE PROCESS PROVIDED FOR IN CLASS C23 AND AT LEAST ONE PROCESS COVERED BY SUBCLASS C21D OR C22F OR CLASS C25
    • C23F1/00—Etching metallic material by chemical means
    • C23F1/10—Etching compositions
    • C23F1/14—Aqueous compositions
    • C23F1/16—Acidic compositions
    • C23F1/30—Acidic compositions for etching other metallic material
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25B—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES FOR THE PRODUCTION OF COMPOUNDS OR NON-METALS; APPARATUS THEREFOR
    • C25B1/00—Electrolytic production of inorganic compounds or non-metals
    • C25B1/01—Products
    • C25B1/02—Hydrogen or oxygen
    • C25B1/04—Hydrogen or oxygen by electrolysis of water
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25B—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES FOR THE PRODUCTION OF COMPOUNDS OR NON-METALS; APPARATUS THEREFOR
    • C25B11/00—Electrodes; Manufacture thereof not otherwise provided for
    • C25B11/02—Electrodes; Manufacture thereof not otherwise provided for characterised by shape or form
    • C25B11/03—Electrodes; Manufacture thereof not otherwise provided for characterised by shape or form perforated or foraminous
    • C25B11/031—Porous electrodes
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25F—PROCESSES FOR THE ELECTROLYTIC REMOVAL OF MATERIALS FROM OBJECTS; APPARATUS THEREFOR
    • C25F3/00—Electrolytic etching or polishing
    • C25F3/02—Etching
    • C25F3/14—Etching locally
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
    • Y02E60/30—Hydrogen technology
    • Y02E60/36—Hydrogen production from non-carbon containing sources, e.g. by water electrolysis
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P20/00—Technologies relating to chemical industry
    • Y02P20/10—Process efficiency
    • Y02P20/133—Renewable energy sources, e.g. sunlight

Definitions

  • the invention belongs to the field of clean and sustainable energy preparation and application, and particularly relates to a multi-principal porous alloy that can be industrially produced and applied, a preparation method thereof, and a porous electrode for electrolyzing seawater.
  • the catalyst must have excellent selectivity.
  • Typical strategies to inhibit chloride corrosion include: designing catalysts that preferentially adsorb oxygen-containing intermediates, building a permeation selectivity layer, and adjusting the electrode structure to exclude chloride ions. But these approaches often require complex structural engineering, and so far very few catalysts can operate at industrial current densities for long periods of time. Therefore, it is very challenging and very meaningful to prepare a seawater electrolysis catalyst that can be prepared in large quantities, has high activity, high selectivity, high stability and integrated functional structure.
  • the purpose of the present invention is to overcome the current common problems of high activity and stability in catalytic materials for electrolysis of seawater, as well as the shortcomings of traditional research catalysts that cannot be prepared in large quantities, and to provide a method for preparing porous alloy materials for electrolysis of seawater electrodes.
  • the multi-main porous alloy includes a matrix and an exterior of the matrix that are two-layer nanostructures, and there is a porous structure between the ligaments.
  • the two-layer nanostructure is an intermediate layer and an outer layer;
  • the matrix is an intermetallic compound,
  • the intermediate layer is an amorphous oxide, and
  • the outer layer is a multi-principal oxide.
  • the amorphous oxide is (NbTiHfZrTa)Oy, 40 ⁇ y ⁇ 80 at%;
  • the multi-principal oxide is (FeCoNiNbTiHfZrTaM)Oy, M is one or more of Pt, Ru, Ir, Cu, 40 ⁇ y ⁇ 80 at%.
  • Another object of the present invention is to provide a method for preparing the above-mentioned multi-principal porous alloy, which method specifically includes the following steps:
  • the corrosion liquid used in the chemical/electrochemical dealloying method in S2) is 0.001 ⁇ 2 mol/L H 2 SO 4 , HNO 3 or HCl solution, the corrosion temperature is 25-80°C, and the corrosion time is 1 -72h.
  • a porous electrode for electrolyzing seawater is prepared by using the above-mentioned preparation method to obtain a multi-principal porous alloy.
  • the porous electrode used for electrolyzing seawater has a unique self-healing ability and can be directly used for electrolyzing water to produce hydrogen in an alkaline seawater electrolyzer, showing excellent electrocatalytic performance: at an industrial electrolysis current density (500 mA cm -2 )
  • the overpotentials for oxygen evolution and hydrogen evolution are 461 and 178 mV respectively, and the OER stability exceeds 1600 h at this current density. No performance degradation and electrode corrosion were found in the stability test.
  • the ligament of the prepared multi-principal porous alloy electrode material multi-principal porous alloy has a two-layer nanostructure, and the pore structure (15-1000 nm) can be precisely controlled through physical metallurgy and preparation processes.
  • the specific surface area is large and can meet the performance and stability requirements under different working conditions.
  • the contact area between the active material of the electrode material and the electrolyte is increased, thereby improving the electrocatalytic efficiency.
  • the multi-principal porous electrode prepared by the present invention has a self-supporting structure, which overcomes the problems of reduced activity of nanomaterials prepared by other methods due to poor conductivity, agglomeration, and shedding, enhances its stability, and significantly increases electrocatalytic activity. improve.
  • the prepared multi-principal porous alloy electrode material has excellent selectivity for electrolysis of seawater, can avoid the oxidation of chloride ions and compete with OER (Oxygen Evolution Reaction), and can produce high-purity oxygen.
  • the prepared electrode material has excellent corrosion resistance and excellent stability in the harsh seawater simulation liquid, so it can greatly increase the service life of the catalyst and reduce costs. At the same time, it provides an innovative idea for designing catalysts for high-performance electrolysis of seawater hydrogen production electrode materials, which has great application potential.
  • Figure 1 is an SEM image of the Fe 40-x Co 10 Ni 10 Nb 10 Ti 10 Zr 10 Hf 10 Pt x (0 ⁇ x ⁇ 5at%) alloy used as a precursor after electrochemical dealloying for 12 hours using the method of the present invention.
  • Figure 2 is an SEM image of the Fe 40-x Co 10 Ni 10 Nb 10 Ti 10 Zr 10 Hf 10 Ir x (0 ⁇ x ⁇ 5at%) alloy as a precursor after electrochemical dealloying for 12 hours using the method of the present invention.
  • Figure 3 is an SEM image of the Fe 40-x Co 10 Ni 10 Nb 10 Ti 10 Zr 10 Hf 10 Cu x (0 ⁇ x ⁇ 5at%) alloy precursor using the method of the present invention.
  • Figure 4 is an SEM image of the Fe 40-x Co 10 Ni 10 Nb 10 Ti 10 Zr 10 Hf 10 Cu x (0 ⁇ x ⁇ 5at%) alloy used as a precursor after electrochemical dealloying for 12 hours using the method of the present invention.
  • Figure 5 is a schematic diagram of the TEM results of the nanoporous (FeCoNiPt) 2 Nb electrode using the method of the present invention.
  • Figure 6 is a schematic diagram of the TEM results of the nanoporous (FeCoNiIr) 2 Nb electrode using the method of the present invention.
  • Figure 7 is a schematic diagram of the polarization curves of nanoporous (FeCoNiPt) 2 Nb and nanoporous (FeCoNiIr) 2 Nb electrodes after conversion to standard hydrogen electrode potential.
  • Figure 8 is a schematic diagram of the polarization curve and the corresponding Taffy slope diagram measured for nanoporous (FeCoNi) 2 Nb in simulated seawater solution.
  • a is the polarization curve diagram
  • b is the Taffy slope diagram.
  • Figure 9 is a schematic diagram of the chronopotential curve of the nanoporous (FeCoNi) 2 Nb electrode material in a seawater simulated solution under a high current density (500 mA cm -2 ).
  • Figure 10 is the SEM image of Co 86 Nb 14 alloy after electrochemical dealloying for 12 hours.
  • the present invention is a multi-principal porous alloy.
  • the ligament of the multi-host porous alloy has a two-layer nanostructure.
  • the two-layer nanostructure consists of a matrix, an intermediate layer and an outer layer from the inside to the outside; the matrix is an intermetallic compound, the middle layer is an amorphous oxide, and the outer layer is a multi-principal oxide.
  • the amorphous oxide is (NbTiHfZrTa)Oy, 40 ⁇ y ⁇ 80 at%;
  • the multi-principal oxide is (FeCoNiNbTiHfZrTaM)Oy, M is one or more of Pt, Ru, Ir, Cu, 40 ⁇ y ⁇ 80 at%.
  • the present invention also provides a method for preparing the above-mentioned multi-principal porous alloy.
  • the method specifically includes the following steps:
  • the corrosion liquid used in the chemical/electrochemical dealloying method in S2) is 0.001 ⁇ 2 mol/L H2SO4 , HNO3 or HCl solution, the corrosion temperature is 25-80 °C, and the corrosion time is 1-72 h.
  • a porous electrode for electrolyzing seawater is prepared by using the above-mentioned preparation method to obtain a multi-principal porous alloy.
  • the porous electrode used for electrolyzing seawater has a unique self-healing ability and can be directly used to electrolyze water to produce hydrogen in an alkaline seawater electrolyzer, showing excellent electrocatalytic performance: at an industrial electrolysis current density (500 mA cm -2 ), the overpotentials for oxygen evolution and hydrogen evolution are 461 and 178 mV respectively, and the OER stability exceeds 1600 h at this current density. No performance degradation and electrode corrosion were found in the stability test.
  • the required elements are Weigh the required pure elements for the precursor alloy ((Fe 99.99 wt%, Co 99.99 wt%, Ni 99.99 wt%, Cu 99.99 wt%, Nb 99.99 wt%, Ir 99.99 wt%, Ru 99.99 wt% , Pt 99.99 wt%), weigh it according to the atomic percentage of the alloy converted into mass, and then use high-purity argon atmosphere vacuum arc melting method to smelt the master alloy button ingot, and smelt it 6-8 times to ensure that the composition of the master alloy ingot is uniform. .Then the copper mold suction casting method is used to obtain the precursor alloy of regular size.
  • the Fe 40-x Co 10 Ni 10 Nb 10 Ti 10 Zr 10 Hf 10 Pt x (0 ⁇ x ⁇ 5at%) alloy prepared in Example 1 was used as the precursor, with 0.5 mol L -1 of H 2 SO 4
  • the aqueous solution was used as a corrosive liquid for electrochemical dealloying. It was taken out after 12 hours and washed several times with ultrapure water and absolute alcohol to remove residual chemical substances in the pores. After drying, a porous electrode material was prepared.
  • Figure 1 shows the SEM image of Fe 40-x Co 10 Ni 10 Nb 10 Ti 10 Zr 10 Hf 10 Pt x (0 ⁇ x ⁇ 5at%) alloy after electrochemical dealloying for 12 hours. It can be observed that the formation of three-dimensional bicontinuous Nano through hole structure, pore size is 50-100 nm.
  • the Fe 40-x Co 10 Ni 10 Nb 10 Ti 10 Zr 10 Hf 10 Ir x (0 ⁇ x ⁇ 5at%) alloy prepared in Example 1 is used as the precursor, and a 0.5 mol/L H 2 SO 4 aqueous solution is used.
  • a corrosive liquid perform electrochemical dealloying, take it out after 12 hours, and wash it with ultrapure water and anhydrous alcohol several times to remove residual chemical substances in the pores. After drying, a porous electrode material is prepared.
  • Figure 2 shows the SEM image of the Fe 40-x Co 10 Ni 10 Nb 10 Ti 10 Zr 10 Hf 10 Ir x (0 ⁇ x ⁇ 5at%) alloy after electrochemical dealloying for 12 hours. It can be observed that the formation of a three-dimensional bicontinuous Nano through hole structure, pore size is 50-500 nm.
  • the Fe 40-x Co 10 Ni 10 Nb 10 Ti 10 Zr 10 Hf 10 Cu x (0 ⁇ x ⁇ 5at%) alloy prepared in Example 1 was used as the precursor, and 0.5 mol L -1 of H 2 SO 4
  • the aqueous solution was used as a corrosive liquid for electrochemical dealloying. It was taken out after 12 hours and washed several times with ultrapure water and absolute alcohol to remove residual chemical substances in the pores. After drying, a porous electrode material was prepared.
  • Figure 3 shows the morphology of Fe 40-x Co 10 Ni 10 Nb 10 Ti 10 Zr 10 Hf 10 Cu x (0 ⁇ x ⁇ 5at%) alloy precursor, which is a typical eutectic structure.
  • Nanostructure that is, the outer layer is amorphous multi-component oxide ((FeCoNiNbPt)Ox), the middle layer is amorphous NbOx, and the matrix is the Laves phase of (FeCoNiPt) 2 Nb.
  • the outer layer is amorphous multi-component oxide ((FeCoNiNbPt)Ox)
  • the middle layer is amorphous NbOx
  • the matrix is the Laves phase of (FeCoNiPt) 2 Nb.
  • the microstructure of the nanoporous electrode prepared in Example 3 was characterized using a transmission electron microscope.
  • Figure 6 shows the transmission characterization results after dealloying of Fe 37 Co 20 Ni 20 Nb 20 Ir 3. It can be observed that the electrode has a unique two-layer nanostructure.
  • the structure is that the outer layer is an amorphous multi-component oxide ((FeCoNiNbIr)Ox), the middle layer is amorphous NbOx, and the matrix is the Laves phase of (FeCoNiIr) 2 Nb.
  • a is the energy spectrum line scan result
  • b is the energy spectrum surface scan result.
  • the standard electrode is a reference electrode to form a three-electrode system. Linear voltammetric scanning is performed in seawater simulated liquid (1 mol L -1 KOH + 0.5 mol L -1 NaCL) at a scanning speed of 2 mV/s -1 .
  • Figure 7 shows the polarization curve of the porous electrode material after conversion to the standard hydrogen electrode potential. After adding a small amount of noble metal, the hydrogen evolution performance of the electrolytic seawater of the electrode material has been greatly improved and corresponds to the current density of 500 mA cm -2 The overpotential decreased from 429 mV to 178 mV.
  • Example 1 We used the Fe 40 Co 20 Ni 20 Nb 20 porous electrode after electrochemical dealloying in Example 1 as the working electrode, the graphite electrode as the auxiliary electrode, and the Hg/HgO standard electrode as the reference electrode to form a three-electrode system, and simulated it in seawater A linear voltammetry scan was performed in liquid (1 mol L -1 KOH + 0.5 mol L -1 NaCL) at a scan speed of 2 mV s -1 , and a chronopotentiometry method was used for stability testing.
  • Figure 8a shows the polarization curve of the porous electrode material after conversion to the standard hydrogen electrode potential.
  • the overpotential corresponding to 500 mA cm -2 at an industrial current density is only 461 mV, which is lower than the oxidation potential of chloride ions, and is therefore very It is good to avoid the oxidation of chloride ions and the competition of OER.
  • Figure 9 shows the stability test of the porous electrode material under industrial current density (500 mA cm -2 ). It can work continuously for more than 1600 h and has very excellent stability.
  • Co 86 Nb 14 alloy is used as the precursor, and 0.5 mol L -1 H 2 SO 4 aqueous solution is used as the corrosive liquid to perform electrochemical dealloying. Take it out after 12 hours, and use ultrapure water and absolute alcohol several times in sequence. After cleaning, the residual chemical substances in the pores are removed, and after drying, the porous electrode material is prepared.
  • Figure 10 shows the SEM image of the Co 86 Nb 14 alloy after electrochemical dealloying for 12 hours. It can be observed that a three-dimensional bicontinuous nanometer through-hole structure is formed.

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Abstract

本发明涉及一种多主元多孔合金及制备方法和用于电解海水的多孔电极。该多主元多孔合金的制备方法：通过熔炼得到名义成分为FeaCobNicNbdTieTafHfgZrhMx的合金作为前驱体；再通过化学/电化学脱合金法选择性去除其中活泼的相制备得到多主元多孔合金。该多主元多孔合金可直接作为电极用于电解海水，在工业电解电流密度下析氧(Oxygen Evolution Reaction, OER)和析氢(Hydrogen Evolution Reaction, HER)过电位分别为461和178 mV，且在此电流密度下OER稳定工作超过1600 h。在电解海水制氢电极器件方面具有很大的应用前景。

Description

多主元多孔合金及制备方法和用于电解海水的多孔电极 技术领域
本发明属于清洁可持续能源制备应用领域，特别涉及一种可工业化生产和应用的一种多主元多孔合金及制备方法和用于电解海水的多孔电极。
 背景技术
氢能作为公认的绿色清洁能源，具有高效、无污染、易储运等特点，被誉为21世纪最具有发展前景的可再生能源。在各种制氢技术中，电解水制氢具有产品纯度高、工艺简单、绿色可循环等优点，被认为是未来通向“氢经济”的最佳途径。而我国具有可再生的、储量巨大的海洋能（海上风能、波浪能、潮流能、海岛太阳能等），其中海洋能耦合电解海水制氢+氢燃料电池是理想的可独立运行的能量循环系统，可以实现海上民用、军事等设施的能源自给。而利用海岸线附近的弃风、弃光资源产生可再生的电力直接驱动海水裂解制氢，不仅能产出可再生的清洁能源氢气，缓解能源危机；还能有效地节约淡水资源，缓解水资源的危机，对促进社会全面可持续发展具有重大意义。
实际应用中活性、稳定性和成本是设计电催化剂时需要考虑的三个关键因素。到目前为止，大多数催化剂的研究主要集中在提高催化剂的催化活性和降低材料成本上。而只有极少数的研究系统地关注提高催化剂的催化稳定性，特别是在碱性海水溶液中。虽然提高低成本催化剂的活性可以降低电解海水的能耗，但催化剂的稳定性可能是实际应用中需要考虑的更重要的因素。这是因为高活性、低稳定性的催化剂相较于高稳定性的催化剂的能耗会随着时间的增加急剧增加。而目前，以海水电解为基础的电极催化剂的稳定性仍然是巨大的挑战，一个关键问题是海水成分非常复杂，其中高浓度的氯离子会加速催化剂的腐蚀，这严重限制了催化剂的长期稳定性。另外氯离子会向阳极扩散与电解海水的OER发生竞争，在热力学角度考虑碱性环境下电解海水的OER反应比氯离子的氧化更容易，但是氯离子氧化的动力学较OER反应更有利，这是因为氯离子氧化为2电子过程而OER反应则是4电子过程，因此避免氯离子的氧化生产不必要的氯化物还需要催化剂具有优异的选择性。抑制氯化物腐蚀的典型策略包括有：设计优先吸附含氧中间体的催化剂，构建渗透选择性层，调节电极结构排斥氯离子等。但是这些方法通常需要复杂的结构工程，而且到目前为止，极少数催化剂可以在工业电流密度下长时间工作。因此制备可宏量制备、高活性、高选择性、高稳定性和功能结构一体化的电解海水催化剂具有非常大的挑战且十分有意义。
 发明内容
本发明的目的在于克服目前电解海水催化材料普遍存在的高活性和稳定性不能兼得的难题，以及传统研究催化剂不能宏量制备的缺点，提供一种电解海水电极多孔合金材料的制备方法。
本发明的技术方案如下：一种多主元多孔合金，所述多主元多孔合金的化学表达式为：Fe aCo bNi cNb dTi eTa fHf gZr hM x，M为Pt、Ru、Ir、Cu中的一种或多种；其中，0＜a≤55 at%，0＜b≤55 at%，0＜c≤55 at%，0≤d≤55 at%，0≤e≤55 at%，0≤f≤55 at%，0≤g≤≤55 at%，0≤h≤55 at%，0≤x≤5 at%，且a+b+c+d+e+f+g+h+x =100 at%。
进一步，所述多主多孔合金的包含基体和基体外部为两层纳米结构，韧带之间为多孔结构。
  进一步，所述两层纳米结构为中间层和外层；基体为金属间化合物，中间层为非晶态的氧化物，外层为多主元氧化物。
进一步，所述非晶态的氧化物为(NbTiHfZrTa)Oy，40≤y≤80 at%；
所述多主元氧化物为(FeCoNiNbTiHfZrTaM)Oy ，M为Pt, Ru, Ir, Cu中的一种或多种，40≤y≤80 at%。
  本发明的另一目的是提供一种上述的多主元多孔合金的制备方法，所述方法具体包括以下步骤：
   S1) 制备尺寸可控的前驱体合金；
S2）将S1)制备得到前驱体合金置于酸性溶液中进行化学/电化学脱合金，去除活泼的相，保留耐蚀的相形成多孔和两层纳米结构的多主元多孔合金，多孔结构孔径为15-1000 nm。
进一步，所述S1）的具体步骤为：
S1.1)金属原料放入无水酒精中采用超声波的方式进行多次清洗，然后将金属原料取出，并根据设计的合金名义成分配比；
S1.2）将称量好的金属原料采用真空电弧炉熔炼制备尺寸可控的前驱体合金。
进一步，所述S2）中的化学/电化学脱合金化法采用的腐蚀液为0.001~2 mol/L的H 2SO 4、HNO 3或HCl溶液，腐蚀温度25-80℃，腐蚀时间为1-72 h。
一种用于电解海水的多孔电极，所述用于电解海水的多孔电极采用上述的制备方法得到多主元多孔合金制备得到。
进一步，所述用于电解海水的多孔电极具有独特的自修复的能力且能直接用于碱性海水电解槽电解水制氢，表现出优异的电催化性能：在工业电解电流密度（500 mA cm -2）下析氧和析氢过电位分别为461和178 mV，且在此电流密度下OER稳定性超过1600 h ，在稳定性测试中未发现性能衰减与电极腐蚀。
本发明的有益效果如下：制备得到的多主元多孔合金电极材料多主多孔合金的韧带具有两层纳米结构，可通过物理冶金和制备工艺的方法精确调控孔结构（15-1000 nm），内部比表面积大，可以满足不同工况下对性能和稳定性的要求。相对于传统的泡沫Ni提高了电极材料活性物质与电解液的接触面积，提高了电催化效率。
本发明所制备得到的多主元多孔电极为自支撑结构克服了其他方法制备的纳米材料因导电性差，团聚导致，脱落而导致的活性降低的问题，增强了其稳定性，电催化活性大幅度提高。
制备得到的多主元多孔合金电极材料具有优异的电解海水选择性，可以避免氯离子的氧化与OER(Oxygen Evolution Reaction)的竞争，可制备高纯度的氧气。
制备得到的电极材料具有卓越的耐腐蚀性，在环境苛刻的海水模拟液中具有十分优异的稳定性，因此可以大幅度提高催化剂的使用寿命、降低成本。同时为高性能电解海水制氢电极材料方面提供了一种设计催化剂的创新思路，具有很大的应用潜力。
 附图说明
图1为采用本发明方法的Fe 40-xCo 10Ni 10Nb 10Ti 10Zr 10Hf 10Pt x(0≤x≤5at%)合金作为前驱体电化学脱合金12 h后的SEM图。
图2 为采用本发明方法的Fe 40-xCo 10Ni 10Nb 10Ti 10Zr 10Hf 10Ir x(0≤x≤5at%)合金作为前驱体电化学脱合金12 h后的SEM图。
图3 为采用本发明方法的Fe 40-xCo 10Ni 10Nb 10Ti 10Zr 10Hf 10Cu x(0≤x≤5at%)合金前驱的SEM图。
图4 为采用本发明方法的Fe 40-xCo 10Ni 10Nb 10Ti 10Zr 10Hf 10Cu x(0≤x≤5at%)合金作为前驱电化学脱合金12h后的SEM图。
图5为采用本发明方法的纳米多孔(FeCoNiPt) 2Nb 电极的TEM结果示意图。
图6为采用本发明方法的纳米多孔(FeCoNiIr) 2Nb 电极的TEM结果示意图。
图7为纳米多孔(FeCoNiPt) 2Nb 和纳米多孔(FeCoNiIr) 2Nb 电极在换算成标准氢电极电位后的极化曲线示意图。
图8为纳米多孔(FeCoNi) 2Nb在模拟海水溶液中测得的极化曲线示意图和相应塔菲斜率图，a为极化曲线图，b为塔菲斜率图。
图9为纳米多孔(FeCoNi) 2Nb电极材料在海水模拟溶液中、大电流密度（500 mA cm -2）下的计时电位曲线示意图。
图10为Co 86Nb 14合金电化学脱合金12h后的SEM图。
具体实施方式
下面结合附图和实施例，对本发明的技术方案做进一步的详细描述。
本发明一种多主元多孔合金，所述多主元多孔合金的化学表达式为：Fe aCo bNi cNb dTi eTa fHf gZr hM x，M为Pt、Ru、Ir、Cu中的一种或多种；其中，0＜a≤55 at%，0＜b≤55 at%，0＜c≤55 at%，0≤d≤55 at%，0≤e≤55 at%，0≤f≤55 at%，0≤g≤≤55 at%，0≤h≤55 at%，0≤x≤5 at%，且a+b+c+d+e+f+g+h+x =100 at%。
   所述多主多孔合金的韧带具有两层纳米结构。
   所述两层纳米结构由内到外依次为基体、中间层和外层；基体为金属间化合物，中间层为非晶态的氧化物，外层为多主元氧化物。
所述非晶态的氧化物为(NbTiHfZrTa)Oy，40≤y≤80 at%；
所述多主元氧化物为(FeCoNiNbTiHfZrTaM)Oy ，M为Pt, Ru, Ir, Cu中的一种或多种，40≤y≤80 at%。
   本发明还提供一种上述的多主元多孔合金的制备方法，所述方法具体包括以下步骤：
    S1) 制备尺寸可控的前驱体合金；
S2）将S1)制备得到前驱体合金置于酸性溶液中进行化学/电化学脱合金，去除活泼的相，保留耐蚀的相形成具有多孔和两层纳米结构的多主元多孔合金，多孔结构孔径为15-1000 nm。
进一步，所述S1）的具体步骤为：
S1.1)金属原料放入无水酒精中采用超声波的方式进行多次清洗，然后将纯金属原料取出，并根据设计的合金名义成分配比；
S1.2）将称量好的金属原料采用真空电弧炉熔炼制备尺寸可控的前驱体合金。
所述S2）中的化学/电化学脱合金化法采用的腐蚀液为0.001~2 mol/L的H 2SO 4、HNO 3或HCl溶液，腐蚀温度25-80℃，腐蚀时间为1-72 h。
一种用于电解海水的多孔电极，所述用于电解海水的多孔电极采用上述的制备方法得到多主元多孔合金制备得到。
所述用于电解海水的多孔电极具有独特的自修复的能力且能直接用于碱性海水电解槽电解水制氢，表现出优异的电催化性能：在工业电解电流密度（500 mA cm -2）下析氧和析氢过电位分别为461和178 mV，且在此电流密度下OER稳定性超过1600 h ，在稳定性测试中未发现性能衰减与电极腐蚀。
实施例1
以Fe 40-xCo 10Ni 10Nb 10Ti 10Zr 10Hf 10M x(M=Pt, Ir, Ru，Cu, 0≤x≤5at%)，作为前驱体合金名义成分，将所需元素进行称量配比，将前驱体合金所需的纯元素（（Fe 99.99 wt%，Co 99.99 wt%，Ni 99.99 wt%，Cu 99.99 wt%，Nb 99.99 wt%，Ir 99.99 wt%，Ru 99.99 wt%，Pt 99.99 wt%），按照合金的原子百分比换算成质量称好，然后采用高纯氩气氛真空电弧熔炼的方法，熔炼得到母合金纽扣锭，熔炼6-8次，以保证母合金锭成分均匀。然后采用铜模吸铸的方法得到规则尺寸的前驱体合金。
实施例2
采用实施例1中制备得到的Fe 40-xCo 10Ni 10Nb 10Ti 10Zr 10Hf 10Pt x（0≤x≤5at%)合金作为前驱体，以0.5 mol L -1的H 2SO 4水溶液作为腐蚀液，进行电化学脱合金化，12 h后取出，并依次用超纯水和无水酒精多次清洗，去除孔隙中残留化学物质，干燥后制备得到多孔电极材料。
图1所示为Fe 40-xCo 10Ni 10Nb 10Ti 10Zr 10Hf 10Pt x（0≤x≤5at%)合金电化学脱合金12h后的SEM图，可以观察形成了三维双连续的纳米通孔结构，孔径尺寸为50-100 nm。a为x=1，b为x=2，c为x=3, d为x=4，e为x=5。
实施例3
采用实施例1中制备得到的Fe 40-xCo 10Ni 10Nb 10Ti 10Zr 10Hf 10Ir x（0≤x≤5at%)合金作为前驱体，以0.5 mol/L的H 2SO 4水溶液作为腐蚀液，进行电化学脱合金化，12 h后取出，并依次用超纯水和无水酒精多次清洗，去除孔隙中残留化学物质，干燥后制备得到多孔电极材料。
图2所示为Fe 40-xCo 10Ni 10Nb 10Ti 10Zr 10Hf 10Ir x（0≤x≤5at%)合金电化学脱合金12h后的SEM图，可以观察形成了三维双连续的纳米通孔结构，孔径尺寸为50-500 nm。a为x=1，b为x=2，c为x=3, d为x=4，e为x=5。
实施例4
采用实施例1中制备得到的Fe 40-xCo 10Ni 10Nb 10Ti 10Zr 10Hf 10Cu x（0≤x≤5at%)合金作为前驱体，以0.5 mol L -1的H 2SO 4水溶液作为腐蚀液，进行电化学脱合金化，12 h后取出，并依次用超纯水和无水酒精多次清洗，去除孔隙中残留化学物质，干燥后制备得到多孔电极材料。
图3所示为Fe 40-xCo 10Ni 10Nb 10Ti 10Zr 10Hf 10Cu x（0≤x≤5at%)合金前驱体形貌图，为典型的共晶组织。a为x=1，b为x=2，c为x=3, d为x=4。
图4所示为Fe 40-xCo 10Ni 10Nb 10Ti 10Zr 10Hf 10Cu x（0≤x≤5at%)合金电化学脱合金12h后的SEM图，可以观察形成了三维双连续的纳米通孔结构，孔径尺寸为50-500 nm。a为x=1，b为x=2，c为x=3, d为x=4。
实施例5
用透射电镜对实施例2中制备得到的纳米多孔电极进行微观结构表征，图5为Fe 37Co 20Ni 20Nb 20Pt 3脱合金后的透射表征结果，可以观察到该电极具有独特的两层纳米结构，即外层为非晶态多组元的氧化物((FeCoNiNbPt)Ox)，中间层为非晶态的NbOx，基体为(FeCoNiPt) 2Nb的Laves相。
实施例6
用透射电镜对实施例3制备得到的纳米多孔电极进行微观结构表征，图6为Fe 37Co 20Ni 20Nb 20Ir 3脱合金后的透射表征结果，可以观察到该电极具有独特的两层纳米结构，即外层为非晶态多组元的氧化物((FeCoNiNbIr)Ox)，中间层为非晶态的NbOx，基体为(FeCoNiIr) 2Nb的Laves相。a为能谱线扫结果，b为能谱面扫结果。
实施例7
我们分别以实施例1中电化学脱合金化后的Fe 40-xCo 20Ni 20Nb 20Pt x(x=0, 3 at%)多孔电极作为工作电极，石墨电极为辅助电极，Hg/HgO标准电极为参比电极构成三电极体系，在海水模拟液中（1 mol L -1 KOH+0.5 mol L -1NaCL）中进行线性伏安扫描，扫描速度为2 mV/s -1。
图7所示为多孔电极材料在换算成标准氢电极电位后的极化曲线，添加少量的贵金属后电极材料的电解海水析氢性能有了大幅度的提高和500 mA cm -2电流密度下对应的过电位从429 mV降低到178 mV。
实施例8
我们以实施例1中电化学脱合金化后的Fe 40Co 20Ni 20Nb 20多孔电极作为工作电极，石墨电极为辅助电极，Hg/HgO标准电极为参比电极构成三电极体系，在海水模拟液中（1 mol L -1KOH+0.5 mol L -1 NaCL）中进行线性伏安扫描，扫描速度为2 mV s -1，同时采用计时电位法进行稳定性测试。
图8a所示为多孔电极材料在换算成标准氢电极电位后的极化曲线，在工业电流密度下 500 mA cm -2对应的过电位仅为461 mV，低于氯离子的氧化电位，从而很好的避免了氯离子的氧化和OER的竞争。
图9所是为多孔电极材料在工业电流密度下（500 mA cm -2）的稳定性测试，可持续工作超1600 h具有非常优异抗的稳定性。
实施例9
采用Co 86Nb 14合金作为前驱体，以0.5 mol L -1的H 2SO 4水溶液作为腐蚀液，进行电化学脱合金化，12 h后取出，并依次用超纯水和无水酒精多次清洗，去除孔隙中残留化学物质，干燥后制备得到多孔电极材料。
图10所示为Co 86Nb 14合金电化学脱合金12h后的SEM图，可以观察形成了三维双连续的纳米通孔结构。
以上对所提供的一种多主元多孔合金及制备方法和用于电解海水的多孔电极，进行了详细介绍。以上实施例的说明只是用于帮助理解本申请的方法及其核心思想；同时，对于本领域的一般技术人员，依据本申请的思想，在具体实施方式及应用范围上均会有改变之处，综上所述，本说明书内容不应理解为对本申请的限制。
如在说明书及权利要求书当中使用了某些词汇来指称特定组件。本领域技术人员应可理解，硬件制造商可能会用不同名词来称呼同一个组件。本说明书及权利要求书并不以名称的差异来作为区分组件的方式，而是以组件在功能上的差异来作为区分的准则。如在通篇说明书及权利要求书当中所提及的“包含”、“包括”为一开放式用语，故应解释成“包含/包括但不限定于”。“大致”是指在可接收的误差范围内，本领域技术人员能够在一定误差范围内解决所述技术问题，基本达到所述技术效果。说明书后续描述为实施本申请的较佳实施方式，然所述描述乃以说明本申请的一般原则为目的，并非用以限定本申请的范围。本申请的保护范围当视所附权利要求书所界定者为准。
还需要说明的是，术语“包括”、“包含”或者其任何其他变体意在涵盖非排他性的包含，从而使得包括一系列要素的商品或者系统不仅包括那些要素，而且还包括没有明确列出的其他要素，或者是还包括为这种商品或者系统所固有的要素。在没有更多限制的情况下，由语句“包括一个……”限定的要素，并不排除在包括所述要素的商品或者系统中还存在另外的相同要素。
应当理解，本文中使用的术语“和/或”仅仅是一种描述关联对象的关联关系，表示可以存在三种关系，例如，A和/或B，可以表示：单独存在A，同时存在A和B，单独存在B这三种情况。另外，本文中字符“/”，一般表示前后关联对象是一种“或”的关系。
上述说明示出并描述了本申请的若干优选实施例，但如前所述，应当理解本申请并非局限于本文所披露的形式，不应看作是对其他实施例的排除，而可用于各种其他组合、修改和环境，并能够在本文所述申请构想范围内，通过上述教导或相关领域的技术或知识进行改动。而本领域人员所进行的改动和变化不脱离本申请的精神和范围，则都应在本申请所附权利要求书的保护范围内。

Claims (10)

  1. 一种多主元多孔合金，其特征在于，所述多主元多孔合金的化学表达式为：Fe aCo bNi cNb dTi eTa fHf gZr hM x，M为Pt、Ru、Ir、Cu中的一种或多种；其中，0＜a≤55 at%，0＜b≤55 at%，0＜c≤55 at%，0≤d≤55 at%，0≤e≤55 at%，0≤f≤55 at%，0≤g≤55 at%，0≤h≤55 at%，0≤x≤5 at%，且a+b+c+d+e+f+g+h+x =100 at%。
  2.  根据权利要求1所述的多主元多孔合金，其特征在于，所述多主元多孔合金的韧带为包含基体和基体外部为两层纳米结构。
  3.  根据权利要求2所述的多主元多孔合金，其特征在于，所述基体为金属间化合物，所述两层纳米结构为中间层和外层；中间层为非晶态的氧化物，外层为多主元氧化物。
  4. 根据权利要求3所述的多主元多孔合金，其特征在于，所述非晶态的氧化物为(NbTiHfZrTa)Oy，40≤y≤80 at%。
  5. 根据权利要求3所述的多主元多孔合金，其特征在于，所述多主元氧化物为(FeCoNiNbTiHfZrTaM)Oy ，40≤y≤80 at%。
  6. 一种如权利要求1-5任意一项所述的多主元多孔合金的制备方法，其特征在于，所述方法具体包括以下步骤：
    S1) 制备尺寸可控的前驱体合金；
    S2）将S1)制备得到前驱体合金置于酸性溶液中进行化学/电化学脱合金，去除活泼的相，保留耐蚀的相形成具有多孔结构的多主元多孔合金，多孔结构孔径为15-1000 nm。
  7. 根据权利要求6所述的制备方法，其特征在于，所述S1）的具体步骤为：
    S1.1)金属原料放入无水酒精中采用超声波的方式进行多次清洗，然后将金属原料取出，并根据设计的合金名义成分配比；
    S1.2）将称量好的金属原料采用真空电弧炉熔炼制备尺寸可控的前驱体合金。
  8. 根据权利要求6所述的制备方法，其特征在于，所述S2）中的化学/电化学脱合金采用的腐蚀液为0.001~2 mol/L的H 2SO 4、HNO 3或HCl溶液，腐蚀温度25-80℃，腐蚀时间为1-72 h。
  9.  一种用于电解海水的多孔电极，其特征在于，所述用于电解海水的多孔电极采用如权利要求6-8任意一项所述的制备方法得到多主元多孔合金制备得到。
  10.  根据权利要求9所述的用于电解海水的多孔电极，其特征在于，所述用于电解海水的多孔电极能够直接用于碱性海水电解槽电解水制氢。
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Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN104120325A (zh) * 2014-07-04 2014-10-29 北京科技大学 低热膨胀系数NaMxAlySiz高熵合金及制备方法
KR101684856B1 (ko) * 2016-01-29 2016-12-09 서울대학교 산학협력단 하이엔트로피 합금 폼 및 이의 제조방법
CN113061925A (zh) * 2021-03-22 2021-07-02 北京科技大学 一种多级孔高熵合金电解水催化剂的制备方法
CN114570386A (zh) * 2022-03-23 2022-06-03 华中科技大学 一种异构高熵合金催化剂及其制备方法和应用
CN114990563A (zh) * 2022-03-28 2022-09-02 北京科技大学 用于电解水电极的多孔高熵合金材料的制备方法和应用
CN115491562A (zh) * 2022-08-31 2022-12-20 北京科技大学 多主元多孔合金及制备方法和用于电解海水的多孔电极
JP2023028320A (ja) * 2021-08-19 2023-03-03 高知県公立大学法人 水分解触媒

Family Cites Families (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN114645176B (zh) * 2020-12-21 2024-04-09 武汉苏泊尔炊具有限公司 不粘材料及其制备方法、包含不粘材料的烹饪器具及其制备方法
CN114752956B (zh) * 2022-03-21 2024-05-24 天津大学 一种贵金属微量掺杂类异质结纳米多孔高熵合金电极及其制备方法和应用
CN114799206B (zh) * 2022-03-28 2023-08-08 北京科技大学 用于催化电极多级结构高熵合金材料的制备方法及应用

Patent Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN104120325A (zh) * 2014-07-04 2014-10-29 北京科技大学 低热膨胀系数NaMxAlySiz高熵合金及制备方法
KR101684856B1 (ko) * 2016-01-29 2016-12-09 서울대학교 산학협력단 하이엔트로피 합금 폼 및 이의 제조방법
CN113061925A (zh) * 2021-03-22 2021-07-02 北京科技大学 一种多级孔高熵合金电解水催化剂的制备方法
JP2023028320A (ja) * 2021-08-19 2023-03-03 高知県公立大学法人 水分解触媒
CN114570386A (zh) * 2022-03-23 2022-06-03 华中科技大学 一种异构高熵合金催化剂及其制备方法和应用
CN114990563A (zh) * 2022-03-28 2022-09-02 北京科技大学 用于电解水电极的多孔高熵合金材料的制备方法和应用
CN115323398A (zh) * 2022-03-28 2022-11-11 北京科技大学 用于电解水电极的多孔高熵合金材料的制备方法和应用
CN115491562A (zh) * 2022-08-31 2022-12-20 北京科技大学 多主元多孔合金及制备方法和用于电解海水的多孔电极

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