WO2021213338A1 - 一种具有多层级孔洞结构的磷化镍复合物及其制备方法和应用 - Google Patents

一种具有多层级孔洞结构的磷化镍复合物及其制备方法和应用 Download PDF

Info

Publication number
WO2021213338A1
WO2021213338A1 PCT/CN2021/088176 CN2021088176W WO2021213338A1 WO 2021213338 A1 WO2021213338 A1 WO 2021213338A1 CN 2021088176 W CN2021088176 W CN 2021088176W WO 2021213338 A1 WO2021213338 A1 WO 2021213338A1
Authority
WO
WIPO (PCT)
Prior art keywords
nickel
nickel phosphide
phosphide composite
metal foam
preparation
Prior art date
Application number
PCT/CN2021/088176
Other languages
English (en)
French (fr)
Inventor
张京涛
张珍
陈颖
Original Assignee
广东工业大学
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by 广东工业大学 filed Critical 广东工业大学
Publication of WO2021213338A1 publication Critical patent/WO2021213338A1/zh

Links

Images

Classifications

    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
    • B01J—CHEMICAL OR PHYSICAL PROCESSES, e.g. CATALYSIS OR COLLOID CHEMISTRY; THEIR RELEVANT APPARATUS
    • B01J27/00—Catalysts comprising the elements or compounds of halogens, sulfur, selenium, tellurium, phosphorus or nitrogen; Catalysts comprising carbon compounds
    • B01J27/14—Phosphorus; Compounds thereof
    • B01J27/185—Phosphorus; Compounds thereof with iron group metals or platinum group metals
    • B01J27/1853—Phosphorus; Compounds thereof with iron group metals or platinum group metals with iron, cobalt or nickel
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
    • B01J—CHEMICAL OR PHYSICAL PROCESSES, e.g. CATALYSIS OR COLLOID CHEMISTRY; THEIR RELEVANT APPARATUS
    • B01J35/00—Catalysts, in general, characterised by their form or physical properties
    • B01J35/60—Catalysts, in general, characterised by their form or physical properties characterised by their surface properties or porosity
    • B01J35/66—Pore distribution
    • B01J35/695—Pore distribution polymodal
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
    • B01J—CHEMICAL OR PHYSICAL PROCESSES, e.g. CATALYSIS OR COLLOID CHEMISTRY; THEIR RELEVANT APPARATUS
    • B01J37/00—Processes, in general, for preparing catalysts; Processes, in general, for activation of catalysts
    • B01J37/08—Heat treatment
    • B01J37/10—Heat treatment in the presence of water, e.g. steam
    • 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
    • C25B—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES FOR THE PRODUCTION OF COMPOUNDS OR NON-METALS; APPARATUS THEREFOR
    • C25B11/00—Electrodes; Manufacture thereof not otherwise provided for
    • C25B11/04—Electrodes; Manufacture thereof not otherwise provided for characterised by the material
    • C25B11/051—Electrodes formed of electrocatalysts on a substrate or carrier
    • C25B11/073—Electrodes formed of electrocatalysts on a substrate or carrier characterised by the electrocatalyst material
    • C25B11/091—Electrodes formed of electrocatalysts on a substrate or carrier characterised by the electrocatalyst material consisting of at least one catalytic element and at least one catalytic compound; consisting of two or more catalytic elements or catalytic compounds
    • 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

Definitions

  • the invention belongs to the technical field of electrocatalytic materials, and specifically relates to a nickel phosphide composite with a multi-level pore structure, and a preparation method and application thereof.
  • Hydrogen energy is an ideal high-quality clean energy. It has the advantages of abundant reserves, wide sources, and high energy density. It is known as the most promising secondary energy source in the 21st century. Hydrogen energy will play an important role in solving problems such as energy crisis, global warming and environmental pollution. It will also become a strategic choice for China to optimize the energy consumption structure and ensure the security of national energy supply.
  • hydrogen is mainly produced by methane steam reforming. This process not only produces a large amount of carbon dioxide, but also consumes non-renewable fossil fuels. In contrast, electrocatalytic water splitting to produce hydrogen represents a clean and sustainable method of hydrogen production.
  • electrocatalytic water splitting only requires 1.23V of voltage.
  • the actual voltage that needs to be loaded on the electrolytic cell reaches 1.8-2V, which greatly limits the electrolysis of aquatic products.
  • Wide application of hydrogen hydrogen produced by electrolysis of water can only meet 4% of the global hydrogen demand).
  • platinum-based precious metals are still the best hydrogen evolution electrocatalysts (low hydrogen evolution overpotential, high current density, excellent stability), but their scarcity and high cost limit their application in water electrolysis.
  • the development of non-platinum-based electrocatalysts with high hydrogen evolution performance, low cost, and a wide range of pH applications is an important prerequisite for the wide application of electrocatalytic water splitting to produce hydrogen, and it is also a hot topic in the current research frontier.
  • the purpose of the present invention is to overcome the scarcity and high cost of platinum-based precious metals as hydrogen evolution electrocatalysts in the prior art, and to provide a nickel phosphide composite with a multi-level pore structure.
  • the nickel phosphide composite provided by the present invention has a multi-level pore structure, in which the penetrating large pores are beneficial to the transfer of electrolyte and gas diffusion, and the macro pores and nano pores are beneficial to exposing more active sites and increasing the contact with the electrolyte. Speed up the reaction rate.
  • the nickel phosphide composite with multi-level pore structure can be used as a working electrode for electrochemical decomposition of water to produce hydrogen, and exhibits excellent hydrogen evolution performance at full pH, with low cost, excellent electrocatalytic hydrogen evolution performance and strong stability The advantages.
  • Another object of the present invention is to provide a method for preparing the above-mentioned nickel phosphide composite having a multi-level pore structure.
  • Another object of the present invention is to provide the application of the above-mentioned nickel phosphide composite having a multi-level pore structure.
  • the present invention adopts the following solutions:
  • a nickel phosphide composite with a multi-level pore structure comprising a metal foam framework and nickel phosphide composite micro-sheets covered on the surface of the metal foam framework; the metal foam framework is distributed with through-holes with an average pore diameter of 50-500 ⁇ m, The surface of the metal foam skeleton is distributed with 10-100 ⁇ m macropores; the nickel phosphide composite micro-sheets are distributed with nano-pores.
  • the nickel phosphide composite provided by the present invention has a multi-level pore structure, in which the penetrating large pores are beneficial to the transfer of electrolyte and gas diffusion, and the macro pores and nano pores are beneficial to exposing more active sites and increasing the contact with the electrolyte. Speed up the reaction rate.
  • the nickel phosphide composite with a multi-level pore structure can be used as a working electrode for electrochemically decomposing water to produce hydrogen, and exhibits excellent hydrogen evolution performance at full pH.
  • Its application method is as follows: 0.5 ⁇ 2mol/L potassium hydroxide aqueous solution, 0.1 ⁇ 1mol/L sulfuric acid aqueous solution and 0.05 ⁇ 0.2mol/L phosphate buffer as alkaline, acidic and neutral electrolytes, which have multiple levels
  • the porous nickel phosphide composite is used as the working electrode
  • the calibrated saturated calomel electrode is used as the reference electrode
  • the graphite rod electrode is the counter electrode
  • the test pressure is normal pressure
  • the test temperature is room temperature
  • the electrolysis is performed before the electrochemical performance test.
  • the average pore diameter can be selected within the range of 50-500 ⁇ m, which can realize the transfer of electrolyte and gas diffusion.
  • Ni 2 P, Ni 12 P 5 , NiP 2 , Ni 5 P 4 and the like Conventional nickel phosphide compositions in the art can be used in the present invention, such as Ni 2 P, Ni 12 P 5 , NiP 2 , Ni 5 P 4 and the like.
  • the large holes are formed by metal plating.
  • the nickel phosphide composite with a multi-level pore structure of the present application has a metal foam skeleton-metal plating layer-nickel phosphide composite micro-sheet structure.
  • the nickel phosphide composite microplate structure is distributed on the surface of the metal foam framework and the metal plating layer (including both the outer surface and the hole surface), and the surface of the phosphide composite microplate is distributed with nano-holes.
  • the nickel phosphide composite microplates are composed of Ni 2 P and Ni 12 P 5 .
  • the pore diameter of the nanopore is 60-600 nm.
  • the preparation method of the above-mentioned nickel phosphide composite includes the following steps:
  • S2 Immerse the metal foam obtained in S1 into the mixed solution of nickel source and organic amine, hydrothermally react at 80-120°C for 1-10h, wash and dry;
  • S3 The metal foam obtained by S2 is mixed with a phosphorus source, and kept at 250-400°C for 0.5-4h to obtain the nickel phosphide composite.
  • the S1 step is to electrochemically deposit metal and form macropores.
  • the thickness of the metal deposited under the current density of -0.5A ⁇ cm -2 ⁇ -2A ⁇ cm -2 and the time of 100 ⁇ 1000s is generally 500 ⁇ 1600 ⁇ m, and the deposited metal will form a pore size of 10 on the metal foam framework. ⁇ 100 ⁇ m large pores.
  • the current I j*Area, where j is the current density, and Area is the area of the metal foam of the working electrode.
  • step S2 nickel hydroxide is obtained through hydrothermal reaction.
  • step S3 nickel hydroxide and phosphorus source are calcined to obtain nickel phosphide composite microplates.
  • the preparation method provided by the invention has cheap and easily available raw materials, simple process, short preparation period, and high repeatability, and is suitable for mass preparation.
  • the metal foam in S1 further includes ultrasonic treatment before the constant current treatment.
  • the metal foam is ultrasonically cleaned with 1 mol/L hydrochloric acid, deionized water and absolute ethanol for 10 minutes, respectively.
  • S1 can choose the corresponding electrolyte and electrode.
  • a mixed solution of nickel chloride and ammonium chloride can be used as the electrolyte, specifically 0.05-0.3mol/L nickel chloride and 0.5-3mmol/L ammonium chloride; nickel flakes can be used As the counter electrode and reference electrode (nickel foam is the working electrode);
  • a mixed solution of copper sulfate and sulfuric acid can be used as the electrolyte, specifically 0.5-1mol/L copper sulfate and 0.05-0.1mol/L L sulfuric acid, copper foam is used as the working electrode, and the copper sheet is the counter electrode and reference electrode.
  • nickel sources and organic amines used in the hydrothermal reaction to form nickel hydroxide and organic amines can be used in the present invention, and the concentration control can also be selected according to conventional control conditions.
  • the nickel source in S2 is one or more of nickel nitrate, nickel sulfate or nickel chloride; the organic amine source is hexamethylenetetramine, diethylenetriamine or triethylene One or more of diamines.
  • the concentration of the nickel source in S2 is 0.1 to 0.2 mol/L; the concentration of the organic amine source is 0.2 to 0.4 mol/L, in terms of amino groups.
  • the phosphorus source in S3 is one or more of sodium hypophosphite or red phosphorus.
  • the reaction in S3 is carried out under an inert atmosphere, and the flow rate of the inert gas is 10 to 200 sccm.
  • the inert atmosphere is argon.
  • the temperature is increased in S3 at a temperature increase rate of 2-10°C ⁇ min -1.
  • the present invention has the following beneficial effects:
  • the nickel phosphide composite provided by the present invention has a multi-level pore structure, in which the penetrating large pores are beneficial to the transfer of electrolyte and gas diffusion, and the macro pores and nano pores are beneficial to exposing more active sites and increasing the contact with the electrolyte. Speed up the reaction rate.
  • the nickel phosphide composite with a multi-level pore structure can be used as a working electrode for electrochemically decomposing water to produce hydrogen, and exhibits excellent hydrogen evolution performance at full pH.
  • the preparation method provided by the invention has cheap and easily available raw materials, simple process, short preparation period, and high repeatability, and is suitable for mass preparation.
  • FIG. 1 is an X-ray diffraction diagram of a nickel phosphide composite with a multi-level pore structure provided in Example 1 of the present invention
  • Embodiment 2 is a scanning electron micrograph of a nickel phosphide composite with a multilayer hole structure provided by Embodiment 1 of the present invention
  • Fig. 3 is a linear sweep voltammetric curve of hydrogen evolution of a nickel phosphide compound with a multi-level pore structure provided in Example 1 of the present invention in alkaline, acidic and neutral electrolytes;
  • Example 4 is a graph showing the constant potential stability test curve of a nickel phosphide composite with a multi-level pore structure provided in Example 1 of the present invention in alkaline, acidic and neutral electrolytes.
  • This embodiment provides a nickel phosphide composite with a multi-level pore structure.
  • the preparation process is as follows.
  • the nickel foam (average pore diameter of 250 microns) was ultrasonically cleaned with 1 mol/L hydrochloric acid, deionized water, and ethanol for 10 minutes. Then prepare 30mL of a mixed solution of 0.1mol/L nickel chloride and 2mol/L ammonium chloride as the electrolyte, nickel sheets as the counter electrode and reference electrode, and the washed nickel foam as the working electrode, and the nickel foam is immersed in the electrolyte 1 cm 2 , in the two-electrode mode with a constant current program of -1A ⁇ cm -2 for 500 seconds, the resulting nickel foam was washed with deionized water and dried in a vacuum drying oven.
  • the above 4 pieces of dried nickel foam were immersed in 30mL of an aqueous solution prepared by dissolving 1mmol of nickel nitrate hexahydrate and 6mmol of hexamethylenetetramine in deionized water, and transferred to a polytetrafluoroethylene lining
  • the sample was encapsulated in a hydrothermal kettle and reacted hydrothermally at 100°C for 10 hours. After being naturally cooled to room temperature, the sample was taken out and rinsed with deionized water and dried in a vacuum drying oven.
  • the above hydrothermally treated and dried sample is placed in a quartz boat together with 0.8 g of sodium hypophosphite, and the quartz boat is pushed into the center of the tube furnace at a speed of 2°C ⁇ min -1 in an argon atmosphere with a flow rate of 100sccm Warm up to 300°C, keep it for 2h, cool to room temperature naturally, take out the sample, rinse with deionized water and dry it in a vacuum drying oven at 60°C for later use.
  • the sample is a nickel phosphide composite with a multi-level pore structure. .
  • the nickel foam (average pore diameter of 250 microns) was ultrasonically cleaned with 1 mol/L hydrochloric acid, deionized water, and ethanol for 10 minutes. Then prepare 30mL of a mixed solution of 0.1mol/L nickel chloride and 2mol/L ammonium chloride as the electrolyte, nickel sheets as the counter electrode and reference electrode, and the washed nickel foam as the working electrode, and the nickel foam is immersed in the electrolyte 1 cm 2 , in the two-electrode mode with a constant current program of -1A ⁇ cm -2 for 500 seconds, the resulting nickel foam was washed with deionized water and dried in a vacuum drying oven.
  • the above 4 pieces of dried nickel foam were immersed in 30mL of an aqueous solution prepared by dissolving 1mmol of nickel nitrate hexahydrate and 6mmol of hexamethylenetetramine in deionized water, and transferred to a polytetrafluoroethylene lining
  • the sample was encapsulated in a hydrothermal kettle and reacted hydrothermally at 100°C for 10 hours. After being naturally cooled to room temperature, the sample was taken out and rinsed with deionized water and dried in a vacuum drying oven.
  • the above hydrothermally treated and dried sample is placed in a quartz boat together with 0.8 g of sodium hypophosphite, and the quartz boat is pushed into the center of the tube furnace at a speed of 2°C ⁇ min -1 in an argon atmosphere with a flow rate of 100sccm Warm up to 400°C, keep it for 0.5h, cool to room temperature naturally, take out the sample, rinse with deionized water and dry it in a vacuum drying oven at 60°C for later use.
  • the sample is a nickel phosphide composite with multi-level pore structure. Things.
  • the nickel foam (average pore diameter of 250 microns) was ultrasonically cleaned with 1 mol/L hydrochloric acid, deionized water, and ethanol for 10 minutes. Then prepare 30mL of a mixed solution of 0.1mol/L nickel chloride and 2mol/L ammonium chloride as the electrolyte, nickel sheets as the counter electrode and reference electrode, and the washed nickel foam as the working electrode, and the nickel foam is immersed in the electrolyte 1 cm 2 , in the two-electrode mode with a constant current program of -1A ⁇ cm -2 for 500 seconds, the resulting nickel foam was washed with deionized water and dried in a vacuum drying oven.
  • the above 4 pieces of dried nickel foam were immersed in 30mL of an aqueous solution prepared by dissolving 1mmol of nickel nitrate hexahydrate and 6mmol of hexamethylenetetramine in deionized water, and transferred to a polytetrafluoroethylene lining
  • the sample was encapsulated in a hydrothermal kettle and reacted hydrothermally at 120°C for 6 hours. After it was naturally cooled to room temperature, the sample was taken out and rinsed with deionized water and dried in a vacuum drying oven.
  • the above hydrothermally treated and dried sample is placed in a quartz boat together with 0.8 g of sodium hypophosphite, and the quartz boat is pushed into the center of the tube furnace at a speed of 2°C ⁇ min -1 in an argon atmosphere with a flow rate of 100sccm Raise the temperature to 300°C, keep it for 2h, cool to room temperature naturally, take out the sample, rinse it with deionized water and dry it in a vacuum drying oven at 60°C for later use.
  • the sample is a nickel phosphide nanosheet with multi-level pore structure. Complex.
  • the copper foam (average pore diameter of 250 microns) was ultrasonically cleaned with 1 mol/L hydrochloric acid, deionized water, and ethanol for 10 minutes. Then prepare 30mL of a mixed solution of 0.5mol/L copper sulfate and 0.05mol/L sulfuric acid as the electrolyte, copper sheets as the counter electrode and reference electrode, and the washed copper foam as the working electrode.
  • the copper foam is immersed in the electrolyte for 1cm 2 , In the two-electrode mode with a constant current program of -1.5A ⁇ cm -2 for 100 seconds, the resulting copper foam was washed with deionized water and dried in a vacuum drying oven.
  • the above 4 pieces of dried copper foam were immersed in 30mL of an aqueous solution prepared by dissolving 1mmol of nickel nitrate hexahydrate and 6mmol of hexamethylenetetramine in deionized water, and transferred to a polytetrafluoroethylene lining
  • the sample was encapsulated in a hydrothermal kettle and reacted hydrothermally at 120°C for 6 hours. After it was naturally cooled to room temperature, the sample was taken out and rinsed with deionized water and dried in a vacuum drying oven.
  • the above hydrothermally treated and dried sample is placed in a quartz boat together with 0.8 g of sodium hypophosphite, and the quartz boat is pushed into the center of the tube furnace at a speed of 2°C ⁇ min -1 in an argon atmosphere with a flow rate of 100sccm Warm up to 250°C, keep it for 4h, cool to room temperature naturally, take out the sample, rinse with deionized water and dry it in a vacuum drying oven at 60°C for later use.
  • the sample is a nickel phosphide nanosheet with multi-level pore structure. Complex.
  • This comparative example provides a nickel phosphide composite.
  • the preparation process of the nickel phosphide composite is the same as in Example 1 except that the constant current program is not processed.
  • This comparative example provides a nickel foam treated by electrodeposition.
  • the preparation process is the same as in Example 1, except that the hydrothermal reaction and subsequent annealing treatment are not carried out.
  • the nickel phosphide composite having a multi-level pore structure prepared in Example 1 is taken as an example for characterization and performance testing.
  • Figure 1 is the X-ray diffraction pattern of the nickel phosphide composite with multi-level pore structure prepared in Example 1.
  • the diffraction pattern is identified as the nickel foam as the base material and the Ni 2 P uniformly supported on the surface of the nickel foam And Ni 12 P 5 diffraction peak composition.
  • the test scan step is 0.02° ⁇ s -1 , and the scan range is 35° ⁇ 75°.
  • FIG. 2 is a scanning electron microscope picture of the nickel phosphide composite having a multilayer hole structure prepared in Example 1 under different magnifications.
  • Figure 2a is a scanned image at 100 magnification. It can be seen that the nickel phosphide composite has a multi-level pore structure, including its base material nickel foam skeleton with an average size of 250 microns through-holes, and a wide surface of the nickel foam skeleton The size of the distribution is about 10-100 micrometers of macropores.
  • Figure 2b is a scanned image at 500 magnification. It can be further seen that the nickel foam skeleton of the nickel phosphide composite, whether inside or outside the macropores, is uniformly and widely loaded with flakes composed of flake particles. Clusters.
  • Figure 2c is a scanned image at a magnification of 20,000. It can be carefully observed that these flake clusters are composed of micro flakes with a size of 2 to 4 microns and a thickness of several tens of nanometers. The surface of these microplates is widely distributed with nano-holes with a size of tens to hundreds of nanometers.
  • the nickel phosphide composite has through macropores with an average size of 250 microns, which is conducive to electrolyte transfer and gas diffusion, and its 10-100 micron macropores and nano-pores are conducive to exposing more active sites and increasing interaction with electrolysis. Liquid contact speeds up the reaction rate.
  • the nickel phosphide composite with multi-level pore structure prepared in Example 1 was directly used as the working electrode, the corrected saturated calomel electrode was used as the reference electrode, and the graphite rod As a counter electrode, linear sweep voltammetry and potentiostat were used to test its electrocatalytic water decomposition performance in 1mol/L potassium hydroxide aqueous solution, 0.5mol/L sulfuric acid aqueous solution and 0.1mol/L phosphate buffer to produce hydrogen.
  • the above electrochemical test pressure is normal pressure and the test temperature is room temperature. Before the electrochemical performance test, high-purity hydrogen is blown into the electrolyte for half an hour, and hydrogen is blown in during the whole test to make the electrolyte in a hydrogen saturated state.
  • Figure 3 is a nickel phosphide composite with a multi-level pore structure prepared by the present invention and a comparative experimental sample as a working electrode in acidic (Figure 3a), alkaline ( Figure 3b) and neutral (Figure 3c) electrolytes
  • curve 1 uses platinum as the working electrode, saturated calomel electrode as the reference electrode, graphite rod as the counter electrode, 1mol/L potassium hydroxide saturated with hydrogen, 0.5mol/L sulfuric acid and 0.1mol/L phosphate buffer The liquid is electrolyte, the test temperature is room temperature, and the scanning speed is 5 millivolts per second. Hydrogen evolution linear scanning voltammetry curve under test conditions.
  • Curve 2 is that the nickel phosphide composite with multi-level pore structure prepared in Example 1 is used as the working electrode, the saturated calomel electrode is the reference electrode, the graphite rod is the counter electrode, and 1mol/L potassium hydroxide saturated with hydrogen, 0.5 mol/L sulfuric acid and 0.1mol/L phosphate buffer are electrolytes, the test temperature is room temperature, and the scanning speed is 5 millivolts per second. The linear scanning voltammetry curve of hydrogen evolution under the test conditions.
  • Curve 3 is based on the nickel phosphide composite prepared in Comparative Example 1 as the working electrode, the saturated calomel electrode as the reference electrode, the graphite rod as the counter electrode, 1mol/L potassium hydroxide saturated with hydrogen, 0.5mol/L sulfuric acid and The 0.1mol/L phosphate buffer is the electrolyte, the test temperature is room temperature, and the scanning speed is 5 millivolts per second. The linear scan voltammetry curve of hydrogen evolution under the test conditions.
  • Curve 4 uses the foamed nickel with multi-level pores prepared in Comparative Example 2 as the working electrode, saturated calomel electrode as the reference electrode, graphite rod as the counter electrode, 1mol/L potassium hydroxide saturated with hydrogen, 0.5mol/L Sulfuric acid and 0.1 mol/L phosphate buffer are electrolytes, the test temperature is room temperature, and the scanning speed is 5 millivolts per second. The linear scanning voltammetry curve of hydrogen evolution under the test conditions.
  • Curve 5 uses blank nickel foam as working electrode, saturated calomel electrode as reference electrode, graphite rod as counter electrode, 1mol/L potassium hydroxide saturated with hydrogen, 0.5mol/L sulfuric acid and 0.1mol/L phosphate buffer It is an electrolyte, the test temperature is room temperature, and the scanning speed is 5 millivolts per second. The linear scanning voltammetry curve of hydrogen evolution under the test conditions.
  • the current density of -10mA ⁇ cm -2 should be achieved in the acid electrolyte, the nickel phosphide composite with a multi-level pore structure, the sample (nickel phosphide composite) prepared in Comparative Example 1, and the The required potentials for the sample (nickel foam with multi-level pores), blank nickel foam, and platinum sheet prepared in proportion 2 are: -92mV, -141mV, -146mV, -352mV, -54mV; and in alkaline electrolyte
  • the required potentials for the above five samples are -154mV, -184mV, -223mV, -336mV, -164mV; in neutral electrolyte, they are: -132mV, -162mV , -203mV, -374mV, -302mV.
  • the potential value of the nickel phosphide compound with a multi-level pore structure is smaller (92mV), second only to the precious metal platinum (54mV) Its catalytic activity is also second only to platinum, and its required potential value is the smallest under alkaline and neutral conditions, and its catalytic activity even exceeds platinum, making it the best electrocatalyst among them.
  • the above analysis proves that the nickel phosphide composite with multi-level pore structure has excellent electrocatalytic activity for water decomposition and hydrogen evolution in a wide range of pH.
  • the nickel phosphide composite with multi-level pore structure can have excellent electrocatalytic water decomposition and hydrogen evolution activity in a wide range of pH.
  • Figure 4 shows the results of the nickel phosphide composite with multi-level pore structure prepared in Example 1 of the present invention in alkaline ( Figure 4a), acid ( Figure 4b) and neutral ( Figure 4c) electrolytes. Constant potential test curve diagram.
  • the test conditions are: three-electrode system, the nickel phosphide composite with multi-level pore structure prepared in Example 1 is the working electrode, the saturated calomel electrode is the reference electrode, the graphite rod is the counter electrode, and the hydrogen-saturated 1mol/L Potassium hydroxide, 0.5mol/L sulfuric acid and 0.1mol/L phosphate buffer are electrolytes, the test pressure is normal pressure, and the test temperature is room temperature.
  • the nickel phosphide composite with multi-level pore structure prepared in Example 1 is used as the working electrode when the constant potential is -150mV, -120mV and -150mV, respectively, in alkaline, acidic and neutral conditions.
  • the electrolysis was continued for 20 hours in the electrolyte, and the hydrogen evolution current density was maintained at 14mA ⁇ cm -2 , 15mA ⁇ cm -2 and 6mA ⁇ cm -2 respectively .
  • the nickel phosphide composite as an electrode has excellent stability in a wide range of pH applications.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Materials Engineering (AREA)
  • Organic Chemistry (AREA)
  • Engineering & Computer Science (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Metallurgy (AREA)
  • Electrochemistry (AREA)
  • Inorganic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Catalysts (AREA)
  • Electrodes For Compound Or Non-Metal Manufacture (AREA)
  • Electrolytic Production Of Non-Metals, Compounds, Apparatuses Therefor (AREA)

Abstract

本发明涉及一种具有多层级孔洞结构的磷化镍复合物及其制备方法和应用。该磷化镍复合物包括金属泡沫骨架和金属泡沫骨架表面覆盖的磷化镍复合物微米片；金属泡沫骨架间分布有平均孔径为50～500μm的贯穿大孔，金属泡沫骨架表面分布有10～100μm的大孔；磷化镍复合物微米片上分布有纳米孔洞。本发明提供的磷化镍复合物具有多层级孔洞结构，其中贯穿大孔有利于电解质的传递和气体扩散，大孔及纳米孔洞有利于暴露更多的活性位点并增加与电解液的接触，加快反应速率。该磷化镍复合物可以作为工作电极用于电化学分解水产氢，且在全pH下均展现出优异的析氢性能，具有低成本，电催化析氢性能优异和稳定性强的优点。

Description

一种具有多层级孔洞结构的磷化镍复合物及其制备方法和应用 技术领域
本发明属于电催化材料技术领域，具体涉及一种具有多层级孔洞结构的磷化镍复合物及其制备方法和应用。
技术背景
随着人类社会的进步，社会发展对能源的需求日益增加。目前，石油、煤炭、天然气等传统化石能源仍然是人类生存所依赖的主要能量来源。由于大量使用，这些化石能源不仅面临日益枯竭，同时带来了严重的环境污染，已经成为制约人类社会可持续发展的瓶颈。开发可以代替传统化石能源的绿色可再生能源成为解决能源与环境问题双重挑战，促进人类社会可持续发展的关键。
氢能(氢气)，是一种理想的优质清洁能源，具有储量丰富、来源广泛、能量密度高等优点，被誉为21世纪最具发展前景的二次能源。氢能在解决能源危机、全球变暖及环境污染等问题方面将发挥重要的作用，也将成为我国优化能源消费结构、保障国家能源供应安全的战略选择。目前，氢气主要通过甲烷蒸汽重整制取，该过程不仅产生大量的二氧化碳，而且还消耗不可再生的化石燃料。相比之下，电催化分解水制氢代表了一种清洁，可持续的氢气生产方法。
理论上，电催化分解水只需要1.23V的电压。在实际应用中，由于体系欧姆电阻、溶液电阻及电荷传递电阻的存在和催化剂自身较高的析氢/析氧过电位，使得实际需要加载在电解池上的电压达到1.8～2V，大大限制了电解水产氢的广泛应用(电解水产氢仅能满足全球4％的氢气需求)。为了降低电解水制氢的外加电能，提高电催化分解水的效率，除了优化电解池结构外，还需要开发具有高效产氢效率的电催化剂。目前，铂基贵金属仍然是最好的析氢电催化剂(低析氢过电位，高电流密度，优异的稳定性)，但其稀缺性和高成本限制了它们在水电解中的应用。开发具有高析氢性能、低成本，pH适用范围广的非铂基电催化剂是电催化分解水制氢广泛应用的一个重要前提，也是目前研究前沿的热点问题。
发明内容
本发明的目的在于克服现有技术中作为析氢电催化剂铂基贵金属存在稀缺、成本高的缺陷或不足，提供一种具有多层级孔洞结构的磷化镍复合物。本发明提供的磷化镍复合物具有多层级孔洞结构，其中贯穿大孔有利于电解质的传递和气体扩散，大孔及纳米孔洞有利于暴露更多的活性位点并增加与电解液的接触，加快反应速率。该具有多层级孔洞结构的磷化镍 复合物可以作为工作电极用于电化学分解水产氢，且在全pH下均展现出优异的析氢性能，具有低成本，电催化析氢性能优异和稳定性强的优点。
本发明的另一目的在于提供上述具有多层级孔洞结构的磷化镍复合物的制备方法。
本发明的另一目的在于提供上述具有多层级孔洞结构的磷化镍复合物的应用。
为实现本发明的目的，本发明采取如下方案：
一种具有多层级孔洞结构的磷化镍复合物，包括金属泡沫骨架和金属泡沫骨架表面覆盖的磷化镍复合物微米片；金属泡沫骨架间分布有平均孔径为50～500μm的贯穿大孔，金属泡沫骨架表面分布有10～100μm的大孔；磷化镍复合物微米片上分布有纳米孔洞。
本发明提供的磷化镍复合物具有多层级孔洞结构，其中贯穿大孔有利于电解质的传递和气体扩散，大孔及纳米孔洞有利于暴露更多的活性位点并增加与电解液的接触，加快反应速率。该具有多层级孔洞结构的磷化镍复合物可以作为工作电极用于电化学分解水产氢，且在全pH下均展现出优异的析氢性能。
其应用方法如下：0.5～2mol/L氢氧化钾水溶液，0.1～1mol/L硫酸水溶液及0.05～0.2mol/L磷酸盐缓冲液分别作为碱性，酸性和中性电解液，所述具有多层级孔洞结构的磷化镍复合物作为工作电极，校正过的饱和甘汞电极作为参比电极，石墨棒电极为对电极，测试压力为常压，测试温度为室温，在电化学性能测试前对电解液鼓入高纯氢气半小时，且在测试全程保持氢气鼓入；分别仅需-92mV，-154mV及-132mV即可在酸性电解液，碱性电解液及中性电解液中实现-10mA·cm -2的电流密度，并且在总长为20小时的稳定性测试中无明显衰减。
本领域常规的金属泡沫骨架均可用于本发明中，可通过购买得到。其平均孔径可在50～500μm内进行选取，可实现电解质的传递和气体扩散即可。
本领域常规的磷化镍组成均可用于本发明中，例如Ni 2P、Ni 12P 5、NiP 2、Ni 5P 4等。
优选地，所述大孔由金属镀层形成。
本领域常规的可电镀的金属均可形成电镀得到本申请中的大孔，例如镍、铜、钴、铁、锌等。
本申请的具有多层级孔洞结构的磷化镍复合物具有金属泡沫骨架—金属镀层—磷化镍复合物微米片结构。
磷化镍复合物微米片结构分布于金属泡沫骨架和金属镀层的表面(既包括外表面，也包括孔表面)，且磷化物复合物微米片表面分布着纳米孔洞。
优选地，所述磷化镍复合物微米片由Ni 2P和Ni 12P 5组成。
优选地，所述纳米孔洞的孔径为60～600nm。
上述磷化镍复合物的制备方法，包括如下步骤：
S1：对金属泡沫进行恒电流处理使其表面沉积上金属并形成大孔，所述恒电流处理的电流密度为-0.5A·cm -2～-2A·cm -2，处理时间为100～1000s；
S2：将S1得到的金属泡沫浸入至镍源和有机胺的混合溶液中，于80～120℃下水热反应1～10h，洗涤，干燥；
S3：将S2得到的金属泡沫与磷源混合，于250～400℃下保温0.5～4h，即得所述磷化镍复合物。
S1步骤通过电化学沉积金属并形成大孔。在电流密度为-0.5A·cm -2～-2A·cm -2，时间为100～1000s条件下沉积的金属厚度一般为500～1600μm，且沉积的金属将在金属泡沫骨架上形成孔径为10～100μm的大孔。具体的，恒电流处理时，电流I＝j*Area，其中j为电流密度，Area为工作电极金属泡沫的面积。
S2步骤通过水热反应得到氢氧化镍。
S3步骤通过氢氧化镍与磷源煅烧得到磷化镍复合物微米片。
本发明提供的制备方法原材料便宜易得，工艺简单，制备周期短，并且重复性高，适合大批量制备。
优选地，S1中所述金属泡沫在恒电流处理前还包括超声处理。
本领域常规的超声处理均可用于本发明中。
更为优选地，金属泡沫用1mol/L盐酸、去离子水和无水乙醇依次分别超声清洗10分钟。
根据沉积的金属不同，S1可选择相应的电解液和电极。例如，沉积镍金属时，可选用氯化镍和氯化铵的混合溶液作为电解液，具体可为0.05～0.3mol/L的氯化镍和0.5～3mmol/L氯化铵；可选用镍片作为对电极和参比电极(镍泡沫为工作电极)；沉积铜金属时，可选用硫酸铜和硫酸的混合溶液为电解液，具体可为0.5～1mol/L的硫酸铜和0.05～0.1mol/L硫酸，选用铜泡沫为工作电极，铜片为对电极和参比电极。
本领域常规的用于水热反应形成氢氧化镍的镍源和有机胺均可用于本发明中，浓度控制也可根据常规的控制条件进行选取。
优选地，S2中所述镍源为硝酸镍、硫酸镍或氯化镍中的一种或几种；所述有机胺源为六亚甲基四胺、二亚乙基三胺或三亚乙基二胺中的一种或几种。
优选地，S2中所述镍源的浓度为0.1～0.2mol/L；所述有机胺源的浓度为0.2～0.4mol/L，以氨基计。
优选地，S3中所述磷源为次磷酸钠或红磷中的一种或几种。
优选地，S3中所述反应在惰性气氛下进行，惰性气体的气流量为10～200sccm。
更为优选地，所述惰性气氛为氩气。
优选地，S3中以2～10℃·min -1的升温速率进行升温。
上述磷化镍复合物在全pH条件下电催化分解水产氢方面的应用也在本发明的保护范围内。
与现有技术相比，本发明具有如下有益效果：
本发明提供的磷化镍复合物具有多层级孔洞结构，其中贯穿大孔有利于电解质的传递和气体扩散，大孔及纳米孔洞有利于暴露更多的活性位点并增加与电解液的接触，加快反应速率。该具有多层级孔洞结构的磷化镍复合物可以作为工作电极用于电化学分解水产氢，且在全pH下均展现出优异的析氢性能。
本发明提供的制备方法原材料便宜易得，工艺简单，制备周期短，并且重复性高，适合大批量制备。
附图说明
图1为本发明实施例1提供的具有多层级孔洞结构的磷化镍复合物X射线衍射图；
图2为本发明实施例1提供的具有多层级孔洞结构的磷化镍复合物的扫描电镜图；
图3为本发明实施例1提供的具有多层级孔洞结构的磷化镍复合物在碱性，酸性及中性电解液中的析氢线性扫描伏安曲线；
图4为本发明实施例1提供的具有多层级孔洞结构的磷化镍复合物在碱性，酸性及中性电解液中的恒电位稳定性测试曲线图。
具体实施方式
下面结合实施例进一步阐述本发明。这些实施例仅用于说明本发明而不用于限制本发明的范围。下例实施例中未注明具体条件的实验方法，通常按照本领域常规条件或按照制造厂商建议的条件；所使用的原料、试剂等，如无特殊说明，均为可从常规市场等商业途径得到的原料和试剂。本领域的技术人员在本发明的基础上所做的任何非实质性的变化及替换均属于本发明所要求保护的范围。
实施例1
本实施例提供一种具有多层级孔洞结构的磷化镍复合物。其制备过程如下。
将镍泡沫(平均孔径为250微米)用1mol/L盐酸、去离子水、乙醇依次分别超声清洗10分钟。然后配制30mL 0.1mol/L氯化镍和2mol/L氯化铵的混合溶液作为电解液，镍片作为对电极和参比电极，洗净的镍泡沫作为工作电极，将镍泡沫没入电解液中1cm 2，在两电极模式下用-1A·cm -2的恒电流程序处理500秒，将所得的镍泡沫用去离子水清洗并在真空干燥箱中干燥。接着将以上4片干燥好的镍泡沫浸泡在30mL由1mmol六水合硝酸镍和6mmol 六亚甲基四胺溶解于去离子水配制而成的水溶液中，并转入到含有聚四氟乙烯内衬的水热釜中封装好，在100℃水热反应10小时，自然冷却到室温后，将样品取出用去离子水冲洗并在真空干燥箱中干燥。最后将以上水热处理并干燥好的样品与0.8克次磷酸钠一起置于石英舟中，将石英舟推入管式炉中央，在流速为100sccm氩气氛围中以2℃·min -1的速度升温到300℃，并保温2h，自然冷却到室温，取出样品用去离子水冲洗并置于60℃真空干燥箱中烘干待用，该样品即为具有多层级孔洞结构的磷化镍复合物。
实施例2
将镍泡沫(平均孔径为250微米)用1mol/L盐酸、去离子水、乙醇依次分别超声清洗10分钟。然后配制30mL 0.1mol/L氯化镍和2mol/L氯化铵的混合溶液作为电解液，镍片作为对电极和参比电极，洗净的镍泡沫作为工作电极，将镍泡沫没入电解液中1cm 2，在两电极模式下用-1A·cm -2的恒电流程序处理500秒，将所得的镍泡沫用去离子水清洗并在真空干燥箱中干燥。接着将以上4片干燥好的镍泡沫浸泡在30mL由1mmol六水合硝酸镍和6mmol六亚甲基四胺溶解于去离子水配制而成的水溶液中，并转入到含有聚四氟乙烯内衬的水热釜中封装好，在100℃水热反应10小时，自然冷却到室温后，将样品取出用去离子水冲洗并在真空干燥箱中干燥。最后将以上水热处理并干燥好的样品与0.8克次磷酸钠一起置于石英舟中，将石英舟推入管式炉中央，在流速为100sccm氩气氛围中以2℃·min -1的速度升温到400℃，并保温0.5h，自然冷却到室温，取出样品用去离子水冲洗并置于60℃真空干燥箱中烘干待用，该样品即为具有多层级孔洞结构的磷化镍复合物。
实施例3
将镍泡沫(平均孔径为250微米)用1mol/L盐酸、去离子水、乙醇依次分别超声清洗10分钟。然后配制30mL 0.1mol/L氯化镍和2mol/L氯化铵的混合溶液作为电解液，镍片作为对电极和参比电极，洗净的镍泡沫作为工作电极，将镍泡沫没入电解液中1cm 2，在两电极模式下用-1A·cm -2的恒电流程序处理500秒，将所得的镍泡沫用去离子水清洗并在真空干燥箱中干燥。接着将以上4片干燥好的镍泡沫浸泡在30mL由1mmol六水合硝酸镍和6mmol六亚甲基四胺溶解于去离子水配制而成的水溶液中，并转入到含有聚四氟乙烯内衬的水热釜中封装好，在120℃水热反应6小时，自然冷却到室温后，将样品取出用去离子水冲洗并在真空干燥箱中干燥。最后将以上水热处理并干燥好的样品与0.8克次磷酸钠一起置于石英舟中，将石英舟推入管式炉中央，在流速为100sccm氩气氛围中以2℃·min -1的速度升温到300℃，并保温2h，自然冷却到室温，取出样品用去离子水冲洗并置于60℃真空干燥箱中烘干待用，该样品即为具有多层级孔洞结构的磷化镍纳米片复合物。
实施例4
将铜泡沫(平均孔径为250微米)用1mol/L盐酸、去离子水、乙醇依次分别超声清洗10分钟。然后配制30mL 0.5mol/L硫酸铜和0.05mol/L硫酸的混合溶液作为电解液，铜片作为对电极和参比电极，洗净的铜泡沫作为工作电极，将铜泡沫没入电解液中1cm 2，在两电极模式下用-1.5A·cm -2的恒电流程序处理100秒，将所得的铜泡沫用去离子水清洗并在真空干燥箱中干燥。接着将以上4片干燥好的铜泡沫浸泡在30mL由1mmol六水合硝酸镍和6mmol六亚甲基四胺溶解于去离子水配制而成的水溶液中，并转入到含有聚四氟乙烯内衬的水热釜中封装好，在120℃水热反应6小时，自然冷却到室温后，将样品取出用去离子水冲洗并在真空干燥箱中干燥。最后将以上水热处理并干燥好的样品与0.8克次磷酸钠一起置于石英舟中，将石英舟推入管式炉中央，在流速为100sccm氩气氛围中以2℃·min -1的速度升温到250℃，并保温4h，自然冷却到室温，取出样品用去离子水冲洗并置于60℃真空干燥箱中烘干待用，该样品即为具有多层级孔洞结构的磷化镍纳米片复合物。
对比例1
本对比例提供一种磷化镍复合物，该磷化镍复合物的制备过程，除不进行恒电流程序处理外，其余均与实施例1一致。
对比例2
本对比例提供一种经电沉积处理的镍泡沫。其制备过程除不进行水热反应及后续的退火处理外，其余均与实施例1一致。
样品表征与性能测试
本发明以实施例1中制得的具有多层级孔洞结构的磷化镍复合物为例，进行表征和性能测试。
(1)样品表征
图1为实施例1所制得的具有多层级孔洞结构的磷化镍复合物X射线衍射图，经鉴定该衍射图谱由作为基底材料的镍泡沫，以及镍泡沫表面所均匀负载的Ni 2P和Ni 12P 5的衍射峰组成。该测试扫描步长为0.02°·s -1，扫描范围为35°～75°。
图2为实施例1所制得的具有多层级孔洞结构的磷化镍复合物不同倍数下的扫描电镜图片。其中图2a为100倍率下扫描图片，可以看出该磷化镍复合物拥有多层级的孔洞结构，包括其基底材料镍泡沫骨架间平均尺寸为250微米的贯穿大孔，以及镍泡沫骨架表面广泛分布的尺寸约为10～100微米的大孔。图2b为500倍率下扫描图片，可以进一步看出该磷化镍复合物的基底材料镍泡沫骨架上，不管是大孔内部还是外部，都均匀、广泛地负载着由片状颗粒组成的片状团簇。图2c为20000倍率下的扫描图片，可以仔细地观察到这些片状团簇由大小为2～4微米，厚度为几十纳米的微米片组成。这些微米片的表面广泛地分布着尺寸为几十～几百纳米的纳米孔洞。该磷化镍复合物所具有的平均尺寸为250微米的贯穿大孔有利于电解 质的传递和气体扩散，其10～100微米大孔及纳米孔洞有利于暴露更多的活性位点并增加与电解液的接触，加快反应速率。
(2)性能测试
使用Gamry1010E电化学工作站，在标准三电极体系下，将实施例1所制备的具有多层级孔洞结构的磷化镍复合物直接作为工作电极，校正过的饱和甘汞电极作为参比电极，石墨棒作为对电极，采用线性扫描伏安法及恒电位法测试其分别在1mol/L氢氧化钾水溶液，0.5mol/L硫酸水溶液及0.1mol/L磷酸盐缓冲液中的电催化分解水产氢性能。以上电化学测试压力为常压，测试温度为室温，在电化学性能测试前对电解液鼓入高纯氢气半小时，且在测试全程保持氢气鼓入使得电解液处于氢饱和状态。
同时，分别选用铂片和空白镍泡沫、对比例1和2制备得到的样品作为工作电极进行对比。
图3为本发明制得的具有多层级孔洞结构的磷化镍复合物以及对比实验样品作为工作电极分别在酸性(图3a)、碱性(图3b)及中性(图3c)电解液中所测的析氢线性扫描伏安曲线。其中：曲线1是以铂片为工作电极，饱和甘汞电极为参比电极，石墨棒为对电极，氢气饱和的1mol/L氢氧化钾，0.5mol/L硫酸及0.1mol/L磷酸盐缓冲液为电解液，测试温度为室温，扫描速度为5毫伏每秒测试条件下的析氢线性扫描伏安曲线。曲线2是实施例1所制的具有多层级孔洞结构的磷化镍复合物为工作电极，饱和甘汞电极为参比电极，石墨棒为对电极，氢气饱和的1mol/L氢氧化钾，0.5mol/L硫酸及0.1mol/L磷酸盐缓冲液为电解液，测试温度为室温，扫描速度为5毫伏每秒测试条件下的析氢线性扫描伏安曲线。曲线3是以对比例1制得的磷化镍复合物为工作电极，饱和甘汞电极为参比电极，石墨棒为对电极，氢气饱和的1mol/L氢氧化钾，0.5mol/L硫酸及0.1mol/L磷酸盐缓冲液为电解液，测试温度为室温，扫描速度为5毫伏每秒测试条件下的析氢线性扫描伏安曲线。曲线4是以对比例2制得的具有多层级孔洞的泡沫镍为工作电极，饱和甘汞电极为参比电极，石墨棒为对电极，氢气饱和的1mol/L氢氧化钾，0.5mol/L硫酸及0.1mol/L磷酸盐缓冲液为电解液，测试温度为室温，扫描速度为5毫伏每秒测试条件下的析氢线性扫描伏安曲线。曲线5是以空白镍泡沫为工作电极，饱和甘汞电极为参比电极，石墨棒为对电极，氢气饱和的1mol/L氢氧化钾，0.5mol/L硫酸及0.1mol/L磷酸盐缓冲液为电解液，测试温度为室温，扫描速度为5毫伏每秒测试条件下的析氢线性扫描伏安曲线。
由图3可知，在酸性电解液中要实现-10mA·cm -2的电流密度，具有多层级孔洞结构的磷化镍复合物、对比例1制得的样品(磷化镍复合物)、对比例2制得的样品(具有多层级孔洞的镍泡沫)、空白镍泡沫、铂片需要的电位分别为：-92mV、-141mV、-146mV、-352mV、 -54mV；而在碱性电解液中实现-10mA·cm -2的电流密度时以上五个样品所需电位分别为-154mV，-184mV、-223mV、-336mV、-164mV；在中性电解液中则分别为：-132mV、-162mV、-203mV、-374mV、-302mV。根据以上数据分析，我们可以发现无论在酸性电解液中，达到同样电流密度时具有多层级孔洞结构的磷化镍复合物所需的电位值较小(92mV)，仅次于贵金属铂(54mV)，催化活性也仅次于铂，而在碱性和中性条件下其所需电位值最小，催化活性甚至超过了铂，成为其中最优秀的电催化剂。以上分析证明了具有多层级孔洞结构的磷化镍复合物在广泛的pH中均具有优秀的电催化分解水析氢活性。
其优秀的电催化分解水析氢活性主要得益于其独特的多层级孔洞结构和高活性的磷化镍复合物；多层级孔洞的优势在于：其中贯穿大孔有利于电解质的传递和气体扩散，大孔及纳米孔洞有利于暴露更多的活性位点并增加与电解液的接触，加快反应速率；由Ni 2P和Ni 12P 5组成的磷化镍复合物由于Ni 2P和Ni 12P 5的协同作用而具有较高的本征活性。因此具有多层级孔洞结构的磷化镍复合物可以在广泛的pH中均具有优秀的电催化分解水析氢活性。
而图4为本发明实施例1制得的具有多层级孔洞结构的磷化镍复合物分别在碱性(图4a)、酸性(图4b)及中性(图4c)电解液中所测的恒电位测试曲线图。测试条件是：三电极体系，实施例1所制的具有多层级孔洞结构的磷化镍复合物为工作电极，饱和甘汞电极为参比电极，石墨棒为对电极，氢气饱和的1mol/L氢氧化钾，0.5mol/L硫酸及0.1mol/L磷酸盐缓冲液为电解液，测试压力为常压，测试温度为室温。从图4曲线结果可知，采用实施例1所制备的具有多层级孔洞结构的磷化镍复合物为工作电极在恒电位为-150mV、-120mV及-150mV时分别在碱性、酸性及中性电解液中持续电解20小时，析氢电流密度分别维持在14mA·cm -2、15mA·cm -2和6mA·cm -2左右没有明显衰减，证明了采用本发明所制备的具有多层级孔洞结构的磷化镍复合物作为电极在广泛的pH中应用均具有优秀的稳定性。
以上所述是本发明的特定示例实施方式，对于本领域的技术人员，在不脱离本发明的原理下，还可以做出若干的改进与修辞。事实上，本发明的范围由所附的权利要求及其等效限定。

Claims (10)

  1. 一种具有多层级孔洞结构的磷化镍复合物，其特征在于，包括金属泡沫骨架和金属泡沫骨架表面覆盖的磷化镍复合物微米片；金属泡沫骨架间分布有平均孔径为50～500μm的贯穿大孔，金属泡沫骨架表面分布有10～100μm的大孔；磷化镍复合物微米片上分布有纳米孔洞。
  2. 根据权利要求1所述磷化镍复合物，其特征在于，所述金属泡沫骨架为镍泡沫骨架、铜泡沫骨架、钴泡沫骨架或铁泡沫骨架。
  3. 根据权利要求1所述磷化镍复合物，其特征在于，所述大孔由金属镀层形成；所述金属镀层为镍层、铜层、钴层或铁层。
  4. 根据权利要求1所述磷化镍复合物，其特征在于，所述所述磷化镍复合物微米片由Ni 2P和Ni 12P 5组成；所述纳米孔洞的孔径为60～600nm。
  5. 权利要求1～4任一所述磷化镍复合物的制备方法，其特征在于，包括如下步骤：
    S1：对金属泡沫进行恒电流处理使其表面沉积上金属并形成大孔，所述恒电流处理的电流密度为-0.5A·cm -2～-2A·cm -2；处理时间为100～1000s；
    S2：将S1得到的金属泡沫浸入至镍源和有机胺的混合溶液中，于80～120℃下水热反应1～10h，洗涤，干燥；
    S3：将S2得到的金属泡沫与磷源混合，于250～400℃下保温0.5～4h，即得所述磷化镍复合物。
  6. 根据权利要求5所述制备方法，其特征在于，S1中所述金属泡沫在恒电流处理前还包括超声处理。
  7. 根据权利要求5所述制备方法，其特征在于，S2中所述镍源为硝酸镍、硫酸镍或氯化镍中的一种或几种；所述有机胺源为六亚甲基四胺、二亚乙基三胺或三亚乙基二胺中的一种或几种。
  8. 根据权利要求5所述制备方法，其特征在于，S3中所述磷源为次磷酸钠或红磷中的一种或几种。
  9. 根据权利要求5所述制备方法，其特征在于，S3中所述反应在惰性气氛下进行，惰性气体的气流量为10～200sccm；S3中以2～10℃·min -1的升温速率进行升温。
  10. 权利要求1～4任一所述磷化镍复合物在全pH条件下电催化分解水产氢方面的应用。
PCT/CN2021/088176 2020-04-22 2021-04-19 一种具有多层级孔洞结构的磷化镍复合物及其制备方法和应用 WO2021213338A1 (zh)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN202010323346.0 2020-04-22
CN202010323346.0A CN111575729B (zh) 2020-04-22 2020-04-22 一种具有多层级孔洞结构的磷化镍复合物及其制备方法和应用

Publications (1)

Publication Number Publication Date
WO2021213338A1 true WO2021213338A1 (zh) 2021-10-28

Family

ID=72114077

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2021/088176 WO2021213338A1 (zh) 2020-04-22 2021-04-19 一种具有多层级孔洞结构的磷化镍复合物及其制备方法和应用

Country Status (2)

Country Link
CN (1) CN111575729B (zh)
WO (1) WO2021213338A1 (zh)

Cited By (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113862726A (zh) * 2021-11-18 2021-12-31 吉林大学 一种钼硒双元素掺杂的多孔片层状磷化镍材料的制备方法及应用
CN114093678A (zh) * 2021-11-24 2022-02-25 滨州学院 一种过渡金属磷化物纳米片电极材料的制备方法
CN114289043A (zh) * 2020-09-22 2022-04-08 新疆大学 一种自支撑多孔纳米板钴镍磷化物催化剂制备方法及应用
CN114618539A (zh) * 2022-02-23 2022-06-14 燕山大学 一种分级结构硼氢化钠产氢催化剂及其制备方法和应用
CN114717601A (zh) * 2022-05-17 2022-07-08 临沂大学 三相界面复合的集成式碱水电解制氢电极及其制备方法
CN114808012A (zh) * 2022-04-19 2022-07-29 湖南师范大学 一种磷化物/二元金属氮化物纳米多孔异质结电催化剂及其制备方法和应用
CN115010220A (zh) * 2022-06-17 2022-09-06 南通大学 一种磷化物协同氢氧化物异质结构的电极及其制备方法
CN115094460A (zh) * 2022-07-19 2022-09-23 同济大学 一种碱性电解槽用镍基复合电极及其制备方法
CN115845855A (zh) * 2022-12-09 2023-03-28 上海氯碱化工股份有限公司 用于氯化氢催化制氯的耐氟化氢催化剂及其制备方法
CN115976538A (zh) * 2022-12-12 2023-04-18 青岛农业大学 一种磷掺杂金属镍@铁氧化物异质多级结构复合物、其制备方法及应用
CN116273124A (zh) * 2023-03-22 2023-06-23 陕西科技大学 一种Ni-Ni2P-Ni5P4/g-C3N4光催化剂及其制备方法和应用
WO2024124971A1 (zh) * 2022-12-15 2024-06-20 中国科学院大连化学物理研究所 一种整体式镍铁磷化物多孔电极及其制备方法

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111575729B (zh) * 2020-04-22 2021-01-15 广东工业大学 一种具有多层级孔洞结构的磷化镍复合物及其制备方法和应用
CN113502499A (zh) * 2021-07-14 2021-10-15 大连理工大学 一类自支撑金属磷化物纳微结构电极材料及其制备方法和应用
CN114164448B (zh) * 2021-10-31 2022-12-16 吉林大学 一种异相磷化镍材料及其制备方法
CN114990624B (zh) * 2022-06-14 2023-08-22 陕西科技大学 一种三维花状锌掺杂的Ni2P/Ni12P5异质结自支撑电催化剂材料的制备方法
CN115261917A (zh) * 2022-07-01 2022-11-01 中国科学院大连化学物理研究所 一维Ni12P5/Ni2P多晶异质结构高效水氧化催化剂的制备方法

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN106807416A (zh) * 2017-01-12 2017-06-09 南开大学 一种电催化分解水制氢的自支撑磷化镍纳米片材料及其制备方法
CN107694584A (zh) * 2017-10-15 2018-02-16 华东师范大学 一种自支撑磷化镍催化剂及其制备方法和应用
WO2019241717A1 (en) * 2018-06-15 2019-12-19 University Of Houston System HIERARCHICAL METAL PHOSPHIDE-SANDWICHED Ni5P4-BASED MICROSHEET ARRAYS AS ROBUST PH-UNIVERSAL ELECTROCATALYSTS FOR EFFICIENT HYDROGEN GENERATION
CN111575729A (zh) * 2020-04-22 2020-08-25 广东工业大学 一种具有多层级孔洞结构的磷化镍复合物及其制备方法和应用

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3075885A1 (en) * 2015-03-31 2016-10-05 International Iberian Nanotechnology Laboratory Method for manufacturing of a porous electrode material
CN105720236B (zh) * 2016-03-27 2018-06-22 华南理工大学 一种钠离子电池负极用泡沫镍自支撑片状Ni3P/C复合材料及其制备方法
CN105854911A (zh) * 2016-06-23 2016-08-17 中国石油大学(华东) 一种用于析氢/析氧双功能的微米磷化镍电催化材料及其制备方法
CN107749350B (zh) * 2017-10-18 2019-05-14 德清鼎兴电子有限公司 一种超级电容铜镍复合电极及其制备工艺
CN110055552B (zh) * 2019-05-15 2020-09-25 宁波大学 一种高效氮化镍析氢电极制备方法
CN110484934B (zh) * 2019-09-02 2021-06-08 燕山大学 镍磷/磷化镍-碳布三维自支撑析氢电极材料的制备方法
CN110644016B (zh) * 2019-09-16 2021-08-20 燕山大学 水电解离析氢用磷化镍-碳布自支撑电极的制备方法
CN110512228B (zh) * 2019-09-16 2021-06-22 燕山大学 一种磷化镍/泡沫镍电化学功能析氢材料的制备方法

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN106807416A (zh) * 2017-01-12 2017-06-09 南开大学 一种电催化分解水制氢的自支撑磷化镍纳米片材料及其制备方法
CN107694584A (zh) * 2017-10-15 2018-02-16 华东师范大学 一种自支撑磷化镍催化剂及其制备方法和应用
WO2019241717A1 (en) * 2018-06-15 2019-12-19 University Of Houston System HIERARCHICAL METAL PHOSPHIDE-SANDWICHED Ni5P4-BASED MICROSHEET ARRAYS AS ROBUST PH-UNIVERSAL ELECTROCATALYSTS FOR EFFICIENT HYDROGEN GENERATION
CN111575729A (zh) * 2020-04-22 2020-08-25 广东工业大学 一种具有多层级孔洞结构的磷化镍复合物及其制备方法和应用

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
MENEZES PRASHANTH W., INDRA ARINDAM, DAS CHITTARANJAN, WALTER CARSTEN, GÖBEL CAREN, GUTKIN VITALY, SCHMEIΒER DIETER, DRIESS MATTHI: "Uncovering the Nature of Active Species of Nickel Phosphide Catalysts in High-Performance Electrochemical Overall Water Splitting", ACS CATALYSIS, vol. 7, no. 1, 6 January 2017 (2017-01-06), US , pages 103 - 109, XP055860024, ISSN: 2155-5435, DOI: 10.1021/acscatal.6b02666 *
ZHANG JINGTAO; ZHANG ZHEN; JI YONGFEI; YANG JINDONG; FAN KE; MA XINZHOU; WANG CHAO; SHU RIYANG; CHEN YING: "Surface engineering induced hierarchical porous Ni12P5-Ni2P polymorphs catalyst for efficient wide pH hydrogen production", APPLIED CATALYSIS B. ENVIRONMENTAL, vol. 282, 6 October 2020 (2020-10-06), AMSTERDAM, NL , XP086354617, ISSN: 0926-3373, DOI: 10.1016/j.apcatb.2020.119609 *

Cited By (22)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN114289043A (zh) * 2020-09-22 2022-04-08 新疆大学 一种自支撑多孔纳米板钴镍磷化物催化剂制备方法及应用
CN114289043B (zh) * 2020-09-22 2024-08-30 新疆大学 一种自支撑多孔纳米板钴镍磷化物催化剂制备方法及应用
CN113862726B (zh) * 2021-11-18 2022-09-27 吉林大学 一种钼硒双元素掺杂的多孔片层状磷化镍材料的制备方法及应用
CN113862726A (zh) * 2021-11-18 2021-12-31 吉林大学 一种钼硒双元素掺杂的多孔片层状磷化镍材料的制备方法及应用
CN114093678A (zh) * 2021-11-24 2022-02-25 滨州学院 一种过渡金属磷化物纳米片电极材料的制备方法
CN114093678B (zh) * 2021-11-24 2023-07-14 滨州学院 一种过渡金属磷化物纳米片电极材料的制备方法
CN114618539A (zh) * 2022-02-23 2022-06-14 燕山大学 一种分级结构硼氢化钠产氢催化剂及其制备方法和应用
CN114808012B (zh) * 2022-04-19 2023-12-22 湖南师范大学 一种磷化物/二元金属氮化物纳米多孔异质结电催化剂及其制备方法和应用
CN114808012A (zh) * 2022-04-19 2022-07-29 湖南师范大学 一种磷化物/二元金属氮化物纳米多孔异质结电催化剂及其制备方法和应用
CN114717601A (zh) * 2022-05-17 2022-07-08 临沂大学 三相界面复合的集成式碱水电解制氢电极及其制备方法
CN114717601B (zh) * 2022-05-17 2024-01-30 临沂大学 三相界面复合的集成式碱水电解制氢电极及其制备方法
CN115010220A (zh) * 2022-06-17 2022-09-06 南通大学 一种磷化物协同氢氧化物异质结构的电极及其制备方法
CN115010220B (zh) * 2022-06-17 2023-12-01 南通大学 一种磷化物协同氢氧化物异质结构的电极及其制备方法
CN115094460A (zh) * 2022-07-19 2022-09-23 同济大学 一种碱性电解槽用镍基复合电极及其制备方法
CN115094460B (zh) * 2022-07-19 2023-08-29 同济大学 一种碱性电解槽用镍基复合电极及其制备方法
CN115845855B (zh) * 2022-12-09 2024-05-28 上海氯碱化工股份有限公司 用于氯化氢催化制氯的耐氟化氢催化剂及其制备方法
CN115845855A (zh) * 2022-12-09 2023-03-28 上海氯碱化工股份有限公司 用于氯化氢催化制氯的耐氟化氢催化剂及其制备方法
CN115976538A (zh) * 2022-12-12 2023-04-18 青岛农业大学 一种磷掺杂金属镍@铁氧化物异质多级结构复合物、其制备方法及应用
CN115976538B (zh) * 2022-12-12 2024-05-31 青岛农业大学 一种磷掺杂金属镍@铁氧化物异质多级结构复合物、其制备方法及应用
WO2024124971A1 (zh) * 2022-12-15 2024-06-20 中国科学院大连化学物理研究所 一种整体式镍铁磷化物多孔电极及其制备方法
CN116273124A (zh) * 2023-03-22 2023-06-23 陕西科技大学 一种Ni-Ni2P-Ni5P4/g-C3N4光催化剂及其制备方法和应用
CN116273124B (zh) * 2023-03-22 2024-06-07 陕西科技大学 一种Ni-Ni2P-Ni5P4/g-C3N4光催化剂及其制备方法和应用

Also Published As

Publication number Publication date
CN111575729B (zh) 2021-01-15
CN111575729A (zh) 2020-08-25

Similar Documents

Publication Publication Date Title
WO2021213338A1 (zh) 一种具有多层级孔洞结构的磷化镍复合物及其制备方法和应用
CN110201670B (zh) 基于三氯化铁/尿素低共熔溶剂的镍铁双金属氢氧化物/泡沫镍催化剂、其制备方法及应用
CN107051568B (zh) 一种析氧Fe掺杂二硒化钴@N-CT复合催化剂及其制备方法和应用
CN107785181A (zh) 一种超级电容器电极材料及其制备方法
CN112044458A (zh) 一种多层级金属磷化物及其制备方法和应用
CN106757143A (zh) 一种水分解反应用催化电极及其制备方法
CN103422116A (zh) 一种多孔镍基钌氧化物复合析氢电极的制备方法
CN110129825B (zh) 一种高效Ni/Ni(OH)2析氢电极及其制备方法
CN108823591B (zh) 一种镍铁联硒化合物及其制备方法和应用
CN104332324B (zh) 多孔金属镍及其表面镍基氧化物多孔薄膜超级电容电极材料的制备方法
CN108376617B (zh) 一种纳米多孔氢氧化镍薄膜的电化学制备方法及其应用
Ming et al. Facile growth of transition metal hydroxide nanosheets on porous nickel foam for efficient electrooxidation of benzyl alcohol
CN110965076A (zh) 一种双功能三维分层核壳结构电解水电极的制备方法
CN106222694B (zh) 海绵结构合金负载三元氧化物层析氢电极材料的制备方法
CN107833758B (zh) 一种镍基一体化电极的制备方法及应用
CN113136597B (zh) 一种铜锡复合材料及其制备方法和应用
CN102864464A (zh) 一种高催化活性和高稳定性析氢电极的制备方法
CN110592616A (zh) 一种电镀法制备铂/二氧化钛纳米管复合电极的方法
CN114959768B (zh) 一种镍基析氧电极、其制备方法及应用
CN110644016A (zh) 水电解离析氢用磷化镍-碳布自支撑电极的制备方法
CN107803212B (zh) 一种富缺陷Fe2O3-FeF2纳米多孔薄膜、制备方法及其应用
CN110699701B (zh) 一种负载金属镍和三氧化二钒复合物的泡沫镍及其制备方法和应用
CN108707924B (zh) 硒化钌纳米粒子修饰TiO2纳米管阵列的析氢电催化剂、制备方法及应用
Ji et al. Controlled synthesis of CeOx-NiCo2O4 nanocomposite with 3D umbrella-shaped hierarchical structure: A sharp-tip enhanced electrocatalyst for efficient oxygen evolution reaction over a broad pH region
CN108274014B (zh) 一种具有多重分枝状的纳米合金及其制备方法

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 21792304

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 21792304

Country of ref document: EP

Kind code of ref document: A1