A porous intermetallic compound material and a method for preparing the same

Abstract

The application discloses a kind of porous intermetallic compound materials, the chemical formula of the material is Ni (1‑2) M, the M includes one of Mg, Zn, the Ni is nickel element, the Mg is magnesium element, the Zn is zinc element, the element in the chemical formula of the material satisfies charge balance;The material has double continuous open pore structure.The structure of the material obtained in the application is arranged in ordered lattice point array, active site distribution is more uniform, and geometric effect is enhanced;Bonding mode tends to covalent bond, electron localization is shared, and electronic effect is enhanced;Unique double continuous open pore structure, high electrical conductivity and thermal conductivity, large specific surface area and high catalytic activity and the like characteristics.

Description

TECHNICAL FIELD

[0001] The present application relates to the technical field of materials, in particular to a porous intermetallic compound material and a preparation method thereof. BACKGROUND

[0002] Transition metal nickel-based materials have the advantages of high abundance, high strength, high catalytic activity, good stability, etc., and are widely used in catalysis, energy storage, magnetism, aerospace, etc. In the prior art, transition metal nickel-based materials are often prepared into solid solutions with chemical disorder structure and intermetallic compounds with chemical order structure. Intermetallic compounds have high melting point, good wear resistance, oxidation resistance and corrosion resistance, etc. due to the fact that they have both covalent bonds and metallic bonds. Some researchers prepared transition metal nickel into intermetallic compounds, which can improve the catalytic ability to some extent, but the effect is still not significant. Therefore, it is an urgent need in the market to develop an intermetallic compound material with high catalytic performance and stable structure. SUMMARY

[0003] The present application discloses a porous intermetallic compound material, which has a unique bicontinuous open pore structure, and the structure of the material is arranged in an ordered lattice array, so that the active sites are more uniformly distributed and the catalytic activity is higher.

[0004] The present application is achieved by the following technical solutions:

[0005] The porous intermetallic compound material provided by the present application has a chemical formula of Ni (1-2) M, wherein M includes one of Mg and Zn, Ni is a nickel element, Mg is a magnesium element, and Zn is a zinc element, and the elements in the chemical formula of the intermetallic compound material satisfy charge balance; and the intermetallic compound material has a bicontinuous open pore structure.

[0006] The Ni-Mg and Ni-Zn intermetallic compound materials of the present application have a unique bicontinuous open pore structure, which is beneficial to improve the specific surface area of the catalyst and significantly improve the electrical conductivity, thermal conductivity, catalytic activity, etc. of the catalyst.

[0007] As a further solution, the intermetallic compound material also has a chemically ordered lattice array structure. The structure is arranged in an ordered lattice array, so that the active sites are more uniformly distributed, the geometric effect is enhanced, the bonding mode is more inclined to covalent bond, the electron localization is shared, and the electronic effect is enhanced, which is beneficial to further improve the catalytic performance of the material.

[0008] As a further solution, the average pore size of the bicontinuous open pore structure is 30 nm-3 μm.

[0009] As a further solution, the chemical formula of the intermetallic compound material is MgNi2, the average pore size of the bicontinuous open pore structure of the MgNi2 is 30 nm-500 nm, and the chemically ordered lattice point array structure of the MgNi2 is a hexagonal structure.

[0010] As a further solution, the chemical formula of the intermetallic compound material is β1-NiZn, the average pore size of the bicontinuous open pore structure of the β1-NiZn is 200 nm-500 nm, and the chemically ordered lattice point array structure of the β1-NiZn is a tetragonal structure.

[0011] As a further solution, the MgNi2 has characteristic XRD diffraction peaks of 22.49°, 44.01°, 44.93°, 45.91°, 71.96°, and 79.57°.

[0012] As a further solution, the β1-NiZn has characteristic XRD diffraction peaks of 43.22°, 46.60°, 57.28°, 68.02°, 76.85°, and 84.09°.

[0013] As a further solution, the intermetallic compound Ni (1-2) The molar ratio of Ni and M in the alloy precursor of M is (10-70):(30-90).

[0014] The present application also provides a preparation method of the intermetallic compound material, and the method is selected from I solution or II solution:

[0015] I solution: the alloy precursor of the intermetallic compound is placed in a closed environment for treatment, the closed environment includes one of a vacuum environment, an inert atmosphere environment, and a reducing atmosphere environment, and the treatment conditions include a pressure of 5×10 -5 Pa-500 Pa, a temperature of 300℃-550℃, a heating rate of 10℃ / min-50℃ / min, and a treatment time of 0.5h-5h;

[0016] II solution: the alloy precursor of the intermetallic compound and the alkali metal are placed in a closed container with an argon atmosphere, and then the container with the alloy precursor of the intermetallic compound and the alkali metal is transferred as a whole into an environment with an inert atmosphere or a reducing atmosphere, and then treated at a pressure of 50 Pa-500 Pa, a temperature of 200℃-400℃, and a heating rate of 10℃ / min-50℃ / min for 0.2h-3h; and then soaked after cooling to remove M and the alkali metal to form a porous structure.

[0017] In the preparation method of the present application, the temperature, pressure, heating rate and treatment time in the control method can obtain a uniform distribution of the bicontinuous open pore structure, and the degree of corrosion and phase change process can be controlled by selective corrosion of the nickel-based alloy precursor, so as to adjust the crystal system structure of the obtained material; thereby successfully preparing a porous intermetallic compound with large specific surface area, high electrical conductivity, high mechanical strength, high stability and controllable structure.

[0018] As a further scheme, the preparation method of the alloy precursor of the intermetallic compound in the I scheme and the II scheme comprises weighing the metal Ni and the metal M according to the molar ratio of Ni and M in the alloy precursor of the intermetallic compound, and melting to obtain the alloy precursor of the intermetallic compound in an inert atmosphere or a reducing atmosphere.

[0019] As a further scheme, the inert atmosphere comprises one or more of argon, nitrogen, helium, neon, krypton and xenon; and the reducing atmosphere comprises a mixed atmosphere of the inert atmosphere and hydrogen, wherein the volume fraction of hydrogen is greater than 0% and less than 50%.

[0020] As a further scheme, the alkali metal comprises one or more of lithium, sodium and potassium.

[0021] As a further scheme, the soaking treatment in the II scheme comprises soaking with water or an acid solution, the soaking time of the water is 1h-24h; and the soaking time of the acid solution is 1h-24h, so as to remove the element M and the alkali metal in the pore structure.

[0022] As a further scheme, the acid solution comprises (NH4)2SO4, and the concentration of the acid solution is 0.8M-1.2M.

[0023] The present application also provides applications of the porous intermetallic compound material as a catalyst in the hydrogen evolution reaction of water electrolysis and as an electrode active material in lithium primary batteries, sodium primary batteries, potassium primary batteries, magnesium primary batteries, zinc primary batteries, copper primary batteries, aluminum primary batteries, calcium primary batteries, zinc primary batteries, lithium secondary batteries, sodium secondary batteries, potassium secondary batteries, magnesium secondary batteries, zinc secondary batteries, copper secondary batteries, aluminum secondary batteries, calcium secondary batteries and zinc secondary batteries.

[0024] The present application also provides applications of the intermetallic compound material β1-NiZn and the intermetallic compound material MgNi2 as a catalyst in the hydrogen evolution reaction of water electrolysis and as a negative electrode active material in lithium secondary batteries.

[0025] The present application has the following characteristics and advantages:

[0026] (1) The intermetallic compound material of the present application has ordered lattice point array structure, more uniform active site distribution, enhanced geometric effect, covalent bond tendency, electron localization sharing, enhanced electronic effect, unique double-continuous open pore structure, high electrical conductivity and thermal conductivity, large specific surface area and high catalytic activity.

[0027] (2) The porous MgNi2 and β1-NiZn intermetallic compound materials can significantly improve the battery performance and catalytic reaction rate when applied to lithium batteries and hydrogen evolution catalytic reactions.

[0028] (3) The method of the present application can realize large-scale and uniform production. BRIEF DESCRIPTION OF DRAWINGS

[0029] In order to more clearly illustrate the porous intermetallic compound material in the embodiments of the present application, the drawings required to be used in the embodiments or prior art description will be briefly introduced below. Obviously, the drawings in the following description are only some embodiments of the present application.

[0030] Figure 1 The scanning electron microscope images of the porous MgNi2 intermetallic compound in Example 1 of the present application and the porous Ni in Comparative Example 1; wherein Figure 1 a is Example 1, Figure 1 b is Comparative Example 1.

[0031] Figure 2 The X-ray diffraction images of the porous MgNi2 intermetallic compound in Example 1 of the present application and the porous Ni in Comparative Example 1; wherein Figure 2 a is Example 1, Figure 2 b is Comparative Example 1.

[0032] Figure 3 The high-resolution scanning transmission electron microscope image of the porous MgNi2 intermetallic compound in Comparative Example 1 of the present application.

[0033] Figure 4 The scanning electron microscope image of the porous MgNi2 intermetallic compound in Example 2 of the present application.

[0034] Figure 5 The scanning electron microscope image of the porous MgNi2 intermetallic compound in Example 3 of the present application.

[0035] Figure 6 The scanning electron microscope image of the porous β1-NiZn intermetallic compound in Example 4 of the present application.

[0036] Figure 7 The X-ray diffraction image of the porous β1-NiZn intermetallic compound in Example 4 of the present application.

[0037] Figure 8 Scanning electron microscope images of the porous β1-NiZn intermetallic compound in Example 5 of the present application and the porous Ni in Comparative Example 2; wherein Figure 8 a is Example 5, Figure 8 b is Comparative Example 2.

[0038] Figure 9 X-ray diffraction images of the porous β1-NiZn intermetallic compound in Example 5 of the present application and the porous Ni in Comparative Example 2; wherein Figure 9 a is Example 5, Figure 9 b is Comparative Example 2.

[0039] Figure 10 Current-voltage curve of the electrocatalytic hydrogen evolution reaction in Example 6 of the present application.

[0040] Figure 11 Battery cycle test results in Example 7 of the present application.

[0041] Figure 12 Battery cycle test results in Example 8 of the present application. DETAILED DESCRIPTION

[0042] In order to facilitate the understanding of the porous intermetallic compound material and the preparation method thereof of the present application, the porous intermetallic compound material and the preparation method thereof of the present application will be described more fully below, and the embodiments of the present application are given, but the scope of the present application is not limited thereby.

[0043] Example 1:

[0044] The present embodiment provides a porous MgNi2 intermetallic compound material and a preparation method thereof.

[0045] Firstly, the metal Ni and the metal Mg are mixed according to the molar ratio of 68:32;

[0046] Secondly, the Ni-Mg alloy is prepared by using an induction melting device under an Ar gas atmosphere, and then the intermetallic compound MgNi2 belt-shaped alloy precursor is prepared by using a rapid quenching and spinning device;

[0047] Thirdly, the belt-shaped alloy precursor obtained in the second step is placed in a sealed quartz tube tube furnace, the gas pressure in the furnace is pumped to 5x10 -5 Pa by using a vacuum pump, and the temperature is raised to 450℃ at a rate of 20℃ / min, and the temperature is kept for 2 hours; after the reaction is completed, the sample is taken out after the furnace is cooled, and the porous MgNi2 intermetallic compound is obtained.

[0048] Example 2:

[0049] The present embodiment provides a porous MgNi2 intermetallic compound material and a preparation method thereof.

[0050] In the first step, metal Ni and metal Mg are mixed in a molar ratio of 68:32;

[0051] In the second step, the Ni-Mg alloy is prepared by using an induction melting device under an Ar gas atmosphere, and then the intermetallic compound MgNi2 belt alloy precursor is prepared by using a rapid quenching and tape casting device;

[0052] In the third step, the belt alloy precursor obtained in the second step is placed in a sealed quartz tube tube furnace, the gas pressure in the furnace is pumped to 5x10 -5 Pa by a vacuum pump, and the temperature is raised to 400℃ at a rate of 20℃ / min, and the temperature is kept for 2 hours; after the reaction is completed, the sample is taken out after the furnace is cooled, and a porous MgNi2 intermetallic compound is obtained.

[0053] Example 3:

[0054] The present embodiment provides a porous MgNi2 intermetallic compound material and a preparation method thereof.

[0055] In the first step, metal Ni and metal Mg are mixed in a molar ratio of 68:32;

[0056] In the second step, the Ni-Mg alloy is prepared by using an induction melting device under an Ar gas atmosphere, and then the intermetallic compound MgNi2 belt alloy precursor is prepared by using a rapid quenching and tape casting device;

[0057] In the third step, the belt alloy precursor obtained in the second step is placed in a sealed quartz tube tube furnace, the gas pressure in the furnace is pumped to 100 Pa by a vacuum pump, and the temperature is raised to 520℃ at a rate of 20℃ / min under a mixed gas atmosphere of 95% Ar and 5% H2, and the temperature is kept for 2 hours; after the reaction is completed, the sample is taken out after the furnace is cooled, and a porous MgNi2 intermetallic compound is obtained.

[0058] Example 4:

[0059] The present embodiment provides a porous β1-NiZn intermetallic compound material and a preparation method thereof.

[0060] In the first step, metal Ni and metal Zn are mixed in a molar ratio of 15:85;

[0061] In the second step, the Ni-Zn alloy is prepared by using an induction melting device under an Ar gas atmosphere, and then the intermetallic compound β1-NiZn belt alloy precursor is prepared by using a rapid quenching and tape casting device;

[0062] Third step, the strip alloy precursor obtained in the second step was put into a sealed quartz tube tube furnace, the gas pressure in the furnace was pumped to 100 Pa by a vacuum pump, and the temperature was raised to 400℃ at a rate of 20℃ / min under a mixed gas atmosphere of 95% Ar and 5% H2, and the temperature was kept for 2 hours. After the reaction was completed, the sample was taken out after the furnace was cooled, and a porous β1-NiZn intermetallic compound was obtained.

[0063] Example 5:

[0064] The present embodiment provides a β1-NiZn intermetallic compound material and a preparation method thereof.

[0065] First step, the metal Ni and the metal Zn were mixed according to a molar ratio of 15:85;

[0066] Second step, the Ni-Zn alloy was prepared by using an induction melting device under an Ar gas atmosphere, and then the strip alloy precursor of the intermetallic compound β1-NiZn was prepared by using a rapid quenching strip casting device;

[0067] Third step, 27.4g of Li and 1g of the strip alloy precursor of the intermetallic compound β1-NiZn (γ-Ni2Zn 11 ) were mixed in an argon atmosphere glove box, and then were put into a Mo crucible and sealed. After being taken out of the glove box, they were quickly transferred into a quartz tube tube furnace, the gas pressure in the furnace was pumped to 160 Pa by a vacuum pump, and the temperature was raised to 300℃ at a rate of 20℃ / min under a mixed gas atmosphere of 95% Ar and 5% H2, and the temperature was kept for 0.5 hours. After the reaction was completed, the sample was taken out after the furnace was cooled. Subsequent treatment was carried out by immersing in water for 12h and immersing in 1M (NH4)2SO4 solution for 12h to remove the Li and Zn solidified in the pores of the sample, and finally a porous β1-NiZn intermetallic compound was obtained.

[0068] Example 6:

[0069] The porous MgNi2 intermetallic compound obtained in Example 1 was applied as a catalyst in the hydrogen evolution reaction of water electrolysis, and its electrocatalytic hydrogen evolution performance was tested. The test conditions were as follows: a three-electrode system, the working electrode was a self-supporting porous MgNi2 intermetallic compound strip, the counter electrode was a Pt mesh, the reference electrode was an Ag / AgCl, the electrolyte was a 1M KOH aqueous solution, and the voltage scanning speed was 10mV / s.

[0070] Example 7:

[0071] The porous MgNi2 intermetallic compound obtained in Example 3 was used as a negative electrode material of a lithium metal battery, and its electrochemical performance was tested. A half-cell was assembled using a metal lithium sheet as a counter electrode, and the electrolyte was a 1molL -1LiTFSI ether electrolyte (salt: LiTFSI, solvents: DOL and DME, volume ratio: 1:1, additive: 3 wt.% LiNO3), 200 μL, separator: Glassy Fiber. After battery assembly, preheating at 0.2 mA / cm². -2 The current density will be 2 mAh cm⁻¹ -2 Li was electrochemically deposited on a porous MgNi2 intermetallic compound sheet, followed by electrochemical deposition at 0.5 mA / cm². -2 Current density and 0.5 mAh / cm -2 Cyclic testing was conducted at the areal capacity. Additionally, an assembled lithium-ion symmetric battery was tested under the same conditions as a comparison.

[0072] Example 8:

[0073] The porous MgNi2 intermetallic compound obtained in Example 3 was used as the negative electrode material for a lithium metal battery, and its electrochemical performance was tested. A half-cell was assembled using a lithium metal sheet as the counter electrode, and the electrolyte was 1 mol / L. -1 LiTFSI ether electrolyte (salt: LiTFSI, solvents: DOL and DME, volume ratio: 1:1, additive: 3 wt.% LiNO3), 200 μL, separator: Glassy Fiber. After battery assembly, preheating at 0.2 mA / cm². -2 The current density will be 2 mAh cm⁻¹ -2 Li was electrochemically deposited on a porous MgNi2 intermetallic compound sheet, followed by electrochemical deposition at 0.5 mA / cm². -2 Current density and 1mAhcm -2 Cyclic testing was conducted at the areal capacity. Additionally, an assembled lithium-ion symmetric battery was tested under the same conditions as a comparison.

[0074] Comparative Example 1:

[0075] A porous Ni material and its preparation method.

[0076] The first step is to mix metallic Ni and metallic Mg in a molar ratio of 68:32.

[0077] The second step is to prepare Ni-Mg alloy by induction melting equipment under Ar atmosphere, and then to prepare porous Ni strip alloy precursor by rapid cooling strip spinning equipment.

[0078] The third step involves placing the strip-shaped alloy precursor obtained in the second step into a sealed quartz tube furnace, and using a vacuum pump to evacuate the furnace pressure to 5 × 10⁻⁶. -5 Pa was heated to 600℃ at a rate of 20℃ / min and held for 2 hours. After the reaction was completed, the sample was taken out after the furnace cooled down to obtain porous Ni.

[0079] Comparative Example 2:

[0080] A porous Ni material and a preparation method thereof.

[0081] In the first step, metal Ni and metal Zn are mixed in a molar ratio of 15:85;

[0082] In the second step, the Ni-Zn alloy is prepared by using an induction melting device under an Ar gas atmosphere, and then a porous Ni alloy precursor in a strip shape is prepared by using a rapid quenching strip casting device.

[0083] In the third step, 27.4 g of Li and 1 g of the porous Ni alloy precursor in a strip shape (γ-Ni2Zn 11 ) are mixed in a glove box under an argon atmosphere, and then are placed in a Mo crucible and sealed; the glove box is taken out and is quickly transferred into a quartz tube tube furnace, the gas pressure in the furnace is pumped to 160 Pa by using a vacuum pump, the temperature is raised to 550 DEG C at a rate of 20 DEG C / min under a mixed gas atmosphere of 95% Ar and 5% H2, and the sample is taken out after the furnace is cooled; the subsequent treatment is carried out by immersing in water for 12 h and immersing in a 1M (NH4)2SO4 solution for 12 h, so as to remove the Li and Zn solidified in the pores of the sample, and finally the porous Ni is obtained.

[0084] Results and analysis

[0085] We successfully obtain the porous Ni (1-2) M intermetallic compound, the intermetallic compound obtained by the method has an ordered lattice array structure, a more uniform active site distribution, and enhanced geometric effects; the bonding mode tends to be a covalent bond, the electron is localized and shared, and the electronic effect is enhanced; and the intermetallic compound has the characteristics of a unique double-continuous open pore structure, high electrical conductivity and thermal conductivity, a large specific surface area, and high catalytic activity. We can verify the above through the comparison between the examples 1-5 and the comparative examples 1-2.

[0086] In the preparation method, the pore structure of the intermetallic compound with a double-continuous porous structure can be further improved to improve the specific surface area of the intermetallic compound by adjusting the method conditions; and the structure of the intermetallic compound can be selected, so as to form a structure with a more uniform active site distribution and enhanced geometric and electronic effects. First, we compare example 1 and comparative example 1, and the results are shown in Figures 1-5 . Figure 1From the scanning electron microscope images of the porous MgNi2 intermetallic compound prepared in Example 1 and the porous Ni prepared in Comparative Example 1, it can be seen that the porous MgNi2 intermetallic compound and the porous Ni both have a bicontinuous porous structure. The bicontinuous porous structure refers to a structure having mutually connected solid ligaments and mutually connected pores. The bicontinuous porous structure is beneficial to achieving high electrical conductivity, high thermal conductivity and high mass transfer efficiency, and at the same time, improving the specific surface area of the entire material, thereby being beneficial to improving the reaction activity of the material. The average pore diameter of the porous MgNi2 intermetallic compound of the present application is about 120 nm, and the average pore diameter of the porous Ni is about 600 nm. It can be seen that the temperature of the method of the present application can be beneficial to obtaining a pore structure with a smaller average pore diameter, and can further improve the pore structure of the porous MgNi2 intermetallic compound. Figure 2 From the X-ray diffraction images of the porous MgNi2 intermetallic compound prepared in Example 1 and the porous Ni prepared in Comparative Example 1, it can be seen that the porous MgNi2 of the present application is a hexagonal MgNi2 intermetallic compound phase, and the porous Ni of Comparative Example 1 is a face-centered cubic phase. Through Figure 3 high-resolution scanning transmission electron microscopy, it is further verified that the porous MgNi2 intermetallic compound of the present application has a chemically ordered atomic structure. We further designed Example 2-Example 3 for comparison and verification with Example 1. The average pore diameter of the porous MgNi2 intermetallic compound obtained in Example 2 is 50 nm, as shown in Figure 4 The average pore diameter of the porous MgNi2 intermetallic compound obtained in Example 3 is 260 nm, as shown in Figure 5 We further found that the porous Ni (1-2) The structure of the M intermetallic compound is also related to the coordination of the elements in the precursor of the porous Ni (1-2) M intermetallic compound and the selection of the elements. We compared and verified Example 3 and Example 4, and Example 4 successfully obtained a porous β1-NiZn intermetallic compound, as shown in Figure 7 The average pore diameter of the porous β1-NiZn intermetallic compound obtained in Example 4 is about 400 nm, as shown in Figure 6 The porous β1-NiZn intermetallic compound obtained in Example 4 is a tetragonal structure. It can be seen that the average pore diameter of the porous Ni (1-2) M intermetallic compound and the structure of the catalyst can be further selected by adjusting the experimental conditions in the method of the present application.

[0087] On this basis, we also designed Example 5 and Comparative Example 2 for comparison, and the results are shown in Figure 8 and Figure 9 Figure 8 ​The scanning electron microscope images of the porous β1-NiZn intermetallic compound prepared in Example 5 and the porous Ni prepared in Comparative Example 2 can be seen that the porous β1-NiZn intermetallic compound and the porous Ni both have a double-continuous porous structure, wherein the average pore size of the porous β1-NiZn intermetallic compound is about 400 nm, and the average pore size of the porous Ni is about 2 μm; Figure 9 The X-ray diffraction images of the porous β1-NiZn intermetallic compound prepared in Example 5 and the porous Ni prepared in Comparative Example 2 can be seen that the porous β1-NiZn is a tetragonal β1-NiZn intermetallic compound phase, and the porous Ni is a face-centered cubic phase.

[0088] We further obtained the porous Ni (1-2) The M intermetallic compound can be used as a catalyst and a battery negative electrode material, as shown in Examples 6-9. Figure 10 For the measured current-voltage curve, it is shown that the starting voltage of the porous MgNi2 intermetallic compound for catalyzing the hydrogen evolution reaction is 0 V, and the current of 100 mA / cm 2 The overvoltage required for the current is 177 mV, which shows high catalytic performance. Figure 11 The results show that the porous MgNi2 intermetallic compound electrode can be stably cycled for 300 hours without obvious overvoltage change, while the lithium metal electrode shows overvoltage increase after 100 hours of cycling, which indicates that the porous MgNi2 intermetallic compound electrode can effectively inhibit lithium dendrite growth and relieve volume expansion, thereby improving the performance of lithium metal batteries. Figure 12 The results show that the porous MgNi2 intermetallic compound electrode can be stably cycled for 260 hours without obvious overvoltage change, while the lithium metal electrode shows overvoltage increase after 40 hours of cycling, which indicates that the porous MgNi2 intermetallic compound electrode can effectively inhibit lithium dendrite growth and relieve volume expansion, thereby improving the performance of lithium metal batteries.

[0089] In summary, the porous Ni (1-2) The M intermetallic compound has high electrical conductivity and thermal conductivity, large specific surface area and high catalytic activity, and can play an important role as a battery negative electrode material and a catalyst.

[0090] It should be noted that the above only describes the preferred embodiments of the present application and is not intended to limit the present application, and any modification, equivalent replacement, improvement, etc. made within the spirit and principle of the present application shall be included in the protection scope of the present application.

Claims

1. A porous intermetallic compound material, characterized by, The chemical formula of the intermetallic compound material is Ni (1-2) M, the M including one of Mg, Zn, the Ni is a nickel element, the Mg is a magnesium element, the Zn is a zinc element, the elements in the chemical formula of the intermetallic compound material satisfy charge balance; the intermetallic compound material has a double-continuous open pore structure, and the intermetallic compound material has a chemically ordered lattice point array structure; The chemical formula of the intermetallic compound material is MgNi2, the average pore size of the bicontinuous open pore structure of the MgNi2 is 30nm-500nm, and the chemically ordered lattice point array structure of the MgNi2 is a hexagonal structure; the MgNi2 has characteristic XRD diffraction peaks at 22.49°, 44.01°, 44.93°, 45.91°, 71.96°, and 79.57°; or the chemical formula of the intermetallic compound material is β1-NiZn, the average pore size of the bicontinuous open pore structure of the β1-NiZn is 200nm-500nm, and the chemically ordered lattice point array structure of the β1-NiZn is a tetragonal structure; the β1-NiZn has characteristic XRD diffraction peaks at 43.22°, 46.60°, 57.28°, 68.02°, 76.85°, and 84.09°; The preparation method of the porous intermetallic compound material is selected from I scheme or II scheme: I. Scheme: The intermetallic compound alloy precursor is disposed in a closed environment, which includes one of a vacuum environment, an inert atmosphere environment, and a reducing atmosphere environment, and the processing conditions include a pressure of 5 x 10 -5 Pa-500 Pa, a temperature of 300-550 °C, a temperature rising rate of 10-50 °C / min, a processing time of 0.5-5 h, and the sample is taken out after the furnace is cooled down after the reaction is completed. The II scheme is as follows: placing an intermetallic compound alloy precursor and an alkali metal in an airtight container in an argon atmosphere, then transferring the container with the intermetallic compound alloy precursor and the alkali metal as a whole to an inert atmosphere environment or a reducing atmosphere environment, and then treating at a pressure of 50Pa-500Pa and a temperature of 200℃-400℃ at a heating rate of 10℃ / min-50℃ / min for 0.2h-3h; then soaking after cooling to remove M and the alkali metal to form a porous structure.

2. The porous intermetallic compound material of claim 1, wherein, The intermetallic compound material Ni (1-2) The molar ratio of Ni and M in the alloy precursor of M is (10-70):(30-90).

3. The method of producing a porous intermetallic compound material according to any one of claims 1 to 2, characterized in that, The method is selected from I scheme or II scheme: I. Scheme: The intermetallic compound alloy precursor is disposed in a closed environment, which includes one of a vacuum environment, an inert atmosphere environment, and a reducing atmosphere environment, and the processing conditions include a pressure of 5x10 -5 Pa-500 Pa, a temperature of 300-550 °C, a temperature rising rate of 10-50 °C / min, a processing time of 0.5-5 h, and the sample is taken out after the furnace is cooled down after the reaction is completed. The II scheme is as follows: placing an intermetallic compound alloy precursor and an alkali metal in an airtight container in an argon atmosphere, then transferring the container with the intermetallic compound alloy precursor and the alkali metal as a whole to an inert atmosphere environment or a reducing atmosphere environment, and then treating at a pressure of 50Pa-500Pa and a temperature of 200℃-400℃ at a heating rate of 10℃ / min-50℃ / min for 0.2h-3h; then soaking after cooling to remove M and the alkali metal to form a porous structure.

4. The production method according to claim 3, characterized by, The preparation method of the intermetallic compound alloy precursor in the I scheme and the II scheme includes weighing metal Ni and metal M according to the molar ratio of Ni and M in the intermetallic compound alloy precursor, and melting under an inert atmosphere or a reducing atmosphere to obtain the intermetallic compound alloy precursor.

5. The preparation method according to claim 3, characterized in that, The inert atmosphere includes one or more of argon, helium, neon, krypton, and xenon; the reducing atmosphere includes a mixed atmosphere of the inert atmosphere and hydrogen, wherein the volume fraction of hydrogen is greater than 0% and less than 50%; The alkali metal includes one or more of lithium, sodium, and potassium; The soaking treatment in the II scheme includes sequentially soaking in water and an acidic solution, and the water soaking time is 1h-24h; the acidic solution soaking time is 1h-24h; The acidic solution includes (NH4)2SO4, and the concentration of the acidic solution is 0.8M-1.2M.

6. Application of the porous intermetallic compound material of any one of claims 1-2 as a catalyst.

7. Use of the porous intermetallic compound material according to any one of claims 1 to 2 as a catalyst in the hydrogen evolution reaction of water electrolysis.

8. Use of the porous intermetallic compound material according to any one of claims 1 to 2 as a negative electrode in a battery.

9. Use of the porous intermetallic compound material according to any one of claims 1 to 2 as a negative electrode active material in a lithium secondary battery.

Images