A method for synthesizing magnesium-based hydrogen storage alloy fibers with in-situ nano-catalytic phase uniform distribution

Abstract

The application relates to a method for synthesizing magnesium-based hydrogen storage alloy fibers with in-situ nano-catalytic phases uniformly distributed. The application aims to solve the problems of coarse structure, easy segregation of alloy elements, uneven distribution of catalytic phases, high preparation cost and complex process of nanocrystals of the magnesium-based hydrogen storage alloy. The method comprises the following steps: 1, raw materials are obtained by proportioning according to atomic percentage; 2, a cast alloy is obtained by smelting the raw materials in a protective gas by using an electric resistance furnace; 3, a cylindrical pre-alloy rod is prepared by wire cutting in the cast alloy; and 4, the treated pre-alloy rod is placed in a crucible of a melt-spinning device to prepare hydrogen storage alloy fibers with a diameter of 50-100 mu m. The method significantly improves the performance of the magnesium-based hydrogen storage alloy, and the application is applied to the field of magnesium-based hydrogen storage alloy.

Description

Technical Field

[0001] This invention relates to a method for synthesizing magnesium-based hydrogen storage alloy fibers with uniformly distributed in-situ nanocatalytic phases. Background Technology

[0002] Hydrogen energy, as a clean and low-carbon green energy source, boasts high calorific value, wide availability, and flexible storage and transportation, making it widely used in industry, transportation, construction, and power generation. Against the backdrop of global carbon emission reduction, hydrogen energy can replace traditional energy sources such as gasoline, diesel, and natural gas in various scenarios, promoting deep decarbonization in industry and transportation, and achieving energy transformation. However, achieving high-density, low-energy-consumption, and highly safe hydrogen storage remains a pressing issue.

[0003] Magnesium-based hydrogen storage alloys are considered a promising type of metallic hydrogen storage material, possessing unique advantages such as high hydrogen storage capacity (7.6 wt.%, 110 g / L), good reversibility, high safety, abundant resources, low cost, and being environmentally friendly and pollution-free. However, the kinetic and thermodynamic properties of pure magnesium are limited by several factors, such as the ease with which magnesium oxidizes in air, resulting in a slow dissociation rate of hydrogen molecules on the magnesium surface; the diffusion rate of hydrogen atoms in MgH2 is three orders of magnitude lower than in Mg; and the excessively high bond energy of the Mg-H bond leads to a dehydrogenation temperature exceeding 300℃, limiting its practical application. To improve the performance of magnesium-based hydrogen storage alloys, alloying, catalyst doping, and nano-sizing techniques have all shown significant effects.

[0004] Magnesium-based hydrogen storage alloys suffer from several drawbacks during large-scale production. The primary Mg dendrites are coarse, and when modified by alloying, the alloying elements exhibit severe segregation. Furthermore, the addition of large amounts of alloying elements can lead to a decrease in the hydrogen storage capacity of magnesium-based hydrogen storage alloys. Catalyst doping only affects the surface of magnesium-based hydrogen storage alloys and cannot achieve uniform distribution of the catalytic phase within the alloy. Additionally, the preparation of nanomaterials is costly and complex.

[0005] In summary, current magnesium-based hydrogen storage alloys suffer from problems such as coarse microstructure, easy segregation of alloying elements, uneven distribution of the catalytic phase, and high cost and complex process in preparing nanocrystals. Therefore, to solve these problems, there is an urgent need to develop a simple, low-cost, industrially applicable method for preparing high-capacity magnesium-based hydrogen storage alloy fibers with a uniform and fine microstructure and a uniformly distributed catalytic phase. Summary of the Invention

[0006] The purpose of this invention is to solve the problems of coarse microstructure, easy segregation of alloying elements, inability to uniformly distribute catalytic phase, and high cost and complex process of preparing nanocrystals in magnesium-based hydrogen storage alloys. The invention provides a method for synthesizing magnesium-based hydrogen storage alloy fibers with uniformly distributed in-situ nanocatalytic phase.

[0007] This invention discloses a method for synthesizing magnesium-based hydrogen storage alloy fibers with uniformly distributed in-situ nanocatalytic phases, which is carried out as follows:

[0008] 1. Prepare raw materials by mixing 97% Mg, 2-3% Ni, and ≤1% Y in atomic percentage, totaling 100%.

[0009] 2. The raw materials are melted in a resistance furnace under a protective gas at a temperature of 750-800℃. After complete melting, the alloy is poured into a mold to obtain a cast alloy.

[0010] III. Cylindrical precast alloy rods were prepared from cast alloys by wire cutting;

[0011] 4. Place the processed pre-made alloy rod in the crucible of the melt quenching equipment. The rotation speed of the copper roller is 1200-1700 r / min, the induction heating power is 11-13 A, and the crucible feed rate is 30-50 μm / s to prepare hydrogen storage alloy fibers with a diameter of 50-100 μm.

[0012] The present invention has the following beneficial effects:

[0013] 1. This invention employs melt spin quenching preparation technology, which significantly reduces grain size due to the high cooling rate. At the same time, it expands the solid solubility of Y element in the magnesium matrix, solving the problems of coarse microstructure and element segregation in conventional solidified alloys. This technology has the advantages of short preparation process and low preparation cost, and solves the disadvantages of complex preparation process and high cost of nanomaterials.

[0014] 2. The hydrogen storage alloy fiber obtained by the method of the present invention has an approximately one-dimensional linear structure with a large specific surface area. It can directly absorb and release hydrogen using the fiber structure, avoiding the need for long-term ball milling of hydrogen storage alloy powder prepared by conventional methods, thus simplifying the process.

[0015] 3. The method of this invention achieves uniform elemental distribution in hydrogen storage alloy fibers. During hydrogen absorption and desorption cycles, the catalytic phase can be generated in situ and dispersed within the fiber alloy, improving the catalytic efficiency of the catalytic phase. The magnesium-based hydrogen storage alloy prepared by this method has a uniform microstructure, fine grain size, and uniformly dispersed nanocatalytic phase, significantly improving the performance of magnesium-based hydrogen storage alloys. 97 Ni 2.5 Y 0.5 The hydrogen storage alloy fiber absorbs 6.28 wt.% H2 within 100 minutes under conditions of 325℃ and 3MPa, and can completely release it in 5.35 minutes. This solves the problems of easy segregation of catalytic elements and catalyst doping only affecting the surface of magnesium-based hydrogen storage alloys in high-capacity magnesium-based hydrogen storage alloys. Attached Figure Description

[0016] Figure 1The hydrogen storage alloy fiber Mg prepared in Example 1 97 Ni 2.5 Y 0.5 Surface morphology diagram of the alloy;

[0017] Figure 2 Mg for hydrogen storage alloy fibers 97 Microstructure of Ni3 in its internal cross section;

[0018] Figure 3 Mg for hydrogen storage alloy fibers 97 Ni 2.75 Y 0.25 Internal cross-sectional microstructure diagram;

[0019] Figure 4 Mg for hydrogen storage alloy fibers 97 Ni 2.5 Y 0.5 Internal cross-sectional microstructure diagram;

[0020] Figure 5 Mg for hydrogen storage alloy fibers 97 Microstructure of the internal cross section of Ni2Y1 alloy;

[0021] Figure 6 The Mg fiber prepared in Example 1 97 Ni 2.5 Y 0.5 SEM image of in-situ formation of the catalytic phase in the alloy;

[0022] Figure 7 The Mg fiber prepared in Example 1 97 Ni3, Mg 97 Ni 2.75 Y 0.25 Mg 97 Ni 2.5 Y 0.5 Mg 97 Hydrogen absorption and desorption properties of Ni2Y1 alloy at 325℃ and 3MPa;

[0023] Figure 8 As-cast Mg prepared for Comparative Example 1 97 Ni 2.5 Y 0.5 Microstructure morphology of the alloy;

[0024] Figure 9 As-cast Mg prepared for Comparative Example 1 97 Ni 2.5 Y 0.5 Hydrogen absorption and desorption properties of the alloy at 325℃ and 3MPa. Detailed Implementation

[0025] The technical solution of the present invention is not limited to the specific embodiments listed below, but also includes any combination of the specific embodiments.

[0026] Specific Implementation Method 1: This implementation method describes a method for synthesizing magnesium-based hydrogen storage alloy fibers with uniformly distributed in-situ nanocatalytic phases, as follows:

[0027] 1. Prepare raw materials by mixing 97% Mg, 2-3% Ni, and ≤1% Y in atomic percentage, totaling 100%.

[0028] 2. The raw materials are melted in a resistance furnace under a protective gas at a temperature of 750-800℃. After complete melting, the alloy is poured into a mold to obtain a cast alloy.

[0029] III. Cylindrical precast alloy rods were prepared from cast alloys by wire cutting;

[0030] 4. Place the processed pre-made alloy rod in the crucible of the melt quenching equipment. The rotation speed of the copper roller is 1200-1700 r / min, the induction heating power is 11-13 A, and the crucible feed rate is 30-50 μm / s to prepare hydrogen storage alloy fibers with a diameter of 50-100 μm.

[0031] In step two, the melting temperature is set to 750-800℃, and mechanical stirring is performed every 20 minutes during the melting process. After complete melting, the alloy is poured into a preheated 300℃ cast iron mold to obtain the as-cast alloy. In step three, a cylindrical precast alloy rod with a diameter of 10mm and a height of 30mm is prepared by wire cutting.

[0032] Specific Implementation Method Two: This implementation method differs from Specific Implementation Method One in that the raw materials are pure Mg, Mg-70wt.% Ni master alloy, and Mg-20wt.% Y master alloy, all with a purity higher than 99.9wt.%. Everything else is the same as in Specific Implementation Method One.

[0033] Specific Implementation Method Three: This implementation method differs from Specific Implementation Method One or Two in that the raw materials are composed of 97% Mg, 2.5% Ni, and 0.5% Y in atomic ratio. Everything else is the same as in Specific Implementation Method One or Two.

[0034] Specific Implementation Method Four: This implementation method differs from Specific Implementation Methods One to Three in that the raw materials are composed of 97% Mg and 3% Ni in atomic ratio. Everything else is the same as in Specific Implementation Methods One to Three.

[0035] Specific Implementation Method Five: This implementation method differs from Specific Implementation Methods One to Four in that the raw materials consist of 97% Mg, 2.75% Ni, and 0.25% Y in atomic ratio. The other steps are the same as in Specific Implementation Methods One to Four.

[0036] Specific Implementation Method Six: This implementation method differs from Specific Implementation Methods One to Five in that the raw materials consist of 97% Mg, 2% Ni, and 1% Y in atomic ratio. The other steps are the same as in Specific Implementation Methods One to Five.

[0037] Specific Implementation Method Seven: This implementation method differs from Specific Implementation Methods One through Six in that the protective gas is a mixture of sulfur hexafluoride and carbon dioxide. The other steps are the same as in Specific Implementation Methods One through Six.

[0038] Specific Implementation Method Eight: This implementation method differs from Specific Implementation Methods One to Seven in that the mold is a preheated cast iron mold at 300°C. The other steps are the same as in Specific Implementation Methods One to Seven.

[0039] Specific Implementation Method Nine: This implementation method differs from Specific Implementation Methods One to Eight in that the diameter of the cylindrical prefabricated alloy rod is 10mm and the height is 30mm. The other steps are the same as in Specific Implementation Methods One to Eight.

[0040] Specific Implementation Method Ten: This implementation method differs from Specific Implementation Methods One to Nine in that: the pre-fabricated alloy rod processing method involves sanding the surface to remove impurities and oxide scale, followed by thorough cleaning. Other steps are the same as in Specific Implementation Methods One to Nine.

[0041] Specific Implementation Method Eleven: The difference between this implementation method and Specific Implementation Methods One through Ten is that the furnace cavity of the melt quenching equipment is evacuated to 6×10⁻⁶. -3 Pa, then fill with 0.5 Pa of argon protective gas. The other steps are the same as in specific embodiments one to ten.

[0042] The beneficial effects of the present invention are verified using the following embodiments:

[0043] Example 1

[0044] This embodiment describes an in-situ formed dispersed nanocatalytic phase of Mg. 97 Ni 2.5 Y 0.5 High-capacity magnesium-based hydrogen storage alloy fiber, composed of 97 at.% Mg, 2.5 at.% Ni and 0.5 at.% Y, is prepared by the following method:

[0045] I. The materials used were industrial pure Mg, Mg-70wt.%Ni master alloy, and Mg-20wt.%Y master alloy, all with a purity higher than 99.9wt.%. Since pure Mg is highly susceptible to oxidation in air, it was polished with sandpaper to remove the oxide scale. To facilitate melting and diffusion of the Mg-Ni and Mg-Y master alloys, ensuring uniform element distribution and reducing segregation, the master alloys used were selected with alloy particles of the smallest possible size. Because Mg is prone to burn-off, an additional 3wt.% Mg was added to compensate for burn-off.

[0046] II. Mg 97 Ni 2.5 Y 0.5 The alloy was smelted in an electric resistance furnace. First, pure Mg ingots were placed in a crucible, and the furnace temperature was set to 750°C. A protective gas mixture of sulfur hexafluoride and carbon dioxide was introduced into the furnace. Once the pure Mg reached a molten state, Mg-Ni and Mg-Y master alloy particles were added to the molten Mg, and the furnace temperature was increased to 800°C. To ensure uniform alloy melting, mechanical stirring was performed every 20 minutes until no obvious particles remained at the bottom of the crucible. The alloy was then cast into a preheated 300°C cast iron mold to obtain Mg... 97 Ni 2.5 Y 0.5 Alloy ingot.

[0047] III. In the as-cast state of Mg 97 Ni 2.5 Y 0.5 Cylindrical pre-made alloy rods with a diameter of 10mm and a height of 30mm are cut from the alloy ingot by wire cutting. The surface impurities and oxide scale are removed by sanding on sandpaper. After cleaning, they are placed in the crucible of the melt spin quenching equipment.

[0048] IV. Vacuum the furnace chamber of the melt quenching equipment to 6×10 using mechanical and molecular pumps. -3 Pa, then fill with 0.5 Pa of argon protective gas to prevent the magnesium alloy from oxidizing or burning during the heating process.

[0049] 5. Turn on the power to the copper roller speed controller and set the copper roller speed to 1700 r / min. Turn on the power to the induction coil current controller and set the induction heating current to 12.5A. After the alloy rod melts and a convex molten pool is formed, start the feeding device to move upward until the molten pool is infinitely close to the wedge-shaped tip of the copper roller. Set the crucible feed rate to 50 μm / s. Utilizing the high-speed rotation of the copper roller, the wedge-shaped edge of the copper roller continuously quenches the molten alloy in the molten pool. Using centrifugal force, the molten alloy is thrown out and rounded into fine filaments under the action of the surface tension of the molten alloy, thus obtaining Mg. 97 Ni 2.5 Y 0.5 Magnesium-based hydrogen storage alloy fiber.

[0050] Using Mg 97 Ni 2.5 Y 0.5 Magnesium-based hydrogen storage alloy fibers were prepared using the same method to produce Mg 97 Ni3 magnesium-based hydrogen storage alloy fiber (composed of 97 at.% Mg and 3 at.% Ni), Mg 97 Ni 2.75 Y 0.25 Magnesium-based hydrogen storage alloy fiber (composed of 97 at.% Mg, 2.75 at.% Ni and 0.25 at.% Y), Mg 97 Ni2Y1 magnesium-based hydrogen storage alloy fiber (composed of 97 at.% Mg, 2 at.% Ni and 1 at.% Y).

[0051] like Figure 1 The image shows magnesium-based hydrogen storage alloy fiber Mg. 97 Ni 2.5 Y 0.5 The surface morphology shows that the fibers are round and smooth, with a diameter of approximately 60 μm; for example... Figures 2-5 The figures shown are Mg 97 Ni3, Mg 97 Ni 2.75 Y 0.25 Mg 97 Ni 2.5 Y 0.5 Mg 97 The microstructure of Ni2Y1 hydrogen storage alloy fibers after longitudinal section grinding and polishing shows that among the four alloy fibers, Mg grains are small, exhibiting petal-like and near-spherical grains. Ni element is distributed in a network structure around the Mg grain boundaries, restricting Mg grain growth. Under rapid solidification conditions, the solid solubility of Y element increases, and Mg... 97 Ni 2.75 Y 0.25 In the fiber alloy, Y element is completely dissolved; Mg 97 Ni 2.5 Y 0.5 In the fiber alloy, trace amounts of Y element precipitate, indicating that the Y element has reached its maximum solid solution level; Mg 97 In Ni2Y1 fiber alloys, a relatively large amount of Y element precipitates, therefore, Mg 97 Ni 2.5 Y 0.5 In the fiber alloy, the Y element is almost completely dissolved in the magnesium matrix, resulting in the best solid solution effect. The overall microstructure of the fiber alloy is uniform, with no obvious segregation.

[0052] A small amount of magnesium-based hydrogen storage alloy fiber was placed in the reactor of a hydrogen storage testing device. The furnace temperature was set to 400℃, and the mixture was heated under vacuum for 1.5 hours. After the reactor cooled to room temperature, the fiber alloy was removed to characterize the microstructure of the hydrogen storage alloy fiber during hydrogen absorption and desorption.

[0053] like Figure 6 The image shows Mg after heating under vacuum for 1.5 hours. 97 Ni 2.5 Y 0.5 The microstructure of the fiber alloy reveals in-situ formation of ultrafine Mg2Ni and NiY3 catalytic phase particles, uniformly distributed around the magnesium grains. These particles serve as active sites during hydrogen absorption and desorption, enhancing catalytic efficiency and promoting the hydrogen absorption and desorption reactions. Furthermore, these catalytic phase particles also act as pinning agents for the magnesium grains, limiting their rapid growth during cyclic hydrogen absorption and desorption.

[0054] Weigh 0.5g of the fiber alloy hydrogen storage performance test sample and perform multiple hydrogen absorption and desorption cycles at 400℃ and 3MPa to ensure that the alloy reaches the best performance. Then, perform hydrogen absorption and desorption performance tests at 325℃ and 3MPa.

[0055] like Figure 7 The image shows Mg 97 Ni3, Mg 97 Ni 2.75 Y 0.25 Mg 97 Ni 2.5 Y 0.5 Mg 97 The hydrogen absorption and desorption kinetics curves of Ni2Y1 hydrogen storage alloy fiber at 325℃ and 3MPa (left for hydrogen absorption, right for hydrogen desorption) show that the hydrogen absorption amounts at 100 min were 4.46 wt.%, 5.47 wt.%, 6.28 wt.%, and 5.83 wt.%, respectively. The hydrogen absorbed at 325℃ and 0.1MPa was completely released at 4.17 min, 5.25 min, 5.35 min, and 5.57 min, respectively. During hydrogen absorption, due to the high affinity between Y atoms and H atoms, Y elements act as the active site for the reaction, preferentially absorbing hydrogen to form YH. x The hydrogen absorption performance was significantly improved after the introduction of Y element. In Mg 97 Ni 2.5 Y 0.5 In the fiber alloy, the Y element is almost completely dissolved in the magnesium matrix, exhibiting the best solid solution effect and forming a uniformly dispersed catalytic phase, resulting in the best hydrogen storage performance. However, in Mg... 97 In Ni2Y1 fiber alloys, excessive Y element causes significant segregation, which reduces the catalytic effect and its hydrogen storage performance.

[0056] Comparative Example 1: As-cast Mg 97 Ni 2.5 Y 0.5 High-capacity magnesium-based hydrogen storage alloys are prepared by the following methods:

[0057] 1) The raw materials used were industrial pure Mg, Mg-70wt.%Ni master alloy, and Mg-20wt.%Y master alloy, all with a purity higher than 99.9wt.%. Since pure Mg is highly susceptible to oxidation in air, it was polished with sandpaper to remove the oxide scale. To facilitate melting and diffusion of the Mg-Ni and Mg-Y master alloys, ensuring uniform element distribution and reducing segregation, the master alloys used were selected with alloy particles of the smallest possible size. Because Mg is prone to burn-off, an additional 3wt.% Mg was added to compensate for burn-off.

[0058] 2)Mg 97 Ni 2.5 Y 0.5 The alloy was smelted in an electric resistance furnace. First, pure Mg ingots were placed in a crucible, and the furnace temperature was set to 750°C. A protective gas mixture of sulfur hexafluoride and carbon dioxide was introduced into the furnace. Once the pure Mg reached a molten state, Mg-Ni and Mg-Y master alloy particles were added to the molten Mg, and the furnace temperature was increased to 800°C. To ensure uniform alloy melting, mechanical stirring was performed every 20 minutes until no obvious particles remained at the bottom of the crucible. The alloy was then cast into a preheated 300°C cast iron mold to obtain Mg... 97 Ni 2.5 Y 0.5 Alloy ingot.

[0059] 3) Due to the as-cast Mg 97 Ni 2.5 Y 0.5 The alloy possesses good plasticity and toughness, making it difficult to pulverize into powder during ball milling. Therefore, the cast alloy was first prepared into large-particle powder using a manual filing method. Approximately 1g of large-particle powder was placed in a ball mill jar, along with grinding balls of different sizes at a ball-to-powder ratio of 80:1. To prevent oxidation of the alloy during ball milling, argon gas was introduced into the jar as a protective gas, and the jar was installed in a planetary ball mill. The ball milling time was set to 2 hours, and the milling speed was 300 r / min. The resulting alloy powder was sieved in a glove box, yielding alloy powder with a particle size less than 200 mesh, which was identified as the cast hydrogen storage alloy powder.

[0060] 4) Weigh 0.5g of powder as the test sample for hydrogen storage performance of the cast alloy, and perform multiple hydrogen absorption and desorption cycles at 400℃ and 3MPa to ensure that the alloy reaches the best performance. Then, perform hydrogen absorption and desorption performance tests at 325℃ and 3MPa.

[0061] like Figure 8 The image shows as-cast Mg 97 Ni 2.5 Y 0.5 The microstructure of the alloy exhibits three phases: a dark gray Mg phase, a bright white small-sized blocky NiY3 phase, and a eutectic structure of Mg and Mg2Ni at the eutectic boundaries. The Mg grains are relatively large, approximately 10-20 μm in size, and the NiY3 phase segregates at the grain boundaries of the Mg grains. The NiY3 phase, with its highest melting point, precipitates first from the alloy melt. These dispersed granular NiY3 phases act as nucleation sites for the Mg phase. As the melt temperature slowly decreases, the Mg grains precipitate and grow, leading to a continuous decrease in the magnesium content and an increase in the relative Ni content in the residual melt. In the Mg-Ni binary phase diagram, the melt composition gradually shifts towards the Mg-Ni eutectic point, ultimately forming a lamellar Mg and Mg2Ni eutectic structure at the grain boundaries of the Mg matrix.

[0062] like Figure 9 The image shows Mg 97 Ni 2.5 Y 0.5 The hydrogen absorption and desorption performance curves of the as-cast hydrogen storage alloy powder at 325℃ and 3MPa (left for hydrogen absorption, right for hydrogen desorption) show that the hydrogen absorption capacity is 5.64 wt.% after 100 min, and the absorbed hydrogen is completely released in 14.7 min at 325℃ and 0.1MPa. Due to the coarse magnesium grains and severe Y segregation in the as-cast alloy, the catalytic effect is poor, resulting in lower hydrogen storage performance than that of the fiber alloy.

Claims

1. A method for synthesizing magnesium-based hydrogen storage alloy fibers with uniformly distributed in-situ nanocatalytic phases, characterized in that... The preparation method is as follows:

1. Raw materials are prepared by mixing 97% Mg, 2.5% Ni, and 0.5% Y in an atomic ratio.

2. The raw materials are melted in a resistance furnace under a protective gas at a temperature of 750–800 ℃. After complete melting, the raw materials are poured into a mold to obtain a cast alloy. III. Cylindrical precast alloy rods were prepared from cast alloys by wire cutting; IV. The pre-formed alloy rods were placed in the crucible of a melt quenching apparatus. The rotation speed of the copper rollers was 1200–1700 r / min, the induction heating current was 11–13 A, and the crucible feed rate was 30–50 μm / s. Hydrogen storage alloy fibers with a diameter of 50–100 μm were prepared. After heating under vacuum for 1.5 hours, Mg... 97 Ni 2.5 Y 0.5 Ultrafine Mg2Ni and NiY3 catalytic phase particles are generated in situ in the fiber alloy.

2. The method for synthesizing magnesium-based hydrogen storage alloy fibers with uniformly distributed in-situ nanocatalytic phases according to claim 1, characterized in that: The raw materials are pure Mg, Mg-70 wt.% Ni master alloy and Mg-20 wt.% Y master alloy, all with a purity higher than 99.9 wt.%.

3. The method for synthesizing magnesium-based hydrogen storage alloy fibers with uniformly distributed in-situ nanocatalytic phases according to claim 1, characterized in that... The protective gas is a mixture of sulfur hexafluoride and carbon dioxide.

4. The method for synthesizing magnesium-based hydrogen storage alloy fibers with uniformly distributed in-situ nanocatalytic phases according to claim 1, characterized in that... The mold is a cast iron mold preheated to 300 ℃.

5. The method for synthesizing magnesium-based hydrogen storage alloy fibers with uniformly distributed in-situ nanocatalytic phases according to claim 1, characterized in that... The cylindrical precast alloy rod has a diameter of 10 mm and a height of 30 mm.

6. The method for synthesizing magnesium-based hydrogen storage alloy fibers with uniformly distributed in-situ nanocatalytic phases according to claim 1, characterized in that... Precast alloy rod processing method: Sanding with sandpaper to remove surface impurities and oxide scale, then cleaning thoroughly.

7. The method for synthesizing magnesium-based hydrogen storage alloy fibers with uniformly distributed in-situ nanocatalytic phases according to claim 1, characterized in that... The furnace chamber of the melt quenching equipment was evacuated to 6×10 -3 Pa, then fill with argon gas at 0.5 Pa.

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