A method for the preparation of a multi-component alloy porous material by pseudo-binary reaction

Abstract

The present application belongs to the field of metal materials, and particularly relates to a method for preparing a multi-component alloy porous material through pseudo-binary reaction. The method comprises the following steps: 1) respectively preparing powder group A and powder group B, and mixing the two to obtain mixed powder; 2) taking the mixed powder to be pressed into a green body, and sintering the green body to obtain a multi-component alloy porous material. The present application uses pre-alloyed powder as raw material, combines the pre-alloyed powder with a reaction synthesis process, converts the high-temperature sintering of the multi-component alloy into a pseudo-binary reaction, and combines the elements which are easy to be enriched or have a high melting point with the elements which have a low melting point or are evenly diffused in advance. On the one hand, the prepared metal porous material has a uniform distribution of elements, and therefore has good mechanical properties and corrosion resistance, and a long service life. On the other hand, the method ensures the formability of the powder, promotes the sinterability of the alloy porous sample, reduces the sintering difficulty of the porous sample, and can obtain a porous material with good sintering neck and connected pore structure.

Description

Technical Field

[0001] This invention belongs to the field of metallic materials, and particularly relates to a method for preparing multi-component alloy porous materials by pseudo-binary reaction. Background Technology

[0002] In recent years, porous metal materials have shown broad application prospects as core filtration elements or high specific surface area supports in high-temperature filtration, chemical synthesis gas processes such as steam methane reforming (SMR) and autothermal reforming (ATR), catalytic partial oxidation, electrochemistry such as solid oxide fuel cells (SOFC), and electrocatalysis. Porous metal materials possess excellent mechanical properties, allowing them to withstand higher temperature and pressure fluctuations; they are easily processed and assembled into various irregularly shaped elements and modules; simultaneously, they exhibit ideal thermal conductivity and mass transfer characteristics, avoiding large temperature gradients and localized hot spots when used as catalyst supports, thereby improving chemical transfer efficiency and selectivity; and due to their high specific surface area and catalytic activity, they can serve as self-supporting porous alloy catalytic electrode materials.

[0003] Powder-sintered alloy porous materials are an important type of porous material due to their simple preparation process, controllable porosity, and excellent mechanical properties. These porous materials are generally prepared using either element-mixed powder reactive synthesis or pre-alloyed powder diffusion sintering. The element-mixed powder reactive synthesis process uses elemental powders as raw materials, mixing them uniformly in a specific ratio, then forming them using molding or cold isostatic pressing, followed by high-temperature sintering through a precisely controlled stepped heating process. During the sintering process, the different diffusion coefficients of element atoms cause partial diffusion, forming the Kirkendall effect, which generates a certain amount of porosity in the material. Subsequent high-temperature sintering completes the homogenization of phase and component diffusion, ultimately yielding a porous material with reactive synthesis characteristics. The reactive synthesis process uses inexpensive raw materials, and the final material composition can be easily adjusted by regulating the elemental powder ratio. However, there are also problems. Elemental mixed powders are prone to segregation during use. In the reaction synthesis process, there are many multi-component reaction platforms and complex phase transformation reactions. In particular, when there are large differences in the melting points of different elements, low solid solubility of some elements, or the presence of refractory metals or highly reactive metals, sintering is more difficult, process control is more complex, and the uniformity of micro-components is poor, which further affects the mechanical and chemical properties of porous samples.

[0004] Traditional pre-alloyed powder sintering processes use pre-alloyed powder as raw material, followed by molding and high-temperature sintering to obtain porous materials with specific pore structures and strength. This process produces raw materials with uniform composition and no component segregation, resulting in porous samples with uniform pore size and porosity. However, the morphology of the pre-alloyed powder is limited by the atomization process; for difficult-to-reduce powders, only spherical powders can be prepared, making molding relatively difficult. In addition, pre-alloyed powder sintering processes also suffer from poor sinterability and limited methods for controlling pore structure.

[0005] In conclusion, it is necessary to provide a new process to address the technical limitations of the two processes mentioned above. Summary of the Invention

[0006] To address the problems of low porosity control, uncontrollable compositional segregation, and high sintering difficulty in the preparation of existing multi-element alloy porous materials, this invention provides a method for preparing multi-element alloy porous materials by pseudo-binary reaction.

[0007] The main objective of this invention is: I. It can effectively achieve the sintering preparation of multi-component alloy porous materials; Second, it can reduce sintering problems caused by differences in the melting points of components in multi-component alloys; Third, it can effectively control the pore structure of porous materials.

[0008] To achieve the above objectives, the present invention adopts the following technical solution.

[0009] A method for preparing multi-component alloy porous materials by pseudobinary reaction. The method includes: 1) Take powder group A and powder group B separately, and mix them well to form a mixed powder; 2) The mixed powder is pressed into a green body, and the green body is sintered to obtain a multi-component alloy porous material.

[0010] Preferably, in step 1), powder group A and powder group B are both pre-alloyed powders containing one or more metallic elements and / or rare earth elements and / or silicon as components. The pre-alloyed powder is prepared by smelting and combining water atomization and / or gas atomization and / or centrifugal atomization, and the particle size of the pre-alloyed powder prepared by this method is 10-100 μm.

[0011] As a preferred option Step 1) The metal elements and / or rare earth elements contained in powder group A are all relatively high melting point elements, and the melting point of the relatively high melting point elements is ≥1450 ℃; Step 1) The main elements contained in powder group B are all relatively low melting point elements of metal elements and / or rare earth elements, and / or silicon. The melting point of the relatively low melting point elements of metal elements and / or rare earth elements is ≤1100 ℃, and the content of the main elements is controlled to be ≥90 wt% of the total mass of powder group B.

[0012] As a preferred option Step 1) The powder group B also contains additional elements; The additional element is a relatively high melting point element, and the additional element can be used to reduce the oxide of the relatively high melting point element used in powder group A.

[0013] As a preferred option Step 2) The compression molding control pressure is 50-250 MPa.

[0014] As a preferred option Step 2) The sintering process includes low-temperature sintering, medium-temperature sintering, and high-temperature sintering in sequence; The low-temperature sintering is carried out at 120–500 °C for degassing and / or degumming. The intermediate-temperature sintering is carried out at 600–650 °C to stimulate the Kirkendall effect; The high-temperature sintering is carried out at a temperature of ≥1150 ℃, which is lower than the melting point of the components contained in powder group A.

[0015] As a preferred option The total holding time for the low-temperature sintering is 20–60 min; The medium-temperature sintering holding time is 1–3 h; The high-temperature sintering holding time is 1 to 3 hours.

[0016] As a preferred option Step 2) The sintering is carried out in a reducing atmosphere and / or under inert gas protection and / or vacuum conditions; When the sintering is carried out under vacuum conditions, the vacuum level is controlled to be 1.0 × 10⁻⁶. -2 ~1×10 0 Pa.

[0017] For the "pseudo" binary alloy system technical solution of this invention, the elements in powder group A and powder group B must first be distinguished. There are multiple ways to distinguish them. Specifically, iron, nickel, cobalt, manganese, chromium, and copper can be classified as hydrogen-reducible components, while aluminum, silicon, boron, and some rare earth elements can be classified as non-hydrogen-reducible components. For components that can be hydrogen-reducible, water atomization can be used to obtain irregular alloy powders with good formability; while for non-hydrogen-reducible components, inert gas atomization is generally used after melting to avoid irreversible oxidation of the elements in the powder.

[0018] The classification of "pseudo" binary alloy systems can also be based on the differences in the melting points of the elements within the system. To fully utilize the diffusion-forming effect between different components, high-melting-point elements can be smelted into pre-alloyed powders, such as iron-nickel-chromium, titanium-niobium-chromium, and nickel-chromium-molybdenum, while relatively low-melting-point elements can be smelted to prepare another component, such as aluminum-silicon, aluminum-zinc, and copper-zinc. Furthermore, to ensure the precise addition of microalloying elements that have redox relationships with other alloy components, these microalloying elements can be pre-dissolved in a specific alloy composition. For example, yttrium can be pre-dissolved in aluminum, utilizing the reducing properties of aluminum to ensure the activity of the microalloying element and prevent excessive burn-off.

[0019] Therefore, based on the above, when preparing porous materials with specific alloy compositions by sintering, the present invention needs to prioritize design.

[0020] Based on current experimental results, the optimal design principle is to differentiate elements primarily by their melting points. Powder groups A and B are constructed separately, with powder group A consisting entirely of relatively high-melting-point elements and powder group B consisting primarily of relatively low-melting-point elements. This distinction is crucial because the difference in melting points between components during pre-powder preparation leads to component segregation. Furthermore, the initial separation of low-melting-point and high-melting-point elements ensures that the pre-alloyed powders composed of these elements are activated and form pores at different heat treatment stages during pore formation. Simultaneously, the element diffusion eutectic temperature is relatively uniform under this condition, simplifying the process. Moreover, since the high-melting-point components and microalloying elements in the multi-component system have already diffused uniformly beforehand, the high-temperature sintering time can be shortened, ensuring diffusion uniformity within a shorter timeframe.

[0021] The beneficial effects of this invention are: 1) This invention uses pre-alloyed powder as raw material and combines pre-alloyed powder with reaction synthesis process to transform the high-temperature sintering of multi-component alloys into a "pseudo" binary reaction. Elements that are easy to enrich or have high melting points are combined with elements with lower melting points or uniform diffusion in advance. For example, Y and Al form AlY pre-alloyed powder, and Cr combines with Ni and Fe to form NiFeCr powder. On the one hand, the prepared porous metal material has uniform distribution of each element, so it has good mechanical properties and corrosion resistance and long service life. On the other hand, it ensures the formability of the powder, promotes the sinterability of the mixed alloy powder, reduces the sintering difficulty of porous materials, and can obtain porous materials with good sintering neck and interconnected pore structure. 2) Compared with multi-component alloy powders that are entirely produced using pre-alloyed powder processes, this method has lower production requirements, is easier to prepare, and is more suitable for industrial production. 3) It can effectively avoid the problem of difficult composition control when using pre-alloyed powder diffusion sintering process. For different application environments, the ratio of each element in the porous sample can be easily controlled, thus achieving more matched performance. Attached Figure Description

[0022] Figure 1 This is a surface SEM image of the 316L+Al porous metal material prepared in Example 1 of this invention; Figure 2 This is a cross-sectional elemental distribution diagram of the 316L+Al porous metal material prepared in Example 1 of this invention; Figure 3 This is a cross-sectional elemental distribution diagram of the NiFeCrAl porous metal material prepared in Comparative Example 1 of this invention; Figure 4 This is a surface SEM image of the 316L+AlY porous metal material prepared in Example 2 of this invention; Figure 5 This is a cross-sectional Y and Al element distribution diagram of the 316L+AlY porous metallic material prepared in Example 2 of the present invention; Figure 5 This is a cross-sectional Y and Al elemental distribution diagram of the 316LAlY porous metallic material prepared in Comparative Example 2 of this invention; Figure 7 This is a surface SEM image of the Ni-CuZn porous metal material prepared in Example 4 of this invention. Detailed Implementation

[0023] The present invention will be further described clearly and in detail below with reference to specific embodiments and the accompanying drawings. Those skilled in the art will be able to implement the present invention based on these descriptions. Furthermore, the embodiments of the present invention described below are generally only some, not all, of the embodiments of the present invention. Therefore, all other embodiments obtained by those skilled in the art based on the embodiments of the present invention without inventive effort should fall within the scope of protection of the present invention.

[0024] Unless otherwise specified, all raw materials used in the embodiments of the present invention are commercially available or obtainable by those skilled in the art; unless otherwise specified, all methods used in the embodiments of the present invention are methods mastered by those skilled in the art.

[0025] Example 1 A method for preparing multi-component alloy porous materials by pseudobinary reaction, specifically comprising: (1) Powder preparation: Take 316L powder with a particle size of 40-55μm (purity >99.5wt%, Fe 71wt%, Ni 12wt%, Cr 17wt%) and Al powder (particle size about 60 μm, purity >99.5wt%), and mix 90% 316L powder and 10% Al powder by mass percentage. Use a V-type mixer under nitrogen protection to mix the powder to form a mixed powder. In order to obtain a uniform mixture, add zirconia balls to the original powder to improve the mixing efficiency. Each batch of powder is mixed for 24 hours. (2) Granulation: Then, ethanol is used as a solvent to mix with stearic acid accounting for 2.0 wt.% of the total mass of the mixed powder to granulate in order to improve the sample pressing and molding effect; (3) Pressing: After drying the granulated mixed powder and pulverizing it twice through a 100-mesh sieve, it is placed in a molding mold and pressed into a sheet (φ10mm×2.0mm); (4) Sintering: at a vacuum degree below 1.0×10 -2 In Pa's vacuum sintering furnace, a stepwise sintering method was used for the reaction synthesis of green compacts. The temperature was increased from room temperature to 150°C at a rate of 10°C / min and held at this temperature for 10 min to remove gas molecules adsorbed by the green compacts. The temperature was then increased to 450°C at a rate of 10°C / min and held at this temperature for 30 min to remove the binder in the green compacts. The temperature was then increased to 620°C at a rate of 3°C / min and held at this temperature for 2 h to prevent the aluminothermic reaction and promote the Kirkendal effect of diffusive diffusion, which produces a large number of pores. The temperature was then increased to 1240°C at a rate of 5°C / min and held for 2 h to promote the diffusion between elements and the growth of sintering necks to obtain a multi-component alloy porous material with uniform composition, good sintering necks, and interconnected pore structure.

[0026] The prepared multi-component alloy porous material was characterized by SEM and elemental mapping. The characterization results are as follows: Figure 1 and Figure 2 As shown in the figure, the characterization results clearly demonstrate that a stable porous structure was effectively constructed during the preparation process in this example, forming a multi-layered sintered neck and pore structure. Based on the pore structure, a multi-layered three-dimensional structure was further formed. Furthermore, in the elemental characterization results, Fe, Ni, Cr, and Al all exhibited extremely high distribution uniformity. Especially for Fe, Ni, and Cr, they achieved a highly uniform dispersion with a highly consistent elemental distribution and virtually no segregation.

[0027] Comparative Example 1 A method for preparing a multi-component alloy porous material, which is based on the preparation process of Example 1, except that: Replace the 316L powder with the corresponding proportions of Fe powder, Ni powder and Cr powder.

[0028] Based on the multi-component alloy porous material prepared by the above method, the prepared multi-component alloy porous material was characterized by mapping. The characterization results are as follows: Figure 3 As shown. From Figure 3 The characterization results clearly show that Cr exhibits significant segregation and enrichment. This is mainly because chromium has a significantly higher melting point than other elements, while aluminum has an extremely low melting point. When prepared by directly mixing metal powders, the large difference in melting points between the components causes the aluminum powder to melt prematurely, encapsulating the molten chromium powder and resulting in significant component segregation. In particular, comparing the distribution trends of the four elements reveals that Cr and Al show a higher following rate and a certain "complementary" trend, which confirms the above statement.

[0029] Example 2 A method for preparing multi-component alloy porous materials by pseudobinary reaction, specifically comprising: (1) Powder preparation: Take 316L powder with a particle size of 40-55μm (purity >99.5wt%, Fe 71wt%, Ni 12wt%, Cr 17wt%) and AlY powder (particle size about 60 μm, Al 90wt%, Y 10wt%), and mix 90% of 316L powder and 10% of Al powder by mass percentage. Use a V-type mixer under nitrogen protection to mix the powders into a mixed powder. In order to obtain a uniform mixture, zirconia balls are added to the original powder to improve the mixing efficiency. Each batch of powder is mixed for 24 hours. (2) Granulation: Then, ethanol is used as a solvent to mix with stearic acid accounting for 2.0 wt.% of the total mass of the mixed powder to granulate in order to improve the sample pressing and molding effect; (3) Pressing: After drying the granulated mixed powder and pulverizing it twice through a 100-mesh sieve, it is placed in a molding mold and pressed into a sheet (φ10mm×2.0mm); (4) Sintering: at a vacuum degree below 1.0×10 -2 In a vacuum sintering furnace of Pa, a stepwise sintering method was used to synthesize the green body through reaction. The temperature was increased from room temperature to 150°C at a rate of 10°C / min and held at this temperature for 10 min to remove the gas molecules adsorbed in the green body. Then, the temperature was increased to 450°C at a rate of 10°C / min and held at this temperature for 30 min to remove the binder in the green body. Then, the temperature was increased to 620°C at a rate of 3°C / min and held at this temperature for 2 h. Finally, the temperature was increased to 1240°C at a rate of 5°C / min and held for 2 h to obtain a multi-component alloy porous material with uniform composition, good sintering neck and interconnected pore structure.

[0030] It was also characterized using SEM, and the characterization results are as follows: Figure 4 As shown in the figure, it is clear from the figure that the multilayer sintered neck and pore structure prepared in this example, while maintaining porosity and structural stability, further increases the specific surface area and reduces the density of the material, thus achieving lightweighting and a larger active area. Furthermore, the multi-component alloy porous material prepared in this example was characterized using the same elemental distribution methods. In this example, Y and Al were the key elements observed. Figure 5 Only the distribution of Y and Al elements is shown. From... Figure 5 The results show that Al and Y maintain a high degree of dispersion and overlap, without significant segregation.

[0031] Comparative Example 2 A method for preparing a multi-component alloy porous material, which is based on the preparation process of Example 1, except that: Replace the AlY powder with the appropriate ratio of Y powder and Al powder.

[0032] Based on the multi-component alloy porous material prepared by the above method, the prepared multi-component alloy porous material was characterized by mapping. The characterization results are as follows: Figure 6 As shown. In this example, the products are mainly observed for Y and Al elements, therefore... Figure 6 The table only shows the distribution of Y and Al elements. Based on the above, it is clear that when Y and Al are added separately, Y cannot be effectively dispersed in Al initially, resulting in very obvious segregation. Furthermore, based on the overall distribution chart, the actual Y element segregation areas also contain a significant amount of O element. This indicates that when metallic Y powder is added alone, it exhibits strong reduction characteristics, which leads to oxidation and the reduction of some oxides. These oxides tend to be components in powder group A (i.e., 316L powder).

[0033] Therefore, when using additional elements with strong reducing properties, elements such as Al, which are easily diffused and have low melting points, should be used for protection to form homogenization and prevent segregation during the early-stage medium-temperature sintering. Thus, even though yttrium has a high melting point, it should not be added to powder group A for use.

[0034] Example 3 A method for preparing multi-component alloy porous materials by pseudobinary reaction, specifically comprising: (1) Powder preparation: Take FeCoNiCr pre-alloyed powder (Fe 25wt%, Co 25wt%, Ni 25wt%, Cr 25wt%) with a particle size of 50-60 μm and Al powder (particle size of about 60 μm, purity >99.5wt%), and mix 90% FeCoNiCr pre-alloyed powder and 10% Al powder by mass percentage. Use a V-type mixer under nitrogen protection to mix the powder into a mixed powder. In order to obtain a uniform mixture, add zirconia balls to the original powder to improve the mixing efficiency. Each batch of powder is mixed for 24 hours. (2) Granulation: Then, ethanol is used as a solvent to mix with stearic acid accounting for 2.0 wt.% of the total mass of the mixed powder to granulate in order to improve the sample pressing and molding effect; (3) Pressing: After drying the granulated mixed powder and pulverizing it twice through a 100-mesh sieve, it is placed in a molding mold and pressed into a sheet (φ10mm×2.0mm); (4) Sintering: at a vacuum degree below 1.0×10 -2 In a vacuum sintering furnace of Pa, a stepwise sintering method was used to synthesize the green body through reaction. The temperature was increased from room temperature to 150°C at a rate of 10°C / min and held at this temperature for 10 min to remove the gas molecules adsorbed in the green body. Then, the temperature was increased to 450°C at a rate of 10°C / min and held at this temperature for 30 min to remove the binder in the green body. Then, the temperature was increased to 620°C at a rate of 3°C / min and held at this temperature for 2 h. Finally, the temperature was increased to 1240°C at a rate of 5°C / min and held for 2 h to obtain a multi-component alloy porous material with uniform composition, good sintering neck and interconnected pore structure.

[0035] The obtained multi-component alloy porous material was characterized by SEM. The characterization results showed that its sintered neck structure was similar to that of Examples 1 and 2, and it had a good multi-layer sintered neck and pore structure. While maintaining porosity and structural stability, the specific surface area of ​​the material was further increased and the density of the material was reduced, so that it could be lightweight and have a larger active area.

[0036] Example 4 A method for preparing multi-component alloy porous materials by pseudobinary reaction, specifically comprising: (1) Powder preparation: Take CuZn pre-alloyed powder (Cu 85wt%, Zn 15wt%) with a particle size of 50-60 μm and Ni powder (particle size of about 50-55 μm, purity >99.5wt%), and mix 90% Ni powder and 10% CuZn powder by mass percentage. Use a V-type mixer under nitrogen protection to mix the powder. In order to obtain a uniform mixture, add zirconia balls to the original powder to improve the mixing efficiency. Each batch of powder is mixed for 24 hours. (2) Granulation: Then, ethanol is used as a solvent to mix with stearic acid accounting for 2.0 wt.% of the total mass of the mixed powder to granulate in order to improve the sample pressing and molding effect; (3) Pressing: After drying the granulated mixed powder and pulverizing it twice through a 100-mesh sieve, it is placed in a molding mold and pressed into a sheet (φ10mm×2.0mm); (4) Sintering: at a vacuum degree below 1.0×10 -2 In a vacuum sintering furnace of Pa, a stepwise sintering method was used to synthesize the green body through reaction. The temperature was increased from room temperature to 150°C at a rate of 10°C / min and held at this temperature for 10 min to remove the gas molecules adsorbed in the green body. Then, the temperature was increased to 450°C at a rate of 10°C / min and held at this temperature for 30 min to remove the binder in the green body. Then, the temperature was increased to 620°C at a rate of 3°C / min and held at this temperature for 2 h. Finally, the temperature was increased to 1240°C at a rate of 5°C / min and held for 2 h to obtain a multi-component alloy porous material with uniform composition, good sintering neck and interconnected pore structure.

[0037] The obtained multi-component alloy porous material was characterized by SEM, and the characterization results are as follows: Figure 7 As shown. In the actual pre-alloyed powder used in this invention, the amount of powder group A is much greater than that of powder group B. The actual sintering results are similar to those of Examples 1-3, maintaining a good multilayer sintering neck and pore structure. However, comparing Comparative Examples 1 and 2, it can be found that when the component elements of the target multi-component alloy porous material are simply mixed, significant segregation occurs, leading to changes in its structure and composition. It is evident that the pre-alloyed powder constructed by differentiating powder groups by melting point in this invention has a significant effect on the sintering of multi-component alloy porous materials, achieving a positive optimization effect. It plays a positive role and influence on the uniform distribution of components and the control of micro-nano structures such as layers and pores in multi-component alloy porous materials, and has broad application prospects.

Claims

1. A method for preparing multi-component alloy porous materials by pseudobinary reaction, characterized in that, The method includes: 1) Take powder group A and powder group B separately, and mix them well to form a mixed powder; 2) The mixed powder is pressed into a green body, and the green body is sintered to obtain a multi-component alloy porous material; Step 1) Powder group A is a single or pre-alloyed powder containing one or more non-rare earth metal elements and / or rare earth elements as components, and powder group B is a single or pre-alloyed powder containing one or more non-rare earth metal elements and / or rare earth elements and / or silicon as components, and powder group A and powder group B are not both single elements. Step 1) The powder group A consists of non-rare earth metal elements and / or relatively high melting point elements among rare earth elements, wherein the melting point of the relatively high melting point elements is ≥1450 ℃; Step 1) The main elements contained in powder group B are all non-rare earth metal elements and / or relatively low melting point elements of rare earth elements, and / or silicon. The melting point of the non-rare earth metal elements and / or relatively low melting point elements of rare earth elements is ≤1100℃, and the content of the main elements is controlled to be ≥90 wt% of the total mass of powder group B. Step 1) The powder group B also contains additional elements; The additional element is a relatively high melting point element, and the additional element can be used to reduce the oxide of the relatively high melting point element used in powder group A.

2. The method for preparing multi-component alloy porous materials by pseudobinary reaction according to claim 1, characterized in that, The pre-alloyed powder is prepared by smelting and combining water atomization and / or gas atomization and / or centrifugal atomization, and the pre-alloyed powder obtained by this method has a particle size of 10 to 100 μm.

3. The method for preparing multi-component alloy porous materials by pseudobinary reaction according to claim 1, characterized in that, Step 2) The compression molding control pressure is 50-250 MPa.

4. The method for preparing multi-component alloy porous materials by pseudobinary reaction according to claim 1, characterized in that, Step 2) The sintering process includes low-temperature sintering, medium-temperature sintering, and high-temperature sintering in sequence; The low-temperature sintering is used for degassing and / or degumming; The intermediate-temperature sintering is used to induce the Kirkendall effect; The high-temperature sintering is carried out at a temperature of ≥1150 ℃, which is lower than the melting point of the components contained in powder group A.

5. The method for preparing multi-component alloy porous materials by pseudobinary reaction according to claim 4, characterized in that, The total holding time for the low-temperature sintering is 20–60 min; The medium-temperature sintering holding time is 1–3 h; The high-temperature sintering holding time is 1 to 3 hours.

6. A method for preparing multi-component alloy porous materials by pseudobinary reaction according to claim 1, 4, or 5, characterized in that, Step 2) The sintering is carried out in a reducing atmosphere and / or under inert gas protection and / or vacuum conditions; When the sintering is carried out under vacuum conditions, the vacuum level is controlled to be 1.0 × 10⁻⁶. -2 ~1×10 0 Pa.

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