Alloy powder and method of making and use thereof

Abstract

The present application relates to a kind of alloy powder and its preparation method and use.Select suitable alloy system, by low-purity raw material smelting initial alloy melt, high-purity alloy powder and the matrix phase of high-purity alloy powder coated are precipitated in the process of initial alloy melt solidification, while realizing the solid solution alloying of high-purity alloy powder.The matrix phase of high-purity alloy powder coated is removed, and alloy powder can be obtained;Also, the matrix phase of high-purity alloy powder coated can be removed at a suitable time, so as to obtain high-purity alloy powder.The method is simple, and various alloy powder materials including nanoscale, submicron, micron, even millimeter level of different morphology can be prepared, which has good application prospect in catalysis, powder metallurgy, composite materials, magnetic materials, sterilization, metal injection molding, metal powder 3D printing, coating, composite materials and other fields.

Description

Technical Field

[0001] This invention relates to the field of metallic materials technology, and in particular to a type of alloy powder, its preparation method, and its uses. Background Technology

[0002] Metal powders with micro- and nano-sized particles exhibit unique properties in optics, electricity, magnetism, and catalysis that differ from traditional materials due to their special surface effects, quantum size effects, quantum tunneling effects, and Coulomb blocking effects. As a result, they are widely used in optoelectronic devices, microwave absorbing materials, high-efficiency catalysts, and many other fields.

[0003] Currently, metal powder preparation methods are categorized by the state of matter into solid-phase, liquid-phase, and gas-phase methods. Solid-phase methods mainly include mechanical grinding, ultrasonic grinding, thermal decomposition, and explosion methods. Liquid-phase methods mainly include precipitation, alkoxide methods, carbonyl methods, spray drying, freeze-drying, electrolysis, and chemical condensation methods. Gas-phase methods mainly include gas-phase reaction methods, plasma methods, high-temperature plasma methods, evaporation methods, and chemical vapor deposition. Although there are many methods for preparing metal powders, each method has certain limitations. For example, liquid-phase methods suffer from low yield, high cost, and complex processes. Mechanical methods are disadvantaged by difficulties in classifying the powder after preparation, and the purity, fineness, and morphology of the product are difficult to guarantee. Rotating electrode methods and gas atomization methods are currently the main methods for preparing high-performance metal and alloy powders, but they have low production efficiency, low yield of ultrafine powders, and relatively high energy consumption. Air jet milling and hydrogenation dehydrogenation methods are suitable for large-scale industrial production, but they have strong selectivity for raw material metals and alloys. Furthermore, the impurity content, especially the oxygen content, of metal powders or alloy powders has a significant impact on their performance. Currently, the impurity content of metal powders or alloy powders is mainly controlled by adjusting the purity of raw materials and the vacuum level, which is costly. Therefore, developing new methods for preparing high-purity metal powder materials is of great significance. Summary of the Invention

[0004] Therefore, it is necessary to provide a method for preparing high-purity alloy powder materials that is simple in process, low in cost, and easy to operate, in order to address the above-mentioned technical problems.

[0005] To solve the above-mentioned technical problems, the technical solution of the present invention is as follows:

[0006] A metallic material composed of endogenous alloy powder and a coating body, characterized in that it is prepared by solidification of an alloy melt, and its composition includes a dispersed particle phase precipitated endogenously during the initial alloy solidification process and a matrix phase coating the dispersed particles, which respectively correspond to the endogenous alloy powder and the coating body; the elemental composition of the endogenous alloy powder is mainly M. a1 A b1 T c1The elemental composition of the coating is mainly A. b2 T c2 M and A each contain one or more metallic elements, T is an impurity element including oxygen, and a1, b1, c1, b2, and c2 represent the atomic percentage content of the corresponding elements, where a1+b1+c1=100%, b2+c2=100%, c2>c1>0, and b1>0; the melting point of the endogenous alloy powder is higher than the melting point of the coating; the endogenous alloy powder M a1 A b1 T c1 The solid contains element A; the M and the A contain one or more groups of M that do not form intermetallic compounds. 1 -A 1 Combinations of elements, where M 1 A represents any element in M. 1 Let M represent any element in A, and let M be the principal element satisfying M 1 -A 1 M of the element combination conditions 1 The main elements in A are composed of elements that satisfy M. 1 -A 1 Each A in the element combination condition 1 The elemental composition ensures that after the metallic material composed of the endogenous alloy powder and the coating is completely melted and resolidified, it does not form an intermetallic compound composed of the main elements in M ​​and A, but instead forms the endogenous alloy powder M. a1 A b1 T c1 With the coating body A b2 T c2 .

[0007] Additional explanation: T refers to impurity elements including oxygen, meaning that T is an impurity element and includes O.

[0008] The solidification methods of the initial alloy melt include conventional casting, continuous casting, melt casting, and melt drawing. The particle size of the endogenous alloy powder is related to the solidification rate of the initial alloy melt. Generally speaking, the particle size of the endogenous alloy powder is negatively correlated with the solidification rate of the initial alloy melt; that is, the greater the solidification rate of the initial alloy melt, the smaller the particle size of the endogenous alloy powder.

[0009] Furthermore, the solidification method of the initial alloy melt does not include the solidification method corresponding to the atomization powdering technology;

[0010] Additional note: The solidification rate of the initial alloy melt ranges from 0.001 K / s to 10 K / s. 8 K / s;

[0011] Furthermore, the solidification rate of the initial alloy melt ranges from 0.001 K / s to 10 K / s. 7 K / s;

[0012] Furthermore, the particle size range of the endogenous alloy powder includes 3 nm to 10 mm.

[0013] Additional note: The particle size range of the endogenous alloy powder is 3nm to 1mm;

[0014] Preferably, the particle size range of the endogenous alloy powder is 3 nm to 500 μm;

[0015] Preferably, the particle size range of the endogenous alloy powder is 3 nm to 99 μm;

[0016] Preferably, the particle size range of the endogenous alloy powder is 3 nm to 25 μm;

[0017] Preferably, the particle size range of the endogenous alloy powder is 3 nm to 10 μm;

[0018] Furthermore, the particle shape of the endogenous alloy powder is not limited, and may include at least one of dendritic, spherical, near-spherical, cubic, disc-shaped, and rod-shaped; when the particle shape is rod-shaped, the particle size specifically refers to the diameter of the rod cross-section.

[0019] The shape of the metallic material composed of endogenous alloy powder and coating is related to the solidification method: when the solidification method is continuous casting, its shape is generally mainly lath-shaped; when the solidification method is melt casting, its shape is generally mainly strip-shaped or thin plate-shaped; when the solidification method is melt drawing, its shape is generally mainly filament-shaped. The higher the solidification rate, the thinner, finer, and narrower the cross-section of the metallic material composed of endogenous alloy powder and coating; conversely, the lower the solidification rate, the thicker, coarser, and wider the cross-section.

[0020] Furthermore, the shape of the metal material composed of endogenous alloy powder and coating does not include the powder form of products corresponding to atomization powdering technology;

[0021] Furthermore, when the initial alloy melt solidifies by means including melt spinning, and the solidification rate is 100 K / s to 10 7 At K / s, a metallic material strip composed of endogenous alloy powder and a coating body with a thickness of about 10 μm to 5 mm can be obtained, and the particle size of the endogenous alloy powder is in the range of 3 nm to 200 μm.

[0022] Furthermore, when the initial alloy melt is solidified by means including ordinary casting or continuous casting, and the solidification rate is 0.001K / s to 100K / s, a blocky metallic material composed of endogenous alloy powder and a coating body with a size exceeding 5mm in at least one dimension in the three-dimensional direction can be obtained, wherein the particle size of the endogenous alloy powder is in the range of 200μm to 10mm.

[0023] Additional explanation: Furthermore, the metallic material formed by the endogenous alloy powder and the coating is strip-shaped, and the strip thickness is 5μm to 5mm;

[0024] Furthermore, the metallic material formed by the endogenous alloy powder and the coating is strip-shaped, and the strip thickness is 10μm to 1mm;

[0025] Furthermore, the lower limit of the volume percentage content of the endogenous alloy powder in the metal material composed of the endogenous alloy powder and the coating is 1%, and the upper limit is the volume percentage content corresponding to the condition that the endogenous alloy powder can be dispersed in the coating.

[0026] When considering the amount of dispersed endogenous alloy powder that can be coated within a coating, an accurate evaluation is needed based on the volume percentage content of the endogenous alloy powder, as volume relationships are directly related to the ability of the endogenous alloy powder to disperse. This volume percentage content can be calculated by converting the density, atomic weight, and other relationships of each element to the atomic percentage content. When the matrix element of the coating is a large atomic element, the matrix can achieve a higher volume percentage content with a smaller atomic percentage content, thereby significantly increasing the amount of endogenous alloy powder that can be coated. For example, an atomic percentage composition of Ce... 50 Ti 50 The alloy melt has Ce and Ti weight percentages of 74.53 wt% and 25.47 wt%, respectively, and their densities are 6.7 g / cm³. 3 With 4.5g / cm 3 The atomic percentage content of Ce and Ti can be calculated as Ce 50 Ti 50 The volume percentages of Ti in the melt are 66 vol% and 34 vol%, respectively. If Ti precipitates from the melt, its volume percentage is only about 34 vol%, without considering solid solution and impurities. This indicates that even if the atomic percentage of Ti in the Ce-Ti alloy exceeds 50%, its volume percentage can still be significantly lower than 50%, which is beneficial for obtaining dispersed Ti particles.

[0027] Since the application of the metallic material composed of endogenous alloy powder and coating material mainly depends on the effect of the endogenous alloy powder, and the coating material needs to be removed subsequently, when the volume percentage of endogenous alloy powder is less than 1%, it will result in a significant waste of coating material, thus negating the practical significance of the material application.

[0028] Due to different alloy systems and solidification rates, the size and morphology of the resulting endogenous alloy powders also differ. For example, when the cooling rate is relatively fast, the endogenous alloy powder is mainly composed of fine spherical or near-spherical nanoparticles. The growth of these particles is limited, and the particles tend to maintain a certain space and distance between each other. Under the condition of ensuring the diffuse distribution of the endogenous alloy powder, a high volume percentage content can be achieved. When the cooling rate is relatively low, the endogenous alloy powder is mainly composed of coarse dendrites. The growth of these particles is very sufficient, and different particles tend to meet, merge, and entangle during the growth process. Under the condition of ensuring the diffuse distribution of the endogenous dendritic alloy particles, the endogenous dendritic alloy powder can only achieve a relatively low volume percentage content.

[0029] Preferably, the volume percentage content of the endogenous alloy powder in the metallic material composed of the endogenous alloy powder and the coating body ranges from 5% to 50%.

[0030] As a further preferred embodiment, the volume percentage content of the endogenous alloy powder in the metallic material composed of the endogenous alloy powder and the coating body ranges from 5% to 40%; the preferred lower limit ensures economic efficiency, and the preferred upper limit fully ensures that the endogenous alloy powder can be dispersed in the coating body.

[0031] The endogenous alloy powder solidifies and precipitates from the initial melt. According to the nucleation and growth theory, whether it is a near-spherical nanoparticle that has just nucleated and grown or a fully grown micron-sized dendritic particle, its crystal growth has a fixed orientation relationship, so that the precipitated individual particles are mainly composed of a single crystal.

[0032] When the volume percentage of the endogenous alloy powder is high, the possibility of two or more particles merging during the endogenous precipitation of single-crystal particles cannot be ruled out. If two or more single-crystal particles merely softly agglomerate, mutually adsorb, or only partially connect in contact, without fully combining into a single particle through normal grain boundaries as in polycrystalline materials, they remain two single-crystal particles. A key characteristic is that after removing the coating in subsequent processes, these single-crystal particles can be easily separated using techniques including ultrasonic dispersion and air jet milling. In contrast, normal ductile polycrystalline metallic materials are difficult to separate through techniques such as ultrasonic dispersion and air jet milling.

[0033] Preferably, the number of single-crystal particles in the endogenous alloy powder accounts for no less than 60% of the total number of particles.

[0034] As a further preferred embodiment, the number of single-crystal particles in the endogenous alloy powder accounts for no less than 75% of the total number of particles.

[0035] As a further preferred embodiment, the number of single-crystal particles in the endogenous alloy powder accounts for no less than 90% of the total number of particles.

[0036] Additional explanation: In the metallic material composed of endogenous alloy powder and coating, both the endogenous alloy powder and the coating are crystalline.

[0037] The elemental composition of the endogenous alloy powder is mainly M. a1 A b1 T c1 The elemental composition of the coating is mainly A. b2 T c2 M and A each contain one or more metallic elements, T is an impurity element including oxygen, and a1, b1, c1, b2, c2 represent the atomic percentage content of the corresponding elements, and a1+b1+c1=100%, b2+c2=100%.

[0038] Characterizing the composition of elements by atomic percentage allows for accurate expression of changes in element content, such as the increase or decrease of impurity elements, through the concept of amount of substance. However, using mass percentage (or ppm) to characterize the content of individual elements can easily lead to erroneous conclusions due to the differences in atomic weights. For example, if the atomic percentage of Ti is... 45 Gd 45 O 10 The alloy contains 100 atoms, with an oxygen atomic percentage of 10 at%. These 100 atoms are divided into Ti... 45 O4 (atomic percentage composition is Ti) 91.8 O 8.2 ) and Gd 45 O6 (atomic percentage composition is Gd) 88.2 O 11.8 Two parts, Gd 45 The atomic percentage of oxygen in O6 increases to 11.8 at%, and Ti 45 The atomic percentage of oxygen in O4 is reduced to 8.2 at%, which accurately represents the enrichment of O in Gd. However, if the mass percentage of O is used as the measurement, Ti... 45 Gd 45 O 10 The mass percentage content of O in the sample is 1.70 wt%, and the Ti content is... 45 O4 and Gd 45The mass percentage contents of O in O6 are 2.9wt.% and 1.34wt.% respectively, it will be concluded that Ti 40 the O content in O4 is compared with Gd 40 the wrong conclusion that the O content in O6 increases significantly.

[0039] Further, the endogenous alloy powder M a1 A b1 T c1 has a melting point higher than that of the coating body A b2 T c2 When this condition is satisfied, the matrix phase solidifies lastly during the solidification of the initial alloy, and coats the endogenously formed alloy powder.

[0040] Further, in the endogenously formed alloy powder M a1 A b1 T c1 element A is dissolved in solid state, where 0 < b1.

[0041] Preferably, 0 < b1 ≤ 15%; that is, M a1 A b1 T c1 can be solidly dissolved with at most 15% of element A (atomic percentage content). According to different main element compositions of the specific alloy melt, different impurity contents and different solidification rates, the solid solubility of A in M a1 A b1 T c1 endogenous alloy powder is also different. Generally, when the solidification rate of the melt is high and small endogenously formed alloy powder, such as nanopowder, is formed, more element A can be dissolved in solid state.

[0042] Further, the endogenously formed alloy powder contains a certain amount of impurity T, and the content of impurity T in the endogenously formed alloy powder is lower than the content of impurity T in the corresponding coating body, that is, c2 > c1 > 0. This shows that, in the metal material composed of the endogenously formed alloy powder and the coating body prepared by solidification of the alloy melt, impurity elements will be enriched in the coating body A b2 T c2 and at the same time M a1 A b1 T c1 endogenous alloy powder is purified.

[0043] Further, T is impurity elements including oxygen, such as O, H, N, P, S, F, Cl, and 0 < c1 ≤ 1.5%.

[0044] Additional explanation: That is to say, T contains O, and the content of O is greater than zero; among the elements H, N, P, S, F, and Cl listed above, the content of a certain element is zero when it is not present, and greater than zero when it is present; the content of T is the total content of elements O, H, N, P, S, F, and Cl.

[0045] Preferably, T is an impurity element including oxygen such as O, H, N, P, S, F, and Cl, and 0.01% ≤ c1 ≤ 1.5%.

[0046] Both M and A contain one or more metallic elements, and the selection of M and A is crucial for preparing the metallic material composed of endogenous alloy powder and a coating. This is to ensure that no intermetallic compound composed of the main elements in M ​​and A is formed during the solidification of the alloy melt, but rather that the endogenous alloy powder M is formed instead. a1 A b1 T c1 With the coating body A b2 T c2 M and A need to satisfy the following relationship:

[0047] The M and the A contain one or more groups of M that do not form intermetallic compounds. 1 -A 1 Element combination; where M 1 A represents any element in M. 1 Let M represent any element in A, and let M be the principal element satisfying M 1 -A 1 M of the element combination conditions 1 The main elements in A are composed of elements that satisfy M. 1 -A 1 Each A in the element combination condition 1 Composition of elements.

[0048] Furthermore, in M ​​or A, when each of the above combination conditions is satisfied... 1 Element or each A 1 When the atomic percentage of an element accounts for more than 30% of that in M ​​or A, it can be called the main element in M ​​or A, respectively.

[0049] Furthermore, when M contains at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti, Fe, Co, Ni, Mn, Cu, and Ag, and A contains at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, Mg, Ca, Li, Na, K, In, Pb, and Zn, it satisfies the requirement that no intermetallic compounds composed of the main elements in M ​​and A will be formed during the solidification of the alloy melt. According to the alloy phase diagram, for any element in M ​​listed above, a corresponding M that does not form intermetallic compounds can be found in A. 1 -A 1 Combination pairs, such as Cr-Y, Ti-Ce, Fe-Mg, Co-K, Ni-Li, Mn-Mg, Cu-Li, Ag-Pb combination pairs, etc. When there are multiple M pairs between M and A. 1 -A 1 When combining pairs, each M 1 The set of A and each A 1 The set of these alloys will still satisfy the condition that no corresponding intermetallic compounds are formed during the solidification of the alloy melt. For example, Ti-Ce, Ti-Gd, Nb-Ce, and Nb-Gd all satisfy M 1 -A 1 Under the combined condition, (Ti-Nb)-(Ce-Gd) will still satisfy the combined condition that no intermetallic compounds are formed during the solidification of the corresponding alloy melt. In this case, the main elements in M ​​include Ti and Nb; the main elements in A include Ce and Gd.

[0050] Furthermore, when the main elements in M ​​and the main elements in A satisfy one or more sets of M 1 -A 1 Under the condition of combination pairs, if M also contains elements that can combine with the main element M in M... 1 Element M forms stable high-melting-point intermetallic compounds 2 At that time, M 1 With M 2 It will form M, which exists in a high melting point. 1 -M 2 Intermetallic compounds, and M 1 With M 2 Neither of them forms intermetallic compounds with the main element in A. In this case, the endogenous alloy powder is M. 1 -M 2 Intermetallic compound powder.

[0051] Preferably, M comprises at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, and Ti, and A comprises at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu.

[0052] Preferably, when M contains at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, and Ti, and at least one of Fe, Co, and Ni, a high-melting-point intermetallic compound can be formed between the two sub-elements in M. When A contains at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu, an endogenous intermetallic compound powder mainly composed of the two sub-elements in M ​​can be formed.

[0053] Preferably, M contains at least one of the sub-elements W, Cr, Mo, V, Ta, Nb, Zr, Hf, and Ti, and at least one of the sub-elements Fe, Co, and Ni. When the molar ratio of the two sub-elements is approximately 1:1, a stable high-melting-point intermetallic compound can be formed between the two sub-elements in M. When A contains at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu, an endogenous intermetallic compound powder mainly composed of the two sub-elements in M ​​with a molar ratio of approximately 1:1 is formed during the solidification of the alloy melt, as well as a coating mainly composed of element A.

[0054] Preferably, M includes at least one of Mn, Fe, Ni, Cu, and Ag, and A includes at least one of Mg, La, In, Na, K, Li, and Pb.

[0055] Furthermore, M includes at least one of Ir, Ru, Re, Os, Tc, W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti, and Fe, and A includes at least one of Cu and Zn.

[0056] Additional explanation: Furthermore, M includes at least one of Ir, Ru, Re, Os, Tc, W, Cr, Mo, V, Ta, and Nb, and A includes Cu.

[0057] Furthermore, M includes at least one of Ir, Ru, Re, Os, and Tc, and A includes Cu.

[0058] It should be noted that A, M, or T may also contain other alloying elements or impurity elements besides those listed above. As long as changes in the content of these elements do not cause a "qualitative change" in the initial alloy solidification process and its regularity, they will not affect the realization of the above-mentioned technical solution of the present invention.

[0059] This invention also relates to an alloy powder, prepared by removing the coating from a metallic material composed of endogenous alloy powder and a coating, characterized in that its elemental composition is mainly M. a3A b3 T c3 a3, b3, and c3 represent the atomic percentage content of the corresponding elements, b3>0, a3+b3+c3=100%, and the T element content in the alloy powder is higher than the T element content in the endogenous alloy powder, i.e., c3>c1>0.

[0060] The alloy powder is prepared by removing the coating from the metallic material composed of endogenous alloy powder and a coating. Therefore, most of the characteristics of the alloy powder are consistent with those of the endogenous alloy powder. The difference is that the endogenous alloy powder is coated in a coating, eliminating the influence of impurities such as oxygen in the environment. However, when the alloy powder, especially when the particle size is fine, such as nano-alloy powder, is exposed, the surface or surface layer atoms of the alloy powder will combine with impurity elements such as oxygen, resulting in an increase in its nitrogen (T) content, i.e., c3>c1>0.

[0061] Preferably, the number of single-crystal particles in the alloy powder accounts for no less than 60% of the total number of particles.

[0062] As a further preferred embodiment, the number of single-crystal particles in the alloy powder accounts for no less than 75% of the total number of particles.

[0063] As a further preferred embodiment, the number of single-crystal particles in the alloy powder accounts for no less than 90% of the total number of particles.

[0064] Preferably, the particle size of the alloy powder is in the range of 3nm-10mm.

[0065] Additional note: The particle size range of the alloy powder is 3nm to 1mm;

[0066] Preferably, the particle size of the alloy powder is in the range of 3 nm to 500 μm;

[0067] Preferably, the particle size of the alloy powder ranges from 3 nm to 99 μm;

[0068] Preferably, the particle size of the alloy powder is in the range of 3 nm to 25 μm;

[0069] Preferably, the particle size of the alloy powder is in the range of 3 nm to 10 μm;

[0070] Preferably, the particle size of the alloy powder is in the range of 3 nm to 5 μm;

[0071] This invention also relates to a spherical or near-spherical alloy powder, characterized in that the alloy powder described above is subjected to plasma spheroidization treatment to obtain the spherical or near-spherical alloy powder. Its elemental composition is primarily M. a4 A b4 Tc4 , a4, b4 and c4 respectively represent the atomic percentage content of the corresponding constituent elements, with b4>0, a4+b4+c4=100%, and the content of element T in the spherical or nearly spherical alloy powder is higher than the content of element T in the alloy powder not subjected to plasma spheroidization treatment, that is, c4>c3>c1>0.

[0072] Further, before the plasma spheroidization treatment, jet milling pre-crushing treatment is performed on the selected particles, so that possibly entangled particles are dispersed and crushed, which is beneficial to the subsequent spheroidization treatment.

[0073] Further, a screening treatment is performed on the alloy powder before the plasma spheroidization treatment;

[0074] Further, the particle size range of the alloy powder subjected to plasma spheroidization treatment is 5μm-200μm.

[0075] To be supplementary, the particle size range of the alloy powder subjected to plasma spheroidization treatment is 5μm-100μm.

[0076] The present invention also relates to a preparation method of a metal material composed of endogenous alloy powder and a cladding body, characterized in that it is prepared by the following steps:

[0077] (1) Smelting an initial alloy melt with a main elemental composition of M a0 A b0 T c0 , wherein both M and A comprise one or more metal elements, T is an impurity element including oxygen, a0, b0 and c0 represent the atomic percentage content of the corresponding constituent elements, a0+b0+c0=100%, 0<c0≤15%; one or more groups of M that do not form intermetallic compounds are comprised between said element M and said element A 1 -A 1 element combination, wherein M 1 represents any element in M, A 1 represents any element in A; and the main elements in M are composed of various M elements satisfying the M 1 -A 1 element combination condition, and the main elements in A are composed of various A elements satisfying the M 1 element combination condition, and the main elements in A are composed of various A elements satisfying the M 1 -A 1 element combination condition, and the main elements in A are composed of various A 1 elements;

[0078] (2) Solidifying said M a0 A b0 T c0 initial alloy melt into a solid state, to obtain endogenously precipitated M from the melt a1 A b1 T c1A dispersed particle phase and A coating dispersed particles b2 T c2 a matrix phase, which is exactly the metal material composed of the endogenous alloy powder and the cladding body; wherein 0 < c1 < c0 < c2, that is, M a0 A b0 T c0 the content of element T in the initial alloy melt is higher than that of M a1 A b1 T c1 the content of element T in the dispersed particle phase, and at the same time lower than that of A b2 T c2 the content of element T in the matrix phase.

[0079] The solidification methods of the initial alloy melt include common casting, continuous casting, melt spinning, melt drawing and other methods. The particle size of the endogenous alloy powder is related to the solidification rate of the initial alloy melt. Generally speaking, the particle size of the endogenous alloy powder is negatively correlated with the solidification rate of the initial alloy melt, that is: the higher the solidification rate of the initial alloy melt, the smaller the particle size of the endogenous alloy powder.

[0080] Further, the solidification method of the initial alloy melt excludes the solidification method corresponding to atomization powder preparation technology;

[0081] Additional note: the solidification rate of the initial alloy melt ranges from 0.001 K / s to 10 8 K / s;

[0082] Further, the solidification rate of the initial alloy melt ranges from 0.001 K / s to 10 7 K / s;

[0083] Further, the particle size of the endogenous alloy powder ranges from 3 nm to 10 mm.

[0084] Further, there is no limitation on the particle shape of the endogenous alloy powder, which may include at least one of dendrite shape, spherical shape, nearly spherical shape, square shape, cake shape and rod shape; when the particle shape is rod shape, the particle size specifically refers to the diameter size of the cross section of the rod.

[0085] The shape of the metal material composed of the endogenous alloy powder and the cladding body is related to the solidification method: when the solidification method is continuous casting, the shape is generally mainly lath; when the solidification method is melt spinning, the shape is generally mainly strip or thin plate; when the solidification method is melt drawing, the shape is generally mainly filament. When the solidification rate is higher, the cross section of the obtained metal material composed of the endogenous alloy powder and the cladding body is thinner, finer and narrower; on the contrary, the cross section is thicker, coarser and wider;

[0086] Furthermore, the shape of the metal material composed of endogenous alloy powder and coating does not include the powder form of products corresponding to atomization powdering technology;

[0087] Preferably, the initial alloy melt is solidified by melt spinning, and the solidification rate is 100 K / s to 10 K / s. 7 At K / s, a metal strip composed of endogenous alloy powder and a coating body with a thickness of about 10 μm to 5 mm can be obtained, and the particle size of the endogenous alloy powder is in the range of 3 nm to 200 μm.

[0088] Preferably, when the initial alloy melt is solidified by ordinary casting or continuous casting, and the solidification rate is 0.001K / s to 100K / s, a blocky metallic material composed of endogenous alloy powder and a coating body with a size exceeding 5mm in at least one dimension in the three-dimensional direction can be obtained, wherein the particle size of the endogenous alloy powder is in the range of 200μm to 10mm.

[0089] Additional explanation: Furthermore, the metallic material formed by the endogenous alloy powder and the coating is strip-shaped, and the strip thickness is 5μm to 5mm;

[0090] Furthermore, the metallic material formed by the endogenous alloy powder and the coating is strip-shaped, and the strip thickness is 10μm to 1mm;

[0091] Furthermore, the metallic material formed by the endogenous alloy powder and the coating is strip-shaped, and the thickness of the strip is 10μm to 500μm;

[0092] Furthermore, the metallic material formed by the endogenous alloy powder and the coating is strip-shaped, and the thickness of the strip is 10μm to 100μm;

[0093] Furthermore, the lower limit of the volume percentage content of the endogenous alloy powder in the metal material composed of the endogenous alloy powder and the coating is 1%, and the upper limit is the volume percentage content corresponding to the condition that the endogenous alloy powder can be dispersed in the coating.

[0094] Preferably, the volume percentage content of the endogenous alloy powder in the metallic material composed of the endogenous alloy powder and the coating body ranges from 5% to 50%.

[0095] As a further preferred embodiment, the volume percentage content of the endogenous alloy powder in the metallic material composed of the endogenous alloy powder and the coating body ranges from 5% to 40%; the preferred lower limit ensures economic efficiency, and the preferred upper limit fully ensures that the endogenous alloy powder can be dispersed in the coating body.

[0096] Preferably, the number of single-crystal particles in the endogenous alloy powder accounts for no less than 60% of the total number of particles.

[0097] As a further preference, the proportion of the number of single crystal particles in the endogenous alloy powder in the total number of all particles is not less than 75%.

[0098] As a further preference, the proportion of the number of single crystal particles in the endogenous alloy powder in the total number of all particles is not less than 90%.

[0099] Further, the endogenous alloy powder M a1 A b1 T c1 has a melting point higher than that of the cladding body A b2 T c2 ; when this condition is satisfied, the matrix phase solidifies last during solidification of the initial alloy and coats the endogenous alloy powder.

[0100] Further, the endogenous alloy powder M a1 A b1 T c1 has element A dissolved in solid solution, that is 0 < b1.

[0101] As a preference, 0 < b1 ≤ 15%; that is, M a1 A b1 T c1 can dissolve at most 15% of element A in solid solution (atomic percentage content). The solid solubility of A in the M a1 A b1 T c1 endogenous alloy powder varies according to different main element compositions of the specific alloy melt, different impurity contents, and different solidification rates. Generally, when the solidification rate of the melt is high and small endogenous alloy powder is formed, such as nanopowder, it can dissolve more A elements in solid solution.

[0102] Additional note: further, 0.01% < b1 ≤ 15%; further, 0.05% < b1 ≤ 15%; further, 0.1% < b1 ≤ 15%;

[0103] Further, T is an impurity element selected from O, H, N, P, S, F, Cl, including oxygen, and 0 < c1 ≤ 1.5%.

[0104] Additional note: further, T is an element selected from O, H, N, P, S, F, Cl, including O, all of which are non-metallic elements with similar properties. The present invention finds that the above-mentioned T elements in the initial alloy melt have similar thermodynamic effects on the diffusion and phase distribution rules of A, M and T elements in the matrix phase and the dispersed particle phase during the solidification process of the initial alloy melt; through this thermodynamic effect, when the T content is high, the M a1 A b1 T c1Intrinsic alloy powders can dissolve a significant amount of alumina (A). This is likely because the initial alloy melt contains a homogeneous mixture of alumina, methylalumina (M), and tetrahydropalmatus (T) elements. During the initial solidification process, the dispersed particles, primarily composed of methylalumina, precipitate first, displacing tetrahydropalmatus (T) atoms. This precipitation process may create vacancies, which can be replaced by both M and A atoms. Therefore, under the same conditions, a higher T content results in more vacancies being replaced, leading to a higher concentration of alumina (M). a1 A b1 T c1 The higher the content of dissolved alumina in the endogenous alloy powder, the better. Therefore, in addition to the influence of the initial alloy melt's main elemental composition, M... a1 A b1 T c1 The amount of dissolved aluminum (A) in the endogenous alloy powder is also affected by both thermodynamic and kinetic factors during the solidification of the initial alloy melt; thermodynamically speaking, when the nitrogen (T) content is high, the amount of aluminum (M) is higher. a1 A b1 T c1 Intrinsic alloy powders can dissolve a significant amount of alumina (A); kinetically speaking, when the initial alloy melt has a high solidification rate and forms relatively small intrinsic alloy powders, M... a1 A b1 T c1 Endogenous alloy powder can dissolve a relatively large amount of element A.

[0105] Furthermore, the M a0 A b0 T c0 The initial alloy melt is obtained by melting an alloy raw material containing a first raw material and a second raw material; wherein, the main elemental composition of the first raw material is M. d1 T e1 The main elemental composition of the second raw material is A. d2 T e2 d1, e1, d2, and e2 represent the atomic percentages of the corresponding elements, and 0 <e1≤10%,0<e2≤10%,d1+e1=100%,d2+e2=100%。

[0106] As a preferred option, 0 <c0≤10%,0<e1≤7.5%,0<e2≤7.5%。

[0107] As a further preferred option, 0.01% ≤ c0 ≤ 10%, 0.01% ≤ e1 ≤ 7.5%, and 0.01% ≤ e2 ≤ 7.5%.

[0108] This indicates that metallic materials consisting of endogenous alloy powder and a coating containing high-purity target endogenous alloy powder can be prepared using low-purity raw materials.

[0109] Further explanation: In several embodiments, the metallic material composed of endogenous alloy powder and coating contains endogenous M... a1 A b1 T c1 The content of T impurities in alloy powder is higher than that of M. d1 T e1 The raw material cost has been greatly reduced, i.e., endogenous M a1 A b1 T c1 The content of T impurities in the alloy powder is lower than that of M. d1 T e1 The T content in the raw material, that is, c1 is less than e1.

[0110] Further explanation: In several embodiments, the metallic material composed of endogenous alloy powder and coating contains endogenous M... a1 A b1 T c1 The volume percentage of alloy powder and M during raw material preparation d1 T e1 The volume percentage content of the raw materials is comparable; comparable means close. Therefore, the endogenous M in the metallic material composed of the target endogenous alloy powder and the coating can be designed according to the required specifications. a1 A b1 T c1 The volume percentage of the alloy powder can be used to roughly deduce the smelting M. a0 A b0 T c0 M at the initial alloy melt d1 T e1 Raw materials and A d2 T e2 The required volume percentage of each raw material; when M d1 T e1 Raw materials and A d2 T e2 When the volume percentage of each raw material is determined, the relative ratio of a0 to b0 can be calculated using data such as the atomic weight and density of each element.

[0111] It should be noted that, due to the possibility of impurity elements such as oxygen in the atmosphere entering the melt during the smelting process, situations may occur where c0 > e1 and c0 > e2, i.e., M a0 A b0 T c0 The impurity content in the initial alloy melt is higher than the total impurity content in the alloy raw material.

[0112] Additional Notes: Meanwhile, during the initial alloy smelting process, part of the element T may react with M or A to form a small amount of slag floating on the surface of the melt. Since the slag is generally solid and does not belong to the initial alloy melt, the content of element T in the initial alloy melt may also satisfy the conditions of c0<e1 and c0<e2, that is, M a0 A b0 T c0 The impurity content in the initial alloy melt is reduced relative to the total impurity content in the alloy raw materials.

[0113] The present invention also relates to a preparation method of alloy powder, characterized in that the alloy powder is prepared by removing the cladding part in the metal material composed of the endogenetic alloy powder and the cladding body, while retaining the endogenetic alloy powder that cannot be removed simultaneously.

[0114] Further, the method for removing the cladding body and retaining the endogenetic alloy powder comprises at least one of removal by acid solution dissolution reaction, removal by alkali solution dissolution reaction, removal by vacuum volatilization, and removal by natural oxidation-pulverization of the cladding body.

[0115] When removal by acid solution reaction is adopted, appropriate acid type and concentration are selected, and the selection criterion is to ensure that the cladding body A b2 T c2 becomes ions and enters the solution, while the endogenetic alloy powder M a1 A b1 T c1 hardly reacts with the corresponding acid, so as to realize the removal of the cladding body.

[0116] Further, the acid solution is subjected to degassing treatment, so that it has low dissolved amounts of oxygen and nitrogen.

[0117] When removal by alkali solution reaction is adopted, appropriate alkali type and concentration are selected, and the selection criterion is to ensure that the cladding body A b2 T c2 becomes ions and enters the solution, while the endogenetic alloy powder M a1 A b1 T c1 hardly reacts with the corresponding alkali, so as to realize the removal of the cladding body.

[0118] Further, the alkali solution is subjected to degassing treatment, so that it has low dissolved amounts of oxygen and nitrogen.

[0119] When removal by vacuum volatilization is adopted, appropriate vacuum degree and temperature conditions are selected, and the selection criterion is to ensure that the cladding body A with a lower melting point b2 T c2 volatilizes, while the endogenetic alloy powder M with a higher melting point a1 A b1 T c1 does not volatilize and is retained, so as to realize the removal of the cladding body.

[0120] When the coating is easily oxidized and powdered naturally, the naturally oxidized and powdered coating can be preliminarily removed, and then other methods can be used to completely remove the coating.

[0121] Further explanation: In a certain embodiment, M contains Fe, A contains La, and the metallic material composed of the endogenous alloy powder and the coating is a metallic strip composed of endogenous Fe alloy powder and La coating. La is dissolved in the endogenous Fe alloy powder. Through the natural oxidation-pulverization of the La coating, the endogenous Fe alloy powder and the oxide powder of the matrix La are pre-separated. Through the magnetic properties of Fe alloy powder, a magnetic field is used to separate the Fe alloy powder and the oxide of the matrix La.

[0122] This invention also relates to the application of an alloy powder in powder metallurgy, metal injection molding, magnetic materials, and coatings.

[0123] Furthermore, when the particle size of the alloy powder is large, it can be used in powder metallurgy and metal injection molding; when the particle size of the alloy powder is small, such as nanoscale, it can be used in the coatings field, mainly as a coating additive with special functions.

[0124] Furthermore, when the alloy powder is a soft magnetic alloy powder, it can also be used in the field of magnetic materials.

[0125] This invention also relates to the application of spherical or near-spherical alloy powder in powder metallurgy, metal injection molding, and metal powder 3D printing.

[0126] The present invention also relates to the application of a metallic material composed of endogenous alloy powder and coating in coatings and composite materials.

[0127] Furthermore, the method is characterized by selecting a metallic material composed of endogenous alloy powder and a coating body with an average particle size of less than 1000 nm, and removing the coating body; simultaneously or immediately after removing the coating body, the resulting alloy powder is mixed with other components of the coating or composite material to reduce the content of impurities, including O, newly introduced onto the powder surface or surface layer after the alloy powder surface is exposed, thereby obtaining a highly active alloy powder and enabling other components of the coating or composite material to have good bonding with the alloy powder surface at the atomic scale, thus obtaining a coating or composite material with added high-purity ultrafine high-activity alloy powder, which can be applied to various fields including antibacterial coatings, weather-resistant coatings, stealth coatings, microwave-absorbing coatings, wear-resistant coatings, anti-corrosion coatings, resin-based composite materials, etc.

[0128] Furthermore, after the coating is removed, the cleaning and drying processes of the alloy powder, as well as its mixing process with other components of the coating or composite material, are all carried out in a vacuum environment or under a protective atmosphere.

[0129] Furthermore, after the coating is removed, the resulting alloy powder is mixed with the coating or other components of the composite material within 20 minutes.

[0130] As a further preferred option, after the coating is removed, the resulting alloy powder is mixed with the coating or other components of the composite material within 5 minutes.

[0131] In summary, the greatest advantage of the technical solution involved in this invention is that the alloy powder is purified and solution alloyed simultaneously during the alloy powder formation process; and the invention of the metallic material composed of high-purity endogenous alloy powder and coating body also provides a new approach for the preparation, preservation and application of high-purity alloy powder.

[0132] Additional explanation: Although this invention utilizes the basic concept of selective corrosion in principle, it differs fundamentally from the selective corrosion in dealloying. Specifically, the precursor alloy selected in dealloying must be a single amorphous phase, one or more intermetallic compound phases, or a mixture of one or more intermetallic compound phases and amorphous phases. Before the dealloying reaction, the target atoms are uniformly dispersed atomically in each phase of the alloy (whether in the intermetallic compound phase or the amorphous phase, the target atoms do not aggregate with other target atoms to form the target phase); after the dealloying reaction, the active atoms are corroded away, the target atoms are released, and the target atoms recombine and aggregate together through redispersion to form a nanoporous structure. Therefore, the materials prepared by dealloying are generally nanoporous materials, not powder materials, and the macroscopic shape of the materials remains largely unchanged before and after the dealloying reaction. That is, the shape of alloy strips after the dealloying reaction is still that of nanoporous strips; the shape of alloy blocks after the dealloying reaction is still that of nanoporous blocks (see the literature Generalized fabrication of nanoporous metals (Au,Pd,Pt,Ag and Cu) through chemical dealloying, J. Phys Chem C. 113 (2009) 12629-12636). Only when ultrasound or other fragmentation methods are applied can the obtained nanoporous structure be further broken into loose nanoporous fragments or nanoparticles.

[0133] This invention, through the selection of special alloy component pairs, transforms large M... d1 T e1 Raw materials and A d2 T e2 The raw materials are heated to above the melting points of both raw materials to obtain M. a0 A b0 T c0 Initial alloy melt. During the solidification process of the initial alloy melt, the main elemental composition is M. a1A b1 T c1 The dispersed particulate phase precipitates from the melt, and the final elemental composition is mainly A. b2 T c2 The matrix phase eventually solidifies and coats the dispersed particulate phase. This dispersed particulate phase can be nanoparticles when the cooling rate is fast enough, submicron particles when the cooling rate is slightly slower, micron particles when the cooling rate is even slower, and millimeter-sized particles when the cooling rate is even slower. Therefore, the M of this invention... a1 A b1 T c1 Intrinsic alloy powder is formed during the initial solidification of the alloy melt, not during processes such as acid removal. Subsequent removal merely removes the coating to obtain freely dispersed alloy nanoparticles.

[0134] Specifically, the beneficial effects of the present invention are mainly reflected in the following aspects:

[0135] First, this breakthrough enables the production of high-purity endogenous alloy powder from low-purity raw materials, providing a new pathway for preparing high-purity metal powder materials from low-purity raw materials, which is of positive significance. The improvement in the purity of high-purity endogenous alloy powder is mainly achieved through the following two mechanisms:

[0136] 1) The "absorption" effect of element A on impurity elements. Since element A is a lower melting point and more reactive element than element M, it has a stronger affinity for impurity element T. This allows impurity element T to either enter and dissolve more extensively in the matrix phase mainly composed of element A, or form slag with element A in the molten state and separate from the alloy melt; for example, this process can be achieved when element A contains rare earth elements or calcium elements with strong affinity for oxygen.

[0137] 2) During the nucleation and growth of endogenous alloy powder (endogenously precipitated dispersed particle phase), impurity elements will be discharged into the remaining melt. As long as the endogenous alloy powder precipitates no later than the matrix phase during solidification, its impurities will be enriched in the last solidified part of the melt, that is, the part of the melt mainly composed of element A and solidified to form the matrix phase.

[0138] Second, in M a1 A b1 T c1 During the nucleation, growth, and purification of endogenous alloy powder, solid solution alloying of element A, which cannot form intermetallic compounds with M, is simultaneously achieved in M, and this solid solution alloying has a positive effect.

[0139] Through example studies, it was found that M was prepared using raw materials containing high levels of impurity elements. a1 A b1 T c1Intrinsic alloy powders often contain a considerable amount of dissolved alumina (A). Depending on the specific alloy melt's main elemental composition, impurity content, and solidification rate, the amount of A in the M... a1 A b1 T c1 The solid solubility in endogenous alloy powders can also vary. For a given MAT alloy melt, generally speaking, when the T content is high, and the melt solidification rate is high, forming smaller endogenous alloy powders, such as nanoparticles, the M... a1 A b1 T c1 Intrinsic alloy powders can contain a significant amount of alumina (A). Alumina is present in M... a1 A b1 T c1 The solid solution in endogenous alloy powder gives it some of the characteristics of solid solution alloyed powder, which is of positive significance.

[0140] It should be noted that element A is in M a1 A b1 T c1 Solid solution alloying in endogenous alloy powder is the result of the initial alloy melt containing a sufficient amount of alumina (most of the other alumina forms the matrix phase A). b2 T c2This is entirely different from directly adding a small amount of element A to element M to obtain an MA alloy. For example, industrially, trace amounts (e.g., 0.3 wt%) of Y are generally added to Ti metal (note: this corresponds to an atomic percentage of Y of 0.16 at%) to improve the strength and ductility of Ti-Y alloys. The mechanism is that the trace amount of Y added to Ti metal generally combines with impurity elements such as O in Ti metal to form Y₂O₃ oxide. The presence of Y₂O₃ oxide can act as a nucleation point for heterogeneous formation, increasing the nucleation rate, resulting in finer grains during the solidification of Ti metal. Thus, by refining the grains, the strength and ductility of Ti metal are simultaneously improved. This alloying is not strictly alloying, because the small amount of Y added to Ti metal of impure purity exists in the form of Y₂O₃ oxide. This invention allows for the smelting of Ti raw materials containing impurity T and Y raw materials containing impurity T to obtain a Ti-YT alloy melt. After solidification, this alloy melt yields Ti-YT endogenous alloy powder with a small amount of dissolved Y, where Y is the actual alloying element participating in solid solution alloying. This difference allows the Ti-YT endogenous alloy powder to achieve significantly different and beneficial application effects. For example, when Ti-YT alloy micron powder (after removing the matrix phase and undergoing spheroidization treatment) is applied to metal 3D printing, during the laser remelting process, the dissolved Y element "stored" in the Ti-YT alloy powder can absorb O elements (introduced during the removal of the matrix phase and spheroidization treatment) from the surface or surface layer of the Ti-YT alloy powder to form Y₂O₃ oxide. Using Y₂O₃ oxide as heterogeneous nucleation sites, the grain size in the Ti-YT alloy microstructure after laser remelting and solidification can be significantly refined, thereby improving the strength and plasticity of 3D printed devices. In Ti-Y powder prepared by traditional Ti-Y alloy atomization, Y has already been combined with O to form Y₂O₃ oxide. Furthermore, new O is introduced into the powder during the powder preparation process, meaning that no "free" Y can further combine with O during laser remelting. Alternatively, to achieve this, more Y needs to be added to the traditional Ti-Y alloy powder to allow some "free" Y to dissolve in the powder, in addition to the Y₂O₃ oxide. This undoubtedly does not match the superior performance of the Ti-YT alloy powder with only dissolved Y as described in this invention.

[0141] Third, alloy powders dominated by single-crystal particles can be obtained. Compared to polycrystalline powders, single-crystal powders offer numerous significant and beneficial advantages. During the initial solidification of the alloy melt, each intermolecular particle nucleates at a specific location within the melt and grows according to a specific atomic arrangement. By controlling the volume percentage of the matrix phase, ensuring that each intermolecular particle is dispersed, it is difficult for them to merge and grow together. Therefore, the resulting dispersed particle phases are predominantly single-crystal phases. Even dendritic particles with sizes as large as tens of micrometers maintain a certain phase relationship between the growth direction of each secondary dendrite and the growth direction of the main dendrite, thus still belonging to single-crystal particles.

[0142] For polycrystalline materials, the grain boundaries are generally prone to containing impurity elements that are discharged from the crystal during the solidification process, making it difficult to obtain high-purity polycrystalline powder materials. However, when the powder material is mainly composed of single-crystal particles, its purity can be guaranteed. Moreover, the atoms on the surface of single-crystal particles have specific arrangements, such as (111) plane arrangement, which endow the material with special mechanical, physical, and chemical properties, thereby producing beneficial effects.

[0143] Fourth, the metallic material composed of endogenous alloy powder and a coating material creatively utilizes an in-situ generated coating to encapsulate the endogenous alloy powder, maintaining its high purity and high activity. Metal or alloy powders prepared by traditional chemical or physical methods, especially nanoparticles with extremely large specific surface areas, are highly susceptible to natural oxidation, posing a challenge to powder preservation. To address this issue, after preparing the metallic material composed of endogenous alloy powder and a coating material, this invention does not rush to remove the coating material and then seek other methods to protect the endogenous alloy powder from contamination by oxygen and other impurities. Instead, it directly utilizes the coating material to protect the endogenous alloy powder. This metallic material composed of endogenous alloy powder and a coating material can be directly used as a raw material for downstream production. When downstream production requires the use of endogenous alloy powder, the endogenous alloy powder can be released at an appropriate time and under suitable conditions, based on the characteristics of the next process, and then allowed to enter the next production process in the shortest possible time, thereby greatly reducing the chance of contamination of the alloy powder. For example, when the endogenous alloy powder is nanoscale, it can be compounded with resin at the same time as or immediately after the release of the alloy powder to prepare a resin-based composite material with added highly active nano-alloy powder.

[0144] Fifth, by controlling the solidification rate of the initial alloy melt, it is possible to prepare endogenous alloy powders with different and continuous particle sizes, including nanopowders, submicron powders, micron powders, and even millimeter-sized powders. Compared with traditional top-down (by breaking down bulk materials into small particles) or bottom-up (by atomizing large particles) physical or chemical methods, the "primary crystal particle phase precipitation-phase removal method" involved in this invention is a novel method for preparing powder materials with particle sizes ranging from nanometers to millimeters.

[0145] Additional explanation: In the field of powder material preparation, nanoparticles of several nanometers or tens of nanometers can be easily prepared from the atomic or ionic scale using bottom-up methods (such as ion reduction); micron-sized particles of tens of micrometers can be easily prepared using top-down methods (such as ball milling). However, it is difficult to prepare powder materials with a particle size of around 1 μm using either bottom-up or top-down methods. This is because growing from atoms to the 1 μm scale from the bottom up is too difficult, and breaking bulk materials to the 1 μm scale from the top down is equally challenging. Traditional methods for preparing powder materials are only suitable for a certain particle size range. For example, ion reduction prepares nanoparticles smaller than 100 nm, and atomization prepares micron-sized particles larger than 10 μm. However, the method involved in this invention is very suitable for preparing powder materials ranging from several nanometers to several millimeters, requiring only control of the solidification rate of the initial alloy melt, perfectly solving the difficulty in preparing powder materials with a particle size of around 1 μm.

[0146] In particular, this invention is also especially suitable for the large-scale, low-cost preparation of certain special nano-metal powders (such as nano-Ti powder). Due to the special properties of Ti, it is difficult or impossible to produce it through Ag processes like Ag and Cu. + Cu 2+ The chemical reduction of nano-Ag or Cu is typically used to prepare nano-Ti powder, which can only be produced in small batches using physical methods such as explosion. This process is extremely costly, and despite the wide range of applications for nano-Ti powder, the high cost of several thousand yuan per kilogram severely limits its industrial application. This invention, however, ingeniously solves the problem of large-scale, low-cost preparation of high-purity, solid-solution alloyed nano-Ti powder using low-purity raw materials, and has immeasurable value.

[0147] Sixth, supplementary explanation: Through careful design of AM element combination, using low-purity A and M raw materials, and cleverly utilizing T-type elements (O, H, N, P, S, F, Cl), especially the essential characteristic O element, the thermodynamic influence of the diffusion and phase distribution of A, M, and T-type elements during the solidification of the initial MAT alloy melt is achieved. This not only realizes the purification of T in the MAT endogenous alloy powder, but also cleverly realizes and improves the considerable solid solution content of A in the MAT endogenous alloy powder.

[0148] Seventh, supplementary explanation: The M and A described in this invention include one or more groups of M that do not form intermetallic compounds. 1 -A 1 To meet this critical requirement, careful design is needed in the selection of alloy components. The M... 1 -A 1 The solidification structure of the element combination does not form M 1 -A 1 Intermetallic compounds; wherein A comprises at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, Mg, Ca, Li, Na, K, In, Pb, Zn, and Cu; although the above elements seem numerous, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu are all rare earth elements. If rare earth elements are selected from RE... Alternatively, A may contain only at least one of RE, Mg, Ca, Li, Na, K, In, Pb, Zn, and Cu. Among these, RE, Mg, Ca, Li, Na, K, In, Pb, and Zn are extremely reactive, or have extremely low melting points, or are extremely soft metallic elements. They generally do not form alloys with other elements to improve strength or corrosion resistance (in alloys formed with M, A acts as a coating and cannot achieve this effect), and are rarely used, being niche elements for academic research and industrial applications. Cu is rarely alloyed with niche noble metals such as Ir, Ru, Re, Os, and Tc. Even when it is alloyed with W, Cr, Mo, V, Ta, and Nb, it is generally done using powder metallurgy, where Cu powder is mixed with W, Cr, Mo, V, Ta, or Nb powder and then sintered to obtain the corresponding material. Therefore, the M selected in this invention... 1 -A 1 The element combinations mentioned above are all obscure combinations rarely explored in academia and industry. However, this invention takes a different approach, turning the disadvantages of these obscure element combinations into advantages, and applying them to the field of powder material preparation, demonstrating great ingenuity.

[0149] This invention ingeniously utilizes the characteristics of the aforementioned combination of uncommon elements. By taking advantage of the separation phenomenon between Al and Metal during alloy solidification, and the initial precipitation of primary grains dominated by Metal followed by the subsequent precipitation of the matrix phase dominated by Al, it successfully achieves the preparation of metallic materials composed of endogenous alloy powder and coatings. The extremely reactive, or extremely low melting point, or extremely soft characteristics of elements such as Re, Mg, Ca, Li, Na, K, In, Pb, and Zn facilitate the removal of coatings dominated by these elements. Therefore, the ingenious use of this combination of uncommon elements to prepare a type of alloy powder has significant positive implications.

[0150] Therefore, this invention creatively uses low-purity raw materials and integrates multiple beneficial technical solutions such as single-crystal alloy powder generation, alloy powder purification and preservation, and powder solid solution alloying. It can realize the preparation of high-purity nano-, submicron, micron, and millimeter-scale solid solution alloy powders, which have great application prospects in catalysis, powder metallurgy, composite materials, magnetic materials, sterilization, metal injection molding, metal powder 3D printing, coatings, and composite materials. Attached Figure Description

[0151] Figure 1 This is a partial backscattered SEM image of the endogenous nano-Ti alloy powder and Gd coating in Example 3 of the present invention.

[0152] Figure 2 This is a SEM image of the nano-Ti alloy powder of Example 3 of the present invention;

[0153] Figure 3 This is a partial backscattered SEM image of the endogenous Ti-Co dendritic alloy powder and its Gd coating in Example 6 of the present invention.

[0154] Figure 4 This is a SEM image of the Ti-Co dendritic alloy powder of Example 6 of the present invention; Detailed Implementation

[0155] The present invention will be further described in detail below with reference to the embodiments. It should be noted that the embodiments described below are intended to facilitate the understanding of the present invention and do not limit it in any way.

[0156] Example 1

[0157] This embodiment provides a metal strip composed of endogenous nano-Ti alloy powder and Ce coating, a nano-Ti alloy powder, its preparation method and application, including the following steps:

[0158] (1) Low-purity titanium was selected, containing 0.3wt%, 0.1wt%, 0.3wt%, and 0.03wt% Cl, N, O, and H by weight. After conversion to atomic percentage, the atomic percentage contents of Cl, N, O, and H were 0.4at%, 0.33at%, 0.88at%, and 1.39at%, respectively, with a total content of 3at%. Low-purity rare earth Ce was selected, containing 0.3wt% O. After conversion to atomic percentage, the O content in Ce was 2.57at%. Since Ti-Ce is an element combination pair that does not form intermetallic compounds, and Ti has a higher melting point than Ce, Ti alloy powder can be prepared based on this element combination pair.

[0159] Low-purity Ti and low-purity Ce raw materials were mixed in a volume ratio of 1:3, and other trace elements that may be present in the raw materials were included in the main elements to facilitate calculation. Based on elemental density and atomic weight data, the composition of the mixed gold raw material can be expressed as approximately (Ti) 97 Cl 0.4 N 0.33 O 0.88 H 1.39 ) 39 (Ce 97.43 O 2.57 ) 61 Specifically, Ti 37.83 Ce 59.435 Cl 0.156 N 0.129 H 0.54 O 1.91 The total content of impurity element T, including Cl, N, H, and O, is approximately 2.735 at%.

[0160] (2) The above-mentioned low-purity alloy raw materials were subjected to induction melting to obtain a Ti alloy with a composition of approximately 100%. 37.83 Ce 59.435 T 2.735 The initial alloy melt (T represents impurity elements such as Cl, N, H, and O). Some impurity elements in the initial alloy melt may become slag and separate from the melt, thus reducing the impurity content; while some impurities in the environment and atmosphere, such as oxygen, may also enter the melt, thus increasing the impurity content in the melt.

[0161] (3) The initial alloy melt is rapidly solidified into strips approximately 100 μm thick using a copper roller spinning method. During solidification, Ti-dominated dispersed particle phases are embedded and precipitated within a Ce-dominated matrix phase, thus obtaining a metal strip composed of endogenous nano-Ti alloy powder and Ce coating. The atomic percentage composition of the endogenous Ti alloy powder is approximately Ti. 99.1 Ce 0.5 T 0.4 It is mainly composed of single-crystal particles with a particle size ranging from 3 nm to 300 nm. The endogenous Ti alloy powder contains a small amount of Ce dissolved in it, and the content of T impurities is significantly reduced compared to low-purity Ti raw materials, while other large amounts of T impurities are enriched in the Ce coating. In the resulting metal strips composed of endogenous nano-Ti alloy powder and Ce coating, the volume percentage of endogenous Ti alloy powder is comparable to the volume percentage of Ti raw material during preparation, remaining approximately 25 vol%, ensuring the dispersed distribution of Ti alloy powder in the Ce-dominated matrix phase.

[0162] (4) The Ce coating in the metal strip composed of endogenous nano-Ti alloy powder and Ce coating is removed by dilute hydrochloric acid solution. Since the Ti alloy powder does not react with dilute hydrochloric acid solution, Ti-Ce-T alloy powder can be obtained after separation, cleaning and drying. Due to the absorption of impurities such as oxygen by the surface layer and surface atoms of the exposed Ti-Ce-T alloy powder, the content of T impurities in the obtained Ti-Ce-T alloy powder is higher than that in endogenous Ti-Ce-T alloy powder.

[0163] After step (3), you can directly proceed to step (5):

[0164] (5) The Ce coating in the metal strip composed of endogenous nano-Ti alloy powder and Ce coating is removed by dilute hydrochloric acid solution that removes dissolved oxygen. Within 20 minutes, the Ti alloy powder is separated under a protective atmosphere and mixed with epoxy resin and other coating components to prepare a titanium alloy nano-modified polymer anti-corrosion coating.

[0165] Example 2

[0166] This embodiment provides a metal sheet composed of endogenous micron-sized Ti alloy powder and Ce coating, a micron-sized Ti alloy powder, its preparation method and application, including the following steps:

[0167] (1) Low-purity titanium was selected, containing 0.3wt%, 0.1wt%, 0.3wt%, and 0.03wt% Cl, N, O, and H by weight, respectively. After conversion to atomic percentage, the atomic percentage contents of Cl, N, O, and H were 0.4at%, 0.33at%, 0.88at%, and 1.39at%, respectively. The total content was 3at%. Low-purity rare earth Ce was selected, containing 0.3wt% O. After conversion to atomic percentage, the O content in Ce was 2.57at%. Since Ti-Ce is an element combination pair that does not form intermetallic compounds, and Ti has a higher melting point than Ce, Ti alloy powder can be prepared based on this element combination pair.

[0168] Low-purity Ti and low-purity Ce raw materials were mixed in a volume ratio of 1:3, and other trace elements that may be present in the raw materials were included in the main elements to facilitate calculation. Based on elemental density and atomic weight data, the composition of the mixed gold raw material, expressed as an atomic percentage, is approximately (Ti... 97 Cl 0.4 N 0.33 O 0.88 H 1.39 ) 39 (Ce 97.43 O 2.57 ) 61 That is, the atomic percentage content is approximately Ti. 37.83 Ce59.435 Cl 0.156 N 0.129 H 0.54 O 1.91 The total content of impurity element T, including Cl, N, H, and O, is approximately 2.735 at%.

[0169] (2) The above-mentioned low-purity alloy raw materials were subjected to induction melting to obtain a Ti alloy with a composition of approximately 100%. 37.83 Ce 59.435 T 2.735 The initial alloy melt (T represents impurity elements such as Cl, N, H, and O). Some impurity elements in the initial alloy melt may become slag and separate from the melt, thus reducing the impurity content; while some impurities in the environment and atmosphere, such as oxygen, may also enter the melt, thus increasing the impurity content in the melt.

[0170] (3) The initial alloy melt is solidified into a thin plate with a thickness of approximately 4 mm. During solidification, medium-dendritic dispersed particles, mainly composed of Ti, are embedded in a matrix phase mainly composed of Ce, thus obtaining a thin metal plate composed of endogenous micron-sized Ti alloy powder and Ce coating. The atomic percentage composition of the endogenous Ti alloy dendrite powder is approximately Ti. 99.4 Ce 0.3 T 0.3 It is mainly composed of single-crystal dendrite particles with a particle size ranging from 1 μm to 150 μm. Ce is dissolved in the endogenous Ti alloy powder, and the content of T impurities is significantly reduced compared to low-purity Ti raw materials, while other large amounts of T impurities are enriched in the Ce coating. In the resulting metal sheet composed of endogenous micron-sized Ti alloy powder and Ce coating, the volume percentage of endogenous Ti alloy powder is comparable to the volume percentage of titanium raw material during preparation, remaining approximately 25 vol%, ensuring the dispersed distribution of Ti alloy dendrite powder in the Ce-dominated matrix phase.

[0171] (4) The Ce coating in the metal sheet composed of endogenous micron Ti alloy powder and Ce coating is removed by dilute hydrochloric acid solution. Since Ti alloy dendrite powder does not react with dilute hydrochloric acid solution, Ti-Ce-T alloy dendrite powder can be obtained after separation, cleaning and drying.

[0172] (5) The Ti-Ce-T alloy dendrite powder is treated by air jet milling, which disperses the entangled dendrite particles during solidification and breaks the larger dendrite particles into smaller dendrite fragments.

[0173] (6) The Ti alloy dendrite powder obtained above is sieved, and Ti alloy dendrite powder with a particle size range of 15μm to 53μm is selected for plasma spheroidization treatment to obtain spherical or near-spherical Ti alloy powder with little variation in particle size range.

[0174] (7) The spherical or near-spherical Ti alloy powder is used in the field of metal powder 3D printing.

[0175] Example 3

[0176] This embodiment provides a metal strip composed of endogenous nano-Ti alloy powder and Gd coating, a nano-Ti alloy powder, and a method for preparing the same, including the following steps:

[0177] (1) Low-purity Ti raw materials and rare earth raw materials mainly composed of Gd are selected. The impurity T content in both types of raw materials is about 3 at%. Since Ti-Gd is an element combination pair that does not form intermetallic compounds, and the melting point of Ti is higher than that of Gd, Ti alloy powder can be prepared based on this element combination pair.

[0178] (2) Low-purity Ti raw materials and rare earth raw materials mainly composed of Gd were mixed in a volume ratio of 15:85 to form an alloy raw material. The alloy raw materials were then subjected to induction melting to obtain an atomic percentage composition of approximately Ti. 24 Gd 73 The initial alloy melt is T3, in which the T content is approximately 3 at%.

[0179] (3) The initial alloy melt is rapidly solidified into strips with a thickness of approximately 100 μm by copper roller spinning. During solidification, dispersed particles mainly composed of Ti are embedded in the matrix phase mainly composed of Gd, thus obtaining a metal strip composed of endogenous nano-Ti alloy powder and Gd coating. Its microstructure is as follows: Figure 1 As shown. The atomic percentage composition of the endogenous Ti alloy powder is approximately Ti. 99.2 Gd 0.5 T 0.3 It mainly consists of Ti nanocrystals with a small amount of Gd dissolved in solid solution, with particle sizes ranging from 3 nm to 300 nm. The T impurity content in the endogenous Ti alloy powder is significantly reduced compared to the Ti raw material, while a large amount of other T impurities are enriched in the Gd coating. In the obtained endogenous Ti alloy powder and its Gd-coated strips, the volume percentage of the endogenous Ti alloy powder is comparable to the volume percentage of the Ti raw material during preparation, remaining approximately 15 vol%, ensuring the dispersed distribution of the Ti alloy powder in the Gd-dominated matrix phase. Figure 1 As shown.

[0180] (4) The Gd coating in the metal strip composed of endogenous nano-Ti alloy powder and Gd coating is removed by dilute hydrochloric acid solution. Since the Ti alloy powder does not react with dilute hydrochloric acid solution, after separation, cleaning and drying, Ti-Gd-Ti alloy powder with Ti as the main component can be obtained, with a particle size ranging from 3 nm to 300 nm. Figure 2 As shown.

[0181] Example 4

[0182] This embodiment provides a metal strip composed of endogenous nano-Ti-Nb-V alloy powder and Ce-La-Nd-Pr coating, a nano-Ti-Nb-V alloy powder, and a method for preparing the same, including the following steps:

[0183] (1) Low-purity Ti, Nb, and V raw materials and mixed rare earth raw materials mainly composed of Ce, La, Nd, and Pr are selected. The impurity T content in both types of raw materials is about 3 at%. Since Ti-Ce, Ti-La, Ti-Nd, Ti-Pr, Nb-Ce, Nb-La, Nb-Nd, Nb-Pr, V-Ce, V-La, V-Nd, and V-Pr are all element combinations that do not form intermetallic compounds, and the melting points of Ti, Nb, and V are higher than those of Ce, La, Nd, and Pr, Ti-Nb-V alloy powder can be prepared based on these element combinations.

[0184] (2) Low-purity Ti, Nb, and V raw materials were mixed with a mixture of rare earth elements mainly composed of Ce, La, Nd, and Pr at a volume ratio of 1:2 to form an alloy raw material, wherein Ti, Nb, and V were in equimolar ratio. The alloy raw materials were subjected to induction melting to obtain an initial alloy melt of (Ti-Nb-V)-(Ce-La-Nd-Pr)-T, wherein the content of T was approximately 3 at%.

[0185] (3) The initial alloy melt is rapidly solidified into strips approximately 100 μm thick using a copper roller spinning method. During solidification, dispersed particles primarily composed of Ti-Nb-V are embedded within a matrix phase primarily composed of Ce-La-Nd-Pr, thus obtaining metal strips composed of endogenous nano-Ti-Nb-V alloy powder and Ce-La-Nd-Pr coatings. The atomic percentage composition of the endogenous Ti-Nb-V alloy powder is approximately (Ti-Nb-V). 99.2 (Ce-La-Nd-Pr) 0.5 T 0.3 It is mainly composed of infinitely miscible Ti-Nb-V single crystal particles with a particle size ranging from 3 nm to 300 nm. The endogenous Ti-Nb-V alloy powder contains Ce-La-Nd-Pr dissolved in it, and the content of Ti impurities is significantly reduced compared to the Ti, Nb, and V raw materials, while other large amounts of Ti impurities are enriched in the Ce-La-Nd-Pr coating. In the resulting metal strips composed of endogenous nano-Ti-Nb-V alloy powder and Ce-La-Nd-Pr coating, the volume percentage of the endogenous Ti-Nb-V alloy powder is comparable to the volume percentage of Ti, Nb, and V raw materials during preparation, remaining approximately 33 vol%, ensuring the dispersed distribution of the Ti-Nb-V alloy powder in the Ce-La-Nd-Pr-dominated matrix phase.

[0186] (4) The Ce-La-Nd-Pr coating in the metal strip composed of endogenous nano-Ti-Nb-V alloy powder and Ce-La-Nd-Pr coating is removed by dilute hydrochloric acid solution. Since Ti-Nb-V alloy powder does not react with dilute hydrochloric acid solution, after separation, cleaning and drying, Ti-Nb-V alloy powder with the main composition of (Ti-Nb-V)-(Ce-La-Nd-Pr)-T can be obtained. Due to the absorption of impurities such as O by the surface layer of the exposed Ti-Nb-V alloy powder, the content of T impurities in the obtained Ti-Nb-V alloy powder is slightly higher than that in the endogenous Ti-Nb-V alloy powder.

[0187] Example 5

[0188] This embodiment provides a metal strip composed of endogenous submicron Ti-Co alloy powder and Ce-La-Nd-Pr coating, a submicron Ti-Co alloy powder, and a method for preparing the same, including the following steps:

[0189] (1) Low-purity Ti and Co raw materials and mixed rare earth raw materials mainly composed of Ce, La, Nd, and Pr are selected. The molar ratio of Ti to Co raw materials is 1:1, and the impurity T content in both types of raw materials is about 3 at%. Since Ti-Ce, Ti-La, Ti-Nd, and Ti-Pr are all element combinations that do not form intermetallic compounds, and Ti accounts for 50% of Ti-Co raw materials, making it the main element; and the melting point of CoTi intermetallic compounds is as high as 1700℃, which is much higher than the melting point of intermetallic compounds that Co can form with Ce, La, Nd, Pr, etc., when Co:Ti is 1:1, Co mainly combines with Ti to form high-melting-point CoTi intermetallic compounds. Therefore, intermetallic compound CoTi alloy powder can be prepared based on these element combinations.

[0190] (2) Low-purity Ti and Co raw materials were mixed with a mixture of rare earth elements mainly composed of Ce, La, Nd, and Pr at a volume ratio of 1:2 to form an alloy raw material, wherein Ti:Co was in an equimolar ratio. The alloy raw materials were subjected to induction melting to obtain an initial alloy melt of (Ti-Co)-(Ce-La-Nd-Pr)-T, wherein the content of T was approximately 3 at%.

[0191] (3) The initial alloy melt is rapidly solidified into strips approximately 300 μm thick using a copper roller spinning method. During solidification, dispersed particles, primarily composed of Ti-Co, are embedded within a matrix phase primarily composed of Ce-La-Nd-Pr, thus obtaining metal strips composed of endogenous submicron Ti-Co alloy powder and a Ce-La-Nd-Pr coating. The atomic percentage composition of the endogenous Ti-Co alloy powder is approximately (Ti-Co).99 (Ce-La-Nd-Pr) 0.6 T 0.4 The resulting Ti-Co alloy powder is primarily composed of Ti-Co single-crystal particles of intermetallic compounds, with particle sizes ranging from 20 nm to 1 μm. Ce-La-Nd-Pr is dissolved in the endogenous Ti-Co alloy powder, and the content of Ti impurities is significantly reduced compared to the Ti and Co raw materials. Other large amounts of Ti impurities are enriched in the Ce-La-Nd-Pr coating. In the resulting metal strips composed of endogenous submicron Ti-Co alloy powder and Ce-La-Nd-Pr coating, the volume percentage of the endogenous Ti-Co alloy powder is comparable to the volume percentage of the Ti and Co raw materials during preparation, remaining approximately 33 vol%, ensuring the dispersed distribution of the Ti-Co alloy powder within the Ce-La-Nd-Pr-dominated matrix phase.

[0192] (4) The Ce-La-Nd-Pr coating in the metal strip composed of endogenous submicron Ti-Co alloy powder and Ce-La-Nd-Pr coating is removed by dilute hydrochloric acid solution. Since Ti-Co alloy powder does not readily react with dilute hydrochloric acid solution, after separation, cleaning, and drying, Ti-Co alloy powder with the main composition (Ti-Co)-(Ce-La-Nd-Pr)-T can be obtained. Due to the absorption of impurities such as O by the surface layer of the exposed Ti-Co alloy powder, the content of T impurities in the obtained Ti-Co alloy powder is slightly higher than that in endogenous Ti-Co alloy powder.

[0193] Example 6

[0194] This embodiment provides a metal sheet composed of endogenous micron-sized Ti-Co alloy powder and Gd coating, a micron-sized Ti-Co alloy powder, and a method for preparing the same, including the following steps:

[0195] (1) Low-purity Ti and Co raw materials and rare earth raw materials mainly composed of Gd are selected, wherein the molar ratio of Ti to Co raw materials is 1:1, and the impurity T content in both types of raw materials is about 3 at%. Since Ti-Gd is an element combination pair that does not form intermetallic compounds, and Ti accounts for 50% of Ti-Co raw materials, making it the main element; and the melting point of CoTi intermetallic compound is as high as 1700℃, which is much higher than the melting point of intermetallic compounds that Co and Gd can form, when Co:Ti is 1:1, Co mainly combines with Ti to form a high-melting-point CoTi intermetallic compound. Therefore, intermetallic compound CoTi alloy powder can be prepared based on these element combinations.

[0196] (2) Low-purity Ti and Co raw materials were mixed with rare earth raw materials mainly composed of Gd at a volume ratio of 30:70, where Ti:Co was an equimolar ratio. The alloy raw materials were then subjected to induction melting to obtain an initial TiCo-Gd-T alloy melt, in which the T content was approximately 3 at%.

[0197] (3) The initial alloy melt was solidified into a thin plate with a thickness of about 2 mm. During the solidification process, the dendritic particles mainly composed of Ti-Co were embedded in the matrix phase mainly composed of Gd, thus obtaining a metal thin plate composed of endogenous micron-sized Ti-Co alloy powder and Gd coating. The solidification morphology is shown in [reference needed]. Figure 3 As shown. The atomic percentage composition of the endogenous Ti-Co alloy powder is approximately (TiCo). 99.5 Gd 0.3 T 0.2 The resulting Ti-Co alloy powder is primarily composed of Ti-Co single-crystal particles of intermetallic compounds, with particle sizes ranging from 1 μm to 60 μm. A small amount of Gd is dissolved in the endogenous Ti-Co alloy powder, and the content of Ti impurities is significantly reduced compared to the Ti and Co raw materials. A large amount of other Ti impurities are enriched in the Gd coating. In the resulting endogenous Ti-Co alloy powder and its Gd-coated thin plate, the volume percentage of the endogenous Ti-Co alloy powder is approximately 30 vol%, similar to the volume percentage of the Ti and Co raw materials used in the initial preparation, ensuring a dispersed distribution of the Ti-Co alloy powder within the Gd-dominated matrix phase.

[0198] (4) The Gd coating in the metal sheet composed of endogenous micron-sized Ti-Co alloy powder and Gd coating is removed by dilute hydrochloric acid solution. Since Ti-Co alloy powder does not readily react with dilute hydrochloric acid solution, after separation, cleaning, and drying, Ti-Co alloy powder with (Ti-Co)-Gd-T as its main component can be obtained. Its single crystal dendrite morphology is as follows: Figure 4 As shown, due to the absorption of impurities such as O by the surface layer of the exposed Ti-Co alloy powder, the content of T impurities in the obtained Ti-Co alloy powder is slightly higher than that in endogenous Ti-Co alloy powder.

[0199] Example 7

[0200] This embodiment provides a metal strip composed of endogenous micron-sized Fe alloy powder and La coating, a micron-sized Fe alloy powder, and a method for preparing the same, including the following steps:

[0201] (1) Low-purity Fe raw materials and rare earth raw materials mainly composed of La are selected, and the impurity T content in both types of raw materials is about 2.5 at%. Since Fe-La is an element combination pair that does not form intermetallic compounds, and both are main elements, Fe alloy powder can be prepared based on the Fe and La combination pair.

[0202] (2) The low-purity Fe raw material and the rare earth raw material mainly composed of La were mixed in a volume ratio of 1:2. The alloy raw material was then subjected to induction melting to obtain the Fe-La-T initial alloy melt, in which the T content was about 2.5 at%.

[0203] (3) The initial alloy melt is rapidly solidified into strips with a thickness of approximately 500 μm by copper roller spinning. During solidification, a dispersed particle phase mainly composed of Fe is embedded in a matrix phase mainly composed of La, thus obtaining a metal strip composed of endogenous micron-sized Fe alloy powder and La coating. The atomic percentage composition of the endogenous Fe alloy powder is approximately Fe. 99.4 La 0.3 T 0.3 It is mainly composed of Fe single-crystal particles with a particle size ranging from 500 nm to 5 μm. The endogenous Fe alloy powder contains dissolved La, and the content of trace impurities (T) is significantly reduced compared to the Fe raw material, while a large amount of other T impurities are enriched in the La coating. In the resulting metal strips composed of endogenous micron-sized Fe alloy powder and La coating, the volume percentage of endogenous Fe alloy powder is approximately 33 vol%, which is comparable to the volume percentage of the raw material during preparation, ensuring the dispersed distribution of Fe alloy powder in the La-dominated matrix phase.

[0204] (4) The endogenous Fe alloy powder is pre-separated from the La oxide powder of the matrix by natural oxidation-pulverization of the La coating. Utilizing the magnetic properties of the Fe alloy powder, a magnetic field is used to separate the Fe alloy powder from the La oxide powder of the matrix. Then, a small amount of dilute acid solution is used to completely remove the residual La oxide adsorbed on the surface of the Fe alloy powder. Simultaneously, the concentration and amount of acid are controlled to ensure the retention of the Fe alloy powder. After washing, separation, and drying, the final Fe alloy powder is obtained.

[0205] Example 8

[0206] This embodiment provides a metal strip composed of endogenous nano-Cu alloy powder and Li coating, a nano-Cu alloy powder, and a method for preparing the same, including the following steps:

[0207] (1) Low-purity Cu raw materials and low-purity Li raw materials are selected, and the impurity T content in both types of raw materials is about 1 at%. Since Cu-Li is an element combination pair that does not form intermetallic compounds, and both are main elements, Cu alloy powder can be prepared based on the Cu and Li combination pair.

[0208] (2) The low-purity Cu raw material and the low-purity Li raw material are mixed in a volume ratio of 1:3. The alloy raw materials are then subjected to induction melting to obtain an initial Cu-Li-T alloy melt, in which the T content is approximately 1 at.

[0209] (3) The initial alloy melt is rapidly solidified into strips approximately 30 μm thick using a copper roller spinning method. During solidification, a Cu-dominant dispersed particle phase is embedded in a Li-dominant matrix phase, thus obtaining a metal strip composed of endogenous nano-Cu alloy powder and Li coating. The atomic percentage composition of the endogenous Cu alloy powder is approximately Cu... 84.8 Li 15 T 0.2 It is mainly composed of Cu single crystal particles with a large amount of Li dissolved in them, and the particle size ranges from 3 nm to 150 nm. Moreover, the content of T impurities is greatly reduced compared with Cu raw materials, while other large amounts of T impurities are enriched in the Li coating.

[0210] (4) The Li coating in the metal strip composed of endogenous nano-Cu alloy powder and Li coating is removed by a very dilute hydrochloric acid solution. Since Cu alloy powder does not react easily with a very dilute hydrochloric acid solution, after separation, cleaning and drying, nano-sized Cu alloy powder with Cu-Li-T as the main component can be obtained.

[0211] Example 9

[0212] This embodiment provides a metal strip composed of endogenous nano-Cu alloy powder and Pb coating, a nano-Cu alloy powder, and a method for preparing the same, including the following steps:

[0213] (1) Select low-purity Cu and Pb raw materials, and the impurity T content in the two types of raw materials is about 2 at% and 0.5 at%, respectively. Since Cu-Pb is an element combination pair that does not form intermetallic compounds, and both are main elements, Cu alloy powder can be prepared based on the Cu and Pb combination pair.

[0214] (2) The low-purity Cu raw material and Pb raw material are mixed in a volume ratio of 1:3. The alloy raw materials are then subjected to induction melting to obtain an initial Cu-Pb-T alloy melt, in which the T content is approximately 1 at%.

[0215] (3) The initial alloy melt is rapidly solidified into strips approximately 30 μm thick using a copper roller spinning method. During solidification, a Cu-dominant dispersed particle phase is embedded within a Pb-dominant matrix phase, thus obtaining a metal strip composed of endogenous nano-Cu alloy powder and Pb coating. The atomic percentage composition of the endogenous Cu alloy powder is approximately Cu... 99.5 Pb 0.3 T 0.2It mainly consists of Cu single-crystal particles with a small amount of Pb dissolved in them, with particle sizes ranging from 3 nm to 150 nm. The content of trace impurities (T) is significantly reduced compared to the Cu raw material, while a large amount of other T impurities are enriched in the Pb coating. In the resulting metal strips composed of endogenous nano-Cu alloy powder and Pb coating, the volume percentage of endogenous Cu alloy powder is approximately 25 vol%, similar to the volume percentage during raw material preparation, ensuring the dispersed distribution of Cu alloy powder in the Pb-dominated matrix phase.

[0216] (4) The Pb coating in the metal strip composed of endogenous nano-Cu alloy powder and Pb coating is removed by a mixed solution of acetic acid and dilute hydrochloric acid. Since Cu alloy powder does not react easily with the mixed solution of acetic acid and dilute hydrochloric acid, nano-sized Cu alloy powder with Cu-Pb-T as the main component can be obtained after separation, cleaning and drying.

[0217] Example 10

[0218] This embodiment provides a metal strip composed of endogenous nano-Nb-V-Mo-W alloy powder and Cu coating, a nano-Nb-V-Mo-W alloy powder, and its preparation method, including the following steps:

[0219] (1) Low-purity Nb, V, Mo, W raw materials and Cu raw materials are selected, and the impurity T content in both types of raw materials is about 1 at%. Since Cu-Nb, Cu-V, Cu-Mo and Cu-W are all element combinations that do not form intermetallic compounds, and Nb, V, Mo and W are mutually soluble main elements, Nb-V-Mo-W alloy powder can be prepared based on these combinations.

[0220] (2) Low-purity Nb, V, Mo, and W raw materials were mixed with Cu raw material at a volume ratio of 1:2, wherein the molar ratio of Nb:V:Mo:W was 2:1:1:1. The alloy raw materials were then subjected to induction melting to obtain an initial alloy melt of (Nb2VMoW)-Cu-T, wherein the content of T was approximately 1 at%.

[0221] (3) The initial alloy melt is slowly solidified into strips approximately 30 μm thick using a copper roller. During solidification, a dispersed particle phase dominated by Nb₂VMoW is embedded in a Cu-dominated matrix phase, thus obtaining a metal strip composed of endogenous nano-Nb-V-Mo-W alloy powder and a Cu coating. The atomic percentage composition of the endogenous Nb₂VMoW alloy powder is approximately (Nb₂VMoW). 99.3 Cu 0.5 T 0.2It mainly consists of high-entropy Nb₂VMoW single-crystal particles with a small amount of Cu dissolved in them, with particle sizes ranging from 3 nm to 200 nm. Furthermore, the content of trace impurities (T) is significantly reduced compared to the Cu raw material, while a large amount of other T impurities are enriched in the Cu coating. In the resulting metal strips composed of endogenous nano-Nb-V-Mo-W alloy powder and Cu coating, the volume percentage of endogenous Nb₂VMoW alloy powder is comparable to the volume percentage during raw material preparation, remaining approximately 33 vol%, ensuring the dispersed distribution of Nb₂VMoW alloy powder in the Cu-dominated matrix phase.

[0222] (4) The Cu coating in the metal strip composed of endogenous nano Nb-V-Mo-W alloy powder and Cu coating is removed by a medium-concentration hydrochloric acid solution. Since Nb2VMoW alloy powder does not react easily with a medium-concentration hydrochloric acid solution, after separation, cleaning and drying, nano-scale alloy powder with Nb2VMoW as the main component can be obtained.

[0223] Example 11

[0224] This embodiment provides a metal sheet composed of endogenous micron-sized Nb-V-Mo-W alloy powder and Cu coating, a micron-sized Nb-V-Mo-W alloy powder, and a method for preparing the same, including the following steps:

[0225] (1) Low-purity Nb, V, Mo, W raw materials and Cu raw materials are selected, and the impurity T content in both types of raw materials is about 1 at%. Since Cu-Nb, Cu-V, Cu-Mo and Cu-W are all element combinations that do not form intermetallic compounds, and Nb, V, Mo and W are mutually soluble main elements, Nb-V-Mo-W alloy powder can be prepared based on these combinations.

[0226] (2) Low-purity Nb, V, Mo, W raw materials and Cu raw materials are mixed in a volume ratio of 1:2, wherein the molar ratio of Nb:V:Mo:W is 1:1:1:1. The alloy raw materials are then subjected to induction melting to obtain an initial alloy melt of (NbVMoW)-Cu-T, wherein the content of T is approximately 1 at%.

[0227] (3) The initial alloy melt is solidified into a thin plate with a thickness of approximately 4 mm. During solidification, a dispersed dendritic phase dominated by NbVMoW is embedded in the Cu-dominated matrix phase, thus obtaining a metal thin plate composed of endogenous micron-sized Nb-V-Mo-W alloy powder and a Cu coating. The atomic percentage composition of the endogenous NbVMoW dendritic alloy powder is approximately (NbVMoW). 99.6 Cu 0.3 T 0.1It mainly consists of high-entropy NbVMoW single crystal particles with a small amount of Cu dissolved in them, with particle sizes ranging from 1 μm to 150 μm. The content of nitrogen (T) impurities is significantly reduced compared to the Cu raw material, while other large amounts of T impurities are enriched in the Cu coating. In the resulting metal sheet composed of endogenous micron-sized Nb-V-Mo-W alloy powder and Cu coating, the volume percentage of endogenous NbVMoW dendritic alloy powder is comparable to the volume percentage during raw material preparation, remaining approximately 33 vol%, ensuring the dispersed distribution of NbVMoW dendritic alloy powder in the Cu-dominated matrix phase.

[0228] (4) The Cu coating in the metal sheet composed of endogenous micron Nb-V-Mo-W alloy powder and Cu coating is removed by a medium-concentration hot hydrochloric acid solution. Since NbVMoW dendritic alloy powder does not react easily with a medium-concentration hot hydrochloric acid solution, after separation, cleaning and drying, micron-sized dendritic alloy powder with NbVMoW as the main component can be obtained.

[0229] The technical features of the above embodiments can be combined in any way. For the sake of brevity, not all possible combinations of the technical features in the above embodiments are described. However, as long as there is no contradiction in the combination of these technical features, they should be considered to be within the scope of this specification.

[0230] The embodiments described above are merely illustrative of several implementations of the present invention, and while the descriptions are relatively specific and detailed, they should not be construed as limiting the scope of the invention patent. It should be noted that those skilled in the art can make various modifications and improvements without departing from the concept of the present invention, and these all fall within the protection scope of the present invention. Therefore, the protection scope of this invention patent should be determined by the appended claims.

Claims

1. A method for preparing a metallic material composed of endogenous alloy powder and a coating, characterized in that, Prepared by the following steps: Step 1: The main elemental composition of the smelting process is M. a0 A b0 T c0 The initial alloy melt, where a0, b0, and c0 represent the atomic percentage content of the corresponding constituent elements, a0 + b0 + c0 = 100%, 0 <c0≤15%; Step 2: Solidify the initial alloy melt of said M a0 A b0 T c0 into solid to obtain endogenously precipitated M a1 A b1 T c1 dispersed particles and A b2 T c2 matrix phase coating the dispersed particles, which is the metal material consisting of the endogenously generated alloy powder and the coating body; wherein 0 < c1 < c0 < c2, i.e., the M a0 A b0 T c0 content of T element in the initial alloy melt is higher than M a1 A b1 T c1 content of T element in the dispersed particle phase, and lower than A b2 T c2 content of T element in the matrix phase; The metallic material composed of endogenous alloy powder and a coating is prepared by solidification of an alloy melt. Its composition includes a dispersed particle phase precipitated during the initial alloy solidification process and a matrix phase coating the dispersed particles, corresponding respectively to the endogenous alloy powder and the coating. The elemental composition of the endogenous alloy powder is mainly M. a1 A b1 T c1 The elemental composition of the coating is mainly A. b2 T c2 ; Both M and A contain one or more metallic elements, T is an impurity element including oxygen, and a1, b1, c1, b2, and c2 represent the atomic percentage content of the corresponding elements, with a1+b1+c1=100%, b2+c2=100%, c2>c1>0, and b1>0; the melting point of the endogenous alloy powder is higher than that of the coating; the endogenous alloy powder M a1 A b1 T c1 The solid contains element A; the M and the A contain one or more groups of M that do not form intermetallic compounds. 1 -A 1 Combinations of elements, where M 1 A represents any element in M. 1 Let M represent any element in A, and let M be the principal element satisfying M 1 -A 1 M of the element combination conditions 1 The main elements in A are composed of elements that satisfy M. 1 -A 1 Each A in the element combination condition 1 The elemental composition ensures that after the metallic material composed of the endogenous alloy powder and the coating is completely melted and resolidified, it does not form an intermetallic compound composed of the main elements in M ​​and A, but instead forms the endogenous alloy powder M. a1 A b1 T c1 With the coating body A b2 T c2 ; Wherein, M comprises at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti, Fe, Co, Ni, Mn, Cu, and Ag, and A comprises at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, Mg, Ca, Li, Na, K, In, Pb, and Zn; Or M may include at least one of Ir, Ru, Re, Os, Tc, W, Cr, Mo, V, Ta, and Nb, and A may include Cu.

2. The method for preparing a metallic material composed of endogenous alloy powder and a coating body according to claim 1, characterized in that, The shape of the metallic material composed of endogenous alloy powder and coating is related to the solidification method: when the solidification method is continuous casting, its shape is generally mainly strip-shaped; when the solidification method is melt casting, its shape is generally mainly strip-shaped or thin plate-shaped; when the solidification method is melt drawing, its shape is generally mainly filament-shaped.

3. The method for preparing a metallic material composed of endogenous alloy powder and a coating body according to claim 1, characterized in that, The T represents the elements O, H, N, P, S, F, and Cl, including O, and 0 <c1≤1.5%。 4. The method for preparing a metallic material composed of endogenous alloy powder and a coating body according to claim 1, characterized in that, The metallic material composed of the endogenous alloy powder and the coating body is a strip of metallic material composed of endogenous alloy powder and coating body with a thickness of 10µm to 5mm, and the particle size range of the endogenous alloy powder is 3nm to 200µm.

5. The method for preparing a metallic material composed of endogenous alloy powder and a coating body according to claim 1, characterized in that, 0<b1≤15%。 6. The method for preparing a metallic material composed of endogenous alloy powder and a coating body according to claim 1, characterized in that, The number of single-crystal particles in the endogenous alloy powder accounts for no less than 60% of the total number of particles.

7. The method for preparing a metallic material composed of endogenous alloy powder and a coating body according to claim 1, characterized in that, The M a0 A b0 T c0 The initial alloy melt is obtained by melting an alloy raw material containing a first raw material and a second raw material; wherein, the main elemental composition of the first raw material is M. d1 T e1 The main elemental composition of the second raw material is A. d2 T e2 d1, e1, d2, and e2 represent the atomic percentages of the corresponding elements, and 0 <e1≤10%,0<e2≤10%,d1+e1=100%,d2+e2=100%。 8. A method for preparing a metallic material composed of endogenous alloy powder and a coating body according to claim 7, characterized in that, The endogenous alloy powder M a1 A b1 T c1 Compared to M, the impurity content of T is higher. d1 T e1 The raw material cost has been greatly reduced, i.e., c1 is less than e1.

9. A method for preparing a metallic material composed of endogenous alloy powder and a coating body according to claim 7, characterized in that, In the metallic material composed of the endogenous alloy powder and the coating, the endogenous M a1 A b1 T c1 The volume percentage of alloy powder and M during raw material preparation d1 T e1 The volume percentage of the raw materials is equivalent.

10. A method for preparing a metallic material composed of endogenous alloy powder and a coating body according to claim 1, characterized in that, The lower limit of the volume percentage content of the endogenous alloy powder in the metallic material composed of the endogenous alloy powder and the coating is 1%, and the upper limit is the volume percentage content corresponding to the dispersion of the endogenous alloy powder in the coating.

11. The method for preparing a metallic material composed of endogenous alloy powder and a coating body according to claim 1, characterized in that, The volume percentage content of the endogenous alloy powder in the metallic material composed of the endogenous alloy powder and the coating ranges from 1% to 50%.

12. A method for preparing alloy powder, characterized in that, The process involves removing the coating portion from a metallic material composed of endogenous alloy powder and coating prepared by the method described in any one of claims 1-11, while retaining the endogenous alloy powder that cannot be removed simultaneously.

13. The method for preparing alloy powder according to claim 12, characterized in that, Methods for removing the coating while retaining the endogenous alloy powder include at least one of acid solution dissolution reaction removal, alkaline solution dissolution reaction removal, vacuum volatilization removal, and natural oxidation-powdering removal of the coating.

14. The method for preparing alloy powder according to claim 12, characterized in that, M contains Fe, A contains La, and the metallic material composed of the endogenous alloy powder and the coating is a metallic strip composed of endogenous Fe alloy powder and La coating. La is dissolved in the endogenous Fe alloy powder. Through the natural oxidation-pulverization of the La coating, the endogenous Fe alloy powder and the oxide powder of the matrix La are pre-separated. Through the magnetic properties of Fe alloy powder, a magnetic field is used to separate the Fe alloy powder and the oxide of the matrix La.

15. The method for preparing alloy powder according to claim 12, characterized in that, The particle size of the alloy powder ranges from 3 nm to 10 mm.

16. A method for preparing spherical or near-spherical alloy powder, characterized in that, The alloy powder described in claim 12 is subjected to plasma spheroidization treatment to obtain spherical or near-spherical alloy powder.

17. The method for preparing spherical or near-spherical alloy powder according to claim 16, characterized in that, Prior to plasma spheroidization, the selected particles are subjected to air jet mill pre-crushing and / or sieving.

18. A metallic material composed of endogenous alloy powder and a coating, characterized in that, It is prepared by the preparation method of the metallic material composed of endogenous alloy powder and coating as described in any one of claims 1-11.

19. An alloy powder, characterized in that, It is prepared by the method for preparing alloy powder according to claim 12.

20. A spherical or near-spherical alloy powder, characterized in that, It is prepared by the method for preparing spherical or near-spherical alloy powder as described in claim 16.

21. The application of a metallic material composed of endogenous alloy powder and a coating in coatings and composite materials, characterized in that, The metallic material composed of the endogenous alloy powder and the coating is prepared by the preparation method of the metallic material composed of the endogenous alloy powder and the coating as described in any one of claims 1-11.

22. The application of a metallic material composed of endogenous alloy powder and a coating as described in claim 21 in coatings and composite materials, characterized in that, After preparing the metallic material composed of endogenous alloy powder and coating, instead of removing the coating and finding other ways to protect the endogenous alloy powder from oxygen impurities, the coating is directly used to protect the endogenous alloy powder; this metallic material composed of endogenous alloy powder and coating is directly used as a raw material for downstream production. When downstream production requires the use of endogenous alloy powder, the endogenous alloy powder is released at an appropriate time and in a suitable environment, based on the characteristics of the next process. The released endogenous alloy powder is then introduced into the next production process in the shortest possible time, thereby reducing the chance of contamination of the alloy powder.

23. The application of a metallic material composed of endogenous alloy powder and a coating as described in claim 21 in coatings and composite materials, characterized in that, Select a metallic material composed of endogenous alloy powder and a coating with an average particle size of less than 1000 nm. Remove the coating. Simultaneously or immediately after coating removal, mix the resulting alloy powder with other components of the coating or composite material to reduce the content of impurities, including oxygen, newly introduced onto the powder surface or surface layer after the alloy powder surface is exposed. Obtain a highly active alloy powder and ensure good atomic-scale bonding between the other components of the coating or composite material and the alloy powder surface. This results in a coating or composite material containing high-purity, ultrafine, and highly active alloy powder, which can be applied in various fields, including antibacterial coatings, weather-resistant coatings, stealth coatings, microwave-absorbing coatings, wear-resistant coatings, anti-corrosion coatings, and resin-based composite materials.

24. The application of an alloy powder in powder metallurgy, metal injection molding, magnetic materials, and coatings, characterized in that, The alloy powder is prepared by the alloy powder preparation method described in claim 12.

25. The application of an alloy powder in catalysis, sterilization, metal powder 3D printing, and composite materials, characterized in that, The alloy powder is prepared by the alloy powder preparation method described in claim 12.

26. The application of a spherical or near-spherical alloy powder in powder metallurgy, metal injection molding, and metal powder 3D printing, characterized in that, The spherical or near-spherical alloy powder is prepared by the method for preparing spherical or near-spherical alloy powder as described in claim 16.

27. A metallic material composed of endogenous alloy powder and a coating, characterized in that, Prepared by solidification of alloy melt, its composition includes an endogenously precipitated dispersed particle phase during the initial alloy solidification process and a matrix phase coating the dispersed particles, which respectively correspond to the endogenous alloy powder and the coating body; the elemental composition of the endogenous alloy powder is mainly M. a1 A b1 T c1 The elemental composition of the coating is mainly A. b2 T c2 M and A each contain one or more metallic elements, T is an impurity element including oxygen, and a1, b1, c1, b2, and c2 represent the atomic percentage content of the corresponding elements, where a1+b1+c1=100%, b2+c2=100%, c2>c1>0, and b1>0; the melting point of the endogenous alloy powder is higher than the melting point of the coating; the endogenous alloy powder M a1 A b1 T c1 The solid contains element A; the M and the A contain one or more groups of M that do not form intermetallic compounds. 1 -A 1 Combinations of elements, where M 1 A represents any element in M. 1 Let M represent any element in A, and let M be the principal element satisfying M 1 -A 1 M of the element combination conditions 1 The main elements in A are composed of elements that satisfy M. 1 -A 1 Each A in the element combination condition 1 The elemental composition ensures that after the metallic material composed of the endogenous alloy powder and the coating is completely melted and resolidified, it does not form an intermetallic compound composed of the main elements in M ​​and A, but instead forms the endogenous alloy powder M. a1 A b1 T c1 With the coating body A b2 T c2 ; Wherein, M comprises at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti, Fe, Co, Ni, Mn, Cu, and Ag, and A comprises at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, Mg, Ca, Li, Na, K, In, Pb, and Zn; Or M may include at least one of Ir, Ru, Re, Os, Tc, W, Cr, Mo, V, Ta, and Nb, and A may include Cu.

28. A metallic material composed of endogenous alloy powder and a coating body according to claim 27, characterized in that, The T refers to impurity elements including O, H, N, P, S, F, and Cl, and 0 <c1≤1.5%,0<b1≤15%。 29. An alloy powder, prepared by removing the coating from a metallic material composed of endogenous alloy powder and a coating as described in any one of claims 27-28, characterized in that, Its elemental composition is mainly M a3 A b3 T c3 a3, b3, and c3 represent the atomic percentage content of the corresponding elements, b3>0, a3+b3+c3=100%, and the T element content in the alloy powder is higher than the T element content in the endogenous alloy powder according to any one of claims 27-28, i.e., c3>c1>0.

30. A spherical or near-spherical alloy powder, characterized in that, Plasma spheroidization treatment is performed on the alloy powder described in claim 29 to obtain spherical or near-spherical alloy powder, characterized in that its elemental composition is mainly M. a4 A b4 T c4 a4, b4, and c4 represent the atomic percentage content of the corresponding elements, b4>0, a4+b4+c4=100%, and the T element content in the spherical or near-spherical alloy powder is higher than the T element content in the unplasma spheroidized alloy powder, i.e., c4>c3>c1>0.

31. A method for preparing a metallic material composed of endogenous alloy powder and a coating, characterized in that, Prepared by the following steps: An initial alloy melt whose main smelted components are M a0 A b0 T c0 , wherein both M and A comprise one or more metal elements, T is an impurity element including oxygen, a0, b0, c0 represent the atomic percentage content of the corresponding constituent elements, a0+b0+c0=100%, 0<c0; between the element M and the element A, there is one or more groups of M 1 -A 1 element combinations that do not form intermetallic compounds, wherein M 1 represents any element in M, A 1 represents any element in A; and the main elements in M are composed of various M 1 -A 1 elements satisfying the M 1 element combination condition, and the main elements in A are composed of various A 1 -A 1 elements satisfying the M 1 element combination condition; M a0 A b0 T c0 The initial alloy melt solidifies into a solid state, resulting in the intrinsic precipitation of M from the melt. a1 A b1 T c1 Dispersed particle phase and A coating of dispersed particles b2 T c2 The matrix phase is the metallic material composed of endogenous alloy powder and a coating as described in any one of claims 27-28, wherein 0 <c1<c0<c2。 32. The method for preparing a metallic material composed of endogenous alloy powder and a coating body according to claim 31, characterized in that, The M a0 A b0 T c0 The initial alloy melt is obtained by melting an alloy raw material containing a first raw material and a second raw material; wherein, the main elemental composition of the first raw material is M. d1 T e1 The main elemental composition of the second raw material is A. d2 T e2 d1, e1, d2, and e2 represent the atomic percentages of the corresponding elements, and 0 <e1≤10%,0<e2≤10%,d1+e1=100%,d2+e2=100%。 33. A method for preparing alloy powder, characterized in that, It is prepared by removing the coating portion from the metallic material composed of endogenous alloy powder and coating as described in any one of claims 27-28, while retaining the endogenous alloy powder that cannot be removed at the same time.

34. The application of the alloy powder according to claim 29, or the alloy powder prepared by the preparation method according to claim 33, in powder metallurgy, metal injection molding, magnetic materials, and coatings.

35. The application of the spherical or near-spherical alloy powder according to claim 30 in powder metallurgy, metal injection molding, and metal powder 3D printing.

36. The application of the metallic material composed of endogenous alloy powder and coating as described in any one of claims 27-28, or the metallic material composed of endogenous alloy powder and coating prepared by the preparation method described in any one of claims 31-32, in coatings and composite materials.

Images