Method for preparing high-purity powder material, application thereof, and double-phase powder material

Abstract

To provide a method for preparing a high-purity powder material, an application thereof, and a double-phase powder material.SOLUTION: The preparation method comprises firstly preparing intermediate alloy powders having first-phase particles wrapped by a second-phase matrix by an atomization comminuting process, impurity elements being enriched into the second-phase matrix during solidification of the intermediate alloy powders and thereby the first-phase particles being purified, and, by removing the second-phase matrix in the intermediate alloy powders, a high-purity target powder material originated from the original first-phase particles being obtained.SELECTED DRAWING: None

Description

[Technical Field]

[0001] This invention relates to the field of micro-nano powder material technology, and in particular to a method for preparing high-purity powder materials and their applications, and to two-phase powder materials. [Background technology]

[0002] Atomization milling is a powder production method in which metal or alloy liquid is broken into fine droplets by bombardment with a fast-moving fluid (atomization medium) or other means, and then condensed into solid powder. Atomization milling methods mainly include: gas atomization, water atomization, steam-combined atomization, vacuum atomization, plasma atomization, centrifugal atomization, rotating disk atomization, rotating electrode atomization, and ultrasonic atomization.

[0003] With the current principles of atomization milling, the cost of obtaining large quantities of ultrafine metal powders with particle sizes of 10 μm or less is extremely high. It is difficult to directly obtain submicrometer and nanometer powders with particle sizes of 1 μm or less using atomization milling. Furthermore, controlling impurities in atomization milling (especially removing oxygen impurities) is also a key issue that must be resolved. To obtain high-purity metal powders, current technology not only requires the use of high-purity metal raw materials, but also requires strict control of other impurities that may be introduced during the melting and atomization processes. This significantly increases the production costs of metal powders. Therefore, the development of new methods for producing high-purity ultrafine metal powder materials based on current atomization milling technology is of great importance. Summary of the Invention [Problem to be solved by the invention]

[0004] Therefore, to address the above issues, it is necessary to provide a manufacturing method for high-purity powder materials that is simple and easy to handle. [Means for solving the problem]

[0005] A method for preparing a high purity powder material is characterized by comprising the following steps: Step 1: Select the initial alloy raw materials and melt them according to the proportion of the initial alloy components to obtain a uniform initial alloy melt; Step 2: The initial alloy melt is atomized and solidified using atomization milling technology to obtain intermediate alloy powder; the intermediate alloy powder consists of a first phase and a second phase, the first phase is granular, the second phase is a substrate phase with a lower melting point than the first phase, and the first phase granules are coated on the second phase substrate. In the atomization milling process, the impurity elements in the initial alloy melt and the impurity elements introduced during the atomization solidification process are collected in the second phase substrate, thereby purifying the first phase granules; Step 3: The second phase matrix in the intermediate alloy powder is removed, leaving the first phase granules, and the impurity elements in the second phase matrix are also removed, thereby obtaining a high-purity target metal powder material consisting of the first phase granules.

[0006] In this step 1, Furthermore, the impurity element in the initial alloy melt is T. T includes at least one of O, H, N, P, S, F, Cl, I, and Br, and the total content of these impurity elements is the content of T. Furthermore, the sources of impurity elements T in the initial alloy melt are impurities in the initial alloy raw materials and impurities introduced into the atmosphere or crucible during the melting process. Here, the impurities introduced into the atmosphere of the molten alloy are O, N, H, etc. in the atmosphere surrounding the molten alloy.

[0007] Furthermore, if the raw materials are simple or intermediate alloys containing impurity elements, they can be melted in proportion to produce the initial alloy melt. If the supplied raw materials match the composition of the initial alloy melt, they can be remelted to directly obtain the initial alloy melt. Furthermore, the initial alloy raw material is MT containing the impurity element T. For example, if M is Ti and T contains O, the raw material MT is a Ti-O raw material containing the impurity O.

[0008] Furthermore, the average composition of the raw materials of the initial alloy melt includes any combination of the following (1)-(4). Combination (1): The average composition of the initial alloy melt is mainly A a (M x D y) b T d where A includes at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu; M includes at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, and Ti; and D includes at least one of Fe, Co, and Ni, where x, y, a, b, and d represent the atomic percentage contents of the constituent elements; and 0.5%≦a≦99.5%, 0.5%≦b≦99.5%, and 0≦d≦10%;

[0009] In the optimal solution, A includes at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu; M includes at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, and Ti; and D includes at least one of Fe, Co, and Ni.

[0010] The optimal plan is 0.5%≦a≦99.4%, 0.5%≦b≦99.4%, 0 <d≦10%;1%≦a≦99%,1%≦b≦99%,0≦d≦10%;1%≦a≦98.9%,1%≦b≦98.9%,0<d≦10%;2%≦a≦98%,2%≦b≦98%,0≦ d≦10%;2%≦a≦97.9%,2%≦b≦97.9%,0<d≦10%;

[0011] Furthermore, 5%≦x≦55%, 45%≦y≦95%; Moore ratio x:y=0.9~1.1; the optimal solution is x=y=50%, that is, Moore ratio x:y=1:1.

[0012] Combination (2): The average composition of the initial alloy melt is mainly A a M b T dwhere A contains at least one of Mg, Ca, Li, Na, K, Cu, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, and M contains at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti. Among them, a, b, and d represent the atomic percentage contents of the constituent elements. Also, 0.5% ≤ a ≤ 99.5%, 0.5% ≤ b ≤ 99.5%, 0 ≤ d ≤ 10%;

[0013] As an optimal solution, M contains at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti, and A contains at least one of Mg, Ca, Li, Na, K, Cu, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu.

[0014] As an optimal solution, M contains at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti, and A contains Cu.

[0015] As an optimal solution, A contains at least one of Mg, Ca, Li, Na, K, Cu, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, and M contains at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti.

[0016] As an optimal solution, 0.5% ≤ a ≤ 99.4%, 0.5% ≤ b ≤ 99.4%, 0 < d ≤ 10%; 1% ≤ a ≤ 99%, 1% ≤ b ≤ 99%, 0 ≤ d ≤ 10%; 1% ≤ a ≤ 98.9%, 1% ≤ b ≤ 98.9%, 0 < d ≤ 10%; Further, as an optimal solution, 2% ≤ a ≤ 98%, 2% ≤ b ≤ 98%, 0 ≤ d ≤ 10%; 2% ≤ a ≤ 97.9%, 2% ≤ b ≤ 97.9%, 0 < d ≤ 10%;

[0017] Combination (3): The average composition of the initial alloy melt is mainly A a M b T dwhere A includes at least one of Zn, Mg, Sn, Pb, Ga, In, Al, La, Ge, Cu, K, Na, and Li, and M includes at least one of Be, B, Bi, Fe, Ni, Cu, Ag, Si, Ge, Cr, and V. The percentage of Be, B, Si, and Ge atoms in M ​​is 50% or less. a, b, and d represent the percentage atomic content of the constituent elements. Also, 0.5%≦a≦99.5%, 0.5%≦b≦99.5%, and 0≦d≦10%;

[0018] In the optimum solution, A includes at least one of Zn, Mg, Sn, Pb, Ga, In, Al, La, Ge, Cu, K, Na, and Li, and M includes at least one of Be, B, Bi, Fe, Ni, Cu, Ag, Si, Ge, Cr, and V. Furthermore, when M includes Fe and Ni, it does not include Cr and V.

[0019] In the optimum solution, A is a combination of at least one of Zn, Mg, Sn, Pb, Ga, In, Al, La, Ge, Cu, K, Na, and Li, and M is a combination of at least one of Be, B, Bi, Fe, Ni, Cu, Ag, Si, Ge, Cr, and V. Furthermore, when M contains Fe and Ni, it does not contain Cr and V.

[0020] When the percentage content of Be, B, Si, and Ge atoms in M ​​is less than 50%, it can be guaranteed that the material made of M is mainly metallic.

[0021] In the optimal solution, M contains at least one of Be, B, Bi, Fe, Ni, Cu, Ag, Si, Ge, Cr, and V. In addition, the percentage of Be, B, Si, and Ge atoms in M ​​is 30% or less.

[0022] In the optimal solution, A contains at least one of Zn, Mg, Sn, Pb, Ga, In, Al, La, Ge, Cu, K, Na, and Li, and M contains at least one of Be, B, Bi, Fe, Ni, Cu, Ag, Si, Ge, Cr, and V, where a, b, and d represent the atomic percentage contents of the constituent elements, and 0.5%≦a≦99.5%, 0.5%≦b≦99.5%, and 0≦d≦10%.

[0023] As an optimal solution, when M contains B, A contains at least one of Sn, Ge, Cu, and Zn. When M contains Bi, A contains at least one of Sn, Ga, and Al.

[0024] As an optimal solution, when M contains at least one of Fe, Ni, Cu, and Ag, A contains at least one of La, In, Na, K, Li, Pb, and Mg. When M contains at least one of Fe and Ni, A contains at least one of La, In, Na, K, Li, and Mg. When M contains at least one of Cu and Ag, A contains at least one of Pb, Na, K, and Li.

[0025] As an optimal solution, when M contains at least one of Si and Ge, A contains at least one of Zn, Sn, Pb, Ga, In, and Al.

[0026] As an optimal solution, when M contains at least one of Cr and V, A contains Zn.

[0027] As an optimal solution, 0.5% ≤ a ≤ 99.4%, 0.5% ≤ b ≤ 99.4%, 0 < d ≤ 10%; 1% ≤ a ≤ 99%, 1% ≤ b ≤ 99%, 0 ≤ d ≤ 10%; 1% ≤ a ≤ 98.9%, 1% ≤ b ≤ 98.9%, 0 < d ≤ 10%; Further, as an optimal solution, 2% ≤ a ≤ 98%, 2% ≤ b ≤ 98%, 0 ≤ d ≤ 10%; 2% ≤ a ≤ 97.9%, 2% ≤ b ≤ 97.9%, 0 < d ≤ 10%;

[0028] Combination (4): The average composition of the initial alloy melt is mainly A a M b Al c T dwhere A contains at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, and M contains at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti. Al is aluminum. Among them, a, b, c, d represent the atomic percentage contents of the constituent elements. Also, 0.5 ≤ a ≤ 99.4%, 0.5 ≤ b ≤ 99.4%, 0.1% ≤ c ≤ 25%, 0 ≤ d ≤ 10%;

[0029] As an optimal solution, A contains at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, and M contains at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti.

[0030] As an optimal solution, 0.5 ≤ a ≤ 99.3%, 0.5 ≤ b ≤ 99.3%, 0.1% ≤ c ≤ 25%, 0 < d ≤ 10%; As an optimal solution, 1 ≤ a ≤ 98.9%, 1 ≤ b ≤ 98.9%, 0.1% ≤ c ≤ 25%, 0 ≤ d ≤ 10%; 1 ≤ a ≤ 98.8%, 1 ≤ b ≤ 98.8%, 0.1% ≤ c ≤ 25%, 0 < d ≤ 10%; Further, as an optimal solution, 2 ≤ a ≤ 97.9%, 2 ≤ b ≤ 97.9%, 0.1% ≤ c ≤ 25%, 0 ≤ d ≤ 10%; 2 ≤ a ≤ 97.8%, 2 ≤ b ≤ 97.8%, 0.1% ≤ c ≤ 25%, 0 < d ≤ 10%.

[0031] Furthermore, the average composition of the raw materials for the initial alloy melting includes any one combination of the above (1)-(4).

[0032] Furthermore, among the average compositions of the initial melts in step 1, the combination of A and M is extremely important, and the selection principle is to ensure that no intermetallic compound is formed between A and M during the solidification of the melt. Or even if M forms a high-melting-point intermetallic compound with other element (D), no intermetallic compound is formed between A and M. Thereby, during the solidification process of the initial alloy melt, it is realized that mainly the matrix phase of A and mainly the granular phase of M(D) are phase-separated. Subsequently, it is advantageous for the preparation of the powder material mainly composed of M(D).

[0033] Furthermore, in step 2, the intermediate alloy powder does not contain any intermetallic compounds consisting of A and M. Furthermore, the intermediate alloy powder does not contain the intermetallic compound consisting of A and D.

[0034] Furthermore, in any atomization milling method, the intermediate alloy powder produced is significantly different in shape from the alloy strip or alloy ingot obtained by other solidification methods, and the process principles of alloy melting and solidification are also significantly different. For example, atomization milling produces powder using the principle of "melt atomization-droplet solidification."

[0035] Furthermore, when the average composition of the initial alloy melt is described by combination (1) in step 1, the intermediate alloy powder mainly forms first-phase granules of (MxDy)x1Tz1 and second-phase matrix of Ax2Tz2, where 98%≦x1≦100%, 0≦z1≦2%; 70%≦x2≦100%, 0≦z2≦30%; z1≦d≦z2, 2z1≦z2, where x1, z1, x2, and z2 represent the atomic percentage contents of the constituent elements.

[0036] The optimal solution is 98%≦x1<100%, 0 <z1≦2%;70%≦x2<100%, 0<z2≦30%;z1<d<z2,2z1<z2。 The optimal solution is 98.5%≦x1≦100%, 0≦z1≦1.5%; 70%≦x2≦100%, 0≦z2≦30%; z1≦d≦z2, 2z1≦z2. The optimal solution is 98.5%≦x1<100%, 0 <z1≦1.5%;70%≦x2<100%, 0<z2≦30%;z1<d<z2,2z1<z2。 The optimal solution is 99%≦x1≦100%, 0≦z1≦1%; 70%≦x2≦100%, 0≦z2≦30%; z1≦d≦z2, 2z1≦z2. The optimal solution is 99%≦x1<100%, 0 <z1≦1%;70%≦x2<100%, 0<z2≦30%;z1<d<z2,2z1<z2。

[0037] In the optimal solution, when the average composition of the initial alloy melt is described by combination (1) in step 1, the composition is mainly (MxDy)x1Tz1, and the first phase granules do not contain the A element.

[0038] In the optimal case, if the average composition of the initial alloy melt is described by the combination (1) in step 1, the composition of the first phase granules is (M x D y ) x1 T z1 is.

[0039] If the average composition of the initial alloy melt is described by combination (2) or combination (3) in step 1, the intermediate alloy powder contains mainly M. x1 T z1 Phase 1 granules and A x2 T z2 A second phase matrix of the following is formed, wherein 98%≦x1≦100%, 0≦z1≦2%; 70%≦x2≦100%, 0≦z2≦30%; z1≦d≦z2. 2z1≦z2; x1, z1, x2, z2 represent the atomic percentage contents of the constituent elements.

[0040] The optimal solution is 98%≦x1<100%, 0 <z1≦2%;70%≦x2<100%, 0<z2≦30%;z1<d<z2,2z1<z2。 The optimal plan is 98.5%≦x1≦100%, 0≦z1≦1.5%; 70%≦x2≦100%, 0≦z2≦30%; z1≦d≦z2, 2z1≦z2. The optimal plan is 98.5%≦x1<100%, 0 <z1≦1.5%;70%≦x2<100%, 0<z2≦30%;z1<d< z2,2z1<z2。 The optimal solution is 99%≦x1≦100%, 0≦z1≦1%; 70%≦x2≦100%, 0≦z2≦30%; z1≦d≦z2, 2z1≦z2. The optimal solution is 99%≦x1<100%, 0 <z1≦1%;70%≦x2<100%, 0<z2≦30%;z1<d<z2,2z1<z2。

[0041] In the optimal case, when the average composition of the initial alloy melt is described in step 1 (2) or step 3, the composition is mainly M.x1 T z1 The first-phase particles of T do not contain element A.

[0042] As an optimal solution, when the average composition of the initial alloy melt is described by the combination (2) or combination (3) in step 1, the composition of the first-phase particles is M x1 T z1 That's it.

[0043] When the average composition of the initial alloy melt is described by the combination (4) in step 1, mainly M in the intermediate alloy powder x1 Al y1 T z1 The first-phase particles of and A x2 Al y2 T z2 The second-phase matrix of is formed. Among them, 78%≦x1≦99.9%, 0.1%≦y1≦22%, 0≦z1≦2%; 70%≦x2≦99.8%, 0.2%≦y2≦30%, 0≦z2≦30%, z1≦d≦z2, 2z1≦z2, y1<y2. x1, y1, z1, x2, y2, z2 represent the atomic percentage contents of the constituent elements.

[0044] As an optimal solution, 78%≦x1≦99.8%, 0.1%≦y1≦21.9%, 0<z1≦2%; 70%≦x2≦99.7%, 0.2%≦y2≦29.9%, 0<z2≦30%, z1<d<z2, 2z1<z2. As an optimal solution, 78%≦x1≦99.9%, 0.1%≦y1≦22%, 0≦z1≦1.5%; 70%≦x2≦99.8%, 0.2%≦y2≦30%, 0≦z2≦30%, z1≦d≦z2, 2z1≦z2. As an optimal solution, 78%≦x1≦99.8%, 0.1%≦y1≦21.9%, 0<z1≦1.5%; 70%≦x2≦99.7%, 0. 2%≦y2≦29.9%, 0<z2≦30%, z1<d<z2, 2z1<z2. As the optimal solution, 78% ≤ x1 ≤ 99.9%, 0.1% ≤ y1 ≤ 22%, 0 ≤ z1 ≤ 1%; 70% ≤ x2 ≤ 99.8%, 0.2% ≤ y2 ≤ 30%, 0 ≤ z2 ≤ 30%, z1 ≤ d ≤ z2, 2z1 ≤ z2. As the optimal solution, 78% ≤ x1 ≤ 99.8%, 0.1% ≤ y1 ≤ 21.9%, 0 < z1 ≤ 1%; 70% ≤ x2 ≤ 99.7%, 0.2% ≤ y2 ≤ 29.9%, 0 < z2 ≤ 30%, z1 < d < z2, 2z1 < z2. Furthermore, y1 < y2.

[0045] As the optimal solution, when the average composition of the initial alloy melt is described by the combination (4) in Step 1, the components are mainly M x1 Al y1 T z1 of the first-phase particles and do not contain element A.

[0046] As the optimal solution, when the average composition of the initial alloy melt is described by the combination (4) in Step 1, the components of the first-phase particles are M x1 Al y1 T z1 only.

[0047] Furthermore, during the atomization powder-making process, the impurity elements of the initial alloy melt gather in the second-phase matrix, and the first-phase particles are purified.

[0048] Furthermore, z1 ≤ d ≤ z2, 3z1 ≤ z2. As the optimal solution, z1 ≤ d ≤ z2, 3z1 ≤ z2, and also 0 ≤ z1 ≤ 1%.

[0049] Furthermore, z1 < d < z2, 3z1 < z2. That is, the content of impurity T in the first-phase particles is lower than that in the initial alloy melt. Also, three times the content of impurity T in the first-phase particles is still lower than that in the second-phase matrix. As the optimal solution, z1 < d < z2, 3z1 < z2. Also, 0 < z1 < 1%.

[0050] Furthermore, when the initial alloy raw material is M-T containing the impurity element T, the atomic percentage content z1 of the impurity element T in the first-phase particles is smaller than the atomic percentage content of the impurity element T in the M-T raw material.

[0051] In this invention, the content of the impurity element T is expressed in atomic percentage content. The atomic percentage content of an element represents the composition of each element, and the increase / decrease in the content of an element can be accurately expressed using the concept of the amount of substance. For example, the increase / decrease and change in the content of an impurity element. If the content of each element is expressed in mass percentage content (or ppm concept), it is easy to reach an erroneous conclusion because the atomic weight of each element is different. For example, the atomic percentage content of Ti 45 Gd 45 O 10 The alloy contains 100 atoms, and the atomic percentage content of O is 10 at%. 45 O4 (atomic ratio is Ti 91.8 O 8.2 ) and Gd 45 O6 (atomic ratio is Gd 88.2 O 11.8 ) and Gd 45 The oxygen atomic percentage content in O6 increased to 11.8 at% and Ti 45 The atomic percentage of oxygen in O4 is reduced to 8.2 at%, accurately representing the concentration of O in Gd. However, when measured using the mass percentage of O, Ti 45 Gd 45 O 10 The mass percentage of O in the 45 O4 and Gd 45 The mass percentage contents of O in O6 are 2.9 wt.% and 1.34 wt.%, but Ti 45 The mass percentage content of O in O4 is Gd 45 O6 leads to the erroneous conclusion of a significant increase.

[0052] Additionally, atomization milling techniques include at least one of gas atomization, water atomization, steam-co-atomization, vacuum atomization, plasma atomization, centrifugal atomization, spinning disk atomization, and rotating electrode atomization.

[0053] Furthermore, the granule shape of this intermediate alloy powder includes spherical, near-spherical, water droplet, dumbbell, irregular rod, and the like.

[0054] By adjusting the atomization parameters, the initial alloy melt undergoes the atomization process to obtain droplets of different sizes, which then solidify to obtain intermediate alloy powders of different particle sizes. When the energy of the atomization medium is relatively high, intermediate alloy powders with small particle sizes are obtained, and the solidification rate of the intermediate alloy powder is generally higher. When the energy of the atomization medium is low, intermediate alloy powders with larger particle sizes are obtained, and the solidification rate of the intermediate alloy powder is generally lower.

[0055] Furthermore, the particle size range of the intermediate alloy powder is 1 μm to 8 mm. Furthermore, the particle size range of the intermediate alloy powder is 1 μm to 4 mm. Furthermore, the particle size range of the intermediate alloy powder is 1 μm to 1 mm. Furthermore, the particle size range of the intermediate alloy powder is 1 μm to 250 μm. Furthermore, the particle size range of the intermediate alloy powder is 1 μm to 100 μm. Furthermore, the particle size range of the intermediate alloy powder is 1 μm to 50 μm. Furthermore, the particle size range of the intermediate alloy powder is 1 μm to 20 μm.

[0056] Furthermore, the particle size of the first phase granules in the intermediate alloy powder correlates with the atomization solidification rate of the initial alloy melt. Generally, the particle size of the first phase granules in the intermediate alloy powder correlates inversely with the atomization solidification rate of the initial alloy melt. That is, the higher the atomization solidification rate of the initial alloy melt, the smaller the particle size of the first phase granules in the intermediate alloy powder.

[0057] Furthermore, the atomization solidification rate of the initial alloy melt is 10 3 K / s~10 6 At K / s, intermediate alloy powder with micron-level particle size can be obtained.

[0058] Furthermore, the atomization solidification rate of the initial alloy melt is 50K / s to 10 3 At K / s, intermediate alloy powder with particle sizes of several hundred microns or millimeters can be obtained.

[0059] Furthermore, the volume fraction of the first phase granules in the intermediate alloy powder is determined by the contents of A and M. The atomic percentage content of M in the intermediate alloy powder is generally 0.5%≦b≦99.5% or 0.5%≦b≦99.4%, so the volume fraction of the first phase granules, which are mainly composed of M, is also close to this ratio.

[0060] Furthermore, the percentage content of the first phase granules in the intermediate alloy powder ranges from 0.5% to 99.5%.

[0061] Furthermore, the specific value of the volume fraction of the first phase granules in the intermediate alloy powder can be determined by combining the average composition of the intermediate alloy powder, the composition of the first and second phases, and the atomic weight and density of each element, and can be calculated based on these parameters.

[0062] Furthermore, the method in which the first phase granules are coated with the second phase substrate includes a mosaic structure in which a plurality of first phase granules are dispersed in the second phase substrate, or a core-shell structure in which a single first phase granule is coated with the second phase substrate.

[0063] Furthermore, the particle size range of the first phase granules in this intermediate alloy powder is 3 nm to 7.9 mm. Furthermore, the particle size range of the first phase granules in this intermediate alloy powder is 3 nm to 3.9 mm. Furthermore, the particle size range of the first phase granules in this intermediate alloy powder is 3 nm to 0.95 mm. Furthermore, the particle size range of the first phase granules in this intermediate alloy powder is 3 nm to 245 μm. Furthermore, the particle size range of the first phase granules in this intermediate alloy powder is 3 nm to 96 μm. Furthermore, the particle size range of the first phase granules in this intermediate alloy powder is 3 nm to 47 μm. Furthermore, the particle size range of the first phase granules in this intermediate alloy powder is 3 nm to 18.5 μm.

[0064] Furthermore, when the b value content in the initial alloy, which is mainly composed of components Aa(MxDy)bTd, AaMbTd, or AaMbAlcTd, is low, such as 0.5%≦b≦75%, the volume percentage content of the first-phase granules of the main components (MxDy)x1Tz1, Ax1Tz1, or Ax1Aly1Tz1 in the intermediate alloy powder during the droplet atomization solidification process is low, and the first-phase granules are likely to precipitate as a large amount of diffused granules and be embedded in the second-phase matrix.

[0065] Furthermore, when 0.5%≦b≦75% and the cooling rate of the atomized droplets is high, the first-phase granules in the intermediate alloy powder have enough time to grow, and primarily form nanoscale (e.g., 3 nm to 100 nm) or submicron-scale (e.g., 100 nm to 1 μm) first-phase granules.

[0066] Furthermore, when 0.5% ≤ b ≤ 75% or the cooling rate of the atomized droplets is low, the primary phase particles can grow sufficiently, and primary phase particles mainly on the sub-micron scale (for example, 100 nm to 1 μm) or the micrometer level (for example, 1 μm to 100 μm) can be formed.

[0067] In addition, since the atoms of the second-phase matrix elements in the master alloy powder according to the present invention are generally larger than the atoms of the primary phase particle elements, the second-phase matrix can pass through a smaller atomic percentage content and obtain a higher volume percentage content. For example, for an initial alloy with a La25Fe75 atomic percentage composition (without considering the impurity situation), b = 75%, and by the atomization powder manufacturing technology, a master alloy powder composed of a La matrix and primary phase Fe particles can be obtained. Among them, the weight percentage contents of La and Fe are 45.33 wt% and 54.67 wt% respectively, and the two densities are 6.2 g / cm 3 and 7.8 g / cm 3 respectively. For the master alloy powder with an atomic percentage of La 25 Fe 75 , the volume percentage contents of La and Fe in the master alloy powder can be calculated, which are 51 vol.% and 49 vol.% respectively. This ensures that even if b is significantly larger than 50%, the volume percentage content of the obtained primary phase particles is less than 50% and is dispersed and distributed in the matrix phase. Therefore, it is reasonable to set the above b = 75% as the limit value at which the primary phase particles can be dispersed and precipitated in the second-phase matrix.

[0068] Furthermore, when the content of the b value is high in the initial alloy of the main component A a (M x D y ) b T d , A a M b T d , or A a M b Al c T d , for example, 75% < b ≤ 99.5% or 75% < b ≤ 99.4%, and during the process of droplet atomization and solidification, the main component (M x D y ) x1 T z1 , Ax1 T z1 Or A x1 Al y1 T z1 The volume percentage of the first phase granules in the intermediate alloy powder is higher, and a large number of the first phase granules precipitated during the solidification process will inevitably form bridges, coalescence, and growth. At this time, the first phase granules in the intermediate alloy powder are likely to be coated on the second phase substrate as one or several coalescence grains after precipitation.

[0069] Furthermore, when the b value is very high, such as 95%≦b≦99.5% or 95%≦b≦99.4%, the first phase granules dominate the volume of the intermediate alloy powder, and the first phase granules exist as only one grain in the intermediate alloy powder, and this granule and the outer covering second phase substrate can form a core-shell structure.

[0070] Furthermore, when the b value is extremely high, such as 95%≦b≦99.5% or 95%≦b≦99.4%, the particle size of the intermediate alloy powder produced through atomization milling technology is in the range of 1 μm to 8 mm, and the particle size of the first phase granules within the intermediate alloy powder is only slightly smaller than that of the corresponding intermediate alloy powder. For example, if the particle size of the intermediate alloy powder is 100 μm, the particle size of the single first phase granule within it can be 96 μm.

[0071] In the description of step 3, the method for removing the second phase substrate in the intermediate alloy powder further includes at least one of acid reaction removal, alkali reaction removal, and vacuum evaporation removal.

[0072] The composition and concentration of the acid solution and alkaline solution are not specifically limited, as long as they can ensure that the first phase granules are retained while removing the base phase.

[0073] The temperature and vacuum level of this vacuum treatment are not specifically limited, as long as it is possible to ensure that the first phase granules are retained while removing the base phase.

[0074] Furthermore, the method for removing the second phase substrate in the intermediate alloy powder includes natural oxidation-pulverization peeling removal of the second phase substrate.

[0075] If the second phase is an element that is easily oxidized by oxygen, such as La or Ce, the second phase substrate can be separated from the first phase particles through the natural oxidation-pulverization process of the second phase substrate.Furthermore, other techniques such as magnetic separation can be used to separate the magnetic first phase particles from the natural oxide of the second phase substrate.

[0076] Furthermore, when the average composition of the initial alloy melt is as described in step 1 combination (1), the composition of the high purity target powder material is mainly (MxDy)x1Tz1.

[0077] In the optimal solution, if the average composition of the initial alloy melt is as described by combination (1) in step 1, the high-purity target powder material, whose composition is mainly (MxDy)x1Tz1, does not contain element A.

[0078] In the optimal case, if the average composition of the initial alloy melt is described by combination (1) in step 1, the high purity target powder material will have a composition mainly of (MxDy)x1Tz1.

[0079] Furthermore, when the average composition of the initial alloy melt is described by combination (2) or (3) of step 1, the composition of the high purity target powder material is mainly M x1 T z1 is.

[0080] In the optimal case, if the average composition of the initial alloy melt is described by combination (2) or (3) in step 1, the composition is mainly M. x1 T z1 The high purity target powder material does not contain A elements.

[0081] In the optimal case, if the average composition of the initial alloy melt is described by combination (2) or (3) in step 1, the high purity target powder material will contain M x1 T z1 It is an ingredient of.

[0082] Furthermore, when the average composition of the initial alloy melt is explained by the combination (4) in step 1, the composition of the high purity target powder material is mainly M x1 Al y1 T z1 is.

[0083] In the optimal case, if the average composition of the initial alloy melt is described by combination (4) in step 1, the composition is mainly M x1 Al y1 T z1 The high purity target powder material does not contain A elements.

[0084] In the optimal case, if the average composition of the initial alloy melt is described by combination (4) in step 1, the high purity target powder material contains M x1 Al y1 T z1 It is an ingredient of.

[0085] Furthermore, the particle size range of the high-purity target powder material is 3nm to 7.9mm. Furthermore, the particle size range of the high-purity target powder material is 3nm to 3.9mm. Furthermore, the particle size range of the high-purity target powder material is 3nm to 0.95mm. Furthermore, the particle size range of the high-purity target powder material is 3nm to 245μm. Furthermore, the particle size range of the high-purity target powder material is 3nm to 96μm. Furthermore, the particle size range of the high-purity target powder material is 3nm to 47μm. Furthermore, the particle size range of the high-purity target powder material is 3nm to 18.5μm.

[0086] Furthermore, the shape of the high purity target powder includes spherical, near-spherical, branched, rod-shaped, and plate-shaped.

[0087] The present invention relates to the application of the target powder material obtained by the above manufacturing method to catalytic materials, powder metallurgy, composite materials, wave-absorbing materials, bactericidal materials, metal injection molding, 3D printing additive manufacturing, and coating materials.

[0088] The present invention also relates to a two-phase powder material. The two-phase powder material is characterized by a powder form, and each single granule further comprises an inner powder and a coating. The solidification structure of the two-phase powder material comprises a matrix phase and a granule phase, the matrix phase being the coating phase, and the granule phase being the inner powder in the two-phase powder material. The melting point of the coating is lower than that of the inner powder, and the inner powder is coated by the coating.

[0089] The chemical composition and structure of the two-phase powder material include any of the following four combinations:

[0090] 1) The component of the in-situ powder in this two-phase powder material is mainly (MxDy)x1Tz1, and the average component of the coating is mainly A x2 T z2 ; also, 8% ≤ x1 ≤ 100%, 0 ≤ z1 ≤ 2%; 70% ≤ x2 ≤ 100%, 0 ≤ z2 ≤ 30%; z1 ≤ d ≤ z2, 2z1 ≤ z2. x1, z1, x2, and z2 respectively represent the atomic percentage contents of the corresponding compositional elements. Among them, A contains at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu, M contains at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, and Ti, D contains at least one of Fe, Co, and Ni, and T contains at least one of O, H, N, P, S, F, Cl, I, and Br. x and y represent the atomic percentage contents of the corresponding compositional elements. 5% ≤ x ≤ 55%, 45% ≤ y ≤ 95%. Furthermore, the molar ratio x:y = 0.9 - 1.1. As the optimal solution, x = y = 50%. That is, the Moore ratio is x:y = 1:1

[0091] As the optimal solution, A is composed of at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu. As the optimal solution, M is composed of at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, and Ti. As the optimal solution, D is composed of at least one of Fe, Co, and Ni

[0092] As the optimal solution, 98% ≤ x1 < 100%, 0 < z1 ≤ 2%; 70% ≤ x2 < 100%, 0 < z2 ≤ 30%; z1 < d < z2, 2z1 < z2. As the optimal solution, 98.5% ≤ x1 ≤ 100%, 0 ≤ z1 ≤ 1.5%; 70% ≤ x2 ≤ 100%, 0 ≤ z2 ≤ 30%; z1 ≤ d ≤ z2, 2z1 ≤ z2. As the optimal solution, 98.5% ≤ x1 < 100%, 0 < z1 ≤ 1.5%; 70% ≤ x2 < 100%, 0 < z2 ≤ 30%; z1 < d < z2, 2z1 < z2. As the optimal solution, 99% ≤ x1 ≤ 100%, 0 ≤ z1 ≤ 1%; 70% ≤ x2 ≤ 100%, 0 ≤ z2 ≤ 30%; z1 ≤ d ≤ z2, 2z1 ≤ z2. As the optimal solution, 99% ≤ x1 < 100%, 0 < z1 ≤ 1%; 70% ≤ x2 < 100%, 0 < z2 ≤ 30%; z1 < d < z2, 2z1 < z2

[0093] As an optimal solution, the endogenous powder in the two-phase powder material with the main component (MxDy)x1Tz1 does not contain element A.

[0094] In the optimal design, the composition of the internal powder of this two-phase powder material is (MxDy)x1Tz1, and the average composition of the coating is Ax2Tz2.

[0095] 2) The components of the endogenous powder in this two-phase powder material are mainly M x1 T z1 The average composition of the coating is mainly A x2 T z2 , and 98%≦x1≦100%, 0≦z1≦2%; 70%≦x2≦100%, 0≦z2≦30%; z1≦d≦z2, 2z1≦z2, where x1, z1, x2, and z2 represent the atomic percentage contents of the corresponding composition elements, where A includes at least one of Mg, Ca, Li, Na, K, Cu, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu, M includes at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, and Ti, and T includes at least one of O, H, N, P, S, F, Cl, I, and Br.

[0096] In the optimum case, when M includes at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, and Ti, A includes one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu.

[0097] In the optimum solution, when M includes at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, and Ti, A includes Cu.

[0098] In the optimal plan, A is composed of at least one of Mg, Ca, Li, Na, K, Cu, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu, and in the optimal plan, M is composed of at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, and Ti.

[0099] As the optimal solution, 98% ≦ x1 < 100%, 0 < z1 ≦ 2%; 70% ≦ x2 < 100%, 0 < z2 ≦ 30%; z1 < d < z2, 2z1 < z2. As the optimal solution, 98.5% ≦ x1 ≦ 100%, 0 ≦ z1 ≦ 1.5%; 70% ≦ x2 ≦ 100%, 0 ≦ z2 ≦ 30%; z1 ≦ d ≦ z2, 2z1 ≦ z2. As the optimal solution, 98.5% ≦ x1 < 100%, 0 < z1 ≦ 1.5%; 70% ≦ x2 < 100%, 0 < z2 ≦ 30%; z1 < d < z2, 2z1 < z2. As the optimal solution, 99% ≦ x1 ≦ 100%, 0 ≦ z1 ≦ 1%; 70% ≦ x2 ≦ 100%, 0 ≦ z2 ≦ 30%; z1 ≦ d ≦ z2, 2z1 ≦ z2. As the optimal solution, 99% ≦ x1 < 100%, 0 < z1 ≦ 1%; 70% ≦ x2 < 100%, 0 < z2 ≦ 30%; z1 < d < z2, 2z1 < z2.

[0100] As the optimal solution, the internal powder in the two-phase powder material of the main component Mx1Tz1 does not contain element A.

[0101] As the optimal solution, the component of the internal powder in this two-phase powder material is M x1 T z1 and the average component of the coating is Ax2Tz2.

[0102] 3) The component of the internal powder in this two-phase powder material is mainly M x1 T z1 and the average component of the coating is mainly A x2 T z2 and also 98% ≦ x1 ≦ 100%, 0 ≦ z1 ≦ 2%; 70% ≦ x2 ≦ 100%, 0 ≦ z2 ≦ 30%; z1 ≦ d ≦ z2, 2z1 ≦ z2. x1, z1, x2, z2 respectively represent the atomic percentage contents of the corresponding compositional elements. Among them, A contains at least one of Zn, Mg, Sn, Pb, Ga, In, Al, La, Ge, Cu, K, Na, Li, M contains at least one of Be, B, Bi, Fe, Ni, Cu, Ag, Si, Ge, Cr, V, and the total content of the atomic percentages of Be, B, Si, Ge in M is 50% or less, and T contains at least one of O, H, N, P, S, F, Cl, I, Br.

[0103] In the optimum solution, A contains at least one of Zn, Mg, Sn, Pb, Ga, In, Al, La, Ge, Cu, K, Na, and Li. M contains at least one of Be, B, Bi, Fe, Ni, Cu, Ag, Si, Ge, Cr, and V. Furthermore, when M contains Fe and Ni, it does not contain Cr and V.

[0104] In the optimal plan, A is composed of at least one of Zn, Mg, Sn, Pb, Ga, In, Al, La, Ge, Cu, K, Na, and Li. In the optimal plan, M is composed of at least one of Be, B, Bi, Fe, Ni, Cu, Ag, Si, Ge, Cr, and V. Furthermore, when M contains Fe and Ni, it does not contain Cr and V.

[0105] In the optimum case, M contains at least one of Be, B, Bi, Fe, Ni, Cu, Ag, Si, Ge, Cr, and V, and the total atomic percentage of Be, B, Si, and Ge in M ​​is less than 30%.

[0106] In the optimal solution, A includes at least one of Zn, Mg, Sn, Pb, Ga, In, Al, La, Ge, Cu, K, Na, and Li; M includes at least one of Be, Bi, Fe, Ni, Cu, Ag, Cr, and V; and T includes at least one of O, H, N, P, S, F, Cl, I, and Br.

[0107] In the optimum solution, when M includes B, A includes at least one of Sn, Ge, Cu, and Zn. When M includes Bi, A includes at least one of Sn, Ga, and Al.

[0108] In the optimum solution, when M contains at least one of Fe, Ni, Cu, and Ag, A contains at least one of La, In, Na, K, Li, Pb, and Mg. When M contains at least one of Fe and Ni, A contains at least one of La, In, Na, K, Li, and Mg. When M contains at least one of Cu and Ag, A contains at least one of Pb, Na, K, and Li.

[0109] As an optimal solution, when M contains at least one of Si and Ge, A contains at least one of Zn, Sn, Pb, Ga, In, and Al.

[0110] As an optimal solution, when M contains at least one of Cr and V, A contains Zn.

[0111] As an optimal solution, 98% ≤ x1 < 100%, 0 < z1 ≤ 2%; 70% ≤ x2 < 100%, 0 < z2 ≤ 30%; z1 < d < z2, 2z1 < z2. As an optimal solution, 98.5% ≤ x1 ≤ 100%, 0 ≤ z1 ≤ 1.5%; 70% ≤ x2 ≤ 100%, 0 ≤ z2 ≤ 30%; z1 ≤ d ≤ z2, 2z1 ≤ z2. As an optimal solution, 98.5% ≤ x1 < 100%, 0 < z1 ≤ 1.5%; 70% ≤ x2 < 100%, 0 < z2 ≤ 30%; z1 < d < z2, 2z1 < z2. As an optimal solution, 99% ≤ x1 ≤ 100%, 0 ≤ z1 ≤ 1%; 70% ≤ x2 ≤ 100%, 0 ≤ z2 ≤ 30%; z1 ≤ d ≤ z2, 2z1 ≤ z2. As an optimal solution, 99% ≤ x1 < 100%, 0 < z1 ≤ 1%; 70% ≤ x2 < 100%, 0 < z2 ≤ 30%; z1 < d < z2, 2z1 < z2.

[0112] As an optimal solution, the main component M x1 T z1 The internal powder in the two-phase powder material does not contain element A.

[0113] As an optimal solution, the component of the internal powder in this two-phase powder material is M x1 T z1 and the average component of the coating is Ax2Tz2.

[0114] 4) The component of the internal powder in this two-phase powder material is mainly M x1 Al y1 T z1 and the average component of the coating is mainly A x2 Al y2 T z2, and also 78% ≤ x1 ≤ 99.9%, 0.1% ≤ y1 ≤ 22%, 0 ≤ z1 ≤ 2%; 70% ≤ x2 ≤ 99.8%, 0.2% ≤ y2 ≤ 30%, 0 ≤ z2 ≤ 30%, z1 ≤ d ≤ z2, 2z1 ≤ z2. y1 < y2, where x1, y1, z1, x2, y2, z2 represent the atomic percentage contents of the corresponding constituent elements. Among them, A contains at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu; M contains at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti; Al is aluminum. T contains at least one of O, H, N, P, S, F, Cl, I, Br.

[0115] As an optimal solution, A contains at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu. As an optimal solution, M contains at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti.

[0116] As an optimal solution, 78% ≤ x1 ≤ 99.8%, 0.1% ≤ y1 ≤ 21.9%, 0 < z1 ≤ 2%; 70% ≤ x2 ≤ 99.7%, 0.2% ≤ y2 ≤ 29.9%, 0 < z2 ≤ 30%, z1 < d < z2, 2z1 < z2. As an optimal solution, 78% ≤ x1 ≤ 99.9%, 0.1% ≤ y1 ≤ 22%, 0 ≤ z1 ≤ 1.5%; 70% ≤ x2 ≤ 99.8%, 0.2% ≤ y2 ≤ 30%, 0 ≤ z2 ≤ 30%, z1 ≤ d ≤ z2, 2z1 ≤ z2. As an optimal solution, 78% ≤ x1 ≤ 99.8%, 0.1% ≤ y1 ≤ 21.9%, 0 < z1 ≤ 1.5%; 70% ≤ x2 ≤ 99.7%, 0.2% ≤ y2 ≤ 29.9%, 0 < z2 ≤ 30%, z1 < d < z2, 2z1 < z2. As an optimal solution, 78% ≤ x1 ≤ 99.9%, 0.1% ≤ y1 ≤ 22%, 0 ≤ z1 ≤ 1%; 70% ≤ x2 ≤ 99.8%, 0.2% ≤ y2 ≤ 30%, 0 ≤ z2 ≤ 30%, z1 ≤ d ≤ z2, 2z1 ≤ z2. As an optimal solution, 78% ≤ x1 ≤ 99.8%, 0.1% ≤ y1 ≤ 21.9%, 0 < z1 ≤ 1%; 70% ≤ x2 ≤ 99.7%, 0.2% ≤ y2 ≤ 29.9%, 0 < z2 ≤ 30%, z1 < d < z2, 2z1 < z2. As an optimal solution, y1 < y2.

[0117] As the optimal solution, the main component M x1 Al y1 T z1 The endogenous powder in the two-phase powder material does not contain A element.

[0118] As an optimal solution, the components of the internal powder in this two-phase powder material are M x1 Al y1 T z1 The average composition of the coating is A x2 Al y2 T z2 is.

[0119] As an optimal solution, the chemical composition and structure of the two-phase powder material are any of the combinations of 1) to 4) above.

[0120] Furthermore, this two-phase powder material does not contain intermetallic compounds consisting of A and M.

[0121] Furthermore, this two-phase powder material does not contain the intermetallic compound consisting of A and D.

[0122] Furthermore, the granule shapes of the two-phase powder material include spherical, near-spherical, droplet-shaped, dumbbell-shaped, irregular rod-shaped, and the like.

[0123] Furthermore, the particle size range of the two-phase powder material is 1 μm to 8 mm. Furthermore, the particle size range of the two-phase powder material is 1 μm to 4 mm. Furthermore, the particle size range of the two-phase powder material is 1 μm to 1 mm. Furthermore, the particle size range of the two-phase powder material is 1 μm to 250 μm. Furthermore, the particle size range of the two-phase powder material is 1 μm to 100 μm. Furthermore, the particle size range of the two-phase powder material is 1 μm to 50 μm. Furthermore, the particle size range of the two-phase powder material is 1 μm to 20 μm.

[0124] Furthermore, the coating method of the endogenous powder in this two-phase powder material: a mosaic structure in which multiple endogenous powders are scattered in the coating, or a core-shell structure in which a single endogenous powder is outside the coating.

[0125] Furthermore, the particle size range of the endogenous powder in two-phase powder materials is 3nm~7.9mm. Optimally, the particle size range of the endogenous powder in two-phase powder materials is 3nm~3.9mm. Optimally, the particle size range of the endogenous powder in two-phase powder materials is 3nm~0.95mm. Optimally, the particle size range of the endogenous powder in two-phase powder materials is 3nm~245μm. Optimally, the particle size range of the endogenous powder in two-phase powder materials is 3nm~96μm. Optimally, the particle size range of the endogenous powder in two-phase powder materials is 3nm~47μm. Optimally, the particle size range of the endogenous powder in two-phase powder materials is 3nm~18.5μm.

[0126] Furthermore, the two-phase powder material is produced by the above-mentioned method for producing high-purity powder material through steps 1 and 2.

[0127] Furthermore, the volume percentage content range of the endogenous powder in the two-phase powder material is 0.5%~99.5%.

[0128] Furthermore, when the two-phase powder material is produced according to steps 1 and 2 of the method for producing high-purity powder material described above, the specific volume percentage content of the endogenous powder in the two-phase powder material can be calculated according to the average composition of the intermediate alloy powder, by combining the composition of the endogenous powder and the coating in the intermediate alloy powder, and by determining the atomic weight and density of each element.

[0129] Furthermore, elements other than those mentioned above or impurity elements may be contained in A, M, D, or T in the solution of the present invention. The introduction or change of the content of these elements will not result in "alteration" of the solidification process and rules of the initial alloy, and will not affect the realization of the above technical solution.

[0130] Specifically, when the solidification process and rules of the initial alloy do not produce any results due to the "transformation" of the alloy, and when elements other than those mentioned above or impurities are contained in A, M, D, or T, the actual processes and rules of 1) to 3) also exist.

[0131] 1) The intermediate alloy powder does not contain intermetallic compounds consisting mainly of A and M, or A and D.

[0132] 2) The solidification structure of the intermediate alloy powder includes a second-phase matrix and first-phase granules. The melting point of the second-phase matrix is ​​lower than that of the first-phase granules, and the first-phase granules are coated with the second-phase matrix.

[0133] 3) When the impurity content T in the initial alloy melt is not 0, the impurity content T in the first phase granules in the intermediate alloy powder is lower than the impurity content T in the initial alloy melt, and the impurity content T in the first phase granules is twice lower than the impurity content T in the second phase matrix.

[0134] The technical solution of the present invention has the following beneficial effects: First, the "atomization milling + phase removal method" can produce spherical powder materials at nanoscale, submicron, micron, and even millimeter scales, which is a very creative solution.

[0135] In step 2, the target powder material is produced through two mechanisms. One is based on the basic principle of atomization milling, whereby the molten alloy is broken into fine droplets through the impact of a fast-moving fluid (atomization medium), which then solidifies into an intermediate alloy powder of a certain particle size. The second is to precipitate the first-phase granules of the intermediate alloy powder into the second-phase matrix during the atomization droplet solidification process, thereby obtaining even finer first-phase granules. If the droplet solidification rate is sufficiently high and the volume percentage content of the intermediate alloy powder is low, the particle size of the first-phase granules precipitated in the intermediate alloy powder can be nanometer-sized. Therefore, by utilizing the atomization medium's impact on the molten alloy and the subsequent precipitation of the first-phase granules into the second-phase matrix, the present invention overcomes the current technical difficulty of obtaining ultrafine powder materials through atomization medium impact alone and significantly reduces the cost of producing ultrafine powder materials. Conventional "atomization milling" technology alone cannot produce granules with a D50 diameter of 5 μm or less, and it is not possible to produce nanoscale powder granules. On the other hand, simple "phase removal" methods can achieve endogenous first-phase granules ranging from nanoscale to millimeter-scale by controlling the cooling rate of the alloy melt. However, conventional "phase removal" methods involve creating an alloy strip using methods such as the fluttering process, removing the second matrix phase from the alloy strip, and obtaining a powder material consisting of first-phase granules detached from the alloy strip. First-phase nanoparticles are generally spherical, but when the first-phase granules are micron-sized, they mainly precipitate as branched granules. Therefore, conventional "phase removal" methods generally only produce micron-scale branched first-phase powder granules, and it is difficult to produce micron-scale spherical first-phase granules. To obtain micron-scale spherical granules, the branched granules must be spheronized using methods such as plasma spheronization, which significantly increases costs. The "atomization milling + phase removal method" of the present invention effectively solves this problem. When producing micron-level spherical powder, increasing the b value significantly increases the volume percentage of first-phase granules in the intermediate alloy powder, resulting in a spherical intermediate alloy powder with a core-shell structure in which a single first-phase granule is coated on a second-phase substrate. The outer shell of the coating substrate is then removed to obtain a spherical powder material mainly consisting of first-phase granules. Furthermore, increasing the b value also increases the volume percentage of first-phase granules in the intermediate alloy powder, significantly reducing the volume and quantity of the coating substrate that needs to be removed. This also reduces production costs.Therefore, the present invention skillfully combines atomization milling technology with the principle of "phase removal method," and by controlling the operating (impact) parameters of the atomization medium, the cooling rate of the atomized droplets, and the b value of the initial alloy "molten" body, it is possible to control the size and shape of the first-phase granules in the intermediate alloy powder and their distribution characteristics (diffuse mosaic structure or core-shell structure) in the intermediate alloy powder. Furthermore, by removing the second-phase substrate in different intermediate alloy powders, it is possible to realize the production of nano-scale, submicron-scale, micron-scale, and even mini-scale spherical high-purity powder materials.

[0136] Second, through ingenious alloy design, phase separation occurs during the solidification of the initial alloy melt, allowing endogenous granules of a specific particle size to be formed during the solidification process of the initial alloy melt, which can then be separated by subsequent processes. Generally, nanometal powders can be produced relatively easily using bottom-up chemical methods such as chemical reduction. However, production becomes difficult when the granule size reaches the hundreds of nanometers or micron level. Top-down physical methods, such as atomization and ball milling, can relatively easily produce metal granules of tens to hundreds of microns in size. However, producing granules of hundreds of nanometers to a few microns becomes difficult. The technical solution of the present invention, by utilizing the difference in cooling rate during the solidification process of the intermediate alloy powder and combining it with the milling mechanism of the atomization method itself, greatly facilitates the production of target powder materials at the nanoscale, submicron, micron, and millimeter levels. This overcomes the above technical difficulties and is extremely advantageous.

[0137] Third, it can obtain high-purity target powder materials from low-purity raw materials, providing a new method for producing high-purity powder materials from low-purity raw materials, which is a creative method with greatly reduced costs.

[0138] The increased purity of the target powder material of this invention is primarily achieved through the following mechanisms: 1) The main elements of the substrate (e.g., rare earth elements, RE) with high activity and low melting point absorb impurities in the initial alloy melt. The main elements are generally high activity and low melting point elements, and have a very strong affinity with the impurity T during the alloy melting and solidification process. As a result, the impurity T in the initial alloy melt enters the second phase matrix, which is primarily composed of the main elements of the substrate phase, or forms a molten slag with the main elements in the molten state, which is then separated and removed from the alloy melt. 2) During the nucleation growth process of the target powder material (the first phase granules precipitated within), the impurity element T is expelled into the remaining melt. During the solidification process of the intermediate alloy powder, the precipitated first phase granules precipitate slower than the second phase matrix, and the impurity is concentrated in the final solidified melt. That is, the solidified second phase matrix is ​​composed primarily of the main elements of the substrate phase. 3) Due to the presence of the second-phase substrate, crucible-related impurities that enter the melt through interaction between the crucible and the melt during the melting process generally collect in the second-phase substrate. This further reduces the crucible requirements during the melting process and significantly reduces production costs. 4) Because the first-phase granules are surrounded by the second-phase substrate, impurities from the gas introduced from the atmosphere during the atomization solidification process are absorbed and prevented from entering the first-phase granules, further protecting the first-phase granules. Therefore, by skillfully designing and introducing the second-phase substrate, even when using non-high-purity raw materials and a standard crucible during the production of intermediate alloy powder, other impurities that enter the melt during the melting and atomization processes can be prevented, resulting in first-phase granules with low impurity content. The production costs of the target high-purity powder material can also be significantly reduced. For example, a high-purity target metal material (such as high-purity Ti) can be produced using a low-purity raw material (such as sponge Ti).

[0139] Fourth, the intermediate alloy powder is composed of first-phase granules coated with a second-phase substrate. According to alloy solidification and precipitation theory, the first-phase granules in the atomized droplets tend to precipitate from the melt during atomization and solidification of the intermediate alloy powder in spherical, near-spherical, or branched crystal shapes. Because they are coated with the second-phase substrate, the first-phase granules have a smoother surface than the intermediate alloy powder. In particular, when the b value in the initial alloy Aa(MxDy)bTd, AaMbTd, or AaMbAlcTd is lower, the first-phase granules are uniformly dispersed on the second-phase substrate. In this case, even if the intermediate alloy powder produced has a highly irregular shape and poor surface smoothness, the precipitation of smaller, highly spherical, and smooth first-phase granules within it is not affected. The substrate phase can be removed to obtain the desired powder material with high surface quality.

[0140] Fifth, the two-phase powder material composed of the above-mentioned endogenous powder and coating uses a uniquely formed substrate phase coating in situ to encase the endogenous powder, maintaining its high purity and activity. Specifically, metal or alloy powders produced using conventional chemical or physical methods, especially nanopowder with an extremely large specific surface area, are prone to spontaneous oxidation, making powder storage difficult. To address this issue, the technical proposal of the present invention produces a two-phase powder material composed of endogenous powder and coating (substrate phase). Instead of rushing to remove the coating, the coating is used to protect the endogenous metal powder from spontaneous oxidation. This two-phase powder material composed of endogenous powder and coating can be directly used as a feedstock for downstream production, potentially becoming a specialized product. When using high-purity powder for sawing during downstream production, the endogenous metal powder is "released" from the two-phase powder material under appropriate conditions and conditions, depending on the characteristics of the subsequent process, and the endogenous powder is then introduced into the next production process as quickly as possible. This significantly reduces the chance of the endogenous powder being contaminated by impurities such as oxygen. For example, when the endogenous powder is a nanopowder, the endogenous powder can be compounded with a resin at the same time as or immediately after being released from the coating, to produce a resin-based composite material containing highly active endogenous powder.

[0141] Sixth, when M in the initial alloy melt Aa(MxDy)bTd, AaMbTd, or AaMbAlcTd is a combination of elements that meet the requirements, the first phase granules in the intermediate alloy powder also consist of multiple elements, which makes it easier to prepare the target alloy powder material consisting of first phase granules, greatly expanding the composition range and application fields of the target alloy powder material.

[0142] Therefore, the manufacturing method of this invention combines "atomization milling + phase removal method", which has the characteristics of simple process, easy operation, and low cost, and can produce a variety of high-purity powder materials from nanoscale to submicron, micron, and millimeter scale, which can be applied in fields such as catalyst materials, powder metallurgy, composite materials, wave-absorbing materials, sterilization materials, metal injection molding, 3D printing additive manufacturing, and coatings.

[0143] Furthermore, when the target powder is mainly non-metallic elements, the present invention relates to a method for producing a high-purity powder material, characterized by comprising the following steps:

[0144] Step 1: Select the initial alloy raw materials and melt them according to the proportions of the initial alloy raw material components to obtain a uniform initial alloy melt; Step 2: Use atomization milling technology to atomize and solidify the initial alloy melt to obtain an intermediate alloy powder; The intermediate alloy powder consists of a first phase and a second phase, where the first phase is granular and the second phase is a substrate phase with a lower melting point than the first phase, and the first phase granules are coated on the second phase substrate. During the atomization milling process, impurity elements in the initial alloy melt and impurity elements introduced during the atomization solidification process are collected in the second phase substrate, thereby purifying the first phase granules; Step 3: Remove the second phase substrate in the intermediate alloy powder, leaving the first phase granules, and the impurity elements in the second phase substrate are also removed, resulting in a high-purity target metal powder material composed of first phase granules.

[0145] Here, the impurity element in the initial alloy melt is T, and T includes at least one of O, H, N, P, S, F, Cl, I, and Br.

[0146] The average composition of the initial alloy melt is mainly A a Mb T d Yes. A contains at least one of Zn, Sn, Pb, Ga, In, Al, Ge, and Cu. M contains at least one of Be, Si, Ge, and B. The atomic percentage content of Be, Si, Ge, and B in M is 50% or more (including 50%). Among them, a, b, and d represent the atomic percentage content of the corresponding compositional elements. Also, 0.5% ≤ a ≤ 99.5%, 0.5% ≤ b ≤ 99.5%, and 0 ≤ d ≤ 10%.

[0147] As an optimal solution, M contains at least one of Be, Si, Ge, and B. The atomic percentage content of Be, Si, Ge, and B in M is 70% or more (including 70%).

[0148] As an optimal solution, 0.5% ≤ a ≤ 99.4%, 0.5% ≤ b ≤ 99.4%, and 0 < d ≤ 10%. As an optimal solution, 1% ≤ a ≤ 99%, 1% ≤ b ≤ 99%, and 0 ≤ d ≤ 10%. As an optimal solution, 1% ≤ a ≤ 98.9%, 1% ≤ b ≤ 98.9%, and 0 < d ≤ 10%. Further, as an optimal solution, 2% ≤ a ≤ 98%, 2% ≤ b ≤ 98%, and 0 ≤ d ≤ 10%. Further, as an optimal solution, 2% ≤ a ≤ 97.9%, 2% ≤ b ≤ 97.9%, and 0 < d ≤ 10%.

[0149] Furthermore, the average composition of the initial alloy melt is mainly A a M b T d Yes. When M contains at least one of Be, Si, and Ge, A contains at least one of Zn, Sn, Ga, In, and Al. When M contains B, A contains at least one of Sn, Ge, Cu, and Zn.

[0150] The master alloy powder contains the first-phase particles of the main component M x1 T z1 and the second-phase matrix of the main component A x2 T z2 Among them, 98% ≤ x1 ≤ 100%, 0 ≤ z1 ≤ 2%; 70% ≤ x2 ≤ 100%, 0 ≤ z2 ≤ 30%; z1 ≤ d ≤ z2, and 2z1 ≤ z2. x1, z1, x2, and z2 represent the atomic percentage content of the corresponding compositional elements.

[0151] The optimal solution is 98%≦x1<100%, 0 <z1≦2%;70%≦x2<100%, 0<z2≦30%;z1<d<z2,2z1<z2。 The optimal solution is 98.5%≦x1≦100%, 0≦z1≦1.5%; 70%≦x2≦100%, 0≦z2≦30%. The optimal solution is 98.5%≦x1<100%, 0 <z1≦1.5%;70%≦x2<100%, 0<z2≦30%。 The optimal solution is 99%≦x1≦100%, 0≦z1≦1%; 70%≦x2≦100%, 0≦z2≦30%. The optimal solution is 99%≦x1<100%, 0 <z1≦1%;70%≦x2<100%, 0<z2≦30%。

[0152] Furthermore, the main ingredient M x1 T z1 The first phase granules of do not contain A.

[0153] Furthermore, the main component of the first phase granules is M x1 T z1 is.

[0154] Furthermore, during the atomization milling process, impurity elements in the initial alloy melt are collected in the second phase matrix, thereby purifying the first phase granules.

[0155] Further, the atomization milling techniques include at least one of gas atomization, water atomization, steam-associated atomization, vacuum atomization, plasma atomization, centrifugal atomization, spinning disk atomization, and rotating electrode atomization.

[0156] Furthermore, the granule shape of the intermediate alloy powder may be spherical, near-spherical, water droplet-shaped, dumbbell-shaped, or irregular rod-shaped.

[0157] By adjusting the atomization parameters, droplets of different sizes can be obtained as the initial alloy melt passes through the atomization process, and intermediate alloy powders of different sizes can be solidified. If the energy of the atomization medium is sufficiently high, intermediate alloy powders with small particle sizes can be obtained, and the solidification rate of the intermediate alloy powders is generally higher. If the energy of the atomization medium is low, intermediate alloy powders with larger particle sizes can be obtained, and the solidification rate of the intermediate alloy powders is generally lower.

[0158] Furthermore, the particle size range of the intermediate alloy powder is 1 μm to 8 mm. Furthermore, the particle size range of the intermediate alloy powder is 1 μm to 4 mm. Furthermore, the particle size range of the intermediate alloy powder is 1 μm to 1 mm. Furthermore, the particle size range of the intermediate alloy powder is 1 μm to 250 μm. Furthermore, the particle size range of the intermediate alloy powder is 1 μm to 100 μm. Furthermore, the particle size range of the intermediate alloy powder is 1 μm to 50 μm. Furthermore, the particle size range of the intermediate alloy powder is 1 μm to 20 μm.

[0159] Furthermore, the particle size of the first phase granules in the intermediate alloy powder correlates with the atomized solidification rate of the initial alloy melt. Generally, the particle size of the first phase granules in the intermediate alloy powder is negatively correlated with the atomized solidification rate of the initial alloy melt. That is, the higher the atomized solidification rate of the initial alloy melt, the smaller the particle size of the first phase granules in the intermediate alloy powder.

[0160] Furthermore, the atomization solidification rate of the initial alloy melt is 10 3 K / s~10 6 When the temperature is K / s, the initial alloy powder mainly has a particle size of micron order.

[0161] Furthermore, the atomization solidification rate of the initial alloy melt is 50K / s to 10 3 At K / s, the initial alloy powder can be obtained with a particle size of several hundred microns or millimeters.

[0162] Furthermore, the volume fraction of the first phase granules in the intermediate alloy powder is determined by the contents of A and M in the intermediate powder. The atomic percentage content of M in the intermediate alloy powder is generally 0.5%≦b≦99.5% or 0.5%≦b≦99.4%, and the volume fraction of the first phase granules mainly composed of M is also approximately equal to this ratio, and the specific value can be calculated from the atomic weight and density of each element.

[0163] Furthermore, the volume percentage content of the first phase in the intermediate alloy powder ranges from 0.5% to 99.5%.

[0164] Furthermore, the specific value of the volume fraction of the first phase granules in the intermediate alloy powder can be determined by the average composition of the intermediate alloy powder, the composition of the first and second phases, and the atomic weight and density of each element, and can also be calculated by these parameters.

[0165] Furthermore, the first phase granules are coated with a second phase substrate: a mosaic structure in which multiple first phase granules are dispersed in the second phase substrate, or a core-shell structure in which a single first phase granule is surrounded by a second phase substrate.

[0166] Furthermore, the particle size range of the first phase granules in the intermediate alloy powder is 3nm to 7.9mm. Furthermore, the particle size range of the first phase granules in the intermediate alloy powder is 3nm to 3.9mm. Furthermore, the particle size range of the first phase granules in the intermediate alloy powder is 3nm to 0.95mm. Furthermore, the particle size range of the first phase granules in the intermediate alloy powder is 3nm to 245μm. Furthermore, the particle size range of the first phase granules in the intermediate alloy powder is 3nm to 96μm. Furthermore, the particle size range of the first phase granules in the intermediate alloy powder is 3nm to 47μm. Furthermore, the particle size range of the first phase granules in the intermediate alloy powder is 3nm to 18.5μm.

[0167] Furthermore, the method for removing the second phase substrate in the intermediate alloy powder includes at least one of acid reaction removal, alkali reaction removal, and vacuum volatilization removal.

[0168] The composition and concentration of the acid solution and alkaline solution are not specifically limited as long as they remove the base phase while leaving the first granular phase.

[0169] The temperature and vacuum level of the vacuum treatment are not specifically limited, as long as the first phase granular phase remains while removing the substrate phase.

[0170] As the optimal solution, the main component M x1 T z1 The high purity target powder material does not contain A.

[0171] The optimal solution is to use high purity powder material with the following components: x1 T z1 is.

[0172] Furthermore, the particle size range of the high-purity target powder material is 3nm - 7.9mm. Furthermore, the particle size range of the high-purity target powder material is 3nm - 3.9mm. Furthermore, the particle size range of the high-purity target powder material is 3nm - 0.95mm. Furthermore, the particle size range of the high-purity target powder material is 3nm - 245μm. Furthermore, the particle size range of the high-purity target powder material is 3nm - 96μm. Furthermore, the particle size range of the high-purity target powder material is 3nm - 47μm. Furthermore, the particle size range of the high-purity target powder material is 3nm - 18.5μm.

[0173] Furthermore, the shape of the high purity target powder includes spherical, near-spherical, branched, rod-shaped, and plate-shaped.

[0174] Alternatively, the present invention provides a method for producing high purity metal powder material, which has the following characteristics:

[0175] Step 1: The initial alloy raw materials are selected and melted according to the proportions of the initial alloy raw material components to obtain a uniform initial alloy melt. Step 2: The initial alloy melt is atomized and solidified using atomization milling technology to obtain an intermediate alloy powder. The intermediate alloy powder consists of a first phase and a second phase, where the first phase is granular and the second phase is a substrate phase with a lower melting point than the first phase, and the first phase granules are coated on the second phase substrate. During the atomization milling process, impurity elements in the initial alloy melt and those introduced during the atomization solidification process are collected in the second phase substrate, thereby purifying the first phase granules. Step 3: The second phase substrate in the intermediate alloy powder is removed, leaving the first phase granules. The impurity elements in the second phase substrate are also removed, resulting in a high-purity target metal powder material composed of first phase granules.

[0176] The "atomization milling + phase removal method" described above can produce ultra-fine metal powders with low impurity content. To obtain fine powders, atomization technology can be used to initially refine the powder through the production of intermediate alloy powders. At the same time, first-phase granules are formed within the intermediate alloy powder, resulting in a number of finer first-phase granules, including nanometer-sized first-phase granules. The second-phase substrate can then be removed to obtain the target ultra-fine metal powder, dramatically reducing the production costs of ultra-fine metal powder materials. Impurity control is achieved by introducing the second-phase substrate, which allows impurity elements generated during the alloy melting and atomization milling processes to be collected on the second-phase substrate, purifying and protecting the first-phase granules, further reducing the production costs of high-purity target metal powders.

[0177] In step 1, The raw materials for the initial alloy can be either single metals or intermediate alloys, and are selected according to the composition ratio of the initial alloy components. The raw materials for the initial alloy ensure that the melt is completely homogeneous during the melting process, ensuring smooth operation of the subsequent atomization milling.

[0178] In step 2, The initial alloy composition ratio is A a M bWhen, A contains at least one of Mg, Ca, Li, Na, K, Zn, In, Sn, Pb, Ga, Cu, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu. M contains at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti, Fe, Co, Ni, Mn, Cu, Ag, Si, Ge, B, Be, C. Among them, a and b represent the atomic percentage contents of the corresponding constituent elements. 0.5% ≤ b ≤ 98%, a + b = 100%. Also A a M b When the alloy melt is atomized and solidified, it does not form an intermetallic compound of A and M, but forms a first-phase particle of the M component and a second-phase matrix of the A component. As an optimal solution, A contains at least one of Mg, Ca, Li, Na, K, Zn, Pb, Sn, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu. M contains at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti, Fe, Co, Ni, Mn, Cu, Ag, Si, Ge. As an optimal solution, 40% < b ≤ 98%. As an optimal solution, 45% < b ≤ 98%.

[0179] The component mixing ratio of the initial alloy is A a M b Al c When, A contains at least one of Mg, Ca, Li, Na, K, Zn, In, Sn, Pb, Ga, Cu, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu. Al is aluminum. M contains at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti, Fe, Co, Ni, Mn, Cu, Ag, Si, Ge, B, Be, C. Among them, a, b, and c respectively represent the atomic percentage contents of the corresponding constituent elements. 0.5% ≤ b ≤ 98%, 0.1% ≤ c ≤ 30%, a + b + c = 100%. Also A a M b Al c When the alloy melt is atomized and solidified, it does not form an intermetallic compound of A and M, M x1 Al y1 The first-phase particle of the component and A x2 Al y2It forms a second-phase matrix of components. Among them, x1, y1, x2, and y2 represent the atomic percentage contents of the corresponding compositional elements. Also, 0.1% ≤ y1 ≤ 25%, 0.1% ≤ y2 ≤ 35%, x1 + y1 = 100%, and x2 + y2 = 100%. As an optimal solution, A includes at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu. M includes at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti, Fe, Co, Ni. As an optimal solution, 35% < b ≤ 98%. Further as an optimal solution, 40% < b ≤ 98%.

[0180] Furthermore, the atomization powder manufacturing technology includes at least one of gas atomization, water atomization, steam - combined atomization, vacuum atomization, plasma atomization, centrifugal atomization, rotating disk atomization, rotating electrode atomization, and ultrasonic atomization.

[0181] Furthermore, the size range of the intermediate alloy powder particles is 1 μm to 8 mm. The particle shapes of the intermediate alloy powder include spherical, near-spherical, water-drop shape, dumbbell shape, irregular rod shape, etc.

[0182] Furthermore, the volume fraction range of the first-phase particles of the intermediate alloy powder is 0.5% to 98%.

[0183] Furthermore, the method by which the first-phase particles are coated in the second-phase matrix is a core-shell structure outside the second-phase matrix within a single first-phase particle, or a mosaic structure in which a plurality of first-phase particles are dispersed and distributed in the second-phase matrix.

[0184] Furthermore, the impurity elements in the initial alloy melt and the impurity elements introduced during atomization solidification include at least one of H, O, N, S, P, F, Cl, I, Br. Among them, the impurity elements in the initial alloy melt are introduced from the initial alloy raw materials, or the crucible or atmosphere that comes into contact with the melt during the alloy melting process. The impurities introduced during the atomization solidification process are mainly introduced by the atomization atmosphere and the atomization medium.

[0185] In step 3, The method for removing the second-phase matrix in the intermediate alloy powder includes at least one of acid reaction removal, alkali reaction removal, and vacuum volatilization removal.

[0186] Furthermore, the method for removing the second phase substrate in the intermediate alloy powder includes natural oxidation-pulverization peeling removal of the second phase substrate.

[0187] Furthermore, the particle size range of the high-purity target metal powder material consisting of first phase granules is 3nm~300μm, and the shapes of the high-purity target metal powder include spherical, near-spherical, branched, rod-shaped and plate-shaped.

[0188] Additionally, the target metal powder material is sorted according to different particle sizes to obtain a narrower particle size range of the target metal powder material.

[0189] Furthermore, the total content of H, O, N, S, P, F, Cl, I, and Br in the high-purity target metal powder material is 2000 ppm or less.

[0190] The technical features of the above alternative invention will be further explained in detail as follows:

[0191] First, in step 2 of the present invention, fine first-phase granules are obtained by two mechanisms. The first is based on the basic principle of atomization milling, in which the alloy melt is broken into fine droplets through the impact of a fast-moving fluid (atomization medium), which then solidifies into an intermediate alloy powder of a certain particle size. The second is to obtain even finer first-phase granules by utilizing the precipitation of the first-phase granules into the second-phase substrate during the atomization droplet solidification process. Therefore, the present invention further utilizes the atomization principle in which the atomization medium impacts the melt, causing the first-phase granules to precipitate into the second-phase substrate, thereby resolving the current technical difficulty of obtaining fine powder material through the impact of the atomization medium and significantly reducing the production cost of fine metal powder material. Specifically, for initial alloy A, a M b Or A a M b Al c When the b content in the atomized droplets is low, such as 0.5%≦b≦50%, the components in the solidification process of the atomized droplets are mainly A or A x2 Al y2The content of the second phase matrix is ​​also high. The solidification process of the atomized droplets generally corresponds to a high cooling rate of the melt, so when the content of the second phase is high, the first phase granules are easily precipitated in the form of mass diffusion and embedded in the second phase matrix. For example, when the cooling rate of the atomized droplets is 10 3 When the cooling rate of the atomized droplets is faster than 10 K / s and the particle size range of the intermediate alloy powder is 1 μm to 100 μm, the first phase granules cannot grow sufficiently, and mainly form nanoscale (e.g., 3 nm to 100 nm) or submicron-scale (e.g., 100 nm to 1 μm) first phase granules. 3 When the K / s is lower and the particle size range of the intermediate alloy powder is 100 μm to 8 mm, the first phase granules can grow relatively well, mainly forming submicron-level (e.g., 100 nm to 1 μm) or micron-level first phase granules. a M b Or A a M b Al c When the b content in the atomized droplets is high, such as 70%≦b≦98%, the atomized droplets solidify mainly due to M or M x1 Al y1 The content of first-phase granules is high. The large amount of first-phase granules precipitated during the solidification process inevitably bridges, merges, and grows. In this case, the first-phase granules in the intermediate alloy powder are likely to be coated by the second-phase substrate in single or multiple particles after precipitation, regardless of the cooling rate. In particular, when the b value is extremely high, such as 90%≦b≦98%, the first-phase granules are overwhelmingly dominant in the intermediate alloy powder. The first-phase granules can exist alone in the intermediate alloy powder, forming a core-shell structure with the second-phase substrate that coats this granule. Current atomization milling technology can produce intermediate alloy powders with particle sizes ranging from 1 μm to 300 μm. Therefore, when the b value is extremely high, the present invention can also use atomization milling technology to produce intermediate alloy powders with a corresponding particle size. The first-phase granules are slightly smaller than those in the intermediate alloy powder. Therefore, the present invention can control the size of the first-phase granules in the intermediate alloy powder and their distribution characteristics (mosaic or core-shell structure) by controlling the operating (impact) parameters of the atomization medium, the cooling rate of the atomized droplets, and the b value of the initial alloy composition. Furthermore, by removing the second-phase substrate from different intermediate alloy powders, nanoscale, submicron, and micron-scale metal powders can be produced, respectively.

[0192] Next, in the above-mentioned intermediate alloy powder, the second phase substrate coats the first phase granules. According to the alloy solidification and precipitation theory, during atomization and solidification of the intermediate alloy powder, the first phase granules in the atomized droplets tend to precipitate in a spherical, near-spherical or branched shape from the substrate that has not yet completely solidified. Because they coat the second phase substrate, the first phase granules have a smoother surface than the intermediate alloy powder. In particular, in the case of the initial alloy A a M b Or A a M b Al c When the b content is low, such as 0.5%≦b≦50%, a large amount of first-phase granules are dispersed throughout the second-phase matrix, and even if the intermediate alloy powder produced has a highly irregular shape and poor surface smoothness, this does not affect the high sphericity and surface smoothness of the precipitated first-phase granules.

[0193] Third, the second-phase substrate in the intermediate alloy powder is generally composed of elements with low melting points and high activity. Therefore, during the atomization solidification process, impurity elements from the melt easily bond with the second-phase substrate, thereby concentrating on the second-phase substrate and serving to purify and protect the first-phase granules. At the same time, the presence of the second-phase substrate also allows crucible-related impurities that enter the melt through the interaction between the crucible and the melt during the melting process to generally concentrating on the second-phase substrate, further reducing the crucible requirements during the melting process and significantly lowering production costs. In addition, because the first-phase granules are surrounded by the second-phase substrate, impurity elements from the gas introduced by the atmosphere during the atomization solidification process are absorbed by the substrate and are less likely to enter the first-phase granules, further providing protection for the first-phase granules. Therefore, due to the protective effect of the second phase substrate, even if non-high purity raw materials and ordinary crucibles are used in the production process of intermediate alloy powder, or even if other impurity elements are introduced into the melt during the melting and atomization processes, first phase granules with low impurity content can be obtained, which can significantly reduce the production costs of the target high purity metal powder material.

[0194] Fourth, initial alloy A a M b Or A a M b Al cWhen M is a combination of multiple elements, the first phase granules in the intermediate alloy powder also consist of multiple elements, which makes it easier to produce the target alloy powder material from the first phase granules, greatly expanding the range of components and application fields of the target alloy powder material.

[0195] Finally, in step 3 of the present invention, since the second-phase substrate in the intermediate alloy powder has a low melting point and high activity, the method for removing the second-phase substrate and retaining the first-phase granules can be at least one of the following three methods: 1) removing the second-phase substrate by etching with an acid or alkaline solution while retaining the first-phase granules; 2) volatilizing the second-phase substrate by vacuum evaporation while retaining the first-phase granules; 3) for second-phase substrates that are highly oxidizable, such as those of rare earth elements, natural oxidation and pulverization of the substrate element can also be used to turn the second-phase substrate into powdered oxide powder, and then separating the first-phase granules and the substrate powder to obtain the target metal powder material.

[0196] Therefore, the present invention adopts the combination of "atomization milling + phase removal method", which has the characteristics of simple process, easy operation, and low cost, and can produce a variety of high-purity metal powder materials including nanoscale, submicron, and micron scale. It has excellent applications in the fields of catalysis, powder metallurgy, composite materials, sterilization, metal injection molding, 3D printing, and other additive manufacturing. Best Mode of the Invention

[0197] The following specific working example will be used to illustrate the method for producing high purity powder materials. Example 1

[0198] This embodiment provides a method for producing nano-CrV powder, which includes the following steps: Atomic ratio composition is Zn 58 (Cr 50 V 50 ) 42The alloy is selected, raw materials are taken according to the composition, and the initial alloy raw materials are uniformly melted. After that, the alloy melt is atomized and solidified by air atomization milling technology to obtain a near-spherical intermediate alloy powder with a particle size range of 3 μm to 150 μm. The solidification structure of this intermediate alloy powder is a second phase matrix of the component Zn and a large component Cr dispersed on the matrix Zn. 50 V 50 It consists of first phase high melting point granules, among which Cr 50 V 50 The granules are nearly spherical and the particle size ranges from 3nm to 300nm. 50 V 50 The volume content of the granules is about 38%. During the solidification process, impurities are collected in the matrix Zn. Vacuum heat treatment is used to volatilize and remove Zn from the intermediate alloy powder, while the Cr, which is less likely to volatilize, is removed. 50 V 50 Granules are separated from the intermediate alloy powder. 50 V 50 The resulting powder has a particle size range of 3nm to 300nm. 50 V 50 The total content of H, O, N, S, P, F, Cl, I, and Br in the powder is less than 1500 ppm. Example 2

[0199] This embodiment provides a method for producing nano-CrV powder, which includes the following steps: Atomic ratio composition is Zn 80 (Cr 50 V 50 ) 20 The alloy is selected, raw materials are taken according to the composition, and the initial alloy raw materials are uniformly melted. After that, the alloy melt is atomized and solidified by air atomization milling technology to obtain a near-spherical intermediate alloy powder with a particle size range of 1 μm to 100 μm. The solidification structure of this intermediate alloy powder is a second phase matrix of the component Zn and a large component Cr dispersed on the matrix Zn. 50 V 50 It consists of first phase high melting point granules, among which Cr 50 V 50 The granules are nearly spherical and the particle size ranges from 3nm to 300nm. 50 V 50The volume content of the granules is about 17.5%. During the solidification process, impurities are collected in the matrix Zn. The Zn in the intermediate alloy powder was removed by sodium hydroxide solution, and the Cr in the intermediate alloy powder, which does not react with alkali, was removed. 50 V 50 Granules are released, i.e., nano-Cr 50 V 50 The resulting powder has a particle size range of 3nm to 200nm. 50 V 50 The total content of H, O, N, S, P, F, Cl, I, and Br in the powder is less than 1600 ppm. Example 3

[0200] This example provides a method for producing submicron and micron-grade Nb powder, which includes the following steps: The atomic ratio is Cu 54 Nb 46 The alloy is selected and raw materials are taken according to the composition. The initial alloy raw materials are then uniformly melted, and the molten alloy is then atomized and solidified using air atomization milling technology to obtain near-spherical intermediate alloy powder with a particle size range of 5μm to 500μm. The solidification structure of this intermediate alloy powder consists of a second-phase substrate of the component Cu and first-phase high-melting-point granules of the major component Nb scattered on the Cu substrate, among which the Nb granules are near-spherical in shape and have a particle size range of 50nm to 5μm. The volume content of the Nb granules in the intermediate alloy powder is approximately 46%. During the solidification process, impurities gather in the Cu substrate. The Cu in the intermediate alloy powder is volatilized and removed by the hydrochloric acid solution, and the Nb granules in the intermediate alloy powder, which do not easily react with the hydrochloric acid solution, are removed. In other words, Nb powder is obtained. The particle size range is 50nm~5μm. The total content of H, O, N, S, P, F, Cl, I, and Br in the Nb powder is 1400ppm or less. Example 4

[0201] This embodiment provides a method for producing micron-grade FeNi powder, which includes the following steps: Atomic ratio composition is Li 10 (Fe 50 Ni 50 )90 The alloy is selected, raw materials are taken according to the composition, and the initial alloy raw materials are uniformly melted. After that, the alloy melt is atomized and solidified using vacuum milling technology to obtain a near-spherical intermediate alloy powder with a particle size range of 3 μm to 120 μm. The solidification structure of this intermediate alloy powder is a second phase substrate shell of component Li and a second phase shell of component Fe. 50 Ni 50 The first phase consists of high melting point granules, among which Fe 50 Ni 50 The granules are nearly spherical, with a particle size ranging from 2 μm to 110 μm. The volume content of the FeNi granules in the intermediate alloy powder is approximately 82%. During the solidification process, impurities are collected in the Li shell. Fe 50 Ni 50 The magnetic properties of the granules and the natural oxidation-pulverization process of Li in air 50 Ni 50 The granules are separated from the powdered oxide of lithium, i.e., micron Fe 50 Ni 50 Granules are obtained, the particle size of which ranges from 2 μm to 110 μm. 50 Ni 50 The total content of H, O, N, S, P, F, Cl, I, and Br in the powder is less than 1800 ppm. Example 5

[0202] This embodiment provides a method for producing a micron-grade Fe-Cr-V-Ti-Mo powder, which includes the following steps: Atomic ratio composition is La 10 (Fe 20 Cr 20 V 20 Ti 20 Mo 20 ) 90 The alloy is selected, raw materials are taken according to the composition, and the initial alloy raw materials are uniformly melted. After that, the alloy melt is atomized and solidified using water atomization milling technology to obtain a near-spherical intermediate alloy powder with a particle size range of 3 μm to 150 μm. The solidification structure of this intermediate alloy powder is a second phase substrate shell of the component La and a second phase shell of the component Fe. 20 Cr 20 V 20 Ti 20 Mo 20It consists of first phase high melting point granules of Fe e 20 Cr 20 V 20 Ti 20 Mo 20 The granules are nearly spherical and the particle size ranges from 2 μm to 144 μm. 20 Cr 20 V 20 Ti 20 Mo 20 The volume content of the granules is about 78%. During the solidification process, impurities are collected in the La shell. The La substrate in the intermediate alloy powder is reacted with the dilute hydrochloric acid solution and removed, and the Fe substrate in the intermediate alloy powder, which does not easily react with the dilute hydrochloric acid solution, is removed. 20 Cr 20 V 20 Ti 20 Mo 20 The granules are released, i.e., micron Fe 20 Cr 20 V 20 Ti 20 Mo 20 Granules are obtained, the particle size range of which is 2μm~144μm. 20 Cr 20 V 20 Ti 20 Mo 20 The total content of H, O, N, S, P, F, Cl, I, and Br in the powder is less than 1800 ppm. Example 6

[0203] This embodiment provides a method for producing micron-grade Ti powder, which includes the following steps: Atomic ratio composition is Ce 25 Ti 75The alloy is selected and raw materials are taken according to the composition. The initial alloy raw materials are then uniformly melted, and the molten alloy is then atomized and solidified using air atomization milling technology to obtain a near-spherical intermediate alloy powder with a particle size range of 5μm to 100μm. The solidification structure of this intermediate alloy powder consists of a second-phase matrix of the component Ce and a number of first-phase high-melting-point dispersed granules of the component Ti, among which the Ti granules are near-spherical or branched, with a particle size range of 2μm to 50μm. The volume content of the Ti granules in the intermediate alloy powder is approximately 61%. Impurities from the titanium raw materials and the melting process and the atomization atmosphere are collected in the matrix Ce. The Ce substrate in the intermediate alloy powder is removed by dilute hydrochloric acid solution, and the Ti granules in the intermediate alloy powder, which are less reactive with the dilute hydrochloric acid solution, are released. This means that finer micron Ti powder is obtained than the intermediate alloy powder. The particle size range is 2μm~50μm. Micron Fe 20 Cr 20 V 20 Ti 20 Mo 20 The total content of H, O, N, S, P, F, Cl, I, and Br in the powder is less than 1500 ppm. Example 7

[0204] This embodiment provides a method for producing a micron-grade Ti-Zr-Hf-Nb-Ta high entropy powder, which includes the following steps: Atomic ratio composition is Ce 10 (Ti 20 Zr 20 Hf 20 Nb 20 Ta 20 ) 90 The alloy is selected, raw materials are taken according to the composition, and the initial alloy raw materials are uniformly melted. After that, the alloy melt is atomized and solidified using water atomization milling technology to obtain a near-spherical intermediate alloy powder with a particle size range of 3 μm to 150 μm. The solidification structure of this intermediate alloy powder is a second phase shell of the component Ce and a second phase shell of the component Ti. 20 Zr 20 Hf 20 Nb 20 Ta 20 The first phase consists of high melting point inner core granules, among which Ti 20 Zr 20 Hf 20 Nb 20Ta 20 The granules are nearly spherical and the particle size ranges from 2 μm to 142 μm. 20 Zr 20 Hf 20 Nb 20 Ta 20 The volume content of the granules is about 84%. During the solidification process, impurities are collected in the matrix Ce shell. The Ce substrate in the intermediate alloy powder was removed using a dilute hydrochloric acid solution, and the Ti substrate in the intermediate alloy powder, which does not easily react with the dilute hydrochloric acid solution, was removed. 20 Zr 20 Hf 20 Nb 20 Ta 20 Detach the granules, i.e., micron Ti 20 Zr 20 Hf 20 Nb 20 Ta 20 The powder obtained has a particle size range of 2μm to 142μm. 20 Cr 20 V 20 Ti 20 Mo 20 The total content of H, O, N, S, P, F, Cl, I, and Br in the powder is less than 1500 ppm. Example 8

[0205] This embodiment provides a method for producing a micron-grade TiNi powder, which includes the following steps: Atomic ratio composition is Gd 25 (Ti 50 Ni 50 ) 75 The alloy is selected, raw materials are taken according to the composition, and the initial alloy raw materials are uniformly melted. After that, the alloy melt is atomized and solidified by air atomization milling technology to obtain a near-spherical intermediate alloy powder with a particle size range of 5 μm to 100 μm. The solidification structure of this intermediate alloy powder is a second phase matrix of the component Gd and a plurality of components Ti. 50 Ni 50 The first phase consists of high melting point dispersed granules of Ti 50 Ni 50 The granules are nearly spherical or branched, with particle sizes ranging from 2 μm to 50 μm. 50 Ni 50The volume content of the granules is about 56%. Impurities during the solidification process are collected in the matrix Gd. The Gd substrate in the intermediate alloy powder was removed using a dilute hydrochloric acid solution, and the Ti substrate in the intermediate alloy powder, which does not easily react with the dilute hydrochloric acid solution, was removed. 50 Ni 50 The granules are removed, i.e., the micron Ti particles are finer than those of the intermediate alloy powder. 50 Ni 50 The powder obtained is composed of Ti 50 Ni 50 The particle size ranges from 2 μm to 50 μm. 50 Ni 50 The total content of H, O, N, S, P, F, Cl, I, and Br in the powder is less than 1400 ppm. Example 9

[0206] This embodiment provides a method for producing a micron-grade Fe-Cr-Ti powder, which includes the following steps: The atomic ratio of the mixture is La2(Fe 79 Cr 20 Ti1) 98 The alloy is selected, raw materials are taken according to the composition, and the initial alloy raw materials are uniformly melted. After that, the alloy melt is atomized and solidified using water atomization milling technology to obtain a near-spherical intermediate alloy powder with a particle size range of 3 μm to 150 μm. The solidification structure of this intermediate alloy powder is a second phase matrix of the component La and a plurality of components Fe. 79 Cr 20 It consists of first phase high melting point granules of Ti1, among which TFe 79 Cr 20 The Ti1 granules are nearly spherical in shape, with particle sizes ranging from 2.9 μm to 147 μm. 79 Cr 20 The volume content of Ti1 granules is about 94%. Impurities during the solidification process are collected in the substrate La. The La substrate in the intermediate alloy powder was removed using a dilute hydrochloric acid solution, and the Fe substrate in the intermediate alloy powder, which does not easily react with the dilute hydrochloric acid solution, was removed. 79 Cr 20 Ti1 granules are released, i.e., micron Fe 79 Cr 20 Ti1 powder is obtained. The particle size range is 2.9μm~47μm.79 Cr 20 The total content of H, O, N, S, P, F, Cl, I, and Br in Ti1 powder is less than 1800 ppm. Example 10

[0207] This embodiment provides a method for producing a micromate Ti-Al-V powder, which includes the following steps: Atomic ratio composition is Ce 30 Al 12 (Ti 96 V4) 58 The alloy is selected, raw materials are taken according to the composition, and the initial alloy raw materials are uniformly melted. Then, the alloy melt is atomized and solidified by air atomization milling technology to obtain near-spherical intermediate alloy powder or branched crystal form with a particle size range of 3 μm to 150 μm. The solidification structure of this intermediate alloy powder is composed of Ce. 85 Al 15 The second phase matrix and multiple components (Ti 96 V4) 90 Al 10 It consists of first phase high melting point dispersed granules, among which (Ti 96 V4) 90 Al 10 The granules are nearly spherical or branched, with particle sizes ranging from 1 μm to 50 μm. 96 V4) 90 Al 10 The volume content of the granules is about 52%. The impurities during the solidification process are the matrix Ce. 85 Al 15 Gather inside. Ce in the intermediate alloy powder was extracted with dilute hydrochloric acid solution. 85 Al 15 The substrate is removed, and the intermediate alloy powder is hard to react with the dilute hydrochloric acid solution (Ti 96 V4) 90 Al 10 The granules are separated, i.e., finer than the intermediate alloy powder (Ti 96 V4) 90 Al 10 The powder obtained has a particle size range of 1 μm to 50 μm. 96 V4) 90 Al 10The total content of H, O, N, S, P, F, Cl, I, and Br in the powder is less than 1400 ppm. Example 11

[0208] This embodiment provides a method for producing a micromate Fe-Cr-Nb-Mo-Ti-V powder, which includes the following steps: Atomic ratio composition is La 25 (Fe 76 Cr 16 Nb2Mo2Ti2V2) 75 The alloy is selected, raw materials are taken according to the composition, and the initial alloy raw materials are uniformly melted. Then, the alloy melt is atomized and solidified by air atomization milling technology to obtain a near-spherical intermediate alloy powder or branched crystal form with a particle size range of 2 μm to 150 μm. The solidification structure of this intermediate alloy powder is a second phase matrix of the component La and a plurality of components Fe. 76 Cr 16 It consists of first phase high melting point dispersed granules of Nb2Mo2Ti2V2, among which Fe 76 Cr 16 The shape of Nb2Mo2Ti2V2 granules is near-spherical or branched, and the particle size ranges from 1μm to 50μm. 76 Cr 16 The volume content of Nb2Mo2Ti2V2 granules is about 50%. Impurities during the solidification process are collected in the matrix La. The La substrate in the intermediate alloy powder was removed using a dilute hydrochloric acid solution, and the high Cr content Fe in the intermediate alloy powder, which is less likely to react with the dilute hydrochloric acid solution, was removed. 76 Cr 16 The Nb2Mo2Ti2V2 granules are removed. That is, the Fe 76 Cr 16 The Nb2Mo2Ti2V2 powder is obtained. The particle size range is 1μm~50μm. 76 Cr 16 The total content of H, O, N, S, P, F, Cl, I, and Br in the Nb2Mo2Ti2V2 powder is less than 1400 ppm. Example 12

[0209] This embodiment provides a method for producing a micro-mate grade Fe-Cr-Mo-Ti powder, which includes the following steps: The atomic ratio of La5(Fe 76 Cr 20 Mo2Ti2) 95 The alloy is selected, raw materials are taken according to the composition, and the initial alloy raw materials are uniformly melted. After that, the alloy melt is atomized and solidified using water atomization milling technology to obtain a near-spherical intermediate alloy powder with a particle size range of 3 μm to 120 μm. The solidification structure of this intermediate alloy powder is a second phase substrate shell of the component La and a second phase shell of the component Fe. 76 Cr 20 It consists of a first phase high melting point granular core of Mo2Ti2, in which Fe 76 Cr 20 The shape of the Mo2Ti2 granules is nearly spherical, and the particle size ranges from 2 μm to 113 μm. 76 Cr 20 The volume content of Mo2Ti2 granules is about 86%. Impurities during the solidification process are collected in the substrate shell La. The La in the intermediate alloy powder is reacted with the dilute hydrochloric acid solution and removed, and the high Cr content Fe in the intermediate alloy powder, which is less likely to react with the dilute hydrochloric acid solution, is removed. 76 Cr 20 The Mo2Ti2 granules are removed. That is, the micrometer Fe is finer than the intermediate alloy powder. 76 Cr 20 Mo2Ti2 powder is obtained, the particle size range of which is 2μm~50μm. 76 Cr 20 The total content of H, O, N, S, P, F, Cl, I, and Br in the Mo2Ti2 powder is less than 1800 ppm. Example 13

[0210] This embodiment provides a method for producing a micrometer Fe-Cr-C powder, which includes the following steps: Atomic ratio composition is La 2.5 (Fe 84.9 Cr 15 C 0.1 ) 97.5The alloy is selected, raw materials are taken according to the composition, and the initial alloy raw materials are uniformly melted. After that, the alloy melt is atomized and solidified using water atomization milling technology to obtain a near-spherical intermediate alloy powder with a particle size range of 3 μm to 150 μm. The solidification structure of this intermediate alloy powder is a second phase shell of the component La and a second phase shell of the component Fe. 84.9 Cr 15 C 0.1 The first phase consists of high melting point granules, among which Fe 84.9 Cr 15 C 0.1 The granules are nearly spherical and the particle size ranges from 2.9 μm to 146 μm. 84.9 Cr 15 C 0.1 The volume content of the granules is about 92%. During the solidification process, impurities are collected in the La shell. Fe 84.9 Cr 15 C 0.1 The magnetic properties of the granules and the natural oxidation-pulverization process of La in air resulted in the formation of Fe 84.9 Cr 15 C 0.1 Granules are separated from the powdered oxides of La, i.e., micrometer Fe 84.9 Cr 15 C 0.1 Granules are obtained, the particle size of which ranges from 2 μm to 50 μm. 84.9 Cr 15 C 0.1 The total content of H, O, N, S, P, F, Cl, I, and Br in the powder is less than 1600 ppm. Example 14

[0211] This embodiment provides a method for producing nanometer-scale Fe powder, which includes the following steps: Atomic ratio composition is La 59 Fe 41The alloy is selected and raw materials are taken according to the composition. The initial alloy raw materials are then uniformly melted, and the molten alloy is then atomized and solidified using water atomization milling technology to obtain near-spherical intermediate alloy powder with a particle size range of 3μm to 150μm. The solidification structure of this intermediate alloy powder consists of a second-phase substrate shell of the component La and first-phase high-melting-point granules of the major component Fe scattered within the La substrate, with the Fe granules being near-spherical in shape and with a particle size range of 3nm to 300nm. The volume content of the Fe granules in the intermediate alloy powder is approximately 18%. During the solidification process, impurities gather in the substrate La shell. By utilizing the magnetic properties of the Fe granules and the natural oxidation-pulverization process of La in air, the Fe granules are separated from the La-pulverized oxides, resulting in nanometer Fe granules with particle sizes ranging from 2 μm to 50 μm. The total content of H, O, N, S, P, F, Cl, I, and Br in the nanometer Fe powder is less than 1900 ppm. Example 15

[0212] This embodiment provides a method for producing submicron-micron grade Fe powder, which includes the following steps: Atomic ratio composition is La 40 Fe 60 The alloy is selected and raw materials are taken according to the composition. The initial alloy raw materials are then uniformly melted, and the molten alloy is then atomized and solidified using water atomization milling technology to obtain near-spherical intermediate alloy powder with a particle size range of 100μm to 8mm. The solidification structure of this intermediate alloy powder consists of a second-phase substrate shell of the component La and first-phase high-melting-point granules of the major component Fe scattered within the La substrate, with the Fe granules having a near-spherical or branched shape and a particle size range of 100nm to 10μm. The volume content of the Fe granules in the intermediate alloy powder is approximately 32%. During the solidification process, impurities gather in the substrate La shell. The magnetic properties of the Fe granules and the natural oxidation-pulverization process of La in air are used to separate the Fe granules from the La-pulverized oxides, resulting in Fe granules with particle sizes ranging from 100nm to 10μm. The total content of H, O, N, S, P, F, Cl, I, and Br in the Fe powder is less than 1600ppm. The obtained Fe powder was further classified to obtain submicron Fe powder with particle sizes ranging from 100 nm to 1 μm and ultrafine micrometer-class Fe powder with particle sizes ranging from 1 μm to 10 μm. Example 16

[0213] This embodiment provides a method for producing nanometer-level Ti powder, which includes the following steps: Select sponge Ti and rare earth Ce with atomic ratios of 3 at.% and 2.5 at.% containing impurity elements T (including O, H, N, P, S, F, Cl, Br, and I), and fully melt them according to a molar ratio of Ce to Ti of about 2:1. The atomic percentage of the main component Ce 64.9 Ti 32.5 T 2.6 A homogeneous initial alloy melt can be obtained. The initial alloy melt is atomized and solidified using water atomization milling technology to obtain near-spherical intermediate alloy powder with a particle size range of 5 μm to 80 μm. The solidification structure of this intermediate alloy powder is composed of the main component Ce in atomic percentage. 96.3 T 3.7 The second phase matrix and the main component Ti 99.7 T 0.3 The first phase consists of dispersed granules of Ti 99.7 T 0.3 The granules are nearly spherical in shape and have a particle size range of 5nm to 150nm. The primary phase Ti in the intermediate alloy powder 99.7 T 0.3 The volume content of the granules is approximately 19.5%. The substrate Ce in the intermediate alloy powder was 96.3 T 3.7 and removes Ti, which is resistant to reaction with dilute hydrochloric acid solution in the intermediate alloy powder. 99.7 T 0.3 Granules are removed, i.e., nanometer Ti particles finer than the intermediate alloy powder. 99.7 T 0.3 The powder obtained has a particle size range of 5nm to 150nm, and the total content of H, O, N, S, P, F, Cl, I, and Br is 0.3at.%. Main component Ti under protective atmosphere 99.7 T 0.3The nano-powder epoxy resin and other coating ingredients can be mixed to produce nano-Ti modified polymer anti-corrosion coating. Example 17

[0214] This embodiment provides a method for producing a submicron Ti-Nb powder, which includes the following steps: The atomic ratios of Ti, Nb, and rare earth Ce containing impurity elements T (including O, H, N, P, S, F, Cl, Br, and I) were selected as 3 at.%, 1 at.%, and 2.5 at.%, respectively. Each alloy was melted according to a molar ratio of Gd:Ti:Nb of approximately 3:1:1, and the atomic percentage of the main component Gd 58.7 Ti 19.5 Nb 19.5 T 2.3 A homogeneous initial alloy melt can be obtained. The initial alloy melt is atomized and solidified using the gas atomization milling technique to obtain a near-spherical intermediate alloy powder with a particle size range of 15 μm to 150 μm. The solidification structure of this intermediate alloy powder is the atomic percentage of the main component Gd 96.4 T 3.6 The second phase matrix and the main component Ti 49.88 Nb 49.88 T 0.24 The first phase consists of dispersed granules of Ti 49.88 Nb 49.88 T 0.24 The granules are nearly spherical in shape and have a particle size range of 50nm to 500nm. The primary phase Ti in the intermediate alloy powder 49.88 Nb 49.88 T 0.24 The volume content of the granules is approximately 26%. The substrate Gd in the intermediate alloy powder was 96.4 T 3.6 and removes Ti, which is resistant to reaction with dilute hydrochloric acid solution in the intermediate alloy powder. 49.88 Nb 49.88 T 0.24 The granules are separated, i.e., the main component Ti is finer than the intermediate alloy powder. 49.88 Nb 49.88 T 0.24 Submicron powder is obtained, with a particle size range of 50nm~500nm, and the total content of H, O, N, S, P, F, Cl, I, and Br is 0.24at.%. Example 18

[0215] This embodiment provides a method for producing a micron-sized Ti powder, which includes the following steps: Select sponge Ti and rare earth Ce with atomic ratios of 1 at.% and 2.5 at.% containing impurity elements T (including O, H, N, P, S, F, Cl, Br, and I), and fully melt them according to a molar ratio of Ce to Ti of about 5:95. The atomic percentage of the main component Ce 4.9 Ti 94 T 1.1 A homogeneous initial alloy melt can be obtained. The initial alloy melt is atomized and solidified using the gas atomization milling technique to obtain a near-spherical intermediate alloy powder with a particle size range of 15 μm to 100 μm. The solidification structure of this intermediate alloy powder is composed of the main component Ce in atomic percentage. 86 T 14 The second phase matrix shell and the single main component Ti 99.7 T 0.3 The particle size range of the first phase inner core granules is 14.5μm~97μm. 99.7 T 0.3 The volume content of the granules is approximately 91%. The substrate Ce in the intermediate alloy powder was 86 T 147 The shell is removed and the Ti in the intermediate alloy powder is less likely to react with dilute hydrochloric acid solution. 99.7 T 0.3 The inner core granules are released. 99.7 T 0.3 The resulting micron-sized powder has a particle size range of 14.5 μm to 97 μm, and the total content of H, O, N, S, P, Cl, I, and Br is 0.3 at.%. Example 19

[0216] This example provides a method for producing nano-submicron grade Fe powder, which includes the following steps: Fe and rare earth La with atomic ratios of 1 at.% and 2.5 at.% containing impurity elements T (including O, H, N, P, S, F, Cl, Br, and I) were selected, and each alloy was melted according to a La:Fe molar ratio of approximately 3:2. The atomic percentage of the main component La 58.5 Fe 39.6 T 1.9 A homogeneous initial alloy melt can be obtained. The initial alloy melt is atomized and solidified using the gas atomization milling technique to obtain a near-spherical intermediate alloy powder with a particle size range of 15 μm to 150 μm. The solidification structure of this intermediate alloy powder is the atomic percentage of the main component La. 97 T3 second phase matrix and large amount of main component Fe 99.75 T 0.25 It consists of dispersed granules of the first phase, among which is Fe 99.75 T 0.25 The granules are nearly spherical or branched, and the particle size ranges from 50nm to 600nm. The primary phase in the intermediate alloy powder is Fe. 99.75 T 0.25 The volume content of the granules is approximately 18%. The magnetic properties of Fe granules and the natural oxidation-pulverization process of La in air allow for the magnetic selection of Fe. 99.75 T 0.25 Granules 97 T3 Separation from the powdered oxides, i.e., Fe 99.75 T 0.25 Nano-submicron powder is obtained, with a particle size range of 50nm~600nm, and the total content of H, O, N, S, P, F, Cl, I, and Br is 0.25at.%. Example 20

[0217] This embodiment provides a method for producing a micrometer spherical TiNi powder, which includes the following steps: Select raw materials Ti, Ni and rare earth Gd with atomic ratios of 1 at.%, 0.5 at.%, and 2.5 at.% containing impurity elements T (including O, H, N, P, S, F, Cl, Br, and I). Melt each alloy according to a Gd:Ti:Ni molar ratio of approximately 5:47.5:47.5, and measure the atomic percentage of the main component Gd. 4.9 Ti 47.1 Ni 47.1 T 0.9A homogeneous initial alloy melt can be obtained. The initial alloy melt is atomized and solidified using the gas atomization milling technique to obtain a near-spherical intermediate alloy powder with a particle size range of 15 μm to 100 μm. The solidification structure of this intermediate alloy powder is the main component Gd in atomic percentage. 87.5 T 12.5 The second phase matrix shell and the single main component Ti 49.9 Ni 49.9 T 0.2 The particle size range of the first phase inner core granules is 14.5μm~97μm. 49.9 Ni 49.9 T 0.2 The volume content of the granules is approximately 89%. The substrate Gd in the intermediate alloy powder was 87.5 T 12.5 The shell is removed and the Ti in the intermediate alloy powder is less likely to react with dilute hydrochloric acid solution. 49.9 Ni 49.9 T 0.2 The inner core granules are released. That is, the main component Ti 49 .9 Ni 49.9 T 0.2 Near-spherical micrometers are obtained, with particle sizes ranging from 14.5 μm to 97 μm, and the total content of H, O, N, S, P, F, Cl, I, and Br is 0.2 at.%. Example 21

[0218] This embodiment provides a method for producing a nanometer Ti-V-Al alloy powder, which includes the following steps: Select the sponge Ti, V, rare earth Ce and Al raw materials with atomic ratios of 3 at.%, 1 at.%, 2.5 at.% and 0.2 at.% containing impurity elements T (including O, H, N, P, S, F and Cl), and melt the initial alloy raw materials thoroughly according to a certain composition, and obtain the main component Ce in atomic percentage. 70.5 Al 10 (Ti 96 V4) 17 T 2.5 An initial alloy melt of The initial alloy melt is atomized and solidified using water atomization milling technology to obtain a near-spherical intermediate alloy powder with a particle size range of 5 μm to 100 μm. The solidification structure of this intermediate alloy powder is the average component, mainly Ce. 86.5 Al 10.5 The second phase matrix and main components of T3 (Ti 96 V4) 92.25 Al 7.5 T 0.25 The particle size of the first phase dispersed granules ranges from 10nm to 200nm. The shape is nearly spherical. The first phase (Ti96V4) in the intermediate alloy powder 92.25 Al 7.5 T 0.25 The volume content of the granules is approximately 12%. The second phase matrix Ce in the intermediate alloy powder was formed by dilute hydrochloric acid solution. 86.5 Al 10.5 Removes T3 and is resistant to reaction with dilute hydrochloric acid solution in the intermediate alloy powder (Ti 96 V4) 92.25 Al 7.5 T 0.25 Granules are removed, i.e., finer than the intermediate alloy powder (Ti 96 V4) 92.25 Al 7.5 T 0.25 Nanometer powder is obtained, the particle size range of which is 50nm~200nm. The total content of H, O, N, S, P, F, Cl, I, Br is 0.25at.% under protective atmosphere. The main components (Ti 96 V4) 92.25 Al 7.5 T 0.25 The nano-powder can be mixed with epoxy resin and other coating ingredients to produce nano-Ti alloy modified polymer anti-corrosion coating. Example 22

[0219] This embodiment provides a method for producing a nanometer Ti-V-Al alloy powder, which includes the following steps: Select the Ti, V, rare earth Ce and Al raw materials with atomic ratios of 1at.%, 1at.%, 1at.% and 1at.% containing impurity elements T (including O, H, N, P, S, F, and Cl), and melt the initial alloy raw materials thoroughly according to a certain composition, and obtain the main component Ce in atomic percentage. 4.5Al 0.5 (Ti 96 V4) 94 An initial alloy melt of T1 is obtained. The initial alloy melt is atomized and solidified using the air atomization milling technique to obtain a near-spherical intermediate alloy powder with a particle size range of 5 μm to 80 μm. The solidification structure of this intermediate alloy powder is composed of the average component Ce, the main component 82 Al 1.8 T 16.2 The second phase matrix and the main component (Ti 96 V4) 99.5 Al 0.4 T 0.1 The particle size of the dispersed first phase granules ranges from 4.85 μm to 78 μm. The shape is nearly spherical. The structure of the intermediate alloy powder is a core-shell, with a single first phase granule coated on the outer shell of the second phase substrate. 96 V4) 99.5 Al 0.4 T 0.1 The volume content of the granules is about 90%. The second phase matrix Ce in the intermediate alloy powder was formed by dilute hydrochloric acid solution. 82 Al 1.8 T 16.2 The granules in the intermediate alloy powder that are difficult to react with the dilute hydrochloric acid solution are removed. 96 V4) 99.5 Al 0.4 T 0.1 Spherical powder is obtained, the particle size range of which is 4.85μm~78μm, and the total content of H, O, N, S, P, F, Cl, I, and Br is 0.1at.%. The obtained (Ti 96 V4) 99.5 Al 0.4 T 0.1 The alloy spherical powder can be applied to powder metallurgy, injection molding, metal 3D printing, etc. Example 23

[0220] This embodiment provides a method for producing a micron-sized Nb powder, which includes the following steps: Select raw materials Nb and Cu with atomic ratios of 0.5 at.% and 0.5 at.% containing impurity elements T (including O, H, N, P, S, F, Cl, Br, and I), and thoroughly melt the raw materials Nb and Cu according to a molar ratio of Cu to Nb of approximately 12:88. The atomic percentage of the main component Cu 11.9 Nb 87.6 T 0.5 A homogeneous initial alloy melt can be obtained. The initial alloy melt is atomized and solidified using the gas atomization milling technique to obtain a near-spherical intermediate alloy powder with a particle size range of 15 μm to 100 μm. The solidification structure of this intermediate alloy powder is composed of the main component Cu in atomic percentage. 97.7 T 2.3 The second phase matrix shell and the single main component Nb 99.8 T 0.2 The particle size range of the first phase inner core granules is 14.5μm~97μm. The shape is nearly spherical. Nb in the intermediate alloy powder 99.8 T 0.2 The volume content of the granules is approximately 92%. The second phase substrate Cu in the intermediate alloy powder was formed by concentrated hydrochloric acid solution. 97.7 T 2.3 The outer shell is removed and the Nb in the intermediate alloy powder is hard to react with concentrated hydrochloric acid solution. 99.8 T 0.2 The inner core granules are released. That is, the main component is Nb. 99.8 T 0.2 The micron-sized powder is obtained, with a particle size range of 14.5μm~97μm, and the total content of H, O, N, S, P, F, Cl, I, and Br is 0.2at.%. Example 24

[0221] This embodiment provides a method for producing submicron Si powder, which includes the following steps: Select raw Si and raw Zn with atomic ratios of 0.5 at.% and 0.5 at.% containing impurity elements T (including O, H, N, P, S, F, Cl, Br, and I), respectively, and thoroughly melt the raw Si and raw Zn according to a molar ratio of Si to Zn of approximately 30:70 to obtain the main component Si in atomic percentage. 29.85 Zn 69.65 T 0.5 A homogeneous initial alloy melt can be obtained. The initial alloy melt is atomized and solidified using the air atomization milling technique to obtain a near-spherical intermediate alloy powder with a particle size range of 15 μm to 100 μm. The solidification structure of this intermediate alloy powder is the atomic percentage of the main component Zn. 99.35 T 0.65 The second phase matrix and atomic percentage of the main component Si 97.83 T 0.17 The particle size range of the dispersed granules is 100nm to 2μm. The shape is nearly spherical. The first phase Si in the intermediate alloy powder 97.83 T 0.17 The volume content of the dispersed granules is approximately 36%. Zn in the intermediate alloy powder by hydrochloric acid solution 99.35 T 0.65 The substrate is removed, and Si, which does not react easily with the hydrochloric acid solution in the intermediate alloy powder, is added. 97.83 T 0.17 The granules are removed. 97.83 T 0.17 Submicron powder is obtained, with a particle size range of 100nm~2μm, and the total content of H, O, N, S, P, F, Cl, I, and Br is 0.17at.%. Example 25

[0222] This embodiment provides a method for producing a micron-sized Si powder, which includes the following steps: Select raw Si and Zn materials with atomic ratios of 0.5 at.% and 0.5 at.% containing impurity elements T (including O, H, N, P, S, F, Cl, Br, and I), respectively, and thoroughly melt the raw Si and Zn materials according to a molar ratio of Si to Zn of approximately 90:10 to obtain the main component Si in atomic percentage. 89.55 Zn 9.95 T 0.5 A homogeneous initial alloy melt can be obtained. The initial alloy melt is atomized and solidified using the air atomization milling technique to obtain a near-spherical intermediate alloy powder with a particle size range of 15 μm to 100 μm. The solidification structure of this intermediate alloy powder is the atomic percentage of the main component Zn. 96.1 T 3.9 The second phase matrix and atomic percentage of the main component Si 99.1 T 0.1This intermediate alloy powder has a core-shell structure, with single-phase granules on the inside and a second-phase substrate on the outside that coats the first-phase granules. The particle size range of the first-phase granules is 14.5 μm to 97 μm. The shape is nearly spherical. The first-phase Si in the intermediate alloy powder 99.1 T 0.1 The volume content of the granules is approximately 92%. Zn in the intermediate alloy powder by hydrochloric acid solution 96.1 T 3.9 The substrate is removed, and Si, which does not react easily with the hydrochloric acid solution in the intermediate alloy powder, is added. 97.83 T 0.17 The granules are removed. 97.83 T 0.17 The micron powder is obtained, with a particle size range of 14.5μm~97μm, and the total content of H, O, N, S, P, F, Cl, I, and Br is 0.1at.%. Example 26

[0223] This embodiment provides a method for producing nanometer CuSi powder, which includes the following steps: The raw materials Si, Cu, and Pb are selected with atomic ratios of 0.5 at.%, 0.5 at.%, and 0.5 at.%, including impurity elements T (including O, H, N, P, S, F, Cl, Br, and I), and the molar ratio of Cu to Si is 90:10. Each raw material is thoroughly melted, and the atomic percentage of the main component Pb 74.5 (Cu 90 Si 10 ) 25 T 0.5 A homogeneous initial alloy melt can be obtained. The initial alloy melt is atomized and solidified using water atomization milling technology to obtain near-spherical intermediate alloy powder with a particle size range of 5 μm to 80 μm. The solidification structure of this intermediate alloy powder is the atomic percentage of the main component Pb 99.4 T 0.6 The second phase matrix and the main component (Cu 90 Si 10 ) 99.8 T 0.2 The first phase (Cu) is composed of dispersed granules. 90 Si 10 ) 99.8 T 0.2The granules are nearly spherical in shape. The particle size ranges from 5 nm to 150 nm. The first phase (Cu) in the intermediate gold powder 90 Si 10 ) 99.8 T 0.2 The volume content of the granules is approximately 12%. Pb in the intermediate alloy powder was analyzed by dilute hydrochloric acid-acetic acid mixed acid solution. 99.4 T 0.6 The substrate is removed and the mixed acid solution in the intermediate alloy powder is hard to react with (Cu 90 Si 10 ) 99.8 T 0.2 The granules are removed. 90 Si 10 ) 99.8 T 0.2 Nanometer powder is obtained, with a particle size ranging from 5nm to 150nm, and the total content of H, O, N, S, P, F, Cl, I, and Br is 0.2at.%. Example 27

[0224] This embodiment provides a method for producing nanometer-level Ti powder, which includes the following steps: Sponge Ti and rare earth Ce with atomic ratios of 3 at.% and 2.5 at.% containing impurity elements T (including O, H, N, P, S, F, Cl, Br, and I) were selected, and 0.5 at.% Mn was included in the sponge Ti and 0.7 at.% Mg was included in the rare earth Ce. The sponge Ti and rare earth Ce were fully melted according to a molar ratio of Ce to Ti of approximately 2:1, and the atomic percentages of the main components (Ce 99.3 Mg 0.7 ) 64.9 (Ti 99.5 Mn 0.5 ) 32.5 T 2.6 A homogeneous initial alloy melt can be obtained. The initial alloy melt is atomized and solidified using water atomization milling technology to obtain near-spherical intermediate alloy powder with a particle size range of 5 μm to 80 μm. The solidification structure of this intermediate alloy powder is the atomic percentage of the main components (Ce, 99.3 Mg 0.7 ) 96.3 T 3.7 The second phase matrix and the main component (Ti 99.5 Mn0.5 ) 99.7 T 0.3 The first phase (Ti 99.5 Mn 0.5 ) 99.7 T 0.3 The granules are nearly spherical in shape, and their particle size ranges from 5 nm to 150 nm. 99.5 Mn 0.5 ) 99.7 T 0.3 The volume content of the granules is approximately 19.5%. The substrate (Ce) in the intermediate alloy powder was 99.3 Mg 0.7 ) 96.3 T 3.7 and the intermediate alloy powder is less likely to react with dilute hydrochloric acid solution (Ti 99.5 Mn 0.5 ) 99.7 T 0.3 Granules are removed, i.e., finer than the intermediate alloy powder (Ti 99.5 Mn 0.5 ) 99.7 T 0.3 Nanometer powder is obtained, with particle size ranging from 5nm to 150nm, and the total content of H, O, N, S, P, F, Cl, I, and Br is 0.3at.%. The main component (Ti 99.5 Mn 0.5 ) 99.7 T 0.3 Nano-Ti modified polymer anti-corrosion coating can be produced by mixing nanometer powder with epoxy resin and other coating ingredients.

[0225] The technical features of the above implementation examples can be combined in any way. For the sake of brevity, not all possible combinations of the technical features in the above implementation examples are described. However, if there is no contradiction in the combination of these technical features, it should be considered within the scope described in this description. The above examples are more specific and detailed descriptions of some embodiments of the present invention, but they should not be construed as limiting the scope of the invention patent. It should be noted that a person skilled in the art may make some modifications and improvements without departing from the concept of the present invention, and these are within the scope of protection of the present invention. Therefore, the scope of protection of the invention patent should be determined based on the scope of the attached claims.

Claims

1. 1. A method for producing a high purity powder material, comprising: Step 1: selecting and melting initial alloy raw materials to obtain a homogeneous initial alloy melt; Step 2: atomizing and solidifying the initial alloy melt through an atomization milling process to obtain an intermediate alloy powder, the intermediate alloy powder comprising a first phase and a second phase, the first phase being granular, the second phase being a substrate having a lower melting point than the first phase, the first phase granules being coated on the second phase substrate, and the impurity elements in the initial alloy melt and the impurity elements introduced during the atomization milling process being collected in the second phase substrate, thereby purifying the first phase granules; and Step 3 includes removing the second phase matrix in the intermediate alloy powder, leaving the first phase granules, and removing the impurity elements in the second phase matrix; The impurity element in the initial alloy melt is T, and T includes at least one of O, H, N, S, F, Cl, I, and Br; Depending on the ratio of raw materials in the initial alloy melt, the average composition of the initial alloy melt contains one of the following combinations (1) to (4): Combination (1): The average composition of the initial alloy melt is Aa(MxDy)bTd, wherein A includes at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu, M includes at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, and Ti, D includes at least one of Fe, Co, and Ni, and x, y, a, b, and d each represent an atomic percentage of the constituent elements, and 0.5%≦a≦99.5%, 0.5%≦b≦99.5%, 0<d≦10%, 5%≦x≦55%, and 45%≦y≦95%. Combination (2): The average composition of the initial alloy melt is AaMbTd, A includes at least one of Mg, Ca, Li, Na, K, Cu, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu, M includes at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, and Ti, a, b, and d represent atomic percentages of the constituent elements, and 0.5%≦a≦99.5%, 0.5%≦b≦99.5%, and 0<d≦10%. Combination (3): The average composition of the initial alloy melt is AaMbTd, A includes at least one of Zn, Mg, Sn, Pb, Ga, In, Al, La, Ge, Cu, K, Na, and Li, M includes at least one of Be, B, Bi, Fe, Ni, Cu, Ag, Si, Ge, Cr, and V, the atomic percentages of Be, B, Si, and Ge in M ​​are 50% or less, and a, b, and d represent the atomic percentages of the constituent elements, and 0.5%≦a≦99.5%, 0.5%≦b≦99.5%, and 0<d≦10%. Combination (4): A method for producing a high-purity powder material, wherein the average composition of the initial alloy melt is AaMbAlcTd, A includes at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu, M includes at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, and Ti, Al is aluminum, and a, b, c, and d represent the atomic percentages of the constituent elements, and are 0.5≦a≦99.4%, 0.5≦b≦99.4%, 0.1%≦c≦25%, and 0<d≦10%.

2. 1. A two-phase powder material comprising: A single grain contains the powder and the coating; The solidification structure of the two-phase powder material includes a substrate and a granular phase, the substrate is the coating, the granular phase is the powder, the melting point of the coating is lower than the melting point of the powder, and the powder is coated on the coating; the coating method of the powder in the two-phase powder material is a mosaic structure in which multiple powders are dispersed in the coating, or a core-shell structure in which an inner single powder is coated with an outer coating; The chemical composition and structure of dual-phase powder materials include any of the following four combinations: 1) The powder composition of the two-phase powder material is (MxDy)x1Tz1, and the average composition of the coating is Ax2Tz2, where 98%≦x1≦100%, 0≦z1≦2%, 70%≦x2≦100%, 0≦z2≦30%, z1≦d≦z2, and 2z1≦z2, where x1, z1, x2, and z2 respectively refer to the atomic percentages of the corresponding constituent elements, and A includes at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu; M includes at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, and Ti; D includes at least one of Fe, Co, and Ni; T includes at least one of O, H, N, P, S, F, Cl, I, and Br; x and y represent corresponding constituent atomic percentages, and 5%≦x≦55%, 45%≦y≦95%; 2) The powder composition of the two-phase powder material is Mx1Tz1, and the average composition of the coating is Ax2Tz2, where 98%≦x1≦100%, 0≦z1≦2%, 70%≦x2≦100%, 0≦z2≦30%, z1≦d≦z2, and 2z1≦z2, where x1, z1, x2, and z2 respectively represent the atomic percentages of the corresponding constituent elements, A includes at least one of Mg, Ca, Li, Na, K, Cu, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu, M includes at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, and Ti, and T includes at least one of O, H, N, P, S, F, Cl, I, and Br; 3) The powder composition of the two-phase powder material is Mx1Tz1, and the average composition of the coating is Ax2Tz2, where 98%≦x1≦100%, 0≦z1≦2%, 70%≦x2≦100%, 0≦z2≦30%, z1≦d≦z2, and 2z1≦z2, where x1, z1, x2, and z2 respectively represent the atomic percentages of the corresponding constituent elements, A includes at least one of Zn, Mg, Sn, Pb, Ga, In, Al, La, Ge, Cu, K, Na, and Li, M includes at least one of Be, B, Bi, Fe, Ni, Cu, Ag, Si, Ge, Cr, and V, and the atomic percentages of Be, B, Si, and Ge in M ​​are 50% or less, and T includes at least one of O, H, N, P, S, F, Cl, I, and Br; 4) The powder composition of the two-phase powder material is Mx1Aly1Tz1, and the average composition of the coating is Ax2Aly2Tz2, where 78%≦x1≦99.9%, 0.1%≦y1≦22%, 0≦z1≦2%, 70%≦x2≦99.8%, 0.2%≦y2≦30%, 0≦z2≦30%, and 2z1≦z2, and x1, y1, z1, x2, y2, and z2 are the atoms of the corresponding constituent elements, respectively. A refers to the atomic percentage, where A comprises at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu; M comprises at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, and Ti; Al is aluminum; and T comprises at least one of O, H, N, P, S, F, Cl, I, and Br.

3. 1. A method for producing a high purity powder material, comprising: Step 1: Selecting and melting the initial alloy raw materials to obtain a homogeneous initial alloy melt; Step 2: atomizing and solidifying the initial alloy melt through an atomization milling process to obtain an intermediate alloy powder, the intermediate alloy powder comprising a first phase and a second phase, the first phase being granular, the second phase being a substrate having a lower melting point than the first phase, the first phase granules being coated on the second phase substrate, and the impurity elements in the initial alloy melt and the impurity elements introduced during the atomization milling process being collected in the second phase substrate to purify the first phase granules; and Step 3 includes removing the second phase matrix in the intermediate alloy powder, leaving the first phase granules, and removing the impurity elements in the second phase matrix; The impurity element in the initial alloy melt is T, which includes at least one of O, H, N, S, F, Cl, I, and Br; the average composition of the initial alloy melt is AaMbTd, wherein A includes at least one of Zn, Sn, Pb, Ga, In, Al, Ge, and Cu, M includes at least one of Be, Si, Ge, and B, the atomic percentages of Be, B, Si, and Ge in M ​​being 50% or more, a, b, and d represent the atomic percentages of the constituent elements, and 0.5%≦a≦99.5%, 0.5%≦b≦99.5%, and 0<d≦10%; A method for producing a high-purity powder material, wherein the intermediate alloy powder comprises first-phase granules having a component Mx1Tz1 and a second-phase substrate having a component Ax2Tz2, wherein 98%≦x1≦100%, 0≦z1≦2%, 70%≦x2≦100%, 0≦z2≦30%, z1≦d≦z2, and 2z1≦z2, and x1, z1, x2, and z2 respectively represent the atomic percentages of the corresponding constituent elements.

4. 1. A method for producing a high purity powder material, comprising: Step 1: selecting and melting initial alloy raw materials to obtain a homogeneous initial alloy melt; Step 2: atomizing and solidifying the initial alloy melt through an atomization milling process to obtain an intermediate alloy powder, the intermediate alloy powder comprising a first phase and a second phase, the first phase being granular, the second phase being a substrate having a lower melting point than the first phase, the first phase granules being coated on the second phase substrate, and the impurity elements in the initial alloy melt and the impurity elements introduced during the atomization milling process being collected in the second phase substrate to purify the first phase granules; and Step 3 includes removing the second phase matrix in the intermediate alloy powder, leaving the first phase granules, and removing the impurity elements in the second phase matrix; The impurity element in the initial alloy melt is T, and T includes at least one of O, H, N, S, F, Cl, I, and Br; the proportions of the components of the initial alloy are AaMb, A is at least one of Mg, Ca, Li, Na, K, Zn, In, Sn, Pb, Ga, Cu, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu, M is at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti, Fe, Co, Ni, Mn, Cu, Ag, Si, Ge, B, Be, and C, a and b respectively represent the atomic percentages of the corresponding constituent elements, 0.5%≦b≦98%, and a+b=100%, and the AaMb alloy melt does not form an intermetallic compound consisting of A and M during atomization and solidification, but forms first-phase granules of component M and a second-phase matrix of component A, The composition of the initial alloy is AaMbAlc, where A is at least one of Mg, Ca, Li, Na, K, Zn, In, Sn, Pb, Ga, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu, Al is aluminum, M is at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti, Fe, Co, Ni, Mn, Cu, Ag, Si, Ge, B, Be, and C, and a, b, and c are atoms of the corresponding constituent elements. a + b + c = 100%, and the AaMbAlc alloy melt does not form an intermetallic compound consisting of A and M during atomization solidification, but forms first-phase granules of an Mx1Aly1 component and a second-phase matrix of an Ax2Aly2 component, and x1, y1, x2, and y2 represent the atomic percentages of the corresponding constituent elements, respectively, and 0.1%≦y1≦25%, 0.1%≦y2≦35%, x1+y1=100%, and x2+y2=100%.