CN112276101A

CN112276101A - Preparation method and application of high-purity powder material and alloy strip

Info

Publication number: CN112276101A
Application number: CN202011273626.1A
Authority: CN
Inventors: 赵远云; 刘丽
Original assignee: Individual
Current assignee: Individual
Priority date: 2020-08-19
Filing date: 2020-11-14
Publication date: 2021-01-29
Also published as: WO2022036906A1; CN116056818A

Abstract

The invention relates to a preparation method of a high-purity powder material. Firstly, an alloy strip with a solidification structure composed of a matrix phase and a dispersed particle phase is prepared through melt solidification. In the process of solidifying the alloy strip, impurity elements are enriched to the matrix phase, so that the dispersed particle phase is purified. And removing the matrix phase in the alloy strip to obtain the high-purity target powder material consisting of the dispersed granular phase. The preparation method has the characteristics of simple process, easy operation and low cost, can be used for preparing nano-scale, submicron-scale, micron-scale and millimeter-scale high-purity powder materials, and has good application prospects in the fields of catalytic materials, powder metallurgy, composite materials, wave-absorbing materials, sterilizing materials, magnetic materials, metal injection molding, 3D printing, coatings and the like.

Description

Preparation method and application of high-purity powder material and alloy strip

Technical Field

The invention relates to the technical field of metal materials, in particular to a preparation method of a high-purity powder material, application of the high-purity powder material and an alloy strip.

Background

The powder with the micro-nano particle size has special surface effect, quantum size effect, quantum tunneling effect, coulomb blocking effect and the like, and shows a plurality of peculiar properties different from the traditional materials in the aspects of optics, electrics, magnetics, catalysis and the like, so the powder is widely applied to a plurality of fields of photoelectronic devices, wave-absorbing materials, high-efficiency catalysts and the like.

At present, methods for producing ultrafine powders are classified into a solid phase method, a liquid phase method, and a gas phase method from the state of matter. The solid phase method mainly includes mechanical pulverization, ultrasonic pulverization, thermal decomposition, explosion, and the like. The liquid phase method mainly includes precipitation, alkoxide method, carbonyl method, spray heat drying method, freeze drying method, electrolytic method, chemical coagulation method, and the like. The vapor phase method mainly includes a vapor phase reaction method, a plasma method, a high temperature plasma method, an evaporation method, a chemical vapor deposition method, and the like. Although there are many methods for preparing ultrafine powders, each method has certain limitations. For example, the liquid phase method has disadvantages of low yield, high cost, complicated process, and the like. The mechanical method has the disadvantages that the classification is difficult after the powder is prepared, and the purity, the fineness and the appearance of the product are difficult to ensure. The rotary electrode method and the atomization method are the main methods for preparing high-performance metal and alloy powder at present, but the production efficiency is low, the yield of the ultrafine powder is not high, and the energy consumption is relatively large; the jet milling method and the hydrogenation dehydrogenation method are suitable for large-scale industrial production, but have strong selectivity on raw material metals and alloys.

In addition, the impurity content, especially the oxygen content, of the powder has a great influence on its performance. At present, the impurity content of metal or alloy is mainly controlled by a method of controlling the purity and the vacuum degree of raw materials, and the cost is high. Therefore, the development of a new preparation method of the high-purity powder material has important significance.

Disclosure of Invention

In view of the above, it is necessary to provide a method for preparing a high-purity powder material with simple process and easy operation, and an application thereof.

The preparation method of the high-purity powder material is characterized by comprising the following steps of:

step S1, selecting initial alloy raw materials, melting the initial alloy raw materials according to the initial alloy component proportion to obtain a uniform initial alloy melt containing an impurity element T, wherein T comprises at least one of O, H, N, P, S, F, Cl, I and Br, and the average component of the initial alloy melt comprises any one of the following combinations (1) to (4):

combination (1): the average composition of the initial alloy melt is mainly A_a(M_xD_y)_bT_dWherein 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, and D comprises at least one of Fe, Co and Ni, wherein x and Y; a. b and d both represent the atom percentage content of corresponding constituent elements, and a is more than or equal to 24.9 percent and less than or equal to 99.4 percent, b is more than or equal to 0.5 percent and less than or equal to 75 percent, and b is more than or equal to 0<d is less than or equal to 10 percent; preferably, a is more than or equal to 24.9 percent and less than or equal to 59.9 percent, 40 percent<b≤75％，0<d≤10％；

Furthermore, x is more than or equal to 10% and less than or equal to 55%, and y is more than or equal to 45% and less than or equal to 90%;

further, the molar ratio x: y is 0.9-1.1;

preferably, x is 50% of y, i.e. the molar ratio x: y is 1: 1;

combination (2): the average composition of the initial alloy melt is mainly A_aM_bT_dWherein, A is a bagContains 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 M contains at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf and Ti; wherein a, b and d represent the atom percentage content of corresponding constituent elements, and a is more than or equal to 24.9 percent and less than or equal to 99.4 percent, b is more than or equal to 0.5 percent and less than or equal to 75 percent, and b is more than or equal to 0 percent<d≤10％；

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

preferably, when M comprises at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti, A comprises Cu;

preferably, a is more than or equal to 24.9 percent and less than or equal to 54.9 percent, b is more than or equal to 45 percent and less than or equal to 75 percent, and d is more than 0 and less than or equal to 10 percent;

combination (3): the average composition of the initial alloy melt is mainly A_aM_bT_dWherein A comprises at least one of Zn, Mg, Sn, Pb, Ga, In, Al, La, Ge, Cu, K, Na and Li, M comprises at least one of B, Bi, Fe, Ni, Cu, Ag, Si, Ge, Cr and V, a, B and d represent the atom percentage content of the corresponding constituent elements, and a is more than or equal to 24.9% and less than or equal to 59.9%, 40%<b≤75％，0<d≤10％；

Preferably, when M comprises B, a comprises at least one of Sn, Ge, Cu, Zn; when M contains Bi, A contains at least one of Sn, Ga and Al;

preferably, when M comprises at least one of Fe, Ni, Cu, Ag, A comprises at least one of La, In, Na, K, Li, Pb, Mg; preferably, 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;

preferably, when M contains at least one of Si and Ge, a contains at least one of Zn, Sn, Pb, Ga, In, and Al;

preferably, when M comprises at least one of Cr, V, a comprises Zn;

combination (4) when the average composition of the initial alloy melt is predominantly A_aM_bAl_cT_dWhen A contains 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; wherein a, b, c and d respectively represent the atom percentage content of the corresponding constituent elements, and a is more than or equal to 29.8 percent and less than or equal to 64.8 percent, and the percentage content of a is more than or equal to 35 percent<b≤70％，0.1％≤c≤25％，0<d≤10％；

Further, the average composition of the initial alloy melt is any one of the combinations (1) to (4) described above;

step S2, solidifying the initial alloy melt into an initial alloy strip; the solidification structure of the initial alloy strip comprises a matrix phase and a dispersed particle phase; the matrix phase has a lower melting point than the dispersed particle phase, and the dispersed particle phase is coated in the matrix phase; in the solidification process of the initial alloy melt, the impurity element T in the initial alloy melt is redistributed in the dispersed particle phase and the matrix phase and enriched in the matrix phase, so that the dispersed particle phase is purified;

when the average composition of the initial alloy melt is as described in combination (1) of step S1, the dispersed particulate phase in the initial alloy strip has a composition of predominantly (M)_xD_y)_x1T_z1The average component of the matrix phase is mainly A_x2T_z2(ii) a And x1 is more than or equal to 98.5 percent<100％,0<z1≤1.5％；80％≤x2<100％,0<z2≤20％；z1<d<z2，2z1<z 2; x1, z1, x2 and z2 respectively represent the atom percentage content of the corresponding constituent elements; preferably, when the average composition of the initial alloy melt is that described in combination (1) of step S1, the composition of the dispersed particulate phase in the initial alloy strip is (M)_xD_y)_x1T_z1The average component of the matrix phase is A_x2T_z2；

When the average composition of the initial alloy melt is that of the combination (2) or the combination (3) of the step S1, the composition of the dispersed particle phase in the initial alloy strip is mainly M_x1T_z1Average composition of matrix phaseIs divided into_x2T_z2(ii) a And x1 is more than or equal to 98.5 percent<100％,0<z1≤1.5％；80％≤x2<100％,0<z2≤20％；z1<d<z2，2z1<z 2; x1, z1, x2 and z2 respectively represent the atom percentage content of the corresponding constituent elements; preferably, when the average composition of the initial alloy melt is that of the combination (2) or the combination (3) of step S1, the composition of the dispersed particle phase in the initial alloy strip is M_x1T_z1The average component of the matrix phase is A_x2T_z2；

When the average composition of the initial alloy melt is that described in combination (4) of step S1, the dispersed particle phase in the initial alloy strip has a composition of predominantly M_x1Al_y1T_z1The average component of the matrix phase is mainly A_x2Al_y2T_z2(ii) a X1 is more than or equal to 77.8 percent and less than or equal to 99.8 percent, y1 is more than or equal to 0.1 percent and less than or equal to 22 percent, and<z1≤1.5％；69.8％≤x2≤99.7％，0.2％≤y2≤30％，0<z2≤20％，z1<d<z2，2z1<z2，y1<y2, x1, y1, z1, x2, y2 and z2 respectively represent the atom percentage contents of the corresponding constituent elements; preferably, when the average composition of the initial alloy melt is that described in step S1 combination (4), the composition of the dispersed particle phase in the initial alloy strip is M_x1Al_y1T_z1The average component of the matrix phase is A_x2Al_y2T_z2；

And step S3, removing the matrix phase in the initial alloy strip, reserving the dispersed particle phase which cannot be removed simultaneously in the matrix phase removing process, and collecting the dropped dispersed particle phase to obtain the high-purity target powder material consisting of the original dispersed particles.

In the step S1, in the above step,

further, the sources of T impurity elements in the initial alloy melt include: impurities are introduced into the initial alloy raw materials, and impurities are introduced into the atmosphere or the crucible in the smelting process. The atmosphere-introduced impurities refer to impurities such as O, N, H in the ambient atmosphere absorbed by the alloy melt.

Further, T is an impurity element and contains at least one of O, H, N, P, S, F, Cl, I and Br; and the total content of the impurity elements is the content of the impurity element T;

further, if the raw materials are the respective simple substances or intermediate alloys containing impurity elements, they may be melted in proportion to prepare the initial alloy melt. If the supplied raw materials are directly the alloy raw materials corresponding to the components of the initial alloy melt, the raw materials can be remelted to obtain the initial alloy melt.

Further, the starting alloy raw material includes an M-T raw material containing an impurity element T. For example, when M is Ti and T comprises O, the M-T material includes a Ti-O material containing O impurities.

Further, the combination of A and M in the average composition of the initial alloy melt in the step S1 is very important, and the selection principle is to ensure that no intermetallic compound is formed between A and M during the solidification process of the alloy melt; or even though M and other elements (D) may form a high melting point intermetallic compound, no intermetallic compound is formed between A and M. Therefore, the two-phase separation of the matrix phase taking the A as the main component and the particle phase taking the M as the main component in the solidification process of the initial alloy melt can be realized, and the subsequent preparation of the powder material taking the M as the main component is facilitated.

In the step S2, in the above step,

further, the initial alloy strip does not contain an intermetallic compound comprising A and M;

further, the alloy melt is solidified by a strip casting method and a continuous casting method; generally, thinner initial alloy strip can be obtained by the strip casting method; thicker alloy strips can be obtained by continuous casting.

The thin alloy strip obtained by the strip casting method or the thick alloy strip obtained by the continuous casting method is completely different from the alloy ingot obtained by the common casting method in appearance, and the alloy ingot obtained by the common casting method generally has no obvious length, width and thickness difference in scale.

Further, the thickness of the initial alloy strip ranges from 5 μm to 50 mm; further, the thickness of the initial alloy strip ranges from 5 μm to 5 mm; preferably, the thickness of the initial alloy strip is in the range of 5 μm to 1 mm; more preferably, the thickness of the initial alloy strip is in the range of 5 μm to 200 μm; more preferably, the thickness of the starting alloy strip is in the range of 5 μm to 20 μm.

When the thickness of the initial alloy strip is in the order of millimeters, it may also be referred to as an alloy sheet.

Further, the width of the cross section of the initial alloy strip is more than 2 times its thickness.

Further, the length of the initial alloy strip is more than 10 times its thickness.

Preferably, the length of the initial alloy strip is more than 50 times its thickness.

Preferably, the length of the initial alloy strip is more than 100 times its thickness.

Further, the solidification rate of the initial alloy melt is 1K/s-10⁷K/s。

Further, the particle size of the dispersed particle phase is related to the solidification rate of the initial alloy melt; in general, the size of the particle size of the dispersed particle phase is inversely related to the solidification rate of the initial alloy melt, i.e., the larger the solidification rate of the initial alloy melt, the smaller the particle size of the dispersed particle phase.

Further, the particle size range of the dispersed particle phase is 2 nm-3 mm; further, the particle size range of the dispersed particle phase is 2 nm-500 mu m; preferably, the particle size range of the dispersed particle phase is 2 nm-99 μm; more preferably, the particle size range of the dispersed particle phase is 2 nm-5 μm; preferably, the particle size range of the dispersed particle phase is 2nm to 200 nm; more preferably, the dispersed particle phase has a particle size in the range of 2nm to 100 nm.

Further, the initial alloy melt solidified at a rate of 10 deg.f⁵K/s～10⁷When K/s, dispersed particles with the particle size mainly in the nanometer scale can be obtained.

Further, the initial alloy melt solidified at a rate of 10 deg.f⁴K/s～10⁵When K/s, dispersed particles with the particle size mainly in the submicron scale can be obtained.

Further, the initial alloy melt solidified at a rate of 10 deg.f²K/s～10⁴When K/s, dispersed particles with the particle size mainly in micron-scale can be obtained.

Further, the solidification rate of the initial alloy melt is 1K/s-10²At K/s, dispersed particles with the particle size mainly in millimeter scale can be obtained.

Further, the shape of the particles of the dispersed particle phase is not limited, and may include at least one of dendrite shape, spherical shape, subsphaeroidal shape, cube shape, cake shape and bar shape; when the particles are in the form of rods, the size of the particles is specified in particular as the diameter dimension of the cross-section of the rod.

Further, when the dispersed particles are in a nanoscale or submicron scale, spherical or nearly spherical particles are obtained in a large probability; when the dispersed particles are in the micron-sized or above, dendritic particles are obtained at a high probability.

Further, the dispersed particle phase is solidified and precipitated from the initial alloy melt, and according to the nucleation and growth theory, no matter the nearly spherical nano particles which just form nuclei and grow in a large size or the micron-sized and millimeter-sized dendritic crystal particles which grow fully, the crystal growth of the particles has a fixed orientation relation, so that the precipitated single particles are mainly composed of a single crystal.

When the dispersed particles are present in a higher percentage by volume throughout the initial alloy strip, the incorporation of two or more particles during the in-growth precipitation of single crystal particles is not excluded. If two or more single crystal grains are merely soft agglomerated, adsorbed to each other, or attached together with only a few sites in contact, one grain is not sufficiently combined through normal grain boundaries as in a polycrystalline material, which is still two single crystal grains. It is characterized in that after the matrix phase is removed in a subsequent process, the single crystal particles can be easily separated by techniques including ultrasonic dispersion treatment, jet milling and the like. Normally ductile metals or alloys, however, are polycrystalline, it is difficult to separate grain boundaries by techniques including ultrasonic dispersion treatment, jet milling, and the like.

Preferably, the number of single crystal grains in dispersed grains in the initial alloy strip is not less than 60% of the total number of dispersed grains.

As a further preference, the ratio of the number of single crystal particles in the dispersed particles to the number of all dispersed particles is not less than 90%.

Further, for a certain initial alloy strip, the volume percentage content of the dispersed particle phase in the initial alloy strip can be determined by calculating corresponding initial alloy melt components, dispersed particle phase components, matrix phase components, combined element atomic weight, density parameters and the like.

When the main element of the matrix phase is a large atomic element, the matrix phase can obtain a higher volume percentage content by a smaller atomic percentage content. Such as La in atomic percent₂₅Fe₇₅The initial alloy strip of (1) (for convenience of calculation, regardless of the presence of impurities), La and Fe in weight percentages of 45.33 wt% and 54.67 wt%, respectively, combined with a density of 6.2g/cm, respectively³And 7.8g/cm³The atomic percentage composition of La and Fe can be calculated to be La₂₅Fe₇₅Is 51 vol.% and 49 vol.%, respectively. This indicates that: even though the La-Fe alloy contains up to 75 at.% Fe, the volume percentage content is still below 50 vol.%, which facilitates the dispersion distribution of the Fe particles in the initial alloy ribbon.

Further, the dispersed particulate phase is present in the initial alloy strip at not greater than 50% vol.

Further, the atomic percent content z1 of the T impurity element in the dispersed particles is less than the atomic percent content of the T impurity element in the M-T raw material.

Further, z1< d < z2, and 2z1< z2,

preferably, z1< d < z2, and 3z1< z2,

preferably, 0< z1< d < z2, 3z1< z2, and 0< z1 ≦ 1.5%; namely, the content of T impurities in the dispersed particle phase is lower than that in the initial alloy melt, and 3 times of the content of the T impurities in the dispersed particle phase is still lower than that in the matrix phase;

preferably, 0< z1< d < z2, 3z1< z2, and 0< z1 ≦ 0.75%.

The invention adopts atom percentage content to express the content of T impurities. The composition of each element is represented by the atomic percentage content of the element, and the increase and decrease of the element content, such as the increase, decrease and change of impurity elements, can be accurately expressed by the concept of the amount of the substance. If the content of each element is characterized by the mass percentage content (or ppm concept) of the element, erroneous conclusions are easily generated due to the difference of atomic weights of each element. For example, such as Ti in atomic percent₄₅Gd₄₅O₁₀The alloy of (4), containing 100 atoms, the atomic percent content of O being 10 at%. The 100 atoms are divided into Ti₄₅O₄(the atomic percentage composition is Ti_91.8O_8.2) With Gd₄₅O₆(the atomic percent composition is Gd_88.2O_11.8) Two moieties, Gd₄₅O₆The atomic percent content of the oxygen in the alloy is increased to 11.8at percent, and Ti₄₅O₄The atomic percent content of the middle oxygen is reduced to 8.2at percent, and the enrichment of O in Gd can be accurately expressed. But if measured by the mass percent content of O, Ti₄₅Gd₄₅O₁₀Wherein the mass percent of O is 1.70wt percent, and Ti₄₅O₄With Gd₄₅O₆The mass percent of O in the Ti alloy is 2.9 wt.% and 1.34 wt.%, respectively, so that Ti is obtained₄₅O₄Middle O content compared with Gd₄₅O₆A false conclusion that the content of medium O is significantly increased.

In the step S3, in the above step,

further, the method for removing the matrix phase in the alloy strip comprises the following steps: at least one of acid reaction removal, alkali reaction removal and vacuum volatilization removal.

The composition and concentration of the acid solution and the alkali solution are not particularly limited as long as the matrix phase can be removed and the dispersed particle phase is retained.

The temperature and the vacuum degree of the vacuum treatment are not particularly limited as long as the matrix phase can be removed and the dispersed particle phase is retained.

Further, the method for removing the matrix phase in the initial alloy strip comprises the steps of natural oxidation-pulverization and peeling removal of the matrix phase.

When the matrix phase is an element which is easy to be naturally oxidized with oxygen, such as La, Ce and the like, the matrix phase can be separated from the dispersed particle phase through the natural oxidation-pulverization process of the matrix phase, and other technical means, such as magnetic separation, can be used for separating the dispersed particle phase with magnetic property from the natural oxide of the matrix phase.

Furthermore, because the target powder material is a dispersed particle phase dropped from the initial alloy strip, the components, particle diameters and the like of the target powder material are all equivalent to those of the corresponding dispersed particle phase.

Further, the particle size range of the target powder material is 2 nm-3 mm; preferably, the particle size range of the target powder material is 2 nm-500 mu m; preferably, the particle size range of the target powder material is 2 nm-99 μm; more preferably, the particle diameter range of the target powder material is 2 nm-5 μm; more preferably, the particle diameter range of the target powder material is 2nm to 200 nm; more preferably, the particle diameter of the target powder material is in the range of 2nm to 100 nm.

Further, after the initial alloy strip is reacted with the acid solution, dispersed particles are separated from the initial alloy strip, and the initial alloy strip is cleaned and dried to obtain the high-purity target powder material.

Further, when the average composition of the initial alloy melt is the composition of step S1 (1), the composition of the high-purity target powder material is mainly (M)_xD_y)_x1T_z1(ii) a Preferably, when the average composition of the initial alloy melt is the composition (1) in step S1, the composition of the high-purity target powder material is (M)_xD_y)_x1T_z1；

Further, when the average composition of the initial alloy melt is divided into stepsS1 in combination of (2) or (3), wherein the high-purity target powder material mainly contains M_x1T_z1(ii) a Preferably, when the average composition of the initial alloy melt is the composition (2) or (3) in step S1, the composition of the high-purity target powder material is M_x1T_z1；

Further, when the average composition of the initial alloy melt is the composition in step S1 (4), the composition of the high-purity target powder material is mainly M_x1Al_y1T_z1. Preferably, when the average composition of the initial alloy melt is the composition in step S1 (4), the composition of the high-purity target powder material is M_x1Al_y1T_z1。

Further, the atomic percentage content of the T impurity element in the target metal powder is not more than 1.5%;

preferably, the atomic percentage content of the T impurity element in the target metal powder does not exceed 0.75%.

Further, after the step S3, the following steps are also performed: screening the high-purity powder material, and then selecting the high-purity powder material with the particle size range of 5-200 mu m for plasma spheroidization to obtain a spherical high-purity powder material;

the invention also relates to application of the high-purity powder material or the spherical high-purity powder material obtained by the preparation method in catalytic materials, powder metallurgy, composite materials, wave-absorbing materials, sterilization materials, metal injection molding, 3D printing and coatings.

Further, the application of the spherical high-purity powder material obtained by the preparation method in the field of 3D printing of metal powder is characterized in that the particle size range of the spherical high-purity powder material is 10-200 μm.

Further, the application of the high-purity powder material obtained by the preparation method in metal injection molding and powder metallurgy is characterized in that the particle size range of the high-purity powder material is 0.1-200 μm.

Further, the application of the high-purity powder material obtained by the preparation method in the coating is characterized in that the particle size range of the high-purity powder material is 2 nm-5 μm.

The invention also relates to an alloy strip which is characterized by comprising inner green powder and a cladding body; the solidification structure of the alloy strip comprises a matrix phase and a dispersed particle phase, wherein the matrix phase is the cladding body, and the dispersed particle phase is the endogenous powder; the melting point of the coating body is lower than that of the endogenous powder, and the endogenous powder is coated in the coating body;

the chemical composition and structure of the alloy strip comprise any one of the following four combinations:

1) the component of the internal powder in the alloy strip is mainly (M)_xD_y)_x1T_z1The average composition of the coating is mainly A_x2T_z2(ii) a And x1 is more than or equal to 98.5 percent<100％,0<z1≤1.5％；80％≤x2<100％,0<z2≤20％；z1<d<z2，2z1<z 2; x1, z1, x2 and z2 respectively represent the atom percentage content of the corresponding constituent elements; wherein 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, and D comprises at least one of Fe, Co and Ni; t comprises at least one of O, H, N, P, S, F, Cl, I and Br; x and y represent the atom percentage content of corresponding constituent elements, x is more than or equal to 10% and less than or equal to 55%, and y is more than or equal to 45% and less than or equal to 90%; further, the molar ratio x: y is 0.9-1.1; preferably, x is 50% of y, i.e. the molar ratio x: y is 1: 1;

preferably, the component of the inner raw powder in the alloy strip is (M)_xD_y)_x1T_z1The average component of the coating is A_x2T_z2；

2) The component of the endogenous powder in the alloy strip is mainly M_x1T_z1The average composition of the coating is mainly A_x2T_z2(ii) a And x1 is more than or equal to 98.5 percent<100％,0<z1≤1.5％；80％≤x2<100％,0<z2≤20％；z1<d<z2，2z1<z 2; x1, z1, x2 and z2 respectively represent the atom percentage content of the corresponding constituent elements; wherein A comprises Mg, Ca, Li, Na, K, Cu, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb. At least one of Dy, Ho, Er, Tm, Yb and Lu, wherein M comprises at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf and Ti; t comprises at least one of O, H, N, P, S, F, Cl, I and Br;

preferably, the component of the inner raw powder in the alloy strip is M_x1T_z1The average component of the coating is A_x2T_z2；

3) The component of the endogenous powder in the alloy strip is mainly M_x1T_z1The average composition of the coating is mainly A_x2T_z2(ii) a And x1 is more than or equal to 98.5 percent<100％,0<z1≤1.5％；80％≤x2<100％,0<z2≤20％；z1<d<z2，2z1<z 2; x1, z1, x2 and z2 respectively represent the atom percentage content of the corresponding constituent elements; wherein A comprises at least one of Zn, Mg, Sn, Pb, Ga, In, Al, La, Ge, Cu, K, Na and Li, and M comprises at least one of B, Bi, Fe, Ni, Cu, Ag, Si, Ge, Cr and V;

preferably, when M comprises at least one of Cr, V, a comprises Zn;

preferably, the component of the inner green powder in the alloy strip is M_x1T_z1The average component of the coating is A_x2T_z2；

4) The component of the endogenous powder in the alloy strip is mainly M_x1Al_y1T_z1The average composition of the coating is mainly A_x2Al_y2T_z2(ii) a X1 is more than or equal to 77.8 percent and less than or equal to 99.8 percent, y1 is more than or equal to 0.1 percent and less than or equal to 22 percent, and<z1≤1.5％；69.8％≤x2≤99.7％，0.2％≤y2≤30％，0<z2≤20％，z1<d<z2，2z1<z2，y1<y2, x1, y1, z1, x2, y2 and z2 respectively represent the atom percentage contents of the corresponding constituent elements; wherein 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;

preferably, the component of the inner raw powder in the alloy strip is M_x1Al_y1T_z1The average component of the coating is A_x2Al_y2T_z2；

Preferably, the chemical composition and structure of the alloy strip are any one of the four combinations 1) to 4) above;

further, the thickness range of the alloy strip is 5 mu m-50 mm; preferably, the thickness of the alloy strip ranges from 5 μm to 5 mm; preferably, the thickness of the alloy strip ranges from 5 μm to 1 mm; more preferably, the thickness of the alloy strip ranges from 5 μm to 200 μm; more preferably, the thickness of the alloy strip is in the range of 5 μm to 20 μm.

Further, the width of the cross section of the alloy strip is more than 2 times of the thickness of the alloy strip; further, the length of the initial alloy strip is more than 10 times its thickness; preferably, the length of the initial alloy strip is more than 50 times its thickness; preferably, the length of the initial alloy strip is more than 100 times its thickness.

Further, the particle size range of the inner raw powder is 2 nm-3 mm; preferably, the particle size range of the endogenous powder is 2 nm-500 mu m; preferably, the particle size range of the inner raw powder is 2 nm-99 μm; more preferably, the particle size of the inner raw powder is in the range of 2nm to 10 μm; more preferably, the particle size of the inner raw powder is in the range of 2nm to 1 μm; more preferably, the particle size range of the inner raw powder is 2nm to 200 nm; more preferably, the particle size of the inner raw powder is in the range of 2nm to 100 nm.

Further, the shape of the endogenous powder comprises at least one of a dendrite shape, a spherical shape, a nearly spherical shape, a cube shape, a cake shape, and a bar shape.

Further, the proportion of the number of single crystal particles in the endogenous powder in the alloy strip in the total number of the endogenous powder is not less than 60%.

Further, the volume percentage of the inner green powder in the alloy strip does not exceed 50%.

Furthermore, z1 is more than or equal to 2z2, and z2 is more than or equal to 0 and less than or equal to 1.5 percent;

preferably, 3z2< z1, and 0< z2 ≦ 1.5%;

more preferably, 3z2< z1, and 0< z2 ≦ 0.75%.

The technical scheme of the invention has the following beneficial effects:

firstly, through ingenious alloy design, phase separation occurs when an initial alloy melt is solidified, endogenous particles with certain particle size target components can be formed in the solidification process of the initial alloy melt, and the endogenous particles can be separated through the subsequent process. In general, nano-metal particles can be relatively easily prepared by a bottom-up chemical method, such as chemical reduction, but are difficult to prepare when the size of the particles is increased to several hundreds of nanometers or even micrometers. Metal particles of several tens or several hundreds of micrometers can be relatively easily prepared by a top-down physical method such as an atomization method, a ball milling method, etc., but are also difficult to prepare when the size of the particles is reduced to several hundreds of nanometers to several micrometers. The technical scheme of the invention can very easily prepare nano-scale, submicron-scale, micron-scale and even millimeter-scale target metal powder particles according to the difference of the cooling speed in the solidification process of the initial alloy strip, breaks through the technical difficulties and has great advantages.

Secondly, the method realizes the purpose of obtaining the high-purity target powder material by using the low-purity raw materials, points out a new way for preparing the high-purity powder material by using the low-purity raw materials, and has positive significance. The purity of the target powder material is improved mainly by the following three mechanisms: 1) the main element (such as RE rare earth element) of the high-activity matrix has the function of absorbing the impurity element of the initial alloy melt. Because the matrix elements are generally high-activity and low-melting-point elements, the matrix elements have extremely strong affinity with the impurity elements T in the melting and solidification processes of the alloy melt, so that the impurity elements T in the initial alloy melt can enter more matrix phases mainly composed of matrix phase main elements or form slag with the matrix main elements in a melt state and are separated from the alloy melt to be removed; 2) in the process of growing the phase nucleation of the dispersed particles separated out endogenously, the impurity element T can be discharged into the residual melt. As long as the dispersed particle phase precipitated endogenously in the solidification process is not precipitated later than the matrix phase, impurities of the dispersed particle phase are concentrated in the last solidified part of the melt, namely the part of the melt which mainly consists of the main elements of the matrix phase and is solidified to form the matrix phase. 3) Due to the existence of the second phase matrix, impurities related to the crucible, which enter the melt due to the interaction between the crucible and the melt in the melting process, are generally concentrated in the second phase matrix, so that the requirement on the crucible in the melting process is further reduced, and the production cost is greatly reduced.

Third, a target metal powder mainly composed of single crystal particles can be obtained. Single crystal powders can achieve a number of significant and beneficial effects compared to polycrystalline powders. In the process of solidifying the initial alloy melt, each endogenous dispersed particle grows from a certain position in the melt according to a specific atomic arrangement mode after nucleation. By controlling the volume percentage content of the dispersed particle phase in the initial alloy strip not to exceed 50 percent, the combination and growth among the endogenous particles are difficult to occur under the condition that each endogenous particle can be dispersed and distributed. The respective, diffusely distributed particle phase finally obtained is therefore mostly a single crystalline phase. Even if the dendrite particles are large to tens of micrometers or millimeters, the growth direction of each secondary dendrite is in a certain phase relation with the growth direction of the main dendrite, and the dendrite particles still belong to single crystal particles. In the case of a polycrystalline material, since a grain boundary generally easily contains an impurity element which is discharged from the inside of the grain during solidification, it is difficult to obtain a high-purity polycrystalline powder material. When the target metal powder is mainly composed of single crystal particles, the purity thereof is inevitably secured. Furthermore, the surface atoms of the single crystal grains have specific arrangements, such as (111) plane arrangement, and the like, and the specific arrangements can endow the target metal powder with special mechanical, physical and chemical properties, thereby generating beneficial effects.

Fourthly, when the average composition of the initial alloy melt is as described in combination (4) of step S1, solid solution of Al element in the metal or alloy material containing W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti, etc. is achieved. In the above alloy materials, the addition of Al has a very important role. For example, the most widely used titanium alloy, Ti6Al4V alloy, is currently used. For the Ti6Al4V alloy powder, the Ti6Al4V alloy powder is generally obtained by smelting Ti6Al4V alloy melt and then carrying out atomization powder preparation technology. Due to the limitation of the atomization powder-making technology, it is difficult to obtain ultrafine Ti6Al4V alloy powder, and even nanometer-sized Ti6Al4V alloy powder cannot be obtained by the atomization powder-making technology. Therefore, it is very important to realize the addition of the Al element to the Ti — V alloy by the "dephasing method" according to the present invention and to prepare Ti6Al4V alloy powders having various particle sizes. The invention finds that when an appreciable content of Al element (which may exceed 10 at.% or even higher) is added to an alloy composed of A (at least one of rare earth elements RE) and M (at least one of elements W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti, etc.), the Al element in the solidified structure of the alloy can exist in a matrix phase mainly composed of RE and a dispersed particle phase mainly composed of M at the same time through a certain content distribution relationship. Since the RE-Al matrix phase can be easily removed by acid reaction, and Al in dispersed Al-containing particles mainly containing M is protected by the inert M element and cannot be easily removed by acid reaction (for example, Ti6Al4V alloy has good acid corrosion resistance), the preparation of Al-containing titanium alloy powder by removing the matrix phase by acid reaction is possible.

Fifthly, the alloy strip composed of the inner raw powder and the cladding body (matrix phase) creatively utilizes the in-situ generated matrix phase to wrap the inner raw powder, so that the high purity and the high activity of the inner raw powder are maintained. Particularly, the metal or alloy powder prepared by the traditional chemical method or physical method, especially the nano powder with active specific surface, is easy to be naturally oxidized, and faces the problem of difficult powder storage. In order to solve the problem, according to the technical scheme, after the alloy strip composed of the endogenous metal powder and the cladding (matrix phase) is prepared, the cladding is not removed urgently, and the endogenous metal powder is directly protected from natural oxidation by the cladding. The alloy strip formed by the endogenous metal powder and the cladding body can be directly used as a raw material for downstream production, and therefore, the alloy strip has the potential of becoming a special product. When high-purity powder is required to be used in downstream production, the endogenous metal powder can be released from the cladding body in the alloy strip at a proper time and in a proper environment according to the characteristics of the next process, and then the released endogenous powder enters the next production flow in a shortest time as possible, so that the possibility that the endogenous metal powder is polluted by impurities such as oxygen is greatly reduced. For example, when the endogenous metal powder is a nano powder, the resin-based composite material to which the endogenous metal powder is added can be prepared with high activity by compounding the resin with the endogenous metal powder simultaneously with or immediately after the endogenous metal powder is released from the coating body.

Sixth, the solid alloy obtained by solidification in the step S2 is in a ribbon shape, which ensures uniformity of product shape and feasibility of mass production. When the alloy strip is a thin alloy strip, the alloy strip can be prepared by a strip throwing method, the alloy thin strip with uniform thickness can be obtained as long as the flow of the alloy melt flowing to the rotating roller is kept fixed and the rotating speed of the rotating roller is fixed, and the preparation process can be continuously carried out, thereby being beneficial to large-scale production. When the alloy strip is a thick alloy strip, the alloy strip can be prepared by a mature continuous casting method, the continuous casting principle is similar to the melt-spinning principle, a continuous thick strip with uniform thickness can be obtained through a melt, the preparation process can be continuously carried out, and the large-scale production is facilitated. When the alloy strips are uniform in thickness, the cooling speed is uniform, and the obtained dispersed particles are uniform in granularity. In contrast, if the solidified alloy is in the form of an ingot, the ingot generally has a uniform thickness and no significant length or end point, which generally results in difficulty in dissipating heat from the internal melt, and is likely to obtain abnormally large endogenous particles, which is only required when the large endogenous particles are simply collected and purified. And the continuous production of the common cast ingot is difficult. Therefore, the alloy strip is obtained through solidification, and is suitable for preparing powder materials through a phase removal method.

Therefore, the preparation method has the characteristics of simple process, easy operation and low cost, can be used for preparing various high-purity powder materials in nano-scale, submicron-scale and micron-scale, and has good application prospects in the fields of catalytic materials, powder metallurgy, composite materials, wave-absorbing materials, sterilizing materials, magnetic materials, metal injection molding, 3D printing, coatings and the like.

Alternatively, the present invention also provides a method for preparing high purity metal powder, comprising the steps of:

the method comprises the following steps: selecting an initial alloy, melting the initial alloy raw materials according to the initial alloy component proportion to obtain a uniform alloy melt, and then preparing the alloy melt into an alloy strip through a rapid solidification technology;

when the component proportion of the initial alloy is A_aM_bWhen A is selected from 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 and Lu, M is selected from at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti, Fe, Co, Ni, Cu, Ag, Si and Ge, and M does not solely contain Fe; wherein a and b represent the atom percentage content of the corresponding constituent elements, 45%<b is less than or equal to 75 percent, and a + b is 100 percent; and A is_aM_bThe solidification structure of the alloy strip does not contain an intermetallic compound composed of A and M, and the solidification structure of the alloy strip consists of a matrix phase with the component of A and a dispersed particle phase with the component of M;

when it is at homeThe initial alloy comprises La_aFe_bWhen the ratio is higher than that of the total amount of the components, 40 percent<b is less than or equal to 75 percent, a + b is 100 percent, and a and b represent the atom percentage content of corresponding constituent elements; and La_aFe_bThe solidification structure of the alloy strip does not contain an intermetallic compound composed of La and Fe, and the solidification structure of the alloy strip consists of a matrix phase with the component of La and a dispersed particle phase with the component of Fe;

when the component proportion of the initial alloy is A_aM_bAl_cWhen in use, A is selected from at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb and Lu, Al is aluminum, and M is selected from at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti, Fe, Co and Ni; wherein a, b and c respectively represent the atom percentage content of the corresponding constituent elements, 35%<b is less than or equal to 75 percent, c is more than or equal to 0.1 percent and less than or equal to 30 percent, and a + b + c is 100 percent; and A is_aM_bAl_cThe alloy strip does not contain an intermetallic compound formed of A and M in its solidification structure, and its solidification structure contains M as a component_x1Al_y1And component A_x2Al_y2The matrix phase of (a); wherein x1, y1, x2 and y2 respectively represent the atom percentage content of corresponding constituent elements, and y1 is more than or equal to 0.1% and less than or equal to 25%, y2 is more than or equal to 0.1% and less than or equal to 35%, x1+ y1 is 100%, and x2+ y2 is 100%;

in the solidification process of the initial alloy melt, impurity elements in the alloy melt and impurity elements introduced in the solidification process are enriched in the matrix phase, so that the dispersed particle phase is purified;

step two: and removing the matrix phase in the alloy strip and reserving the dispersed particle phase, and removing impurity elements enriched in the matrix phase to obtain the high-purity target metal powder consisting of the dispersed particles.

By adopting the technical scheme, the preparation of the superfine metal powder with low impurity content can be realized. In the aspect of fine powder obtaining, the higher the solidification rate of the alloy melt, the smaller the dispersed particle phase in the obtained alloy strip solidification structure. Therefore, the invention can respectively obtain nano-scale, submicron-scale and micron-scale dispersed particle phases by controlling the size of the solidification rate, and then obtain the target metal powder with corresponding particle size by removing the matrix phase, thereby greatly reducing the preparation cost of the superfine metal powder. In the aspect of impurity control, because the matrix phase generally consists of low-melting-point and high-activity elements, impurity elements are enriched in the matrix phase in the processes of alloy smelting and rapid solidification, so that a dispersed particle phase is purified and protected, and the preparation of high-purity target metal powder is realized.

In addition, in the selection of the alloy composition ratio, although A is mentioned_aM_b、La_aFe_bAnd A_aM_bAl_cThe maximum value of b (atomic percentage content) in the alloy is 75%, but this does not affect the dispersed precipitation of dispersed particles in the matrix phase. Because the matrix phase of the present invention is composed primarily of large atomic elements, its volume percent content in the alloy strip can be much higher than its atomic percent content even if the atomic percent content of the matrix phase is less than 50%. Such as La₂₅Fe₇₅In the solidification structure of the alloy (atomic ratio component), the volume percentage content of the La matrix can still reach 51 percent. When the solidification rate of the alloy melt is fast enough and the Fe particles are in a nanometer level, La₂₅Fe₇₅Fe particles in the alloy solidification structure can not be combined and grown up, and can still be dispersed and separated out.

Further, in order to ensure the dispersed precipitation of dispersed particles, the volume percentage content of the matrix phase in the alloy strip is not lower than 44%.

Further, the rapid solidification technology comprises an alloy melt metal roller melt spinning method, and the solidification rate of the alloy melt is 50K/s-10⁷K/s. When the solidification rate is higher than 10⁵When K/s, nano-scale dispersed particle phase can be obtained; when the solidification rate is 10³K/s～10⁵When K/s, submicron-grade dispersed particle phase can be obtained; when the solidification rate is less than 10³At K/s, micron-sized dispersed particle phase can be obtained.

Further, the thickness of the alloy strip is 5 mu m-5 mm.

Further, the shape of the dispersed particle phase comprises at least one of a dendritic form, a spherical form, a nearly spherical form, a square form, a cake form and a rod form, and the particle size ranges from 2nm to 200 μm.

Further, the impurity elements in the alloy melt and the impurity elements introduced during solidification comprise at least one of H, O, N, S, P, F, Cl, I and Br.

Further, the method for removing the matrix phase in the alloy strip comprises the following steps: at least one of acid reaction removal, alkali reaction removal and vacuum volatilization removal. The composition and concentration of the acid solution and the alkali solution are not particularly limited as long as the matrix phase can be removed and the dispersed particle phase is retained.

Further, the method for removing the matrix phase in the alloy strip comprises the steps of natural oxidation-pulverization and peeling removal of the matrix phase.

Further, the particle size range of the high-purity target metal powder consisting of the dispersed granular phase is 2 nm-200 μm.

Further, the shape of the high-purity target metal powder includes a spherical shape, a nearly spherical shape, a dendritic shape, a rod shape, and a plate shape.

Further, the total content of H, O, N, S, P, F, Cl, I and Br in the high-purity target metal powder is lower than 2000 ppm.

The advantageous aspects of the above-mentioned alternative technical features are explained in further detail below:

firstly, the invention can respectively obtain nano-scale, submicron-scale and micron-scale dispersed particle phases by controlling the solidification rate of the melt, and then obtain target metal powder with corresponding particle size by removing the matrix phase, thereby greatly reducing the preparation cost of the superfine metal powder.

Secondly, because the impurity elements in the melt are easy to combine with the matrix during the solidification process of the melt, the impurity elements are enriched with the matrix phase. Therefore, even if non-high-purity raw materials and a common crucible are adopted, or other gas impurity elements enter a melt in the smelting process, a dispersed particle phase with low impurity content and target metal powder can be obtained, and the production cost of the high-purity powder material is greatly reduced.

Third, when the initial alloy A_aM_bOr A_aM_bAl_cWhen M is a combination of multiple elements, the obtained dispersed granular phase also consists of multiple elements, so that the preparation of the target alloy powder consisting of the dispersed granular phase is simpler, more convenient and more feasible, and the component range and the application field of the target alloy powder are greatly expanded.

Finally, in the second step of the invention, according to the characteristic that the matrix phase in the alloy strip is a low-melting-point and high-activity component, the matrix phase can be removed by at least one of the following three ways, and the dispersed particle phase is retained: 1) removing the matrix phase by an acid solution or alkali solution corrosion method, and simultaneously keeping the dispersed particle phase; 2) for the extremely volatile matrix phase, removing the matrix phase by a vacuum volatilization method, and simultaneously keeping the dispersed particle phase; 3) for a matrix phase which is extremely easy to oxidize naturally, such as a matrix phase with a main component of rare earth elements, the matrix phase can be changed into pulverized oxide powder in a natural oxidation-pulverization mode of the matrix phase elements, and then the dispersed particle phase is further separated from a product of matrix pulverization to obtain the target metal powder.

Therefore, the preparation method has the characteristics of simple process, easy operation and low cost, can be used for preparing various high-purity powder materials in nano-scale, submicron-scale and micron-scale, and has good application prospects in the fields of catalysis, powder metallurgy, composite materials, sterilization, metal injection molding, 3D printing and other additive manufacturing.

Detailed Description

Hereinafter, the method for preparing the high purity powder material will be further described by the following specific examples.

Example 1

The embodiment provides a preparation method of nano CrV powder, which comprises the following steps:

selecting Zn as the formula of atomic ratio₅₄Cr₂₃V₂₃The alloy is prepared by weighing raw materials according to a formula, uniformly melting the initial alloy raw materials, and then carrying out melt spinning on the initial alloy raw materials by a copper roller by a strip spinning technology of 10 DEG C⁶The solidification rate of K/s is prepared into Zn with the thickness of 20 mu m₅₄Cr₂₃V₂₃Alloy strip. The solidification structure of the alloy strip is composed of a matrix phase containing Zn and a matrix phase containing Cr as a major component₅₀V₅₀In which Cr is present in the form of dispersed particulate phase of₅₀V₅₀The shape of the particles is nearly spherical, and the particle size range is 3 nm-200 nm. Cr (chromium) component₅₀V₅₀The volume content of the particles in the alloy strip is about 42%; the impurity elements are enriched in the Zn matrix in the solidification process.

Removing Zn in the alloy strip by vacuum heat treatment to remove Cr difficult to volatilize in the alloy strip₅₀V₅₀The particles are separated out to obtain the nano Cr₅₀V₅₀Powder with grain size of 3-200 nm and nanometer Cr₅₀V₅₀The total content of H, O, N, S, P, F, Cl, I and Br in the powder is less than 1500 ppm.

Example 2

selecting Zn as the formula of atomic ratio₅₄Cr₂₃V₂₃The alloy is prepared by weighing raw materials according to a formula, melting the initial alloy raw materials uniformly, and then carrying out strip spinning on the initial alloy raw materials by a copper roller by about 10⁶The solidification rate of K/s is prepared into Zn with the thickness of 20 mu m₅₄Cr₂₃V₂₃Alloy strip. The solidification structure of the alloy strip is composed of a matrix phase containing Zn and a matrix phase containing Cr as a major component₅₀V₅₀In which Cr is present in the form of dispersed particulate phase of₅₀V₅₀The shape of the particles is nearly spherical, and the particle size range is 3 nm-200 nm. Cr (chromium) component₅₀V₅₀The volume content of the particles in the alloy strip is about 42%; the impurity elements are enriched in the Zn matrix in the solidification process.

Dissolving and removing Zn in the alloy strip by sodium hydroxide alkali solution to ensure that Cr in the alloy strip which is difficult to react with the alkali solution is difficult to react₅₀V₅₀The particles are separated out to obtain the nano Cr₅₀V₅₀Powder with grain size of 3-200 nm and nanometer Cr₅₀V₅₀The total content of H, O, N, S, P, F, Cl, I and Br in the powder is lowAt 1500 ppm.

Example 3

The embodiment provides a preparation method of nano Ti powder, which comprises the following steps:

the formula with atomic ratio is Ce₃₀Ti₇₀The alloy is prepared by weighing raw materials according to a formula, melting the initial alloy raw materials uniformly, and then carrying out strip spinning on the initial alloy raw materials by a copper roller by about 10⁷The solidification rate of K/s is used for preparing Ce with the thickness of 15 mu m₃₀Ti₇₀Alloy strip. The solidification structure of the alloy strip consists of a matrix phase with Ce as a component and a dispersed granular phase with Ti as a large amount of components, wherein the Ti granules are nearly spherical, and the grain size range is 3-150 nm. The volume content of Ti particles in the alloy strip is about 55%; impurity elements are enriched in the Ce matrix in the solidification process.

And dissolving and removing the Ce matrix in the alloy strip through a hydrochloric acid solution, so that Ti particles which are difficult to react with the acid solution in the alloy strip are separated out, and the nano Ti powder is obtained, wherein the particle size range of the nano Ti powder is 3-150 nm, and the total content of H, O, N, S, P, F, Cl, I and Br in the nano Ti powder is lower than 1500 ppm.

Example 4

The embodiment provides a preparation method of nano Ti-Zr-Hf-Nb-Ta powder, which comprises the following steps:

the formula with atomic ratio is Ce₄₀(Ti₂₀Zr₂₀Hf₂₀Nb₂₀Ta₂₀)₆₀The alloy is prepared by weighing raw materials according to a formula, melting the initial alloy raw materials uniformly, and then carrying out strip spinning on the initial alloy raw materials by a copper roller by about 10⁷The solidification rate of K/s is used for preparing Ce with the thickness of 15 mu m₄₀(Ti₂₀Zr₂₀Hf₂₀Nb₂₀Ta₂₀)₆₀Alloy strip. The solidification structure of the alloy strip is composed of a matrix phase with Ce and a great deal of Ti₂₀Zr₂₀Hf₂₀Nb₂₀Ta₂₀In the form of a dispersed particulate phase of (1), wherein Ti₂₀Zr₂₀Hf₂₀Nb₂₀Ta₂₀The shape of the particles is nearly spherical, and the particle size range is 3 nm-150 nm. T isi₂₀Zr₂₀Hf₂₀Nb₂₀Ta₂₀The volume content of the particles in the alloy strip is about 50%; impurity elements are enriched in the Ce matrix in the solidification process.

Dissolving and removing the Ce matrix in the alloy strip by using a hydrochloric acid solution to ensure that Ti which is difficult to react with the acid solution in the alloy strip₂₀Zr₂₀Hf₂₀Nb₂₀Ta₂₀The particles are separated out to obtain the nano Ti₂₀Zr₂₀Hf₂₀Nb₂₀Ta₂₀Powder with the grain size of 3 nm-150 nm and nano Ti₂₀Zr₂₀Hf₂₀Nb₂₀Ta₂₀The total content of H, O, N, S, P, F, Cl, I and Br in the powder is less than 1500 ppm.

Example 5

The embodiment provides a preparation method of nano-submicron Ti-Nb powder, which comprises the following steps:

the formula with atomic ratio is Ce₅₀(Ti₅₀Nb₅₀)₅₀The alloy is prepared by weighing raw materials according to a formula, melting the initial alloy raw materials uniformly, and then carrying out strip spinning on the initial alloy raw materials by a copper roller by about 10⁴The solidification rate of K/s is used for preparing Ce with the thickness of 150 mu m₅₀(Ti₅₀Nb₅₀)₅₀Alloy strip. The solidification structure of the alloy strip is composed of a matrix phase with Ce and a great deal of Ti₅₀Nb₅₀In the form of a dispersed particulate phase of (1), wherein Ti₅₀Nb₅₀The shape of the particles is nearly spherical, and the particle size range is 50 nm-1 mu m. Ti₅₀Nb₅₀The volume content of the particles in the alloy strip is about 34%; impurity elements are enriched in the Ce matrix in the solidification process.

Dissolving and removing the Ce matrix in the alloy strip by using a hydrochloric acid solution to ensure that Ti which is difficult to react with the acid solution in the alloy strip₅₀Nb₅₀The particles are separated out to obtain the nano-submicron grade Ti₅₀Nb₅₀Powder with a particle size ranging from 50nm to 1 μm and Ti₅₀Nb₅₀The total content of H, O, N, S, P, F, Cl, I and Br in the powder is less than 1500 ppm.

Example 6

The embodiment provides a preparation method of micron Ti-Co powder, which comprises the following steps:

selecting Gd as an atomic ratio formula₅₀(Ti₅₀Co₅₀)₅₀The alloy is prepared by weighing raw materials according to a formula, uniformly melting the initial alloy raw materials, and preparing Gd with the thickness of 3mm by a copper roller melt-spinning technology at a solidification rate of about 150K/s₅₀(Ti₅₀Co₅₀)₅₀Alloy strip. The alloy strip has a solidification structure composed of a matrix phase containing Gd and a large amount of Ti₅₀Co₅₀In the form of a dispersed particulate phase of (1), wherein Ti₅₀Co₅₀The shape of the particles is dendritic, and the particle size range is 1-100 mu m. Ti₅₀Co₅₀The volume content of the particles in the alloy strip is about 30%; impurity elements are enriched in the Gd matrix in the solidification process.

Dissolving and removing Gd matrix in the alloy strip through a dilute hydrochloric acid solution, so that Ti in the alloy strip, which is difficult to react with the dilute hydrochloric acid solution₅₀Co₅₀The particles are separated out to obtain the micron-sized Ti₅₀Co₅₀Powder having a particle size ranging from 1 to 100 μm and Ti₅₀Co₅₀The total content of H, O, N, S, P, F, Cl, I and Br in the powder is less than 1500 ppm.

Example 7

The embodiment provides a preparation method of submicron-micron Fe powder, which comprises the following steps:

selecting an atomic ratio formula of La₄₀Fe₆₀The alloy is prepared by weighing raw materials according to a formula, melting the initial alloy raw materials uniformly, and then carrying out strip spinning on the initial alloy raw materials by a copper roller by about 10³Solidification rate of K/s La with a thickness of 500 μm was prepared₄₀Fe₆₀Alloy strip. The solidification structure of the alloy strip consists of a matrix phase with La as a component and a dispersed particle phase with Fe as a large component, wherein the Fe particles are approximately spherical, and the particle size range is 500 nm-5 mu m. The volume content of Fe particles in the alloy strip is about 32%; the impurity elements are enriched in the La group in the solidification processIn the body.

La matrix is subjected to natural oxidation-pulverization process in air₄₀Fe₆₀La in the alloy is changed into lanthanum oxide, and then Fe particles are separated from the lanthanum oxide by utilizing the magnetic property of Fe, so that submicron-micron Fe powder is obtained, the particle size range of the submicron-micron Fe powder is 500 nm-5 mu m, and the total content of H, O, N, S, P, F, Cl, I and Br in the Fe powder is lower than 1500 ppm.

Example 8

The embodiment provides a preparation method of nano Fe powder, which comprises the following steps:

selecting an atomic ratio formula of La₂₅Fe₇₅The alloy is prepared by weighing raw materials according to a formula, melting the initial alloy raw materials uniformly, and then carrying out strip spinning on the initial alloy raw materials by a copper roller by about 10⁶Solidification rate of K/s La with a thickness of 20 μm was prepared₂₅Fe₇₅Alloy strip. The solidification structure of the alloy strip consists of a matrix phase with La as a component and a dispersed particle phase with Fe as a large component, wherein the Fe particles are approximately spherical, and the particle size range is 3-200 nm. The volume content of Fe particles in the alloy strip is about 49%; and impurity elements are enriched in the La matrix in the solidification process.

La matrix is subjected to natural oxidation-pulverization process in air₂₅Fe₇₅La in the alloy is changed into lanthanum oxide, and then the magnetic property of Fe is utilized to separate nano Fe particles from the lanthanum oxide, so that nano Fe powder is obtained, the particle size range of the nano Fe powder is 3-200 nm, and the total content of H, O, N, S, P, F, Cl, I and Br in the Fe powder is lower than 1800 ppm.

Example 9

The embodiment provides a preparation method of submicron-micron FeNi powder, which comprises the following steps:

the atomic ratio formula is selected to be Li₅₀(Fe₅₀Ni₅₀)₅₀The alloy is prepared by weighing raw materials according to a formula, melting the initial alloy raw materials uniformly, and then carrying out strip spinning on the initial alloy raw materials by a copper roller by about 10³K/s solidification Rate Li with a thickness of 500 μm was prepared₅₀(Fe₅₀Ni₅₀)₅₀Alloy strip. The alloy stripThe solidification structure of (2) is composed of a matrix phase containing Li and a large amount of Fe₅₀Ni₅₀In the form of a dispersed particulate phase of (1), wherein Fe₅₀Ni₅₀The shape of the particles is nearly spherical or dendritic, and the particle size range is 500 nm-5 mu m. Fe₅₀Ni₅₀The volume content of the particles in the alloy strip is about 34%; impurity elements are enriched in the Li matrix during the solidification process.

By natural oxidation-pulverization process of Li matrix in air₅₀(Fe₅₀Ni₅₀)₅₀Li in the alloy is changed into oxide powder and then Fe is utilized₅₀Ni₅₀Magnetic property of (2) Fe₅₀Ni₅₀Separating the particles from the oxidation product of Li to obtain submicron-micron Fe₅₀Ni₅₀Powder with a particle size ranging from 500nm to 5 μm and Fe₅₀Ni₅₀The total content of H, O, N, S, P, F, Cl, I and Br in the powder is less than 1800 ppm.

Example 10

The embodiment provides a preparation method of nano Ti-Al-V powder, which comprises the following steps:

the formula with atomic ratio is Ce₃₀Al₁₂(Ti₉₆V₄)₅₈The alloy is prepared by weighing raw materials according to a formula, melting the initial alloy raw materials uniformly, and then carrying out strip spinning on the initial alloy raw materials by a copper roller by about 10⁶K/s solidification rate to prepare Ce with thickness of 20 mu m₃₀Al₁₂(Ti₉₆V₄)₅₈Alloy strip. The alloy strip has a solidification structure composed of Ce₈₅Al₁₅The matrix phase of (A) and a large amount of (Ti)₉₆V₄)₉₀Al₁₀In the form of a dispersed particulate phase of (A), wherein (Ti)₉₆V₄)₉₀Al₁₀The shape of the particles is nearly spherical, and the particle size range is 3 nm-200 nm. (Ti)₉₆V₄)₉₀Al₁₀The volume content of the particles in the alloy strip is about 52%; impurity elements are enriched in Ce in the solidification process₈₅Al₁₅In the matrix.

Ce is separated by dilute hydrochloric acid solution₃₀Al₁₂(Ti₉₆V₄)₅₈Ce in alloy strip₈₅Al₁₅Removal of matrix phase by reaction, making it difficult to react with dilute hydrochloric acid solution (Ti)₉₆V₄)₉₀Al₁₀The particles are separated out to obtain the nano (Ti)₉₆V₄)₉₀Al₁₀Powder with a particle size in the range of 3nm to 200nm and a nano (Ti)₉₆V₄)₉₀Al₁₀The total content of H, O, N, S, P, F, Cl, I and Br in the powder is less than 1400 ppm.

Example 11

The embodiment provides a preparation method of submicron-micron Ti-Al-V powder, which comprises the following steps:

the formula with atomic ratio is Ce₃₀Al₁₂(Ti₉₆V₄)₅₈The alloy is prepared by weighing raw materials according to a formula, melting the initial alloy raw materials uniformly, and then carrying out strip spinning on the initial alloy raw materials by a copper roller by about 10³K/s solidification Rate Ce prepared to a thickness of about 500 μm₃₀Al₁₂(Ti₉₆V₄)₅₈Alloy strip. The alloy strip has a solidification structure composed of Ce₈₅Al₁₅The matrix phase of (A) and a large amount of (Ti)₉₆V₄)₉₀Al₁₀In the form of a dispersed particulate phase of (A), wherein (Ti)₉₆V₄)₉₀Al₁₀The shape of the particles is nearly spherical or dendritic, and the particle size range is 500 nm-5 mu m. (Ti)₉₆V₄)₉₀Al₁₀The volume content of the particles in the alloy strip is about 52%; impurity elements are enriched in Ce in the solidification process₈₅Al₁₅In the matrix.

Ce is separated by dilute hydrochloric acid solution₃₀Al₁₂(Ti₉₆V₄)₅₈Ce in alloy strip₈₅Al₁₅Removal of matrix phase by reaction, making it difficult to react with dilute hydrochloric acid solution (Ti)₉₆V₄)₉₀Al₁₀Separating out the particles to obtain submicron-micron (Ti)₉₆V₄)₉₀Al₁₀Powder with particle size of 500 nm-5 μm and nanometer size (Ti)₉₆V₄)₉₀Al₁₀The total content of H, O, N, S, P, F, Cl, I and Br in the powder is less than 1400 ppm.

Example 12

sponge Ti and rare earth Ce raw materials with the atom percentage contents of T (containing O, H, N, P, S, F, Cl, Br and I) impurity elements of 3 at.% and 2.5 at.% are selected. Fully melting sponge Ti and rare earth Ce according to the molar ratio of Ce to Ti of about 1:1 to obtain the alloy with the atomic percentage composition mainly comprising Ce_47.25Ti_47.25T_2.5The homogeneous initial alloy melt of (a).

Strip by copper roll strip casting technique at about 10⁶K/s solidification Rate the initial alloy melt was prepared as Ce with a thickness of 15 μm_47.25Ti_47.25T_2.5Alloy strip. The alloy strip has a solidification structure mainly composed of Ce_95.2T_4.8A matrix phase of a major component of mainly Ti_99.8T_0.2In the form of a dispersed particulate phase of (1), wherein Ti_99.8T_0.2The dispersed particles are nearly spherical and have a particle size ranging from 3nm to 150 nm. Ti_99.8T_0.2The volume content of dispersed particles in the alloy strip is about 34%;

obtained Ce_47.25Ti_47.25T_2.5The alloy strip is an alloy strip formed by the inner raw powder and the cladding body.

Ce in alloy strip by dilute acid solution_95.2T_4.8Matrix is removed, so that Ti in the alloy strip which is difficult to react with dilute acid solution is removed_99.8T_0.2The particles are separated out to obtain Ti_99.8T_0.2The nano powder has the particle size range of 3-150 nm, and the total content of O, H, N, P, S, F, Cl, Br and I is 0.2 at.%.

Under a protective atmosphere, the main component is Ti_99.8T_0.2The nano powder is mixed with epoxy resin and other coating components to prepare the nano Ti modified polymer anticorrosive coating.

Example 13

The embodiment provides a preparation method of micro dendrite Ti-Nb powder, which comprises the following steps:

sponge Ti, Nb sheets and rare earth Gd raw materials with the atomic percentage contents of T (containing O, H, N, P, S, F, Cl, Br and I) impurity elements of 3 at.%, 1 at.% and 2.5 at.% are selected. Melting the raw materials of the alloy according to the mol ratio of Gd to Ti to Nb of about 2:1:1 to obtain the alloy with the atomic percentage of the main component of Gd_48.75Ti_24.5Nb_24.5T_2.25The homogeneous initial alloy melt of (a).

About 10 by the copper roller melt spinning technique³The initial alloy melt is prepared into Gd with the thickness of 300 mu m at the solidification rate of K/s_48.75Ti_24.5Nb_24.5T_2.25Alloy strip. The solidified structure of the alloy strip consists of Gd as the main component in atomic percentage_95.9T_4.1A matrix phase of a major component of mainly Ti_49.85Nb_49.85T_0.3The dispersed particulate phase of (a). Wherein Ti_49.85Nb_49.85T_0.3The dispersed particles are dendritic and have a particle size of 1-50 μm. Ti_49.85Nb_49.85T_0.3The dispersed particles are present in the alloy strip in an amount of about 35% by volume;

gd in the alloy strip is treated by dilute acid solution_95.9T_4.1Matrix phase is removed, so that Ti in the alloy strip which is difficult to react with dilute acid solution is removed_49.85Nb_49.85T_0.3The dispersed particles are separated out to obtain the main component Ti_49.85Nb_49.85T_0.3The particle size of the micro-rice flour is 1-50 mu m, and the total content of O, H, N, P, S, F, Cl, Br and I is 0.3 at.%.

Mixing the above Ti_49.85Nb_49.85T_0.3The alloy powder is sieved by a screen of 1000 meshes and 2000 meshes to obtain graded Ti with the particle size ranges of 53-13 mu m and 13-6.5 mu m respectively_49.85Nb_49.85T_0.3And (3) alloy powder. Respectively carrying out plasma spheroidizing treatment on the mixture to further prepare theTi-Nb-T alloy powder with particle size ranges of 53-13 μm and 13-6.5 μm and shape close to spherical shape. The obtained spherical Ti-Nb-T alloy powder can be used in the fields of 3D metal printing, metal injection molding and powder metallurgy.

Example 14

The embodiment provides a preparation method of nano TiNi powder, which comprises the following steps:

selecting a Ti raw material, a Ni sheet and a rare earth Gd raw material, wherein the atom percentage contents of impurity elements of T (including O, H, N, P, S, F, Cl, Br and I) are respectively 1 at.%, 0.5 at.% and 2.5 at.%. Melting the initial raw material according to a molar ratio of Gd to Ti to Ni of about 2:1:1 to obtain a mixture with the atomic percentage composition mainly comprising Gd_48.8Ti_25.25Ni_25.25T_1.7The homogeneous initial alloy melt of (a).

About 10 by the copper roller melt spinning technique⁶The initial alloy melt is prepared into Gd with the thickness of 15 mu m at the solidification rate of K/s_48.8Ti_25.25Ni_25.25T_1.7Alloy strip. The alloy strip has a solidification structure mainly composed of Gd_96.8T_3.2A matrix phase of a major component of mainly Ti_49.9Ni_49.9T_0.2Is a TiNi intermetallic compound, wherein Ti_49.9Ni_49.9T_0.2The dispersed particles are nearly spherical and have a particle size ranging from 3nm to 150 nm. Ti_49.9Ni_49.9T_0.2The volume content of dispersed particles in the alloy strip is about 32%;

gd in the alloy strip is treated by dilute acid solution_96.8T_3.2Matrix is removed, so that Ti in the alloy strip which is difficult to react with dilute acid solution is removed_99.8T_0.2The particles are separated out to obtain Ti_49.9Ni_49.9T_0.2The nano powder has the particle size range of 3-150 nm, and the total content of O, H, N, P, S, F, Cl, Br and I is 0.2 at.%.

Example 15

selecting Fe sheets and rare earth La raw materials, wherein the atom percentage contents of impurity elements of T (including O, H, N, P, S, F, Cl, Br and I) are respectively 1 at.% and 2.5 at.%. Melting the alloy raw materials according to the molar ratio of La to Fe of about 1:2 to obtain the alloy with the main atomic percent of La_32.8Fe_65.7T_1.5The homogeneous initial alloy melt of (a).

About 10 by the copper roller melt spinning technique⁴K/s solidification rate the initial alloy melt is prepared into La with the thickness of 100 mu m_32.8Fe_65.7T_1.5Alloy strip. The solidification structure of the alloy strip consists of La as the main component in atomic percentage_95.9T_4.1A matrix phase of a large amount of a component mainly consisting of Fe_99.85T_0.15The dispersed particulate phase of (a). Wherein Fe_99.85T_0.15The dispersed particles are in the shape of nearly spherical or dendritic crystals, and the particle size range of the dispersed particles is 500 nm-3 mu m. Fe_99.85T_0.15The dispersed particles are present in the alloy strip in an amount of about 36% by volume;

la in alloy strip by dilute acid solution_95.9T_4.1Removing matrix phase, and removing Fe by using Fe magnetism_99.85T_0.15Rapidly separating dispersed particles from the acid solution to obtain the product with Fe as the main component_99.85T_0.15The particle size of the submicron-micron powder is 500 nm-3 mu m, and the total content of O, H, N, P, S, F, Cl, Br and I is 0.15 at.%.

Example 16

The embodiment provides a preparation method of nano Ti-V-Al alloy powder, which comprises the following steps:

sponge Ti, V blocks, rare earth Ce and Al raw materials with the atomic percentage contents of T (containing O, H, N, P, S, F, Cl) impurity elements of 1 at.%, 1 at.%, 2.5 at.%, and 0.2 at.% are selected. Fully melting the initial alloy raw materials according to a certain proportion to obtain the alloy with the atomic percentage composition mainly containing Ce_40.2(Ti₉₆V₄)_37.9Al_20.5T_1.4The initial alloy melt of (a).

About 10 by the copper roller melt spinning technique⁶K/s solidification rate to prepare Ce with thickness of 20 mu m from initial alloy melt_40.2(Ti₉₆V₄)_37.9Al_20.5T_1.4Alloy strip. The alloy strip has a solidification structure composed of Ce as the main component_73.2Al_24.3T_2.5A matrix phase of a major component of (Ti)₉₆V₄)₈₄Al_15.8T_0.2In the form of a dispersed particulate phase of (A), wherein (Ti)₉₆V₄)₈₄Al_15.8T_0.2The dispersed particles are nearly spherical and have a particle size ranging from 5nm to 200 nm. (Ti)₉₆V₄)₈₄Al_15.8T_0.2The volume content of dispersed particles in the alloy strip is about 33%;

ce in alloy strip by dilute acid solution_73.2Al_24.3T_2.5Matrix removal, making the alloy strip refractory to dilute acid solution reaction (Ti)₉₆V₄)₈₄Al_15.8T_0.2The particles are broken off to obtain (Ti)₉₆V₄)₈₄Al_15.8T_0.2The nano powder has the particle size range of 5-200 nm, and the total content of O, H, N, P, S, F, Cl, Br and I is 0.2 at.%.

Under a protective atmosphere, the main component is (Ti)₉₆V₄)₈₄Al_15.8T_0.2The nano powder is mixed with epoxy resin and other coating components to prepare the nano Ti alloy modified polymer anticorrosive coating.

The technical features of the embodiments described above may be arbitrarily combined, and for the sake of brevity, all possible combinations of the technical features in the embodiments described above are not described, but should be considered as being within the scope of the present specification as long as there is no contradiction between the combinations of the technical features.

The above-mentioned embodiments only express several embodiments of the present invention, and the description thereof is more specific and detailed, but not construed as limiting the scope of the invention. It should be noted that, for a person skilled in the art, several variations and modifications can be made without departing from the inventive concept, which falls within the scope of the present invention. Therefore, the protection scope of the present patent shall be subject to the appended claims.

Claims

1. The preparation method of the high-purity powder material is characterized by comprising the following steps of:

step S1, selecting initial alloy raw materials, melting the initial alloy raw materials according to the initial alloy component proportion, and obtaining a uniform initial alloy melt containing an impurity element T, wherein T comprises at least one of O, H, N, P, S, F, Cl, I and Br, and the average component of the initial alloy melt comprises any one of the following combinations:

combination (1): the average composition of the initial alloy melt is mainly A_a(M_xD_y)_bT_dWherein 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, and D comprises at least one of Fe, Co and Ni, wherein x and Y; a. b and d represent the atom percentage content of corresponding constituent elements, and a is more than or equal to 24.9 percent and less than or equal to 99.4 percent, b is more than or equal to 0.5 percent and less than or equal to 75 percent, and b is more than or equal to 0<d≤10％；10％≤x≤55％，45％≤y≤90％；

Combination (2): the average composition of the initial alloy melt is mainly A_aM_bT_dWherein A comprises 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 M comprises at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf and Ti; wherein a, b and d represent the atom percentage content of corresponding constituent elements, and a is more than or equal to 24.9 percent and less than or equal to 99.4 percent, b is more than or equal to 0.5 percent and less than or equal to 75 percent, and b is more than or equal to 0 percent<d≤10％；

Combination (3): the average composition of the initial alloy melt is mainly A_aM_bT_dWherein A contains at least one of Zn, Mg, Sn, Pb, Ga, In, Al, La, Ge, Cu, K, Na and LiM comprises at least one of B, Bi, Fe, Ni, Cu, Ag, Si, Ge, Cr and V, wherein a, B and d represent the atom percentage content of the corresponding constituent elements, and a is more than or equal to 24.9% and less than or equal to 59.9%, and 40%<b≤75％，0<d≤10％；

when the average composition of the initial alloy melt is step S1 combination (1), the composition of the dispersed particulate phase in the initial alloy strip is predominantly (M)_xD_y)_x1T_z1The average component of the matrix phase is mainly A_x2T_z2(ii) a And x1 is more than or equal to 98.5 percent<100％,0<z1≤1.5％；80％≤x2<100％,0<z2≤20％；z1<d<z2，2z1<z 2; x1, z1, x2 and z2 respectively represent the atom percentage content of the corresponding constituent elements;

when the average composition of the initial alloy melt is the combination (2) or the combination (3) of the step S1, the composition of the dispersed particle phase in the initial alloy strip is mainly M_x1T_z1The average component of the matrix phase is mainly A_x2T_z2(ii) a And x1 is more than or equal to 98.5 percent<100％,0<z1≤1.5％；80％≤x2<100％,0<z2≤20％；z1<d<z2，2z1<z2；x1、z1X2 and z2 represent the atom percentage content of the corresponding constituent elements respectively;

when the average composition of the initial alloy melt is the combination (4) of step S1, the composition of the dispersed particle phase in the initial alloy strip is mainly M_x1Al_y1T_z1The average component of the matrix phase is mainly A_x2Al_y2T_z2(ii) a X1 is more than or equal to 77.8 percent and less than or equal to 99.8 percent, y1 is more than or equal to 0.1 percent and less than or equal to 22 percent, and<z1≤1.5％；69.8％≤x2≤99.7％，0.2％≤y2≤30％，0<z2≤20％，z1<d<z2，2z1<z2，y1<y2, x1, y1, z1, x2, y2 and z2 respectively represent the atom percentage contents of the corresponding constituent elements;

2. The method of claim 1, wherein the source of the T impurity element in the initial alloy melt comprises: impurities are introduced into the initial alloy raw materials, and impurities are introduced into the atmosphere or the crucible in the smelting process.

3. The method of claim 1, wherein the starting alloy strip does not contain an intermetallic compound comprising a and M.

4. The method according to claim 1, wherein the number of single crystal grains of dispersed grains in the starting alloy strip is not less than 60% of the total number of dispersed grains.

5. The method for preparing a high purity powder material according to claim 1, wherein z1< d < z2, and 2z1< z 2.

6. The method for preparing a high-purity powder material according to claim 1, wherein the method for removing the matrix phase from the alloy strip comprises the following steps: at least one of acid reaction removal, alkali reaction removal, vacuum volatilization removal and matrix phase natural oxidation-pulverization and peeling removal.

7. The method of claim 1, wherein the high purity powder material has a particle size ranging from 2nm to 3 mm.

8. The method for preparing a high purity powder material according to claim 1, wherein the following step is further performed after step S3: and after screening the high-purity powder material, selecting the high-purity powder material with the particle size range of 5-200 mu m for plasma spheroidization to obtain the spherical high-purity powder material.

9. The use of the high purity powder material or the spherical high purity powder material according to any one of claims 1 to 8 in catalytic materials, powder metallurgy, composite materials, wave absorbing materials, bactericidal materials, magnetic materials, metal injection molding, 3D printing, coatings.

10. An alloy strip, comprising an inner green powder and a cladding; the solidification structure of the alloy strip comprises a matrix phase and a dispersed particle phase, wherein the matrix phase is the cladding body, and the dispersed particle phase is the endogenous powder; the melting point of the coating body is lower than that of the endogenous powder, and the endogenous powder is coated in the coating body;

1) the component of the internal powder in the alloy strip is mainly (M)_xD_y)_x1T_z1The average composition of the coating is mainly A_x2T_z2(ii) a And x1 is more than or equal to 98.5 percent<100％,0<z1≤1.5％；80％≤x2<100％,0<z2≤20％；z1<d<z2，2z1<z 2; x1, z1, x2 and z2 respectively represent the atomic percentages of the corresponding constituent elementsAn amount; wherein 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, and D comprises at least one of Fe, Co and Ni; t comprises at least one of O, H, N, P, S, F, Cl, I and Br; x and y represent the atom percentage content of corresponding constituent elements, x is more than or equal to 10% and less than or equal to 55%, and y is more than or equal to 45% and less than or equal to 90%;

2) the component of the endogenous powder in the alloy strip is mainly M_x1T_z1The average composition of the coating is mainly A_x2T_z2(ii) a And x1 is more than or equal to 98.5 percent<100％,0<z1≤1.5％；80％≤x2<100％,0<z2≤20％；z1<d<z2，2z1<z 2; x1, z1, x2 and z2 respectively represent the atom percentage content of the corresponding constituent elements; wherein A comprises 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 M comprises at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf and Ti; t comprises at least one of O, H, N, P, S, F, Cl, I and Br;

3) the component of the endogenous powder in the alloy strip is mainly M_x1T_z1The average composition of the coating is mainly A_x2T_z2(ii) a And x1 is more than or equal to 98.5 percent<100％,0<z1≤1.5％；80％≤x2<100％,0<z2≤20％；z1<d<z2，2z1<z 2; x1, z1, x2 and z2 respectively represent the atom percentage content of the corresponding constituent elements; wherein A comprises at least one of Zn, Mg, Sn, Pb, Ga, In, Al, La, Ge, Cu, K, Na and Li, and M comprises at least one of B, Bi, Fe, Ni, Cu, Ag, Si, Ge, Cr and V; t comprises at least one of O, H, N, P, S, F, Cl, I and Br;

4) the component of the endogenous powder in the alloy strip is mainly M_x1Al_y1T_z1The average composition of the coating is mainly A_x2Al_y2T_z2(ii) a X1 is more than or equal to 77.8 percent and less than or equal to 99.8 percent, y1 is more than or equal to 0.1 percent and less than or equal to 22 percent, and<z1≤1.5％；69.8％≤x2≤99.7％，0.2％≤y2≤30％，0<z2≤20％，z1<d<z2，2z1<z2，y1<y2, x1, y1, z1, x2, y2 and z2 respectively represent correspondencesThe atomic percentage content of the constituent elements; wherein 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; t comprises at least one of O, H, N, P, S, F, Cl, I and Br.