ALLOY POWDER, PREPARATION METHOD THEREFOR, AND USE THEREFOR

Abstract

The present disclosure relates to a method for preparing a category of alloy powder and an application thereof. By selecting a suitable alloy system and melting initial alloy melt through low-purity raw materials, high-purity alloy powder, and matrix phase wrapping high-purity alloy powder are precipitated during the solidification process of the initial alloy melt, and the solid solution alloying of the high-purity alloy powder is achieved at the same time. Alloy powder can be obtained by removing the matrix phase wrapping the high-purity alloy powder; high-purity alloy powder can also be obtained by removing the matrix phase wrapping the high-purity alloy powder at an appropriate time. The method is simple and can prepare a variety of alloy powder materials with different morphology at nano-scale, sub-micron level, micron level, and even millimeter level.

Claims

1. A method for preparing a metal material composed of endogenous alloy powder and wrapping body, which is prepared by the following steps: at step 1: melting initial alloy melt with the main elementary composition of M.sub.a0A.sub.b0T.sub.c0, wherein a0, b0, and c0 represent the atomic percent contents of corresponding constituent elements respectively, and a0+b0+c0=100%, and 0<c0<15%; at step 2: solidifying the M.sub.a0A.sub.b0T.sub.c0 initial alloy melt into a solid state, thus obtaining dispersed M.sub.a1A.sub.b1T.sub.c1 particle phase endogenously precipitated from the melt and A.sub.b2T.sub.c2 matrix phase wrapping the dispersed particles, the as-obtained solid material is the metal material composed of endogenous alloy powder and wrapping body; among which 0<c1<c0<c2, it means that the content of element T in the M.sub.a0A.sub.b0T.sub.c0 initial alloy melt is higher than that in the dispersed M.sub.a1A.sub.b1T.sub.c1 particle phase, but lower than that in the A.sub.b2T.sub.c2 matrix phase; the metal material composed of endogenous alloy powder and wrapping body is prepared by solidification of the alloy melt, and the structure of the metal material includes the dispersed particle phase endogenously precipitated during the solidification of the initial alloy and the matrix phase wrapping the dispersed particles, which correspond to the endogenous alloy powder and the wrapping body, respectively; the major elementary composition of the endogenous alloy powder is M.sub.a1A.sub.b1T.sub.c1, and the major element composition of the wrapping body is A.sub.b2T.sub.c2; both M and A contain one or more metal elements, T is an impurity element including oxygen, a1, b1, c1, b2, and c2 represent atomic percentage contents of the corresponding element respectively, and a1+b1+c1=100%, b2+c2=100%, c2>c1>0, b1>0; the melting point of the endogenous alloy powder is higher than that of the wrapping body; and the endogenous M.sub.a1A.sub.b1T.sub.c1 alloy powder contains element A in a solid solution; the M and A comprise a pair or pairs of M.sup.1-A.sup.1 element combinations that will not form corresponding intermetallic compounds, wherein M.sup.1 represents any single element in M and A.sup.1 represents any single element in A, the main elements in M are composed of each M.sup.1 element that satisfies the combination conditions of M.sup.1-A.sup.1, and the main elements in A are composed of each A.sup.1 element that satisfies the combination conditions of M.sup.1-A.sup.1, so that the metal material composed of endogenous alloy powder and wrapping body will not form intermetallic compounds composed of the main elements in M and the main elements in A after being completely melted and re-solidified, but form an endogenous M.sub.a1A.sub.b1T.sub.c1 alloy powder and a A.sub.b2T.sub.c2 wrapping body.

2. The method for preparing a metal material composed of endogenous alloy powder and wrapping body according to claim 1, wherein the shape of the metal material composed of endogenous alloy powder and wrapping body is related to the solidification methods: in the case of continuous casting, its shape is mainly lath shape; and in the case of melt spinning, its shape is mainly ribbon or sheet shape; and in the case of melt extraction, its shape is mainly wire shape.

3. The method for preparing a metal material composed of endogenous alloy powder and wrapping body according to claim 1, wherein T is the collection of O, H, N, P, S, F, and Cl elements, and T includes 0, and 0<c1≤1.5%.

4. The method for preparing a metal material composed of endogenous alloy powder and wrapping body according to claim 1, wherein M includes at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti, Fe, Co, Ni, Mn, Cu, and Ag, and A includes at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, Mg, Ca, Li, Na, K, In, Pb, and Zn.

5. The method for preparing a metal material composed of endogenous alloy powder and wrapping body according to claim 1, wherein M includes at least one of Jr, Ru, Re, Os, Tc, W, Cr, Mo, V, Ta, and Nb, and A includes Cu.

6. (canceled)

7. The method for preparing a metal material composed of endogenous alloy powder and wrapping body according to claim 1, wherein 0<b1≤15%.

8. The method for preparing a metal material composed of endogenous alloy powder and wrapping body according to claim 1, wherein the number of mono-crystalline particles in the endogenous alloy powder accounts for more than 60% of the total number of the particles.

9. The method for preparing a metal material composed of endogenous alloy powder and wrapping body according to claim 1, wherein the M.sub.a0A.sub.b0T.sub.c0 initial alloy melt is prepared by melting alloy raw materials that comprise the first and the second raw materials; the major elementary composition of the first raw material is M.sub.d1T.sub.e1, and the major element composition of the second raw material is A.sub.d2T.sub.e2, d1, e1, d2, and e2 represent atomic percentage contents of the corresponding constituent elements respectively, and 0<e1≤10%, 0<e2≤10%, d1+e1=100%, d2+e2=100%.

10-12. (canceled)

13. The method for preparing a metal material composed of endogenous alloy powder and wrapping body according to claim 1, wherein the volume percentage content of the endogenous alloy powder in the metal material composed of endogenous alloy powder and wrapping body ranges from 1% to 50%.

14. A method for preparing alloy powder, wherein the alloy powder is prepared by removing the wrapping body part of the metal material composed of endogenous alloy powder and wrapping body which is prepared by the method according to claim 1, while retaining the endogenous alloy powder which cannot be simultaneously removed.

15. The method for preparing alloy powder according to claim 14, wherein the methods for removing the wrapping body while retaining the endogenous alloy powder include at least one of an acid solution dissolution reaction for removal, an alkali solution dissolution reaction for removal, a vacuum volatilization for removal, and a wrapping body natural oxidation-powdering peeling removal.

16. (canceled)

17. The method for preparing alloy powder according to claim 14, wherein the particle size of the alloy powder ranges from 3 nm to 10 mm.

18. A method for preparing spherical or sub-spherical alloy powder, wherein the spherical or sub-spherical alloy powder is prepared through a plasma spheroidization treatment of the alloy powder according to claim 14.

19. The method for preparing spherical or sub-spherical alloy powder according to claim 18, wherein before the plasma spheroidization treatment the selected particles are subject to jet mill pre-crushing treatment or (and) screening treatment.

20. A metal material composed of endogenous alloy powder and wrapping body, wherein the metal material composed of endogenous alloy powder and wrapping body is prepared by of the preparation method of metal material composed of endogenous alloy powder and wrapping body according to claim 1.

21. An alloy powder, wherein the alloy powder is prepared by the method for preparing alloy powder according to claim 14.

22. A spherical or sub-spherical alloy powder, wherein the spherical or sub-spherical alloy powder is prepared by the method for preparing spherical or sub-spherical alloy powder according to claim 18.

23. An application of the metal material composed of endogenous alloy powder and wrapping body in coatings and composite materials, wherein the metal material composed of endogenous alloy powder and wrapping body is prepared by of the preparation methods of metal material composed of endogenous alloy powder and wrapping body according to claim 1.

24. The application of a metal material composed of endogenous alloy powder and wrapping body in coatings and composite materials according to claim 23, wherein after the preparation of the metal material composed of endogenous alloy powder and wrapping body, the wrapping body is not removed immediately, and subsequently, the endogenous alloy powder is tried to be protected in other ways from being contaminated by impurities such as oxygen, but the wrapping body is directly used to protect the endogenous powder from being naturally oxidized; such metal material composed of the endogenous powder and the wrapping body can be directly used as a raw material for downstream production; and when the endogenous powder is needed for downstream production, based on the characteristics of the next working procedure, the endogenous powders are released from the wrapping body in the shortest possible time, so that the chance of contamination of the alloy powder is greatly reduced.

25. The application of a metal material composed of endogenous alloy powder and wrapping body in coatings and composite materials according to claim 23, wherein the metal material composed of endogenous alloy powder and wrapping body with the average particle size of the endogenous alloy powder lower than 1000 nm is selected and its wrapping body is removed; the obtained alloy powder is mixed with other components of the coatings or composite materials at the same time or immediately after the removal of the wrapping body, so as to reduce the content of impurities including 0, which is newly introduced on the surface of the alloy powder due to the exposure of the alloy powder surface; and thus coatings or composite materials added with high-purity, ultra-fine and high-activity alloy powder can be obtained, which can be applied in various fields including anti-bacterial coatings, weather-proof coatings, camouflage coatings, wave-absorbing coatings, wear-resistant coatings, anti-corrosive coatings, and resin-based composites.

26. An application of the alloy powder in powder metallurgy, metal injection molding, magnetic materials, and coatings, wherein the alloy powder is prepared by the method for preparing alloy powder according to claim 14.

27. An application of the alloy powder in catalysis, sterilization, metal powder 3D printing, and composite materials, wherein the alloy powder is prepared by the method for preparing alloy powder according to claim 14.

28. An application of the spherical or sub-spherical alloy powder in powder metallurgy, metal injection molding, and metal powder 3D printing, wherein the spherical or sub-spherical alloy powder is prepared by the method for preparing spherical or sub-spherical alloy powder according to claim 18.

29. A metal material composed of endogenous alloy powder and wrapping body, wherein the metal material is prepared by solidification of an alloy melt, and a structure of the metal material includes a dispersed particle phase endogenously precipitated during solidification of the initial alloy and the matrix phase wrapping the dispersed particles, which correspond to the endogenous alloy powder and the wrapping body, respectively; the major elementary composition of the endogenous alloy powder is M.sub.a1A.sub.b1T.sub.c1, and the major elementary composition of the wrapping body is A.sub.b2T.sub.c2; both M and A contain one or more metal elements, T is an impurity element including oxygen, a1, b1, c1, b2, and c2 represent atomic percentage contents of the corresponding element respectively, and a1+b1+c1=100%, b2+c2=100%, c2>c1>0, b1>0; the melting point of the endogenous alloy powder is higher than that of the wrapping body; the endogenous M.sub.a1A.sub.b1T.sub.c1 alloy powder contains element A in a solid solution; and the M and A comprise a pair or pairs of M.sup.1-A.sup.1 element combinations that will not form corresponding intermetallic compounds, wherein M.sup.1 represents any single element in M and A.sup.1 represents any single element in A, the main elements in M are composed of each M.sup.1 element that satisfies the combination conditions of M.sup.1-A.sup.1, and the main elements in A are composed of each A.sup.1 element that satisfies the combination conditions of M.sup.1-A.sup.1, so that the metal material composed of endogenous alloy powder and wrapping body will not form intermetallic compounds composed of the main elements in M and the main elements in A after being completely melted and re-solidified, but form an endogenous M.sub.a1A.sub.b1T.sub.c1 alloy powder and a A.sub.b2T.sub.c2 wrapping body.

30. The metal material composed of endogenous alloy powder and wrapping body according to claim 29, wherein M includes at least one of W, Cr, Mo, V, Ta, Nb, Zr, Hf, Ti, Fe, Co, Ni, Mn, Cu, and Ag, A includes at least one of Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, Mg, Ca, Li, Na, K, In, Pb, and Zn, and T is the collection of O, H, N, P, S, F, Cl elements, and T includes 0, and 0<c1<1.5%, and 0<b1≤15%.

31. An alloy powder, wherein the alloy powder is prepared by removing the wrapping body in the metal materials composed of endogenous alloy powder and wrapping body according to claim 29, and its major elementary composition is M.sub.a3A.sub.b3T.sub.c3, a3, b3, and c3 represent atomic percentage contents of the corresponding elementary compositions respectively, b3>0, a3+b3+c3=100%, and the content of element T in the alloy powder is higher than that in the endogenous alloy powder according to claim 29, that is, c3>c1>0.

32. A spherical or sub-spherical alloy powder, wherein the spherical or sub-spherical alloy powder is prepared through a plasma spheroidization treatment of the alloy powder according to claim 31, and its major elementary composition is M.sub.a4A.sub.b4T.sub.c4, a4, b4, and c4 represent atomic percentage contents of the corresponding elementary compositions respectively, b4>0, a4+b4+c4=100%, and the content of element T in the spherical or sub-spherical alloy powder is higher than that in the alloy powder without plasma spheroidization treatment, that is, c4>c3>c1>0.

33. A method for preparing a metal material composed of endogenous alloy powder and wrapping body, which is prepared by the following steps: (1) melting initial alloy melt with the main elementary composition of M.sub.a0A.sub.b0T.sub.c0, wherein both M and A contain one or more metal elements, T is the impurity element including oxygen, a0, b0, and c0 represent atomic percentage contents of the corresponding element respectively, a0+b0+c0=100%, 0<c0; the M and A comprise a pair or pairs of M.sup.1-A.sup.1 element combinations that will not form corresponding intermetallic compounds, wherein M.sup.1 represents any single element in M and A.sup.1 represents any single element in A, and the main elements in M are composed of each M.sup.1 element that satisfies the combination conditions of M.sup.1-A.sup.1, and the main elements in A are composed of each A.sup.1 element that satisfies the combination conditions of M.sup.1-A.sup.1, (2) solidifying the M.sub.a0A.sub.b0T.sub.c0 initial alloy melt into a solid state, thus obtaining dispersed M.sub.a1A.sub.b1T.sub.c1 particle phase endogenously precipitated from the melt and A.sub.b2T.sub.c2 matrix phase wrapping the dispersed particles, which are the metal material composed of endogenous alloy powder and wrapping body according to claim 29, and 0<c1<c0<c2.

34. The method for preparing a metal material composed of endogenous alloy powder and wrapping body according to claim 33, wherein the M.sub.a0A.sub.b0T.sub.c0 initial alloy melt is prepared by melting alloy raw materials that comprise the first and the second raw materials; the major elementary composition of the first raw material is M.sub.d1T.sub.e1, and the major element composition of the second raw material is A.sub.d2T.sub.e2, d1, e1, d2, and e2 represent atomic percentage contents of the corresponding constituent elements respectively, and 0<e1≤10%, 0<e2≤10%, d1+e1=100%, d2+e2=100%.

35. A method for preparing alloy powder, wherein the alloy powder is prepared by removing the wrapping body part of the metal material composed of endogenous alloy powder and wrapping body according to claim 29, while retaining the endogenous alloy powder which cannot be simultaneously removed.

36. An application of the alloy powder according to claim 31, in powder metallurgy, metal injection molding, magnetic materials, and coatings.

37. An application of the spherical or sub-spherical alloy powder according to claim 32 in powder metallurgy, metal injection molding, and metal powder 3D printing.

38. An application of the metal material composed of endogenous alloy powder and wrapping body according to claim 29 in coatings and composite materials.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0156] FIG. 1 shows the local back-scattering SEM of the endogenous nano-scale Ti alloy powder and Gd wrapping body in Example 3 of the present disclosure;

[0157] FIG. 2 shows the SEM of the nano-scale Ti alloy powder in Example 3 of the present disclosure;

[0158] FIG. 3 shows the local back-scattering SEM of the endogenous Ti—Co dendrite alloy powder and Gd wrapping body in Example 6 of the present disclosure;

[0159] FIG. 4 shows the SEM of the Ti—Co dendrite alloy powder in Example 6 of the present disclosure.

DETAILED DESCRIPTION

[0160] The present disclosure is described in detail below, together with Examples. It should be noted that the following examples are intended to facilitate the understanding of the present disclosure, and will not confine the present disclosure in any way.

Example 1

[0161] This example provides a metal ribbon composed of endogenous nano-scale Ti alloy powder and Ce wrapping body, a nano-scale Ti alloy powder, and their preparation method and application, which includes the following steps:

[0162] Low-purity titanium including Cl, N, O, and H with a weight percentage content of 0.3 wt %, 0.1 wt %, 0.3 wt %, and 0.03 wt %, respectively, is selected. After converting into atomic percentage content, atomic percentage content of Cl, N, O, and H are 0.4 at %, 0.33 at %, 0.88 at %, and 1.39 at %, respectively, that is, their total content is 3 at %. Low-purity rare earth Ce which contains 0.3 wt % of O is selected. After converting into atomic percentage content, the content of 0 in Ce is 2.57 at %. Since Ti—Ce is an element pair that does not form an intermetallic compound, and the melting point of Ti is higher than that of Ce, thus Ti alloy powder can be prepared based on the Ti—Ce element pair.

[0163] The low-purity Ti and low-purity Ce raw materials with a volume ratio of 1:3 are mixed, and other trace elements that may exist in the raw materials are classified as the main element to facilitate the calculation. According to the element density and atomic weight data, the composition of the alloy raw materials can be expressed as (Ti.sub.97Cl.sub.0.4N.sub.0.33O.sub.0.88H.sub.1.39).sub.39(Ce.sub.97.43O.sub.2.57).sub.61 in terms of atomic percentage content, which can be further expressed as Ti.sub.37.83Ce.sub.59.435Cl.sub.0.156N.sub.0.129H.sub.0.54O.sub.1.91, wherein the total content of impurity element T such as Cl, N, H, and O is about 2.735 at %.

[0164] The low-purity alloy raw materials are melted by induction, and an initial alloy melt with a composition of Ti.sub.37.83Ce.sub.59.435T.sub.2.735 (wherein T represents impurity elements such as Cl, N, H, and O) is obtained. Some impurity elements in the initial alloy melt may become slag and separate from the melt, resulting in the decrease of the impurity content; and some impurities in the environment and atmosphere, such as oxygen, may enter into the melt, increasing the impurity content.

[0165] The initial alloy melt is solidified into the ribbons with a thickness of about 100 μm through copper roller spinning. In the solidification process, the dispersed particle phase mainly composed of Ti precipitates into the matrix phase mainly composed of Ce, thus the metal ribbon composed of endogenous nano-scale Ti alloy powder and Ce wrapping body can be obtained. Wherein atomic percentage composition of the endogenous Ti alloy powder is about Ti.sub.99.1Ce.sub.0.5T.sub.0.4, which is mainly composed of mono-crystalline particles with a particle size ranging from 3 nm to 300 nm. A small amount of Ce is solidly dissolved in the endogenous Ti alloy powder, and the content of impurity T is greatly reduced compared with the low-purity Ti raw materials, and a large amount of impurity T is enriched in the Ce wrapping body. In the as-prepared metal ribbon composed of endogenous nano-scale Ti alloy powder and Ce wrapping body, the volume percentage content of the endogenous Ti alloy powder is equivalent to the volume percentage content of the Ti raw materials when the raw materials are prepared, which is about 25 vol %, thus ensuring the dispersed distribution of the Ti alloy powder in the matrix phase mainly composed of Ce.

[0166] The Ce wrapping body in the metal ribbon is composed of endogenous nano-scale Ti alloy powder and the Ce wrapping body is removed by dilute hydrochloride acid solution. Since Ti alloy powder does not react with dilute hydrochloride acid, after separation, cleaning, and drying, Ti—Ce-T alloy powder can be obtained. Because of the absorption of impurities such as oxygen by the surface atoms after the exposure of Ti—Ce-T alloy powder, the content of impurity T in the obtained Ti—Ce-T alloy powder is higher than that of the endogenous Ti—Ce-T alloy powder.

[0167] The process of step (5) can also be carried out directly after step (3):

[0168] The Ce wrapping body in the metal ribbon composed of endogenous nano-scale Ti alloy powder and Ce wrapping body is removed by diluted deoxygenated hydrochloride acid solution, then the Ti alloy powder is separated under a protective atmosphere and subsequently mixed with epoxy resin and other coating components within 20 minutes, then nano-scale titanium-alloy-modified polymer anti-corrosive coating can be prepared.

Example 2

[0169] This example provides a metal sheet composed of endogenous micron Ti alloy powder and Ce wrapping body, a micron Ti alloy powder, and their preparation method and application, which includes the following steps:

[0170] Low-purity titanium including Cl, N, O, and H with a weight percentage content of 0.3 wt %, 0.1 wt %, 0.3 wt %, and 0.03 wt % respectively, is selected. After converting into atomic percentage content, atomic percentage content of Cl, N, O, and H are 0.4 at %, 0.33 at %, 0.88 at %, and 1.39 at %, respectively, that is, their total content is 3 at %. Low-purity rare earth Ce which contains 0.3 wt % of O is selected. After converting into atomic percentage content, the content of 0 in Ce is 2.57 at %. Since Ti—Ce is an element pair that does not form an intermetallic compound, and the melting point of Ti is higher than that of Ce, thus Ti alloy powder can be prepared based on the Ti—Ce element pair.

[0171] The low-purity Ti and low-purity Ce raw materials with a volume ratio of 1:3 are mixed, and other trace elements that may exist in the raw materials are classified as the main element to facilitate the calculation. According to the element density and atomic weight data, the composition of the alloy raw materials can be expressed as (Ti.sub.97Cl.sub.0.4N.sub.0.33O.sub.0.88H.sub.1.39).sub.39(Ce.sub.97.43O.sub.2.57).sub.61 in terms of atomic percentage content, which can be further expressed as Ti.sub.37.83Ce.sub.59.435Cl.sub.0.156N.sub.0.129H.sub.0.54O.sub.1.91, wherein the total content of impurity element T such as Cl, N, H, and O is about 2.735 at %.

[0172] The low-purity alloy raw materials are melted by induction, and an initial alloy melt with a composition of Ti.sub.37.83Ce.sub.59.435T.sub.2.735 (wherein T represents impurity elements such as Cl, N, H, and O) is obtained. Some impurity elements in the initial alloy melt may become slag and separate from the melt, resulting in the decrease of the impurity content; and some impurities in the environment and atmosphere, such as oxygen, may enter into the melt, increasing the impurity content.

[0173] The initial alloy melt is solidified into the sheet with a thickness of about 4 mm. In the solidification process, the dispersed dendritic particle phase mainly composed of Ti precipitates into the matrix phase mainly composed of Ce, thus the metal sheet composed of endogenous micron Ti alloy powder and Ce wrapping body can be obtained. Wherein atomic percentage composition of the dendritic endogenous Ti alloy powder is about Ti.sub.99.4Ce.sub.0.3T.sub.0.3, which is mainly composed of mono-crystalline particles with a particle size ranging from 1 μm to 150 μm. A small amount of Ce is solidly dissolved in the endogenous Ti alloy powder, and the content of impurity T is greatly reduced compared with the low-purity Ti raw materials, and a large amount of impurity T is enriched in the Ce wrapping body. In the as-prepared metal sheet composed of endogenous micron Ti alloy powder and Ce wrapping body, the volume percentage content of the endogenous Ti alloy powder is equivalent to the volume percentage content of the Ti raw materials when the raw materials are prepared, which is about 25 vol %, thus ensuring the dispersed distribution of the dendritic Ti alloy powder in the matrix phase mainly composed of Ce.

[0174] The Ce wrapping body in the metal sheet is composed of endogenous micron Ti alloy powder and the Ce wrapping body is removed by dilute hydrochloride acid solution. Since dendritic Ti alloy powder does not react with dilute hydrochloride acid, after separation, cleaning, and drying, dendritic Ti—Ce-T alloy powder can be obtained.

[0175] The Ti—Ce-T alloy dendrite powder is treated with a jet mill, and the entangled dendritic particles are dispersed and the relatively large dendritic particles can be rushed into small dendritic particles.

[0176] The obtained dendritic Ti alloy powder is screened and the dendritic Ti alloy dendrite powder with a particle size ranging from 15 μm to 53 μm is selected for plasma spheroidization, thus spherical or sub-spherical Ti alloy powder with a particle size nearly unchanged can be obtained.

[0177] The spherical or sub-spherical Ti alloy powder can be applied in the field of metal powder 3D printing.

Example 3

[0178] This example provides a metal ribbon composed of endogenous nano-scale Ti alloy powder and Gd wrapping body, a nano-scale Ti alloy powder, and their preparation method, which includes the following steps:

[0179] Low-purity Ti raw material and rare earth raw material mainly composed of Gd are selected. The content of impurity T in both two kinds of raw materials is about 3 at %. Since Ti—Gd is an element pair that does not form an intermetallic compound, and the melting point of Ti is higher than that of Gd, thus Ti alloy powder can be prepared based on the Ti—Gd element pair.

[0180] The low-purity Ti raw material and rare earth raw material mainly composed of Gd with a volume ratio of 15:85 are mixed and melted by induction, thus an initial alloy melt with the composition of Ti.sub.24Gd.sub.73T.sub.3 can be obtained, wherein the content of T is about 3 at %.

[0181] The initial alloy melt is solidified into the ribbon with a thickness of about 100 μm through copper roller spinning. In the solidification process, the dispersed particle phase mainly composed of Ti precipitates into the matrix phase mainly composed of Gd, thus the metal ribbon composed of endogenous nano-scale Ti alloy powder and Gd wrapping body can be obtained. The micromorphology of the metal ribbon is shown in FIG. 1. Wherein atomic percentage composition of the endogenous Ti alloy powder is about Ti.sub.99.2Gd.sub.0.5T.sub.0.3, which is mainly composed of nano-scale mono-crystalline Ti particles with a small amount of solidly dissolved Gd. The particle size of the nano-scale mono-crystalline Ti particles ranges from 3 nm to 300 nm. The content of impurity T is greatly reduced compared with the low-purity Ti raw materials, and a large amount of impurity T is enriched in the Gd wrapping body. In the as-prepared metal ribbon composed of endogenous Ti alloy powder and Gd wrapping body, the volume percentage content of the endogenous Ti alloy powder is equivalent to the volume percentage content of the Ti raw materials when the raw materials are prepared, which is about 15 vol %, thus ensuring the dispersed distribution of the Ti alloy powder in the matrix phase mainly composed of Gd, as shown in FIG. 1.

[0182] The Gd wrapping the body in the metal ribbon is composed of endogenous nano-scale Ti alloy powder and Gd wrapping body is removed by a dilute hydrochloride acid solution. Since Ti alloy powder does not react with dilute hydrochloride acid, after separation, cleaning, and drying, Ti—Gd-T alloy powder mainly composed of Ti can be obtained, of which the particle size ranges from 3 nm to 300 nm, as shown in FIG. 2.

Example 4

[0183] This example provides a metal ribbon composed of endogenous nano-scale Ti—Nb—V alloy powder and Ce—La—Nd—Pr wrapping body, a nano-scale Ti—Nb—V alloy powder, and their preparation method, which includes the following steps:

[0184] Low-purity Ti, Nb, and V raw materials and rare earth raw materials mainly composed of Ce, La, Nd, and Pr are selected. The content of impurity T in both kinds of raw materials is about 3 at %. Since Ti—Ce, Ti—La, Ti—Nd, Ti—Pr, Nb—Ce, Nb—La, Nb—Nd, Nb—Pr, V—Ce, V—La, V—Nd, and V—Pr are element pairs that do not form intermetallic compounds, and the melting point of Ti, Nb, and V is higher than that of Ce, La, Nd, and Pr, thus Ti—Nb—V alloy powder can be prepared based on these element combination pairs.

[0185] The low-purity Ti, Nb, and V raw materials and rare earth raw materials mainly composed of Ce, La, Nd, and Pr with a volume ratio of 1:2 are mixed, wherein the Ti, Nb, and V are with equal molar ratios. The alloy raw materials are melted by induction, and thus an initial alloy melt with the composition of (Ti—Nb—V)—(Ce—La—Nd—Pr)-T can be obtained, wherein the content of T is about 3 at %.

[0186] The initial alloy melt is solidified into the ribbon with a thickness of about 100 μm through copper roller spinning. In the solidification process, the dispersed particle phase mainly composed of Ti—Nb—V precipitates into the matrix phase mainly composed of Ce—La—Nd—Pr, thus the metal ribbon composed of endogenous nano-scale Ti—Nb—V alloy powder and Ce—La—Nd—Pr wrapping body can be obtained. Wherein atomic percentage composition of the endogenous Ti—Nb—V alloy powder is about (Ti—Nb—V).sub.99.2(Ce—La—Nd—Pr).sub.0.5T.sub.0.3, which is mainly composed of mono-crystalline Ti—Nb—V particles with ultimate mutual solubility. The particle size of the mono-crystalline Ti—Nb—V particles ranges from 3 nm to 300 nm. Ce—La—Nd—Pr is solidly dissolved in the endogenous Ti—Nb—V alloy powder, and the content of impurity T is greatly reduced compared with the low-purity Ti, Nb, and V raw materials, and a large amount of impurity T is enriched in the Ce—La—Nd—Pr wrapping body. In the as-prepared metal ribbon composed of endogenous nano-scale Ti—Nb—V alloy powder and Ce—La—Nd—Pr wrapping body, the volume percentage content of the endogenous Ti—Nb—V alloy powder is equivalent to the volume percentage content of the Ti, Nb, and V raw materials when the raw materials are prepared, which is about 33 vol %, thus ensuring the dispersed distribution of the Ti—Nb—V alloy powder in the matrix phase mainly composed of Ce—La—Nd—Pr.

[0187] The Ce—La—Nd—Pr wrapping body in the metal ribbon composed of endogenous nano-scale Ti—Nb—V alloy powder and Ce—La—Nd—Pr wrapping body is removed by dilute hydrochloride acid solution. Since Ti—Nb—V alloy powder does not react with dilute hydrochloride acid, after separation, cleaning and drying, Ti—Nb—V alloy powder mainly composed of (Ti—Nb—V)—(Ce—La—Nd—Pr)-T can be obtained. Because of the absorption of impurities such as oxygen by the surface atoms after the exposure of Ti—Nb—V alloy powder, the content of impurity T in the as-prepared Ti—Nb—V alloy powder is higher than that of the endogenous Ti—Nb—V alloy powder.

Example 5

[0188] This example provides a metal ribbon composed of endogenous sub-micron Ti—Co alloy powder and Ce—La—Nd—Pr wrapping body, a sub-micron Ti—Co alloy powder, and their preparation method, which includes the following steps:

[0189] Low-purity Ti and Co raw materials and rare earth raw materials mainly composed of Ce, La, Nd, and Pr are selected, wherein the molar ratio of Ti and Co raw materials is 1:1. The content of impurity T in both two kinds of raw materials is about 3 at %. Since Ti—Ce, Ti—La, Ti—Nd, and Ti—Pr are element pairs that do not form intermetallic compounds, and Ti accounts for 50% of the Ti—Co raw materials, which is the main element; and the melting point of CoTi intermetallic compound is as high as 1700° C., which is much higher than the melting point of the intermetallic compounds can be formed by Co and Ce, La, Nd, and Pr; when Co:Ti is 1:1, Co mainly combines with Ti to form CoTi intermetallic compound with a high melting point. Therefore, intermetallic compound CoTi alloy powder can be prepared on the basis of these element combination pairs.

[0190] The low-purity Ti and Co raw material and rare earth raw material mainly composed of Ce, La, Nd, and Pr with a volume ratio of 1:2 are mixed, wherein Co:Ti is 1:1. The alloy raw materials are melted by induction, and thus an initial alloy melt with the composition of (Ti—Co)—(Ce—La—Nd—Pr)-T can be obtained, wherein the content of T is about 3 at %.

[0191] The initial alloy melt is solidified into the ribbon with a thickness of about 300 μm through copper roller spinning. In the solidification process, the dispersed particle phase mainly composed of sub-micron Ti—Co precipitates into the matrix phase mainly composed of Ce—La—Nd—Pr, thus the metal ribbon composed of endogenous sub-micron Ti—Co alloy powder and Ce—La—Nd—Pr wrapping body can be obtained. Wherein atomic percentage composition of the endogenous Ti—Co alloy powder is about (Ti—Co).sub.99(Ce—La—Nd—Pr).sub.0.6T.sub.0.4, which is mainly composed of mono-crystalline Ti—Co intermetallic compound particles with a particle size ranging from 20 nm to 1 μm. Ce—La—Nd—Pr is solidly dissolved in the endogenous Ti—Co alloy powder, and the content of impurity T is greatly reduced compared with the low-purity Ti and Co raw materials, and a large amount of impurity T is enriched in the Ce—La—Nd—Pr wrapping body. In the as-prepared metal ribbon composed of endogenous sub-micron Ti—Co alloy powder and Ce—La—Nd—Pr wrapping body, the volume percentage content of the endogenous Ti—Co alloy powder is equivalent to the volume percentage content of the Ti and Co raw materials when the raw materials are prepared, which is about 33 vol %, thus ensuring the dispersed distribution of the Ti—Co alloy powder in the matrix phase mainly composed of Ce—La—Nd—Pr.

[0192] The Ce—La—Nd—Pr wrapping body in the metal ribbon is composed of endogenous sub-micron Ti—Co alloy powder and Ce—La—Nd—Pr wrapping body is removed by dilute hydrochloride acid solution. Since Ti—Co alloy powder does not react with dilute hydrochloride acid, after separation, cleaning, and drying, Ti—Co alloy powder mainly composed of (Ti—Co)—(Ce—La—Nd—Pr)-T can be obtained. Because of the absorption of impurities such as oxygen by the surface atoms after the exposure of Ti—Co alloy powder, the content of impurity T in the as-prepared Ti—Co alloy powder is higher than that of the endogenous Ti—Co alloy powder.

Example 6

[0193] This example provides a metal sheet composed of endogenous micron Ti—Co alloy powder and Gd wrapping body, a micron Ti—Co alloy powder, and their preparation method, which includes the following steps:

[0194] Low-purity Ti and Co raw materials and rare earth raw materials mainly composed of Gd are selected, wherein the molar ratio of Ti and Co raw materials is 1:1. The content of impurity T in both two kinds of raw materials is about 3 at %. Since Ti—Gd is an element pair that does not form intermetallic compounds, and Ti accounts for 50% of the Ti—Co raw materials, which is the main element; and the melting point of CoTi intermetallic compound is as high as 1700° C., which is much higher than the melting point of the intermetallic compounds can be formed by Co and Gd; when Co:Ti is 1:1, Co mainly combines with Ti to form CoTi intermetallic compound with a high melting point. Therefore, intermetallic compound CoTi alloy powder can be prepared on the basis of these element combination pairs.

[0195] The low-purity Ti and Co raw material and rare earth raw material mainly composed of Gd with a volume ratio of 30:70 are mixed, wherein Co:Ti is 1:1. The alloy raw materials are melted by induction, and thus an initial alloy melt with the composition of (Ti—Co)—Gd-T can be obtained, wherein the content of T is about 3 at %.

[0196] The initial alloy melt is solidified into the sheet with a thickness of about 2 mm. In the solidification process, the dispersed dendritic particle phase mainly composed of Ti—Co precipitates into the matrix phase mainly composed of Gd, thus the metal sheet composed of endogenous micron Ti—Co alloy powder and Gd wrapping body can be obtained. The micromorphology of the metal sheet is shown in FIG. 3. Wherein atomic percentage composition of the dendritic endogenous Ti—Co alloy powder is about (TiCo).sub.99.5Gd.sub.0.3T.sub.0.2, which is mainly composed of mono-crystalline Ti—Co intermetallic compound particles with a particle size ranging from 1 μm to 60 μm. A small amount of Gd is solidly dissolved in the endogenous Ti—Co alloy powder, and the content of impurity T is greatly reduced compared with the low-purity Ti and Gd raw materials, and a large amount of impurity T is enriched in the Gd wrapping body. In the as-prepared metal sheet composed of endogenous micron Ti—Co alloy powder and Gd wrapping body, the volume percentage content of the endogenous Ti—Co alloy powder is equivalent to the volume percentage content of the Ti and Co raw materials when the raw materials are prepared, which is about 30 vol %, thus ensuring the dispersed distribution of the Ti—Co alloy powder in the matrix phase mainly composed of Gd.

[0197] The Gd wrapping body in the metal sheet is composed of endogenous micron Ti—Co alloy powder and the Gd wrapping body is removed by dilute hydrochloride acid solution. Since Ti—Co alloy powder does not react with dilute hydrochloride acid, after separation, cleaning and drying, Ti—Co alloy powder mainly composed of (Ti—Co)—Gd-T can be obtained, of which the mono-crystalline dendrite morphology is shown in FIG. 4. Because of the absorption of impurities such as oxygen by the surface atoms after the exposure of Ti—Co alloy powder, the content of impurity T in the as-prepared Ti—Co alloy powder is higher than that of the endogenous Ti—Co alloy powder.

Example 7

[0198] This example provides a metal ribbon composed of endogenous micron Fe alloy powder and La wrapping body, a micron Ti alloy powder, and their preparation method, which includes the following steps:

[0199] Low-purity Fe raw material and rare earth raw material mainly composed of La are selected. The content of impurity T in both two kinds of raw materials is about 2.5 at %. Since Fe—La is an element pair that does not form intermetallic compounds, and both Fe and La are the main elements; Therefore, Fe alloy powder can be prepared on the basis of a Fe and La combination pair.

[0200] The low-purity Fe raw material and rare earth raw material mainly composed of La with a volume ratio of 1:2 are mixed and melted by induction. Thus an initial alloy melt with the composition of Fe—La-T can be obtained, wherein the content of T is about 2.5 at %.

[0201] The initial alloy melt is solidified into the ribbon with a thickness of about 500 μm through copper roller spinning. In the solidification process, the dispersed particle phase mainly composed of Fe precipitates into the matrix phase mainly composed of La, thus the metal ribbon composed of endogenous micron Fe alloy powder and La wrapping body can be obtained. Wherein atomic percentage composition of the endogenous Fe alloy powder is about Fe.sub.99.4La.sub.0.3T.sub.0.3, which is mainly composed of mono-crystalline Fe particles with a particle size ranging from 500 nm to 5 μm. La is solidly dissolved in the endogenous Fe alloy powder, and the content of impurity T in endogenous Fe alloy powder is greatly reduced compared with the low-purity Fe raw materials, and a large amount of impurity T is enriched in the La wrapping body. In the as-prepared metal ribbon composed of endogenous micron Fe alloy powder and La wrapping body, the volume percentage content of the endogenous Fe alloy powder is equivalent to the volume percentage content of the Fe raw material when the raw materials are prepared, which is about 33 vol %, thus ensuring the dispersed distribution of the Fe alloy powder in the matrix phase mainly composed of La.

[0202] The endogenous Fe alloy powder is pre-separated from the oxidized La matrix through a natural oxidation-pulverization process of the La wrapping body, and the Fe alloy powder can be separated from the oxidized La matrix with a magnetic field based on the magnetic property of the Fe alloy powder. Then the residual La oxide adsorbed on the surface of the Fe alloy powder can be completely removed by a small amount of dilute acid solution, meanwhile, ensuring the Fe alloy powder can be retained by controlling the concentration and amount of the acid. After cleaning, separation, and drying, Fe alloy powder is obtained.

Example 8

[0203] This example provides a metal ribbon composed of endogenous nano-scale Cu alloy powder and Li wrapping body, a nano-scale Cu alloy powder, and their preparation method, which includes the following steps:

[0204] Low-purity Cu raw material and Li raw material are selected. The content of impurity T in both two kinds of raw materials is about 1 at %. Since Cu—Li is an element pair that does not form intermetallic compounds, and both Cu and Li are the main elements; Therefore, Cu alloy powder can be prepared on the basis of a Cu and Li combination pair.

[0205] The low-purity Cu raw material and low-purity Li raw material with a volume ratio of 1:3 are mixed and melted by induction. Thus an initial alloy melt with the composition of Cu—Li-T can be obtained, wherein the content of T is about 1 at %.

[0206] The initial alloy melt is solidified into the ribbon with a thickness of about 30 μm through copper roller spinning. In the solidification process, the dispersed particle phase mainly composed of Cu precipitates into the matrix phase mainly composed of Li, thus the metal ribbon composed of endogenous nano-scale Cu alloy powder and Li wrapping body can be obtained. Wherein atomic percentage composition of the endogenous Cu alloy powder is about Cu.sub.84.8Li.sub.15T.sub.0.2, which is mainly composed of mono-crystalline Cu alloy particles solidly dissolved with a large amount of Li. The particle size of the mono-crystalline Cu alloy particles ranges from 3 nm to 150 nm. The content of impurity T in endogenous Cu alloy powder is greatly reduced compared with the Cu raw materials, and a large amount of other impurity T is enriched in the Li wrapping body.

[0207] The Li wrapping body in the metal ribbon is composed of endogenous nano-scale Cu alloy powder and the Li wrapping body is removed by a very dilute hydrochloride acid solution. Since Cu alloy powder does not react with very dilute hydrochloride acid, after separation, cleaning and drying, nano-scale Cu alloy powder mainly composed of Cu—Li-T can be obtained.

Example 9

[0208] This example provides a metal ribbon composed of endogenous nano-scale Cu alloy powder and Pb wrapping body, a nano-scale Cu alloy powder, and their preparation method, which includes the following steps:

[0209] Low-purity Cu raw material and Pb raw material are selected. The content of impurity T in both two kinds of raw materials is about 2 at % and 0.5 at %, respectively. Since Cu—Pb is an element pair that does not form intermetallic compounds, and both Cu and Pb are the main elements; Therefore, Cu alloy powder can be prepared on the basis of a Cu and Pb combination pair.

[0210] The low-purity Cu raw material and low-purity Pb raw material with a volume ratio of 1:3 are mixed and melted by induction. Thus an initial alloy melt with the composition of Cu—Pb-T can be obtained, wherein the content of T is about 1 at %.

[0211] The initial alloy melt is solidified into the ribbon with a thickness of about 30 μm through copper roller spinning. In the solidification process, the dispersed particle phase mainly composed of Cu precipitates into the matrix phase mainly composed of Pb, thus the metal ribbon composed of endogenous nano-scale Cu alloy powder and Pb wrapping body can be obtained. Wherein atomic percentage composition of the endogenous Cu alloy powder is about Cu.sub.99.5Pb.sub.0.3T.sub.0.2, which is mainly composed of mono-crystalline Cu alloy particles solidly dissolved with a small amount of Pb. The particle size of the mono-crystalline Cu alloy particles ranges from 3 nm to 150 nm. The content of impurity T in endogenous Cu alloy powder is greatly reduced compared with the Cu raw materials, and a large amount of other impurity T is enriched in the Pb wrapping body. In the as-prepared metal ribbon composed of endogenous nano-scale Cu alloy powder and Pb wrapping body, the volume percentage content of the endogenous Cu alloy powder is equivalent to the volume percentage content of the Cu raw material when the raw materials are prepared, which is about 25 vol %, thus ensuring the dispersed distribution of the Cu alloy powder in the matrix phase mainly composed of Pb.

[0212] The Pb wrapping body in the metal ribbon is composed of endogenous nano-scale Cu alloy powder and Pb wrapping body is removed by the mixture of acetic acid and dilute hydrochloride acid. Since Cu alloy powder does not react with the mixture of acetic acid and dilute hydrochloride acid, after separation, cleaning and drying, nano-scale Cu alloy powder mainly composed of Cu—Pb-T can be obtained.

Example 10

[0213] This example provides a metal ribbon composed of endogenous nano-scale Nb—V—Mo—W alloy powder and Cu wrapping body, a nano-scale Nb—V—Mo—W alloy powder, and their preparation method, which includes the following steps:

[0214] Low-purity Nb, V, Mo, and W raw materials and Cu raw materials are selected. The content of impurity Tin both two kinds of raw materials is about 1 at %. Since Cu—Nb, Cu—V, Cu—Mo, and Cu—W are element combination pairs that do not form intermetallic compounds, and Nb, V, Mo, and W are the main mutually soluble elements. Therefore, Nb—V—Mo—W alloy powder can be prepared on the basis of these element combination pairs.

[0215] The low-purity Nb, V, Mo, and W raw material and Cu raw material 1 with a volume ratio of 1:2 are mixed, wherein the molar ratio of Nb:V:Mo:W is 2:1:1:1. The alloy raw materials are melted by induction, and thus an initial alloy melt with the composition of (Nb.sub.2VMoW)—Cu-T can be obtained, wherein the content of T is about 1 at %.

[0216] The initial alloy melt is solidified into the ribbon with a thickness of about 30 μm through copper roller spinning. In the solidification process, the dispersed particle phase mainly composed of Nb.sub.2VMoW precipitates into the matrix phase mainly composed of Cu, thus the metal ribbon composed of endogenous nano-scale Nb.sub.2VMoW alloy powder and Cu wrapping body can be obtained. Wherein atomic percentage composition of the endogenous Nb.sub.2VMoW alloy powder is about (Nb.sub.2VMoW).sub.99.3Cu.sub.0.5T.sub.0.2, which is mainly composed of high-entropy mono-crystalline Nb.sub.2VMoW alloy particles solidly dissolved with a small amount of Cu. The particle size of the high-entropy mono-crystalline Nb.sub.2VMoW alloy particles ranges from 3 nm to 200 nm. The content of impurity T in endogenous Nb.sub.2VMoW alloy powder is greatly reduced compared with the Nb, V, Mo, and W raw materials, and a large amount of other impurity T is enriched in the Cu wrapping body. In the as-prepared metal ribbon composed of endogenous nano-scale Nb—V—Mo—W alloy powder and Cu wrapping body, the volume percentage content of the endogenous Nb.sub.2VMoW alloy powder is equivalent to the volume percentage content of the Nb, V, Mo, and W raw material when the raw materials are prepared, which is about 33 vol %, thus ensuring the dispersed distribution of the Nb.sub.2VMoW alloy powder in the matrix phase mainly composed of Cu.

[0217] The Cu wrapping body in the metal ribbon is composed of endogenous nano-scale Nb—V—Mo—W alloy powder and Cu wrapping body is removed by hydrochloride acid solution with medium concentration. Since Nb.sub.2VMoW alloy powder does not react with hydrochloride acid solution with medium concentration, after separation, cleaning, and drying, nano-scale alloy powder mainly composed of Nb.sub.2VMoW can be obtained.

Example 11

[0218] This example provides a metal ribbon composed of endogenous micro Nb—V—Mo—W alloy powder and Cu wrapping body, a micro Nb—V—Mo—W alloy powder, and their preparation method, which includes the following steps:

[0219] Low-purity Nb, V, Mo, and W raw materials and Cu raw materials are selected. The content of impurity Tin both two kinds of raw materials is about 1 at %. Since Cu—Nb, Cu—V, Cu—Mo, and Cu—W are element combination pairs that do not form intermetallic compounds, and Nb, V, Mo, and W are the main mutually soluble elements. Therefore, Nb—V—Mo—W alloy powder can be prepared on the basis of these element combination pairs.

[0220] The low-purity Nb, V, Mo, and W raw material and Cu raw material 1 with a volume ratio of 1:2 are mixed, wherein the molar ratio of Nb:V:Mo:W is 1:1:1:1. The alloy raw materials are melted by induction, and thus an initial alloy melt with the composition of (NbVMoW)—Cu-T can be obtained, wherein the content of T is about 1 at %.

[0221] The initial alloy melt is solidified into the sheet with a thickness of about 4 mm. In the solidification process, the dispersed dendritic particle phase mainly composed of NbVMoW precipitates into the matrix phase mainly composed of Cu, thus the metal sheet composed of endogenous micro NbVMoW alloy powder and Cu wrapping body can be obtained. Wherein atomic percentage composition of the endogenous NbVMoW dendritic alloy powder is about (NbVMoW).sub.99.6Cu.sub.0.3T.sub.0.1, which is mainly composed of high-entropy mono-crystalline NbVMoW alloy particles solidly dissolved with a small amount of Cu. The particle size of the high-entropy mono-crystalline NbVMoW alloy particles ranges from 3 nm to 200 nm. The content of impurity T in endogenous NbVMoW alloy powder is greatly reduced compared with the Nb, V, Mo and W raw materials, and a large amount of other impurity T is enriched in the Cu wrapping body. In the as-prepared metal sheet composed of endogenous micro Nb—V—Mo—W alloy powder and Cu wrapping body, the volume percentage content of the endogenous NbVMoW dendritic alloy powder is equivalent to the volume percentage content of the Nb, V, Mo, and W raw material when the raw materials are prepared, which is about 33 vol %, thus ensuring the dispersed distribution of the NbVMoW dendritic alloy powder in the matrix phase mainly composed of Cu.

[0222] The Cu wrapping body in the metal sheet is composed of endogenous micro Nb—V—Mo—W alloy powder and Cu wrapping body is removed by hydrochloride acid solution with medium concentration. Since NbVMoW dendritic alloy powder does not react with hydrochloride acid solution with medium concentration, after separation, cleaning, and drying, nano-scale alloy powder mainly composed of NbVMoW can be obtained.

[0223] The technical features of the above examples may be arbitrarily combined. For conciseness, all possible combinations of the technical features of the above embodiments have not been completely described. However, as long as there is no contradiction between the combinations of these technical features, they shall be considered to be within the scope of the present disclosure.

[0224] The above examples only express several embodiments of the disclosure, and their descriptions are more specific and detailed, but they cannot be interpreted as a limitation on the scope of the present disclosure. It should be noted that for one of ordinary skill in the art, several variations and improvements may be made without deviating from the concept of the disclosure, which all fall within the scope of protection of the disclosure. Therefore, the scope of protection of the present disclosure shall be subject to the attached claims.