CN109604963B - Preparation method of heterogeneous high-entropy alloy with variable modulation period and modulation ratio - Google Patents

Preparation method of heterogeneous high-entropy alloy with variable modulation period and modulation ratio Download PDF

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CN109604963B
CN109604963B CN201811594109.7A CN201811594109A CN109604963B CN 109604963 B CN109604963 B CN 109604963B CN 201811594109 A CN201811594109 A CN 201811594109A CN 109604963 B CN109604963 B CN 109604963B
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entropy alloy
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CN109604963A (en
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江峰
吴亚科
孙军
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Xian Jiaotong University
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Abstract

The invention discloses a preparation method of a non-homogeneous high-entropy alloy with variable modulation period and modulation ratio, belonging to the field of high-performance alloy manufacturing. Determining initial and final state modulation periods, modulation ratios, cycle numbers and grain sizes of all layers of the heterogeneous material, determining a master alloy which meets the grain sizes, processing the master alloy into corresponding thicknesses according to the initial modulation period and the modulation ratios, cleaning the surface of the master alloy, determining fly plates and substrate materials, calculating a welding window, determining welding parameters, welding to obtain a single-period heterogeneous high-entropy alloy, forming the single-period heterogeneous high-entropy alloy, welding the single-period heterogeneous high-entropy alloy after composite forming successively according to the cycle numbers, and performing cold deformation on the combined single-period heterogeneous high-entropy alloy according to the final state modulation period to obtain a finished product. The high-speed collision welding technology is matched with cold deformation treatment to prepare the heterogeneous high-entropy alloy, so that the preparation method of the high-performance heterogeneous high-entropy alloy is greatly optimized, and the performance level and the application range of the high-performance heterogeneous high-entropy alloy are improved.

Description

Preparation method of heterogeneous high-entropy alloy with variable modulation period and modulation ratio
[ technical field ] A method for producing a semiconductor device
The invention belongs to the field of high-performance alloy manufacturing, and particularly relates to a preparation method of a heterogeneous high-entropy alloy with variable modulation period and modulation ratio.
[ background of the invention ]
The high-entropy alloy is an alloy based on a new alloy design concept proposed by samsung in 2004, the content of each element is more than 5%, no obvious dominant element exists, the high-entropy alloy is generally single-phase FCC or BCC in structure, and sometimes has a mixed structure. The high-entropy alloy has good thermal stability, wear resistance and corrosion resistance, and is a class of high-performance alloy which is vigorously developed at present.
But parts of high-entropy alloy systems, e.g. Fe40Mn40Co10Cr10But the alloy has the characteristics of excellent low-temperature performance and limited room-temperature strength, and the practical use of the alloy is limited. Although room temperature strength can be improved to some extent by conventional strengthening means, plasticity is reduced, and thus the use of conventional strengthening means is limited. In the current academic research, the discovery that the back stress reinforcement can be formed by preparing a mixed heterogeneous alloy structure with a plurality of layers of different grain sizes in matching and combination, the strength and the plasticity of the material are obviously improved, and the preparation method is considered to be an important means for developing high-performance high-entropy alloy and expanding the application of the high-performance high-entropy alloy. However, the existing preparation method usually prepares the heterogeneous high-entropy alloy by heat treatment, mechanical treatment or powder metallurgy method, and has the problems of low internal bonding strength of the alloy, limited size range and internal structure of the formed heterogeneous alloy and the like, and the operability is low.
[ summary of the invention ]
The invention aims to overcome the defects of the prior art and provides a preparation method of a heterogeneous high-entropy alloy with variable modulation period and modulation ratio. The high-speed collision welding technology is matched with cold deformation treatment to prepare the heterogeneous high-entropy alloy, so that the preparation method of the high-performance heterogeneous high-entropy alloy is greatly optimized, and the performance level and the application range of the high-performance heterogeneous high-entropy alloy are improved.
In order to achieve the purpose, the invention adopts the following technical scheme to realize the purpose:
a preparation method of a heterogeneous high-entropy alloy with variable modulation period and modulation ratio comprises the following steps:
step 1, determining initial and final state modulation periods, a modulation ratio, a period number and grain sizes of each layer of the heterogeneous alloy;
step 2, determining the master alloy meeting the grain size;
step 3, processing the master alloy into corresponding thickness according to the initial modulation period and the modulation ratio in the step 1, and cleaning the surface of the master alloy;
step 4, determining the materials of the flying plate and the base plate, calculating a welding window, determining welding parameters, and welding to obtain a single-period heterogeneous high-entropy alloy;
step 5, molding the single-period heterogeneous high-entropy alloy, and gradually welding the composite molded single-period heterogeneous high-entropy alloy according to the number of the cycles determined in the step 1;
and 6, carrying out cold deformation on the single-period heterogeneous high-entropy alloy compounded in the step 5 according to the final state modulation period to obtain a finished product.
The invention further improves the following steps:
selecting a solid solution alloy from the master alloy in the step 2 if the aging strengthening is performed and the difference of the heat treatment temperature is less than 50 ℃; otherwise, selecting the unprocessed annealing state.
If the solid solution alloy is selected in the step 2, aging treatment for recovering the alloy performance is required after cold deformation in the step 6.
And 4, welding by using one of explosion welding, electromagnetic pulse welding or metal film gasification impact welding.
Step 5, molding, namely welding for one-step molding if the number of the single-period heterogeneous high-entropy alloy layers is 2-3; if the number of layers is 4 or more, the layers are connected and molded by welding.
And 5, molding, namely sequentially connecting the components one by one if the number of layers is 4 or more, and compounding the same material and then compounding the dissimilar material.
The cold deformation in step 6 is performed by one of rolling, drawing, and forging.
The cold deformation thickness reduction in the step 6 is more than or equal to 0% and less than 100%.
Compared with the prior art, the invention has the following beneficial effects:
according to the invention, high-quality connection among layers of the heterogeneous high-entropy alloy can be realized through high-speed collision welding technologies including explosion welding, electromagnetic pulse welding or metal film gasification impact welding, the modulation period, the modulation ratio and the cycle number of the heterogeneous high-entropy alloy can be randomly selected according to design requirements, the ideal combination of wide alloy combination and wide-grain-size-range large-scale alloy can be realized, the operability is strong, the room temperature strength of the high-entropy alloy is powerfully improved, and the variety and the performance of the heterogeneous high-entropy alloy are powerfully improved.
[ description of the drawings ]
FIG. 1 shows a single-period heterogeneous high-entropy alloy of Fe in example 140Mn40Co10Cr10A schematic diagram;
FIG. 2 is a schematic view of example 2 of the present invention; wherein (a) is a single-period heterogeneous high-entropy alloy (Fe) obtained by electromagnetic pulse welding40Mn40Co10Cr10)97.8C3.3And (b) is heterogeneous high-entropy alloy (Fe) with cycle number of 2 obtained by metal thin film gasification impact welding40Mn40Co10Cr10)97.8C3.3And (c) the non-homogeneous high-entropy alloy (Fe) with the cycle number of 2 obtained after 33.3 percent cold rolling and aging40Mn40Co10Cr10)97.8C3.3；
FIG. 3 is a schematic view of example 3 of the present invention; wherein (a) is Fe obtained by gasification impact welding of metal film40Mn40Co10Cr10Coarse crystal and fine crystal composite board (b) is Fe obtained by metal film gasification impact welding20Co20Ni20Cr20Mn20Coarse crystal and fine crystal composite board (c) is Fe obtained by electromagnetic pulse welding40Mn40Co10Cr10And Fe20Co20Ni20Cr20Mn20Single-period heterogeneous high-entropy alloy of (a), (b) explosive welding Fe with period number of 240Mn40Co10Cr10And Fe20Co20Ni20Cr20Mn20A non-homogeneous high-entropy alloy of composition, (e) Fe with a periodicity of 2 obtained after 91% cold rolling40Mn40Co10Cr10And Fe20Co20Ni20Cr20Mn20A heterogeneous high entropy alloy of composition;
FIG. 4 is a schematic view of example 4 of the present invention; wherein (a) is Fe obtained by electromagnetic pulse welding40Mn40Co10Cr10Coarse crystal and fine crystal composite board, (b) Fe obtained by electromagnetic pulse welding40Mn40Co10Cr10Coarse and fine crystals and Fe20Co20Ni20Cr20Mn20A coarse-grain composite board, and (c) Fe obtained by electromagnetic pulse welding40Mn40Co10Cr10And Fe20Co20Ni20Cr20Mn20Single-period heterogeneous high-entropy alloy of (a), (b) explosive welding Fe with period number of 240Mn40Co10Cr10And Fe20Co20Ni20Cr20Mn20A non-homogeneous high-entropy alloy of composition, (e) Fe with a periodicity of 2 obtained after 91% cold rolling40Mn40Co10Cr10And Fe20Co20Ni20Cr20Mn20Heterogeneous height of compositionEntropy alloy.
[ detailed description ] embodiments
In order to make the technical solutions of the present invention better understood, the technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the drawings in the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, not all of the embodiments, and are not intended to limit the scope of the present disclosure. Moreover, in the following description, descriptions of well-known structures and techniques are omitted so as to not unnecessarily obscure the concepts of the present disclosure. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Various structural schematics according to the disclosed embodiments of the invention are shown in the drawings. The figures are not drawn to scale, wherein certain details are exaggerated and possibly omitted for clarity of presentation. The shapes of various regions, layers and their relative sizes and positional relationships shown in the drawings are merely exemplary, and deviations may occur in practice due to manufacturing tolerances or technical limitations, and a person skilled in the art may additionally design regions/layers having different shapes, sizes, relative positions, according to actual needs.
In the context of the present disclosure, when a layer/element is referred to as being "on" another layer/element, it can be directly on the other layer/element or intervening layers/elements may be present. In addition, if a layer/element is "on" another layer/element in one orientation, then that layer/element may be "under" the other layer/element when the orientation is reversed.
It should be noted that the terms "first," "second," and the like in the description and claims of the present invention and in the drawings described above are used for distinguishing between similar elements and not necessarily for describing a particular sequential or chronological order. It is to be understood that the data so used is interchangeable under appropriate circumstances such that the embodiments of the invention described herein are capable of operation in sequences other than those illustrated or described herein. Furthermore, the terms "comprises," "comprising," and "having," and any variations thereof, are intended to cover a non-exclusive inclusion, such that a process, method, system, article, or apparatus that comprises a list of steps or elements is not necessarily limited to those steps or elements expressly listed, but may include other steps or elements not expressly listed or inherent to such process, method, article, or apparatus.
The invention is described in further detail below with reference to the accompanying drawings:
the invention discloses a preparation method of a heterogeneous high-entropy alloy with variable modulation period and modulation ratio, which comprises the following steps:
step 1, determining initial and final state modulation cycles, modulation ratio, cycle number and grain size of each layer of a heterogeneous material according to design requirements of the heterogeneous high-entropy alloy;
step 2, purchasing a commercial master alloy high-entropy alloy meeting the grain size required by design, wherein if the master alloy can be subjected to aging strengthening and the heat treatment temperature is similar, a solid solution state is used, otherwise, an unprocessed annealing state is used;
step 3, processing the master alloy into a corresponding thickness according to the initial modulation period and the modulation ratio, and cleaning the surface of the master alloy;
step 4, determining flying plate and substrate materials according to the properties of each component material of the heterogeneous high-entropy alloy, calculating a welding window and determining welding parameters to complete welding arrangement, and welding by using one of explosive welding, electromagnetic pulse welding or metal film gasification impact welding technologies to obtain a single-period heterogeneous high-entropy alloy;
step 5, if the number of the alloy layers in a single period is 2-3, the alloy layers are formed in one step by using the process of the step 4; if the number of the alloy layers in a single period is 4 or more, the process of the step 4 is used for forming layer by layer, or the alloy layers are connected component by component according to the principle of firstly compounding the same material and then compounding a different material;
step 6, according to the requirement of the cycle number, the single-cycle heterogeneous high-entropy alloy prepared in the step 5 is sequentially compounded by using the process of the step;
step 7, according to the final state modulation period, cold deformation is carried out on the heterogeneous high-entropy alloy by using one of rolling, drawing or forging, and the cold deformation thickness reduction is more than or equal to 0% and less than 100%;
and 8, if the solid solution alloy is used in the step 2, aging the prepared heterogeneous high-entropy alloy to recover the alloy performance.
The preparation principle of the invention is as follows: the high-speed collision welding technology can realize high-quality connection between wide homogeneous and heterogeneous alloys, and the composite size is not limited, so that the preparation of the heterogeneous high-entropy alloy with any modulation period, modulation ratio and period number can be realized, the performance is high, the influence of the property difference between the alloys is avoided, the variety of the heterogeneous high-entropy alloy is greatly expanded, and the performance of the high-entropy alloy can be greatly improved.
Example 1
Determination of non-homogeneous high-entropy alloy Fe40Mn40Co10Cr10The initial state modulation period and the final state modulation period are respectively 1500 mu m and 1500 mu m, the modulation ratio of coarse crystal to fine crystal is 2:1, the period number is 1, and two kinds of grain sizes, namely 50 mu m and 1 mu m, are used; two kinds of mother alloy with grain size are purchased, the alloy can not be strengthened by aging, so that an undeformed and annealed state is used; respectively processing coarse crystal plates and fine crystal plates with the thicknesses of 1000 mu m and 500 mu m according to the initial modulation period and the modulation ratio, and cleaning the surfaces of the master alloy; the method comprises the steps of taking a coarse-grain plate as a substrate and a fine-grain plate as a flying plate, determining welding parameters according to the properties of the materials, and compounding the coarse-grain plate and the fine-grain plate by using an explosive welding technology to prepare the heterogeneous high-entropy alloy Fe with the cycle number of 140Mn40Co10Cr10。
As shown in FIG. 1, the heterogeneous high-entropy alloy of this embodiment is made of the same Fe40Mn40Co10Cr10The number of cycles is 1, so that the double-layer single-cycle heterogeneous high-entropy alloy Fe can be prepared by only one welding process40Mn40Co10Cr10。
Example 2
Determination of non-homogeneous high entropy alloys (Fe)40Mn40Co10Cr10)97.8C3.3The initial state modulation period and the final state modulation period are respectively 1500 mu m and 1000 mu m, the ratio of coarse crystal to fine crystal modulation is 2:1, the period number is 2, and two kinds of grain sizes, namely 50 mu m and 1 mu m, are used; two kinds of mother alloy with grain size are purchased, the alloy can be age-strengthened, so solid solution state should be used; respectively processing two coarse crystal plates and two fine crystal plates with the thicknesses of 1000 mu m and 500 mu m according to the initial modulation period and the modulation ratio, and cleaning the surface of the master alloy; the method comprises the steps of taking a coarse-grain plate as a substrate and a fine-grain plate as a flying plate, determining welding parameters according to the properties of the materials, and compounding the coarse-grain plate and the fine-grain plate by using an electromagnetic pulse welding technology to prepare two single-period heterogeneous high-entropy alloys (Fe)40Mn40Co10Cr10)97.8C3.3As shown in FIG. 2 (a); for the two single-period heterogeneous high-entropy alloys (Fe) obtained in the previous step40Mn40Co10Cr10)97.8C3.3Determining welding parameters according to the properties of the materials, cleaning the alloy surface, and compounding two single-period heterogeneous high-entropy alloys (Fe) by using a metal thin film gasification impact welding technology40Mn40Co10Cr10)97.8C3.3As shown in FIG. 2 (b); according to the requirement of the modulation period of the final state, the heterogeneous high-entropy alloy (Fe) with the period number of 2 is obtained by compounding40Mn40Co10Cr10)97.8C3.3Cold rolling was performed with a reduction of 1000 μm (about 33.3%) in thickness, as shown in FIG. 2 (c); cold rolled heterogeneous high entropy alloy (Fe) at 400 DEG C40Mn40Co10Cr10)97.8C3.3Aging for 3 hours;
FIG. 2(a) shows a single-period heterogeneous high-entropy alloy (Fe) prepared by electromagnetic pulse welding40Mn40Co10Cr10)97.8C3.3FIG. 2(b) is a schematic diagram of a non-homogeneous high-entropy alloy (Fe) with a cycle number of 2 prepared by using a metal thin film gasification impact welding technique40Mn40Co10Cr10)97.8C3.3FIG. 2(c) is a schematic view showing the results of 33.3% cold rolling and agingHeterogeneous high entropy alloy (Fe) with a period number of 240Mn40Co10Cr10)97.8C3.3And the modulation period and the modulation ratio meet the design requirements.
Example 3
Determination of non-homogeneous high-entropy alloys from Fe40Mn40Co10Cr10And Fe20Co20Ni20Cr20Mn20Composition, initial and final modulation periods of 1000 μm and 90 μm, respectively, Fe40Mn40Co10Cr10For Fe20Co20Ni20Cr20Mn20The modulation ratio is 4:1, the modulation ratio of coarse crystal to fine crystal is 1:1, the period number is 2, and two kinds of grain sizes of 50 μm and 1 μm are used; the method is characterized in that mother alloys with two grain sizes are purchased, and both alloys are in an unprocessed and annealed state because the two alloys can not be subjected to aging strengthening; according to the initial modulation period and the modulation ratio, coarse crystal Fe and fine crystal Fe with the thickness of 400 mu m are respectively processed40Mn40Co10Cr10And coarse and fine crystalline Fe of thickness 100 μm20Co20Ni20Cr20Mn20Two plates are arranged respectively, and the surface of the master alloy is cleaned; using coarse-grain plate as base plate and fine-grain plate as flying plate, determining welding parameters according to the properties of the materials, and respectively compounding Fe by using metal film gasification impact welding technology40Mn40Co10Cr10And Fe20Co20Ni20Cr20Mn20A coarse crystal plate and a fine crystal plate, as shown in fig. 3(a) and (b), and then compounding two high-entropy alloy coarse-fine crystal composite plates by using an electromagnetic pulse welding technology, so as to prepare two single-period heterogeneous high-entropy alloys, as shown in fig. 3 (c); for the two blocks of Fe obtained above40Mn40Co10Cr10And Fe20Co20Ni20Cr20Mn20Determining welding parameters according to the properties of the materials, cleaning the alloy surface, and compounding by using an explosive welding technology to obtain the heterogeneous high-entropy alloy with the cycle number of 2, as shown in figure 3 (d); compounding the obtained number of cycles according to the requirement of the modulation cycle of the final stateThe heterogeneous high entropy alloy of 2 was cold rolled with a reduction in thickness of 910 μm (91%), as shown in FIG. 3 (e); as shown in FIG. 3(e), Fe was finally obtained with a cycle number of 240Mn40Co10Cr10And Fe20Co20Ni20Cr20Mn20The heterogeneous high-entropy alloy meets the design requirements.
As shown in FIG. 3, FIGS. 3(a) and (b) are Fe prepared by using a thin metal film gasification impact welding technique40Mn40Co10Cr10And Fe20Co20Ni20Cr20Mn20Coarse and fine grain composite panels of composition, fig. 3(c) Fe prepared using electromagnetic pulse welding technique40Mn40Co10Cr10And Fe20Co20Ni20Cr20Mn20Single period heterogeneous high entropy alloy of composition, fig. 3(d) is Fe with period number 2 prepared using explosive welding technique40Mn40Co10Cr10And Fe20Co20Ni20Cr20Mn20Non-homogeneous high entropy alloy of composition, FIG. 3(e) Fe with periodicity of 2 obtained after 91% cold rolling40Mn40Co10Cr10And Fe20Co20Ni20Cr20Mn20The formed heterogeneous high-entropy alloy meets the design requirements on the modulation period and the modulation ratio.
Example 4
Determination of non-homogeneous high-entropy alloys from Fe40Mn40Co10Cr10And Fe20Co20Ni20Cr20Mn20Composition, initial and final modulation periods of 1000 μm and 90 μm, respectively, Fe40Mn40Co10Cr10For Fe20Co20Ni20Cr20Mn20The modulation ratio is 4:1, the modulation ratio of coarse crystal to fine crystal is 1:1, the period number is 2, and two kinds of grain sizes of 50 μm and 1 μm are used; two kinds of grain size mother alloy are purchased, and both alloys should be used in a non-processed annealed state because the two alloys cannot be age-strengthened(ii) a According to the initial modulation period and the modulation ratio, coarse crystal Fe and fine crystal Fe with the thickness of 400 mu m are respectively processed40Mn40Co10Cr10And coarse and fine crystalline Fe of thickness 100 μm20Co20Ni20Cr20Mn20Two plates are arranged respectively, and the surface of the master alloy is cleaned; with Fe40Mn40Co10Cr10Coarse-grain plate as substrate, according to Fe40Mn40Co10Cr10Fine crystal plate, Fe20Co20Ni20Cr20Mn20The coarse crystal plate and the fine crystal plate are sequentially welded by using an electromagnetic pulse welding technology to prepare two Fe blocks40Mn40Co10Cr10And Fe20Co20Ni20Cr20Mn20Single-period heterogeneous high entropy alloys of composition, as shown in fig. 4(a) - (c); for two blocks of Fe obtained40Mn40Co10Cr10And Fe20Co20Ni20Cr20Mn20Determining welding parameters according to the properties of the materials, cleaning the alloy surface, and compounding by using an explosive welding technology to obtain the heterogeneous high-entropy alloy with the cycle number of 2, as shown in a figure 4 (d); according to the requirement of the final state modulation period, the heterogeneous high-entropy alloy with the period number of 2 obtained by compounding is subjected to cold rolling, and the thickness reduction is 910 mu m (91%), as shown in a graph 4 (e); as shown in FIG. 4(e), Fe was finally obtained with a cycle number of 240Mn40Co10Cr10And Fe20Co20Ni20Cr20Mn20The heterogeneous high-entropy alloy meets the design requirements.
As shown in FIG. 4, FIGS. 4(a), (b) and (c) are Fe prepared using an electromagnetic pulse welding technique, respectively40Mn40Co10Cr10Coarse and fine grain composite sheet, Fe40Mn40Co10Cr10Coarse and fine crystals and Fe20Co20Ni20Cr20Mn20Coarse grain composite sheet, Fe40Mn40Co10Cr10And Fe20Co20Ni20Cr20Mn20Single period heterogeneous high entropy alloy of composition, fig. 4(d) is Fe with period number 2 prepared using explosive welding technique40Mn40Co10Cr10And Fe20Co20Ni20Cr20Mn20Non-homogeneous high entropy alloy of composition, FIG. 4(e) Fe with periodicity of 2 obtained after 91% cold rolling40Mn40Co10Cr10And Fe20Co20Ni20Cr20Mn20The formed heterogeneous high-entropy alloy meets the design requirements on the modulation period and the modulation ratio.
The above-mentioned contents are only for illustrating the technical idea of the present invention, and the protection scope of the present invention is not limited thereby, and any modification made on the basis of the technical idea of the present invention falls within the protection scope of the claims of the present invention.

Claims (8)

1. A preparation method of a heterogeneous high-entropy alloy with variable modulation period and modulation ratio is characterized by comprising the following steps:
step 1, determining initial and final state modulation periods, a modulation ratio, a period number and grain sizes of each layer of the heterogeneous alloy;
step 2, determining the master alloy meeting the grain size;
step 3, processing the master alloy into corresponding thickness according to the initial modulation period and the modulation ratio in the step 1, and cleaning the surface of the master alloy;
step 4, determining the materials of the flying plate and the base plate, calculating a welding window, determining welding parameters, and welding to obtain a single-period heterogeneous high-entropy alloy;
step 5, molding the single-period heterogeneous high-entropy alloy, and gradually welding the composite molded single-period heterogeneous high-entropy alloy according to the number of the cycles determined in the step 1;
and 6, carrying out cold deformation on the single-period heterogeneous high-entropy alloy compounded in the step 5 according to the final state modulation period to obtain a finished product.
2. The method for preparing the heterogeneous high-entropy alloy with the variable modulation period and modulation ratio as claimed in claim 1, wherein the master alloy in the step 2 is selected as a solid solution alloy if aging strengthening is performed and the difference of the heat treatment temperature is less than 50 ℃; otherwise, selecting the unprocessed annealing state.
3. The method for preparing the heterogeneous high-entropy alloy with variable modulation period and modulation ratio as claimed in claim 2, wherein if the alloy in the solid solution state is selected in the step 2, the aging treatment for recovering the alloy performance is further performed after the cold deformation in the step 6.
4. The method for preparing the heterogeneous high entropy alloy with variable modulation period and modulation ratio according to claim 1, wherein the welding in step 4 is one of explosive welding, electromagnetic pulse welding or metal film gasification impact welding.
5. The method for preparing the heterogeneous high-entropy alloy with variable modulation period and modulation ratio as claimed in claim 1, wherein in the step 5, the single-period heterogeneous high-entropy alloy is formed by welding once if the number of layers is 2-3; if the number of layers is 4 or more, the layers are connected and molded by welding.
6. The method for preparing the heterogeneous high-entropy alloy with variable modulation period and modulation ratio according to claim 5, wherein the forming in step 5 is performed by sequentially connecting components one by one if the number of layers is 4 or more, and combining the same kind of material first and then combining the different kinds of material.
7. The method for preparing the variable modulation period and modulation ratio heterogeneous high entropy alloy of claim 1, wherein the cold deformation in step 6 is by one of rolling, drawing or forging.
8. The method for preparing the heterogeneous high-entropy alloy with variable modulation period and modulation ratio according to claim 1, wherein the cold deformation thickness reduction in the step 6 is greater than or equal to 0% and less than 100%.
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