CN114196861A - High-entropy Laves phase intermetallic compound - Google Patents

High-entropy Laves phase intermetallic compound Download PDF

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CN114196861A
CN114196861A CN202111390850.3A CN202111390850A CN114196861A CN 114196861 A CN114196861 A CN 114196861A CN 202111390850 A CN202111390850 A CN 202111390850A CN 114196861 A CN114196861 A CN 114196861A
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entropy
intermetallic compound
laves
phase intermetallic
laves phase
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聂小武
盛明强
马比阿伟
余强
韩亚平
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Nanchang Institute of Technology
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C27/00—Alloys based on rhenium or a refractory metal not mentioned in groups C22C14/00 or C22C16/00
    • C22C27/02—Alloys based on vanadium, niobium, or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
    • C22B9/00—General processes of refining or remelting of metals; Apparatus for electroslag or arc remelting of metals
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    • C22B9/20—Arc remelting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C27/00—Alloys based on rhenium or a refractory metal not mentioned in groups C22C14/00 or C22C16/00
    • C22C27/04—Alloys based on tungsten or molybdenum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon

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Abstract

The invention discloses a high-entropy Laves phase intermetallic compound, relates to the field of novel metal material preparation, and particularly relates to a high-entropy Laves phase intermetallic compound. The invention aims to obtain a novel metal material which has a highly ordered crystal structure of a Laves phase intermetallic compound and has the characteristic of multiple main elements of a high-entropy alloy. High-entropy Laves phase intermetallic compound is binary intermetallic compoundA compound or ternary intermetallic compound; the chemical formula of the binary Laves phase intermetallic compound is M2N; the chemical formula type of the ternary Laves phase intermetallic compound is ABC. The high-entropy Laves phase intermetallic compound is used in the fields of aviation, aerospace, military, civil use and the like.

Description

High-entropy Laves phase intermetallic compound
Technical Field
The invention relates to the field of metal material preparation, in particular to a high-entropy Laves phase intermetallic compound.
Background
The high-entropy alloy is a multi-principal element disordered solid solution alloy different from the traditional alloy type, generally has four or more than five metal elements as main elements, the ratio of the mole number of each main metal element to the total mole number of the alloy is between 5 at.% and 30 at.%, solute and solvent components cannot be distinguished, BCC, FCC and BCC + FCC solid solution phases are usually formed, and the formation of intermetallic compounds is inhibited. Because the content of one element is not more than 30at percent and is used as a main element, the mixed entropy of the alloy is obviously increased, and a high entropy effect, a delayed diffusion effect, a lattice distortion effect and a cocktail effect are generated, so that the material has excellent comprehensive performance. While the Laves phase intermetallic compound is a kind of ordered metal material completely different from the high entropy alloy. Unlike other types of metallic materials, such materials are compounds of metals and metals or metals and metalloids (e.g., silicon, arsenic, tellurium), having long-range ordered crystal structures and metallic fundamental properties different from their constituent elements. The main element atoms are mainly combined by covalent bonds, and the arrangement of the main element atoms is highly ordered. Due to the existence of covalent bonds, the Laves phase intermetallic compound has unique materials with high strength, high hardness, high melting point, high creep resistance, low plasticity, special electrical, magnetic and acoustic properties and the like. Both high-entropy alloy and Laves phase intermetallic compounds are metal materials which are mainly developed at home and abroad at present. The alloy designed by combining the advantages of the Laves phase intermetallic compound and the high-entropy alloy has excellent performance.
Disclosure of Invention
The invention aims to obtain a metal material which has a highly ordered crystal structure of a Laves phase intermetallic compound and has the characteristic of multiple main elements of a high-entropy alloy, and provides the high-entropy Laves phase intermetallic compound.
The high-entropy Laves phase intermetallic compound is a binary intermetallic compound or a ternary intermetallic compound; the chemical formula of the binary Laves phase intermetallic compound is M2N; the chemical formula type of the ternary Laves phase intermetallic compound is ABC; a binary intermetallic compound containing 5 to 16 elements, which is composed of M representing 1 to 8 elements and N representing 1 to 8 elements; the ternary Laves phase intermetallic compound containing 5-24 elements is composed of A representing 1-8 elements, B representing 1-8 elements and C representing 1-8 elements; a, B, C, M and N are selected from Mo element, Fe element, Cr element, Nb element, Ta element, W element, Zr element, Mo element, Cr element, V element, Sc element, Hf element, Ru element, Si element and rare earth element; the atomic percent of each element in the binary Laves phase intermetallic compound is 3 to 70 percent; the atomic percent of each element in the ternary Laves phase intermetallic compound is 3 to 70 percent; m and N are not the same element, and A, B and C are not the same element; the high-entropy Laves phase intermetallic compound contains 0.00001 to 1 volume percent of solid solution, nonmetal compound or intermetallic compound with other crystal structures.
The invention has the beneficial effects that:
the high-entropy Laves-phase intermetallic compound obtained by the invention combines the characteristics of the Laves-phase intermetallic compound and the high-entropy alloy, and on the basis of the Laves-phase intermetallic compound, elements which are close to an equimolar ratio and form the intermetallic compound are added, and the main elements are five or more than five, so that a metal material which has both a highly ordered crystal structure of the Laves-phase intermetallic compound and the characteristics of multiple main elements of the high-entropy alloy is formed. The high-entropy Laves phase intermetallic compound obtained by the invention is still an intermetallic compound, and different kinds of atoms have strong bonding, so that the crystal structure is more stable, and the atoms and the dislocation of the high-entropy Laves phase intermetallic compound are enabled to be more stableThe mobility is reduced at high temperature, and compared with high-entropy alloy and traditional metal materials, the alloy has more excellent hardness, strength and thermal stability and better high-temperature resistance, and is more suitable for being used as a high-temperature structural material; compared with the traditional intermetallic compound, the high-entropy Laves phase intermetallic compound has good room temperature plasticity due to the high entropy effect brought by the multiple principal elements. For example, compared with high-entropy alloy and traditional metal materials, the use temperature of the high-entropy Laves phase intermetallic compound can be increased by 200-400 ℃; part M is less plastic at room temperature (less than 5%) than other Laves phase intermetallics2The room temperature plasticity of the N-type high-entropy Laves phase intermetallic compound can be improved by more than 30 percent, and the strength can also be improved by more than one time. The characteristics of the high-entropy Laves phase intermetallic compound enable the high-entropy Laves phase intermetallic compound to have wide application prospects in the fields of aviation, aerospace, military, civil use and the like, and have important commercial values.
Drawings
FIG. 1 is an X-ray diffraction pattern of a binary high-entropy Laves-phase intermetallic compound obtained in example one;
FIG. 2 is an X-ray diffraction pattern of a binary high-entropy Laves-phase intermetallic compound obtained in example two;
FIG. 3 is an X-ray diffraction pattern of the ternary high-entropy Laves-phase intermetallic compound obtained in example III.
Detailed Description
The first embodiment is as follows: the high-entropy Laves-phase intermetallic compound is a binary Laves-phase intermetallic compound or a ternary Laves-phase intermetallic compound; the chemical formula type of the binary high-entropy Laves phase intermetallic compound is M2N; the chemical formula type of the ternary high-entropy Laves phase intermetallic compound is ABC; a binary intermetallic compound containing 5 to 16 elements, which is composed of M representing 1 to 8 elements and N representing 1 to 8 elements; a ternary intermetallic compound containing 5 to 24 elements, which is composed of A representing 1 to 8 elements, B representing 1 to 8 elements and C representing 1 to 8 elements; a, B, C, M and N are selected from Mo element, Fe element, Cr element, Nb element, Ta element, W element, Zr element, Mo element, Cr element, V element, Sc element, Hf element, Ru elementSelecting elements, Si elements and rare earth elements; the atomic percent of each element in the binary Laves phase intermetallic compound is 3 to 70 percent; the atomic percent of each element in the ternary Laves phase intermetallic compound is 3 to 70 percent; m and N are not the same element, and A, B and C are not the same element; the high-entropy Laves phase intermetallic compound contains 0.00001 to 1 volume percent of solid solution, nonmetal compound or intermetallic compound with other crystal structures.
The solid solution or the nonmetal compound in the present embodiment refers to other crystalline substances having a crystal structure different from that of the intermetallic compound having another crystal structure and the finally formed high-entropy Laves phase intermetallic compound; the various elements are melted together and solidify, possibly producing a small amount of a second phase, which may be a solid solution or other non-compound material.
The second embodiment is as follows: the first difference between the present embodiment and the specific embodiment is: the principle of selecting elements in the binary high-entropy Laves-phase intermetallic compound is that at least three Laves-phase intermetallic compounds exist in a compound formed by the reaction of any one of 1-8 elements represented by M and one of 1-8 elements represented by N, the chemical formula types and the crystal structures of the Laves-phase intermetallic compounds formed by the reaction are the same, and the elements in the high-entropy Laves-phase intermetallic compound are selected as the elements of the binary high-entropy Laves-phase intermetallic compound. The rest is the same as the first embodiment.
The same crystal structure in this embodiment means: the most basic structural features of the metal crystal are the same with the regular arrangement that its internal atoms are three-dimensionally periodic in space.
The third concrete implementation mode: the present embodiment differs from the first or second embodiment in that: when M consists of two or more elements, the molar ratio of each element provided by M in the binary high-entropy Laves-phase intermetallic compound is the same; when N is composed of two or more elements, the molar ratio between the respective elements provided by N in the binary high-entropy Laves-phase intermetallic compound is the same. The others are the same as in the first or second embodiment.
The fourth concrete implementation mode: the difference between this embodiment mode and one of the first to third embodiment modes is: the principle of selecting elements in the ternary high-entropy Laves-phase intermetallic compound is that at least two intermetallic compounds exist in a compound formed by the reaction of any one of A representing 1-8 elements, any one of B representing 1-8 elements and any one of C representing 1-8 elements in the selected elements, and the chemical formula types and crystal structures of the high-entropy Laves-phase intermetallic compound formed by the reaction are the same, so that the elements in the high-entropy Laves-phase intermetallic compound are selected as the elements of the ternary high-entropy Laves-phase intermetallic compound. The rest is the same as one of the first to third embodiments.
The same crystal structure in this embodiment means: the most basic structural features of the metal crystal are the same with the regular arrangement that its internal atoms are three-dimensionally periodic in space.
The fifth concrete implementation mode: the difference between this embodiment and one of the first to fourth embodiments is: when A is composed of two or more elements, the molar ratio among the elements provided by A in the ternary high-entropy Laves-phase intermetallic compound is the same, when B is composed of two or more elements, the molar ratio among the elements provided by B in the ternary high-entropy Laves-phase intermetallic compound is the same, and when C is composed of two or more elements, the molar ratio among the elements provided by C in the ternary high-entropy Laves-phase intermetallic compound is the same. The other is the same as one of the first to fourth embodiments.
The sixth specific implementation mode: the difference between this embodiment and one of the first to fifth embodiments is: the high-entropy Laves phase intermetallic compound is prepared by a fusion casting method, a rapid solidification method or a rapid solidification method combined with a powder metallurgy method. The other is the same as one of the first to fifth embodiments.
The seventh embodiment: the difference between this embodiment and one of the first to sixth embodiments is: the casting method comprises the steps of weighing and uniformly mixing all elements according to a molar ratio, smelting by adopting an electric arc furnace or an induction smelting furnace, and pouring alloy into a casting mold to obtain a high-entropy Laves phase intermetallic compound ingot or casting. The rest is the same as one of the first to sixth embodiments.
The specific implementation mode is eight: the present embodiment differs from one of the first to seventh embodiments in that: the rapid solidification method is to prepare the high-entropy Laves phase intermetallic compound in the shape of powder, thin slice or strip by a mold cooling technology, an atomization technology and a surface melting and deposition technology. The rest is the same as one of the first to seventh embodiments.
The specific implementation method nine: the present embodiment differs from the first to eighth embodiments in that: the rapid solidification method is combined with a powder metallurgy method, powder, thin slices or strip-shaped high-entropy Laves phase intermetallic compounds obtained by the rapid solidification method are sintered under the conditions of high temperature or high temperature and high pressure or are printed by a metal 3D printer, and high-entropy Laves phase intermetallic compound block materials or components are obtained. The rest is the same as the first to eighth embodiments.
The following examples were used to demonstrate the beneficial effects of the present invention:
the first embodiment is as follows: the high-entropy Laves phase intermetallic compound is a binary high-entropy Laves phase intermetallic compound with a chemical formula type of M2N, wherein M is Fe element and Cr element, and N is Ta element, Si element and Mo element; m reacts with N to form Fe2Ta、Fe2Si、Fe2Mo and Cr2The crystal structures of the four intermetallic compounds Ta are all Laves phases, the molar ratios of all elements provided by M in the binary high-entropy Laves-phase intermetallic compound are the same, the molar ratios of all elements provided by N in the binary high-entropy Laves-phase intermetallic compound are the same, and the molar fractions of Fe, Cr, Ta, Si and Mo in the binary high-entropy Laves-phase intermetallic compound are 66.67%, 33.33% and 33.33% in sequence.
The preparation method comprises the following steps: the raw materials of Fe element, Cr element, Ta element, Si element and Mo element are all simple substances (purity)>99.5 wt.%), and then placing the ingredients in a vacuum arc furnace, vacuumVacuumizing an electric arc furnace, flushing with high-purity argon, smelting the raw materials under the condition of argon protection, repeatedly smelting for 5 times, and smelting after turning an ingot by 180 degrees after finishing smelting each time; cooling the cast ingot obtained by the last smelting and solidification, and taking out the cast ingot from the vacuum electric arc furnace to obtain the binary M2An N-type high-entropy Laves phase intermetallic compound.
This binary M2The N-type high-entropy Laves phase intermetallic compound can also be prepared by adopting a rapid solidification technology (such as a mold cooling technology, an atomization technology, a surface melting and deposition technology) to prepare powder, thin slices or strip-shaped binary M2An N-type high-entropy Laves phase intermetallic compound. Binary M2The N-type high-entropy Laves phase intermetallic compound can also be prepared by adopting a powder metallurgy technology: preparing powder, slice or strip binary M by adopting rapid solidification technology or mechanical alloying technology2N-type high-entropy Laves phase intermetallic compound, powder, flake or strip binary M2Sintering the N-type high-entropy Laves phase intermetallic compound under the conditions of high temperature or high temperature and high pressure or printing by using a metal 3D printer to obtain the binary M2An N-type high-entropy Laves phase intermetallic compound bulk material or member.
FIG. 1 is an X-ray diffraction pattern of the binary high-entropy Laves-phase intermetallic compound obtained in example one, from which it can be seen that the binary M is finally obtained2The crystal structure of the N-type high-entropy Laves phase intermetallic compound is still mainly Laves phase, and the volume fraction of the solid solution or the nonmetal compound or the intermetallic compound with other crystal structures is only 0.001-0.8%; example one obtained binary high entropy Laves phase intermetallic compound and Fe2Ta、Fe2Si、Fe2Mo and Cr2Ta four intermetallic compounds, the binary M2The N-type high-entropy Laves phase intermetallic compound has excellent mechanical property, and the yield strength and plasticity at room temperature can be improved by more than one time.
Example two: the high-entropy Laves phase intermetallic compound is a binary high-entropy Laves phase intermetallic compound with a chemical formula type of M2N, wherein M is Fe element and Cr element, N is Ta element,Si element and Mo element; m reacts with N to form Fe2Ta、Fe2Si、Fe2Mo and Cr2The crystal structures of the four intermetallic compounds Ta are all Laves phases, the molar ratios of all elements provided by M in the binary high-entropy Laves-phase intermetallic compound are the same, and the molar fractions of Fe, Cr, Ta, Si and Mo in the binary high-entropy Laves-phase intermetallic compound are 66.67%, 33.33% and 33.33% in sequence. .
The preparation method comprises the following steps: the raw materials of Cr element, Fe element, Si element, Mo element and Ta element are all simple substances (purity)>99.5 wt.%), then putting the ingredients into a vacuum arc furnace, vacuumizing the vacuum arc furnace, flushing the vacuum arc furnace with high-purity argon, smelting the raw materials under the condition of argon protection, repeatedly smelting for 5 times, and smelting after turning the cast ingot 180 degrees after finishing smelting each time; cooling the cast ingot obtained by the last smelting and solidification, and taking out the cast ingot from the vacuum electric arc furnace to obtain the binary M2An N-type high-entropy Laves phase intermetallic compound.
This binary M2The N-type high-entropy Laves phase intermetallic compound can also be prepared by adopting a rapid solidification technology (such as a mold cooling technology, an atomization technology, a surface melting and deposition technology) to prepare powder, thin slices or strip-shaped binary M2An N-type high-entropy Laves phase intermetallic compound. Binary M2The N-type high-entropy Laves phase intermetallic compound can also be prepared by adopting a powder metallurgy technology: preparing powder, slice or strip binary M by adopting rapid solidification technology or mechanical alloying technology2N-type high-entropy Laves phase intermetallic compound, powder, flake or strip binary M2Sintering the N-type high-entropy Laves phase intermetallic compound under the conditions of high temperature or high temperature and high pressure or printing by using a metal 3D printer to obtain the binary M2An N-type high-entropy Laves phase intermetallic compound bulk material or member.
The resulting binary M2The crystal structure of the N-type high-entropy Laves phase intermetallic compound is still mainly the intermetallic compound of the Laves phase, solid solution or nonmetal compound or other crystal structuresThe volume fraction of the compound is only 0.002% -0.7%, and FIG. 2 is the X-ray diffraction pattern of the binary high-entropy Laves phase intermetallic compound obtained in example II, and the finally obtained binary M can be seen from the pattern2The crystal structure of the N-type high-entropy Laves phase intermetallic compound is still mainly Laves phase, and the volume fraction of the solid solution or the nonmetal compound or the intermetallic compound with other crystal structures is only 0.002% -0.7%; example two obtained binary high-entropy Laves phase intermetallic compound and Fe2Ta、Fe2Si、Fe2Mo and Cr2Ta four intermetallic compounds, the binary M2The N-type high-entropy Laves phase intermetallic compound has excellent mechanical property, and the room temperature hardness can be improved by more than one time.
Example three: a high-entropy Laves phase intermetallic compound is a ternary high-entropy Laves phase intermetallic compound, the type of a chemical formula is ABC, wherein A is Fe element, B is Cr element, and C is Ta element, Si element and Mo element; A. the reaction of B and C can form three intermetallic compounds of FeCrTa, FeCrSi and FeCrMo, the crystal structures are all Laves, the molar ratios of all elements provided by C in the ternary Laves phase intermetallic compound are the same, and the molar fractions of Fe, Cr, Ta, Si and Mo in the ternary high-entropy Laves phase intermetallic compound are 33.33%, 33.34% and 33.34% in sequence.
The preparation method comprises the following steps: preparing materials according to the molar fraction ratio, wherein raw materials of Fe element, Cr element, Ta element, Si element and Mo element are all simple substances (the purity is more than 99.5 wt.%), then putting the materials into a vacuum electric arc furnace, vacuumizing and flushing the vacuum electric arc furnace with high-purity argon, smelting the raw materials under the argon protection condition, repeatedly smelting for 5 times, and smelting after turning an ingot for 180 degrees every time of smelting is finished; and cooling the cast ingot obtained by the last smelting and solidification, and taking out the cast ingot from the vacuum electric arc furnace to obtain the ternary ABC type high-entropy Laves phase intermetallic compound.
The ternary ABC type high-entropy Laves phase intermetallic compound can also be prepared by adopting a rapid solidification technology (such as a die cooling technology, an atomization technology and a surface melting and deposition technology) to prepare the ternary ABC type high-entropy Laves phase intermetallic compound in the form of powder, thin slices or strips. The ternary ABC type high-entropy Laves phase intermetallic compound can also be prepared by adopting a powder metallurgy technology: the ternary ABC type high-entropy Laves phase intermetallic compound in the form of powder, thin slices or strips is prepared by adopting a rapid solidification technology or a mechanical alloying technology, and is sintered at a high temperature or under a high temperature and high pressure condition or is printed by a metal 3D printer to obtain the ternary ABC type high-entropy Laves phase intermetallic compound block material or component.
The crystal structure of the finally obtained ternary ABC type high-entropy Laves phase intermetallic compound is still mainly Laves phase, the volume fraction of solid solution or nonmetal compound or intermetallic compound with other crystal structure is only 0.001% -0.9%, FIG. 3 is the X-ray diffraction pattern of the ternary high-entropy Laves phase intermetallic compound obtained in the third embodiment, it can be seen from the pattern that the crystal structure of the finally obtained ternary ABC type high-entropy Laves phase intermetallic compound is still mainly Laves phase, and the volume fraction of the solid solution or nonmetal compound or intermetallic compound with other crystal structure is only 0.001% -0.9%; compared with three intermetallic compounds of FeCrTa, FeCrSi and FeCrMo, the ternary ABC type high-entropy Laves phase intermetallic compound obtained in the third embodiment has excellent mechanical properties, and the yield strength and hardness at room temperature can be improved by more than 25%.
In addition to the above specific examples, all the high entropy Laves phase intermetallic compounds with different compositions obtained by the design method according to the present invention, and the modifications or variations thereof based on the present invention are included in the scope of the present invention.

Claims (2)

1. A high-entropy Laves-phase intermetallic compound is characterized in that the high-entropy Laves-phase intermetallic compound is a binary high-entropy Laves-phase intermetallic compound with a chemical formula type of M2N, wherein M is Fe element and Cr element, and N is Ta element, Si element and Mo element; m reacts with N to form Fe2Ta、Fe2Si、Fe2Mo and Cr2Ta four Laves phasesThe crystal structures of the intermetallic compounds are all Laves phases, the molar ratios of all elements provided by M in the binary high-entropy Laves-phase intermetallic compounds are the same, the molar ratios of all elements provided by N in the binary high-entropy Laves-phase intermetallic compounds are the same, and the molar fractions of Fe, Cr, Ta, Si and Mo in the binary high-entropy Laves-phase intermetallic compounds are 66.67%, 33.33% and 33.33% in sequence.
2. A high entropy Laves phase intermetallic compound according to claim 1 characterized in that the preparation method of the high entropy Laves phase intermetallic compound is performed by the following steps: preparing materials according to the proportion that the mole fraction of Fe element, Cr element, Ta element, Si element and Mo element is 66.67%, 33.33% and 33.33%, wherein the raw materials of the Fe element, the Cr element, the Ta element, the Si element and the Mo element are simple substances with the purity of more than 99.5 wt%, then putting the materials into a vacuum electric arc furnace, vacuumizing the vacuum electric arc furnace, flushing the vacuum electric arc furnace with high-purity argon, smelting the raw materials under the protection of argon, repeatedly smelting for 5 times, and smelting after turning an ingot by 180 degrees after finishing one smelting; cooling the cast ingot obtained by the last smelting and solidification, and taking out the cast ingot from the vacuum electric arc furnace to obtain the binary M2An N-type high-entropy Laves phase intermetallic compound.
CN202111390850.3A 2021-11-23 2021-11-23 High-entropy Laves phase intermetallic compound Withdrawn CN114196861A (en)

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN115821141A (en) * 2022-09-23 2023-03-21 哈尔滨工业大学 Laves phase precipitation modified AlCoCrFeNi two-phase high-entropy alloy and preparation method thereof

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN115821141A (en) * 2022-09-23 2023-03-21 哈尔滨工业大学 Laves phase precipitation modified AlCoCrFeNi two-phase high-entropy alloy and preparation method thereof
CN115821141B (en) * 2022-09-23 2023-11-24 哈尔滨工业大学 Laves phase precipitation modified AlCoCrFeNi dual-phase high-entropy alloy and preparation method thereof

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Application publication date: 20220318