US20170314097A1 - High-strength and ultra heat-resistant high entropy alloy (hea) matrix composites and method of preparing the same - Google Patents

High-strength and ultra heat-resistant high entropy alloy (hea) matrix composites and method of preparing the same Download PDF

Info

Publication number
US20170314097A1
US20170314097A1 US15/495,411 US201715495411A US2017314097A1 US 20170314097 A1 US20170314097 A1 US 20170314097A1 US 201715495411 A US201715495411 A US 201715495411A US 2017314097 A1 US2017314097 A1 US 2017314097A1
Authority
US
United States
Prior art keywords
hea
forming
alloy
matrix composite
metal
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Pending
Application number
US15/495,411
Inventor
Soon Hyung Hong
Ho Jin Ryu
Bin Lee
Jun Ho Lee
Rizaldy Muhammad Pohan
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Korea Advanced Institute of Science and Technology KAIST
Original Assignee
Korea Advanced Institute of Science and Technology KAIST
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority to KR20160053871 priority Critical
Priority to KR1020160053871 priority
Priority to KR1020170035200A priority patent/KR101927611B1/en
Priority to KR1020170035200 priority
Application filed by Korea Advanced Institute of Science and Technology KAIST filed Critical Korea Advanced Institute of Science and Technology KAIST
Assigned to KOREA ADVANCED INSTITUTE OF SCIENCE AND TECHNOLOGY reassignment KOREA ADVANCED INSTITUTE OF SCIENCE AND TECHNOLOGY ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: HONG, SOON HYUNG, LEE, BIN, LEE, JUN HO, POHAN, RIZALDY MUHAMMAD, RYU, HO JIN
Publication of US20170314097A1 publication Critical patent/US20170314097A1/en
Pending legal-status Critical Current

Links

Images

Classifications

    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C1/00Making alloys
    • C22C1/04Making alloys by powder metallurgy
    • C22C1/05Mixtures of metal powder with non-metallic powder
    • C22C1/051Making hard metals based on borides, carbides, nitrides, oxides or silicides; Preparation of the powder mixture used as the starting material
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C1/00Making alloys
    • C22C1/04Making alloys by powder metallurgy
    • C22C1/0433Nickel- or cobalt-based alloys
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C1/00Making alloys
    • C22C1/10Alloys containing non-metals
    • C22C1/1084Alloys containing non-metals by mechanical alloying (blending, milling)
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C21/00Alloys based on aluminium
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C32/00Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides whether added as such or formed in situ
    • C22C32/001Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides whether added as such or formed in situ with only oxides
    • C22C32/0015Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides whether added as such or formed in situ with only oxides with only single oxides as main non-metallic constituents
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C32/00Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides whether added as such or formed in situ
    • C22C32/0047Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C32/00Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides whether added as such or formed in situ
    • C22C32/0089Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides whether added as such or formed in situ with other, not previously mentioned inorganic compounds as the main non-metallic constituent, e.g. sulfides, glass
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C33/00Making ferrous alloys
    • C22C33/02Making ferrous alloys by powder metallurgy
    • C22C33/0257Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B22CASTING; POWDER METALLURGY
    • B22FWORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER
    • B22F2998/00Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10Processes characterised by the sequence of their steps

Abstract

A high-strength and ultra heat-resistant high entropy alloy (HEA) matrix composite material and a method of preparing the HEA matrix composite material are provided. The HEA matrix composite material may include at least four matrix elements among Co, Cr, Fe, Ni, Mn, Cu, Mo, V, Nb, Ta, Ti, Zr, W, Si, Hf and Al, and a body-centered cubic (BCC) forming alloy element.

Description

    CROSS-REFERENCE TO RELATED APPLICATION
  • This application claims the benefit of Korean Patent Application No. 10-2016-0053871, filed on May 2, 2016, and Korean Patent Application No. 10-2017-0035200 filed on Mar. 21, 2017, in the Korean Intellectual Property Office, the disclosures of which are incorporated herein by reference.
  • BACKGROUND 1. Field of the Invention
  • At least one example embodiment relates to a high-strength and ultra heat-resistant high entropy alloy (HEA) matrix composite material and a method of preparing the HEA matrix composite material.
  • 2. Description of the Related Art
  • Existing alloy materials have been developed to enhance characteristics, for example, a hardness, a toughness, a heat resistance, a corrosion resistance, and the like, by addition of trace elements based on main metals, for example, Ti, Ni, and the like. Currently, such development of alloy materials by addition of trace elements has reached its limit.
  • Recently, research on high entropy alloys (HEAs) is being actively conducted. HEAs are reported to have excellent mechanical properties in comparison to existing metals due to effects of the HEAs, for example, a sluggish diffusion, a lattice distortion caused by a difference in size between elements, and a high mixing entropy by mixing at least four or five metal elements in near-equiatomic ratios.
  • A CoCrFeMnNi HEA reported in the journal Science in 2014 exhibits a fracture toughness of about 200 MPa·m0.5 and has physical properties close to three times that of a titanium alloy, and accordingly is gaining attention as next-generation extreme environment materials that may replace existing alloys.
  • In a high-energy milling process using a face-centered cubic (FCC) HEA with a high ductility, cold welding in a ball and a container may occur, which may lead to a reduction in a powder yield and a contamination by the ball.
  • In a composite HEA to which a reinforcing material is added, the reinforcing material may tend to be a reactive site that causes cold welding, and a yield may be severely reduced due to the cold welding. Thus, there is a desire for a new technology for reducing a cold welding phenomenon of a composite HEA using a powder metallurgy process.
  • SUMMARY
  • The present disclosure is to solve the foregoing problems, and an aspect provides a high entropy alloy (HEA) matrix composite material and a method of preparing the HEA matrix composite material which may significantly increase a yield by reducing a cold welding phenomenon while enhancing mechanical properties and heat resistance of an alloy.
  • However, the problems to be solved in the present disclosure are not limited to the foregoing problems, and other problems not mentioned herein would be clearly understood by one of ordinary skill in the art from the following description.
  • According to an aspect, there is provided a HEA matrix composite material including at least four matrix elements among Co, Cr, Fe, Ni, Mn, Cu, Mo, V, Nb, Ta, Ti, Zr, W, Si, Hf and Al, and a body-centered cubic (BCC) forming alloy element.
  • The HEA matrix composite material may further include a reinforcing material. The reinforcing material may include at least one of a metal oxide, a metal silicide, a metal carbide, a metal nitride and a metal boride. Each of the metal oxide, the metal silicide, the metal carbide, the metal nitride and the metal boride may include at least one selected from the group consisting of Al, Si, Ti, Zr, Ta, Mg, Be, Ba, Zn, Cr, Y, Sn, W, Hf, V, Nb, Mo, W, La and B.
  • The reinforcing material may be present in an amount of 0.01% by volume (vol %) to 50 vol % in the HEA matrix composite material.
  • A valence electron concentration (VEC) of the BCC forming alloy element may be less than or equal to “7.”
  • The BCC forming alloy element may be different from the matrix elements, and may include at least one of, Al, Cr, Mn, Mo, Nb, Ta, Ti, V and W.
  • The BCC forming alloy element may be present in an amount of 0.01% by moles (mol %) to 90 mol % in the HEA matrix composite material.
  • A VEC of the HEA matrix composite material may be less than or equal to “10.”
  • The HEA matrix composite material may further include a precipitate(s). The precipitate(s) may include at least one of a metal oxide, a metal silicide, a metal carbide, a metal nitride, a metal boride and an intermetallic compound. Each of the metal oxide, the metal carbide, the metal nitride, the metal boride and the intermetallic compound may include at least one of Co, Cr, Fe, Ni, Mn, Cu, Mo, V, Nb, Al, Si, Ti, Zr, Ta, Mg, Be, Ba, Zn, Cr, Y, Sn, W, Hf, Nb, Ta, Mo, W, Ta, La and B.
  • The precipitate(s) may include at least one of Ni3Nb, TiC, MoC, CrC, Cr23C6, Mo23C6, W23C6, Co23C6, Fe23C6, Mo6C, W6C, Co6C, Ni6C, Ni3Al, Ni3Ti, TiAl and CraMobNic in which a, b and c are rational numbers.
  • According to another aspect, there is provided a method of preparing a HEA matrix composite material, including preparing a powder mixture by mixing a body-centered cubic (BCC) forming alloy element and at least four matrix elements selected from the group consisting of Co, Cr, Fe, Ni, Mn, Cu, Mo, V, Nb, Ta, Ti, Zr, W, Si, Hf and Al, forming a mechanically alloyed powder by mechanically alloying the powder mixture, and sintering the mechanically alloyed powder at a high temperature, wherein the forming of the mechanically alloyed powder includes bonding the BCC forming alloy element to at least a portion of the matrix elements.
  • The forming of the mechanically alloyed powder may include acquiring a HEA matrix composite material at a yield of 50% or greater using a high-energy ball mill.
  • The preparing of the powder mixture may include adding either a reinforcing material or a precipitate(s) forming element, or both to the powder mixture.
  • The method may further include, after the preparing of the powder mixture or the forming of the mechanically alloyed powder, adding a precipitate(s) forming element. The precipitate(s) forming element may include at least one of Co, Cr, Fe, Ni, Mn, Cu, Mo, V, Nb, Al, Si, Ti, Z, Zr, Ta, Mg, Be, Ba, Zn, Cr, Y, Sn, W, Hf, Nb, Mo, W, La and B.
  • The method may further include, after the sintering of the mechanically alloyed powder, forming a precipitate(s). The forming of the precipitate(s) may include forming the precipitate(s) by a heat treatment at a temperature of 300° C. to 1500° C.
  • The sintering of the mechanically alloyed powder may include sintering the mechanically alloyed powder at a temperature corresponding to 50% to 99% of a melting point of the mechanically alloyed powder.
  • Additional aspects of example embodiments will be set forth in part in the description which follows and, in part, will be apparent from the description, or may be learned by practice of the disclosure.
  • BRIEF DESCRIPTION OF THE DRAWINGS
  • These and/or other aspects, features, and advantages of the invention will become apparent and more readily appreciated from the following description of example embodiments, taken in conjunction with the accompanying drawings of which:
  • FIG. 1 is a flowchart illustrating a method of preparing a high entropy alloy (HEA) matrix composite material according to an example embodiment;
  • FIG. 2 is a diagram illustrating yields of powders of HEA matrix composite materials prepared in Examples 1, 2 and 3 and Comparative Examples 1 and 2 according to an example embodiment;
  • FIG. 3 is an X-ray diffraction (XRD) graph of HEA matrix composite materials prepared in Examples 1 to 3 according to an example embodiment;
  • FIG. 4 illustrates scanning electron microscopy (SEM) images of HEA matrix composite materials prepared in Examples 1 and 2 according to an example embodiment;
  • FIG. 5 is a graph illustrating a hardness of HEA matrix composite materials prepared in Examples 1 to 3 and Comparative Examples 1 and 2 according to an example embodiment; and
  • FIG. 6 is a graph illustrating a compressive strength of a HEA matrix composite material prepared in Example 1 according to an example embodiment.
  • DETAILED DESCRIPTION
  • Hereinafter, example embodiments of the present disclosure will be described in detail with reference to the accompanying drawings. When it is determined detailed description related to a related known function or configuration they may make the purpose of the present disclosure unnecessarily ambiguous in describing the present disclosure, the detailed description will be omitted here. Also, terms used herein are defined to appropriately describe the example embodiments and thus may be changed depending on a user, the intent of an operator, or a custom of a field to which the present disclosure pertains. Accordingly, the terms must be defined based on the following overall description of this specification. Like reference numerals present in the drawings refer to the like elements throughout.
  • According to an example embodiment, a high entropy alloy (HEA) matrix composite material may be provided. The HEA matrix composite material may slightly increase a brittleness of a powder by adding a body-centered cubic (BCC) forming alloy element to a HEA matrix having a face-centered cubic (FCC) structure, to prevent a cold welding phenomenon and to increase a yield of an alloyed powder in a mechanical alloying process. Also, a precipitate(s) as well as a γ′ phase, an oxide, a carbide, a nitride, a boride and a silicide may be formed, and thus it is possible to enhance both a high-temperature stability and mechanical properties of an alloy.
  • The HEA matrix composite material may include a matrix element, and a BCC forming alloy element. The HEA matrix composite material may further include a reinforcing material and/or a precipitate(s).
  • The matrix element may be used to form a matrix HEA of the HEA matrix composite material, and may desirably be an element to form an alloy with an FCC structure. For example, all elements capable of forming an alloy with an FCC structure may be used as the matrix element without a limitation. The matrix element may include, for example, at least four of Co, Cr, Fe, Ni, Mn, Cu, Mo, V, Nb, Ta, Ti, Zr, W, Si, Hf and Al, and may desirably include, for example, a quaternary alloy such as CoCrFeNi, CoCrFeMn, CoCrFeCu, CoCrFeMo, CoCrFeV, CoCrFeNb, CuCrFeNi and CoCrCuNi; a quinary alloy such as CoCrFeNiMn, CoCrFeNiCu, CoCrFeNiMn, CoCrFeNiMo, CoCrFeNiV, CuCrFeNiMn, CoCrCuFeNi and CoCrFeNiNb; and a senary alloy such as CoCrFeNiMnMo, CoCrFeNiMnCu, CoCrFeNiMnV and CoCrFeNiMnNb.
  • The matrix element may be present in an amount of 5% by moles (mol %) to 35 mol % in the matrix HEA.
  • The BCC forming alloy element may be used to prevent cold welding and to enhance mechanical properties. For example, a BCC forming alloy element for reducing an average valence electron concentration (VEC) of an alloy to be less than or equal to “8” may be added to an alloy matrix, for example, an FCC alloy matrix with an average VEC greater than or equal to “8.” Thus, cold welding may be prevented in a mechanical alloying process and a yield of an alloyed powder may be significantly enhanced. Also, a contamination by a ball due to the cold welding may be prevented, and mechanical properties of an alloy may be enhanced.
  • For example, the BCC forming alloy element may be an element to reduce an average VEC of a HEA, and may have a VEC less than or equal to “7,” a VEC less than or equal to “6.8,” or a VEC less than or equal to “5.” The BCC forming alloy element may include, for example, at least one of Al, Cr, Mn, Mo, Nb, Ta, Ti, V and W. The BCC forming alloy element may be different from the matrix element. A VEC may refer to a sum of the number of peripheral electrons and the number of electrons included in a d-orbital. Based on the paper published by Guo et al. in the Journal of Applied Physics in 2011, an FCC phase and a BCC phase of a HEA may be determined by a VEC of a component of the HEA.
  • The BCC forming alloy element may be present in an amount of 0.01 mol % to 90 mol %, an amount of 0.1 mol % to 60 mol %, an amount of 0.1 mol % to 30 mol %, an amount of 0.1 mol % to 20 mol %, or an amount of 0.1 mol % to 5 mol % in the HEA matrix composite material. When the amount of the BCC forming alloy element is within the above ranges, a metal composite material that has excellent mechanical properties and that is used to prevent cold welding in a mechanical alloying process may be provided.
  • The reinforcing material may be used to enhance a strength of the HEA matrix composite material. The reinforcing material may include, for example, at least one of a metal oxide, a metal silicide, a metal carbide, a metal nitride and a metal boride. Each of the metal oxide, the metal silicide, the metal carbide, the metal nitride and the metal boride may include, for example, at least one of Al, Si, Ti, Zr, Ta, Mg, Be, Ba, Zn, Cr, Y, Sn, W, Hf, V, Nb, Mo, W, La, and B.
  • The metal oxide may include, for example, at least one of Al2O3, SiO2, TiO2, ZrO2, Ta2O5, MgO, BeO, BaTiO3, ZnO, BaO, CrO2, Y2O3, SnO2, WO2, W2O3, and WO3. The metal carbide may include, for example, at least one of SiC, TiC, ZrC, HfC, VC, NbC, TaC, Mo2C and WC. The metal nitride may include, for example, at least one of TiN, ZrN, HfN, VN, NbN, TaN, AlN, AlON, and Si3N4. The metal boride may include, for example, at least one of TiB2, ZrB2, HfB2, VB2, NbB2, TaB2, WB2, MoB2, B4C and LaB6.
  • The reinforcing material may be present in an amount of 0.01% by volume (vol %) to 50 vol % and desirably in an amount of 0.05 vol % to 10 vol % in the HEA matrix composite material. When the amount of the reinforcing material is within the above ranges, the reinforcing material may be uniformly dispersed in an alloy matrix and a strength of a metal composite material may be enhanced.
  • The precipitate(s) may enhance high-temperature properties of a metal composite material so that a HEA matrix composite material applicable as a material for a high temperature may be formed. The precipitate(s) may be formed by, for example, at least one of a matrix element, a BCC forming alloy element and an added precipitate(s) forming element or material. The precipitate(s) may include a γ′ phase, and/or at least one of an oxide, a carbide, a nitride, a boride, a silicide and an intermetallic compound.
  • For example, the γ′ phase may be a crystalline phase that includes at least one element or at least two elements among a BCC forming alloy element, a precipitate(s) forming element and a matrix element dispersed in a matrix HEA. The γ′ phase may include, for example, at least one of Ni3Al, Ni3Ti and TiAl.
  • The oxide, the carbide, the nitride, the boride, the silicide and the intermetallic compound in the precipitate(s) may include, for example, at least one of a metal oxide, a metal silicide, a metal carbide, a metal nitride, a metal boride and an intermetallic compound. Each of the metal oxide, the metal silicide, the metal carbide, the metal nitride, the metal boride and the intermetallic compound may include, for example, at least one of Co, Cr, Fe, Ni, Mn, Cu, Mo, V, Nb, Al, Si, Ti, Zr, Ta, Mg, Be, Ba, Zn, Cr, Y, Sn, W, If, Nb, Mo, W, La and B.
  • The metal carbide may include, for example, TiC, MoC, CrC, Cr23C6, Mo23C6, W23C6, Co23C6, Fe23C6, Mo6C, W6C, Co6C, Ni6C, and the like.
  • The intermetallic compound may be, for example, an intermetallic compound with at least two elements. The intermetallic compound with at least two elements may include, for example, M1 aM2 b and M1 aM2 bM3 c (in which M1, M2 and M3 are selected from Co, Cr, Fe, Ni, Mn, Cu, Mo, V, Nb, Al, Si, Ti, Zr, Ta, Mg, Bo, Ba, Zn, Cr, Y, Sn, W, Hf, Nb, Mo, W, La, and B, and a, b and c denote the same rational number or different rational numbers and may be a rational number less than or equal to “100”). For example, M1 aM2 b may be Ni3Nb, Ni3Al, Ni3Ti, TiAl, and the like, and M1 aM2 bM3 c may be a CrMoNi-based compound, such as CraMobNic, and the like.
  • In an example, the precipitate(s) may be formed by either a matrix element or a BCC forming alloy element, or both in a process of alloying the HEA matrix composite material, and/or may be formed by adding a precipitate(s) forming element before or after a mechanically alloyed powder is formed. In another example, the precipitate(s) may be formed by sintering the mechanically alloyed powder and/or by a heat treatment after the sintering.
  • For example, the precipitate(s) forming element may be the same as or different from a matrix element. The precipitate(s) forming may include, for example, at least one of Co, Cr, Fe, Mn, Cu, Mo, V, Nb, Ni, Al, Si, Ti, Zr, Ta, Mg, Be, Ba, Zn, Cr, Y, Sn, W, Hf, V, Nb, Ta, Mo, W, Ta, La, and B. The precipitate(s) forming element may be present in an amount exceeding 0 mol % and less than or equal to 300 mol %, and desirably in an amount of 1 mol % to 100 mol % with respect to the matrix element and/or the BCC forming alloy element.
  • The HEA matrix composite material may have an average VEC less than or equal to “10,” an average VEC of “5” to “8,” or an average VEC of “6” to “7.5.” For example, the matrix element may form an FCC structure. Accordingly, when a BCC forming alloy element with a lower VEC than that of the matrix element is added, an average VEC of an alloy matrix composite material may be reduced and the alloy matrix composite material may have both a BCC structure and an FCC structure. Also, by reducing the average VEC of the alloy matrix composite material, it is possible to prevent cold welding between matrix alloy elements in a mechanical alloying process.
  • According to an example embodiment, a method of preparing a HEA matrix composite material may be provided. In the method, a BCC forming alloy element may be added to a matrix element or a reinforcing material may be additionally added, and thus it is possible to enhance a mechanical strength and a yield of the HEA matrix composite material. Also, a precipitate(s) may be additionally added, and thus it is possible to enhance a high-temperature characteristic of the HEA matrix composite material.
  • FIG. 1 is a flowchart illustrating a method of preparing a HEA matrix composite material according to an example embodiment. The method of FIG. 1 may include operation 110 of preparing a powder mixture, operation 120 of forming a mechanically alloyed powder, and operation 130 of sintering the mechanically alloyed powder at a high temperature.
  • In operation 110, the powder mixture may be prepared by mixing a matrix element and a BCC forming alloy element. The matrix element and the BCC forming alloy element have been described above in the description of the HEA matrix composite material. A powder mixing method applicable in the technical field of the present disclosure may be used in operation 110, and accordingly further description thereof is not repeated herein.
  • In operation 120, the mechanically alloyed powder may be formed by mechanically alloying the powder mixture. Operation 120 may be performed to prevent cold welding of powders in a mechanical alloying process by adding the BCC forming alloy element so as to increase a yield of an alloy, and to prevent impurities from flowing into the alloy by preventing a contamination by a ball mill.
  • In an example, in operation 120, the BCC forming alloy element may be bonded to at least a portion of the matrix element and may be dispersed in the alloy matrix. In another example, the BCC forming alloy element may be bonded to at least a portion of the matrix element, to form a BCC alloy. The BCC alloy may also be dispersed in the alloy matrix.
  • In operation 110, a reinforcing material (for example, a reinforcing material forming element and/or material) may be additionally added to the powder mixture. The reinforcing material has been described above.
  • For example, operation 120 may be performed within 120 hours, for a period of 1 hour to 120 hours, or a period of 10 hours to 50 hours.
  • In operation 120, the HEA matrix composite material may be provided at a yield greater than or equal to 50%, a yield greater than or equal to 60%, a yield greater than or equal to 80%, or a yield greater than or equal to 90%.
  • In operation 120, a high-energy ball mill may be used. For example, a vibration mill, a planetary mill, an attrition mill, and the like may be used, however, there is no limitation thereto.
  • In operation 130, the mechanically alloyed powder may be sintered at a high temperature so that the mechanically alloyed powder may be formed of bulk materials. For example, in operation 130, a normal sintering method, a reaction sintering method, a pressurizing sintering method, an isostatic pressure sintering method, a gas pressure sintering method, or a high-temperature pressurizing sintering method may be used, however, there is no limitation thereto.
  • In operation 130, the mechanically alloyed powder may be sintered at a temperature that corresponds to 50% to 99%, 50% to 80%, 60% to 80%, 70% to 80%, 50% to 70%, 60% to 70%, or 50% to 60% of a melting point of the mechanically alloyed powder.
  • Operation 130 may be performed in an atmosphere including at least one of air, nitrogen, carbon and boron for 60 hours or less, for a period of 1 minute to 60 hours, a period of 5 minutes to 10 hours, a period of 5 minutes to 5 hours or a period of 5 minutes to 1 hour.
  • The method may further include operation 140 of adding a precipitate(s) forming element. Operation 140 may be performed after operation 110 to add and mix the precipitate(s) forming element and the powder mixture, and/or operation 140 may be performed after operation 120 to add and mix the precipitate(s) forming element and the mechanically alloyed powder and to further perform mechanical alloying as necessary.
  • In operation 140, the precipitate(s) forming element may be added in an amount exceeding 0 mol % and less than or equal to 300 mol %, and desirably in an amount of 1 mol % to 100 mol %, with respect to the matrix element and/or the BCC forming alloy element.
  • The method may further include operation 150 of forming a precipitate(s). In operation 150, the precipitate(s) may be formed by a heat treatment of the mechanically alloyed powder sintered in operation 130. For example, the heat treatment may be performed at a temperature of 300° C. to 1500° C. for 60 hours or less, for a period of 1 minute to 60 hours, a period of 10 minutes to 50 hours, a period of 1 hour to 20 hours, or a period of 1 hour to 10 hours. When a temperature and a period of time for the heat treatment are within the above ranges, the precipitate(s) may be efficiently formed, and a high-temperature characteristic of an alloy material may be enhanced. For example, in operation 150, the heat treatment may be performed in an atmosphere including at least one of air, nitrogen, carbon and boron.
  • Example 1
  • Mechanical alloying was performed using a planetary mill for 24 hours, to prepare an Al0.3CoCrFeMnNi HEA powder to which 3 vol % of Y2O3 was added. About 5.7 mol % of Al was added as a BCC forming alloy element. A yield of the prepared Al0.3CoCrFeMnNi HEA powder is shown in FIG. 2.
  • The prepared 3 vol % Y2O3/Al0.3CrCrFeMnNi HEA powder was sintered at 900° C. for 5 minutes using a spark plasma sintering method, to prepare a sintered alloy. A phase and a microstructure of the sintered alloy were analyzed and a hardness and a compressive strength of the sintered alloy were measured as shown in FIGS. 3 to 6. The microstructure was obtained by a scanning electron microscope (SEM).
  • Example 2
  • Mechanical alloying was performed using a planetary mill for 24 hours, to prepare an Al0.3CoCrFeMnNi HEA powder to which 5 vol % of TiC was added. About 5.7 mol % of Al was added as a BCC forming alloy element. A yield of the prepared Al0.3CoCrFeMnNi HEA powder is shown in FIG. 2.
  • The prepared 5 vol % TiC/Al0.3CoCrFeMnNi HEA powder was sintered at 900° C. for 5 minutes using a spark plasma sintering method, to prepare a sintered alloy. A phase and a microstructure of the sintered alloy were analyzed and a hardness of the sintered alloy was measured as shown in FIGS. 3 to 5.
  • Example 3
  • Mechanical alloying was performed using a planetary mill for 24 hours, to prepare a Mo0.8CoCrFeMnNi HEA powder. About 13.8 mol % of Mo was added as a BCC forming alloy element. A yield of the prepared Mo0.8CoCrFeMnNi HEA powder is shown in FIG. 2.
  • The prepared Mo0.8CoCrFeMnNi HEA powder was sintered at 900° C. for 5 minutes using a spark plasma sintering method, to prepare a sintered alloy. A phase and a microstructure of the sintered alloy were analyzed and a hardness of the sintered alloy was measured as shown in FIGS. 3 to 5.
  • Comparative Example 1
  • An alloyed powder was prepared in the same manner as in Example 1 except that a CoCrFeNiMn HEA was formed. A yield of the alloyed powder is shown in FIG. 2. The prepared CoCrFeNiMn HEA powder was sintered at 900° C. for 5 minutes using a spark plasma sintering method, to prepare a sintered alloy. A hardness of the sintered alloy was measured as shown in FIG. 5.
  • Comparative Example 2
  • An alloyed powder was prepared in the same manner as in Example 1 except that a CoCrFeNiMn HEA to which 3 vol % of Y2O3 was added was formed. A yield of the alloyed powder is shown in FIG. 2. The prepared CoCrFeNiMn HEA was sintered at 900° C. for 5 minutes using a spark plasma sintering method, to prepare a sintered alloy. A hardness of the sintered alloy was measured as shown in FIG. 5.
  • Referring to FIG. 2, the CoCrFeNiMn HEA of Comparative Example 1 to which Al was not added as a BCC alloying element has a yield of 17.6%, and the CoCrFeNiMn HEA of Comparative Example 2 to which 3 vol % of Y2O3 was added has a yield of 16.4%, whereas the Al0.3CoCrFeMnNi HEA powder of Example 1 to which 3 vol % of Y2O3 was added has a yield of 81.2% that is superior to the yields of the CoCrFeNiMn HEAs of Comparative Examples 1 and 2. This is because most of powders are entangled in a ball and a container due to cold welding in a mechanical alloying process, thereby lowering a yield of the alloyed powder. However, since Al was added as a BCC alloying element to the 3 vol % Y2O3/Al0.3CoCrFeMnNi HEA powder in Example 1, it is possible to reduce the cold welding by enhancing a brittleness of the powder, and possible to obtain an alloyed powder at a high yield.
  • In an X-ray diffraction (XRD) graph of FIG. 3, a phase analysis of the sintered alloy is shown. It can be found from the XRD graph that Mo was added to the sintered alloy prepared in Example 3, to form a BCC phase and to form a precipitate that includes Cr, Mo and Ni.
  • Referring to FIG. 4, it can be found that reinforcing materials are uniformly dispersed as shown in SEM images that show the microstructures of the sintered alloys of Examples 1 and 2.
  • Referring to FIG. 5, it can be found that the hardness of the Al0.3CoCrFeMnNi alloy to which 3 vol % of Y2O3 was added in Example 1 and the hardness of the Al0.3CoCrFeMnNi alloy to which 5 vol % of TiC was added in Example 2 were enhanced in comparison to the CoCrFeNiMn alloy of Comparative Example 1 and the CoCrFeNiMn alloy of Comparative Example 2 to which 3 vol % of Y2O3 was added. Referring to FIG. 6, it can be found that the 3 vol % Y2O3/Al0.3CoCrFeMnNi alloy of Example 1 has a high compressive strength, which may indicate that mechanical properties may be enhanced by adding Al and a reinforcing material and a powder yield may also be enhanced by adding Al as a BCC alloying element to a HEA.
  • Thus, a BCC forming alloy element and a reinforcing material may be added, to enhance a heat resistance and mechanical properties of a HEA matrix composite material, to prevent cold welding in a mechanical alloying process, and to increase a yield of an alloyed powder.
  • According to example embodiments, it is possible to prevent cold welding by adding a BCC forming alloy element to a HEA matrix, to increase a yield of an alloyed powder of a HEA matrix composite material. Also, it is possible to enhance a heat resistance and mechanical properties of the HEA matrix composite material by additionally adding a reinforcing material.
  • Although the example embodiments have been described with reference to the accompanying drawings, the present disclosure is not limited to the described example embodiments. Instead, it would be appreciated by one of ordinary skill in the art that various modifications and changes may be made to these example embodiments without departing from the principles and spirit of the present disclosure. It is intended therefore that the scope of the present invention not be limited to the foregoing embodiments, but be defined by the claims appended hereto and their equivalents.

Claims (14)

What is claimed is:
1. A high entropy alloy (HEA) matrix composite material comprising:
at least four matrix elements selected from the group consisting of Co, Cr, Fe, Ni, Mn, Cu, Mo, V, Nb, Ta, Ti, Zr, W, Si, Hf and Al; and
a body-centered cubic (BCC) forming alloy element.
2. The HEA matrix composite material of claim 1, further comprising:
a reinforcing material comprising at least one selected from the group consisting of a metal oxide, a metal silicide, a metal carbide, a metal nitride and a metal boride,
wherein each of the metal oxide, the metal silicide, the metal carbide, the metal nitride and the metal boride comprises at least one selected from the group consisting of Al, Si, Ti, Zr, Ta, Mg, Be, Ba, Zn, Cr, Y, Sn, W, Hf, V, Nb, Mo, W, La and B.
3. The HEA matrix composite material of claim 2, wherein the reinforcing material is present in an amount of 0.01% by volume (vol %) to 50 vol % in the HEA matrix composite material.
4. The HEA matrix composite material of claim 1, wherein a valence electron concentration (VEC) of the BCC forming alloy element is less than or equal to “7.”
5. The HEA matrix composite material of claim 1, wherein the BCC forming alloy element is different from the matrix elements, and comprises at least one selected from the group consisting of, Al, Cr, Mn, Mo, Nb, Ta, Ti, V and W.
6. The HEA matrix composite material of claim 1, wherein the BCC forming alloy element is present in an amount of 0.01% by moles (mol %) to 90 mol % in the HEA matrix composite material.
7. The HEA matrix composite material of claim 1, wherein a VEC of the HEA matrix composite material is less than or equal to “10.”
8. The HEA matrix composite material of claim 1, further comprising:
a precipitate(s) comprising at least one selected from the group consisting of a metal oxide, a metal silicide, a metal carbide, a metal nitride, a metal boride and an intermetallic compound,
wherein each of the metal oxide, the metal carbide, the metal nitride, the metal boride and the intermetallic compound comprises at least one selected from the group consisting of Co, Cr, Fe, Ni, Mn, Cu, Mo, V, Nb, Al, Si, Ti, Zr, Ta, Mg, Be, Ba, Zn, Cr, Y, Sn, W, Hf, Nb, Mo, W, La and B.
9. A method of preparing a high entropy alloy (HEA) matrix composite material, the method comprising:
preparing a powder mixture by mixing a body-centered cubic (BCC) forming alloy element and at least four matrix elements selected from the group consisting of Co, Cr, Fe, Ni, Mn, Cu, Mo, V, Nb, Ta, Ti, Zr, W, Si, Hf and Al;
forming a mechanically alloyed powder by mechanically alloying the powder mixture; and
sintering the mechanically alloyed powder at a high temperature,
wherein the forming of the mechanically alloyed powder comprises bonding the BCC forming alloy element to at least a portion of the matrix elements.
10. The method of claim 9, wherein the forming of the mechanically alloyed powder comprises acquiring a HEA matrix composite material at a yield of 50% or greater using a high-energy ball mill.
11. The method of claim 9, wherein the preparing of the powder mixture comprises adding a reinforcing material to the powder mixture.
12. The method of claim 9, further comprising, after the preparing of the powder mixture or the forming of the mechanically alloyed powder:
adding a precipitate(s) forming element,
wherein the precipitate(s) forming element comprises at least one selected from the group consisting of Co, Cr, Fe, Ni, Mn, Cu, Mo, V, Nb, Al, Si, Ti, Zr, Ta, Mg, Be, Ba, Zn, Cr, Y, Sn, W, Hf, Nb, Ta, Mo, W, Ta, La and B.
13. The method of claim 9, further comprising, after the sintering of the mechanically alloyed powder:
forming a precipitate(s),
wherein the forming of the precipitate(s) comprises forming the precipitate(s) by a heat treatment at a temperature of 300° C. to 1500° C.
14. The method of claim 9, wherein the sintering of the mechanically alloyed powder comprises sintering the mechanically alloyed powder at a temperature corresponding to 50% to 99% of a melting point of the mechanically alloyed powder.
US15/495,411 2016-05-02 2017-04-24 High-strength and ultra heat-resistant high entropy alloy (hea) matrix composites and method of preparing the same Pending US20170314097A1 (en)

Priority Applications (4)

Application Number Priority Date Filing Date Title
KR20160053871 2016-05-02
KR1020160053871 2016-05-02
KR1020170035200A KR101927611B1 (en) 2016-05-02 2017-03-21 High- strength and heat-resisting high entropy alloy matrix composites and method of manufacturing the same
KR1020170035200 2017-03-21

Publications (1)

Publication Number Publication Date
US20170314097A1 true US20170314097A1 (en) 2017-11-02

Family

ID=60158187

Family Applications (1)

Application Number Title Priority Date Filing Date
US15/495,411 Pending US20170314097A1 (en) 2016-05-02 2017-04-24 High-strength and ultra heat-resistant high entropy alloy (hea) matrix composites and method of preparing the same

Country Status (1)

Country Link
US (1) US20170314097A1 (en)

Cited By (74)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108048713A (en) * 2017-12-18 2018-05-18 华中科技大学 A kind of aluminium zinc-magnesium copper system high-strength thin-crystal aluminium alloy and preparation method thereof
CN108149117A (en) * 2017-11-22 2018-06-12 兰州理工大学 A kind of MoCrFeMnNi high-entropy alloys and preparation method thereof
CN108374113A (en) * 2018-04-11 2018-08-07 长沙理工大学 A kind of preparation method of TaTiZrAlSi high-entropy alloys and its powder
CN108372294A (en) * 2018-04-23 2018-08-07 长沙理工大学 A kind of high-entropy alloy powder and preparation method thereof
CN108421985A (en) * 2018-03-12 2018-08-21 北京科技大学 A method of preparing entropy alloy in oxide dispersion intensifying
CN108425060A (en) * 2018-01-31 2018-08-21 中国人民解放军国防科技大学 Stand under load inversion of phases NbZrTiTaAlxHigh-entropy alloy and its preparation method and application
CN108588501A (en) * 2018-05-21 2018-09-28 江苏理工学院 One kind having self-lubricating solid Al alloy composite and preparation method thereof
CN108588627A (en) * 2018-04-10 2018-09-28 北京工业大学 A kind of heat-insulated protection high-entropy alloy coating
CN108642362A (en) * 2018-04-27 2018-10-12 中南大学 A kind of high-entropy alloy and preparation method thereof
CN108642399A (en) * 2018-05-17 2018-10-12 哈尔滨工业大学 One kind having base high-entropy alloy and preparation method thereof
CN108747006A (en) * 2018-06-12 2018-11-06 贵州理工学院 A kind of method for laser welding of CoCrCuFeNi high-entropy alloys
CN108950286A (en) * 2018-09-28 2018-12-07 宝鸡文理学院 A method of preparing ZnAlCrMnNbB high-entropy alloy
CN108950255A (en) * 2018-06-28 2018-12-07 江苏科技大学 Five yuan of FeCoNiMoSi system high-entropy alloys and preparation method thereof
CN109108273A (en) * 2018-10-11 2019-01-01 中国人民解放军国防科技大学 NbZrTiTa infusibility high-entropy alloy powder preparation method and NbZrTiTa infusibility high-entropy alloy powder
CN109161776A (en) * 2018-10-10 2019-01-08 湘潭大学 A kind of porous high-entropy alloy of pre-alloyed CrMoNbTiZr and preparation method thereof
CN109355546A (en) * 2018-11-19 2019-02-19 中原工学院 A kind of production target multi-principal elements alloy and preparation method thereof
CN109518066A (en) * 2019-01-11 2019-03-26 湘潭大学 A kind of pre-alloyed high-entropy alloy porous material and preparation method thereof
CN109518018A (en) * 2018-11-28 2019-03-26 湘潭大学 MnNbTaTiV high entropy alloy material and preparation method thereof that one kind is wear-resisting, anti-corrosion
CN109604611A (en) * 2019-01-09 2019-04-12 苏州科技大学 A kind of powder metallurgy prepares the forming method of wear-and corrosion-resistant high-entropy alloy gear
CN109628819A (en) * 2019-01-18 2019-04-16 湘潭大学 A kind of VTiCuHfZr high-entropy alloy and preparation method thereof
CN109622979A (en) * 2019-01-11 2019-04-16 湘潭大学 A kind of preparation method of pre-alloyed high-entropy alloy porous material
CN109666811A (en) * 2019-01-29 2019-04-23 大连理工大学 A kind of radiation resistance high-entropy alloy and preparation method thereof
CN109702199A (en) * 2019-02-26 2019-05-03 中国科学院兰州化学物理研究所 A kind of high-entropy alloy-base self-lubricating oily bearing material
CN109898005A (en) * 2019-04-28 2019-06-18 合肥工业大学 A kind of WVTaZrHf infusibility high-entropy alloy of high intensity and preparation method thereof
CN109897997A (en) * 2019-04-03 2019-06-18 北京科技大学 One kind two-phase of al-mg-si containing lithium enhancing eutectic lightweight medium entropy alloy and preparation method thereof
CN109913673A (en) * 2019-03-13 2019-06-21 湘潭大学 The high-entropy alloy and preparation method thereof of resistance to aluminum melting corrosion
CN109930054A (en) * 2019-04-03 2019-06-25 北京科技大学 A kind of high entropy composite material and preparation method of friction material lightweight
CN109930052A (en) * 2019-03-28 2019-06-25 昆明理工大学 A kind of safe nuclear reactor involucrum high entropy alloy material and preparation method thereof
CN109957700A (en) * 2019-04-12 2019-07-02 苏州大学 Laser melting deposition manufacturing FeCrCuTiV high-entropy alloy powder and preparation method thereof
CN109972066A (en) * 2019-05-05 2019-07-05 西北工业大学 The method for improving AlCoCrCuFeNi high-entropy alloy power magnetic property using magnetic field
CN109967852A (en) * 2019-04-04 2019-07-05 贵州理工学院 A kind of diffusion welding connection method of CoCrCuFeNi high-entropy alloy
CN110004349A (en) * 2019-02-13 2019-07-12 昆明理工大学 A kind of carbon nanotube enhancing high-entropy alloy composite material and preparation method
CN110079824A (en) * 2019-05-17 2019-08-02 哈尔滨工业大学 The method that high-energy ball milling prepares high-entropy alloy type electro-catalysis oxygen evolution reaction catalysts
CN110129732A (en) * 2019-05-23 2019-08-16 北京理工大学 A kind of high resistivity high-entropy alloy film and preparation method thereof
CN110144476A (en) * 2019-06-04 2019-08-20 中北大学 A kind of preparation method of aluminium cobalt ferrochrome nickel high-entropy alloy
CN110190259A (en) * 2019-06-12 2019-08-30 四川大学 A kind of preparation method and lithium ion battery negative material of the high entropy oxide of nanometer
CN110257684A (en) * 2019-07-22 2019-09-20 合肥工业大学 A kind of preparation process of FeCrCoMnNi high-entropy alloy-base composite material
CN110273078A (en) * 2019-06-28 2019-09-24 江苏大学 A kind of magnetism (FeCoNi1.5CuBmREn)P/ Al composite material and preparation method
CN110310793A (en) * 2019-06-28 2019-10-08 江苏大学 A kind of Hard Magnetic high-entropy alloy and preparation method thereof
CN110343930A (en) * 2019-08-22 2019-10-18 西安工业大学 A kind of Flouride-resistani acid phesphatase high-entropy alloy, cladding tubes and preparation method thereof
CN110358962A (en) * 2019-07-12 2019-10-22 长沙理工大学 A kind of large scale rule billet infusibility high-entropy alloy and preparation method thereof
CN110373595A (en) * 2019-08-06 2019-10-25 西安工业大学 A kind of high entropy high temperature alloy of high-performance and preparation method thereof
CN110423930A (en) * 2019-08-21 2019-11-08 福建工程学院 A kind of high entropy ceramic-metal composite of Ultra-fine Grained and preparation method thereof
CN110479959A (en) * 2019-08-28 2019-11-22 黑龙江科技大学 A kind of method that lost foam casting prepares magnesium-based composite material
CN110578104A (en) * 2018-06-09 2019-12-17 南京理工大学 TiC and graphite whisker reinforced high-entropy alloy-based composite material and preparation method thereof
CN110592411A (en) * 2019-09-30 2019-12-20 广东省智能制造研究所 Alloy member and method for producing same
CN110590372A (en) * 2019-10-14 2019-12-20 石家庄铁道大学 Transition metal carbonitride high-entropy ceramic and preparation method and application thereof
CN110643955A (en) * 2019-11-15 2020-01-03 广东省新材料研究所 High-entropy alloy coating and preparation method thereof
CN110735078A (en) * 2019-10-14 2020-01-31 中南大学 CrFeMnMoSiZr high-entropy alloy porous material and preparation method thereof
CN110776323A (en) * 2019-12-16 2020-02-11 中国科学院兰州化学物理研究所 High-purity superfine high-entropy ceramic powder and preparation method thereof
CN110776311A (en) * 2019-11-06 2020-02-11 常州大学 Method for preparing perovskite type composite oxide high-entropy ceramic by hot-pressing sintering
CN110791693A (en) * 2019-11-20 2020-02-14 安徽工业大学 High-entropy alloy with low Al content, high strength and toughness and acid corrosion resistance and preparation method thereof
CN110819839A (en) * 2018-08-10 2020-02-21 天津大学 High-entropy alloy reinforced magnesium-based composite material and preparation method thereof
CN110983145A (en) * 2019-12-23 2020-04-10 昆明理工大学 High-entropy alloy with excellent creep resistance and preparation method thereof
CN110983144A (en) * 2019-11-28 2020-04-10 中国科学院金属研究所 Nitride reinforced high-entropy alloy and preparation method thereof
CN111004953A (en) * 2019-12-30 2020-04-14 湘潭大学 Molten aluminum corrosion resistant cermet material and preparation method and application thereof
CN111074224A (en) * 2020-01-06 2020-04-28 中国科学院宁波材料技术与工程研究所 Corrosion-resistant high-entropy alloy nitride coating, and preparation method and application thereof
TWI693290B (en) * 2019-11-27 2020-05-11 國立中央大學 Ti-RICH MEDIUM ENTROPY ALLOY
CN111187964A (en) * 2020-02-10 2020-05-22 东北大学 High-strength-plasticity antibacterial high-entropy alloy and preparation method thereof
CN111218606A (en) * 2020-01-16 2020-06-02 肇庆高新区纳德科技有限公司 Tool bit formula of low-temperature high-strength edge grinding wheel and preparation method of tool bit formula
KR20200066925A (en) * 2018-12-03 2020-06-11 포항공과대학교 산학협력단 High entropy alloy and manufacturing method of the same
WO2020118802A1 (en) * 2018-12-10 2020-06-18 北京理工大学 Lightweight high-entropy alloy having high strength and high plasticity and preparation method therefor
CN111349838A (en) * 2018-12-24 2020-06-30 中国科学院理化技术研究所 Preparation method of high-entropy alloy composite material
CN111363964A (en) * 2020-03-10 2020-07-03 中国人民解放军军事科学院国防科技创新研究院 W-Ta-Mo-Nb-Hf-C high-temperature high-entropy alloy and preparation method thereof
CN111636026A (en) * 2020-06-11 2020-09-08 华中科技大学 High-niobium low-density refractory multi-principal-element alloy and vacuum drop casting method thereof
CN111809094A (en) * 2020-06-03 2020-10-23 上海理工大学 High-entropy alloy resistant to high-temperature oxidation, thermal barrier coating and preparation method of thermal barrier coating
CN111804886A (en) * 2020-07-20 2020-10-23 哈尔滨吉星机械工程有限公司 Preparation method of magnesium-based composite material applied to automobile differential support
CN111850543A (en) * 2020-06-22 2020-10-30 昆明理工大学 Laser cladding seven-element high-entropy alloy coating and preparation method thereof
CN111945034A (en) * 2020-07-30 2020-11-17 东北大学 BCC-structure high-entropy alloy containing boron and preparation method thereof
CN111996434A (en) * 2020-08-21 2020-11-27 南方科技大学 Block titanium molybdenum niobium alloy and preparation method thereof
CN112077430A (en) * 2020-09-17 2020-12-15 西北工业大学 Method for diffusion welding and welded product
CN112609118A (en) * 2020-11-30 2021-04-06 大连理工大学 High-temperature-resistant refractory high-entropy alloy and preparation method thereof
CN112725818A (en) * 2020-12-10 2021-04-30 西北工业大学 Porous high-entropy alloy self-supporting electrode and method for electrolyzing water
CN112877559A (en) * 2021-01-11 2021-06-01 长沙微纳坤宸新材料有限公司 Multi-component ultrahigh-entropy light-weight refractory composite material

Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20160326616A1 (en) * 2015-05-04 2016-11-10 Seoul National University R&Db Foundation Entropy-controlled bcc alloy having strong resistance to high-temperature neutron radiation damage

Patent Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20160326616A1 (en) * 2015-05-04 2016-11-10 Seoul National University R&Db Foundation Entropy-controlled bcc alloy having strong resistance to high-temperature neutron radiation damage

Cited By (79)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108149117A (en) * 2017-11-22 2018-06-12 兰州理工大学 A kind of MoCrFeMnNi high-entropy alloys and preparation method thereof
CN108048713A (en) * 2017-12-18 2018-05-18 华中科技大学 A kind of aluminium zinc-magnesium copper system high-strength thin-crystal aluminium alloy and preparation method thereof
CN108425060A (en) * 2018-01-31 2018-08-21 中国人民解放军国防科技大学 Stand under load inversion of phases NbZrTiTaAlxHigh-entropy alloy and its preparation method and application
CN108421985A (en) * 2018-03-12 2018-08-21 北京科技大学 A method of preparing entropy alloy in oxide dispersion intensifying
CN108588627A (en) * 2018-04-10 2018-09-28 北京工业大学 A kind of heat-insulated protection high-entropy alloy coating
CN108374113A (en) * 2018-04-11 2018-08-07 长沙理工大学 A kind of preparation method of TaTiZrAlSi high-entropy alloys and its powder
CN108372294A (en) * 2018-04-23 2018-08-07 长沙理工大学 A kind of high-entropy alloy powder and preparation method thereof
CN108642362A (en) * 2018-04-27 2018-10-12 中南大学 A kind of high-entropy alloy and preparation method thereof
CN108642399A (en) * 2018-05-17 2018-10-12 哈尔滨工业大学 One kind having base high-entropy alloy and preparation method thereof
CN108588501A (en) * 2018-05-21 2018-09-28 江苏理工学院 One kind having self-lubricating solid Al alloy composite and preparation method thereof
CN110578104A (en) * 2018-06-09 2019-12-17 南京理工大学 TiC and graphite whisker reinforced high-entropy alloy-based composite material and preparation method thereof
CN110578104B (en) * 2018-06-09 2021-05-14 南京理工大学 TiC and graphite whisker reinforced high-entropy alloy-based composite material and preparation method thereof
CN108747006A (en) * 2018-06-12 2018-11-06 贵州理工学院 A kind of method for laser welding of CoCrCuFeNi high-entropy alloys
CN108950255A (en) * 2018-06-28 2018-12-07 江苏科技大学 Five yuan of FeCoNiMoSi system high-entropy alloys and preparation method thereof
CN110819839A (en) * 2018-08-10 2020-02-21 天津大学 High-entropy alloy reinforced magnesium-based composite material and preparation method thereof
CN108950286A (en) * 2018-09-28 2018-12-07 宝鸡文理学院 A method of preparing ZnAlCrMnNbB high-entropy alloy
CN109161776A (en) * 2018-10-10 2019-01-08 湘潭大学 A kind of porous high-entropy alloy of pre-alloyed CrMoNbTiZr and preparation method thereof
CN109108273A (en) * 2018-10-11 2019-01-01 中国人民解放军国防科技大学 NbZrTiTa infusibility high-entropy alloy powder preparation method and NbZrTiTa infusibility high-entropy alloy powder
CN109355546A (en) * 2018-11-19 2019-02-19 中原工学院 A kind of production target multi-principal elements alloy and preparation method thereof
CN109518018A (en) * 2018-11-28 2019-03-26 湘潭大学 MnNbTaTiV high entropy alloy material and preparation method thereof that one kind is wear-resisting, anti-corrosion
KR20200066925A (en) * 2018-12-03 2020-06-11 포항공과대학교 산학협력단 High entropy alloy and manufacturing method of the same
KR102198924B1 (en) 2018-12-03 2021-01-05 포항공과대학교 산학협력단 High entropy alloy and manufacturing method of the same
WO2020118802A1 (en) * 2018-12-10 2020-06-18 北京理工大学 Lightweight high-entropy alloy having high strength and high plasticity and preparation method therefor
CN111349838A (en) * 2018-12-24 2020-06-30 中国科学院理化技术研究所 Preparation method of high-entropy alloy composite material
CN109604611A (en) * 2019-01-09 2019-04-12 苏州科技大学 A kind of powder metallurgy prepares the forming method of wear-and corrosion-resistant high-entropy alloy gear
CN109518066A (en) * 2019-01-11 2019-03-26 湘潭大学 A kind of pre-alloyed high-entropy alloy porous material and preparation method thereof
CN109622979A (en) * 2019-01-11 2019-04-16 湘潭大学 A kind of preparation method of pre-alloyed high-entropy alloy porous material
CN109628819A (en) * 2019-01-18 2019-04-16 湘潭大学 A kind of VTiCuHfZr high-entropy alloy and preparation method thereof
CN109666811A (en) * 2019-01-29 2019-04-23 大连理工大学 A kind of radiation resistance high-entropy alloy and preparation method thereof
CN110004349A (en) * 2019-02-13 2019-07-12 昆明理工大学 A kind of carbon nanotube enhancing high-entropy alloy composite material and preparation method
CN109702199A (en) * 2019-02-26 2019-05-03 中国科学院兰州化学物理研究所 A kind of high-entropy alloy-base self-lubricating oily bearing material
CN109913673A (en) * 2019-03-13 2019-06-21 湘潭大学 The high-entropy alloy and preparation method thereof of resistance to aluminum melting corrosion
CN109930052A (en) * 2019-03-28 2019-06-25 昆明理工大学 A kind of safe nuclear reactor involucrum high entropy alloy material and preparation method thereof
CN109897997A (en) * 2019-04-03 2019-06-18 北京科技大学 One kind two-phase of al-mg-si containing lithium enhancing eutectic lightweight medium entropy alloy and preparation method thereof
CN109930054A (en) * 2019-04-03 2019-06-25 北京科技大学 A kind of high entropy composite material and preparation method of friction material lightweight
CN109967852A (en) * 2019-04-04 2019-07-05 贵州理工学院 A kind of diffusion welding connection method of CoCrCuFeNi high-entropy alloy
WO2020206724A1 (en) * 2019-04-12 2020-10-15 苏州大学 High-entropy fecrcutiv alloy powder for laser melting deposition manufacturing and preparation method therefor
CN109957700A (en) * 2019-04-12 2019-07-02 苏州大学 Laser melting deposition manufacturing FeCrCuTiV high-entropy alloy powder and preparation method thereof
CN109898005A (en) * 2019-04-28 2019-06-18 合肥工业大学 A kind of WVTaZrHf infusibility high-entropy alloy of high intensity and preparation method thereof
CN109972066A (en) * 2019-05-05 2019-07-05 西北工业大学 The method for improving AlCoCrCuFeNi high-entropy alloy power magnetic property using magnetic field
CN110079824A (en) * 2019-05-17 2019-08-02 哈尔滨工业大学 The method that high-energy ball milling prepares high-entropy alloy type electro-catalysis oxygen evolution reaction catalysts
CN110129732A (en) * 2019-05-23 2019-08-16 北京理工大学 A kind of high resistivity high-entropy alloy film and preparation method thereof
CN110144476A (en) * 2019-06-04 2019-08-20 中北大学 A kind of preparation method of aluminium cobalt ferrochrome nickel high-entropy alloy
CN110190259A (en) * 2019-06-12 2019-08-30 四川大学 A kind of preparation method and lithium ion battery negative material of the high entropy oxide of nanometer
CN110273078A (en) * 2019-06-28 2019-09-24 江苏大学 A kind of magnetism (FeCoNi1.5CuBmREn)P/ Al composite material and preparation method
CN110310793A (en) * 2019-06-28 2019-10-08 江苏大学 A kind of Hard Magnetic high-entropy alloy and preparation method thereof
CN110358962A (en) * 2019-07-12 2019-10-22 长沙理工大学 A kind of large scale rule billet infusibility high-entropy alloy and preparation method thereof
CN110257684A (en) * 2019-07-22 2019-09-20 合肥工业大学 A kind of preparation process of FeCrCoMnNi high-entropy alloy-base composite material
CN110373595A (en) * 2019-08-06 2019-10-25 西安工业大学 A kind of high entropy high temperature alloy of high-performance and preparation method thereof
CN110423930A (en) * 2019-08-21 2019-11-08 福建工程学院 A kind of high entropy ceramic-metal composite of Ultra-fine Grained and preparation method thereof
CN110343930A (en) * 2019-08-22 2019-10-18 西安工业大学 A kind of Flouride-resistani acid phesphatase high-entropy alloy, cladding tubes and preparation method thereof
CN110479959A (en) * 2019-08-28 2019-11-22 黑龙江科技大学 A kind of method that lost foam casting prepares magnesium-based composite material
CN110592411A (en) * 2019-09-30 2019-12-20 广东省智能制造研究所 Alloy member and method for producing same
CN110735078A (en) * 2019-10-14 2020-01-31 中南大学 CrFeMnMoSiZr high-entropy alloy porous material and preparation method thereof
CN110590372A (en) * 2019-10-14 2019-12-20 石家庄铁道大学 Transition metal carbonitride high-entropy ceramic and preparation method and application thereof
CN110776311A (en) * 2019-11-06 2020-02-11 常州大学 Method for preparing perovskite type composite oxide high-entropy ceramic by hot-pressing sintering
CN110776311B (en) * 2019-11-06 2021-07-30 常州大学 Method for preparing perovskite type composite oxide high-entropy ceramic by hot-pressing sintering
CN110643955A (en) * 2019-11-15 2020-01-03 广东省新材料研究所 High-entropy alloy coating and preparation method thereof
CN110791693A (en) * 2019-11-20 2020-02-14 安徽工业大学 High-entropy alloy with low Al content, high strength and toughness and acid corrosion resistance and preparation method thereof
TWI693290B (en) * 2019-11-27 2020-05-11 國立中央大學 Ti-RICH MEDIUM ENTROPY ALLOY
CN110983144A (en) * 2019-11-28 2020-04-10 中国科学院金属研究所 Nitride reinforced high-entropy alloy and preparation method thereof
CN110776323A (en) * 2019-12-16 2020-02-11 中国科学院兰州化学物理研究所 High-purity superfine high-entropy ceramic powder and preparation method thereof
CN110983145A (en) * 2019-12-23 2020-04-10 昆明理工大学 High-entropy alloy with excellent creep resistance and preparation method thereof
CN111004953B (en) * 2019-12-30 2021-04-27 湘潭大学 Molten aluminum corrosion resistant cermet material and preparation method and application thereof
CN111004953A (en) * 2019-12-30 2020-04-14 湘潭大学 Molten aluminum corrosion resistant cermet material and preparation method and application thereof
CN111074224A (en) * 2020-01-06 2020-04-28 中国科学院宁波材料技术与工程研究所 Corrosion-resistant high-entropy alloy nitride coating, and preparation method and application thereof
CN111218606A (en) * 2020-01-16 2020-06-02 肇庆高新区纳德科技有限公司 Tool bit formula of low-temperature high-strength edge grinding wheel and preparation method of tool bit formula
CN111187964A (en) * 2020-02-10 2020-05-22 东北大学 High-strength-plasticity antibacterial high-entropy alloy and preparation method thereof
CN111363964A (en) * 2020-03-10 2020-07-03 中国人民解放军军事科学院国防科技创新研究院 W-Ta-Mo-Nb-Hf-C high-temperature high-entropy alloy and preparation method thereof
CN111809094A (en) * 2020-06-03 2020-10-23 上海理工大学 High-entropy alloy resistant to high-temperature oxidation, thermal barrier coating and preparation method of thermal barrier coating
CN111636026A (en) * 2020-06-11 2020-09-08 华中科技大学 High-niobium low-density refractory multi-principal-element alloy and vacuum drop casting method thereof
CN111850543A (en) * 2020-06-22 2020-10-30 昆明理工大学 Laser cladding seven-element high-entropy alloy coating and preparation method thereof
CN111804886A (en) * 2020-07-20 2020-10-23 哈尔滨吉星机械工程有限公司 Preparation method of magnesium-based composite material applied to automobile differential support
CN111945034A (en) * 2020-07-30 2020-11-17 东北大学 BCC-structure high-entropy alloy containing boron and preparation method thereof
CN111996434A (en) * 2020-08-21 2020-11-27 南方科技大学 Block titanium molybdenum niobium alloy and preparation method thereof
CN112077430A (en) * 2020-09-17 2020-12-15 西北工业大学 Method for diffusion welding and welded product
CN112609118A (en) * 2020-11-30 2021-04-06 大连理工大学 High-temperature-resistant refractory high-entropy alloy and preparation method thereof
CN112725818A (en) * 2020-12-10 2021-04-30 西北工业大学 Porous high-entropy alloy self-supporting electrode and method for electrolyzing water
CN112877559A (en) * 2021-01-11 2021-06-01 长沙微纳坤宸新材料有限公司 Multi-component ultrahigh-entropy light-weight refractory composite material

Similar Documents

Publication Publication Date Title
US20170314097A1 (en) High-strength and ultra heat-resistant high entropy alloy (hea) matrix composites and method of preparing the same
KR101927611B1 (en) High- strength and heat-resisting high entropy alloy matrix composites and method of manufacturing the same
KR101966584B1 (en) In-situ strengthened high entropy powder, alloy thereof and method of manufacturing the same
EP2860273B1 (en) Heat-resistant molybdenum alloy
EP1953254B1 (en) X-ray tube rotating anode target and x-ray tube
KR20170123968A (en) In-situ strengthened high entropy powder, alloy thereof and method of manufacturing the same
US20040079191A1 (en) Hard alloy and W-based composite carbide powder used as starting material
JP5905903B2 (en) Heat-resistant alloy and manufacturing method thereof
US20090148334A1 (en) Nanophase dispersion strengthened low cte alloy
Li et al. Microstructure and properties of Ti (C, N)–TiB2–FeCoCrNiAl high-entropy alloys composite cermets
JP5872590B2 (en) Heat-resistant alloy and manufacturing method thereof
JP6011946B2 (en) Nickel-based intermetallic compound composite sintered material and method for producing the same
JP5851826B2 (en) WC-based cemented carbide for cutting tools having excellent plastic deformation resistance at high temperatures, coated cutting tools, and methods for producing the same
US20120063943A1 (en) Metal composite powder, sintered body, and preparation method thereof
Falodun et al. Characterization of spark plasma sintered TiN nanoparticle strengthened titanium alloy using EBSD and TKD
JP2004263251A (en) Group 7a element-containing cemented carbide
KR102150756B1 (en) High-strength and heat-resistant precipitates/dispersion strengthened high entropy super-alloys and method of manufacturing the same
EP3705216A1 (en) Cemented carbide composite material, method for producing same, and cemented carbide tool
KR101450661B1 (en) The method of preparation for ternary titanium carbonitride sintered bodies having enhanced mechanical properties and ternary titanium carbonitride sintered bodies prepared thereby
JP6202787B2 (en) Molybdenum heat-resistant alloy, friction stir welding tool, and manufacturing method
JP5799969B2 (en) Ceramic crystal particles, ceramic sintered body, and method for producing them
JP2005068479A (en) Boron-containing cemented carbide
EP3792370A1 (en) Heat-resistant tungsten alloy, friction stir welding tool, and production method
JP2004238660A (en) Chromium-containing cemented carbide
EP2796580B1 (en) Alloy composition

Legal Events

Date Code Title Description
AS Assignment

Owner name: KOREA ADVANCED INSTITUTE OF SCIENCE AND TECHNOLOGY

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNORS:HONG, SOON HYUNG;RYU, HO JIN;LEE, BIN;AND OTHERS;REEL/FRAME:042134/0218

Effective date: 20170418

STPP Information on status: patent application and granting procedure in general

Free format text: DOCKETED NEW CASE - READY FOR EXAMINATION

STPP Information on status: patent application and granting procedure in general

Free format text: NON FINAL ACTION MAILED

STPP Information on status: patent application and granting procedure in general

Free format text: RESPONSE TO NON-FINAL OFFICE ACTION ENTERED AND FORWARDED TO EXAMINER

STPP Information on status: patent application and granting procedure in general

Free format text: RESPONSE TO NON-FINAL OFFICE ACTION ENTERED AND FORWARDED TO EXAMINER

STCB Information on status: application discontinuation

Free format text: FINAL REJECTION MAILED

STPP Information on status: patent application and granting procedure in general

Free format text: NON FINAL ACTION MAILED

STCB Information on status: application discontinuation

Free format text: FINAL REJECTION MAILED