CN113373366A - Multi-element refractory high-entropy alloy and preparation method thereof - Google Patents

Multi-element refractory high-entropy alloy and preparation method thereof Download PDF

Info

Publication number
CN113373366A
CN113373366A CN202110674552.0A CN202110674552A CN113373366A CN 113373366 A CN113373366 A CN 113373366A CN 202110674552 A CN202110674552 A CN 202110674552A CN 113373366 A CN113373366 A CN 113373366A
Authority
CN
China
Prior art keywords
entropy alloy
alloy
entropy
refractory high
ingot
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.)
Granted
Application number
CN202110674552.0A
Other languages
Chinese (zh)
Other versions
CN113373366B (en
Inventor
何峰
王锦程
崔丁聪
王志军
李俊杰
张凯威
杨中晟
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.)
Northwestern Polytechnical University
Original Assignee
Northwestern Polytechnical University
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
Application filed by Northwestern Polytechnical University filed Critical Northwestern Polytechnical University
Priority to CN202110674552.0A priority Critical patent/CN113373366B/en
Publication of CN113373366A publication Critical patent/CN113373366A/en
Application granted granted Critical
Publication of CN113373366B publication Critical patent/CN113373366B/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D18/00—Pressure casting; Vacuum casting
    • B22D18/06—Vacuum casting, i.e. making use of vacuum to fill the mould
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacture And Refinement Of Metals (AREA)

Abstract

The invention discloses a multi-element refractory high-entropy alloy and a preparation method thereof, and relates to the technical field of novel metal materials. The high-entropy alloy consists of main elements Ti, V, Nb and Hf and a trace element M, and the high-entropy alloy comprises the components of TiaVbNbcHfdMeWherein a, b, c, d and e represent the mole percentage of each element, a is 30-50 at%, b is 10-30 at%, c is 10-30 at%, d is 10-30 at%, and e is 1-9 at%. The high-entropy alloy provided by the invention has a simple body-centered cubic structure, has good room-temperature tensile plasticity and strength, makes up for the defects of the prior art, meets the requirements of high-performance metal structure materials, and provides new component selection for the BCC high-entropy alloy, so that the BCC high-entropy alloy has great application potential.

Description

Multi-element refractory high-entropy alloy and preparation method thereof
Technical Field
The invention relates to the technical field of novel metal materials, in particular to a multi-element refractory high-entropy alloy and a preparation method thereof.
Background
In recent years, the high-entropy alloy breaks through the traditional alloy design concept of single principal element component design, and is a novel multi-principal element metal material mainly designed by configuration entropy, and the excellent physical and chemical properties of the novel multi-principal element metal material attract wide attention. Unlike conventional alloys, high entropy alloys are the result of the co-action of a plurality of principal elements, rather than being unique in that they exhibit the characteristics of a single element, and tend to form a solid solution phase, such as the simple Body Centered Cubic (BCC) or Face Centered Cubic (FCC) phases. The refractory high-mid-entropy alloy (the melting point is more than 2123K) mainly comprises metal elements of IVB (Ti, Zr, Hf), VB (V, Nb, Ta) and VIB (Cr, Mo and W), and is mainly based on metal elements of a body-centered cubic (BCC) structure, so that the refractory high-mid-entropy alloy is mostly a single-phase BCC solid solution phase or a BCC solid solution phase. High entropy alloys are generally defined as alloys containing more than 5 constituent elements, or a mixture entropy of ≥ 1.6R. The refractory high-entropy alloy has the advantages of high melting point, high hardness, corrosion resistance, excellent high-temperature strength and the like, the application temperature of the refractory high-entropy alloy is up to 1373-1593K, the refractory high-entropy alloy is much higher than that of the conventional high-temperature alloy such as Inconel 718 alloy and the like, and the refractory high-entropy alloy has lower elastic modulus and specific modulus compared with nickel-based high-temperature alloy and stainless steel and has potential application prospects in the fields of aerospace (turbines and engine blades), nuclear industry, biomedicine and the like.
The sliding system of the BCC refractory high-entropy alloy at room temperature is far less than that of the high-entropy alloy with an FCC structure, and the alloy generally shows obvious brittleness at room temperature or higher temperature. The existing research shows that the room temperature strength of TaNbWMoV high-entropy alloy and TaNbWMo high-entropy alloy can reach more than 1 GPa. But the compression plasticity of the alloy does not exceed 10% at room temperature, and the tensile plasticity is lower, so that the application of the BCC refractory high-entropy alloy is greatly hindered.
Disclosure of Invention
In order to solve the defects in the prior art, the invention provides a multi-element refractory high-entropy alloy and a preparation method thereof, wherein the alloy has a simple body-centered cubic structure, has good room-temperature tensile plasticity and strength, makes up the defects in the prior art, meets the requirements of high-performance metal structure materials, and provides new component selection for the BCC high-entropy alloy, so that the alloy has great application potential.
The first purpose of the invention is to provide a multi-element refractory high-entropy alloy, which consists of main elements Ti, V, Nb, Hf and a trace element M, wherein the high-entropy alloy comprises the components of TiaVbNbcHfdMeWherein a, b, c, d and e respectively represent the mol percentage of the corresponding elements, a is 30-50 at%, b is 10-30 at%, c is 10-30 at%, d is 10-30 at%, and e is 1-9 at%;
wherein the trace element M comprises one or more of Cr, Zr, Mo, Ta and Al, and the molar percentage of each component of the trace element is as follows: cr is less than or equal to 3at percent, Al is less than or equal to 6at percent, Zr is less than or equal to 6at percent, Mo is less than or equal to 6at percent, and Ta is less than or equal to 6at percent.
Preferably, the high-entropy alloy is Ti41V27Nb14.5Hf14.5M3、Ti41V27Nb14Hf14M4、Ti41V27Nb13Hf13M6Or Ti41V27Nb11.5Hf11.5M9。
Preferably, the high-entropy alloy has a body-centered cubic structure.
The second purpose of the invention is to provide a preparation method of the multi-element refractory high-entropy alloy, which comprises the following steps:
smelting: placing the raw materials in a vacuum arc melting furnace, controlling the current to be 180-280A under the inert atmosphere condition, carrying out multiple melting for 3-6 min each time, then carrying out batch operation for 3-6 min, turning over, carrying out next melting, and casting the alloy melt into a mold after the melting is finished to obtain an as-cast alloy ingot;
suction casting: and placing the as-cast alloy ingot on a casting mold, smelting the alloy ingot, performing suction casting when the alloy ingot is completely liquid and has good fluidity, cooling, and removing the mold to obtain a rectangular suction casting alloy ingot, namely the multi-element refractory high-entropy alloy.
Preferably, at least 5 smelts are carried out.
More preferably, in the first smelting process, the current is controlled to be 180-210A; in the second smelting and the subsequent multiple smelting processes, the current is controlled to be 260-280A.
Preferably, the raw materials are cleaned by vibration with ethanol, dried and then placed in a vacuum arc melting furnace, and the metal with the lowest melting point is placed on the bottom layer and the metal with the highest melting point is placed on the surface layer.
Preferably, after the raw materials are placed in a vacuum arc melting furnace, the oxygen is discharged from the furnace chamber by repeatedly vacuumizing and filling inert gas for a plurality of times, and then the melting operation is carried out; wherein the vacuum is pumped to 2 × 10-3Pa, and introducing argon into the furnace chamber to-0.05 MPa.
Preferably, in the process of suction casting, the current is controlled to be 150-400A after the alloy ingot in the cast state is ignited for low-temperature preheating, and the current is increased to 350-400A after the whole ingot is heated, so that the ingot is melted.
The third purpose of the invention is to provide the application of the multi-element refractory high-entropy alloy in the aerospace field.
Compared with the prior art, the invention has the following beneficial effects:
the multi-element refractory high-entropy alloy provided by the invention has a simple body-centered cubic structure, has good room-temperature tensile plasticity and strength, makes up for the defects of the prior art, meets the requirements of high-performance metal structure materials, and provides new component selection for the BCC high-entropy alloy, so that the alloy has great application potential.
The multi-element refractory high-entropy alloy provided by the invention basically achieves the room-temperature plasticity of 25% or above, wherein Ti41V27Nb13Hf13Ta6The room temperature plasticity is about 33.4 percent, the tensile strength can reach 1032MPa, and the yield strength can reach 926 MPa. Ti41V27Nb13Hf13Mo6At room temperatureThe plasticity is about 26.3 percent, the tensile strength can reach 1219MPa, and the yield strength can reach 1112 MPa. Ti41V27Nb11.5Hf11.5Cr3Al6The room temperature plasticity is about 19.5 percent, the tensile strength can reach 1216MPa, and the yield strength can reach 1178 MPa.
The multi-element refractory high-entropy alloy provided by the invention has potential application prospects in the fields of aerospace (turbines and engine blades), nuclear industry, biomedicine and the like.
Drawings
FIG. 1 is a flow chart of a preparation process of the multi-element refractory high-entropy alloy provided by the invention.
FIG. 2 is a XRD (X-ray diffraction) spectrum of the high-entropy alloy provided by examples 1-6 and comparative examples 1 and 2;
FIG. 3 is a tensile stress-strain curve of the high entropy alloys provided in examples 4-6 and comparative examples 1 and 2.
Fig. 4 is a tensile stress-strain graph of the high entropy alloy provided in example 1 and comparative examples 1 and 2.
Fig. 5 is a BSE (back-scattered electron) photograph of the high-entropy alloy provided in example 1 and comparative example 2 and an EDS (edge scattering electron) surface distribution diagram of the high-entropy alloy provided in example 1.
Fig. 6 is a tensile stress-strain graph of the high entropy alloys provided in examples 2 and 5 and comparative example 1.
Fig. 7 is a tensile stress-strain graph of the high entropy alloys provided in examples 3 and 6 and comparative example 1.
Fig. 8 is a BSE (back-scattered electron) photograph of the high-entropy alloys provided in example 1, example 7, and example 8.
Fig. 9 is a tensile stress-strain graph of the high entropy alloys provided in examples 1, 7 and 8.
Detailed Description
The present invention is described in detail below with reference to the attached drawings and specific embodiments so that those skilled in the art can better understand the present invention and can implement the present invention, but the present invention is not limited by the examples.
The invention provides a multicomponent refractoryThe high-entropy alloy consists of main elements of Ti, V, Nb, Hf and a trace element of M, and the high-entropy alloy comprises the components of TiaVbNbcHfdMeWherein a, b, c, d and e respectively represent the mol percentage of the corresponding elements, a is 30-50 at%, b is 10-30 at%, c is 10-30 at%, d is 10-30 at%, and e is 1-9 at%;
wherein the trace element M comprises one or more of Cr, Zr, Mo, Ta and Al, and the molar percentage of each component of the trace element is as follows: cr is less than or equal to 3at percent, Al is less than or equal to 6at percent, Zr is less than or equal to 6at percent, Mo is less than or equal to 6at percent, and Ta is less than or equal to 6at percent.
The raw materials used in the following examples are all metal raw materials with a purity of not less than 99.95%.
Example 1
A multi-element refractory high-entropy alloy with Ti as chemical formula41V27Nb14.5Hf14.5Cr3Abbreviated as Cr3(ii) a Wherein, the proportion of each element is mole percentage.
Ti41V27Nb14.5Hf14.5Cr3The preparation method of the multi-element refractory high-entropy alloy is shown in figure 1 and comprises the following steps:
s1, preparing materials: vibrating and cleaning a high-purity (more than or equal to 99.95%) metal raw material by using alcohol, and drying for later use; the dosage of the raw materials is Ti according to the mole percentage of each element41V27Nb14.5Hf14.5Cr3Weighing, sequentially putting the weighed materials into a water-cooled metal crucible, putting the metal with the lowest melting point on the bottom layer, and putting the metal with the highest melting point on the surface layer;
s2, vacuumizing: the method comprises the following steps of (1) filling raw materials into a non-consumable vacuum arc melting furnace, closing a furnace door, and carrying out vacuumizing treatment on a sample chamber: first, the mechanical pump is turned on, and when the vacuum degree is less than 5X 100Opening the molecular pump after Pa until the maximum frequency of the molecular pump reaches 450HZ and the vacuum degree is less than or equal to 2 multiplied by 10-3Pa, closing the molecular pump, introducing high-purity argon to the sample chamber to achieve-0.05 MPa, and repeating the processes of vacuumizing and filling argon for 2 times to fully remove oxygen in the furnace body;
s3, smelting: smelting a pure titanium ingot for 5min to absorb residual oxygen, then repeatedly smelting the raw materials for 5 times, wherein each smelting time is 5min, and then carrying out next smelting after 5min of intermission;
the first smelting uses low current 200A to carry out low-temperature smelting so as to reduce the volatilization loss of volatile elements; stopping arc striking after the mixture is fully mixed, turning the cast ingot by 180 degrees by using a deflector rod after the cast ingot is cooled, and then turning the cast ingot by the turning operation after each time of smelting is finished so as to ensure the smelting uniformity;
the current is controlled to be 270A for high-temperature smelting from the second smelting to the fifth smelting, and the electromagnetic stirring function is used, the current is 1.5A, the fluidity of the alloy is enhanced, and the components are uniform;
s4, suction casting: placing a circular cast ingot smelted in a copper crucible on a casting mold, conducting low-temperature preheating by using a small current 180A after arc striking, waiting for the cast ingot to become red, increasing the current to 380A instantly after the whole is uniformly heated so as to melt the cast ingot, and simultaneously clicking a suction casting button to suction cast liquid alloy into a rectangular mold with the size of 60 multiplied by 10 multiplied by 8mm so as to prevent casting defects caused by over-rapid solidification; cooling and removing the mould to obtain a rectangular suction casting alloy ingot, namely the multielement Ti41V27Nb14.5Hf14.5Cr3Refractory high entropy alloy.
Example 2
A multi-element refractory high-entropy alloy with Ti as chemical formula41V27Nb14Hf14Mo4Abbreviated as Mo4(ii) a Wherein, the proportion of each element is mole percentage.
The preparation method of the high-entropy alloy is the same as that of the embodiment 1, except that the raw materials are used in such a manner that the molar percentage of each element is Ti41V27Nb14Hf14Mo4And weighing.
Example 3
A multi-element refractory high-entropy alloy with Ti as chemical formula41V27Nb14Hf14Ta4Abbreviated as Ta4(ii) a Wherein, the proportion of each element is mole percentage.
The preparation method of the high-entropy alloy is the same as that of the embodiment 1, except that the raw materials are used in such a manner that the molar percentage of each element is Ti41V27Nb14Hf14Ta4And weighing.
Example 4
A multi-element refractory high-entropy alloy with Ti as chemical formula41V27Nb13Hf13Zr6Abbreviated as Zr6(ii) a Wherein, the proportion of each element is mole percentage.
The preparation method of the high-entropy alloy is the same as that of the embodiment 1, except that the raw materials are used in such a manner that the molar percentage of each element is Ti41V27Nb13Hf13Zr6And weighing.
Example 5
A multi-element refractory high-entropy alloy with Ti as chemical formula41V27Nb13Hf13Mo6Abbreviated as Mo6(ii) a Wherein, the proportion of each element is mole percentage.
The preparation method of the high-entropy alloy is the same as that of the embodiment 1, except that the raw materials are used in such a manner that the molar percentage of each element is Ti41V27Nb13Hf13Mo6And weighing.
Example 6
A multi-element refractory high-entropy alloy with Ti as chemical formula41V27Nb13Hf13Ta6Abbreviated as Ta6(ii) a Wherein, the proportion of each element is mole percentage.
The preparation method of the high-entropy alloy is the same as that of the embodiment 1, except that the raw materials are used in such a manner that the molar percentage of each element is Ti41V27Nb13Hf13Ta6And weighing.
Example 7
A multi-element refractory high-entropy alloy with Ti as chemical formula41V27Nb13Hf13Cr3Al3Abbreviated as Cr3Al3(ii) a Wherein, the proportion of each element is mole percentage.
The preparation method of the high-entropy alloy is the same as that of the embodiment 1, except that the raw materials are used in such a manner that the molar percentage of each element is Ti41V27Nb13Hf13Cr3Al3And weighing.
Example 8
A multi-element refractory high-entropy alloy with Ti as chemical formula41V27Nb11.5Hf11.5Cr3Al6Abbreviated as Cr3Al6(ii) a Wherein, the proportion of each element is mole percentage.
The preparation method of the high-entropy alloy is the same as that of the embodiment 1, except that the raw materials are used in such a manner that the molar percentage of each element is Ti41V27Nb11.5Hf11.5Cr3Al6And weighing.
Comparative example 1
A high-entropy alloy, the chemical formula of which is Ti41V27Nb16Hf16Abbreviated as Nb16Hf16(ii) a Wherein, the proportion of each element is mole percentage.
The preparation method of the high-entropy alloy is the same as that of the embodiment 1, except that the raw materials are used in such a manner that the molar percentage of each element is Ti41V27Nb16Hf16And weighing.
Comparative example 2
A multi-element refractory high-entropy alloy with Ti as chemical formula41V27Nb13Hf13Cr6Abbreviated as Cr6(ii) a Wherein, the proportion of each element is mole percentage.
Preparation method of high-entropy alloy and high-entropy alloyExample 1 the same procedure was followed except that the starting materials were used in such amounts that the molar percentages of the elements were Ti41V27Nb13Hf13Cr6And weighing.
In order to illustrate various properties of the multi-element refractory high-entropy alloy provided by the invention, the multi-element refractory high-entropy alloy provided by the embodiments 1 to 8 and the high-entropy alloy provided by the comparative examples 1 to 2 are subjected to related property analysis. See FIGS. 2-9.
The XRD phase identification test is carried out, the working voltage and current of an X-ray diffractometer are 40KV and 40mA respectively, an X-ray source is a Cu Ka (lambda is 0.1542nm) ray, the scanning speed is 5 DEG/min, the scanning step length is 0.02 DEG/step, and the scanning range is 20-100 DEG; performing tissue characterization through BSE (back scattered electron), polishing the upper and lower surfaces of a sample before measurement to be flat and parallel, and performing electrolytic polishing treatment on a measurement surface; the tensile mechanical property of a 48 x 10mm plate-shaped sample is tested in an electronic universal material testing machine, the alloy components with the optimal performance are obtained through analysis and comparison, and the alloying effect of solid solution elements in the TiVNbHfM alloy is determined.
FIG. 2 is an XRD spectrum of the high-entropy alloy provided in examples 1-6 and comparative examples 1-2, and it can be seen from FIG. 2 that most of the high-entropy alloys of TiVNbHfM are single-phase BCC structures, and the asymmetric peak may be caused by grain boundary and intragranular component segregation, or BCC2Precipitated phases of the structure; with solid solution of refractory elements, diffraction peaks shift in different directions as a whole, and the value of the lattice constant a changes.
FIG. 3 is a tensile stress-strain curve of the high-entropy alloys provided in examples 4 to 6 and comparative examples 1 to 2, and it can be seen from FIG. 3 that Zr6/Ta6/Mo6The room temperature plasticity of the alloy basically reaches 25 percent and above, but Cr6Brittle fracture occurred.
FIG. 4 is Ti41V27Nb14.5Hf14.5Cr3With Ti41V27Nb13Hf13Cr6Tensile stress-strain diagram of alloy, Cr3Has good plasticity and strength compared with Ti41V27Nb16Hf16Is improved.
In order to explore Cr6The cause of brittle fracture, a tissue characterization, is performed, as shown in figure 5,
FIG. 5 is a BSE (Back-scattered electron) photograph and an EDS (EDS surface distribution) map of the high-entropy alloy provided in example 1 and comparative example 2, and it can be seen from FIG. 5 that Cr is shown6With a granular precipitate phase in the crystal, and Cr3No precipitated phase, smooth grain boundary, no foreign matter, and solid solution phase. Cr (chromium) component3The EDS surface distribution diagram also reflects the even distribution of the five elements of Ti, V, Hf, Nb and Cr, which indicates that the solid solution degree is higher. In order to prevent the solid solution element from adversely affecting the plasticity of the TiVNbHfM alloy, the content thereof needs to be precisely controlled, and therefore the Cr content needs to be controlled to be within 3%.
Fig. 6 is a tensile stress-strain graph of the high entropy alloys provided in examples 2 and 5 and comparative example 1. Fig. 7 is a tensile stress-strain graph of the high entropy alloys provided in examples 3 and 6 and comparative example 1. Fig. 8 is a BSE (back-scattered electron) photograph of the high-entropy alloys provided in example 1, example 7, and example 8. Fig. 9 is a tensile stress-strain graph of the high entropy alloys provided in examples 1, 7 and 8.
As can be seen from FIGS. 6 to 9, room temperature plasticity of TiVNbHfM alloy was substantially 20% or more, where Ti was contained41V27Nb13Hf13Ta6The room temperature plasticity is about 33.4 percent, the tensile strength can reach 1032MPa, and the yield strength can reach 926 MPa. Ti41V27Nb11.5Hf11.5Mo6The room temperature plasticity is about 26.3 percent, the tensile strength can reach 1219MPa, and the yield strength can reach 1112 MPa. Ti41V27Nb11.5Hf11.5Cr3Al6The room temperature plasticity is about 19.5 percent, the tensile strength can reach 1216MPa, and the yield strength can reach 1178 MPa. According to the capability of improving plasticity, the solid solution elements can be sequenced to Ta > Zr > Cr > Mo > Al, excellent plasticity is required, and solid solution Ta can be selected; according to the capability of improving the strength, the solid solution elements can be sequenced to be Ta < Zr/Cr < Mo < Al), high specific strength is required, and Al can be solid-dissolved.
FIG. 8 shows Cr3Al6The segregation in the crystal is more obvious, and a trace amount of granular precipitated phase exists in the crystal boundary, so that the tensile plasticity is reduced. And Cr3And Cr3Al3No precipitated phase, smooth grain boundary, no foreign matter, solid solution phase and high solid solution degree. Albeit Cr3Al6The alloy has certain plasticity, but in order to prevent the solid solution elements from adversely affecting the plasticity of the TiVNbHfM alloy, the Al content needs to be controlled within 6 percent. The TiVNbHfM alloy can be subjected to solid solution strengthening and toughening by combining different refractory elements, and the TiVNbHfM high-entropy alloy with uniform strong plasticity is obtained through alloy design and experimental verification.
In conclusion, the multi-element refractory high-entropy alloy provided by the invention has a simple body-centered cubic structure, has good room-temperature tensile plasticity and strength, makes up for the defects of the prior art, meets the requirements of high-performance metal structure materials, and provides new component selection for the BCC high-entropy alloy, so that the alloy has great application potential.
The high-entropy alloy has high melting point of the constituent elements, alloy melting is carried out by a non-consumable vacuum arc melting process, and a multi-element TiVNbHfM high-entropy alloy material with uniform components and excellent mechanical properties is prepared by regulating and controlling the melting times and the melting current.
The multi-element refractory high-entropy alloy provided by the invention has potential application prospects in the fields of aerospace (turbines and engine blades), nuclear industry, biomedicine and the like.
The foregoing is only a preferred embodiment of the present invention, and it should be noted that those skilled in the art can make various improvements and modifications without departing from the principle of the present invention, and these improvements and modifications should also be construed as the protection scope of the present invention.

Claims (10)

1. The multi-element refractory high-entropy alloy is characterized in that the high-entropy alloy consists of main elements Ti, V, Nb and Hf and a trace element M, and the high-entropy alloy comprises TiaVbNbcHfdMeWherein a, b, c, d and e respectively represent the mol percentage of the corresponding elements, a is 30-50 at%, b is 10-30 at%, c is 10-30 at%, d is 10-30 at%, and e is 1-9 at%;
wherein the trace element M comprises one or more of Cr, Zr, Mo, Ta and Al, and the molar percentage of each component of the trace element is as follows: cr is less than or equal to 3at percent, Al is less than or equal to 6at percent, Zr is less than or equal to 6at percent, Mo is less than or equal to 6at percent, and Ta is less than or equal to 6at percent.
2. The multi-element refractory high-entropy alloy of claim 1, wherein the high-entropy alloy is Ti41V27Nb14.5Hf14.5M3、Ti41V27Nb14Hf14M4、Ti41V27Nb13Hf13M6Or Ti41V27Nb11.5Hf11.5M9。
3. The multi-element refractory high-entropy alloy of claim 1, wherein the high-entropy alloy is of a body-centered cubic structure.
4. A preparation method of the multi-element refractory high-entropy alloy as claimed in any one of claims 1 to 3, characterized by comprising the following steps:
smelting: placing the raw materials in a vacuum arc melting furnace, controlling the current to be 180-280A under the inert atmosphere condition, carrying out multiple melting for 3-6 min each time, then carrying out batch operation for 3-6 min, turning over, carrying out next melting, and casting the alloy melt into a mold after the melting is finished to obtain an as-cast alloy ingot;
suction casting: and placing the as-cast alloy ingot on a casting mold, smelting the alloy ingot, performing suction casting when the alloy ingot is completely liquid and has good fluidity, cooling, and removing the mold to obtain a rectangular suction casting alloy ingot, namely the multi-element refractory high-entropy alloy.
5. Method for the production of a multi-element refractory high-entropy alloy according to claim 4, wherein at least 5 heats are carried out.
6. The preparation method of the multi-element refractory high-entropy alloy as claimed in claim 5, wherein in the first smelting process, the current is controlled to be 180-210A; in the second smelting and the subsequent multiple smelting processes, the current is controlled to be 260-280A.
7. The method for preparing the multi-element refractory high-entropy alloy according to claim 4, wherein the raw materials are cleaned by vibration with ethanol, dried and then placed in a vacuum arc melting furnace, and the metal with the lowest melting point is placed on the bottom layer and the metal with the highest melting point is placed on the surface layer.
8. The method for preparing the multi-element refractory high-entropy alloy according to claim 4, wherein after the raw materials are placed in a vacuum arc melting furnace, oxygen is exhausted from the furnace chamber by repeatedly vacuumizing and filling inert gas for a plurality of times, and then melting operation is carried out; wherein the vacuum is pumped to 2 × 10-3Pa, and introducing argon into the furnace chamber to-0.05 MPa.
9. The method for preparing the multi-element refractory high-entropy alloy as claimed in claim 4, wherein in the process of suction casting, the current is controlled to be 150-200A for low-temperature preheating after the alloy ingot in the cast state is ignited, and the current is increased to be 350-400A after the whole ingot is heated, so that the ingot is melted.
10. Use of the multi-element refractory high-entropy alloy of any one of claims 1 to 3 in the aerospace field.
CN202110674552.0A 2021-06-17 2021-06-17 Multi-element refractory high-entropy alloy and preparation method thereof Active CN113373366B (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
CN202110674552.0A CN113373366B (en) 2021-06-17 2021-06-17 Multi-element refractory high-entropy alloy and preparation method thereof

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN202110674552.0A CN113373366B (en) 2021-06-17 2021-06-17 Multi-element refractory high-entropy alloy and preparation method thereof

Publications (2)

Publication Number Publication Date
CN113373366A true CN113373366A (en) 2021-09-10
CN113373366B CN113373366B (en) 2022-08-30

Family

ID=77577560

Family Applications (1)

Application Number Title Priority Date Filing Date
CN202110674552.0A Active CN113373366B (en) 2021-06-17 2021-06-17 Multi-element refractory high-entropy alloy and preparation method thereof

Country Status (1)

Country Link
CN (1) CN113373366B (en)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN114752792A (en) * 2022-04-18 2022-07-15 北京工业大学 High-entropy alloy with excellent mechanical property and oxidation resistance at high temperature and preparation method thereof
CN115386774A (en) * 2021-09-30 2022-11-25 北京理工大学 Refractory high-entropy alloy with high strength and high uniform elongation and preparation method thereof
CN115404385A (en) * 2022-05-20 2022-11-29 太原理工大学 Refractory high-entropy alloy with excellent room-temperature tensile ductility and preparation method thereof

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN105886805A (en) * 2016-05-18 2016-08-24 北京理工大学 High-plasticity five-element refractory high-entropy alloy and preparation method thereof
CN107619982A (en) * 2017-11-03 2018-01-23 北京理工大学 Hexa-atomic the infusibility high-entropy alloy and its verification method of a kind of high-ductility high intensity
US20180119255A1 (en) * 2016-11-01 2018-05-03 Ohio State Innovation Foundation HIGH-ENTROPY AlCrTiV ALLOYS
CN108220742A (en) * 2018-03-14 2018-06-29 北京理工大学 A kind of microalloying Ti-Zr-Hf-V-Nb-Ta infusibility high-entropy alloys and preparation method thereof
CN109402482A (en) * 2018-12-10 2019-03-01 北京理工大学 It is a kind of to have both high-intensitive and high-ductility lightweight high-entropy alloy and preparation method thereof
CN110541103A (en) * 2019-08-27 2019-12-06 北京工业大学 High-strength high-plasticity quaternary refractory high-entropy alloy and preparation method thereof

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN105886805A (en) * 2016-05-18 2016-08-24 北京理工大学 High-plasticity five-element refractory high-entropy alloy and preparation method thereof
US20180119255A1 (en) * 2016-11-01 2018-05-03 Ohio State Innovation Foundation HIGH-ENTROPY AlCrTiV ALLOYS
CN107619982A (en) * 2017-11-03 2018-01-23 北京理工大学 Hexa-atomic the infusibility high-entropy alloy and its verification method of a kind of high-ductility high intensity
CN108220742A (en) * 2018-03-14 2018-06-29 北京理工大学 A kind of microalloying Ti-Zr-Hf-V-Nb-Ta infusibility high-entropy alloys and preparation method thereof
CN109402482A (en) * 2018-12-10 2019-03-01 北京理工大学 It is a kind of to have both high-intensitive and high-ductility lightweight high-entropy alloy and preparation method thereof
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
CN110541103A (en) * 2019-08-27 2019-12-06 北京工业大学 High-strength high-plasticity quaternary refractory high-entropy alloy and preparation method thereof

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN115386774A (en) * 2021-09-30 2022-11-25 北京理工大学 Refractory high-entropy alloy with high strength and high uniform elongation and preparation method thereof
CN115386774B (en) * 2021-09-30 2023-10-13 北京理工大学 Refractory high-entropy alloy with high strength and high uniform elongation and preparation method thereof
CN114752792A (en) * 2022-04-18 2022-07-15 北京工业大学 High-entropy alloy with excellent mechanical property and oxidation resistance at high temperature and preparation method thereof
CN115404385A (en) * 2022-05-20 2022-11-29 太原理工大学 Refractory high-entropy alloy with excellent room-temperature tensile ductility and preparation method thereof
CN115404385B (en) * 2022-05-20 2023-08-15 太原理工大学 Refractory high-entropy alloy with excellent room-temperature tensile ductility and preparation method thereof

Also Published As

Publication number Publication date
CN113373366B (en) 2022-08-30

Similar Documents

Publication Publication Date Title
CN108642363B (en) High-strength high-plasticity eutectic high-entropy alloy and preparation method thereof
CN108220742B (en) Microalloyed Ti-Zr-Hf-V-Nb-Ta refractory high-entropy alloy and preparation method thereof
CN113373366B (en) Multi-element refractory high-entropy alloy and preparation method thereof
CN107419154B (en) One kind having hyperelastic TiZrHfNbAl high-entropy alloy and preparation method thereof
CN111549270B (en) Low-density high-strength high-plasticity high-entropy alloy material and preparation method thereof
CN113789464B (en) Ceramic phase reinforced refractory high-entropy alloy and preparation method thereof
CN110229991B (en) Quinary high-entropy alloy with excellent strong plasticity matching and preparation method thereof
CN110438387B (en) Silicide precipitation strengthening refractory high-entropy alloy and preparation method thereof
CN103602872A (en) TiZrNbVMo[x] high entropy alloy and preparation method thereof
CN111647789B (en) Alloying-method-based refined chromium-iron-cobalt-nickel-based high-entropy alloy crystal grain and preparation method thereof
CN114134385B (en) Refractory medium-entropy alloy and preparation method thereof
CN104213013A (en) TiZrNbMoxHfy multi-principal component high temperature alloy and preparation method thereof
CN113403520B (en) Ternary refractory medium-entropy alloy and preparation method thereof
CN113528920B (en) High-plasticity NbMoTaTiWC series refractory high-entropy alloy and preparation method thereof
CN110172630B (en) Quaternary hypoeutectic high-entropy alloy with good strong plasticity matching and preparation method thereof
CN114774752B (en) High-strength high-toughness TiZrNbMoV refractory high-entropy alloy and preparation method thereof
CN111676410B (en) High-strength high-toughness CoFeNiTiV high-entropy alloy and preparation method thereof
CN115627406A (en) Light refractory multi-principal-element alloy, and preparation method and application thereof
CN111676409B (en) Preparation method of low-density low-cost Fe-Mn-Al-C intermediate entropy alloy
CN113416878A (en) Re and Ru solid solution reinforced VNbTiTaRe and VNbTiTaRu high-entropy alloy and preparation method thereof
CN106011574B (en) A kind of Nb-Si based alloys of no hafnium high antioxidant and preparation method thereof
CN108277418B (en) MoNbTaTiHf high-entropy alloy material and preparation method thereof
CN114318105B (en) High-strength high-plasticity CrHfMoNbTi high-entropy alloy and preparation method thereof
CN111394636B (en) High-strength high-plasticity high-entropy alloy with martensite phase transformation and preparation method thereof
CN114134355A (en) Strengthening and toughening control method for refractory high-entropy alloy

Legal Events

Date Code Title Description
PB01 Publication
PB01 Publication
SE01 Entry into force of request for substantive examination
SE01 Entry into force of request for substantive examination
GR01 Patent grant
GR01 Patent grant