阅读说明：本技术 一种高强度高弹性应变的TiNbHfFeNi共晶高熵合金及其制备方法 (TiNbHfFeNi eutectic high-entropy alloy with high strength and high elastic strain and preparation method thereof ) 是由 朱正旺 李欢 张海峰 张宏伟 付华萌 李宏 王爱民 张龙 李正坤 耿铁强 于 2021-07-22 设计创作，主要内容包括：本发明涉及一种高强度高弹性应变的TiNbHfFeNi共晶高熵合金及其制备方法,属于金属材料技术领域。该共晶高熵合金的组成元素为Ti、Nb、Hf、Fe、Ni,原子百分比表达式为Ti-(30)Nb-(20)Hf-(10)Fe-(10)Ni-(30)。该合金铸态下为BCC与B2组成的共晶片层结构。室温压缩屈服强度为1755MPa,弹性应变为2.52％,抗压强度为2245MPa。在500℃的环境下具有1500MPa的屈服强度,弹性应变高达5.5％。该合金具有高强度高弹性应变等优点,并且合金具有优秀的高温力学性能。(The invention relates to a TiNbHfFeNi eutectic high-entropy alloy with high strength and high elastic strain and a preparation method thereof, belonging to the technical field of metal materials. The eutectic high-entropy alloy comprises the following components of Ti, Nb, Hf, Fe and Ni, and the atomic percentage expression is Ti 30 Nb 20 Hf 10 Fe 10 Ni 30 . The alloy is in an as-cast state of a eutectic lamellar structure consisting of BCC and B2. The room temperature compressive yield strength is 1755MPa, the elastic strain is 2.52 percent, and the compressive strength is 2245 MPa. The elastic strain of the material is up to 5.5 percent, and the material has a yield strength of 1500MPa under the environment of 500 ℃. The alloy has the advantages of high strength, high elastic strain and the like, and has excellent high-temperature mechanical properties.)

1. A high-strength high-elastic-strain TiNbHfFeNi eutectic high-entropy alloy is characterized in that: the atomic percent expression of the high-entropy alloy is Ti₃₀Nb₂₀Hf₁₀Fe₁₀Ni₃₀。

2. The TiNbHfFeNi eutectic high-entropy alloy with high strength and high elastic strain according to claim 1, wherein: the purities of the components of titanium, niobium, hafnium, iron and nickel are more than or equal to 99.9 percent, and the pure metal raw materials are all blocky or granular.

3. The preparation method of the TiNbHfFeNi eutectic high-entropy alloy with high strength and high elastic strain according to claim 1, is characterized by comprising the following steps:

step 1), converting the atomic percentage into the mass percentage according to the high-entropy alloy components, and weighing the ingredients;

step 2), removing oxide skins on the surfaces of the weighed raw materials one by one, and cleaning the raw materials;

step 3), placing the processed raw materials in a copper crucible of a vacuum non-consumable electric arc furnace according to the sequence of melting points from low to high; and titanium sponge is put into the rest copper crucible;

step 4) pumping the vacuum chamber in the smelting furnace to the vacuum degree of 1 multiplied by 10^-3～5×10^-3And (4) after Pa, filling high-purity argon of-0.05 to-0.1 MPa into the furnace, and repeatedly and uniformly smelting for multiple times to obtain the button-shaped ingot.

4. The preparation method of the TiNbHfFeNi eutectic high-entropy alloy with high strength and high elastic strain according to claim 3, characterized by comprising the following steps: in the step 1), the adopted raw materials are titanium sponge, niobium particles, crystallized hafnium, iron blocks and nickel particles.

5. The preparation method of the TiNbHfFeNi eutectic high-entropy alloy with high strength and high elastic strain according to claim 3, characterized by comprising the following steps: in the step 4), magnetic stirring is started in the process of repeatedly and uniformly smelting for multiple times, wherein the smelting times are 4 times.

6. A high strength high elastic strain tinbfhffeni eutectic high entropy alloy prepared according to the method of claim 3, wherein: the eutectic high-entropy alloy is in an eutectic lamellar structure consisting of BCC and B2 in an as-cast state.

7. The TiNbHfFeNi eutectic high-entropy alloy with high strength and high elastic strain according to claim 6, wherein: the compressive yield strength of the eutectic high-entropy alloy is 1755MPa at room temperature, the elastic strain is 2.52%, the compressive strength is 2245MPa, and the eutectic high-entropy alloy has obvious work hardening behavior after yielding in the compression process; the product has a yield strength of 1500MPa in an environment of 500 ℃, and the elastic strain is 5.5%; the product has a yield strength of 1200MPa in an environment of 600 ℃, and the elastic strain is 5.3 percent; the product has a yield strength of 951MPa and an elastic strain of 4.2 percent under the environment of 700 ℃.

Technical Field

The invention belongs to the field of designed metal materials and preparation thereof, and particularly relates to a TiNbHfFeNi eutectic high-entropy alloy with high strength and high elastic strain and a preparation method thereof.

Background

Due to the higher and higher requirements on various properties of the materials and the rapid development of the modern industrial industry in China, the common single traditional material cannot keep up with the higher requirements of the material. Most of the alloys that we commonly use are composed of two elements. Until the mid 1990 s, the concept of multi-principal element high entropy alloys was proposed by scholars like samourer Lei et al. The concept of the high-entropy alloy breaks through the concept of alloy preparation in the past, and the main components of the high-entropy alloy are at least five alloy elements. Once the high-entropy alloy concept is put forward, the attention point for researching the alloy is concentrated in the phase diagram, so that the cognition of people on the middle part of the phase diagram is improved, and the high-entropy alloy theory has important scientific research significance. The high-entropy alloy obtains good high-temperature stability, high strength, high hardness, good wear resistance, high corrosion resistance and a plurality of excellent properties due to the mutual coordination of various metal elements. The excellent performances enable the high-entropy alloy to have application prospects in various industries, such as aerospace, mechanical electronics, biomedical treatment, bridge construction, automobile industry and the like.

The design concept of the eutectic high-entropy alloy is firstly provided by Luyi of university of major continuance of engineering, and the design concept combines the excellent performances of the eutectic alloy and the high-entropy alloy. And designs a dual-phase AlCoCrFeNi2.1 eutectic high-entropy alloy with a hard B2 structure and a soft FCC structure. However, so far, experimental studies and theoretical studies on eutectic alloys are still very lacking.

Therefore, the eutectic high-entropy alloy with excellent performance is obtained through reasonable element content regulation and control, and the research on various performances and microstructure of the alloy structure has very important application value and theoretical significance.

Disclosure of Invention

The invention develops a TiNbHfFeNi eutectic high-entropy alloy with high strength and high elastic strain, and the eutectic high-entropy alloy has a two-phase (BCC + B2) structure.

The technical scheme of the invention is as follows:

a high-strength high-elastic-strain TiNbHfFeNi eutectic high-entropy alloy is characterized in that: the atomic percent expression of the high-entropy alloy is Ti₃₀Nb₂₀Hf₁₀Fe₁₀Ni₃₀。

Wherein the purities of the constituent elements of titanium, niobium, hafnium, iron and nickel are more than or equal to 99.9 percent, and the pure metal raw materials are all blocky or granular.

The invention discloses a preparation method of a TiNbHfFeNi eutectic high-entropy alloy with high strength and high elastic strain, which is characterized by comprising the following steps of:

step 1), converting the atomic percentage into the mass percentage according to the high-entropy alloy components, and weighing the ingredients;

step 2), removing oxide skins on the surfaces of the weighed raw materials one by one, and cleaning the raw materials (wherein industrial ethanol can be used for ultrasonic cleaning);

step 3), placing the processed raw materials in a copper crucible of a vacuum non-consumable electric arc furnace according to the sequence of melting points from low to high; and titanium sponge is put into the rest copper crucible;

step 4) pumping the vacuum chamber in the smelting furnace to the vacuum degree of 1 multiplied by 10^-3～3.5×10^-3And (4) after Pa, filling high-purity argon of-0.05 to-0.1 MPa into the furnace, and repeatedly and uniformly smelting for multiple times to obtain the button-shaped ingot.

As a preferred technical scheme:

in the step 1), the adopted raw materials are titanium sponge, niobium particles, crystallized hafnium, iron blocks and nickel particles.

In the step 4), magnetic stirring is started in the process of repeatedly and uniformly smelting for multiple times, wherein the smelting times are 4 times.

The TiNbHfFeNi eutectic high-entropy alloy with high strength and high elastic strain prepared by the method is characterized in that: the eutectic high-entropy alloy is in an eutectic lamellar structure consisting of BCC and B2 in an as-cast state.

Compared with the prior art, its advantage lies in:

1. the preparation method of the TiNbHfFeNi eutectic high-entropy alloy designed by the invention is simple and reliable.

2. The TiNbHfFeNi eutectic high-entropy alloy provided by the invention has a novel microstructure, and is a eutectic lamellar structure consisting of a Nb-rich BCC phase and a Nb-poor B2 phase.

3. The TiNbHfFeNi eutectic high-entropy alloy provided by the invention has the characteristics of high elastic strain, high strength and the like. The compressive yield strength of the eutectic high-entropy alloy is 1755MPa at room temperature, the elastic strain is 2.52%, the compressive strength is 2245MPa, and the eutectic high-entropy alloy has obvious work hardening behavior after yielding in the compression process; the product has a yield strength of 1500MPa in an environment of 500 ℃, and the elastic strain is 5.5%; the product has a yield strength of 1200MPa in an environment of 600 ℃, and the elastic strain is 5.3 percent; the product has a yield strength of 951MPa and an elastic strain of 4.2 percent under the environment of 700 ℃.

Drawings

FIG. 1 is an XRD spectrum of the prepared TiNbHfFeNi eutectic shape memory high-entropy alloy;

FIG. 2 is a microstructure of the prepared TiNbHfFeNi eutectic shape memory high-entropy alloy;

FIG. 3 is a room temperature compressive engineering stress-strain curve of the prepared TiNbHfFeNi eutectic shape memory high-entropy alloy;

FIG. 4 is a true stress-strain curve of the prepared TiNbHfFeNi eutectic shape memory high-entropy alloy compressed at different high temperatures.

Detailed Description

The technical scheme of the invention is clearly and completely described in the following with reference to the accompanying drawings and specific embodiments.

Examples

The preparation method of the TiNbHfFeNi eutectic high-entropy alloy comprises the following specific steps:

(1) preparing raw materials: the metal raw material used in the invention is high-purity (more than or equal to 99.9%). Wherein, the raw material Ti is sponge titanium, Nb is niobium particles, Hf is crystallized hafnium, Fe is iron block, and Ni is nickel particles. Weighing and proportioning according to the mass ratio, removing oxide skin on the surface of the raw material, cleaning by ultrasonic oscillation in alcohol, and drying.

(2) Preparing an alloy: the invention adopts a vacuum arc furnace to smelt the alloy. The raw materials of Fe and Ni are separately placed in one copper crucible, and the raw materials of Nb, Hf and Ti are placed in the other copper crucible, so that the intermediate alloy is firstly prepared. Oxygen-absorbing titanium sponge is added into the vacant copper crucible. Vacuum-pumping to 3.5X 10^-3Pa, then filling high-purity argon to-0.08 MPa. And (3) opening magnetic stirring in the smelting process to ensure that the chemical components are uniform. And putting the smelted intermediate alloys together, smelting the final alloy, and repeatedly smelting for 4 times.

And (3) finishing alloy smelting, filling air after the furnace body is cooled, opening the furnace door, taking out an alloy ingot to obtain an as-cast alloy, and performing structural characterization and mechanical property test.

Referring to fig. 1, it can be seen that the eutectic high entropy alloy of the embodiment of the present invention has a BCC + B2 crystal structure at room temperature. Referring to FIG. 2, the microscopic structure was a co-wafer layer, wherein the black phase was a Nb-rich BCC phase and the white phase was a Nb-poor B2 phase, and the thickness of the black phase was about 40nm, which reached the standard of the nano-material. Referring to fig. 3, it can be seen that the compressive yield strength of the alloy is 1755MPa, the elastic strain is 2.52%, the compressive strength is 2245MPa, and the work hardening behavior is evident after the yield is reached in the compression process. It can be seen that the alloy has the advantages of high strength, high elastic strain and the like. Referring to fig. 4, it can be seen from the true compressive stress-strain curve that the alloy has excellent high temperature mechanical properties (i.e. high elastic strain and high strength), and has a yield strength of 1500MPa at 500 ℃, and the elastic strain becomes as high as 5.5%. The alloy has a yield strength of 1200MPa in an environment of 600 ℃, and the elastic strain is up to 5.3 percent. The alloy has a yield strength of 951MPa in an environment of 700 ℃, and the elastic strain is up to 4.2 percent. The yield strength and elastic strain become lower with increasing temperature, and the elastic modulus does not change significantly.

The invention is not the best known technology.

The above embodiments are merely illustrative of the technical ideas and features of the present invention, and the purpose thereof is to enable those skilled in the art to understand the contents of the present invention and implement the present invention, and not to limit the protection scope of the present invention. All equivalent changes and modifications made according to the spirit of the present invention should be covered within the protection scope of the present invention.