阅读说明：本技术 900℃组织稳定的立方形γ′纳米粒子共格析出强化的高温合金及制备方法 (Cubic gamma' nano particle coherent precipitation strengthened high-temperature alloy with stable structure at 900 ℃ and preparation method thereof ) 是由 王清 李金临 董闯 吕梦甜 于 2021-08-26 设计创作，主要内容包括：本发明提供一种900℃组织稳定的立方形γ’纳米粒子共格析出强化的高温合金及制备方法,属于Co基高温合金领域,包括Co、Ni、Al、W、Mo、Ti、Nb、Ta、Cr元素,其合金成分的质量百分比(wt.％)为,Ni：22.6～28.2,Al：2.6～4.2,W：9.1～17.7,Mo：0～5.0,Ti：1.2～1.5,Nb：0～2.4,Ta：0～4.6,Cr：2.4～5.1,Co：余量。本发明通过合金成分设计实现了立方形的γ′纳米粒子在γ基体上共格析出,且γ′纳米粒子在900℃可长期稳定存在,使该合金具有良好的高温力学性能、优异的抗氧化性、耐蚀性及抗热腐蚀能力；另外,本发明的制备工艺简单,是一种在航空航天领域具有良好应用前景的新型高温合金。(The invention provides a 900 ℃ structure stable cubic gamma' nano particle coherent precipitation strengthened superalloy and a preparation method thereof, belonging to the field of Co-based superalloys, comprising Co, Ni, Al, W, Mo, Ti, Nb, Ta and Cr elements, wherein the mass percentage (wt.%) of the alloy components is as follows: 22.6-28.2, Al: 2.6-4.2, W: 9.1 to 17.7, Mo: 0 to 5.0, Ti: 1.2 to 1.5, Nb: 0 to 2.4, Ta: 0-4.6, Cr: 2.4-5.1, Co: and (4) the balance. The invention realizes coherent precipitation of cubic gamma 'nano particles on a gamma matrix through alloy component design, and the gamma' nano particles can stably exist for a long time at 900 ℃, so that the alloy has good high-temperature mechanical property, excellent oxidation resistance, corrosion resistance and hot corrosion resistance; in addition, the preparation process is simple, and the high-temperature alloy has good application prospect in the field of aerospace.)

1. The cubic gamma ' -nano particle coherent precipitation strengthened superalloy with the 900 ℃ structure stability is characterized by consisting of two coherent phases of gamma/gamma ', wherein a matrix is in an FCC-gamma solid solution structure, and a precipitation phase is an ordered superstructure phase of an FCC-gamma solid solution and is gamma ' - (Co/Ni)₃(Al,W,Mo,Ti,Nb,Ta)(ii) a The cubic gamma' -nano particle coherent precipitation strengthened Co-Ni-Al-W/Mo-Cr-Ti/Nb/Ta high-temperature alloy comprises Co, Ni, Al, W, Mo, Ti, Nb, Ta and Cr elements, wherein the mass percentage (wt.%) of the alloy components is as follows: 22.6-28.2, Al: 2.6-4.2, W: 9.1 to 17.7, Mo: 0 to 5.0, Ti: 1.2 to 1.5, Nb: 0 to 2.4, Ta: 0-4.6, Cr: 2.4-5.1, Co: and (4) the balance.

2. The 900 ℃ structure-stable cubic gamma' nanoparticle coherent precipitation-strengthened superalloy as claimed in claim 1, wherein the Co-Ni-Al-W/Mo-Cr-Ti/Nb/Ta superalloy has a specific structure morphology: cubic gamma' - (Co/Ni)₃The (Al, W, Mo, Ti, Nb, Ta) nano particles are coherently precipitated on an FCC-gamma matrix, and the gamma' nano particles are not obviously coarsened after long-term aging at 900 ℃, so that the high-temperature structure stability is realized.

3. A method of making a 900 ℃ tissue stable cubic gamma prime nanoparticle coherent precipitation strengthened superalloy as claimed in claim 1 or 2, comprising the steps of: firstly, putting the alloy components into vacuum arc melting according to the mass percentage for at least four times to obtain alloy ingots with uniform components; secondly, carrying out solution treatment on the alloy ingot by using a muffle furnace, wherein the treatment temperature is 1250-1300 ℃, the treatment time is 15-18 h, and water quenching; and then carrying out aging treatment for 10-500 h at 800-900 ℃, and carrying out water quenching to obtain the Co-Ni-Al-W/Mo-Cr-Ti/Nb/Ta high-temperature alloy.

Technical Field

The invention belongs to the field of Co-based high-temperature alloys, and relates to a Co-Ni-Al-W/Mo-Cr-Ti/Nb/Ta high-temperature alloy which is strengthened by coherent precipitation of cubic gamma' nanoparticles with a stable structure at 900 ℃ and a preparation method thereof.

Background

The high-temperature alloy has excellent mechanical property and creep resistance at high temperature, and is applied to the fields of aerospace engines and industrial gas turbines, wherein the high-temperature alloy has cubic ordered gamma' (L1)₂-Ni₃Al structure) nano particles are most widely applied to Ni-based high-temperature alloys which are coherently precipitated on a face-centered cubic FCC-gamma matrix. However, with the continuous development of aerospace technology in recent years, the service temperature of the Ni-based superalloy is close to the melting point thereof, and it is difficult to continuously meet the actual demand. The Co element has a higher melting point and a better hot corrosion resistance than the Ni element, so the Co-based superalloy becomes a research hotspot in recent years. The traditional Co-based high-temperature alloy is usually added with elements such as Cr, W, Nb, Ta, Ti, C and the like, and can precipitate carbide (MC/M) on an FCC-gamma matrix while playing a role of solid solution strengthening₂₃C₆Etc.), but the precipitation strengthening of the carbide particles is much lower at high temperatures than the gamma/gamma' coherent precipitation strengthening. In addition, the Co element can generate isomerous transformation from an FCC structure to a close-packed hexagonal HCP structure below 420 ℃, and the instability of the structure seriously limits the further improvement of the high-temperature performance and the use temperature of the traditional Co-based high-temperature alloy.

Unlike conventional Co-based superalloys, Sato et Al in 2006 first discovered a Co-Al-W ternary alloy system with L1₂Structural gamma' -Co₃(Al, W) precipitate phase, and successfully prepare the alloy with the similar coherent structure as the Ni-based superalloy, namely cubic gamma' -Co₃The (Al, W) nano particles are coherently precipitated on a gamma-Co matrix, so that the alloy shows excellent mechanical properties at 870 ℃. Gamma' -Ni, however, stable to high temperatures₃Al is different from metastable gamma' -Co₃The (Al, W) phase is easily decomposed into FCC-gamma, beta-CoAl and chi-Co during aging at high temperature of 900 ℃ and above₃W and mu-Co₇W₆The stable phase will destroy the original gamma/gamma' co-crystal due to the change of the crystal structure of the precipitated phaseA lattice relationship; and large lattice distortion exists between the stable precipitated phases and the matrix, and stress concentration is easily generated in the dislocation motion process, so that crack initiation is induced, and the mechanical property of the alloy is deteriorated.

Therefore, two core problems that restrict the development and application of current Co-based superalloys: on one hand, how to realize coherent precipitation of cubic gamma' nano particles on an FCC-gamma matrix; on the other hand, the cubic gamma' nano particles can stably exist for a long time in a high-temperature service environment at the temperature of 900 ℃ and above. In view of the above, the invention provides a Co-Ni-Al-W/Mo-Cr-Ti/Nb/Ta high-temperature alloy which is coherent precipitation strengthened by cubic gamma' nano particles with a stable structure at 900 ℃.

Disclosure of Invention

The invention designs and develops a 900 ℃ structure stable cubic gamma 'nano particle coherent precipitation strengthened Co-Ni-Al-W/Mo-Cr-Ti/Nb/Ta high-temperature alloy, compared with the existing Co-based high-temperature alloy, the alloy has cubic gamma' - (Co/Ni)₃The (Al, W, Mo, Ti, Nb and Ta) nano particles are coherently precipitated on an FCC-gamma matrix, and the gamma' nano particles are not obviously coarsened after long-term aging at 900 ℃, so that the alloy shows excellent thermodynamic stability, and has good high-temperature mechanical property, excellent oxidation resistance, excellent corrosion resistance and excellent hot corrosion resistance. The invention aims to develop a novel high-temperature alloy with good application prospect in the field of aerospace through alloy component design.

The technical scheme adopted by the invention is as follows:

a cubic gamma ' nano particle coherent precipitation strengthened Co-Ni-Al-W/Mo-Cr-Ti/Nb/Ta high-temperature alloy with stable structure at 900 ℃, wherein the Co-Ni-Al-W/Mo-Cr-Ti/Nb/Ta high-temperature alloy consists of two coherent phases of gamma/gamma ', a matrix is an FCC-gamma solid solution structure, and a precipitation phase is an ordered superstructure phase of FCC-gamma solid solution, namely gamma ' - (Co/Ni)₃(Al, W, Mo, Ti, Nb, Ta). The cubic gamma' -nano particle coherent precipitation strengthened Co-Ni-Al-W/Mo-Cr-Ti/Nb/Ta high-temperature alloy comprises Co, Ni, Al, W, Mo, Ti, Nb, Ta and Cr elements, wherein the mass percentage (wt.%) of the alloy components is as follows: 22.6-28.2, Al: 2.6-4.2, W: 9.1 to 17.7Mo: 0 to 5.0, Ti: 1.2 to 1.5, Nb: 0 to 2.4, Ta: 0-4.6, Cr: 2.4-5.1, Co: and (4) the balance.

The Co-Ni-Al-W/Mo-Cr-Ti/Nb/Ta high-temperature alloy has a specific microstructure appearance: cubic gamma' - (Co/Ni)₃The (Al, W, Mo, Ti, Nb and Ta) nano particles are coherently precipitated on a face-centered cubic FCC-gamma matrix, and the gamma' nano particles are not obviously coarsened after long-term aging at 900 ℃, so that the alloy has high-temperature structure stability, and the alloy has good high-temperature mechanical property, excellent oxidation resistance, corrosion resistance and hot corrosion resistance.

A preparation method of a 900 ℃ structure-stable cubic gamma' nanoparticle coherent precipitation-strengthened Co-Ni-Al-W/Mo-Cr-Ti/Nb/Ta high-temperature alloy comprises the following steps: firstly, putting the alloy components into vacuum arc melting according to the mass percentage for at least four times to obtain an alloy ingot; secondly, carrying out solution treatment on the alloy ingot by adopting a muffle furnace, wherein the treatment temperature is 1250-1300 ℃, the treatment time is 15-18 h, and water quenching is carried out, so that the purpose is to obtain a supersaturated solid solution with uniform components, eliminate component segregation and dissolve non-uniform precipitated phases in the alloy; and then carrying out aging treatment for 10-500 h at 800-900 ℃, carrying out water quenching, and controlling the size and volume percentage of gamma ' particles by changing the aging temperature and time so as to enable the gamma/gamma ' coherent structure to reach the best in order to disperse and distribute the gamma ' nanoparticles on the FCC-gamma solid solution matrix, thereby improving the mechanical property of the high-temperature alloy.

The conception for realizing the technical scheme is as follows:

the cluster type component design method of the applicant is utilized to design the components of the Co-Ni-Al-W/Mo-Cr-Ti/Nb/Ta high-temperature alloy. The component design method is based on a structure model of 'cluster + connecting atom', and divides a stable solid solution structure into two parts of cluster and connecting atom, wherein the cluster is a nearest neighbor coordination polyhedron formed by taking a certain atom as a center, for example, the cluster in an FCC (fluid catalytic cracking) structure is a cuboctahedron with a coordination number of CN12, and the connecting atom is arranged at a gap position of a cluster stack and is usually positioned at the next nearest neighbor shell layer of the cluster. Thus, a simple cluster composition [ cluster ] can be determined](connecting atom)_mI.e. one cluster is matched to m connecting atoms. The cluster component design method is successfully applied to the design of various engineering alloys such as high-temperature special stainless steel, low-elasticity beta-Ti alloy, high-temperature high-entropy alloy and the like, and provides a new idea and method for the component design of high-performance engineering alloys.

According to the previous work of the applicant, in the Ni-based superalloy system, elements can be classified into three groups, i.e., Al-based elements, according to their roles in the alloyCr series elementAnd a base Ni-based elementWherein Al-based elements and Ni-based elements have strong interaction, so that Al-based elements preferentially occupy the central atomic position of the cluster, and Cr-based elements having relatively weak interaction with the matrix occupy the linking atomic position, thereby obtaining an ideal cluster composition formula of the Ni-based superalloyIn the Co-based superalloy, only the alloying elements are classified into the Al system because the W element is more distributed into the precipitation phase and the Cr element is dissolved in the matrix, which is typically different from the Ni-based superalloyMo, Ti, Nb, Ta) and Co systemsTwo elements, thereby obtaining the ideal cluster composition formula of the Co-based high-temperature alloy

In the case of a Co-based superalloy, the Al-based elementVegetable extractAll are gamma' phase forming elements, wherein Al can form compact Al on the surface of the alloy at high temperature₂O₃The protective film plays a key role in the oxidation resistance of the alloy, and meanwhile, the density of Al is low, so that the alloy density is favorably reduced. W and Mo are important solid solution strengthening elements, the stability of the gamma 'phase can be improved, and the coarsening rate of the gamma' phase is controlled by W; however, too much W and Mo may cause acicular chi-Co to form in the alloy₃(W, Mo), and the W density is large, and excessive addition increases the alloy density. The addition of Ti, Nb and Ta can obviously increase the dissolution temperature of the gamma 'phase and increase the volume fraction of the gamma' phase; however, if Nb and Ta are added excessively, a TCP phase rich in Nb and Ta is precipitated at the grain boundary of the alloy, and the mechanical properties of the alloy are seriously deteriorated. For Co series elementsThe addition of the Ni element can expand the function of the composition of the gamma 'phase of the Co-Al-W ternary system and simultaneously improve the stability of the gamma' phase. In a Co-Al-W ternary system, the addition of Ni can also reduce the lattice constant of a precipitated phase gamma ', thereby reducing the lattice mismatch between a matrix gamma and the precipitated phase gamma ', and being more beneficial to coherent precipitation of the gamma ' phase. Cr is a forming element of a gamma phase, has a solid solution strengthening effect, and can form Cr on the surface of the alloy at high temperature similarly to Al₂O₃The protective film improves the oxidation resistance and the hot corrosion resistance of the alloy; however, when the Cr content is too high, the alloy is likely to precipitate a σ phase, which lowers the structural stability of the alloy, and is not favorable for the precipitation of cubic γ' nanoparticles. Finally, the components of the Co-Ni-Al-W/Mo-Cr-Ti/Nb/Ta high-temperature alloy which is strengthened by coherent precipitation of cubic gamma' nanoparticles with stable structure at 900 ℃ are Co- (22.6-28.2) Ni- (2.6-4.2) Al- (9.1-17.7) W- (0-5.0) Mo- (1.2-1.5) Ti- (0-2.4) Nb- (0-4.6) Ta- (2.4-5.1) Cr (wt.%).

The preparation method of the invention comprises the following steps: high-purity metal materials are adopted and mixed according to the mass percentage. By using vacuum non-selfThe consumable arc melting furnace melts the ingredients for at least four times under the protection of argon atmosphere to obtain an alloy ingot with uniform components and the mass of about 120g, and the mass loss in the melting process is not more than 0.1 percent. Carrying out solid solution treatment on the alloy ingot by using a muffle furnace, wherein the temperature of the solid solution treatment is 1250-1300 ℃, and the time is 15-18 h, so as to obtain a supersaturated solid solution with uniform components, eliminate component segregation and dissolve uneven precipitated phases in the alloy; and then, carrying out aging treatment on the alloy sample, wherein the aging treatment temperature is 800-900 ℃, the aging time is 10-500 h, and in order to disperse and distribute the gamma ' nanoparticles on the FCC-gamma solid solution matrix and control the size and volume percentage of the gamma ' particles by changing the aging temperature and time, the gamma/gamma ' coherent structure is optimal, so that the mechanical property of the high-temperature alloy is improved, and all the heat treatment processes are water quenching treatment. Using metallographic microscope (OM), Scanning Electron Microscope (SEM), Transmission Electron Microscope (TEM) and X-ray diffractometer (XRD, Cu K)_αRadiation, λ 0.15406nm) to detect alloy structure and structure; the hardness test of the series alloy in different heat treatment states is carried out by using an HVS-1000 Vickers hardness tester. Therefore, the Co-Ni-Al-W/Mo-Cr-Ti/Nb/Ta high-temperature alloy which is coherent precipitation strengthened by the cubic gamma' nano particles with the stable structure at 900 ℃ is determined. The mass percentage (wt.%) of the alloy components is Ni: 22.6-28.2, Al: 2.6-4.2, W: 9.1 to 17.7, Mo: 0 to 5.0, Ti: 1.2 to 1.5, Nb: 0 to 2.4, Ta: 0-4.6, Cr: 2.4-5.1, Co: and (4) the balance. The indexes of the structure and the room temperature performance of the material are as follows: the alloy has a room temperature hardness of 342-430 kgf mm^-2Room temperature yield strength σ_sNot less than 830MPa, tensile strength sigma_b1080MPa or more and 24 percent or more of elongation delta after fracture; yield strength sigma at 800 DEG C_sNot less than 510MPa, tensile strength sigma_bNot less than 630MPa, and the elongation delta after fracture not less than 6.8 percent; 900 ℃ yield strength sigma_sNot less than 280MPa, tensile strength sigma_bNot less than 300MPa, and the elongation delta after fracture not less than 78%; after the alloy is aged at 800-900 ℃ (10-500 h), cubic gamma' nanoparticles (93-364 nm) are coherently precipitated on a gamma matrix.

Compared with the prior art, the invention has the beneficial effects that:

(1) the invention designs and develops a Co-Ni-Al-W/Mo-Cr-Ti/Nb/Ta high-temperature alloy which is strengthened by coherent precipitation of cubic gamma' nano particles and has a stable structure at 900 ℃ according to a self-developed cluster component method. Different from the traditional Co-based high-temperature alloy carbide dispersion strengthening and solid solution strengthening mechanism, the invention adopts a brand new concept of coherent precipitation strengthening, through coherent precipitation of cubic gamma ' phase nano particles on a gamma matrix, the cubic gamma ' phase nano particles exist stably at 900 ℃, the volume fraction of the gamma ' phase is kept above 60%, the size of the gamma ' nano particles does not change greatly after long-term aging, other harmful phases are not precipitated, the gamma ' phase is uniformly precipitated and a coherent phase interface, the initiation of cracks is hindered, the mechanical property of the Co-Ni-Al-W/Mo-Cr-Ti/Nb/Ta high-temperature alloy is improved, and meanwhile, the addition of Cr and Al enables the alloy to have excellent oxidation resistance, corrosion resistance and hot corrosion resistance.

(2) The microstructure of the superalloy appears as a cubic gamma' - (Co/Ni)₃The (Al, W, Mo, Ti, Nb, Ta) nano particles are coherently precipitated on an FCC-gamma matrix, and the gamma' nano particles are not obviously coarsened after long-term aging at 900 ℃, so that the high-temperature tissue stability is realized; due to the unique gamma/gamma' coherent structure, the series of high-temperature alloys have good high-temperature mechanical properties, excellent oxidation resistance, corrosion resistance and hot corrosion resistance.

Drawings

FIG. 1 is an SEM histotopography of the alloy prepared in example 1 with cubic gamma prime nanoparticles coherently precipitated on an FCC-gamma matrix.

Detailed Description

The following describes the embodiments of the present invention in detail with reference to the technical solutions.

Example 1: co-22.6Ni-2.6Al-17.7W-1.5Ti-0.7Nb-1.5Ta-2.5Cr (wt.%) alloy

The method comprises the following steps: alloy preparation

High-purity metal materials are adopted and mixed according to the mass percentage. The ingredients are melted repeatedly for at least four times by adopting a vacuum non-consumable arc melting furnace under the protection of argon atmosphere to obtain an alloy ingot with uniform components and a mass of about 120g, and the mass loss in the melting process is not more than 0.1 percent. Carrying out solution treatment on the alloy ingot at the temperature of 1300 ℃/15h by using a muffle furnace, water quenching and solution treatment, wherein the purpose of the solution treatment is to reduce or eliminate component segregation of a structure and dissolve uneven precipitated phases; then carrying out aging treatment at 900 ℃ for 500h and water quenching.

Step two: alloy texture Structure and mechanical Property testing

The OM, SEM and XRD are used for detecting the microstructure and structure of the alloy after aging treatment, and the result shows that the alloy structure is that cubic gamma ' nano particles are coherently precipitated on a gamma matrix, the gamma ' nano particles can stably exist for a long time at the high temperature of 900 ℃, the microstructure pattern of the alloy is shown in figure 1, and the size of the gamma ' nano particles is about 235nm after aging for 500 hours; hardness test was carried out by using a Vickers hardness tester HV 424kgf mm^-2And the mechanical property data at room temperature is measured by using a UTM5504 electronic universal tensile testing machine: yield strength sigma_s960MPa tensile Strength σ_b1320MPa, elongation after break delta 24%; mechanical properties data at 800 ℃: yield strength sigma_s590MPa tensile strength sigma_b700MPa, and 6.8 percent of elongation after fracture; mechanical properties data at 900 ℃: yield strength sigma_s320MPa tensile strength sigma_b360MPa and 78% elongation after break.

Example 2: co-28.2Ni-2.6Al-17.7W-1.5Ti-0.7Nb-1.5Ta-2.5Cr (wt.%) alloy

The method comprises the following steps: alloy preparation

High-purity metal materials are adopted and mixed according to the mass percentage. The ingredients are melted repeatedly for at least four times by adopting a vacuum non-consumable arc melting furnace under the protection of argon atmosphere to obtain an alloy ingot with uniform components and a mass of about 120g, and the mass loss in the melting process is not more than 0.1 percent. Carrying out solution treatment on the alloy ingot at the temperature of 1300 ℃/15h by using a muffle furnace, water quenching and solution treatment, wherein the purpose of the solution treatment is to reduce or eliminate component segregation of a structure and dissolve uneven precipitated phases; then carrying out aging treatment at 900 ℃ for 10h, and carrying out water quenching.

Step two: alloy texture Structure and mechanical Property testing

The microstructure and the structure of the alloy after the aging treatment are detected by using OM, SEM and XRD, and the result shows that the alloy structure is that cubic gamma' nano particles are coherently precipitated on a gamma matrix, and is similar to the embodiment 1; hardness test was carried out by using a Vickers hardness tester (HV 400 kgf. mm)^-2And the mechanical property data at room temperature is measured by using a UTM5504 electronic universal tensile testing machine: yield strength sigma_s890MPa tensile Strength σ_b1230MPa, elongation at break delta 29%; mechanical properties data at 800 ℃: yield strength sigma_s550MPa tensile strength sigma_b650MPa, elongation after break delta 8.1%; mechanical properties data at 900 ℃: yield strength sigma_s300MPa tensile strength sigma_b330MPa and 85% elongation after break.

Example 3: co-22.6Ni-2.6Al-17.7W-1.5Ti-0.8Nb-1.5Ta-5.1Cr (wt.%) alloy

The method comprises the following steps: alloy preparation

High-purity metal materials are mixed according to mass percentage. The ingredients are melted repeatedly for at least four times by adopting a vacuum non-consumable arc melting furnace under the protection of argon atmosphere to obtain an alloy ingot with uniform components and a mass of about 120g, and the mass loss in the melting process is not more than 0.1 percent. Carrying out solution treatment on the alloy ingot at the temperature of 1300 ℃/15h by using a muffle furnace, water quenching and solution treatment, wherein the purpose of the solution treatment is to reduce or eliminate component segregation of a structure and dissolve uneven precipitated phases; then carrying out aging treatment at 900 ℃ for 100h, and carrying out water quenching.

Step two: testing the organization structure, mechanical property and corrosion resistance of the alloy

The microstructure and the structure of the alloy after the aging treatment are detected by using OM, SEM and XRD, and the result shows that the alloy structure is that cubic gamma' nano particles are coherently precipitated on a gamma matrix, and is similar to the embodiment 1; hardness test was carried out by using a Vickers hardness tester HV 392kgf mm^-2And the mechanical property data at room temperature is measured by using a UTM5504 electronic universal tensile testing machine: yield strength sigma_s870MPa tensile Strength σ_b1180MPa, and elongation after break delta of 31%; mechanical properties at 800 DEG CData: yield strength sigma_s530MPa tensile Strength σ_b640MPa, and elongation after break delta of 10.2%; mechanical properties data at 900 ℃: yield strength sigma_s290MPa tensile strength sigma_b320MPa and 89% elongation after break.

Example 4: co-24.0Ni-4.2Al-9.4W-5.0Mo-1.2Ti-2.4Nb-2.7Cr (wt.%) alloy

The method comprises the following steps: alloy preparation

High-purity metal materials are mixed according to mass percentage. The ingredients are melted repeatedly for at least four times by adopting a vacuum non-consumable arc melting furnace under the protection of argon atmosphere to obtain an alloy ingot with uniform components and a mass of about 120g, and the mass loss in the melting process is not more than 0.1 percent. Performing solid solution treatment of 1250 ℃/18h on the alloy ingot by using a muffle furnace, water quenching and solid solution treatment, wherein the purpose of the solid solution treatment is to reduce or eliminate component segregation of a structure and dissolve uneven precipitated phases; then carrying out aging treatment at 800 ℃ for 500h and water quenching.

Step two: testing the organization structure, mechanical property and corrosion resistance of the alloy

The microstructure and the structure of the alloy after the aging treatment are detected by using OM, SEM and XRD, and the result shows that the alloy structure is that cubic gamma' nano particles are coherently precipitated on a gamma matrix, and is similar to the embodiment 1; hardness test was carried out by using a Vickers hardness tester HV 352kgf mm^-2And the mechanical property data at room temperature is measured by using a UTM5504 electronic universal tensile testing machine: yield strength sigma_s830MPa tensile strength sigma_b1080MPa, elongation after break delta 32%; mechanical properties data at 800 ℃: yield strength sigma_s510MPa tensile strength σ_b630MPa, elongation after break delta 10.8%; mechanical properties data at 900 ℃: yield strength sigma_s280MPa tensile strength sigma_b300MPa, and 91% elongation after break.

Example 5: co-23.5Ni-3.8Al-13.5W-2.5Mo-1.3Ti-4.6Ta-3.4Cr (wt.%) alloy

The method comprises the following steps: alloy preparation

High-purity metal materials are mixed according to mass percentage. The ingredients are melted repeatedly for at least four times by adopting a vacuum non-consumable arc melting furnace under the protection of argon atmosphere to obtain an alloy ingot with uniform components and a mass of about 120g, and the mass loss in the melting process is not more than 0.1 percent. Performing solid solution treatment of 1250 ℃/18h on the alloy ingot by using a muffle furnace, water quenching and solid solution treatment, wherein the purpose of the solid solution treatment is to reduce or eliminate component segregation of a structure and dissolve uneven precipitated phases; then carrying out aging treatment at 800 ℃ for 10h, and carrying out water quenching.

Step two: testing the organization structure, mechanical property and corrosion resistance of the alloy

The microstructure and the structure of the alloy after the aging treatment are detected by using OM, SEM and XRD, and the result shows that the alloy structure is that cubic gamma' nano particles are coherently precipitated on a gamma matrix, and is similar to the embodiment 1; hardness test was carried out by using a Vickers hardness tester HV of 386kgf mm^-2And the mechanical property data at room temperature is measured by using a UTM5504 electronic universal tensile testing machine: yield strength sigma_s860MPa tensile Strength σ_b1120MPa, and 30% elongation after break; mechanical properties data at 800 ℃: yield strength sigma_s515MPa tensile strength sigma_b630MPa, elongation after break delta 11.2%; mechanical properties data at 900 ℃: yield strength sigma_s280MPa tensile strength sigma_b300MPa and 90% elongation after break.

The above-mentioned embodiments only express the embodiments of the present invention, but not should be understood as the limitation of the scope of the invention patent, it should be noted that, for those skilled in the art, many variations and modifications can be made without departing from the concept of the present invention, and these all fall into the protection scope of the present invention.