Nickel-based alloy with excellent high-temperature creep resistance and preparation method thereof

Abstract

The application provides a nickel-based alloy with excellent high-temperature creep resistance and a preparation method. The preparation method comprises the following steps: generating highly pure nanoceramic particles in a melt by an in-melt generation method, and stirring under the action of a magnetic field formed in a vacuum induction melting furnace, so that the nanoceramic particles are fully dispersed in the nickel-based alloy melt; and then, after vacuum casting, high-temperature homogenization treatment, high-temperature forging and vacuum heat treatment, a nickel-based alloy with excellent high-temperature creep resistance is finally obtained. The alloy has a creep life of 44.4h-83.9h, an elongation of 32.4%-46.3%, and a creep rate of 1.24*10 ‑7 s ‑1 -2.29*10 ‑7 s ‑1 .

Description

TECHNICAL FIELD

[0001] The present application relates to the technical field of high-performance high-temperature alloys, in particular to a nickel-based alloy with excellent high-temperature creep resistance and a preparation method thereof. BACKGROUND

[0002] Nickel-based alloys are widely used in service environments such as aircraft engines and gas turbines. Since nickel-based alloys are usually used in high-temperature environments, their creep resistance will decrease under high-temperature conditions, so it is necessary to improve the high-temperature creep resistance of nickel-based alloys. In addition, creep resistance is crucial to the above-mentioned application environments, because poor creep resistance can lead to machine part failure, forcing the equipment to be replaced or repaired prematurely, causing unnecessary economic losses, and even sudden high-temperature creep failure can cause catastrophic accidents such as explosions, so creep resistance directly determines the service life and reliability of the parts. The general high-temperature creep failure mechanism is based on the following contents: first, grain boundary weakening: voids are nucleated at the grain boundary, and micro-pores are generated at the interface between the grain boundary precipitates (such as M 23 C6 carbide) and the matrix due to stress concentration, while the viscous flow of the grain boundary at high temperature causes misfit between adjacent grains, promoting crack initiation and leading to accelerated creep rupture; second, degradation of strengthening phase: the γ' phase (Ni3Al) in the Ni-based alloy grows from 20-50 nm to submicron > 200 nm), causing the dislocation bypass mechanism (Orowan mechanism) to fail. Currently, the premature failure of high-temperature creep is mainly solved by solid solution strengthening and precipitation strengthening, and in addition, grain boundary strengthening can also be achieved by adding rare earth metal elements for micro-alloying. Although the above methods improve the high-temperature creep resistance to some extent, there are still the following problems: first, the improvement effect is not obvious. Second, the use of rare earth elements greatly increases the production cost of the alloy, and may also introduce unfavorable phases, which is not conducive to industrial production. Third, the complex process leads to uneven alloy organization, easy segregation, and even extremely difficult forging in the subsequent processing and forming stage. Fourth, while improving the creep resistance, the plasticity and other properties will be reduced, and it is difficult to simultaneously improve the creep resistance and plasticity. Therefore, how to reduce the raw material cost, simplify the process, simultaneously improve the strength, plasticity and creep resistance of the nickel-based alloy and realize industrialized production is a technical problem to be solved at present. SUMMARY

[0003] To solve the above technical problems, the present application provides a nickel-based alloy with excellent high-temperature creep resistance, and its preparation method is as follows:

[0004] Step 1, at room temperature, according to the mass percentage: Nb: 20-45%, B: 30-70%, put the Nb powder and B powder into a ball mill with a rotation speed of 65-90 rpm and mix for 8-10 hours to obtain a mixed powder A;

[0005] The particle size of the Nb powder is 40-145 microns, and the particle size of the B powder is 100-150 microns.

[0006] Step 2, the mixed powder B, mixed powder C and mixed powder D obtained by mixing the powder A obtained in step 1 with pure Ni powder in a volume ratio of 1-3:6-8, 2-4:6-9 and 1-4:7-9 respectively in a ball mill with a rotation speed of 45-70 rpm for 6-8 hours;

[0007] The particle size of the pure Ni powder is 75-135 microns;

[0008] Step 3, the powder B, powder C and powder D in step 2 are filled into a nickel-based thin cylinder in an upper-middle-lower order in a proportion of 2-3:3-4:5-6 by mass, and then sealed to obtain a nickel-based alloy containing a gradient distribution of mixed powder;

[0009] Step 4, under the condition of argon protection, the nickel-based alloy is heated to 1500-1600℃ and kept for 60-90min to obtain a nickel-based alloy melt, and the gradient distribution of mixed powder containing nickel-based alloy obtained in step 3 is gradually inserted into the nickel-based alloy melt for melting, and then after pouring, high temperature homogenization treatment, high temperature forging, vacuum solid solution and aging treatment, a nickel-based alloy with excellent high temperature creep resistance is obtained;

[0010] The high temperature homogenization treatment is kept at 1150-1170℃ for 5h;

[0011] The high temperature forging is carried out at a forging temperature of 1000-1200℃ and a forging ratio of 11-13:1;

[0012] The vacuum solid solution treatment is kept at 1038-1177℃ for 90-100min under vacuum condition and water cooled;

[0013] The vacuum aging treatment is kept at 795-820℃ for 5.5-9.5h under vacuum condition and air cooled;

[0014] The composition of the nickel-based alloy is: C: 0.04-0.08wt.%; Cr: 19.00-21.00wt.%; Si: 0.04-0.045wt.%; Mn: 0.36-0.44wt.%; P≤0.015wt.%; S≤0.007wt.%; Fe≤0.70wt.%; Al: 0.30-0.60wt.%; Ti: 1.90-2.40wt.%; the balance is Ni;

[0015] The mass percentage of the gradient distribution of mixed powder containing nickel-based alloy in the nickel-based alloy liquid is 0.02wt.%-0.12wt.%;

[0016] The nickel-based alloy with excellent high-temperature creep resistance contains uniformly dispersed nanoparticles, and has a creep life of 44.4h-83.9h, an elongation of 32.4%-46.3%, and a creep rate of 1.24*10 -7 s -1 -2.29*10 -7 s -1 .

[0017] Further, the particle size of the Nb powder is 60-130 microns, and the particle size of the B powder is 110-140 microns.

[0018] Further, the powder A and the pure Ni powder are mixed according to the volume ratio of 1-2:5-7, 2-3:7-8, and 2-3:8-9, and the particle size of the pure Ni powder is 82-120 microns.

[0019] Further, the powder B, the powder C, and the powder D are sequentially filled into the nickel-based thin cylinder according to the mass ratio of 2-3:3-4:5-6.

[0020] Further, the nickel-based alloy has the following components: C: 0.05-0.06wt.%; Cr: 19.70-20.00wt.%; Si: 0.04-0.043wt.%; Mn: 0.38-0.42wt.%; P≤0.013wt.%; S≤0.006wt.%; Fe≤0.60wt.%; Al: 0.40-0.60wt.%; Ti: 1.90-2.35wt.%; and the balance is Ni. BRIEF DESCRIPTION OF DRAWINGS

[0021] Figure 1 A schematic diagram of the nickel-based alloy containing mixed powders with gradient distribution prepared in Example 1 of the present application;

[0022] Figure 2 A creep curve diagram of the nickel-based alloy containing nanoceramic particles in Example 2 of the present application at 810℃ / 339MPa;

[0023] Figure 3 A creep curve diagram of the nickel-based alloy containing nanoceramic particles in Example 3 of the present application at 800℃ / 319MPa;

[0024] Figure 4 A creep curve diagram of the nickel-based alloy containing nanoceramic particles in Example 4 of the present application at 800℃ / 299MPa;

[0025] Figure 5 A creep curve diagram of the nickel-based alloy in Comparative Example 1 of the present application at 800℃ / 279MPa. DETAILED DESCRIPTION

[0026] The technical solutions in the embodiments of the present application will be clearly and completely described below. Obviously, the described embodiments are only some of the embodiments of the present application, but not all the embodiments. Based on the embodiments in the present application, all other embodiments obtained by those skilled in the art without creative work fall within the protection scope of the present application.

[0027] Embodiment 1

[0028] The preparation method of the gradient distribution mixed powder containing nickel-based alloy comprises the following steps:

[0029] Step 1: under the condition of room temperature, Nb powder and B powder are mixed in a ball mill with a rotating speed of 85 rpm for 9 hours according to the mass percentage of Nb: 23% and B: 77% to obtain powder A. The particle size of the Nb powder is 73 microns, and the particle size of the B powder is 123 microns.

[0030] Step 2: the powder A obtained in step 1 and pure Ni powder are mixed in a ball mill with a rotating speed of 70 rpm for 7 hours according to the volume ratio of 2:8, 4:6 and 1:9 to obtain mixed powder B, mixed powder C and mixed powder D. The particle size of the pure Ni powder is 107 microns.

[0031] Step 3: the powder B, the powder C and the powder D in step 2 are filled into a nickel-based thin cylinder in the order of top, middle and bottom according to the mass ratio of 1:2:7, and then the nickel-based thin cylinder is sealed to obtain the gradient distribution mixed powder containing nickel-based alloy, as shown in FIG. 1. Figure 1

[0032] Embodiment 2

[0033] The preparation method of the nickel-based alloy 1 with excellent high-temperature creep resistance comprises the following steps:

[0034] Under the condition of argon protection, the nickel-based alloy is heated to 1550℃ and kept for 75 min to obtain a nickel-based alloy melt. The gradient distribution mixed powder containing nickel-based alloy obtained in embodiment 1 is gradually inserted into the nickel-based alloy melt to melt. Under the driving force of high-temperature thermodynamics, the mixed powder generates nano ceramic particles in the nickel-based melt. After pouring, high-temperature homogenization treatment, high-temperature forging, vacuum solid solution and aging treatment, the nickel-based alloy 1 with excellent high-temperature creep resistance is obtained.

[0035] The mass ratio of the gradient distribution mixed powder containing nickel-based alloy and the nickel-based alloy is 0.006%:1.

[0036] ​The nickel-based alloy has the following components in percentage of mass: C: 0.051wt.%; Cr: 19.5wt.%; Si: 0.04wt.%; Mn: 0.36wt.%; P: 0.015wt.%; S: 0.007wt.%; Fe: 0.70wt.%; Al: 0.30wt.%; Ti: 1.90wt.%; and the balance of Ni;

[0037] The high-temperature homogenization treatment is: holding at 1153℃ for 5h;

[0038] The high-temperature forging is: forging at 1168℃ with a forging ratio of 12:1;

[0039] The vacuum solid solution treatment is: holding at 1155℃ for 90min under vacuum condition, and water cooling;

[0040] The vacuum aging treatment is: holding at 802℃ for 6.5h under vacuum condition, and air cooling.

[0041] The nickel-based alloy 1 prepared in this embodiment has uniformly dispersed nano ceramic particles with a particle size of 56-95nm, and the creep curve of the alloy at 810℃ and 339MPa is shown in Figure 2 The creep time reaches 44.4h and the creep elongation reaches 46.3%, and the creep rate after fitting calculation is 2.29×10 -7 s -1 .

[0042] Example 3

[0043] The nickel-based alloy 2 with excellent high-temperature creep resistance is prepared by the following steps:

[0044] The nickel-based alloy is heated to 1550℃ under argon protection and held for 75min to obtain a nickel-based alloy melt, and the gradient distribution nickel-based alloy containing mixed powder obtained in Example 1 is gradually inserted into the nickel-based alloy melt for melting. Under the driving force of high-temperature thermodynamics, the mixed powder generates nano ceramic particles in the nickel-based melt, and then the high-temperature creep resistant nickel-based alloy 2 is obtained after pouring, high-temperature homogenization treatment, high-temperature forging, vacuum solid solution and aging treatment;

[0045] The mass ratio of the gradient distribution nickel-based alloy containing mixed powder to the nickel-based alloy is 0.007%:1;

[0046] The nickel-based alloy has the following components in percentage of mass: C: 0.053wt.%; Cr: 19.59wt.%; Si: 0.047wt.%; Mn: 0.39wt.%; P: 0.014wt.%; S: 0.0069wt.%; Fe: 0.70wt.%; Al: 0.42wt.%; Ti: 1.93wt.%; and the balance of Ni; the high-temperature homogenization treatment is: 1150℃ for 5h;

[0047] The high-temperature forging is at a forging temperature of 1182℃ and a forging ratio of 11:1;

[0048] The vacuum solid solution treatment is: 1160℃ for 92min under vacuum condition and water cooling;

[0049] The vacuum aging treatment is: 798℃ for 6.5h under vacuum condition and air cooling;

[0050] The nickel-based alloy 2 prepared in the embodiment has uniformly dispersed nano ceramic particles with a particle size of 57-90nm, and its creep curve at 800℃ and 319MPa is shown in Figure 3 The creep time reaches 59.9h and the creep elongation reaches 38.3%, and the creep rate after fitting calculation is 1.28×10 -7 s -1 .

[0051] Example 4

[0052] The nickel-based alloy 3 with excellent high-temperature creep resistance is prepared by the following steps:

[0053] The nickel-based alloy is heated to 1550℃ under argon protection and kept for 75min to obtain a nickel-based alloy melt, and the gradient distribution nickel-based alloy containing mixed powder obtained in Example 1 is gradually inserted into the nickel-based alloy melt for melting. Under the driving force of high-temperature thermodynamics, the mixed powder generates nano ceramic particles in the nickel-based melt, and then the nickel-based alloy 3 with excellent high-temperature creep resistance is obtained after pouring, high-temperature homogenization treatment, high-temperature forging, vacuum solid solution and aging treatment;

[0054] The mass ratio of the gradient distribution nickel-based alloy containing mixed powder to the nickel-based alloy is 0.008%:1;

[0055] The nickel-based alloy has the following components in terms of mass percentage: C: 0.062 wt.%; Cr: 19.78 wt.%; Si: 0.043 wt.%; Mn: 0.36 wt.%; P: 0.011 wt.%; S: 0.005 wt.%; Fe: 0.70 wt.%; Al: 0.50 wt.%; Ti: 1.98 wt.%; the balance being Ni; the balance being Ni;

[0056] The high-temperature homogenization treatment is performed at 1155°C for 5h;

[0057] The high-temperature forging is performed at a forging temperature of 1175°C and a forging ratio of 12:1;

[0058] The vacuum solid solution treatment is performed at 1170°C for 95min under vacuum and water cooling;

[0059] The vacuum aging treatment is performed at 798°C for 6.5h under vacuum and air cooling;

[0060] The nickel-based alloy 3 prepared in the embodiment has uniformly dispersed nanoceramic particles with a particle size of 59-98nm, and the creep curve of the alloy at 800°C and 299MPa is shown in Figure 4 The creep time reaches 83.9h and the creep elongation reaches 32.4%, and the creep rate is 1.24x10 -7 s -1 .

[0061] Comparative Example 1

[0062] A nickel-based alloy, and a preparation method thereof, includes the following steps:

[0063] The nickel-based alloy is heated to 1550°C under argon protection for 75min to obtain a nickel-based alloy melt. The nickel-based alloy melt is cast into a cast nickel-based alloy ingot under vacuum, and then subjected to high-temperature homogenization treatment, high-temperature forging, vacuum solid solution and aging heat treatment to obtain the nickel-based alloy.

[0064] The nickel-based alloy has the following components in terms of mass percentage: C: 0.069 wt.%; Cr: 20.00 wt.%; Si: 0.044 wt.%; Mn: 0.39 wt.%; P: 0.010 wt.%; S: 0.001 wt.%; Fe: 0.70 wt.%; Al: 0.56 wt.%; Ti: 2.10 wt.%; the balance being Ni; the balance being Ni;

[0065] The high-temperature homogenization treatment is performed at 1153°C for 5h;

[0066] The high-temperature forging is at a forging temperature of 1169 DEG C and a forging ratio of 11:1.

[0067] The vacuum solid solution treatment is heat preservation at 1163 DEG C for 90 minutes under vacuum condition and water cooling.

[0068] The vacuum aging treatment is heat preservation at 801 DEG C for 7.5 hours under vacuum condition and air cooling.

[0069] The creep curve of the nickel-based alloy prepared in the comparative example 1 is as shown in the figure Figure 5 , the creep time is 6.19 hours, the creep elongation is 14.5%, and the creep rate is 2.22*10 -6 s -1 after fitting calculation.

[0070] The nickel-based alloy 1 prepared in the embodiment 2 has excellent high-temperature creep resistance, and the creep curve thereof under the condition of 810 DEG C and 339 MPa applied load is as shown in the figure Figure 2 , compared with the creep curve of the comparative example 1 under the condition of 800 DEG C and 279 MPa applied load (as shown in the figure Figure 5 ), the creep time of the embodiment 2 is greatly improved by about 617%, the creep elongation is improved by about 219%, and the creep rate is reduced by about 869%. Therefore, the high-temperature creep resistance of the nickel-based alloy 1 obtained in the embodiment is significantly better than that of the nickel-based alloy obtained in the comparative example 1.

[0071] The nickel-based alloy 2 prepared in the embodiment 3 has excellent high-temperature creep resistance, and the creep curve thereof under the condition of 800 DEG C and 319 MPa applied load is as shown in the figure Figure 3 , compared with the creep curve of the comparative example 1 under the condition of 800 DEG C and 279 MPa applied load (as shown in the figure Figure 5 ), the creep time of the embodiment 3 is greatly improved by about 868%, the creep elongation is improved by about 164%, and the creep rate is reduced by about 1634%. Therefore, the high-temperature creep resistance of the nickel-based alloy 2 obtained in the embodiment is significantly better than that of the nickel-based alloy obtained in the comparative example 1.

[0072] The nickel-based alloy 3 prepared in the embodiment 4 has excellent high-temperature creep resistance, and the creep curve thereof under the condition of 800 DEG C and 299 MPa applied load is as shown in the figure Figure 4 , compared with the creep curve of the comparative example 1 under the condition of 800 DEG C and 279 MPa applied load (as shown in the figure Figure 5As shown in Table 1, under the same working temperature and slightly higher load conditions, the creep time of the nickel-based alloy obtained in the present embodiment is greatly improved, the creep time is increased by about 1255%, the creep elongation is increased by about 123%, and the creep rate is reduced by about 1690%. Therefore, the high-temperature creep resistance of the nickel-based alloy obtained in the present embodiment is significantly better than that of the nickel-based alloy obtained in Comparative Example 1.

[0073] Comparative Example 2

[0074] In the doctoral thesis entitled "Preparation and Microstructure Performance of Oxide Dispersion Strengthened Nickel-based Superalloy" and collected in CNKI in 2022, the target nickel-based superalloy was prepared by adding 0.6% rare earth hydride (YH2) and hot pressing sintering. The creep time of the nickel-based superalloy under the condition of 800℃ and 100MPa load is 13.0h, the creep elongation is 17.5%, and the creep rate is 1.43x10 -4 s -1 The nickel-based superalloy strengthened by 0.6% YH2 has the following composition according to mass percentage: C: 0.054wt.%; Cr: 20.5wt.%; Fe 0.67wt.%; Al: 0.25wt.%; Ti: 0.56wt.%; Y: 0.6%; and the balance is Ni.

[0075] Compared with Comparative Example 2, the creep time, creep elongation, and creep rate of Examples 2-4 all have absolute advantages (shown in Table 1) under the same temperature and higher load conditions without using rare earth elements as a strengthening means and simplifying the preparation process. Therefore, the nickel-based superalloy obtained in the present application has good high-temperature creep resistance and meets the needs of industrial service performance of nickel-based superalloy.

[0076] Table 1 Comparison of high-temperature creep resistance of nickel-based alloy in comparative examples and examples

[0077]

[0078] The components, proportions, and process parameters used in Examples 2-4 of the present application are different, and the high-temperature creep resistance obtained in each example is also different, but it is higher than that obtained by the prior art, and it maintains a high strength and ductility. Therefore, it is not accidental that the high-temperature creep resistance of the nickel-based alloy strengthened by trace nanoceramic particles is greatly improved and maintains a high strength and ductility, but is determined by the synergistic control of component interaction, component proportion, process, and process parameters. And only within the scope of the present application, the optimal technical effect can be achieved.

[0079] In summary, compared with the prior art, the application firstly selects a simple preparation process and an easy-to-implement strengthening method, which greatly reduces the preparation cost; secondly, the ceramic particle content added by the application is extremely low, and the nano ceramic particles are prepared in the form of in-situ endogenous, which simplifies the process while ensuring the purity of the material; finally, without using rare earth metals and other precious metals and without reducing the toughness and strength of the nickel-based superalloy at high temperature, the high-temperature creep resistance of the nickel-based alloy is significantly improved. The specific analysis reasons mainly include: first, the nano ceramic particle lattice structure has good interface wettability with the matrix material, and the nano ceramic particle diameter is only 30-100 nm. Second, the nano ceramic particles effectively enhance the bonding force between the grain boundaries. Third, the addition of nano ceramic particles refines the gamma prime strengthening phase and weakens the degradation of the gamma prime strengthening phase at high temperature. Therefore, the nickel-based superalloy strengthened by trace nano ceramic particles effectively prolongs the service life of the workpiece during high-temperature long-time service; the large increase in elongation can avoid unannounced safety accidents caused by rapid crack propagation before workpiece failure, and reduces the safety hidden danger. At the same time, compared with the existing nickel-based alloy, the proposed technology greatly improves the high-temperature service life of the nickel-based alloy under the premise of controlling the cost, can be used in high-temperature long-time service industrial environment, is suitable for industrial production, breaks through the technical bottleneck of the existing technology that it is difficult to simultaneously improve the high-temperature creep resistance and high-temperature toughness of the high-temperature nickel alloy, the raw material cost is high, the preparation process is complex, and industrialization is difficult to achieve.

Claims

1. A nickel-based alloy with excellent high-temperature creep resistance, its preparation method is as follows: Step 1: At room temperature, according to the mass percentages: Nb: 23%, B: 77%, put Nb powder and B powder into a ball mill with a speed of 65-90 rpm and mix for 8-10 hours to obtain mixed powder A; The particle size of the Nb powder is 40-145 micrometers, and the particle size of the B powder is 100-150 micrometers. Step 2: Mix the mixed powder A obtained in Step 1 with pure Ni powder in a ball mill at a speed of 45-70 rpm for 6-8 hours at volume ratios of 1-3:6-8, 2-4:6-9 and 1-4:7-9 respectively to obtain mixed powder B, mixed powder C and mixed powder D. The pure Ni powder has a particle size of 75-135 micrometers; Step 3: Fill the nickel-based thin tube with mixed powders B, C, and D in step 2 in a mass ratio of 1-3:2-4:5-7 in the order of top, middle, and bottom, and then seal it to obtain a nickel-based alloy with a gradient distribution containing mixed powders. Step 4: Under argon protection, the nickel-based alloy is heated to 1500-1600℃ and held for 60-90 minutes to obtain a nickel-based alloy melt. The composition of the nickel-based alloy is: C: 0.04-0.08wt.%; Cr: 19.00-21.00wt.%; Si: 0.04-0.045wt.%; Mn: 0.36-0.44wt.%; P≤0.015wt.%; S≤0.007wt.%; Fe≤0.70wt.%; Al: 0.30-0.60wt.%; Ti: 1.90-2.40wt.%; balance Ni. The nickel-based alloy with gradient distribution containing mixed powder obtained in Step 3 is gradually inserted into the nickel-based alloy melt for melting. After casting, high-temperature homogenization treatment, high-temperature forging, vacuum solution treatment and aging treatment, a nickel-based alloy with excellent high-temperature creep resistance is obtained. The high-temperature homogenization treatment involves holding the temperature at 1150℃-1170℃ for 5 hours. The high-temperature forging described herein involves a forging temperature of 1000-1200℃ and a forging ratio of 11-13:

1. The vacuum solution treatment is as follows: holding at 1038-1177℃ under vacuum conditions for 90-100 minutes, followed by water cooling; Vacuum aging treatment is performed by holding the temperature at 795℃-820℃ under vacuum for 5.5-9.5 hours, followed by air cooling. The gradient distribution contains a nickel-based alloy with mixed powder and a nickel-based alloy melt with a mass ratio of 0.02wt.%-0.12wt.%:1; The aforementioned nickel-based alloy with excellent high-temperature creep resistance contains uniformly dispersed nanoparticles. At 800℃, it exhibits a creep life of 44.4h-83.9h, an elongation of 32.4%-46.3%, and a creep rate of 1.24×10⁻⁶. -7 s -1 -2.29×10 -7 s -1 .

2. The nickel-based alloy with excellent high-temperature creep resistance according to claim 1, characterized in that, The particle size of Nb powder in step 1 is 60-130 micrometers, and the particle size of B powder is 110-140 micrometers.

3. The nickel-based alloy with excellent high-temperature creep resistance according to claim 1, characterized in that, The mixed powder A described in step 2 is mixed with pure Ni powder in a ball mill at a speed of 45-70 rpm for 6-8 hours at volume ratios of 1-2:5-7, 2-3:7-8, and 2-3:8-9 to obtain mixed powder B, mixed powder C, and mixed powder D. The pure Ni powder has a particle size of 82-120 micrometers.

4. The nickel-based alloy with excellent high-temperature creep resistance according to claim 1, characterized in that, The mixed powders B, C, and D described in step 3 are filled into the nickel-based thin cylinder in a top-middle-bottom order according to a mass ratio of 2-3:3-4:5-6.

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