A method for preparing a mixed solid solution Ni-Pd-Re-Sc-Ti precision alloy slab

Abstract

The application belongs to the technical field of preparation and processing of high-temperature alloy materials, and particularly relates to a preparation method of mixed solid solution Ni-Pd-Re-Sc-Ti precision alloy slab. In order to realize composition homogenization and structure stability of the alloy on an atomic scale, the application adopts the following technical scheme: the mixed solid solution Ni-Pd-Re-Sc-Ti precision alloy slab contains Pd 21.14-30.42wt%, Re 5.41-14.79wt%, Sc 0.32-0.57wt%, Ti 3.24-5.12wt%, and the balance of Ni. The preparation method comprises the following steps: raw material preparation; smelting and casting to obtain an alloy billet; vacuum consumable melting to obtain an alloy rod; after drilling the alloy billet, the alloy rod is inserted into the alloy billet to obtain an alloy blank; preheating and rotary forging; wire drawing treatment; jacket forging; 2-pass hot rolling treatment after preheating; annealing treatment; 2-pass cold rolling treatment; and surface degreasing and cleaning. The mixed solid solution Ni-Pd-Re-Sc-Ti precision alloy slab prepared by the application has good tensile strength, yield strength, elongation and hardness.

Description

Technical Field

[0001] This invention belongs to the field of high-temperature alloy material preparation and processing technology, specifically relating to a method for preparing Ni-Pd-Re-Sc-Ti precision alloy slabs in a mixed solid solution. Background Technology

[0002] Precision resistance alloys are a class of functional materials with special physical properties. Their core characteristics lie in their ability to maintain a high degree of resistance stability over a wide temperature range, while also possessing an extremely low temperature coefficient of resistance (TCR), good long-term stability, low thermoelectric potential, and excellent resistance to environmental factors such as humidity and oxidation. They are core electronic materials for critical electronic components in aerospace, nuclear energy, precision instruments, and medical fields, and their performance directly determines the reliability, stability, and lifespan of the final product. Currently, high-performance alloys, represented by nickel-based alloys, are widely used due to their excellent electrical and mechanical properties. However, as modern cutting-edge equipment develops towards long-term reliable operation in extreme environments, traditional nickel-based alloys are gradually facing performance bottlenecks. On the one hand, developing a new generation of high-precision resistance alloys requires not only attention to their macroscopic resistivity and TCR, but also fundamentally solving core scientific problems such as the control of microstructure uniformity in multi-component systems, the precise suppression of harmful phases and impurity elements, and the synergistic stability of microstructure and electrical sensitivity in extreme environments. On the other hand, while pursuing high strength and high thermal stability, existing alloy systems often suffer from a significant reduction in plasticity, toughness, and hot working properties, leading to defects such as cracking, compositional segregation, and microstructure inhomogeneity during the preparation of large and complex slabs, which seriously restricts the yield and consistency of component performance.

[0003] There is an urgent need for a novel material design and preparation concept. Through compositional innovation and process reform, this concept aims to achieve atomic-scale compositional homogenization and structural stability of alloys while ensuring excellent processing performance. This will enable the development of next-generation precision resistor materials that meet the demands of future extreme environments and ultra-high precision requirements. Therefore, developing a method for preparing precision alloy slabs with high mechanical properties, good processing performance, and excellent electrical properties in the Ni-Pd-Re-Sc-Ti multi-component system is of significant industrial demand and technological value. This invention aims to solve the aforementioned problems in existing technologies by providing a dedicated preparation method with a reasonable process, strong controllability, and high yield. Summary of the Invention

[0004] The main objective of this invention is to overcome the shortcomings of existing technologies and provide a method for preparing high-precision multi-component microalloyed nickel-based alloy slabs. This method addresses the challenges encountered during the preparation of Ni-Pd-Re-Ti-Sc and other multi-component high-performance nickel-based alloy slabs, such as severe macroscopic segregation, formation of coarse and brittle phases, and aggregation of non-metallic inclusions at grain boundaries, caused by the significant differences in physical properties between high-melting-point elements (Re), high-density elements (Pd), and highly reactive elements (Sc, Ti) and the nickel matrix. This method ensures the purity of the alloy, significantly improves its overall mechanical properties, and ultimately yields multi-component microalloyed alloy slabs with uniform microstructure, excellent performance, and high precision.

[0005] To achieve the above objectives, the present invention adopts the following technical solution: a mixed solid solution Ni-Pd-Re-Sc-Ti precision alloy slab, composed of Ni, Pd, Re, Sc, and Ti, wherein the mass percentages of each element are: 5.41~9.79%Re, 16.14~25.42%Pd, 3.24~5.12%Ti, 0.32~0.57%Sc, with the balance being Ni. The mass percentages of each component satisfy the relationship: Pd = 1.5 xRe + 3 xSc + 2 xTi.

[0006] The method for preparing a mixed solid solution Ni-Pd-Re-Sc-Ti precision alloy slab includes the following steps:

[0007] S1. Clean the surfaces of Ni, Pd, and Re components, mix them according to the above mass percentages, and perform vacuum melting to obtain a round alloy ingot with a diameter of 150-200 mm.

[0008] S2. Clean the surfaces of each component of Sc and Ti, mix them according to the above mass percentages, and perform vacuum arc remelting to obtain Ti-Sc alloy rods with a diameter of 40mm;

[0009] S3. Drill holes in the round alloy ingot and insert 3-5 Ti-Sc alloy bars to obtain the billet;

[0010] S4. Preheat the billet;

[0011] S5. The preheated billet is rotated and forged to obtain the forging;

[0012] S6. Shot blasting treatment of the forgings;

[0013] S7. Repeat S5 and S6 3-4 times to obtain a fully processed workpiece, and cut it into bars with a length of no more than 1000 mm and a diameter of 20-30 mm.

[0014] S8. Perform a first annealing treatment on the bar stock to relieve stress;

[0015] S9. The sample obtained in S8 is subjected to a wire drawing process to obtain a wire with a diameter of 0.5 mm;

[0016] S10. The filament obtained in S9 is placed into a sheath and the sheath is welded and sealed.

[0017] S11. Preheat the shroud and perform rotary forging, then remove the shroud to obtain the forging;

[0018] S12. Shot blasting is performed on the forgings to obtain bars with a diameter of 40-50mm;

[0019] S13. Preheat the bar stock and perform two passes of unidirectional hot rolling, then use a wire cutting machine to adjust the width to obtain a 30-40mm plate;

[0020] S14. Perform a first annealing treatment on the sheet material obtained in S13 to relieve stress;

[0021] S15. The sample obtained in S14 is subjected to two cold rolling passes to obtain a 15-20mm cold-rolled sheet;

[0022] S16. Perform surface degreasing and cleaning treatment on the cold-rolled sheet.

[0023] Furthermore, in step S1, the specific method of melting and casting is as follows: a certain amount of Ni, Pd, and Re are weighed according to the mass percentage ratio and added to the crucible for melting under vacuum conditions, and then cast into a billet with a diameter of 150-200mm.

[0024] Furthermore, in S2, the specific method of vacuum consumable melting is as follows: Sc powder is mixed with sponge titanium, pressed, and welded into a consumable electrode with a diameter of 20 mm, and then melted in a water-cooled copper crucible with a diameter of 40 mm. The melting vacuum degree is set to ≤1 Pa, the melting current is 4 kA, and the melting voltage is 30 V to obtain an alloy rod with a diameter of 40 mm.

[0025] Furthermore, in step S4, the preheating temperature is set to 1000-1100℃.

[0026] Furthermore, in S5, the specific method of rotary forging is as follows: the rotary forging processing pressure is 90-110MPa, and the loading frequency is 500-600 times / min.

[0027] Furthermore, in S8, the specific method for annealing is as follows: the bar is first ground to remove surface impurities, and then annealed at 10e... -2 Under vacuum conditions, heat to 1100℃ within 30 minutes and then allow to cool naturally to room temperature.

[0028] Furthermore, in S9, the specific method of wire drawing is as follows: remove impurities from the surface of the sample obtained in S8, perform rapid drawing of the rod for 8 passes with an average reduction in surface area of ​​30%, and perform intermediate annealing after every 4 passes at a temperature of 1000℃ for 10 minutes; then perform rapid drawing for 12 passes with an average reduction in surface area of ​​25%, and perform intermediate annealing after every 4 passes at a temperature of 1000℃ for 10 minutes; finally, place it in a wire drawing machine and pull it outward by traction force to gradually reduce its cross-sectional area to form a wire or slender shape. The entire wire drawing process is immersed in the wire drawing liquid, and finally, an alloy wire with a diameter of 0.5 mm is obtained.

[0029] Furthermore, in S10, the specific method for the sheath is as follows: a stainless steel sheath and gasket are selected, boron nitride is applied inside the sheath as a transition layer, and the fine filaments obtained in S9 are tightly arranged in the sheath, and the opening is sealed by welding with a gasket.

[0030] Furthermore, in S11, the specific method of rotary forging is as follows: the preheating temperature is 1050-1100℃, the rotary forging processing pressure is 90-110MPa, and the loading frequency is 500-600 times / min.

[0031] Furthermore, in S13, the specific method of hot rolling is as follows: the billet is heated to 1000-1200℃, and then two passes of unidirectional hot rolling are performed, with the hot rolling temperature controlled at 1000-1200℃ and the reduction amount per pass being 10-15%; the wire cutting machine controls the width of the plate to be 42-50mm.

[0032] Furthermore, in S14, the annealing process is specifically performed as follows: the annealing temperature is 1050-1100℃, and the holding time is 30-60min.

[0033] Furthermore, in S15, the specific method of cold rolling is as follows: the annealed slab is fed into a twin-roll mill along the hot rolling direction for two passes of unidirectional cold rolling, with an average reduction of 20-30% per pass.

[0034] The beneficial effects of this invention are:

[0035] This invention provides a method for preparing a Ni-Pd-Re-Sc-Ti precision alloy slab using a mixed solid solution method. The alloy material comprises Ni, Pd, Re, Sc, and Ti. By adjusting the content of each component, the environmental adaptability and performance stability of the alloy material are significantly improved. The precision alloy slab prepared using the alloy material of this invention allows the added elements Pd, Re, and Sc to be effectively dissolved in the matrix through solid-state mechanical mixing and rotary forging. The resulting alloy slab exhibits ultra-high strength, good toughness, and excellent high-temperature stability.

[0036] In the process of preparing precision alloy slabs, this invention employs a solid-state mechanical mixing + rotary forging method. On the one hand, drilling-insertion instead of casting allows the added elements to diffuse slowly and in a controlled manner into the matrix during thermomechanical treatment, avoiding the formation of brittle phases and effectively improving the strength of the microstructure. On the other hand, rotary forging, as the core deformation and composite tool, provides multi-directional, high-frequency, and cumulative strain, enabling thorough mixing between different microstructures and ensuring the integrity of the composite process. Wire drawing + secondary rotary forging achieves three-dimensional balance of properties, greatly improving the isotropy of the material. Attached Figure Description

[0037] The invention will now be further described with reference to the accompanying drawings.

[0038] Figure 1 This is a flowchart of the process for manufacturing a Ni-Pd-Re-Sc-Ti precision alloy slab using a mixed solid solution method according to the present invention. Detailed Implementation

[0039] The technical solutions of the present invention will be clearly and completely described below with reference to the embodiments of the present invention. Obviously, the described embodiments are only some embodiments of the present invention, and not all embodiments. Based on the embodiments of the present invention, all other embodiments obtained by those of ordinary skill in the art without creative effort are within the scope of protection of the present invention. Example 1

[0040] A method for preparing a Ni-Pd-Re-Sc-Ti precision alloy slab with mixed solid solution includes the following steps:

[0041] S1. The surfaces of Ni, Pd and Re components are cleaned, and Re is 8.72wt%, Pd 23.41wt%, with the balance Ni. Vacuum melting is then performed to obtain a circular alloy ingot with a diameter of 180mm.

[0042] S2. Clean the surfaces of each component of Sc and Ti, and perform vacuum consumable melting with 0.41wt% Sc and 4.55wt% Ti. The specific method of vacuum consumable melting is as follows: Sc powder is mixed with sponge titanium, pressed and welded into a consumable electrode with a diameter of 20mm, and then melted in a water-cooled copper crucible with a diameter of 40mm. The melting vacuum degree is set to ≤1Pa, the melting current is 4kA and the melting voltage is 30V to obtain a Ti-Sc alloy rod with a diameter of 40mm.

[0043] S3. Drill holes in the round alloy ingot and insert four Ti-Sc alloy bars to obtain the billet;

[0044] S4. Preheat the billet to 1050℃;

[0045] S5. The preheated billet is subjected to rotary forging. The specific method of rotary forging is as follows: the rotary forging processing pressure is 105MPa and the loading frequency is 530 times / min to obtain the forging.

[0046] S6. Shot blasting treatment of the forgings;

[0047] S7. Repeat S5 and S6 three times to obtain a fully processed workpiece, and then cut it into bars with a length of no more than 1000 mm and a diameter of 23 mm.

[0048] S8. The bar stock undergoes a first annealing treatment. The specific annealing method involves first grinding the bar stock to remove surface impurities, and then annealing it at 10°C. -2 Under vacuum, heat to 1100℃ within 30 minutes and then cool naturally to room temperature to relieve stress;

[0049] S9. The sample obtained in S8 is subjected to a wire drawing process to obtain a wire with a diameter of 0.5 mm;

[0050] S10. The wire obtained in S9 is put into a sleeve and the sleeve is welded and sealed. The specific method of the sleeve is as follows: a stainless steel sleeve and gasket are selected, boron nitride is covered inside the sleeve as a transition layer, the wire obtained in S9 is tightly arranged in the sleeve, and the opening is welded and sealed with a gasket.

[0051] S11. The cladding is preheated and then subjected to rotary forging. The specific method of rotary forging is as follows: the preheating temperature is 1050℃, the rotary forging processing pressure is 93MPa, the loading frequency is 500 times / min, and the forging is obtained after removing the cladding.

[0052] S12. The forging is shot blasted to obtain a bar with a diameter of 45mm;

[0053] S13. The bar stock is preheated and subjected to two passes of unidirectional hot rolling. The specific method of hot rolling is as follows: the billet is heated to 1000℃, and then subjected to two passes of unidirectional hot rolling. The hot rolling temperature is controlled at 1100℃, and the reduction in each pass is 10%. The wire cutting machine controls the width of the plate to 48mm to obtain a plate with a thickness of 35mm.

[0054] S14. The board is subjected to a first annealing treatment. The specific method of the annealing treatment is as follows: the annealing temperature is 1100℃, the holding time is 50min, and the stress is relieved.

[0055] S15. The sample obtained in S14 is subjected to two passes of cold rolling. The specific method of cold rolling is as follows: the annealed slab is fed into a twin-roll mill along the hot rolling direction for two passes of unidirectional cold rolling. The average reduction per pass is 20%, and a 15mm cold-rolled plate is obtained.

[0056] S16. Perform surface degreasing and cleaning treatment on the cold-rolled sheet.

[0057] The finished sheet prepared in Example 1 was tested for mechanical properties. The tensile strength was 1820 MPa, the yield strength was 1479 MPa, the elongation was 10.6%, and the hardness was HRC48.7, which met the requirements for use. Example 2

[0058] A method for preparing a Ni-Pd-Re-Sc-Ti precision alloy slab with mixed solid solution includes the following steps:

[0059] S1. The surfaces of Ni, Pd and Re components are cleaned, and Re is 6.4wt%, Pd 18.5wt%, with the balance Ni. Vacuum melting is then performed to obtain a round alloy ingot with a diameter of 200mm.

[0060] S2. Clean the surfaces of each component of Sc and Ti, and perform vacuum consumable melting with 0.38wt% Sc and 3.88wt% Ti. The specific method of vacuum consumable melting is as follows: Sc powder is mixed with sponge titanium, pressed and welded into a consumable electrode with a diameter of 20mm, and then melted in a water-cooled copper crucible with a diameter of 40mm. The melting vacuum degree is set to ≤1Pa, the melting current is 4kA and the melting voltage is 30V to obtain a Ti-Sc alloy rod with a diameter of 40mm.

[0061] S3. Drill holes in the round alloy ingot and insert 5 Ti-Sc alloy bars to obtain the billet;

[0062] S4. Preheat the billet to 1100℃;

[0063] S5. The preheated billet is subjected to rotary forging. The specific method of rotary forging is as follows: the rotary forging processing pressure is 110MPa and the loading frequency is 600 times / min to obtain the forging.

[0064] S6. Shot blasting treatment of the forgings;

[0065] S7. Repeat S5 and S6 4 ​​times to obtain a fully processed workpiece, and cut it into bars with a length of no more than 1000 mm and a diameter of 30 mm.

[0066] S8. The bar stock undergoes a first annealing treatment. The specific annealing method involves first grinding the bar stock to remove surface impurities, and then annealing it at 10°C. -2 Under vacuum, heat to 1100℃ within 30 minutes and then cool naturally to room temperature to relieve stress;

[0067] S9. The sample obtained in S8 is subjected to a wire drawing process to obtain a wire with a diameter of 0.5 mm;

[0068] S10. The wire obtained in S9 is put into a sleeve and the sleeve is welded and sealed. The specific method of the sleeve is as follows: a stainless steel sleeve and gasket are selected, boron nitride is covered inside the sleeve as a transition layer, the wire obtained in S9 is tightly arranged in the sleeve, and the opening is welded and sealed with a gasket.

[0069] S11. Preheat the shroud and perform rotary forging. The specific method of rotary forging is as follows: the preheating temperature is 1050-1100℃, the rotary forging processing pressure is 110MPa, the loading frequency is 600 times / min, and the forging is obtained after removing the shroud.

[0070] S12. The forging is shot blasted to obtain a bar with a diameter of 50 mm;

[0071] S13. The bar stock is preheated and subjected to two passes of unidirectional hot rolling. The specific method of hot rolling is as follows: the billet is heated to 1150℃, and then subjected to two passes of unidirectional hot rolling. The hot rolling temperature is controlled at 1200℃, and the reduction in each pass is 15%. The wire cutting machine controls the width of the plate to 42mm to obtain a plate with a thickness of 40mm.

[0072] S14. The plate is subjected to a first annealing treatment. The specific method of the annealing treatment is as follows: the annealing temperature is 1100℃, the holding time is 60min, and the stress is relieved.

[0073] S15. The sample obtained in S14 is subjected to two cold rolling passes. The specific method of cold rolling is as follows: the annealed slab is fed into a twin-roll mill along the hot rolling direction for two unidirectional cold rolling passes, with an average reduction of 30% per pass, to obtain a 20mm cold-rolled plate.

[0074] S16. Perform surface degreasing and cleaning treatment on the cold-rolled sheet.

[0075] The finished sheet prepared in Example 2 was tested for mechanical properties. The tensile strength was 1762 MPa, the yield strength was 1456 MPa, the elongation was 8.2%, and the hardness was HRC50.6, which met the requirements for use. Example 3

[0076] A method for preparing a Ni-Pd-Re-Sc-Ti precision alloy slab with mixed solid solution includes the following steps:

[0077] S1. The surfaces of Ni, Pd and Re components are cleaned, and Re is 6.44wt%, Pd 21.14wt%, with the balance Ni. Vacuum melting is then performed to obtain a circular alloy ingot with a diameter of 180mm.

[0078] S2. Clean the surfaces of each component of Sc and Ti, and perform vacuum consumable melting with 0.50wt% Sc and 4.99wt% Ti. The specific method of vacuum consumable melting is as follows: Sc powder is mixed with sponge titanium, pressed and welded into a consumable electrode with a diameter of 20mm, and then melted in a water-cooled copper crucible with a diameter of 40mm. The melting vacuum degree is set to ≤1Pa, the melting current is 4kA and the melting voltage is 30V to obtain a Ti-Sc alloy rod with a diameter of 40mm.

[0079] S3. Drill holes in the round alloy ingot and insert three Ti-Sc alloy bars to obtain the billet;

[0080] S4. Preheat the billet to 1000℃;

[0081] S5. The preheated billet is subjected to rotary forging. The specific method of rotary forging is as follows: the rotary forging processing pressure is 90MPa and the loading frequency is 500 times / min to obtain the forging.

[0082] S6. Shot blasting treatment of the forgings;

[0083] S7. Repeat S5 and S6 4 ​​times to obtain a fully processed workpiece, and cut it into bars with a length of no more than 1000 mm and a diameter of 20 mm.

[0084] S8. The bar stock undergoes a first annealing treatment. The specific annealing method involves first grinding the bar stock to remove surface impurities, and then annealing it at 10°C. -2 Under vacuum, heat to 1100℃ within 30 minutes and then cool naturally to room temperature to relieve stress;

[0085] S9. The sample obtained in S8 is subjected to a wire drawing process to obtain a wire with a diameter of 0.5 mm;

[0086] S10. The wire obtained in S9 is put into a sleeve and the sleeve is welded and sealed. The specific method of the sleeve is as follows: a stainless steel sleeve and gasket are selected, boron nitride is covered inside the sleeve as a transition layer, the wire obtained in S9 is tightly arranged in the sleeve, and the opening is welded and sealed with a gasket.

[0087] S11. The cladding is preheated and then subjected to rotary forging. The specific method of rotary forging is as follows: the preheating temperature is 1050℃, the rotary forging processing pressure is 90MPa, the loading frequency is 500 times / min, and the forging is obtained after removing the cladding.

[0088] S12. The forging is shot blasted to obtain a bar with a diameter of 40 mm;

[0089] S13. The bar stock is preheated and subjected to two passes of unidirectional hot rolling. The specific method of hot rolling is as follows: the billet is heated to 1000℃, and then subjected to two passes of unidirectional hot rolling. The hot rolling temperature is controlled at 1200℃, and the reduction in each pass is 10%. The wire cutting machine controls the width of the plate to 50mm to obtain a plate with a thickness of 30mm.

[0090] S14. The board is subjected to a first annealing treatment. The specific method of the annealing treatment is as follows: the annealing temperature is 1050℃, the holding time is 30min, and the stress is relieved.

[0091] S15. The sample obtained in S14 is subjected to two passes of cold rolling. The specific method of cold rolling is as follows: the annealed slab is fed into a twin-roll mill along the hot rolling direction for two passes of unidirectional cold rolling. The average reduction per pass is 20%, and a 15mm cold-rolled plate is obtained.

[0092] S16. Perform surface degreasing and cleaning treatment on the cold-rolled sheet.

[0093] The finished sheet prepared in Example 3 was tested for mechanical properties. The tensile strength was 1921 MPa, the yield strength was 1637 MPa, the elongation was 15.2%, and the hardness was HRC49.8, which met the requirements for use.

[0094] It should be noted that, in this document, relational terms such as "first" and "second" are used only to distinguish one entity or operation from another, and do not necessarily require or imply any such actual relationship or order between these entities or operations. Furthermore, the terms "comprising," "including," or any other variations thereof are intended to cover non-exclusive inclusion, such that a process, method, article, or apparatus that comprises a list of elements includes not only those elements but also other elements not expressly listed, or elements inherent to such process, method, article, or apparatus.

[0095] Although embodiments of the invention have been shown and described, it will be understood by those skilled in the art that various changes, modifications, substitutions and alterations can be made to these embodiments without departing from the principles and spirit of the invention, the scope of which is defined by the appended claims and their equivalents.

Claims

1. A method for producing a precision alloy slab of a cast solid solution Ni-Pd-Re-Sc-Ti, characterized by, It comprises the following mass percentage raw materials: Pd 21.14-30.42wt%, Re 5.41-14.79wt%, Sc 0.32-0.57wt%, Ti 3.24-5.12wt%, and the balance of Ni, wherein the mass percentages of Pd, Re, Sc and Ti in the raw materials satisfy the relationship: Pd=1.5*Re+3*Sc+2*Ti; and its preparation process comprises the following steps: S1. cleaning the surfaces of each component of Ni, Pd and Re, and proportioning according to the above mass percentages, vacuum smelting to obtain a round alloy ingot; S2. cleaning the surfaces of each component of Sc and Ti, and proportioning according to the above mass percentages, vacuum consumable smelting to obtain a Ti-Sc alloy rod; S3. drilling the round alloy ingot and inserting 3-5 Ti-Sc alloy rods to obtain a blank; S4. preheating the blank; S5. rotating the preheated blank to obtain a forged piece; S6. shot blasting the forged piece; S7. repeating S5 and S6 for 3-4 times to obtain a completely processed workpiece, and cutting the workpiece into a rod; S8. annealing the rod once to remove stress; S9. drawing the sample obtained in S8 to obtain a wire; S10. loading the wire obtained in S9 into a sheath and welding the sheath to be sealed; S11. preheating the sheath and rotating to obtain a forged piece after cutting off the sheath; S12. shot blasting the forged piece to obtain a rod; S13. preheating the rod and performing 2 passes of unidirectional hot rolling, and then adjusting the width using a wire cutting machine to obtain a plate; S14. annealing the plate obtained in S13 once to remove stress; S15. cold rolling the sample obtained in S14 for 2 passes to obtain a cold rolled plate; S16. surface degreasing and cleaning the cold rolled plate.

2. The method for preparing a mixed solid solution Ni-Pd-Re-Sc-Ti precision alloy slab according to claim 1, characterized in that, The specific method of vacuum consumable smelting in S2 is as follows: mixing Sc powder with titanium sponge, pressing and welding into a consumable electrode with a diameter of 20 mm, and then smelting in a water-cooled copper crucible with a diameter of 40 mm, setting the smelting vacuum degree to be ≤1 Pa, the smelting current to be 4 kA, and the smelting voltage to be 30 V, to obtain an alloy rod with a diameter of 40 mm.

3. The method for preparing a mixed solid solution Ni-Pd-Re-Sc-Ti precision alloy slab according to claim 1, characterized in that, The specific method of rotating forging in S5 is as follows: the rotating forging processing pressure is 90-110 MPa, and the loading frequency is 500-600 times / min.

4. The method for preparing a mixed solid solution Ni-Pd-Re-Sc-Ti precision alloy slab according to claim 1, characterized in that, The specific method of annealing treatment in S8 is: first, the bar is polished to remove surface impurities, and then 10e -2 Pa is heated to 1100℃ in vacuum state within 30min and then naturally cooled to room temperature.

5. The method for preparing a mixed solid solution Ni-Pd-Re-Sc-Ti precision alloy slab according to claim 1, characterized in that, The specific method of rotating forging in S11 is as follows: the preheating temperature is 1050-1100℃, the rotating forging processing pressure is 90-110 MPa, and the loading frequency is 500-600 times / min.

6. The method of claim 1, wherein the method of producing a Ni-Pd-Re-Sc-Ti precision alloy slab is characterized by, The specific method of hot rolling in S13 is as follows: heating the blank to 1000-1200℃, and then performing 2 passes of unidirectional hot rolling, controlling the hot rolling temperature to be 1000-1200℃, and the reduction per pass to be 10-15%; the wire cutting machine controls the plate width to be 42-50 mm.

7. The method of claim 1, wherein the method is characterized by the steps of: The specific method of annealing in S14 is as follows: the annealing temperature is 1050-1100℃, and the holding time is 30-60 min.

8. The method of claim 1, wherein the method of producing a Ni-Pd-Re-Sc-Ti precision alloy slab is characterized by, The specific method of the S15 cold rolling is that the slab after the annealing treatment is fed into a double-roller mill along the hot rolling direction to perform 2 passes of one-way cold rolling, and the average pass reduction is 20-30%.

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