High-temperature corrosion-resistant high-temperature alloy and preparation method thereof

Abstract

The embodiment of the invention provides a high-temperature corrosion-resistant superalloy and a preparation method thereof, relates to the technical field of metal structure materials, and discloses a nickel-based wrought superalloy which comprises the following components in percentage by weight: 0.04-0.08% of C, 28.5-29.5% of Cr, 10.0-12.0% of W, 3.0-5.0% of Mo, 1.0-1.5% of Al, 0.5-0.8% of Ti, less than or equal to 1% of Fe, 0.8% of Si and the balance of Ni. The deformation high temperature is solid solution strengthening type nickel-based anti-oxidation high-temperature alloy, and the alloy density is 8.88 g / cm < 3 >. The high-temperature alloy designed by the invention is mainly used for a sintering key part of a coke reactor, ensures that the high-temperature alloy has high temperature resistance, oxidation resistance, CO resistance and tar corrosion resistance at a use temperature, and also has very good plasticity and excellent welding performance.

Description

Technical Field

[0001] This invention relates to the field of metallic materials technology, specifically to a high-temperature corrosion-resistant high-temperature alloy and its preparation method. Background Technology

[0002] Coke has become the most important basic raw material in blast furnace smelting. In recent years, with the development and progress of blast furnace smelting technology, especially the rapid development of large-capacity blast furnaces, high blast temperature technology, and oxygen-enriched pulverized coal injection technology, coke, as the backbone of the blast furnace burden, has played an even more prominent role in ensuring gas and liquid permeability within the furnace. The quality of coke, especially its reactivity and post-reaction strength, has a significant impact on the modern blast furnace smelting process, becoming a key factor limiting the stable, balanced, high-quality, and efficient production of molten iron. The ironmaking and coking industries have reached an unprecedented level of awareness of its importance and dependence on its parameters. The NSC method is specifically designed for the routine testing of coke reactivity and resistance to melting loss. The reactor testing of key sintering components uses high-temperature alloy welded pipes, which are resistant to high temperatures, oxidation, CO, and tar corrosion, while also possessing excellent plasticity and superior welding performance.

[0003] The coke reactivity and post-reaction strength testing device is mainly used to determine the reactivity and post-reaction strength of coke required for blast furnace ironmaking. The timeliness and accuracy of its test data are crucial for the stable operation of the blast furnace. The selected high-temperature alloys need to possess the following characteristics: 1. Sufficiently high Cr content, typically around 20%, to ensure the formation of a Cr2O3-based oxide film in the oxidizing environment, giving the alloy good oxidation resistance and heat corrosion resistance; 2. Solid solution strengthening by adding refractory metal elements, such as Mo, W, or Co. Solid solution strengthening elements improve the alloy's strength from room temperature to high temperatures by generating lattice distortion, deformation of long and short-range stress fields, and the creation of short-range ordered or atomically segregated regions, thereby increasing interatomic bonding forces; 3. Controlled C content, adding a reasonable amount of C to strengthen grain boundaries and improve the alloy's creep strength; 4. The selected high-temperature alloys are primarily Ni-based, followed by Co-based. Ni-based high-temperature alloys have a stable austenitic structure and good oxidation and corrosion resistance. The high-temperature alloy steel used in the coke reactors currently in use (meeting GB / T 4000—2008) is GH23 or GH44.

[0004] GH44 alloy is a solid solution strengthened nickel-based oxidation-resistant alloy containing high levels of Cr (23.5~26.5%) and W (13.0~16.0%). It exhibits high plasticity and moderate hot strength below 900 °C, along with excellent oxidation resistance and good stamping and welding properties. It is suitable for manufacturing sheet metal stamping and welding structural components for the main combustion chamber and afterburner of aero-engines, which operate for extended periods below 900 °C, as well as mounting edges, ducts, guide vanes, heat shields, and guide vanes. Therefore, the selection of high-temperature alloy steel for reactors is reasonable. However, with in-depth research on the reactivity and post-reaction strength of coke, the thermal properties of coke under alkali metal corrosion conditions have begun to be studied. The high-temperature alloy steel reactors in GB / T 4000—2008 exhibit poor resistance to alkali metal corrosion. Summary of the Invention

[0005] The present invention aims to at least solve one of the technical problems existing in the prior art, and provides a high-temperature corrosion-resistant high-temperature alloy and its preparation method.

[0006] In a first aspect, embodiments of the present invention provide a high-temperature corrosion-resistant high-temperature alloy, wherein the composition of the high-temperature alloy by weight percentage includes C 0.04~0.08%, Cr 28.5~29.5%, W 10.0~12.0%, Mo 3.0~5.0%, Al 1.0~1.5%, Ti 0.5~0.8%, Fe ≤1%, Si 0.8%, and Ni as the balance.

[0007] Furthermore, the weight percentage content of Cr in the deformed superalloy is 29~29.5%.

[0008] Furthermore, the total weight percentage of W and Mo in the deformed superalloy is 15-17%.

[0009] Furthermore, the Al+Ti content of the deformed superalloy is 1.3~2% by weight.

[0010] Secondly, embodiments of the present invention provide a method for preparing a high-temperature corrosion-resistant high-temperature alloy, wherein the high-temperature alloy is the high-temperature alloy described above, and the method includes the following steps: Step 1, Annealing: Hold the hot-rolled ingot at 1200-1250℃ for 5-30 minutes, then cool it to room temperature with water; Step 2, Deformation treatment: The annealed sheet is subjected to cold deformation with a total deformation of 60-80%, using multiple passes of pressing, with each pass having a pressing rate of 20-25%, and lubricated with emulsion. Step 3, solution treatment: keep the cold-rolled sheet at 1140-1160℃ for 2-4 hours, air cool to room temperature, and then dry by pickling.

[0011] Furthermore, the microstructure of the prepared high-temperature corrosion-resistant superalloy is single-phase austenite and a small amount of MC and M23C6 type carbides, with an average grain size of no more than 100 μm.

[0012] Furthermore, the oxidation rate of the prepared high-temperature corrosion-resistant superalloy at 900℃ is 0.0573 g / (m). 2 The oxidation rate at 1000℃ is 0.113 g / (m·h). 2 ·h).

[0013] Compared with existing technologies, the high-temperature corrosion-resistant high-temperature alloy and its preparation method proposed in this invention have the following beneficial effects: This invention effectively regulates the grain size and uniformity of the alloy by controlling the alloy composition and heat treatment process, thereby improving the alloy's high-temperature strength, oxidation resistance, and corrosion resistance. The short-time annealing in step 1 aims to eliminate residual internal stress generated during hot rolling, providing a uniform microstructure for the subsequent cold rolling deformation process and reducing the alloy's deformation resistance. The annealing temperature and holding time in this step are selected based on eliminating residual stress and controlling grain size; therefore, a holding time of 1200-1250℃ for 5-10 minutes is chosen to both eliminate some residual internal stress and control grain size. The deformation treatment in step 2 aims to introduce deformation distortion energy, providing the driving force for recrystallization induced by subsequent solution treatment. This step should ensure the introduction of uniform and sufficient deformation distortion energy while suppressing the temperature rise of the alloy caused by deformation. Therefore, cold rolling with a total deformation of 60-80% is selected, with a reduction rate of 20-25% per pass. Controlling the reduction rate per pass can suppress deformation temperature rise and ensure uniform deformation, while controlling the total deformation ensures the introduction of sufficient deformation distortion energy. The main purpose of step 3, solution treatment, is to induce recrystallization. This process should prevent abnormal grain growth while ensuring sufficient recrystallization, and at the same time, the migration rate of grain boundaries should be slowed down as much as possible. Therefore, holding at 1140-1160℃ for 2-4 hours is selected, which ensures sufficient recrystallization and controls abnormal grain growth. Based on this preparation process, the oxidation resistance and acid and alkali corrosion resistance of the alloy in the service environment are improved by further increasing the Cr content, while the content of the solid solution strengthening element Mo is increased to further improve the performance of the alloy.

[0014] This invention utilizes a heat treatment process of annealing, cold rolling, and solution treatment to control the alloy grain size and eliminate internal stress, thereby enabling the alloy to serve for extended periods in harsh environments. Besides improving the manufacturing process, the purpose and composition range of controlling the main elements in the aforementioned high-temperature deformation mixture are based on the following reasons: Cr, W, and Mo are all important solid solution strengthening elements in nickel-based superalloys. Cr enters the matrix, causing lattice distortion and reducing stacking fault energy, thus improving the alloy's high-temperature creep resistance. Furthermore, Cr is a good antioxidant; in hot corrosive environments, Cr can promote the formation of a dense Cr2O3 oxide film on the alloy surface, reducing the maximum corrosion depth. Therefore, the Cr content was increased to 29.5%.

[0015] Mo can increase Mo effectively inhibits dislocation movement and improves the creep properties of the alloy by reducing mismatch. At the same time, Mo can also reduce the notch sensitivity of the alloy. However, excessive addition of Mo can lead to the precipitation of the harmful TCP phase, which also has an adverse effect on the hot corrosion resistance and oxidation resistance of the alloy. Therefore, the Mo content should be controlled at 3-5%.

[0016] The inclusion of titanium dioxide (W) into the γ-matrix can increase strength. Furthermore, W can improve the creep properties of the alloy. W has a similar effect to Mo; to control the W+Mo content at 15-17%, W is controlled at 10-12%. Attached Figure Description

[0017] To more clearly illustrate the specific embodiments of the present invention or the technical solutions in the prior art, the drawings used in the description of the specific embodiments or the prior art will be briefly introduced below. Obviously, the drawings described below are some embodiments of the present invention. For those skilled in the art, other drawings can be obtained from these drawings without creative effort.

[0018] Figure 1 This is a photograph of the microstructure of the high-temperature corrosion-resistant high-temperature alloy in solid solution state as described in Comparative Example 1 of the present invention; Figure 2 The image shows the microstructure of the high-temperature corrosion-resistant high-temperature alloy in solid solution state as described in Example 1 of this invention. Figure 3 The image shows the microstructure of the high-temperature corrosion-resistant high-temperature alloy in solid solution state as described in Example 2 of this invention. Figure 4 The image shows the microstructure of the high-temperature corrosion-resistant high-temperature alloy in solid solution state as described in Example 3 of this invention. Figure 5 The image shows the microstructure of the high-temperature corrosion-resistant high-temperature alloy in solid solution state as described in Example 4 of this invention. Figure 6This is a photograph of the microstructure of the high-temperature corrosion-resistant high-temperature alloy in solid solution state as described in Example 5 of the present invention. Detailed Implementation

[0019] To enable those skilled in the art to better understand the technical solutions of the present invention, the present invention will be further described in detail below with reference to the accompanying drawings and specific embodiments. Obviously, the described embodiments are only some, not all, of the embodiments of the present invention. All other embodiments obtained by those skilled in the art based on the described embodiments of the present invention without creative effort are within the scope of protection of the present invention.

[0020] Unless otherwise specifically stated, the technical or scientific terms used in the embodiments of this invention should be understood in their ordinary meaning as understood by one of ordinary skill in the art to which this invention pertains. The terms "comprising" or "including," as used in the embodiments of this invention, do not limit the shapes, numbers, steps, actions, operations, components, elements, and / or groups thereof mentioned, nor do they exclude the appearance or addition of one or more other different shapes, numbers, steps, actions, operations, components, elements, and / or groups thereof, or the inclusion of these.

[0021] Unless otherwise specifically stated, the relative arrangement, numerical expressions, and values ​​of the components and steps described in these embodiments do not limit the scope of the invention. It should also be understood that, for ease of description, the dimensions of the various parts shown in the drawings are not drawn to actual scale, and techniques, methods, and apparatus known to those skilled in the art may not be discussed in detail; however, where appropriate, the illustrated techniques, methods, and apparatus should be considered part of the specification. In all the examples shown and discussed herein, any other specific example may have different values. It should be noted that similar symbols and letters in the following figures denote similar items; therefore, once an item is defined in one figure, it need not be further discussed in subsequent figures.

[0022] In the description of the embodiments of the present invention, the terms "one embodiment," "some embodiments," "example," "specific example," or "some examples," etc., refer to specific features, structures, materials, or characteristics described in connection with that embodiment or example, which are included in at least one embodiment or example of the present invention. In the embodiments of the present invention, the illustrative expressions of the above terms do not necessarily refer to the same embodiment or example. Moreover, the specific features, structures, materials, or characteristics described may be combined in a suitable manner in any one or more embodiments or examples. Furthermore, without contradiction, those skilled in the art can combine and integrate the different embodiments or examples described in the embodiments of the present invention, as well as the features of different embodiments or examples.

[0023] This invention relates to a high-temperature corrosion-resistant high-temperature alloy, the composition of which by weight percentage includes C 0.04~0.08%, Cr 28.5~29.5%, W 10.0~12.0%, Mo 3.0~5.0%, Al 1.0~1.5%, Ti 0.5~0.8%, Fe ≤1%, Si 0.8%, and Ni as the balance.

[0024] Furthermore, the weight percentage content of Cr in the deformed superalloy is 29~29.5%.

[0025] Furthermore, the total weight percentage of W and Mo in the deformed superalloy is 15-17%.

[0026] Furthermore, the Al+Ti content of the deformed superalloy is 1.3~2% by weight.

[0027] Based on the same inventive concept, this invention also provides a method for preparing a high-temperature corrosion-resistant high-temperature alloy, wherein the high-temperature alloy is the high-temperature alloy described above, and the method includes the following steps: Step 1, Annealing: Hold the hot-rolled ingot at 1200-1250℃ for 5-30 minutes, then cool it to room temperature with water; Step 2, Deformation treatment: The annealed sheet is subjected to cold deformation with a total deformation of 60-80%, using multiple passes of pressing, with each pass having a pressing rate of 20-25%, and lubricated with emulsion. Step 3, solution treatment: keep the cold-rolled sheet at 1140-1160℃ for 2-4 hours, air cool to room temperature, and then dry by pickling.

[0028] Furthermore, the microstructure of the prepared high-temperature corrosion-resistant superalloy is single-phase austenite and a small amount of MC and M23C6 type carbides, with an average grain size of no more than 100 μm.

[0029] Furthermore, the oxidation rate of the prepared high-temperature corrosion-resistant superalloy at 900℃ is 0.0573 g / (m). 2 The oxidation rate at 1000℃ is 0.113 g / (m·h). 2 ·h).

[0030] The high-temperature corrosion-resistant superalloy and its preparation method of this invention effectively regulate the grain size and uniformity of the alloy by controlling the alloy composition and heat treatment regime, thereby improving the high-temperature strength, oxidation resistance, and corrosion resistance of the alloy. In step 1, the short-time annealing treatment is to eliminate the residual internal stress generated during hot rolling, providing a uniform microstructure for the subsequent cold rolling deformation process and reducing the deformation resistance of the alloy during cold rolling. The selection of the annealing temperature and holding time in this step is based on eliminating residual stress and controlling grain size; therefore, a holding time of 1200-1250℃ for 5-10 minutes is chosen to both eliminate some residual internal stress and control grain size. The purpose of the deformation treatment in step 2 is to introduce deformation distortion energy, providing the driving force for recrystallization induced by the subsequent solution treatment. This step should ensure the introduction of uniform and sufficient deformation distortion energy while suppressing the temperature rise of the alloy caused by deformation. Therefore, cold rolling with a total deformation of 60-80% is selected, with a reduction rate of 20-25% per pass. Controlling the reduction rate per pass can suppress deformation temperature rise and ensure uniform deformation, while controlling the total deformation ensures the introduction of sufficient deformation distortion energy. The main purpose of step 3, solution treatment, is to induce recrystallization. This process should prevent abnormal grain growth while ensuring sufficient recrystallization, and at the same time, the migration rate of grain boundaries should be slowed down as much as possible. Therefore, holding at 1140-1160℃ for 2-4 hours is selected, which ensures sufficient recrystallization and controls abnormal grain growth. Based on this preparation process, the oxidation resistance and acid and alkali corrosion resistance of the alloy in the service environment are improved by further increasing the Cr content, while the content of the solid solution strengthening element Mo is increased to further improve the performance of the alloy.

[0031] This invention utilizes a heat treatment process of annealing, cold rolling, and solution treatment to control the alloy grain size and eliminate internal stress, thereby enabling the alloy to serve for extended periods in harsh environments. Besides improving the manufacturing process, the purpose and composition range of controlling the main elements in the aforementioned high-temperature deformation mixture are based on the following reasons: Cr, W, and Mo are all important solid solution strengthening elements in nickel-based superalloys. Cr enters the matrix, causing lattice distortion and reducing stacking fault energy, thus improving the alloy's high-temperature creep resistance. Furthermore, Cr is a good antioxidant; in hot corrosive environments, Cr can promote the formation of a dense Cr2O3 oxide film on the alloy surface, reducing the maximum corrosion depth. Therefore, the Cr content was increased to 29.5%.

[0032] Mo can increase Mo effectively inhibits dislocation movement and improves the creep properties of the alloy by reducing mismatch. At the same time, Mo can also reduce the notch sensitivity of the alloy. However, excessive addition of Mo can lead to the precipitation of the harmful TCP phase, which also has an adverse effect on the hot corrosion resistance and oxidation resistance of the alloy. Therefore, the Mo content should be controlled at 3-5%.

[0033] The inclusion of titanium dioxide (W) into the γ-matrix can increase strength. Furthermore, W can improve the creep properties of the alloy. W has a similar effect to Mo; to control the W+Mo content at 15-17%, W is controlled at 10-12%.

[0034] The following will describe in detail the high-temperature corrosion-resistant high-temperature alloy and its preparation method of the present invention through several specific embodiments.

[0035] Comparative example Alloy composition: C 0.04%, Cr 24%, W 14%, Mo 0.8%, Al 0.3%, Ti 0.5%, Fe 4%, Si 0.8%, Ni balance.

[0036] Step 1, Annealing treatment: Hold the hot-rolled sheet at 1150℃ for 5 minutes, then cool it to room temperature with water; Step 2, Deformation treatment: The solution-treated sheet is cold-rolled with a total deformation of 60%, lubricated with emulsion, and the reduction rate per pass is 18%; Step 3, solution treatment: The cold-rolled sheet is solution treated at 1150℃ for 2 hours, then cooled to room temperature with water, and the solution-treated sheet is pickled and dried. The microstructure of the alloy obtained in this embodiment is as follows: Figure 1 As shown, the oxidation rate at 900℃ is 0.0741 g / (m²). 2 ·h); The yield strength at room temperature is 329MPa, the tensile strength is 880MPa, and the elongation is 60%; the yield strength at 900℃ is 123MPa, the tensile strength is 237MPa, and the elongation is 50%.

[0037] Example 1 Alloy composition: C 0.04%, Cr 28.5%, W 10%, Mo 3.0%, Al 1.0%, Ti 0.5%, Fe 1%, Si 0.8%, Ni balance.

[0038] Step 1, Annealing treatment: Hold the hot-rolled sheet at 1200℃ for 5 minutes, then cool it to room temperature with water; Step 2, Deformation treatment: The solution-treated sheet is cold-rolled with a total deformation of 60%, lubricated with emulsion, and the reduction rate is 20% per pass; Step 3, solution treatment: The cold-rolled sheet is solution treated at 1140℃ for 2 hours, then cooled to room temperature with water, and the solution-treated sheet is pickled and dried.

[0039] The microstructure of the alloy obtained in this embodiment is as follows: Figure 2 As shown, the oxidation rate at 900℃ is 0.0632 g / (m²).2 ·h); The room temperature yield strength is 342MPa, the tensile strength is 896MPa, and the elongation is 60%; the 900℃ yield strength is 131MPa, the tensile strength is 248MPa, and the elongation is 47%.

[0040] Example 2 Alloy composition: C 0.08%, Cr 29.5%, W 12%, Mo 5.0%, Al 1.5%, Ti 0.8%, Fe 1%, Si 0.8%, Ni balance.

[0041] Step 1, Annealing treatment: Hold the hot-rolled sheet at 1250℃ for 30 minutes, then cool it to room temperature with water; Step 2, Deformation treatment: The solution-treated sheet is cold-rolled with a total deformation of 80%, lubricated with emulsion, and the reduction rate is 25% per pass; Step 3, solution treatment: The cold-rolled sheet is solution treated at 1160℃ for 4 hours, then cooled to room temperature with water, and the solution-treated sheet is pickled and dried.

[0042] The microstructure of the alloy obtained in this embodiment is as follows: Figure 3 As shown, the oxidation rate at 900℃ is 0.0590 g / (m²). 2 ·h); The yield strength at room temperature is 359MPa, the tensile strength is 912MPa, and the elongation is 54%; the yield strength at 900℃ is 145MPa, the tensile strength is 256MPa, and the elongation is 45%.

[0043] Example 3 Alloy composition: C 0.06%, Cr 29.0%, W 11%, Mo 4%, Al 1.2%, Ti 0.6%, Fe 1%, Si 0.8%, Ni balance.

[0044] Step 1, Annealing treatment: Hold the hot-rolled sheet at 1200℃ for 30 minutes, then cool it to room temperature with water; Step 2, Deformation treatment: The solution-treated sheet is cold-rolled with a total deformation of 70%, lubricated with emulsion, and the reduction rate per pass is 23%; Step 3, Solution treatment: The cold-rolled sheet is solution treated at 1150℃ for 4 hours, then cooled to room temperature with water, and the solution-treated sheet is pickled and dried.

[0045] The microstructure of the alloy obtained in this embodiment is as follows: Figure 4 As shown, the oxidation rate at 900℃ is 0.0588 g / (m²). 2·h); The yield strength at room temperature is 347MPa, the tensile strength is 902MPa, and the elongation is 50%; the yield strength at 900℃ is 141MPa, the tensile strength is 248MPa, and the elongation is 40%.

[0046] Example 4 Alloy composition: C 0.08%, Cr 28.5%, W 10%, Mo 3%, Al 1.5%, Ti 0.5%, Fe 1%, Si 0.8%, Ni balance.

[0047] Step 1, Annealing treatment: Hold the hot-rolled sheet at 1200℃ for 10 minutes, then cool it to room temperature with water; Step 2, Deformation treatment: The solution-treated sheet is cold-rolled with a total deformation of 70%, lubricated with emulsion, and the reduction rate is 25% per pass; Step 3, solution treatment: The cold-rolled sheet is solution treated at 1160℃ for 2 hours, then cooled to room temperature with water, and the solution-treated sheet is pickled and dried.

[0048] The microstructure of the alloy obtained in this embodiment is as follows: Figure 5 As shown, the oxidation rate at 900℃ is 0.0586 g / (m²). 2 ·h); The yield strength at room temperature is 415MPa, the tensile strength is 1056MPa, and the elongation is 58%; the yield strength at 900℃ is 159MPa, the tensile strength is 298MPa, and the elongation is 46%.

[0049] Example 5 Alloy composition: C 0.08%, Cr 29.5%, W 12%, Mo 4%, Al 1.5%, Ti 0.5%, Fe 1%, Si 0.8%, Ni balance.

[0050] Step 1, Annealing treatment: Hold the hot-rolled sheet at 1200℃ for 30 minutes, then cool it to room temperature with water; Step 2, Deformation treatment: The solution-treated sheet is cold-rolled with a total deformation of 80%, lubricated with emulsion, and the reduction rate is 20% per pass; Step 3, solution treatment: The cold-rolled sheet is solution treated at 1140℃ for 4 hours, then cooled to room temperature with water, and the solution-treated sheet is pickled and dried.

[0051] The microstructure of the alloy obtained in this embodiment is as follows: Figure 6 As shown, the oxidation rate at 900℃ is 0.0573 g / (m2·h); the yield strength at room temperature is 435 MPa, the tensile strength is 1085 MPa, and the elongation is 60%; the yield strength at 900℃ is 166 MPa, the tensile strength is 304 MPa, and the elongation is 50%.

[0052] The properties of the high-temperature corrosion-resistant superalloys prepared in each embodiment are shown in Table 1 below: Table 1 Properties of High-Temperature Corrosion-Resistant High-Temperature Alloys

[0053] It is understood that the above embodiments are merely exemplary implementations used to illustrate the principles of the present invention, and the present invention is not limited thereto. For those skilled in the art, various modifications and improvements can be made without departing from the spirit and essence of the present invention, and these modifications and improvements are also considered to be within the scope of protection of the present invention.

Claims

1. A high-temperature corrosion-resistant high-temperature alloy, characterized in that, The composition of the high-temperature alloy by weight percentage includes C 0.04~0.08%, Cr 28.5~29.5%, W 10.0~12.0%, Mo 3.0~5.0%, Al 1.0~1.5%, Ti 0.5~0.8%, Fe≤1%, Si 0.8%, and Ni as the balance.

2. The high-temperature corrosion-resistant high-temperature alloy according to claim 1, characterized in that, The Cr content in the deformed superalloy is 29-29.5% by weight.

3. The high-temperature corrosion-resistant high-temperature alloy according to claim 1, characterized in that, The total weight percentage of W and Mo in the deformed superalloy is 15-17%.

4. A high-temperature corrosion-resistant high-temperature alloy according to any one of claims 1 to 3, characterized in that, The Al+Ti content of the deformed superalloy is 1.3~2% by weight.

5. A method for preparing a high-temperature corrosion-resistant superalloy, characterized in that, The high-temperature alloy is the high-temperature alloy according to any one of claims 1 to 4, and the method includes the following steps: Step 1, Annealing: Hold the hot-rolled ingot at 1200-1250℃ for 5-30 minutes, then cool it to room temperature with water; Step 2, Deformation treatment: The annealed sheet is subjected to cold deformation with a total deformation of 60-80%, using multiple passes of pressing, with each pass having a pressing rate of 20-25%, and lubricated with emulsion. Step 3, solution treatment: keep the cold-rolled sheet at 1140-1160℃ for 2-4 hours, air cool to room temperature, and then dry by pickling.

6. The method for preparing a high-temperature corrosion-resistant superalloy according to claim 5, characterized in that, The microstructure of the prepared high-temperature corrosion-resistant superalloy is single-phase austenite and a small amount of MC and M23C6 type carbides, with an average grain size of no more than 100 μm.

7. The method for preparing a high-temperature corrosion-resistant high-temperature alloy according to claim 5, characterized in that, The oxidation rate of the prepared high-temperature corrosion-resistant superalloy at 900℃ is 0.0573 g / (m). 2 The oxidation rate at 1000℃ is 0.113 g / (m·h). 2 ·h).

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