Preparation method of nickel-based superalloy, component and nickel-based superalloy

Abstract

The application provides a preparation method of a nickel-based high-temperature alloy, which comprises the following steps: obtaining a workpiece, a multistage forging step and a heat treatment step; the components in the workpiece comprise 3-3.2 wt% of Ti, 1.5-1.7 wt% of Al, 19-20 wt% of Cr, 13-14 wt% of Co, 4-4.5 wt% of Mo, 0.05-0.1 wt% of C, 0.04-0.06 wt% of Zr and the balance of Ni and inevitable impurities; in the multistage forging step, the workpiece is forged for at least two stages; the forging temperature of the first stage forging is in the range of 1000-1200 DEG C, and the deformation amount is 35-45%; the forging temperature of the second stage forging is in the range of 1000-1200 DEG C, and the deformation amount is 55-65%. The preparation method of the nickel-based high-temperature alloy, the component and the nickel-based high-temperature alloy provided by the application have small size and uniformly distributed MC type carbide and controlled η phase precipitation, can effectively improve the high-temperature creep performance of the nickel-based high-temperature alloy, and the preparation method is simple and low in cost.

Description

Technical Field

[0001] This invention belongs to the field of high-temperature creep performance improvement technology of nickel-based superalloys, and particularly relates to a method for preparing nickel-based superalloys, components, and nickel-based superalloys for improving high-temperature creep performance. Background Technology

[0002] Waspaloy is a nickel-based superalloy, specifically a Ni-Cr-Co based precipitation-hardening wrought superalloy. It operates at temperatures below 815℃. Through solid solution strengthening by adding cobalt, chromium, and molybdenum, the addition of aluminum and titanium to form γ' precipitation strengthening phases, and the addition of boron and zirconium to purify and strengthen grain boundaries, it exhibits high yield strength and fatigue resistance at 760℃-870℃, and good oxidation and corrosion resistance in gas turbine atmospheres below 870℃. It also possesses good machinability and stable microstructure, making it suitable for manufacturing various high-temperature resistant components. Studies have shown that the precipitation of the η phase in nickel-based superalloys, such as Waspaloy alloys, can severely impair their performance during long-term high-temperature service. Related research has found that small-sized MC-type carbides in the alloy can significantly reduce the precipitation rate of the η phase. However, the MC carbides produced in actual Waspaloy production vary in size, with a large number of large-sized MC carbides. Therefore, controlling the size of the MC carbides is crucial for controlling the η phase and thus improving its high-temperature creep performance. Researchers urgently need to provide practical solutions for controlling the size of the MC carbides. Summary of the Invention

[0003] The purpose of this invention is to overcome the shortcomings of the prior art and provide a method for preparing a nickel-based superalloy, a component, and a nickel-based superalloy, which has small-sized and uniformly distributed MC-type carbides and controlled η-phase precipitation, which can effectively improve the high-temperature creep performance of the nickel-based superalloy. The preparation method is simple and low-cost.

[0004] The technical solution of this invention is as follows: On one hand, a method for preparing a nickel-based superalloy to improve high-temperature creep performance is provided, comprising the following steps:

[0005] Obtain a workpiece whose composition includes: 3-3.2 wt% Ti, 1.5-1.7 wt% Al, 19-20 wt% Cr, 13-14 wt% Co, 4-4.5 wt% Mo, 0.05-0.1 wt% C, 0.04-0.06 wt% Zr and the balance Ni and unavoidable impurities;

[0006] The process involves a multi-stage forging process, in which the workpiece undergoes at least two forging stages, including a first-stage forging stage and a second-stage forging stage. In the first-stage forging stage, the workpiece is forged at a temperature ranging from 1000℃ to 1200℃, and the forging deformation of the workpiece is 35% to 45%. The second-stage forging stage follows the first-stage forging stage, where the workpiece is forged again at a temperature ranging from 1000℃ to 1200℃, and the forging deformation of the workpiece is 55% to 65%.

[0007] The heat treatment step involves heat treating the workpiece obtained after multiple forging steps to obtain a nickel-based high-temperature alloy.

[0008] As a further improvement to this technical solution, the heat treatment step is a multi-stage heat treatment, including at least a first-stage heat treatment, a second-stage heat treatment, and a third-stage heat treatment; the first-stage heat treatment temperature is 1000℃-1100℃, and the heat treatment time is more than 3 hours; the second-stage heat treatment temperature is 800℃-850℃, and the heat treatment time is more than 20 hours; the third-stage heat treatment temperature is 700℃-780℃, and the heat treatment time is more than 15 hours.

[0009] As a further improvement to this technical solution, the multi-stage forging process also includes a solution treatment step between the two forging stages.

[0010] As a further improvement to this technical solution, the solution treatment step includes a first solution treatment step between the first forging step and the second forging step, wherein the workpiece is placed at a constant temperature of 1050℃-1100℃ for 3-5 hours.

[0011] As a further improvement to this technical solution, the workpiece is a Waspaloy nickel-based alloy.

[0012] As a further improvement to this technical solution, the composition of the Waspaloy nickel-based alloy includes 3.1 wt% Ti, 1.6 wt% Al, 19.5 wt% Cr, 13.5 wt% Co, 4.3 wt% Mo, 0.07 wt% C, 0.05 wt% Zr and the balance Ni and unavoidable impurities.

[0013] As a further improvement to this technical solution, the workpiece has MC-type carbides for controlling the precipitation of the η phase, wherein the average size of the MC-type carbides is no greater than 1 micrometer.

[0014] As a further improvement to this technical solution, the workpiece is a nickel-based high-temperature alloy ingot.

[0015] On the other hand, the present invention also provides a component having a nickel-based superalloy, wherein the component is made of a nickel-based superalloy and the nickel-based superalloy is prepared by the preparation method described above.

[0016] On the other hand, the present invention also provides a nickel-based superalloy, which is prepared by the above-described preparation method.

[0017] This invention provides a method for preparing a nickel-based superalloy, a component, and the nickel-based superalloy itself. The method includes obtaining a workpiece, a multi-stage forging process, and a heat treatment process. The workpiece comprises: 3-3.2 wt% Ti, 1.5-1.7 wt% Al, 19-20 wt% Cr, 13-14 wt% Co, 4-4.5 wt% Mo, 0.05-0.1 wt% C, 0.04-0.06 wt% Zr, and the balance Ni, as well as unavoidable impurities. The multi-stage forging process involves forging the workpiece in at least two stages, including a first-stage forging stage and a second-stage forging stage. The forging temperature range for the first-stage forging is 1000℃-1200℃. The forging deformation of the workpiece... The amount is 35%-45%; the second forging step is after the first forging step, the workpiece is forged again at a forging temperature range of 1000℃-1200℃, and the forging deformation of the workpiece is 55%-65%; the heat treatment step is to heat treat the workpiece obtained after the multi-stage forging step to obtain a nickel-based high-temperature alloy; the present invention provides a method for preparing a nickel-based high-temperature alloy, a component and a nickel-based high-temperature alloy. Through the above preparation steps, the nickel-based high-temperature alloy obtained has MC-type carbides for controlling the precipitation of the η phase. The size of the MC carbides is reduced and more uniform, effectively suppressing the precipitation of the harmful η phase, thereby effectively improving the high-temperature creep performance of the nickel-based high-temperature alloy. Moreover, the preparation method is simple and low in cost. Attached Figure Description

[0018] To more clearly illustrate the technical solutions in the embodiments of the present invention, the accompanying drawings used in the embodiments will be briefly introduced below. Obviously, the drawings described below are only some embodiments of the present invention. For those skilled in the art, other drawings can be obtained based on these drawings without creative effort.

[0019] Figure 1a This is a low-magnification microstructure image of the nickel-based superalloy provided in this embodiment of the invention, obtained by scanning electron microscopy (SEM).

[0020] Figure 1b This is a high-magnification microstructure image of the nickel-based superalloy provided in this embodiment of the invention, obtained by scanning electron microscopy (SEM).

[0021] Figure 2aThis is a schematic diagram illustrating the effect of large-size MC on the precipitation rate of the η phase in a nickel-based superalloy as actually observed in an embodiment of the present invention.

[0022] Figure 2b This is a schematic diagram illustrating the effect of small-sized MC on the precipitation rate of the η phase in a nickel-based superalloy as actually observed in an embodiment of the present invention.

[0023] Figure 3a This is a microstructure diagram of a nickel-based superalloy after forging;

[0024] Figure 3b This is a microstructure diagram of a nickel-based superalloy after forging and solution treatment. Detailed Implementation

[0025] To make the objectives, technical solutions, and advantages of this invention clearer, the invention will be further described in detail below with reference to the accompanying drawings and embodiments. It should be understood that the specific embodiments described herein are merely illustrative and not intended to limit the invention.

[0026] It should be noted that the terms "setup" and "connection" should be interpreted broadly. For example, they can refer to direct setup or connection, or indirect setup or connection through centered components or centered structures.

[0027] Furthermore, in embodiments of this invention, terms such as "longitudinal," "lateral," "length," "width," "thickness," "upper," "lower," "front," "rear," "left," "right," "vertical," "horizontal," "top," "bottom," "inner," and "outer" are used to indicate orientation or positional relationships based on the orientation or positional relationships shown in the accompanying drawings, or in a conventional placement or usage state. These terms are merely for the convenience of describing the invention and simplifying the description, and do not indicate or imply that the structures, features, devices, or elements referred to must have a specific orientation or positional relationship, nor that they must be constructed and operated in a specific orientation. Therefore, they should not be construed as limitations on the invention. In the description of this invention, unless otherwise stated, "a plurality of" means two or more.

[0028] The various specific technical features and embodiments described in the detailed embodiments can be combined in any suitable manner without contradiction. For example, different implementation methods can be formed by combining different specific technical features / embodiments. In order to avoid unnecessary repetition, the various possible combinations of the various specific technical features / embodiments in this invention will not be described separately.

[0029] This invention provides a method for preparing a nickel-based superalloy, comprising a workpiece acquisition step, a multi-stage forging step, and a heat treatment step. In the workpiece acquisition step, the workpiece composition includes: 3-3.2 wt% Ti, 1.5-1.7 wt% Al, 19-20 wt% Cr, 13-14 wt% Co, 4-4.5 wt% Mo, 0.05-0.1 wt% C, 0.04-0.06 wt% Zr, and the balance Ni, as well as unavoidable impurities. In another embodiment, the workpiece can be a nickel-based superalloy ingot. The multi-stage forging step involves forging the workpiece in at least two stages, specifically including a first-stage forging step and a second-stage forging step. In the first forging step, the workpiece is forged at a temperature ranging from 1000℃ to 1200℃, and the forging deformation is 35%-45%. In this embodiment, the forging temperature is 1100℃, and the forging deformation is 40%. The second forging step follows the first forging step, where the workpiece is forged again at a temperature ranging from 1000℃ to 1200℃, and the forging deformation is 55%-65%. In this embodiment, the forging temperature is 1100℃, and the forging deformation is 60%. The heat treatment step involves heat-treating the workpiece obtained after the multi-stage forging steps to obtain a nickel-based superalloy. This invention provides a method for preparing a nickel-based superalloy and the nickel-based superalloy itself. Through the above preparation steps, the obtained nickel-based superalloy has small-sized MC-type carbides. Figure 1a and Figure 1b The microstructure of the nickel-based superalloy was determined using a scanning electron microscope (SEM). Figure 1a The image is at low magnification, showing small MC-type carbides that are uniformly distributed. Figure 1b The high-magnification image shows that the average size of the MC-type carbides is less than 1 micrometer. The distribution of MC carbides is more uniform. Small and uniformly distributed MC-type carbides can effectively suppress the precipitation of the η-phase. This is because the content of Ti, the η-phase-forming element, is relatively high in large-sized MC-type carbides. Specifically, the η-phase is Ni3Ti, requiring 25 at.% Ti. Small-sized MCs have a lower titanium content and are less likely to transform into the η-phase (Ni3Ti), while large-sized MCs have a higher titanium content and are more likely to transform into the η-phase (Ni3Ti). The actual observation shows the effect of different sizes of MC-type carbides on the η-phase precipitation rate, such as... Figure 2a and Figure 2b As shown, η precipitation can be observed in large-size MC-type carbides after aging for 5000 hours. Figure 2a As shown, the η phase precipitated in small-sized MC-type carbides only appears after aging for 10,000 hours, as... Figure 2bAs shown, the precipitation of the η phase is suppressed by small-sized MC, thereby effectively improving the high-temperature creep performance of nickel-based superalloys. Moreover, the preparation method is simple and low-cost.

[0030] In some embodiments, the heat treatment step is a multi-stage heat treatment, including at least a first-stage heat treatment, a second-stage heat treatment, and a third-stage heat treatment. The first-stage heat treatment temperature is 1000℃-1100℃, and the heat treatment time is more than 3 hours; the second-stage heat treatment temperature is 800℃-850℃, and the heat treatment time is more than 20 hours; the third-stage heat treatment temperature is 700℃-780℃, and the heat treatment time is more than 15 hours. Through multi-stage heat treatment, the MC-type carbides are further refined and more uniformly distributed. More specifically, in this embodiment, the first-stage heat treatment temperature is 1070℃, and the heat treatment time is 4 hours; the second-stage heat treatment temperature is 845℃, and the heat treatment time is 24 hours; the third-stage heat treatment temperature is 760℃, and the heat treatment time is 16 hours, resulting in good refinement of the MC-type carbide grains.

[0031] In some embodiments, the multi-stage forging step further includes a solution treatment between adjacent forging stages; the solution treatment includes a first solution treatment between the first forging stage and the second forging stage, wherein the first forged nickel-based superalloy is placed at a constant temperature of 1050℃-1100℃ for 3-5 hours, and in this embodiment, it is placed at 1070℃ for 4 hours. Figure 3a This is a microstructure diagram of the forged nickel-based superalloy; for the effect of forging and solution treatment on the microstructure, please refer to [link / reference]. Figure 3b It is evident that solution treatment can effectively homogenize the microstructure, laying a solid foundation for the next stage of forging or heat treatment.

[0032] In some embodiments, the initial nickel-based superalloy is a Waspaloy nickel-based alloy. In this embodiment, the Waspaloy nickel-based alloy comprises 3.1 wt% Ti, 1.6 wt% Al, 19.5 wt% Cr, 13.5 wt% Co, 4.3 wt% Mo, 0.07 wt% C, 0.05 wt% Zr, and the balance Ni, along with unavoidable impurities. The final Waspaloy nickel-based alloy obtained through the above preparation steps has MC-type carbides for controlling η-phase precipitation, and the average size of the MC-type carbides is no greater than 1 micrometer. In this embodiment, the MC-type carbides are uniformly distributed within the microstructure, effectively suppressing η-phase precipitation and thus improving high-temperature creep performance. In specific applications, the average size of the MC-type carbides can be... The size is controlled below 1 micrometer, with 70%-80% of MC-type carbides having a size between 0.8 and 1 micrometer, 10%-20% having a size between 0.5 and 0.8 micrometers, and 0%-10% having a size below 0.5 micrometers. This ensures that the overall average size is less than 1 micrometer, effectively controlling the precipitation rate of harmful phases while also considering cost factors. A simple preparation method can effectively suppress harmful phases, which is of great significance for improving high-temperature creep performance and has good practicality. In other embodiments, the composition can be fine-tuned, or the number of forgings, the specific temperature parameters and time parameters of forging and heat treatment can be adjusted to obtain small-sized MC-type carbides.

[0033] In some embodiments, the multi-stage forging process further includes a third-stage forging, which is performed after the second-stage forging. The forging temperature of the third-stage forging is in the range of 1000℃-1200℃, and the forging deformation of the workpiece is 70%-75%. After three forging processes, the grain size of the MC-type carbides can be further refined.

[0034] In some embodiments, the solution treatment further includes a secondary solution treatment step between the second-stage forging and the third-stage forging, wherein the secondary solution treatment step involves placing the second forged nickel-based superalloy at any constant temperature between 1050°C and 1100°C for 3-5 hours.

[0035] This invention also provides a nickel-based superalloy, which is prepared by the above-described method.

[0036] This invention also provides a component made of a nickel-based superalloy, wherein the component is made of a nickel-based superalloy and the nickel-based superalloy is prepared using the aforementioned preparation method. Naturally, components obtained from the above-described nickel-based superalloy, or devices or other applications formed by further processing the above-described nickel-based superalloy, should be included within the scope of protection of this invention.

[0037] This invention provides a method for preparing a nickel-based superalloy, a component, and the nickel-based superalloy. The method includes obtaining a workpiece, a multi-stage forging process, and a heat treatment process. The workpiece comprises: 3-3.2 wt% Ti, 1.5-1.7 wt% Al, 19-20 wt% Cr, 13-14 wt% Co, 4-4.5 wt% Mo, 0.05-0.1 wt% C, 0.04-0.06 wt% Zr, and the balance Ni, as well as unavoidable impurities. The multi-stage forging process involves forging the workpiece in at least two stages, including a first-stage forging stage and a second-stage forging stage. The forging temperature range for the first-stage forging is 1000℃-1200℃. The forging deformation of the workpiece is 35%-45%; the second forging step is performed after the first forging step, where the workpiece is forged again at a temperature range of 1000℃-1200℃, and the forging deformation of the workpiece is 55%-65%; the heat treatment step involves heat treating the workpiece obtained after the multi-stage forging steps to obtain a nickel-based superalloy; the present invention provides a method for preparing a nickel-based superalloy, a component, and a nickel-based superalloy. Through the above preparation steps, the obtained nickel-based superalloy has small-sized and more uniform MC-type carbides, effectively suppressing the precipitation of harmful η-phase, thereby effectively improving the high-temperature creep performance of the nickel-based superalloy. Moreover, the preparation method is simple and low-cost.

[0038] The above description is only a preferred embodiment of the present invention and is not intended to limit the present invention. Any modifications, equivalent substitutions or improvements made within the spirit and principles of the present invention should be included within the protection scope of the present invention.

Claims

1. A method for preparing a nickel-based superalloy, characterized in that, Including the following steps: Obtain a workpiece, the workpiece being a Waspaloy nickel-based alloy, the composition of which includes: 3-3.2 wt% Ti, 1.5-1.7 wt% Al, 19-20 wt% Cr, 13-14 wt% Co, 4-4.5 wt% Mo, 0.05-0.1 wt% C, 0.04-0.06 wt% Zr and the balance Ni and unavoidable impurities; The process involves a multi-stage forging process, in which the workpiece undergoes at least two forging stages, including a first-stage forging stage and a second-stage forging stage. In the first-stage forging stage, the workpiece is forged at a temperature ranging from 1000℃ to 1200℃, and the forging deformation is 35% to 45%. The second-stage forging stage, following the first-stage forging stage, involves further forging of the workpiece at a temperature ranging from 1000℃ to 1200℃, and the forging deformation is 55% to 65%. The multi-stage forging process also includes a solution treatment between two adjacent forging stages; the solution treatment includes a first solution treatment between the first forging stage and the second forging stage, wherein the first forged nickel-based superalloy is placed at a constant temperature of 1050℃-1100℃ for 3-5 hours. The heat treatment step involves heat treating the workpiece obtained after multiple forging steps to obtain a nickel-based superalloy. The nickel-based superalloy has MC-type carbides for controlling the precipitation of the η phase. The proportion of MC-type carbides with a size of 0.8-1 micrometer is 70%-80%, the proportion of MC-type carbides with a size of 0.5-0.8 micrometer is 10%-20%, and the proportion of MC-type carbides with a size below 0.5 micrometer is 0-10%.

2. The preparation method according to claim 1, characterized in that, The heat treatment process is a multi-stage heat treatment, including at least a first-stage heat treatment, a second-stage heat treatment, and a third-stage heat treatment; the first-stage heat treatment temperature is 1000℃-1100℃, and the heat treatment time is more than 3 hours; the second-stage heat treatment temperature is 800℃-850℃, and the heat treatment time is more than 20 hours; the third-stage heat treatment temperature is 700℃-780℃, and the heat treatment time is more than 15 hours.

3. The preparation method according to claim 1, characterized in that, The composition of the Waspaloy nickel-based alloy includes 3.1 wt% Ti, 1.6 wt% Al, 19.5 wt% Cr, 13.5 wt% Co, 4.3 wt% Mo, 0.07 wt% C, 0.05 wt% Zr and the balance Ni and unavoidable impurities.

4. The preparation method according to any one of claims 1 to 3, characterized in that, The average size of the MC-type carbides is no greater than 1 micrometer.

5. The preparation method according to claim 1, characterized in that, The workpiece is a nickel-based high-temperature alloy ingot.

6. A component comprising a nickel-based superalloy, characterized in that, The component is made of a nickel-based high-temperature alloy, and the nickel-based high-temperature alloy is prepared by the preparation method as described in any one of claims 1 to 5.

7. A nickel-based superalloy, characterized in that, The nickel-based superalloy is prepared by any one of the preparation methods according to claims 1 to 4.

Images