A method for recovering tissue damage of nickel-based high-temperature alloy

Abstract

The present application discloses a method for restoring tissue damage in a nickel-based superalloy, belonging to the technical field of restoring the mechanical properties of metal materials. The method comprises: placing a tissue-damaged nickel-based superalloy connected to an electrode in a resistance furnace, and subjecting the tissue-damaged nickel-based superalloy to pulse current treatment when the temperature rises to a first temperature range, i.e., subjecting the tissue-damaged nickel-based superalloy to pulse current coordinated regulation treatment to obtain a nickel-based superalloy subjected to pulse current coordinated regulation treatment, selecting nickel-based superalloy samples that meet the requirements of the coordinated treatment, and subjecting the nickel-based superalloy samples that meet the requirements of the coordinated treatment to double aging treatment to obtain a nickel-based superalloy sample after restoration treatment. In this way, the microstructure and mechanical properties of the tissue-damaged nickel-based superalloy are largely restored.

Description

Technical Field

[0001] The present application relates to the technical field of mechanical property restoration of metal materials, and in particular to a method for restoring tissue damage in nickel-based high-temperature alloys. Background Art

[0002] Nickel-based IN718 high-temperature alloy is one of the most widely used core materials for aircraft engine turbine disks. It is widely used due to its excellent ordered precipitation strengthening effect and structural stability under service conditions of 600℃ to 700℃. However, under the coupling of long-term centrifugal stress (200MPa to 300MPa) and local thermal shock (peak temperature 730℃), it is prone to irreversible microstructural degradation. The phase is prone to coarsening and volume fraction decrease, while δ- Phase precipitates and grows near the grain boundary to form Phase precipitation zone weakens the strengthening effect, which leads to a significant decrease in the yield strength, creep performance and fracture toughness of the material.

[0003] Currently, the main method for repairing damaged nickel-based superalloys relies on traditional solution treatment followed by aging heat treatment. Solution treatment involves high-temperature heating to dissolve the precipitated phase back into the matrix, followed by aging to re-precipitate the strengthening phase. However, this method has inherent limitations. While high-temperature, long-term solution treatment achieves complete dissolution of the precipitated phase, it also results in extensive grain growth, which prevents the material from fully restoring its mechanical properties.

[0004] As in the related art, by increasing the solution temperature (relatively The performance of the deformed nickel-iron-chromium-based high-temperature alloy is restored by increasing the phase solution temperature by 100℃ to 200℃. Although the holding time is shortened to 0.5h to 2h, there is a risk of overburning that induces the formation of local liquid phase, and the grain growth rate is increased (the grain size can reach 120μm), which has a great impact on the recovery of the mechanical properties of the material. Summary of the Invention

[0005] This application aims to solve at least one of the technical problems existing in the related art.

[0006] Therefore, an embodiment of the present application provides a method for recovering damaged nickel-based high-temperature alloy tissue.

[0007] An embodiment of the present application provides a method for restoring tissue damage in a nickel-based high-temperature alloy, comprising: performing pulse current coordinated regulation treatment on a nickel-based high-temperature alloy in a tissue-damaged state to obtain a nickel-based high-temperature alloy sample that meets the requirements of the coordinated treatment; performing double aging treatment on the nickel-based high-temperature alloy sample that meets the requirements of the coordinated treatment to obtain a nickel-based high-temperature alloy sample after restoration treatment; wherein the step of performing pulse current coordinated regulation treatment on the nickel-based high-temperature alloy in a tissue-damaged state to obtain a nickel-based high-temperature alloy sample that meets the requirements of the coordinated treatment comprises: using a pure copper clamping device to connect the two ends of the nickel-based high-temperature alloy in a tissue-damaged state to the electrodes of a pulse current generator, and welding a thermocouple to the surface of the nickel-based high-temperature alloy in a tissue-damaged state, and performing real-time temperature measurement on the nickel-based high-temperature alloy in a tissue-damaged state; placing the nickel-based high-temperature alloy in a tissue-damaged state connected to the electrodes in a resistance furnace set to a first temperature range, the first temperature range being 650°C to 850°C; performing pulse current coordinated treatment when the temperature of the nickel-based high-temperature alloy in a tissue-damaged state rises to the first temperature range to obtain a nickel-based high-temperature alloy sample that meets the requirements of the coordinated treatment; and selecting the nickel-based high-temperature alloy sample that meets the requirements of the coordinated treatment.

[0008] Exemplarily, when the temperature of the nickel-based high-temperature alloy in the tissue damage state rises to the first temperature range, pulse current synergistic treatment is performed to obtain the nickel-based high-temperature alloy sample synergistically treated by pulse current, specifically including: when the nickel-based high-temperature alloy in the tissue damage state rises to the first temperature range, pulse current treatment is started; when the nickel-based high-temperature alloy in the tissue damage state reaches the second temperature range, timing is started, and the second temperature range is 980°C to 1050°C; when the timing reaches a first preset time, the pulse current treatment is stopped to obtain the nickel-based high-temperature alloy sample synergistically treated by pulse current, wherein the first preset time is 1min to 10min, and the parameters of the pulse current treatment include: frequency of 20Hz to 50Hz, current density of 330 to , pulse width is 15μs to 30μs.

[0009] Exemplarily, before the step of performing pulse current synergistic control treatment on the nickel-based high-temperature alloy in a tissue-damaged state to obtain a synergistically treated nickel-based high-temperature alloy sample that meets the requirements, the method further includes: performing temperature / stress coupled aging treatment on the nickel-based IN718 alloy raw material to obtain the nickel-based high-temperature alloy in a tissue-damaged state; or, obtaining the nickel-based high-temperature alloy in a tissue-damaged state.

[0010] Exemplarily, the step of subjecting a nickel-based IN718 alloy raw material to a temperature / stress coupled aging treatment to obtain a nickel-based high-temperature alloy in a microstructure damage state includes: using a temperature / stress coupling device to apply 300 MPa axial tensile stress in a third temperature range environment, performing a temperature / stress coupled aging treatment for 1000 hours, and obtaining a nickel-based high-temperature alloy in a microstructure damage state, wherein the third temperature range is 725°C to 735°C.

[0011] Exemplarily, the temperature / stress coupling device includes a resistance furnace and an electronic universal testing machine. The test force measurement accuracy of the electronic universal testing machine is ±0.5% of the indicated value, and the heating system of the resistance furnace adopts a five-stage temperature control method.

[0012] Exemplarily, the steps of performing double aging treatment on the co-treated nickel-based high-temperature alloy sample that meets the requirements to obtain the restored nickel-based high-temperature alloy sample include: placing the co-treated nickel-based high-temperature alloy sample that meets the requirements in a 720°C environment and keeping it for 8 hours, cooling it to 620°C at a rate of 50°C / h, keeping it in a 620°C environment for 8 hours and air-cooling it to room temperature to obtain the restored nickel-based high-temperature alloy sample.

[0013] Exemplarily, after performing a double aging treatment on the co-treated nickel-based high-temperature alloy sample that meets the requirements to obtain the restored nickel-based high-temperature alloy sample, the method further includes: performing a tensile test on the restored nickel-based high-temperature alloy sample and the nickel-based high-temperature alloy in a damaged state.

[0014] The present invention provides a method for recovering tissue damage in nickel-based high-temperature alloys. Phase coarsening and δ phase growth near the grain boundary to form Phase precipitation zone, which leads to a serious decline in the mechanical properties of the material, innovatively proposed a short-time pulse current solution-double aging treatment process. The damaged alloy sample was placed in a pulse current / thermal field environment, and the synergistic effect of the coupling field was used to achieve rapid dissolution of the precipitated phase and purification of the grain boundary. After the optimized parameter pulse current treatment, the double aging heat treatment process was used to promote the precipitation of nano-sized dispersed The strengthening phase has a volume fraction of 25% to 30%, and the nano-sized dispersed phase maintains an ideal coherent interface with the matrix. This method breaks through the limitations of single thermal field control in traditional solution heat treatment and solves the critical temperature / time dissolution threshold of the δ phase in the damaged area of ​​nickel-based IN718 alloy for turbine disks in the existing solution process through the electric field-thermal field coupling effect. There are strong correlation constraints on the stability of the matrix grains, which can repair the damaged structure of IN718 alloy and restore the mechanical properties to the greatest extent, providing an innovative solution for the repair and life extension of high-temperature alloy components.

[0015] The above description is only an overview of the technical solution of the present application. In order to more clearly understand the technical means of the present application, it can be implemented in accordance with the contents of the specification. In order to make the above and other purposes, features and advantages of the present application more obvious and easy to understand, the specific implementation methods of the present application are listed below. BRIEF DESCRIPTION OF THE DRAWINGS

[0016] Various other advantages and benefits will become apparent to those skilled in the art upon reading the detailed description of the preferred embodiment below. The accompanying drawings are for illustration purposes only and are not to be considered as limiting the present application. Throughout the drawings, the same reference numerals are used to denote the same components.

[0017] Figure 1 One of the flow diagrams of the method for recovering nickel-based high-temperature alloy tissue damage provided by an embodiment of the present application is shown;

[0018] Figure 2 The second flow chart of the method for recovering nickel-based high-temperature alloy tissue damage provided by an embodiment of the present application is shown;

[0019] Figure 3 The electron backscatter diffraction (EBSD) IPF diagram of the reference sample of the nickel-based high-temperature alloy in the damaged state provided in Example 2 of the present application is shown;

[0020] Figure 4 An electron backscatter diffraction (EBSD) IPF image of a target sample of a nickel-based high-temperature alloy treated by pulse current according to Example 2 of the present application is shown;

[0021] Figure 5 Shows a scanned image of a nickel-based high-temperature alloy in a damaged state provided in Example 2 of the present application;

[0022] Figure 6 A scanned image of a target sample of a nickel-based high-temperature alloy treated by pulse current provided in Example 2 of the present application is shown;

[0023] Figure 7 The engineering stress-strain curves of the nickel-based superalloy after recovery and the nickel-based superalloy in a damaged state obtained in Examples 1 to 4 of the present application are shown;

[0024] Figure 8 The bar graphs show the yield strength, tensile strength and elongation of the nickel-based superalloys after recovery and the nickel-based superalloys in a damaged state obtained in Examples 1 to 4 of the present application. DETAILED DESCRIPTION

[0025] In order to more clearly understand the above-mentioned objects, features and advantages of the present application, the present application is further described in detail below in conjunction with the accompanying drawings and specific embodiments. It should be noted that the embodiments of the present application and the features therein can be combined with each other in the absence of conflict.

[0026] In the following description, many specific details are set forth to facilitate a full understanding of the present application. However, the present application may also be implemented in other ways different from those described herein. Therefore, the scope of protection of the present application is not limited to the specific embodiments disclosed below.

[0027] At present, there is a strong correlation constraint between the critical temperature-time dissolution threshold of the δ phase in the damaged area of ​​nickel-based IN718 superalloy for turbine disks and the grain size stability. For example, the δ phase dissolution temperature window in nickel-based IN718 superalloy is narrow, and conventional heat treatment is difficult to balance the δ phase dissolution and matrix grain size stability, which can easily lead to grain coarsening or local δ phase residue. Therefore, how to improve the δ phase dissolution efficiency and make the nano-sized grain size stable under the premise of high matrix grain size stability? Phase re-precipitation is the technical bottleneck for repairing service tissue damage in nickel-based IN718 high-temperature alloy.

[0028] In view of this, if Figure 1 As shown, an embodiment of the present application provides a method for recovering tissue damage of a nickel-based high-temperature alloy, comprising:

[0029] Step S110: performing pulse current coordinated control processing on the nickel-based high-temperature alloy in the tissue-damaged state to obtain a nickel-based high-temperature alloy sample that meets the coordinated processing requirements.

[0030] Among them, by subjecting the nickel-based high-temperature alloy in the tissue-damaged state to pulse current coordinated control treatment, utilizing the coupling effect of pulse current / thermal field to short-time solution treatment on the nickel-based high-temperature alloy in the tissue-damaged state, and by reasonably adjusting the parameters of the pulse current and thermal field, a nickel-based high-temperature alloy sample that meets the requirements of coordinated treatment is obtained, so that the matrix grain size of the nickel-based high-temperature alloy sample that meets the requirements of coordinated treatment has high stability, such as the grain size variation range of the matrix is ​​small or there is no obvious change, and the δ phase is dissolved back into the matrix. As a result, in the process of the δ phase dissolving back into the matrix, the grain size of the matrix has high stability, reducing the possibility of grain coarsening or local δ phase residue, so that under the premise of small changes in the matrix grain size and high stability, the δ phase is ensured to have a high dissolution efficiency. It can be understood that in the process of the δ phase dissolving back into the matrix, The phase also dissolves back into the matrix, that is, there is no δ phase in the matrix of the co-treated nickel-based high-temperature alloy. Mutually.

[0031] Among them, step S110 specifically includes the following methods and steps.

[0032] Step S111: connecting the two ends of the nickel-based superalloy in the tissue-damaged state to the electrodes of the pulse current generator using a pure copper clamping device, and welding a thermocouple to the surface of the nickel-based superalloy in the tissue-damaged state to perform real-time temperature measurement of the nickel-based superalloy in the tissue-damaged state;

[0033] Step S112: placing the nickel-based high-temperature alloy in a tissue-damaged state connected to the electrode in a resistance furnace set at a first temperature range of 650° C. to 850° C.;

[0034] Step S113: When the temperature of the nickel-based high-temperature alloy in the tissue-damaged state rises to a first temperature range, pulse current coordinated treatment is performed to obtain a nickel-based high-temperature alloy sample that has been subjected to pulse current coordinated treatment;

[0035] Step S114: Selecting a nickel-based high-temperature alloy sample that meets the requirements for collaborative processing.

[0036] In this embodiment, a pulse current generator applies pulse current treatment to a nickel-based superalloy in a damaged state, while a resistance furnace provides thermal field heating. A pure copper plate is used to secure the damaged nickel-based superalloy to the electrodes of the pulse current generator. The resistance furnace provides temperature compensation, and a temperature detection device (such as a thermocouple) measures the temperature of the damaged nickel-based superalloy in real time, ensuring that the pulse current treatment is performed within a first temperature range. This allows the nickel-based superalloy in a damaged state to be treated using the coupled effects of pulse current and thermal field, resulting in a nickel-based superalloy sample treated with pulse current. The microstructure of the nickel-based superalloy sample treated with pulse current is then observed, and a nickel-based superalloy sample meeting the requirements is selected. Thus, utilizing the pulse current / thermal field coupling effect of the pulse current generator and resistance furnace, a short-term solution treatment is performed on the damaged nickel-based superalloy. This allows the δ phase to dissolve back into the matrix, maintaining a high degree of matrix grain size stability and reducing the likelihood of grain coarsening or localized δ phase retention. This method is simple, time- and energy-efficient. Compared with traditional heat treatment technology, the heat treatment of nickel-based high-temperature alloys in a damaged state can be completed at a lower temperature and in a shorter time, solving the problem of strong correlation constraints between the critical dissolution threshold of the δ phase in the damaged zone of nickel-based IN718 high-temperature alloy used for turbine disks and grain stability.

[0037] Step S120: performing double aging treatment on the co-treated nickel-based high-temperature alloy sample that meets the requirements to obtain a restored nickel-based high-temperature alloy sample.

[0038] Since the grain size of the nickel-based high-temperature alloy matrix that meets the requirements of the co-processing has a high stability and the δ phase is dissolved back into the matrix, the matrix is ​​precipitated again by performing double aging treatment on the nickel-based high-temperature alloy that meets the requirements of the co-processing. Related In other words, the grain size of the matrix in the nickel-based superalloy after the restoration treatment has a high stability, which can be regarded as no change or a small change in the grain size, and the δ phase is solid-dissolved in the matrix and precipitates nano-sized Related Phase, thereby making the alloy material structure and alloy material performance of the nickel-based high-temperature alloy after the restoration treatment better than the alloy material structure and alloy material performance level of the nickel-based high-temperature alloy in the damaged state, and solving the problem in the related technology that the high-temperature and long-time solid solution scheme can achieve complete dissolution of the precipitated phase, but at the same time is accompanied by a large range of grain growth and cannot restore the mechanical properties of the material to a large extent.

[0039] That is to say, the nickel-based high-temperature alloy tissue damage recovery method provided in the embodiment of the present application is to obtain a nickel-based high-temperature alloy sample that meets the requirements of the coordinated treatment by performing pulse current coordinated control treatment on the nickel-based high-temperature alloy in the tissue damage state, so that the δ phase is dissolved back into the matrix in a short time, and the grain size of the matrix has high stability, a small range of variation or no obvious change, reducing the possibility of grain coarsening or local δ phase residue; by performing double aging treatment on the nickel-based high-temperature alloy sample that meets the requirements of the coordinated treatment, the matrix is ​​precipitated again. Related Phase, to obtain the nickel-based high-temperature alloy sample after recovery treatment. Therefore, through the method provided by this application, under the premise of small change in matrix grain size and high stability, the δ phase is ensured to have a high re-dissolution efficiency, and the nano-sized Related The process allows damaged nickel-based superalloy specimens to recover their mechanical properties. This means the recovered nickel-based superalloy specimens have excellent metallic material properties, such as high yield strength, tensile strength, and elongation, thereby extending the service life of superalloy components. Furthermore, the process is simple, saving time and energy.

[0040] The high-quality commercial nickel-based IN718 superalloy hot-rolled plates used in this study were subjected to standard heat treatment. The volume fraction of the phase does not exceed 1.9%, so it is ignored in the study. Phase changes.

[0041] Furthermore, this application is directed to the nickel-based IN718 alloy in a damaged state. Phase coarsening and δ phase growth near the grain boundary to form Phase precipitation zone, which leads to a serious decline in the mechanical properties of the material, innovatively proposed a pulse current solution-double aging treatment process. The damaged alloy is placed in a pulse current / thermal field environment, and through the synergistic effect of the coupling field, the precipitation phase is quickly dissolved and the grain boundary is purified. After the optimized parameter pulse current treatment, the double aging heat treatment process is used to promote the precipitation of nano-sized dispersed The strengthening phase has a volume fraction of 25% to 30%, and the nano-sized dispersed phase maintains an ideal coherent interface with the matrix. This method breaks through the limitations of single thermal field control in traditional solution heat treatment and solves the critical temperature / time dissolution threshold of the δ phase in the damaged area of ​​nickel-based IN718 alloy for turbine disks in the existing solution process through the electric field-thermal field coupling effect. There are strong correlation constraints on the stability of the matrix grains, which can repair the damaged structure of IN718 alloy and restore the mechanical properties to the greatest extent, providing an innovative solution for the repair and life extension of high-temperature alloy components.

[0042] In some possible embodiments provided in this application, the alloy material structure includes phase and δ phase, that is, the nickel-based high-temperature alloy obtained by the method of the present application after recovery treatment has The size, content and distribution of the phase and δ phase are better than those of the nickel-based high-temperature alloy in the damaged state. Specifically, the dissolution rate of the δ phase in the nickel-based high-temperature alloy after the restoration treatment is high, and it can be regarded as no δ phase residue. Phase size is smaller than that of the damaged nickel-based superalloy Phase size, achieving nanometer size Phase precipitation, and Phase content increased.

[0043] In some possible embodiments provided herein, alloy material properties include yield strength, tensile strength, and elongation. In other words, the nickel-based superalloy recovered by the disclosed method exhibits yield strength, tensile strength, and elongation superior to those of a damaged nickel-based superalloy, thereby restoring mechanical properties and extending the life of components in high-temperature service.

[0044] In some possible implementation embodiments provided in this application, before step S110, the method further includes:

[0045] A nickel-based IN718 alloy raw material is subjected to temperature / stress coupled aging treatment to obtain a nickel-based high-temperature alloy in a damaged microstructure state; or a nickel-based high-temperature alloy in a damaged microstructure state is obtained.

[0046] In some examples of this embodiment, the nickel-based superalloy in a tissue-damaged state that undergoes pulse current coordinated regulation treatment can be obtained by subjecting nickel-based IN718 alloy raw materials to temperature / stress coupled aging treatment. For example, during the test process, the nickel-based IN718 alloy raw materials can be subjected to a near-service temperature / stress coupled aging treatment to approximately simulate the service process to obtain a nickel-based superalloy in a tissue-damaged state that is close to service. The nickel-based superalloy tissue damage recovery method provided in the embodiments of this application can be used to verify the recovery of the mechanical properties of the nickel-based superalloy in a tissue-damaged state that is close to service. Alternatively, the nickel-based superalloy in a tissue-damaged state that undergoes pulse current coordinated regulation treatment in the embodiments of this application can be a directly obtained nickel-based superalloy in a tissue-damaged state, such as a nickel-based IN718 superalloy with tissue damage used in an aircraft engine turbine disk. That is, using the method provided in the embodiments of this application, the obtained nickel-based IN718 superalloy with tissue damage used in an aircraft engine turbine disk can be directly subjected to subsequent operations such as pulse current coordinated regulation treatment to achieve the recovery of the mechanical properties of the nickel-based IN718 superalloy with tissue damage used in an aircraft engine turbine disk.

[0047] Furthermore, by subjecting the nickel-based IN718 alloy raw materials to temperature / stress coupling aging treatment, a nickel-based high-temperature alloy in a damaged tissue state is obtained. The raw material is a high-quality commercial nickel-based IN718 high-temperature alloy hot-rolled plate, which is one of the core materials widely used in aircraft engine turbine discs. Specifically, the alloy is subjected to vacuum self-consumption and vacuum induction melting, homogenization treatment, hot forging, rolling into plates, and then standard heat treatment. Specifically, the chemical composition of the raw materials, in terms of mass percentage, includes: Fe 18.32%, Cr 19.42%, Mo 2.98%, Nb 4.89%, Ti 1.01%, Al 0.51%, Mn 0.03%, C 0.031%, B 0.02%, P 0.01%, and the rest is Ni. By subjecting the above raw materials to near-service temperature / stress coupling aging treatment, the nickel-based IN718 high-temperature alloy is subjected to a long-term heat exposure treatment simulating approximate service conditions, and a high-density δ phase is obtained at the grain boundary, Nickel-based high-temperature alloy with damaged structure and phase coarsening and significant degradation of mechanical properties.

[0048] It is understandable that in the process of temperature / stress coupled aging treatment of raw materials to obtain nickel-based high-temperature alloys in a damaged state, the grain size of the matrix does not change, or the grain size of the matrix changes very little and can be regarded as unchanged, but long needle / short rod-shaped δ phase precipitates in the matrix and forms a non-destructive stress. Phase precipitation band, coarsening phase, which affects the material properties of nickel-based high-temperature alloys.

[0049] Furthermore, in order to ensure that the size and state of the nickel-based high-temperature alloy in a damaged state obtained by subjecting the nickel-based IN718 alloy raw material to temperature / stress coupled aging treatment can meet the use requirements of various testing equipment and improve the test accuracy, the nickel-based high-temperature alloy in a damaged state obtained by subjecting the nickel-based IN718 alloy raw material to temperature / stress coupled aging treatment can be processed into a plate-shaped tensile specimen as the object of pulse current coordinated control treatment.

[0050] Specifically, after the step of subjecting the nickel-based IN718 alloy raw material to temperature / stress coupled aging treatment to obtain a nickel-based high-temperature alloy in a damaged state, electric spark wire cutting can be used to process the nickel-based high-temperature alloy in a damaged state into a plate-shaped tensile specimen for subsequent operations. Specifically, after the nickel-based high-temperature alloy in a damaged state is processed into a plate-shaped tensile specimen by electric spark wire cutting, the plate-shaped tensile specimen can be polished, such as by sandpapering the surface of the plate-shaped tensile specimen in stages to eliminate the surface oxide layer and machining marks to obtain a smooth surface. The plate-shaped specimen is then subjected to pulse current coordinated control processing. This operation is conducive to ensuring that the smooth surface of the plate-shaped tensile specimen can be in good contact with the pulse current generator electrode described later.

[0051] In some possible embodiments provided herein, the steps of subjecting a nickel-based IN718 alloy raw material to a temperature / stress coupled aging treatment to obtain a nickel-based high-temperature alloy in a damaged microstructure state include:

[0052] Using a temperature / stress coupling device, 300 MPa axial tensile stress is applied in a third temperature range environment, and a temperature / stress coupling aging treatment is performed for 1000 hours to obtain a nickel-based high-temperature alloy in a tissue damage state. The third temperature range is 725°C to 735°C.

[0053] In this embodiment, a temperature / stress coupling device was used to apply 300 MPa axial tensile stress in an environment of 725°C to 735°C, and the raw material was subjected to a temperature / stress coupling aging treatment for 1000 hours to simulate the service conditions of the nickel-based IN718 alloy. As a result, a high-density δ phase at the grain boundary was obtained. Nickel-based IN718 superalloy in a damaged state with phase coarsening and significant degradation of mechanical properties.

[0054] In the above embodiment, the temperature / stress coupling device includes a resistance furnace and an electronic universal testing machine. The test force measurement accuracy of the electronic universal testing machine is ±0.5% of the indicated value, and the heating system of the box-type resistance furnace adopts a five-stage temperature control method.

[0055] The electronic universal testing machine's test force measurement accuracy (relative error of indication) is ±0.5% of the indicated value. The resistance furnace's heating system utilizes a five-stage temperature control system, ensuring a soaking zone exceeding 300 mm and a temperature deviation of no more than 3°C within the 600°C to 800°C range. This improves the accuracy of simulated service conditions.

[0056] In some possible implementation embodiments provided in this application, step S113 includes the following methods and steps:

[0057] S1131: When the plate-shaped tensile specimen reaches the first temperature range, pulse current treatment begins;

[0058] S1132: When the plate tensile specimen reaches a second temperature range, start timing, where the second temperature range is 980° C. to 1050° C.;

[0059] S1133: When the timing reaches the first preset time, the pulse current treatment is stopped to obtain a nickel-based high-temperature alloy sample that has been co-treated with the pulse current. The first preset time is 1 minute to 10 minutes, and the parameters of the pulse current treatment include: a frequency of 20 Hz to 50 Hz, a current density of to , pulse width is 15μs to 30μs.

[0060] In this embodiment, when the plate-like tensile specimen rises to a first temperature range, which is equivalent to the furnace temperature, with a small temperature difference and a stable temperature, pulse current treatment is started. When the plate-like tensile specimen reaches a second temperature range, such as 980°C to 1050°C, timing is started. When the timing reaches a first preset time, the pulse current treatment is stopped to obtain a nickel-based high-temperature alloy specimen that is co-treated with pulse current. The first preset time is 1 min to 10 min. Thus, the coupling effect of pulse current / thermal field is utilized to perform short-time solid solution treatment on the plate-like tensile specimen. This method has a simple process and saves time and energy.

[0061] The first temperature range can be 650°C, 700°C, 800°C, 850°C, or any other value; the second temperature range can be 980°C, 1000°C, 1020°C, 1050°C, or any other value; the first preset time can be 1 minute, 2 minutes, 3 minutes, 5 minutes, 10 minutes, or any other time. The frequency of the pulse current treatment is 20Hz, 25Hz, 30Hz, 35Hz, 40Hz, 45Hz, 50Hz; the current density is 330 , 530 , 630 , 830 , or any other value; the pulse width is 15μs, 20μs, 25μs, 30μs.

[0062] Therefore, compared to traditional heat treatment techniques, the embodiments of the present application can complete the heat treatment of nickel-based superalloys in a tissue-damaged state at a lower temperature and in a shorter time, resulting in a simple process and saving time and energy. It is understood that the second temperature range can be any other range, as long as it is less than the temperature range of traditional heat treatment techniques in related arts, and the first preset duration can be any other range, as long as it is less than the time range of traditional heat treatment techniques in related arts.

[0063] like Figure 2 As shown, in some possible embodiments provided in this application, the microstructure of nickel-based superalloy samples treated with pulse current can be observed to select nickel-based superalloy samples that meet the requirements of the treatment. Specifically, the following methods and steps may be included:

[0064] Target sample selection based on nickel-based high-temperature alloy samples processed by pulse current synergy.

[0065] Among them, the center position of the nickel-based high-temperature alloy sample co-treated with pulse current was selected as the target sample.

[0066] The target sample is subjected to mechanical grinding and polishing followed by vibration polishing.

[0067] Among them, the step of performing vibration polishing treatment on the target sample after mechanical grinding and polishing specifically includes: performing step-by-step sandpaper grinding treatment, mechanical polishing treatment, and vibration polishing on the target sample in sequence; wherein, the sandpaper used for step-by-step sandpaper grinding is 400 mesh sandpaper, 800 mesh sandpaper, 1200 mesh sandpaper, 1500 mesh sandpaper, and 2000 mesh sandpaper, respectively, and the vibration polishing time is 8 hours.

[0068] That is to say, the target sample is ground step by step with 400 mesh sandpaper, 800 mesh sandpaper, 1200 mesh sandpaper, 1500 mesh sandpaper, and 2000 mesh sandpaper in sequence, and then mechanically polished with a polishing machine. Polishing is stopped when there is no scratch on the surface of the sample. The target sample after mechanical polishing is vibrated polished for 8 hours to ensure that the fine scratches and deformation layer remaining after mechanical polishing of the target sample are removed to facilitate the statistics of the grain size of the target sample.

[0069] The grain size of the target sample after vibration polishing is counted. Based on the grain size of the target sample meeting the first preset requirement, the The solution corrodes the target sample.

[0070] Specifically, 5g, 25ml, is 25ml.

[0071] Among them, the grain size of the target sample after grinding and polishing can be statistically analyzed by scanning electron microscopy using EBSD (Electron Back Scatter Diffraction, EBSD, backscattered electron diffraction) technology. When the grain size of the target sample meets the first preset requirement, it means that the grain size of the target sample has high stability. For example, the difference between the grain size of the target sample and the grain size of the reference sample of the nickel-based high-temperature alloy in the damaged state is within the preset range, almost equal, or the difference range is small. Then, use The solution etches the target sample whose grain size meets the first preset requirement.

[0072] Observe the matrix of the target sample The distribution information of phase and δ phase is based on the target sample The distribution information of the phase and the δ phase meets the second preset requirement, and the co-processed nickel-based high-temperature alloy sample that meets the requirement is selected.

[0073] Among them, the matrix of the target sample can be observed by scanning electron microscope. phase, δ phase distribution information, when the target sample The distribution information of phase and δ phase meets the second preset requirement, indicating that the precipitated The phase and the δ phase have dissolved back into the matrix, that is, the δ phase has a good dissolution rate. Therefore, a nickel-based high-temperature alloy sample that meets the requirements of the co-treatment is selected to determine that a nickel-based high-temperature alloy that meets the requirements of the co-treatment is obtained.

[0074] In some possible embodiments provided in this application, the method for restoring nickel-based high-temperature alloy tissue damage further includes:

[0075] Select reference samples based on the nickel-based high-temperature alloy with damaged structure;

[0076] The reference specimens were subjected to mechanical grinding and polishing followed by vibration polishing;

[0077] Counting the grain size of the reference sample after the vibration polishing process, based on the difference between the grain size of the target sample and the grain size of the reference sample being within a preset range, the grain size of the target sample meets the first preset requirement;

[0078] Observe the matrix of the reference sample The distribution information of phase and δ phase is based on the target sample Phase and δ phase of the target sample are dissolved back into the matrix compared with the reference sample. The distribution information of the phase and the δ phase meets the second preset requirement.

[0079] In this embodiment, a reference sample is selected based on a nickel-based high-temperature alloy in a state of tissue damage, wherein the reference sample can be any position of the nickel-based high-temperature alloy in a state of tissue damage. The reference sample is subjected to mechanical grinding and polishing and then subjected to vibration polishing to ensure that the fine scratches and deformation layer remaining after the mechanical polishing of the target sample are removed to facilitate the statistical calculation of the grain size of the target sample. Then, the grain size of the reference sample after the vibration polishing is calculated. Based on the difference in the grain size of the target sample and the reference sample being within a preset range, it is indicated that the grain size of the target sample has high stability. The difference between the two is small and can be considered to be almost unchanged, indicating that the grain size of the target sample meets the first preset requirement. It is understandable that the reference sample can be ground and polished by the step of grinding and polishing the target sample, and the grain size of the reference sample after the grinding and polishing can be calculated using the same method as the target sample after the grinding and polishing to improve the comparison accuracy between the reference sample and the target sample. It can be understood that, for target samples whose grain size does not meet the first preset requirement, they can be regarded as invalid target samples and there is no need to perform the subsequent method steps. Only target samples whose grain size meets the first preset requirement can be regarded as valid target samples and perform the subsequent method steps.

[0080] Due to the precipitation of high-density δ phase and coarsening in the nickel-based high-temperature alloy in the damaged state Therefore, the matrix of the reference sample also precipitates high-density δ phase and coarse Phase. By observing the matrix of the reference sample The distribution information of phase and δ phase is obtained, and the matrix of the target sample is observed. The distribution information of phase, δ phase and the matrix of reference sample The distribution information of the phase and δ phase is compared. Phase and δ phase are dissolved back into the matrix compared with the reference sample, that is, there is no Phase and δ phase precipitation, The phase and δ phase have dissolved back into the matrix, indicating that the target sample The distribution information of the phase and the δ phase meets the second preset requirement.

[0081] In some possible embodiments provided in this application, the steps of performing a double aging treatment on a co-treated nickel-based superalloy sample that meets the requirements to obtain a recovered nickel-based superalloy sample include:

[0082] The nickel-based high-temperature alloy sample that meets the requirements of the synergistic treatment is placed in a 720°C environment and kept for 8 hours, then cooled to 620°C at a rate of 50°C / h, kept in a 620°C environment for 8 hours and air-cooled to room temperature to obtain a nickel-based high-temperature alloy sample after recovery treatment.

[0083] In this embodiment, the grain size of the nickel-based high-temperature alloy that meets the requirements of the co-processing is not significantly changed compared with the nickel-based high-temperature alloy in the damaged state, and the δ phase, Phase dissolves back into the matrix. Therefore, the double aging treatment is performed on the base high temperature alloy that meets the requirements of the synergistic treatment (such as the target sample that meets the requirements of the synergistic treatment) through the above process parameters to make the nano-sized The phase precipitates again so that the nickel-based high-temperature alloy in the damaged state can recover its mechanical properties, thereby obtaining a nickel-based high-temperature alloy sample after recovery treatment, that is, the nickel-based high-temperature alloy sample after recovery treatment has good metal material properties.

[0084] In some possible embodiments provided in the present application, after performing a double aging treatment on a nickel-based superalloy sample that meets the requirements of the co-processing to obtain a recovered nickel-based superalloy sample, the method further includes:

[0085] Tensile tests were performed on nickel-based superalloy specimens after recovery treatment and nickel-based superalloy specimens in a damaged state.

[0086] In this embodiment, by performing tensile tests on the nickel-based high-temperature alloy specimen after recovery treatment and the nickel-based high-temperature alloy in a tissue-damaged state, a comparison of the alloy material properties of the two can be obtained, so that users can intuitively and accurately understand the mechanical property recovery of the nickel-based high-temperature alloy after recovery treatment compared to the nickel-based high-temperature alloy in a tissue-damaged state.

[0087] Specifically, an electronic universal testing machine can be used to perform tensile testing according to GB / T 228.1-2021 standard, and the strain rate is set to , tensile tests were carried out on the nickel-based high-temperature alloy after recovery treatment and the nickel-based high-temperature alloy in the damaged state.

[0088] Example 1

[0089] 10mm thick, high-quality commercial nickel-based IN718 alloy hot-rolled plates were used as raw materials. These plates were placed in a temperature / stress coupled aging device to obtain a damaged nickel-based superalloy. This damaged nickel-based superalloy was then processed into plate-shaped tensile specimens using wire-cut electrospark cutting. The damaged nickel-based superalloy was then treated using pulsed current to restore its mechanical properties. The following steps were followed:

[0090] (1) Take the parallel length cross-sectional area as 6mm 2 A nickel-based high-temperature alloy with a total length of 37 mm in a damaged state was used as a plate tensile specimen. The surface of the plate tensile specimen was polished with sandpaper step by step to eliminate the surface oxide layer and machining marks and obtain a smooth surface to ensure good contact with the pulse electrode.

[0091] (2) Determine the parameters of pulse current treatment, perform pulse current solution treatment on the plate tensile specimen, and select the target specimen. The second temperature range is 1050℃, the first preset time is 2min, and the pulse current density is 650 , the frequency of the pulse current is 40Hz, and the pulse width of the pulse current is 30μs.

[0092] (3) Grain size statistics. This includes statistically analyzing the grain size of the target sample and the grain size of the reference sample to determine whether the grain size of the target sample meets the first preset requirement. It is understood that before performing grain size statistics, the target sample and the reference sample may be ground and polished.

[0093] (4) Observation Phase, δ phase distribution. Including the target sample with grain size that meets the first preset requirement The distribution of phase and δ phase was observed, and the reference sample Observe the distribution of phase and δ phase to determine the target sample The distribution information of phase and δ phase meets the second preset requirement, and the nickel-based high-temperature alloy treated by pulse current is obtained. It can be understood that when the target sample with grain size meeting the first preset requirement is Before observing the distribution of phase and δ phase, it is necessary to use The solution etches the target sample whose grain size meets the first preset requirement.

[0094] (5) Double aging treatment. Specifically, the nickel-based high-temperature alloy treated with pulse current is subjected to double aging treatment to obtain a nickel-based high-temperature alloy after recovery treatment.

[0095] (6) Tensile property testing: Specifically, tensile property testing is performed on the target sample of the nickel-based superalloy after recovery treatment and the reference sample of the nickel-based superalloy in the damaged state.

[0096] Table 1 Comparison of tensile properties of Example 1

[0097]

[0098] in, Figure 7 The engineering stress-strain curves of the nickel-based superalloy after recovery and the nickel-based superalloy in a damaged state obtained in Examples 1 to 4 of the present application are shown. Figure 8 The following bar graphs show the yield strength, tensile strength, and elongation of the recovered nickel-based superalloys and the damaged nickel-based superalloys obtained in Examples 1 to 4 of the present application. Table 1 is a comparative table of the tensile properties of the recovered nickel-based superalloys and the damaged nickel-based superalloys obtained in Example 1.

[0099] As shown in Table 1, the average yield strength and tensile strength of the nickel-based superalloy in the damaged state are 885 MPa and 1245 MPa, respectively, and the average elongation is 17.2%. The average yield strength and tensile strength of the nickel-based superalloy after recovery obtained in Example 1 are 1134 MPa and 1312 MPa, respectively, and the average elongation is 22.1%. This shows that the average yield strength and tensile strength of the nickel-based superalloy after recovery obtained in Example 1 increased by 28.14% and 5.38%, respectively, compared to the nickel-based superalloy in the damaged state, and the average elongation increased by 28.5%.

[0100] Example 2

[0101] 10mm thick, high-quality commercial nickel-based IN718 alloy hot-rolled plates were used as raw materials. These plates were placed in a temperature / stress coupled aging device to obtain a damaged nickel-based superalloy. This damaged nickel-based superalloy was then processed into plate-shaped tensile specimens using wire-cut electrospark cutting. The damaged nickel-based superalloy was then treated using pulsed current to restore its mechanical properties. The following steps were followed:

[0102] (1) Take the parallel length cross-sectional area as 6mm 2 A nickel-based high-temperature alloy with a total length of 37 mm in a damaged state was used as a plate tensile specimen. The surface of the plate tensile specimen was polished with sandpaper step by step to eliminate the surface oxide layer and machining marks and obtain a smooth surface to ensure good contact with the pulse electrode.

[0103] (2) Determine the parameters of pulse current treatment, perform pulse current solution treatment on the plate tensile specimen, and select the target specimen. The second temperature range is 1020℃, the first preset time is 5min, and the density of pulse current is 650 , the frequency of the pulse current is 40Hz, and the pulse width of the pulse current is 30μs.

[0104] (3) Grain size statistics. This includes statistically analyzing the grain size of the target sample and the grain size of the reference sample to determine whether the grain size of the target sample meets the first preset requirement. It is understood that before performing grain size statistics, the target sample and the reference sample may be ground and polished.

[0105] in, Figure 3 The electron backscatter diffraction (EBSD) IPF map of the reference sample of the nickel-based superalloy with damaged structure is shown. Figure 3 The average grain size of the grain size statistics of the reference sample shown is 85.35 μm. Figure 4The electron backscatter diffraction (EBSD) IPF diagram of the target sample of the nickel-based high-temperature alloy treated by the pulse current of Example 2 is shown, that is, the electron backscatter diffraction (EBSD) IPF diagram of the target sample shown in this step. Specifically, Figure 4 The average grain size of the target sample is 87.68 μm. The difference between the two is within the preset range, indicating that the grain size of the target sample has high stability. The difference between the two is small and can be regarded as almost unchanged, indicating that the grain size of the target sample meets the first preset requirement.

[0106] (4) Observation Phase, δ phase distribution. Including the target sample with grain size that meets the first preset requirement The distribution of phase and δ phase was observed, and the reference sample Observe the distribution of phase and δ phase to determine the target sample The distribution information of phase and δ phase meets the second preset requirement, and the nickel-based high-temperature alloy treated by pulse current is obtained. It can be understood that when the target sample with grain size meeting the first preset requirement is Before observing the distribution of phase and δ phase, it is necessary to use The solution etches the target sample whose grain size meets the first preset requirement.

[0107] in, Figure 5 A scanned image of a reference specimen of a nickel-based superalloy in a service-damaged state is shown. Figure 5 The reference sample can clearly see the precipitation phase, delta phase; Figure 6 A scanned image of a target sample of a nickel-based high-temperature alloy treated by pulse current in Example 2 is shown. Figure 6 The target sample can clearly see that there is no Phase, δ phase, thus, it is explained The δ phase and δ phase have dissolved back into the matrix of the target sample, indicating that the target sample The distribution information of the phase and the δ phase meets the second preset requirement.

[0108] (5) Double aging treatment. Specifically, the nickel-based high-temperature alloy treated with pulse current is subjected to double aging treatment to obtain a nickel-based high-temperature alloy after recovery treatment.

[0109] (6) Tensile property testing: Specifically, tensile property testing is performed on target specimens of nickel-based superalloys after recovery treatment and reference specimens of nickel-based superalloys in a damaged state.

[0110] in, Figure 7The engineering stress-strain curves of the nickel-based superalloy after recovery and the nickel-based superalloy in a damaged state obtained in Examples 1 to 4 of the present application are shown. Figure 8 The following bar graphs show the yield strength, tensile strength, and elongation of the recovered nickel-based superalloys and the microstructure-damaged nickel-based superalloys obtained in Examples 1 to 4 of the present application. Table 2 is a comparative table of the tensile properties of the recovered nickel-based superalloys and the microstructure-damaged nickel-based superalloys obtained in Example 2.

[0111] Table 2 Comparison of tensile properties of Example 2

[0112]

[0113] As shown in Table 2, the average yield strength and tensile strength of the nickel-based superalloy in the damaged state are 885 MPa and 1245 MPa, respectively, and the average elongation is 17.2%. The average yield strength and tensile strength of the nickel-based superalloy after recovery obtained in Example 2 are 1153 MPa and 1345 MPa, respectively, and the average elongation is 24.3%. This shows that the average yield strength and tensile strength of the nickel-based superalloy after recovery obtained in Example 2 increased by 30.3% and 8.03% respectively, and the average elongation increased by 41.28% compared to the nickel-based superalloy in the damaged state.

[0114] Example 3

[0115] 10mm thick, high-quality commercial nickel-based IN718 alloy hot-rolled plates were used as raw materials. These plates were placed in a temperature / stress coupled aging device to obtain a damaged nickel-based superalloy. This damaged nickel-based superalloy was then processed into plate-shaped tensile specimens using wire-cut electrospark cutting. The damaged nickel-based superalloy was then treated using pulsed current to restore its mechanical properties. The following steps were followed:

[0116] (1) Take the cross-sectional area as 6mm 2 A nickel-based high-temperature alloy with a length of 37 mm in a damaged state was used as a plate tensile specimen. The surface of the plate tensile specimen was polished with sandpaper step by step to eliminate the surface oxide layer and machining marks and obtain a smooth surface to ensure good contact with the pulse electrode.

[0117] (2) Determine the parameters of pulse current treatment, perform pulse current solution treatment on the plate tensile specimen, and select the target specimen. The second temperature range is 1000℃, the first preset time is 5min, and the pulse current density is 650 , the frequency of the pulse current is 40Hz, and the pulse width of the pulse current is 15μs.

[0118] (3) Grain size statistics. This includes statistically analyzing the grain size of the target sample and the grain size of the reference sample to determine whether the grain size of the target sample meets the first preset requirement. It is understood that before performing grain size statistics, the target sample and the reference sample may be ground and polished.

[0119] (4) Observation Phase, δ phase distribution. Including the target sample with grain size that meets the first preset requirement The distribution of phase and δ phase was observed, and the reference sample Observe the distribution of phase and δ phase to determine the target sample The distribution information of phase and δ phase meets the second preset requirement, and the nickel-based high-temperature alloy treated by pulse current is obtained. It can be understood that when the target sample with grain size meeting the first preset requirement is Before observing the distribution of phase and δ phase, it is necessary to use The solution etches the target sample whose grain size meets the first preset requirement.

[0120] (5) Double aging treatment. Specifically, the nickel-based high-temperature alloy treated with pulse current is subjected to double aging treatment to obtain a nickel-based high-temperature alloy after recovery treatment.

[0121] (6) Tensile property testing: Specifically, tensile property testing is performed on the target sample of the nickel-based superalloy after recovery treatment and the reference sample of the nickel-based superalloy in the damaged state.

[0122] in, Figure 7 The engineering stress-strain curves of the nickel-based superalloy after recovery and the nickel-based superalloy in a damaged state obtained in Examples 1 to 4 of the present application are shown. Figure 8 The following bar graphs show the yield strength, tensile strength, and elongation of the recovered nickel-based superalloys and the microstructure-damaged nickel-based superalloys obtained in Examples 1 to 4 of the present application. Table 3 compares the tensile properties of the recovered nickel-based superalloys and the microstructure-damaged nickel-based superalloys obtained in Example 3.

[0123] As shown in Table 3, the average yield strength and tensile strength of the nickel-based superalloy in the damaged state are 885 MPa and 1245 MPa, respectively, and the average elongation is 17.2%. The average yield strength and tensile strength of the nickel-based superalloy after recovery obtained in Example 3 are 1142 MPa and 1302 MPa, respectively, and the average elongation is 22.5%. This shows that the average yield strength and tensile strength of the nickel-based superalloy after recovery obtained in Example 3 increased by 29.04% and 4.58%, respectively, compared to the nickel-based superalloy in the damaged state, and the average elongation increased by 23.56%.

[0124] Table 3 Comparison of tensile properties of Example 3

[0125]

[0126] Example 4

[0127] 10mm thick, high-quality commercial nickel-based IN718 alloy hot-rolled plates were used as raw materials. These plates were placed in a temperature / stress coupled aging device to obtain a damaged nickel-based superalloy. This damaged nickel-based superalloy was then processed into plate-shaped tensile specimens using wire-cut electrospark cutting. The damaged nickel-based superalloy was then treated using pulsed current to restore its mechanical properties. The following steps were followed:

[0128] (1) Take the cross-sectional area as 6mm 2 A nickel-based high-temperature alloy with a length of 37 mm in a damaged state was used as a plate tensile specimen. The surface of the plate tensile specimen was polished with sandpaper step by step to eliminate the surface oxide layer and machining marks and obtain a smooth surface to ensure good contact with the pulse electrode.

[0129] (2) Determine the parameters of pulse current treatment, perform pulse current solution treatment on the plate tensile specimen, and select the target specimen. The second temperature range is 980℃, the first preset time is 8min, and the density of pulse current is 500 , the frequency of the pulse current is 30Hz, and the pulse width of the pulse current is 30μs.

[0130] (3) Grain size statistics. This includes statistically analyzing the grain size of the target sample and the grain size of the reference sample to determine whether the grain size of the target sample meets the first preset requirement. It is understood that before performing grain size statistics, the target sample and the reference sample may be ground and polished.

[0131] (4) Observation Phase, δ phase distribution. Including the target sample with grain size that meets the first preset requirement The distribution of phase and δ phase was observed, and the reference sample Observe the distribution of phase and δ phase to determine the target sample The distribution information of phase and δ phase meets the second preset requirement, and the nickel-based high-temperature alloy treated by pulse current is obtained. It can be understood that when the target sample with grain size meeting the first preset requirement is Before observing the distribution of phase and δ phase, it is necessary to use The target sample whose grain size meets the first preset requirement is corroded by the lower solution.

[0132] (5) Double aging treatment. Specifically, the nickel-based high-temperature alloy treated with pulse current is subjected to double aging treatment to obtain a nickel-based high-temperature alloy after recovery treatment.

[0133] (6) Tensile property testing: Specifically, tensile property testing is performed on the target sample of the nickel-based superalloy after recovery treatment and the reference sample of the nickel-based superalloy in the damaged state.

[0134] in, Figure 7 The engineering stress-strain curves of the nickel-based superalloy after recovery and the nickel-based superalloy in a damaged state obtained in Examples 1 to 4 of the present application are shown. Figure 8 The following bar graphs show the yield strength, tensile strength, and elongation of the recovered nickel-based superalloys and the microstructure-damaged nickel-based superalloys obtained in Examples 1 to 4 of the present application. Table 4 is a comparative table of the tensile properties of the recovered nickel-based superalloys and the microstructure-damaged nickel-based superalloys obtained in Example 4.

[0135] Table 4 Comparison of tensile properties of Example 4

[0136]

[0137] As shown in Table 4, the average yield strength and tensile strength of the nickel-based superalloy in the damaged state are 885 MPa and 1245 MPa, respectively, and the average elongation is 17.2%. The average yield strength and tensile strength of the nickel-based superalloy after recovery obtained in Example 4 are 1130 MPa and 1312 MPa, respectively, and the average elongation is 22.1%. This shows that the average yield strength and tensile strength of the nickel-based superalloy after recovery obtained in Example 4 increased by 27.68% and 5.38%, respectively, compared to the nickel-based superalloy in the damaged state, and the average elongation increased by 21.51%.

[0138] The above are merely preferred embodiments of the present application and are not intended to limit the present application. Any modifications, equivalent replacements, and improvements made within the spirit and principles of the present application shall be included within the scope of protection of the present application. The above are merely preferred embodiments of the present application. It should be noted that those skilled in the art may make various improvements and variations without departing from the technical principles of the present application, and such improvements and variations shall also be considered within the scope of protection of the present application.

Claims

1. A method for recovering tissue damage of nickel-based high-temperature alloys, characterized in that: include: The nickel-based high-temperature alloy in the damaged state is subjected to pulse current coordinated control treatment to obtain a nickel-based high-temperature alloy sample that meets the requirements of coordinated treatment; Performing double aging treatment on the co-treated nickel-based high-temperature alloy sample that meets the requirements to obtain a restored nickel-based high-temperature alloy sample; The step of performing pulse current coordinated control treatment on the nickel-based high-temperature alloy in a damaged state to obtain a nickel-based high-temperature alloy sample that meets the requirements of coordinated treatment includes: A pure copper clamping device is used to connect the two ends of the nickel-based high-temperature alloy in the tissue-damaged state to the electrodes of a pulse current generator, and a thermocouple is welded to the surface of the nickel-based high-temperature alloy in the tissue-damaged state to perform real-time temperature measurement of the nickel-based high-temperature alloy in the tissue-damaged state; Placing the nickel-based high-temperature alloy in a tissue-damaged state connected to the electrode in a resistance furnace set at a first temperature range of 650° C. to 850° C.; When the temperature of the nickel-based high-temperature alloy in the tissue-damaged state rises to the first temperature range, pulse current collaborative treatment is performed to obtain a nickel-based high-temperature alloy sample that has been collaboratively treated with pulse current; Selecting a nickel-based high-temperature alloy sample of the co-processing that meets the requirements; The step of performing pulse current synergistic treatment when the temperature of the nickel-based high-temperature alloy in the tissue-damaged state rises to the first temperature range to obtain a nickel-based high-temperature alloy sample synergistically treated with pulse current specifically includes: When the nickel-based high-temperature alloy in the tissue-damaged state rises to the first temperature range, starting the pulse current treatment; When the nickel-based high-temperature alloy in the damaged state reaches a second temperature range, the timing starts, and the second temperature range is 980° C. to 1050° C.; When the timing reaches the first preset time, the pulse current treatment is stopped to obtain the nickel-based high-temperature alloy sample treated with the pulse current, wherein the first preset time is 1 min to 10 min, and the parameters of the pulse current treatment include: frequency of 20 Hz to 50 Hz, current density of 330 to , pulse width is 15μs to 30μs.

2. The method for recovering nickel-based high-temperature alloy tissue damage according to claim 1, characterized in that: Before the step of performing pulse current coordinated control treatment on the nickel-based high-temperature alloy in a tissue-damaged state to obtain a nickel-based high-temperature alloy sample that meets the requirements of coordinated treatment, the method further includes: The nickel-based IN718 alloy raw material is subjected to temperature / stress coupled aging treatment to obtain the nickel-based high-temperature alloy in the tissue damage state; or, the nickel-based high-temperature alloy in the tissue damage state is obtained.

3. The method for recovering nickel-based high-temperature alloy tissue damage according to claim 2, characterized in that: The step of subjecting the nickel-based IN718 alloy raw material to temperature / stress coupled aging treatment to obtain the nickel-based high-temperature alloy in the damaged state comprises: A temperature / stress coupling device is used to apply 300 MPa axial tensile stress in a third temperature range environment, and a temperature / stress coupling aging treatment is performed for 1000 hours to obtain the nickel-based high-temperature alloy in the tissue damage state. The third temperature range is 725°C to 735°C.

4. The method for recovering nickel-based high-temperature alloy tissue damage according to claim 3, characterized in that: The temperature / stress coupling device includes the resistance furnace and an electronic universal testing machine. The test force measurement accuracy of the electronic universal testing machine is ±0.5% of the indicated value. The heating system of the resistance furnace adopts a five-stage temperature control method.

5. The method for recovering nickel-based high-temperature alloy tissue damage according to claim 1, characterized in that: The step of performing double aging treatment on the co-treated nickel-based high-temperature alloy sample that meets the requirements to obtain a restored nickel-based high-temperature alloy sample comprises: The nickel-based high-temperature alloy sample that meets the requirements of the co-treatment is placed in a 720°C environment and kept warm for 8 hours, then cooled to 620°C at a rate of 50°C / h, kept in a 620°C environment for 8 hours and air-cooled to room temperature to obtain the nickel-based high-temperature alloy sample after the recovery treatment.

6. The method for recovering nickel-based high-temperature alloy tissue damage according to claim 1, characterized in that: After the step of performing double aging treatment on the co-treated nickel-based high-temperature alloy sample that meets the requirements to obtain a restored nickel-based high-temperature alloy sample, the method further includes: A tensile test is performed on the nickel-based high-temperature alloy sample after the recovery treatment and the nickel-based high-temperature alloy in the damaged state.

Images