Heat treatment method for improving precipitation phases of different Ni-based alloy coatings

Abstract

The invention discloses a heat treatment method for improving precipitation phases of different Ni-based alloy coatings, and belongs to the technical field of high-temperature alloy materials. According to the method, precipitation and solid solution behaviors of a precipitation phase can be effectively regulated and controlled, formation of the brittle precipitation phase in the alloy in a high-temperature thermal exposure environment is remarkably inhibited by regulating the content of the Ru element and controlling the heat treatment temperature and time, the structure evolution process is delayed, and the structure stability and the high-temperature service performance of the alloy are improved; according to the method, multi-stage heating, long-time constant temperature treatment and vacuum tube sealing treatment are combined, the element diffusion behavior is further optimized, and re-solid solution of a precipitated phase is promoted.

Description

Technical Field

[0001] This invention relates to the field of high-temperature alloy materials, and in particular to a heat treatment method for improving the precipitated phases in coatings of different Ni-based alloys. Background Technology

[0002] Ni-based single-crystal superalloys are widely used in critical hot-end components such as high-pressure turbine blades for aero-engines due to their excellent high-temperature strength, creep resistance, and oxidation resistance. However, during long-term service or high-temperature exposure, precipitates composed of high-melting-point elements such as Mo, W, and Re tend to form in the γ matrix. These needle-like or bamboo-leaf-like precipitates are brittle and do not have a coherent relationship with the γ / γ′ matrix, leading to grain boundary weakening, element depletion, and decreased alloy microstructure stability, significantly reducing their creep resistance and high-temperature reliability.

[0003] In the existing service or remanufacturing processes of Ni-based single-crystal superalloys, coating protection and high-temperature heat treatment are commonly used to improve their high-temperature mechanical properties and heat exposure resistance. However, these traditional technical approaches still have the following main drawbacks: 1) Problem of uncontrollable precipitation of precipitates: During long-term diffusion at high temperature, elements rich in Mo, W, Re and other elements in the alloy are prone to forming brittle precipitates (such as σ phase and μ phase) in the γ phase matrix, which significantly reduces the plasticity, creep life and endurance strength of the alloy. 2) Severe and uncontrollable interdiffusion at the interface: After the NiAl coating and the Ni-based single crystal alloy form a diffusion couple, there is severe interdiffusion of elements, which leads to instability of the interface structure, generation of a large number of voids, and even rapid thinning or failure of the coating.

[0004] Based on the above problems, a heat treatment method for improving the precipitated phases in different Ni-based alloy coatings is proposed. Summary of the Invention

[0005] The purpose of this invention is to provide a heat treatment method for improving the precipitated phases in different Ni-based alloy coatings, so as to solve the problems in the background art.

[0006] To achieve the above objectives, the present invention provides a heat treatment method for improving the precipitated phases in coatings of different Ni-based alloys, comprising the following steps: S1. Polishing the Ni-based single-crystal superalloy and depositing a Ni-based coating on the surface of the Ni-based single-crystal superalloy using physical vapor deposition technology, and achieving different Ru addition amounts by adjusting the target material composition. S2. The prepared Ni-based coating-alloy diffusion couple is placed in a quartz glass tube, vacuumed and sealed, and then placed in a vacuum heat treatment furnace for staged isothermal heat treatment. After the treatment, the product is cooled to obtain the target product.

[0007] Preferably, in S1, the amount of Ru added is 0.05~0.5 at.%; the service temperature of the Ni-based single crystal superalloy is 900~1100℃.

[0008] In S1, the target material is composed of Ni. 50 Al 49.95-x Hf 0.05 Ru x The value of x ranges from 0.05 to 0.5. During the deposition process, different target materials are selected to initiate the arc, thereby achieving different Ru addition amounts in the coating.

[0009] Preferably, in S1, the process parameters of the physical vapor deposition technology are: substrate bias voltage -100V, arc current 100A, deposition gas pressure 1Pa, deposition temperature 300℃, duty cycle 70%, deposition time 2h, and deposition thickness 17~20μm.

[0010] Preferably, in step S2, the vacuum degree is 0.05 to 0.1 Pa.

[0011] Preferably, in step S2, the heat treatment process is as follows: 1) Heat to 800-900℃ at a rate of 15-25℃ / min and hold for 30-50 minutes; 2) Increase the temperature to 1000-1100℃ at a rate of 10-15℃ / min and hold for 60-90 minutes; 3) Heat to 1100-1200℃ at a rate of 5-10℃ / min and hold for 100-300 hours.

[0012] Preferably, in step S2, the cooling method is to cool the furnace to room temperature.

[0013] Preferably, the product after S2 treatment is subjected to component analysis, specifically: the product sample after heat treatment is cut, inlaid, ground and polished along the direction perpendicular to the coating surface, and then the tissue evolution characteristics are observed by means of scanning electron microscopy, transmission electron microscopy, energy dispersive spectroscopy and other means.

[0014] Subsequently, result determination and structural analysis were conducted: Based on different heat treatment times and Ru doping amounts, parameters such as coating thickness changes, interdiffusion layer thickness, pore formation, precipitate phase evolution (precipitation, disappearance, or solid solution), and γ / γ′ microstructure changes (rafting → coarsening → spheroidization) were observed to evaluate the role of Ru-containing Ni-based coatings in regulating high-temperature precipitate phase behavior.

[0015] Therefore, the heat treatment method for improving the precipitated phases in different Ni-based alloy coatings of the present invention has the following beneficial effects: (1) In this invention, the amount of Ru added is precisely controlled by “target material composition adjustment”, which utilizes the effect of Ru to inhibit the coarsening of the γ' phase (delaying the growth rate of the precipitate phase) and avoids the cost increase caused by high Ru content, thus taking into account both performance and economy.

[0016] (2) The heat treatment strategy of “three-stage heating + step heat preservation” is adopted. The low-stage heating can preheat the coating and the substrate, and reduce the internal stress caused by the temperature gradient; the medium-stage heating promotes the initial diffusion of elements and provides a uniform environment for the nucleation of precipitate phase; the high-stage heat preservation can precisely control the growth of γ' phase, effectively suppress coarsening, and improve the uniformity of precipitate phase distribution; combined with a high vacuum of 0.05~0.1Pa and furnace cooling, the coating oxidation is avoided, and the interface stress is reduced by slow cooling, thus reducing the risk of “rafting-peeling” of precipitate phase.

[0017] The technical solution of the present invention will be further described in detail below with reference to the accompanying drawings and embodiments. Attached Figure Description

[0018] Figure 1 The images are SEM images of the products of Examples 1-3 and Comparative Example 1 after exposure for 50 hours, where (a) is Comparative Example 1, (b) is Example 1, (c) is Example 2, and (d) is Example 3. Figure 2 The images show the EDS diagrams of the products of Example 1 and Comparative Example 1 of the present invention, where (a) is Comparative Example 1 and (b) is Example 1. Figure 3 The images are SEM images of the products of Examples 4-6 and Comparative Example 2 after exposure for 300 hours, where (a) is Comparative Example 2, (b) is Example 4, (c) is Example 5, and (d) is Example 6. Figure 4 The flowchart is of the method protected by this invention; Figure 5 The figure shows the characterization results of the product in Comparative Example 3 of this invention. Detailed Implementation

[0019] The technical solution of the present invention will be further described below with reference to the accompanying drawings and embodiments.

[0020] To make the objectives, technical solutions, and advantages of the embodiments of the present invention clearer, the technical solutions of the embodiments of the present invention will be clearly and completely described below with reference to the accompanying drawings. Obviously, the described embodiments are some embodiments of the present invention, but not all embodiments.

[0021] This invention provides a heat treatment method for improving the precipitated phases in coatings of different Ni-based alloys, such as... Figure 4 As shown, it includes the following steps: S1. Sample preparation: Ni-based single-crystal superalloys were selected and subjected to dimensional cutting and polishing. Coating Deposition: A Ni-based coating was deposited on the surface of a Ni-based single-crystal superalloy using physical vapor deposition (PVD). The process parameters were: substrate bias voltage -100V, arc current 100A, deposition gas pressure 1Pa, deposition temperature 300℃, duty cycle 70%, deposition time 2 hours, with a desired thickness of 17~20μm. The target material was Ni. 50 Al 49.95-x Hf 0.05 Ru x During the deposition process, different target materials were selected for arc initiation to achieve different Ru addition amounts in the coating, with Ru addition amounts ranging from 0.05 to 0.5 at.%. S2. Heat treatment: The prepared Ni-based coating-alloy diffusion couple is placed in a quartz glass tube and the tube is evacuated to a vacuum degree of 0.05-0.1 Pa. Then the tube is sealed to ensure that the sample is always in a low oxygen and low pressure environment during the subsequent heat treatment process to avoid oxidation and volatilization of elements. The tube was then placed in a vacuum heat treatment furnace for staged isothermal heat treatment. The interdiffusion behavior and microstructure evolution under high-temperature heat exposure were observed. After heat treatment, the tube was cooled to room temperature with the furnace to avoid stress damage or non-uniform microstructure changes caused by rapid cooling. The specific heat treatment process was as follows: 1) Heat to 800-900℃ at a rate of 15-25℃ / min and hold for 30-50 minutes; 2) Increase the temperature to 1000-1100℃ at a rate of 10-15℃ / min and hold for 60-90 minutes; 3) Heat to 1100-1200℃ at a rate of 5-10℃ / min and hold for 100-300 hours.

[0022] Characterization methods: Cross-section preparation and tissue analysis were performed. After heat treatment, the product was cut, inlaid, ground and polished along the direction perpendicular to the coating surface. The tissue evolution characteristics were observed by means of scanning electron microscopy (SEM), transmission electron microscopy (TEM) and energy dispersive spectroscopy (EDS). Results and Microstructure Analysis: Based on different heat treatment times and Ru doping amounts, parameters such as coating thickness variation, interdiffusion layer (IDZ) thickness, pore formation, precipitate evolution (precipitation, disappearance, or solid solution), and γ / γ′ microstructure changes (rafting → coarsening → spheroidization) were observed to evaluate the role of Ru-containing Ni-based coatings in regulating high-temperature precipitate behavior.

[0023] The following is a detailed description with reference to specific embodiments: Example 1 This embodiment uses the above method to perform heat treatment of the Ni-based alloy coating precipitate phase. The specific steps are as follows: S1. Preparation of Ni-based single-crystal high-temperature alloy samples and coating preparation: The second-generation single-crystal Ni-based high-temperature alloy René N5 was selected as the experimental substrate. Its long-term service temperature is 1100℃. It was cut into samples with a size of 10mm×10mm×2mm and mechanically polished for later use. A Ni-based coating was deposited on the surface of a Ni-based single-crystal alloy using physical vapor deposition (PVD). The process parameters were: substrate bias voltage -100V, arc current 100A, deposition gas pressure 1Pa, deposition temperature 300℃, and duty cycle 70%. The target material selected for this process was Ni. 50 Al 49.90 Hf 0.05 Ru 0.05 The amount of Ru added was 0.05 at.%; S2. The prepared Ni-based coating-René N5 alloy diffusion couple was placed in a quartz glass tube, and the tube was evacuated to a vacuum degree of 0.1 Pa. Then the tube was sealed to ensure that the sample was always in a low oxygen and low pressure environment during the subsequent heat treatment process to avoid oxidation and element volatilization. The tube was then placed in a vacuum heat treatment furnace for isothermal heat treatment. First, the temperature was raised to 800°C at a rate of 15°C / min and held for 30 minutes. Then, the temperature is increased to 1000℃ at a rate of 15℃ / min and held for 60 minutes. Finally, the temperature is increased to 1100℃ at a rate of 10℃ / min and held for 50 hours.

[0024] Example 2 This embodiment uses the above method to perform heat treatment of the Ni-based alloy coating precipitate phase. The specific steps are as follows: S1. Preparation of Ni-based single crystal alloy samples and coating preparation: René N5, a second-generation single crystal Ni-based high-temperature alloy, was selected as the experimental substrate. Its long-term service temperature is 1100℃. The sample was cut into 10mm×10mm×2mm samples and mechanically polished for later use. A Ni-based coating was deposited on the surface of a Ni-based single-crystal alloy using physical vapor deposition (PVD). The process parameters were: substrate bias voltage -100V, arc current 100A, deposition gas pressure 1Pa, deposition temperature 300℃, and duty cycle 70%. The target material selected for this process was Ni. 50 Al 49.85 Hf 0.05 Ru 0.1 The amount of Ru added was 0.1 at.%; S2. The prepared Ni-based coating-René N5 alloy diffusion couple was placed in a quartz glass tube, and the tube was evacuated to a vacuum degree of 0.1 Pa. Then the tube was sealed to ensure that the sample was always in a low oxygen and low pressure environment during the subsequent heat treatment process to avoid oxidation and element volatilization. The tube was then placed in a vacuum heat treatment furnace for isothermal heat treatment. First, the temperature was raised to 850°C at a rate of 20°C / min and held for 45 minutes. Then, the temperature was increased to 1050℃ at a rate of 15℃ / min and held for 80 minutes. Finally, the temperature was increased to 1150℃ at a rate of 8℃ / min and held for 50 hours.

[0025] Example 3 This embodiment uses the above method to perform heat treatment of the Ni-based alloy coating precipitate phase. The specific steps are as follows: S1. Preparation of Ni-based single crystal alloy samples and coating preparation: René N5, a second-generation single crystal Ni-based high-temperature alloy, was selected as the experimental substrate. Its long-term service temperature is 1100℃. The sample was cut into 10mm×10mm×2mm samples and mechanically polished for later use. A Ni-based coating was deposited on the surface of a Ni-based single-crystal alloy using physical vapor deposition (PVD). The process parameters were: substrate bias voltage -100V, arc current 100A, deposition gas pressure 1Pa, deposition temperature 300℃, and duty cycle 70%. The target material selected for this process was Ni. 50 Al 49.80 Hf 0.05 Ru 0.15 This achieves a Ru addition amount of 0.15 at.%; S2. The prepared Ni-based coating-René N5 alloy diffusion couple was placed in a quartz glass tube, and the tube was evacuated to a vacuum degree of 0.1 Pa. Then the tube was sealed to ensure that the sample was always in a low oxygen and low pressure environment during the subsequent heat treatment process to avoid oxidation and element volatilization. The tube was then placed in a vacuum heat treatment furnace for isothermal heat treatment. First, the temperature was raised to 900°C at a rate of 25°C / min and held for 60 minutes. Then, the temperature was increased to 1100℃ at a rate of 15℃ / min and held for 90 minutes. Finally, the temperature is increased to 1200℃ at a rate of 5℃ / min and held for 50 hours.

[0026] Comparative Example 1 This comparative example uses the above method to perform heat treatment of the Ni-based alloy coating precipitate phase. The specific steps are as follows: S1. Preparation of Ni-based single-crystal alloy samples and coating preparation: René N5, a second-generation single-crystal Ni-based high-temperature alloy, was selected as the experimental substrate. It was cut into samples with dimensions of 10mm×10mm×2mm and mechanically polished for later use. A Ni-based coating was deposited on the surface of a Ni-based single-crystal alloy using physical vapor deposition (PVD). The process parameters were: substrate bias voltage -100V, arc current 100A, deposition gas pressure 1Pa, deposition temperature 300℃, and duty cycle 70%. The target material selected for this process was Ni. 50 Al 49.95 Hf 0.05 Ru0 enables a Ru addition amount of 0; S2. The prepared Ni-based coating-René N5 alloy diffusion couple was placed in a quartz glass tube, and the tube was evacuated to a vacuum degree of 0.1 Pa. Then the tube was sealed to ensure that the sample was always in a low oxygen and low pressure environment during the subsequent heat treatment process to avoid oxidation and element volatilization. The tube was then placed in a vacuum heat treatment furnace for isothermal heat treatment. First, the temperature was raised to 800°C at a rate of 15°C / min and held for 30 minutes. Then, the temperature is increased to 1000℃ at a rate of 15℃ / min and held for 60 minutes. Finally, the temperature is increased to 1100℃ at a rate of 10℃ / min and held for 50 hours.

[0027] The heat-treated products of Examples 1-3 and Comparative Example 1 were cut, inlaid, ground, and polished along a direction perpendicular to the coating surface. The tissue evolution characteristics were observed using scanning electron microscopy (SEM), transmission electron microscopy (TEM), and energy dispersive spectroscopy (EDS), as follows: The products from Examples 1-3 and Comparative Example 1 were examined by scanning electron microscopy to determine their interface structure. Figure 1 As shown, it can be seen that as the Ru content increases, the coating thickness gradually decreases and the interfacial diffusion depth (IDZ) decreases significantly. In particular, the coating structure remains intact, clear and stable in the sample of Example 3.

[0028] Energy dispersive spectroscopy (EDS) analysis was performed on the precipitation band regions of the products from Example 1 and Comparative Example 1, such as... Figure 2 As shown, the results indicate that the region of Example 1 exhibits obvious elemental segregation, especially enrichment of Co and Cr elements, forming a grayish-white grid-like structure. It is speculated that this is a secondary γ' phase structure or a precipitate aggregation zone formed by the reorganization of matrix alloying elements during high-temperature interdiffusion, suggesting that this region may be a precursor region of precipitate phase or enrichment zone.

[0029] Example 4 The preparation steps in this embodiment are the same as in Example 1, except that the isothermal heat treatment process in step S2 is modified as follows: First, heat the temperature to 800℃ at a rate of 15℃ / min and hold for 30 minutes; Then, the temperature is increased to 1000℃ at a rate of 15℃ / min and held for 60 minutes. Finally, the temperature is increased to 1100℃ at a rate of 10℃ / min and held for 300 hours.

[0030] Example 5: This example follows the same preparation steps as Example 2, except that the isothermal heat treatment process in step S2 is modified as follows: First, heat the temperature to 850℃ at a rate of 20℃ / min and hold for 45 minutes; Then, the temperature was increased to 1050℃ at a rate of 15℃ / min and held for 80 minutes. Finally, the temperature was increased to 1150℃ at a rate of 8℃ / min and held for 300 hours.

[0031] Example 6 The preparation steps in this embodiment are the same as in Example 3, except that the isothermal heat treatment process in step S2 is modified as follows: First, heat the temperature to 900℃ at a rate of 25℃ / min and hold for 60 minutes; Then, the temperature was increased to 1100℃ at a rate of 15℃ / min and held for 90 minutes. Finally, the temperature is increased to 1200℃ at a rate of 5℃ / min and held for 300 hours.

[0032] Comparative Example 2 The preparation steps of this comparative example are the same as those of comparative example 1, except that the isothermal heat treatment process in step S2 is modified as follows: First, heat the temperature to 800℃ at a rate of 15℃ / min and hold for 30 minutes; Then, the temperature is increased to 1000℃ at a rate of 15℃ / min and held for 60 minutes. Finally, the temperature is increased to 1100℃ at a rate of 10℃ / min and held for 300 hours.

[0033] The products from Examples 4-6 and Comparative Example 2 were examined using scanning electron microscopy, such as... Figure 3As shown, in Comparative Example 2, the coating on the Ru-free sample completely disappeared, and the IDZ region structure reverted to the recovery stage. However, with the increase of Ru content in Examples 4-6, the residual coating thickness increased, the IDZ region thickness decreased, and the microstructure gradually reverted from coarsening and spheroidization to a regular γ / γ' mesh structure. In Example 6, the product maintained an intact coating morphology and complete mesh structure even after 300 hours, indicating that Ru has a significant regulatory effect on improving the thermal stability of the interface structure, delaying the precipitation of the precipitate phase, and promoting microstructure recovery.

[0034] Comparative Example 3 This comparative example uses the above method to perform heat treatment of the Ni-based alloy coating precipitate phase. The specific steps are as follows: S1. Preparation of Ni-based single-crystal alloy samples and coating preparation: René N5, a second-generation single-crystal Ni-based high-temperature alloy, was selected as the experimental substrate. It was cut into samples with dimensions of 10mm×10mm×2mm and mechanically polished for later use. A Ni-based coating was deposited on the surface of a Ni-based single-crystal alloy using physical vapor deposition (PVD). The process parameters were: substrate bias voltage -100V, arc current 100A, deposition gas pressure 1Pa, deposition temperature 300℃, and duty cycle 70%. The target material selected for this process was Ni. 50 Al 49.80 Hf 0.05 Ru 0.15 This achieves a Ru addition amount of 0.15 at.%; S2. The prepared Ni-based coating-René N5 alloy diffusion couple was placed in a quartz glass tube, and the tube was evacuated to a vacuum degree of 0.1 Pa. Then the tube was sealed to ensure that the sample was always in a low oxygen and low pressure environment during the subsequent heat treatment process to avoid oxidation and element volatilization. The tube was then placed in a vacuum heat treatment furnace for heat treatment, where it was heated to 1100°C at a rate of 10°C / min and held at that temperature for 50 hours.

[0035] The products in Comparative Example 3 were characterized and detected, such as... Figure 5 The results showed that, compared with the three-stage heating + stepped heat preservation process in Example 1, the coating thickness in Comparative Example 3 was significantly thinner, and the thinning was more severe, indicating that rapid overall heating intensified the interdiffusion of elements. At the same time, more bright white precipitate phases and TCP phases were formed at the interface and on the upper part of the alloy, and the substrate γ / γ′ structure showed obvious rafting and coarsening, decreased structural stability, and no obvious interdiffusion region. This confirms that the three-stage heating in Example 1 has significant advantages in reducing the interdiffusion rate, controlling the precipitation of precipitate phases, and regulating the evolution of the substrate γ / γ′ structure.

[0036] Furthermore, although Comparative Example 3 exhibits unfavorable characteristics such as severe coating thinning and excessive precipitate segregation, compared with the coating in Comparative Example 2 with 0 at.% Ru addition under three-stage heating, the precipitation, γ / γ′ rafting, and coarsening of the precipitate in Comparative Example 3 are still improved, indicating that the addition of Ru can still partially alleviate the microstructure degradation. Therefore, this invention achieves dual optimization of performance and microstructure stability through Ru doping and staged heating.

[0037] Example 7 This embodiment uses the above method to perform heat treatment of the Ni-based alloy coating precipitate phase. The specific steps are as follows: S1. Preparation of Ni-based single crystal alloy samples and coating preparation: René N5, a second-generation single crystal Ni-based high-temperature alloy, was selected as the experimental substrate. Its long-term service temperature is 1100℃. The sample was cut into 10mm×10mm×2mm samples and mechanically polished for later use. A Ni-based coating was deposited on the surface of a Ni-based single-crystal alloy using physical vapor deposition (PVD). The process parameters were: substrate bias voltage -100V, arc current 100A, deposition gas pressure 1Pa, deposition temperature 300℃, and duty cycle 70%. The target material selected for this process was Ni. 50 Al 49.45 Hf 0.05 Ru 0.5 To achieve a Ru addition amount of 0.5 at.%; S2. The prepared Ni-based coating-René N5 alloy diffusion couple was placed in a quartz glass tube, and the tube was evacuated to a vacuum degree of 0.1 Pa. Then the tube was sealed to ensure that the sample was always in a low oxygen and low pressure environment during the subsequent heat treatment process to avoid oxidation and element volatilization. The tube was then placed in a vacuum heat treatment furnace for isothermal heat treatment. First, the temperature was raised to 900°C at a rate of 25°C / min and held for 60 minutes. Then, the temperature was increased to 1100℃ at a rate of 15℃ / min and held for 90 minutes. Finally, the temperature is increased to 1200℃ at a rate of 5℃ / min and held for 50 hours.

[0038] This invention controls the Ru content within the range of 0.05~0.5 at.%. When the content exceeds 0.5 at.%, experimental results show that mechanical properties begin to deteriorate. This is because excessive addition promotes the formation of refractory / TCP phases or complex compounds, leading to significant mechanical property degradation. It may also be due to changes in the chemical potential balance of the solid solution system, increasing the risk of interfacial segregation and phase separation. Under high-temperature heat treatment conditions, it may exacerbate Kirkendall pores and brittle phase precipitation within the interface or coating, reducing interfacial bonding strength and service reliability. Therefore, this invention selects a Ru content within the range of 0.05~0.5 at.% to balance the effectiveness of suppressing γ′ coarsening with material / preparation costs and long-term microstructural stability. High Ru contents exceeding this range are not conducive to the technical objective of "delaying precipitate phase coarsening and ensuring interfacial stability" and may also introduce new destructive phases and reliability risks. Therefore, the Ru content is 0.05~0.5 at.%.

[0039] Therefore, the present invention provides a heat treatment method for improving the precipitated phases in different Ni-based alloy coatings, which can effectively control the precipitation and solid solution behavior of the precipitated phases. By adjusting the Ru element content and controlling the heat treatment temperature and time, the formation of brittle precipitated phases in the alloy under high-temperature heat exposure environment can be significantly suppressed, the microstructure evolution process can be slowed down, and the stability of the alloy microstructure and high-temperature service performance can be improved. This method combines multi-stage heating, long-term isothermal treatment, and vacuum sealing to further optimize element diffusion behavior and promote the resolution of the precipitate phase. Compared with traditional methods, this invention can significantly reduce the IDZ region and inhibit microstructure degradation, making it suitable for extending the service life and improving the performance of high-temperature components.

[0040] Finally, it should be noted that the above embodiments are only used to illustrate the technical solutions of the present invention and not to limit them. Although the present invention has been described in detail with reference to preferred embodiments, those skilled in the art should understand that modifications or equivalent substitutions can still be made to the technical solutions of the present invention, and these modifications or equivalent substitutions cannot cause the modified technical solutions to deviate from the spirit and scope of the technical solutions of the present invention.

Claims

1. A heat treatment method for improving the precipitated phases in coatings of different Ni-based alloys, characterized in that, Includes the following steps: S1. Polishing the Ni-based single-crystal superalloy and depositing a Ni-based coating on the surface of the Ni-based single-crystal superalloy using physical vapor deposition technology, and achieving different Ru addition amounts by adjusting the target material composition. S2. The prepared Ni-based coating-alloy diffusion couple is placed in a quartz glass tube, vacuumed and sealed, and then placed in a vacuum heat treatment furnace for staged isothermal heat treatment. After the treatment, the product is cooled to obtain the target product.

2. The heat treatment method for improving the precipitated phases of different Ni-based alloy coatings according to claim 1, characterized in that: In S1, the amount of Ru added is 0.05~0.5 at.%; the service temperature of the Ni-based single crystal superalloy is 900~1100℃.

3. The heat treatment method for improving the precipitated phases in different Ni-based alloy coatings according to claim 1, characterized in that: In S1, the process parameters of physical vapor deposition technology are: substrate bias voltage -100V, arc current 100A, deposition gas pressure 1Pa, deposition temperature 300℃, and duty cycle 70%.

4. The heat treatment method for improving the precipitated phases of different Ni-based alloy coatings according to claim 1, characterized in that: In S2, the vacuum degree is 0.05 to 0.1 Pa.

5. The heat treatment method for improving the precipitated phases of different Ni-based alloy coatings according to claim 1, characterized in that: In S2, the heat treatment process is as follows: 1) Heat to 800-900℃ at a rate of 15-25℃ / min and hold for 30-50 minutes; 2) Increase the temperature to 1000-1100℃ at a rate of 10-15℃ / min and hold for 60-90 minutes; 3) Heat to 1100-1200℃ at a rate of 5-10℃ / min and hold for 100-300 hours.

6. The heat treatment method for improving the precipitated phases of different Ni-based alloy coatings according to claim 1, characterized in that: In S2, the cooling method is to cool the furnace to room temperature.

Images