Heat treatment method and application of forged GH3536 high-temperature alloy material

Abstract

This invention relates to a heat treatment method and application of forged GH3536 high-temperature alloy material. The heat treatment method for forged GH3536 high-temperature alloy material includes the following steps: subjecting the forged GH3536 high-temperature alloy material to high-temperature heat treatment; the electromagnetic induction high-temperature pulse oscillation synergistic heat treatment includes: using an electromagnetic induction coil for induction heating, rapidly heating to 1230-1270℃ at a heating rate of 100-105℃ / s, then holding at that temperature for 5 minutes, cooling to 1200℃ at a rate of 10℃ / min, and then placing the alloy into a muffle furnace for high-temperature cyclic oscillation heat treatment using a temperature curve of T=sin(t / 3.5)×65+1175. This invention not only maintains the strength level of the material but also enhances its tensile plasticity, while improving the stability of the alloy's mechanical properties.

Description

Technical Field

[0001] This invention relates to the field of high-temperature alloy material processing, and in particular to a heat treatment method and application for forged GH3536 high-temperature alloy material. Background Technology

[0002] GH3536 alloy is mainly used in high-temperature applications such as aero-engines and industrial furnaces. It can maintain structural stability at temperatures up to 1200℃ and has good oxidation and corrosion resistance. After processing and forming, appropriate heat treatment is required to precisely control the amount and distribution of precipitated phases in the alloy, thereby improving performance, especially enhancing the material's plasticity, enabling it to withstand cyclic thermal and mechanical loads in practical applications.

[0003] Currently, there is a lack of effective heat treatment methods for GH3536 high-temperature alloy materials that can effectively control the quantity and distribution of precipitated phases in the alloy, improve the material's plasticity, and enable it to withstand cyclic thermal and mechanical loads in practical applications. Summary of the Invention

[0004] The purpose of this invention is to provide a heat treatment method for forged GH3536 high-temperature alloy materials, so as to solve the problem that existing methods cannot effectively control the quantity and distribution of precipitates in the alloy, improve the plasticity of the material, and enable it to withstand periodic thermal and mechanical loads in practical applications.

[0005] Another object of the present invention is to provide the application of the heat treatment method for the forged GH3536 high-temperature alloy material described above in improving the normal service of the forged GH3536 high-temperature alloy material.

[0006] To achieve the above objectives, the following technical solution is adopted:

[0007] A heat treatment method for forged GH3536 high-temperature alloy material includes the following steps:

[0008] Step S1: Select GH3536 high-temperature material that has been forged;

[0009] Step S2: Induction heating is performed using an electromagnetic induction coil, with the temperature increased to 1230-1270℃ at a rate of 100-105℃ / s, held for 5 minutes, and then cooled to 1200℃ at a rate of 10℃ / min. Subsequently, the forged GH3536 high-temperature material is fed into a muffle furnace, and the forged GH3536 high-temperature alloy material is subjected to electromagnetic induction high-temperature pulse oscillation synergistic heat treatment using a temperature curve of T=sin(t / 3.5)×65+1175; where T is the furnace temperature in ℃ and t is the time in min.

[0010] Preferably, the forging method for the GH3536 high-temperature material formed in step S1 is hot forging.

[0011] Preferably, the specific temperature curve described in step S2 is as follows:

[0012] After heating to 1225℃ at a rate of 8-10℃ / min, the temperature drops to 1125-1130℃ at a rate of 8-10℃ / min, then heats up again to 1220-1225℃ at a rate of 8-10℃ / min, and then cools down to 1125-1130℃ at a rate of 8-10℃ / min. This cycle is repeated until 60 minutes have elapsed, at which point the sample is placed in water at 25℃ for water cooling.

[0013] Preferably, in step S2, the diameter of the induction coil used for electromagnetic induction is larger than the diameter of the workpiece, and the power and frequency parameters of the induction heating power supply are 40kW and 10kHz, respectively. During the heating process, an infrared thermometer is used to monitor the surface temperature of the workpiece in real time.

[0014] Preferably, the time for placing the induction-heated GH3536 high-temperature material into the muffle furnace in step 2 is controlled within 3 seconds.

[0015] Preferably, the elongation after tensile fracture of the GH3536 high-temperature alloy material obtained by the heat treatment is 54%-61%.

[0016] Preferably, the GH3536 high-temperature alloy material obtained by heat treatment has the following tensile properties:

[0017] (a) Tensile strength: 781MPa-752MPa;

[0018] (b) Yield strength: 290MPa-304MPa.

[0019] Application of heat treatment methods for forged GH3536 high-temperature materials in improving the tensile properties of forged GH3536 high-temperature alloy materials.

[0020] When traditional solution treatment is applied to forged GH3536 high-temperature alloy materials, some blocky carbides remain at the grains and grain boundaries. These carbides at the grain boundaries reduce grain boundary cohesion, tensile and impact properties, and fail to meet application requirements. This invention addresses this issue by changing the solution treatment method for GH3536 high-temperature alloy materials. It utilizes electromagnetic induction high-temperature pulse oscillation combined with heat treatment to precisely control the quantity and distribution of precipitated phases in the alloy. This not only maintains the material's strength level but also significantly enhances its tensile plasticity under high-temperature conditions, while simultaneously improving the stability of the alloy's mechanical properties.

[0021] Compared with the prior art, the beneficial effects of the present invention are as follows:

[0022] By subjecting the forged GH3536 alloy to specific heat preservation and heating / cooling cycles, combined with water cooling technology, the quantity and distribution of precipitated phases in the alloy can be precisely controlled, resulting in better industrial application performance and providing practical improvements for the performance optimization of GH3536 high-temperature alloy materials.

[0023] This invention precisely controls the temperature fluctuations during the solution treatment of GH3536 high-temperature alloy, thereby accurately regulating the growth of alloy grain size and achieving a uniform grain size distribution. Simultaneously, it regulates the quantity, size, and distribution location of precipitated phases, resulting in fine and uniformly distributed carbide precipitates. This not only maintains the material's strength level but also enhances its tensile plasticity and improves the stability of the alloy's mechanical properties. Attached Figure Description

[0024] Figure 1 This is a schematic diagram of the heat treatment technology route.

[0025] Figure 2(a) is a cross-sectional microstructure of the forged GH3536 high-temperature alloy material after heat treatment in Comparative Example 1.

[0026] Figure 2(b) is a cross-sectional microstructure of the forged GH3536 high-temperature alloy material after heat treatment in Comparative Example 2.

[0027] Figure 2(c) is a cross-sectional microstructure of the forged GH3536 high-temperature alloy material after heat treatment in Example 3.

[0028] Figure 2(d) is a cross-sectional microstructure of the forged GH3536 high-temperature alloy material after heat treatment in Example 4.

[0029] Figure 2(e) is a cross-sectional microstructure of the forged GH3536 high-temperature alloy material after heat treatment in Example 5.

[0030] Figure 2(f) is a cross-sectional microstructure diagram of the forged GH3536 high-temperature alloy material after heat treatment in Example 6.

[0031] Figure 3 Mapping images of the forged GH3536 high-temperature alloy material after heat treatment in Comparative Example 1.

[0032] Figure 4 Tensile properties—tensile strength and yield strength—of forged GH3536 high-temperature alloy materials after heat treatment in the examples and comparative examples.

[0033] Figure 5 Tensile properties - elongation after fracture of forged GH3536 high-temperature alloy materials after heat treatment in the examples and comparative examples. Detailed Implementation

[0034] The technical solution of the present invention will be clearly and completely described below with reference to the accompanying drawings and specific embodiments. However, those skilled in the art will understand that the embodiments described below are some embodiments of the present invention, but not all embodiments, and are only used to illustrate the present invention, and should not be regarded as limiting the scope of the present invention. Based on the embodiments of the present invention, all other embodiments obtained by those skilled in the art without creative effort are within the scope of protection of the present invention. Where specific conditions are not specified in the embodiments, conventional conditions or conditions recommended by the manufacturer shall be followed. Where the manufacturers of reagents or instruments are not specified, they are all conventional products that can be purchased commercially.

[0035] The heat treatment method for forged GH3536 high-temperature alloy material includes the following steps:

[0036] The forged GH3536 high-temperature alloy was subjected to electromagnetic induction high-temperature pulse oscillation combined heat treatment.

[0037] Induction heating is performed using an electromagnetic induction coil, rapidly heating to 1230-1270℃ at a rate of 100-105℃ / s, then holding at that temperature for 5 minutes, followed by cooling to 1200℃ at a rate of 10℃ / min. The alloy is then placed in a muffle furnace and subjected to high-temperature cyclic heat treatment using a temperature curve of T = sin(t / 3.5) × 65 + 1175, where T is the furnace temperature in℃ and t is the time in min. The approximate temperature curve for the cyclic phase is as follows:

[0038] After heating to 1225℃ at a rate of 8-10℃ / min, the temperature drops to 1125-1130℃ at a rate of 8-10℃ / min, then heats up again to 1220-1225℃ at a rate of 8-10℃ / min, and then cools down to 1125-1130℃ at a rate of 8-10℃ / min. This cycle is repeated until 60 minutes have elapsed, at which point the sample is placed in water at 25℃ for water cooling.

[0039] When using traditional solution treatment processes, brittle carbides at metal grain boundaries cannot be completely dissolved at a solution temperature of 1175℃. The residual brittle carbides significantly reduce the material's mechanical properties. When the temperature exceeds 1175℃, the high temperature causes abnormal grain growth, severely reducing the material's mechanical properties. This invention addresses the forging process of GH3536 by using a special temperature profile to precisely control the precipitation of grain boundary carbides, thereby significantly improving the material's ductility and toughness.

[0040] In practical operation, the heat treatment method of the present invention is applicable to forged GH3536 high-temperature alloy materials, wherein the forging process refers to the conventional GH3536 high-temperature alloy forging process parameters.

[0041] In a specific embodiment of the present invention

[0042] Step S1: Select the forged GH3536 high-temperature material.

[0043] Step S2: Using induction heating, the GH3536 forging is rapidly heated to 1230-1270℃, and then the forged GH3536 high-temperature alloy material is subjected to electromagnetic induction high-temperature pulse oscillation synergistic heat treatment.

[0044] The electromagnetic induction high-temperature pulse oscillation synergistic heat treatment includes: induction heating using an electromagnetic induction coil, rapidly heating to 1250℃ at a heating rate of 100-105℃ / s, then placing the alloy into a muffle furnace, holding at that temperature for 5 minutes, and cooling to 1200℃ at a rate of 10℃ / min. Subsequently, high-temperature cyclic oscillation heat treatment is performed using a temperature curve T=sin(t / 3.5)×65+1175, where T is the furnace temperature in℃ and t is the time in min. The specific temperature curve for the cyclic stage is approximately as follows:

[0045] After heating to 1225℃ at a rate of 8-10℃ / min, the temperature drops to 1125-1130℃ at a rate of 8-10℃ / min, then heats up again to 1220-1225℃ at a rate of 8-10℃ / min, and then cools down to 1125-1130℃ at a rate of 8-10℃ / min. This cycle is repeated until 60 minutes have elapsed, at which point the sample is placed in water at 25℃ for water cooling.

[0046] In a specific embodiment of the present invention, the heat treatment method for the forged GH3536 high-temperature alloy material is characterized in that the forging method in step S1 is hot forging.

[0047] In a specific embodiment of the present invention, the heat treatment method for the forged GH3536 high-temperature alloy material is characterized in that, in step S2, the diameter of the induction coil is slightly larger than the diameter of the workpiece, the power and frequency parameters of the induction heating power supply are 40kW and 10kHz respectively, and an infrared thermometer is used to monitor the surface temperature of the workpiece in real time during the heating process.

[0048] In a specific embodiment of the present invention, the heat treatment method for the forged GH3536 high-temperature alloy material is characterized in that the time for placing the induction-heated GH3536 nickel-based high-temperature alloy into the muffle furnace in step 2 is controlled within 3 seconds.

[0049] In a specific embodiment of the present invention, the GH3536 high-temperature alloy material obtained by the heat treatment method of the forged GH3536 high-temperature alloy material is described.

[0050] In a specific embodiment of the present invention, the GH3536 high-temperature alloy material is characterized in that the elongation after tensile fracture of the GH3536 high-temperature alloy material obtained by the treatment satisfies the following: both the transverse and longitudinal elongation are 54%-61%.

[0051] In a specific embodiment of the present invention, the GH3536 high-temperature alloy material is characterized in that the tensile properties of the GH3536 high-temperature alloy material obtained by the treatment are satisfied as follows:

[0052] (a) Tensile strength: ≥752MPa

[0053] (b) Yield strength: ≥304MPa

[0054] Examples and Comparative Examples

[0055] Comparative Example 1

[0056] This comparative example provides a heat treatment method for forged GH3536 high-temperature alloy material, including the following:

[0057] (1) Place the forged GH3536 high-temperature alloy material into a muffle furnace that has been heated to 1175℃ and hold for 50 minutes.

[0058] (2) Take out the forged GH3536 alloy sample from the muffle furnace, put it into water at 25°C for water cooling to room temperature, cut off a 1.5mm×1.5mm×1.5mm sample, grind and polish the observation surface, observe the metallographic structure, and perform mechanical property tests.

[0059] After heat treatment of GH3536 in Comparative Example 1, the original orientation of the forged microstructure completely disappeared, the grains became equiaxed, and a large amount of carbides were distributed in the grain boundaries and within the grains, as shown in Figure 2(a). This change reduces the mechanical properties of the alloy. Although the grains grow sufficiently, the significant decrease in strength causes the alloy to lose its advantage of high mechanical properties.

[0060] Figure 3 The mapping diagram for the embodiment is further combined with Figure 3 Elemental distribution observations revealed that the carbides were Cr-rich and Mo-rich M. 23 C6 and M6C type carbides.

[0061] The tensile strength, yield strength, and elongation of the heat-treated GH3536 nickel-based superalloy in the comparative example and the embodiment are shown in the figures below. Figure 4 and Figure 5.

[0062] Comparative Example 2

[0063] This comparative example provides a heat treatment method for forged GH3536 high-temperature alloy material, including the following:

[0064] (1) Place the forged GH3536 high-temperature alloy material into a muffle furnace that has been heated to 1200℃ and hold for 30 minutes.

[0065] (2) Take out the forged GH3536 alloy sample from the muffle furnace, put it into water at 25°C for water cooling to room temperature, cut off a 1.5mm×1.5mm×1.5mm sample, grind and polish the observation surface, observe the metallographic structure, and perform mechanical property tests.

[0066] After heat treatment in Comparative Example 2, the original orientation of the forged microstructure of the grains completely disappeared, and the grain size further increased. However, carbides still existed in the alloy and were uniformly distributed within the grains and at the grain boundaries, which weakened the strength of the grain boundaries and led to a decrease in the mechanical properties of the alloy. Example 3

[0067] The embodiment provides a heat treatment method for forged GH3536 high-temperature alloy material, including the following steps:

[0068] (1) GH3536 high temperature alloy specimens formed by conventional forging.

[0069] (2) The forged GH3536 obtained in step (1) is subjected to high-temperature pulse oscillation synergistic heat treatment and ordinary solution treatment; specifically, an electromagnetic induction coil is used for induction heating to rapidly raise the temperature of the GH3536 forging to 1230°C, and then the alloy is sent into a muffle furnace to perform electromagnetic induction high-temperature pulse oscillation synergistic heat treatment on the forged GH3536 high-temperature alloy material.

[0070] (3) Take out the forged GH3536 alloy sample from the muffle furnace, put it into water at 25°C for water cooling to room temperature, cut off a 1.5mm×1.5mm×1.5mm sample, grind and polish the observation surface, observe the metallographic structure, and perform mechanical property tests. Example 4

[0071] The embodiment provides a heat treatment method for forged GH3536 high-temperature alloy material, including the following steps:

[0072] (1) GH3536 high temperature alloy specimens formed by conventional forging.

[0073] (2) The forged GH3536 obtained in step (1) is subjected to electromagnetic induction high temperature pulse oscillation synergistic heat treatment and ordinary solution treatment; specifically, electromagnetic induction coil is used for induction heating to rapidly raise the temperature of GH3536 forging to 1250℃, and then the alloy is sent into the muffle furnace to perform high temperature pulse oscillation synergistic heat treatment on the forged GH3536 high temperature alloy material.

[0074] (3) Take out the forged GH3536 alloy sample from the muffle furnace, put it into water at 25°C for water cooling to room temperature, cut off a 1.5mm×1.5mm×1.5mm sample, grind and polish the observation surface, observe the metallographic structure, and perform mechanical property tests. Example 5

[0075] The embodiment provides a heat treatment method for forged GH3536 high-temperature alloy material, including the following steps:

[0076] (1) GH3536 high temperature alloy specimens formed by conventional forging.

[0077] (2) The forged GH3536 obtained in step (1) is subjected to electromagnetic induction high temperature pulse oscillation synergistic heat treatment and ordinary solution treatment; specifically, electromagnetic induction coil is used for induction heating to rapidly raise the temperature of GH3536 forging to 1270°C, and then the alloy is sent into the muffle furnace to perform high temperature pulse oscillation synergistic heat treatment on the forged GH3536 high temperature alloy material.

[0078] (3) Take out the forged GH3536 alloy sample from the muffle furnace, put it into water at 25°C for water cooling to room temperature, cut off a 1.5mm×1.5mm×1.5mm sample, grind and polish the observation surface, observe the metallographic structure, and perform mechanical property tests.

[0079] Example: Electromagnetic induction high-temperature pulse oscillation synergistic heat treatment temperature parameters are as follows Figure 1 As shown.

[0080] As can be seen from the microstructures and mechanical properties obtained in Comparative Examples 1 and 2 and Examples 3, 4, and 5, the solution treatment regime has a significant impact on the carbide precipitation and grain size of the forged GH3536 high-temperature alloy samples. Comparing Figures 2(a) and (b), it can be seen that after electromagnetic induction high-temperature pulse oscillation synergistic heat treatment, compared with standard solution treatment, the carbides precipitated along the grain boundaries almost completely disappeared, and the bulk precipitates were also eliminated. Now, only fine carbides exist in the grains in a dispersed form, and the grains have not grown excessively.

[0081] The GH3536 carbide alloy contains elements such as chromium and molybdenum, which have a strong affinity for carbon and tend to form stable carbides. At high temperatures, carbon diffusion and the migration of chromium and molybdenum increase, increasing the likelihood of carbide formation at grain boundaries. These grain boundary carbides can become the source of crack initiation and propagation, reducing the alloy's toughness and strength. During multi-stage cyclic heat treatment, the atomic diffusion rate at grain boundaries is higher than in the intragranular region due to their high-energy state, leading to preferential dissolution of carbides at the grain boundaries. Intragranular carbides dissolve more slowly. Therefore, multi-stage cyclic heat treatment can selectively dissolve grain boundary carbides. Furthermore, the shorter duration of the high-temperature period prevents excessive grain size growth, thus improving the sample's plasticity and strength.

[0082] Based on the above results, it can be seen that the heat treatment process of the present invention is for forged GH3536 high-temperature alloy material. After multiple stages of cyclic heat treatment, the carbides that originally precipitated along the grain boundaries basically disappeared, and only fine carbides remained in the grains, and the grains did not grow excessively.

[0083] The above description is merely a preferred embodiment of the present invention and is not intended to limit the present invention in any way. Although the present invention has been disclosed above with reference to preferred embodiments, it is not intended to limit the present invention. Any person skilled in the art can make some modifications or alterations to the above-disclosed technical content to create equivalent embodiments without departing from the scope of the present invention. Any simple modifications, equivalent changes and alterations made to the above embodiments based on the technical essence of the present invention without departing from the scope of the present invention shall still fall within the scope of the present invention.

Claims

1. A heat treatment method for forged GH3536 high-temperature alloy material, characterized in that, Includes the following steps: Step S1: Select GH3536 high-temperature material that has been forged; Step S2: Induction heating is performed using an electromagnetic induction coil, with the temperature increased to 1230-1270℃ at a rate of 100-105℃ / s, held for 5 minutes, and then cooled to 1200℃ at a rate of 10℃ / min. Subsequently, the forged GH3536 high-temperature material is fed into a muffle furnace, and the forged GH3536 high-temperature alloy material is subjected to electromagnetic induction high-temperature pulse oscillation synergistic heat treatment using a temperature curve of T=sin(t / 3.5)×65+1175; where T is the furnace temperature in ℃ and t is the time in min.

2. The heat treatment method for the forged GH3536 high-temperature alloy material according to claim 1, characterized in that, The forging method for the GH3536 high-temperature material in step S1 is hot forging.

3. The heat treatment method for the forged GH3536 high-temperature alloy material according to claim 1, characterized in that, The specific temperature curve in step S2 is as follows: After heating to 1225℃ at a rate of 8-10℃ / min, the temperature drops to 1125-1130℃ at a rate of 8-10℃ / min, then heats up again to 1220-1225℃ at a rate of 8-10℃ / min, and then cools down to 1125-1130℃ at a rate of 8-10℃ / min. This cycle is repeated until 60 minutes have elapsed, at which point the sample is placed in water at 25℃ for water cooling.

4. The heat treatment method for the forged GH3536 high-temperature alloy material according to claim 1, characterized in that, In step S2, the diameter of the induction coil used for electromagnetic induction is larger than the diameter of the workpiece. The power and frequency parameters of the induction heating power supply are 40kW and 10kHz, respectively. During the heating process, an infrared thermometer is used to monitor the surface temperature of the workpiece in real time.

5. The heat treatment method for the forged GH3536 high-temperature alloy material according to claim 1, characterized in that, In step 2, the time for placing the induction-heated GH3536 high-temperature material into the muffle furnace should be controlled within 3 seconds.

6. The heat treatment method for the forged GH3536 high-temperature alloy material according to any one of claims 1-5, characterized in that, The GH3536 high-temperature alloy material obtained by the heat treatment has an elongation at break of 54%-61%.

7. The heat treatment method for the forged GH3536 high-temperature alloy material according to any one of claims 1-5, characterized in that, The GH3536 high-temperature alloy material obtained by heat treatment meets the following tensile requirements: (a) Tensile strength: 781MPa-752MPa; (b) Yield strength: 290MPa-304MPa.

8. The application of the heat treatment method for forged GH3536 high-temperature material according to any one of claims 1-5 in improving the tensile properties of forged GH3536 high-temperature alloy material.

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