A High-Performance Spinning Forming Method for a Large-Thickness 5B70 Sealed Cabin

Abstract

The present invention provides a high-performance spinning forming method for a large-thickness 5B70 sealed cabin body, comprising the following steps: (1) obtaining 5B70 plates to be spun formed by rolling, and acquiring the rolling parameters and mechanical property parameters of the plates; (2) determining the preheating temperature according to the rolling parameters and mechanical property parameters of the plates, and uniformly preheating the plates with the preheating temperature; (3) determining the spinning processing temperature corresponding to each region according to the spinning deformation amount of different regions of the plates, the rolling parameters and mechanical property parameters of the plates, and performing spinning forming on the preheated plates. By analyzing the mechanical properties of 5B70 and the rolling forming system, the present invention determines the preheating temperature for the spinning forming of the plates, and adopts different spinning processing temperatures for different deformation amount regions, effectively suppressing the deterioration of the plate properties during the spinning forming process, ensuring that the sealed cabin body after spinning forming can maintain high performance throughout the whole region, and having good service effects.

Description

Technical Field

[0001] The present invention belongs to the technical field of spin forming of aluminum-magnesium-scandium alloys, and particularly relates to a high-performance spin forming method for a large-thickness 5B70 sealed cabin body. Background Art

[0002] With the increasing requirement for lightweight of spacecraft sealed cabins, as the traditional main application material of sealed cabins, the yield limit of 5A06 aluminum alloy is relatively low and can no longer meet the development needs of new sealed cabin structures. Therefore, a new aluminum-magnesium-scandium 5B70 alloy is used in the sealed cabin structure to improve the yield limit of the material and enhance the high-load and lightweight level of the cabin body structure.

[0003] Scandium in 5B70 aluminum-magnesium-scandium alloy first significantly refines the as-cast structure, reducing the grain size of the aluminum alloy to 20 - 30 μm; then the uniformly precipitated A13Sc particles coherent with the Al matrix can produce precipitation strengthening; and the dispersed A13Sc particles can strongly pin dislocations, prevent alloy recrystallization, and produce significant substructure strengthening.

[0004] During the spin forming process of 5B70 aluminum-magnesium-scandium alloy, the deformation amount is small and the forming temperature is high. The grains tend to grow and the dislocations tend to annihilate, resulting in the following problems: the strain strengthening and strain rate strengthening effects are weakened, and the yield strength and tensile strength of the material are lost after hot spin forming. Summary of the Invention

[0005] The technical problem solved by the present invention is: overcoming the deficiencies of the prior art, providing a high-performance spin forming method for a large-thickness 5B70 sealed cabin body, effectively suppressing the deterioration trend of the material, and maintaining high mechanical properties of the spin-formed parts.

[0006] The technical solution of the present invention is:

[0007] A high-performance spin forming method for a large-thickness 5B70 sealed cabin body, comprising the following steps:

[0008] (1) Obtain 5B70 plates to be spin formed by rolling, and acquire the rolling parameters and mechanical property parameters of the plates;

[0009] (2) Determine the preheating temperature according to the rolling parameters and mechanical property parameters of the plates, and uniformly preheat the plates at the preheating temperature;

[0010] (3) Determine the spin forming temperature corresponding to each region according to the spin forming deformation amount of different regions of the plates, the rolling parameters and mechanical property parameters of the plates, and perform spin forming on the preheated plates.

[0011] Preferably, in step (1), the rolling process of the 5B70 plate to be spun includes hot rolling and temperature-controlled rolling of the 5B70 ingot in sequence, the hot rolling is performed above the recrystallization temperature of the plate, and the temperature-controlled rolling controls the starting temperature and the ending temperature of the rolling to ensure the mechanical properties of the plate.

[0012] Preferably, the yield strength of the 5B70 plate to be spin-formed obtained by rolling is greater than or equal to 220 MPa.

[0013] Preferably, in step (1), the rolling parameters are the starting temperature T0 of the temperature-controlled rolling of the plate, and the percentage R% of the total deformation of the ingot during the temperature-controlled rolling process to the total deformation during the rolling process.

[0014] Preferably, in step (1), the mechanical property parameter is the yield strength σ of the 5B70 sheet to be spun s .

[0015] Preferably, in step (2), the preheating temperature is determined according to the rolling parameters and mechanical property parameters of the plate, specifically:

[0016] When σ s When ≥260MPa, T t =T0-R / 2;

[0017] When 220MPa≤σ s When <260MPa, T t =250℃;

[0018] Among them, T t Indicates the preheating temperature.

[0019] Preferably, in step (3), the spinning temperature corresponding to each area is determined according to the deformation amount of different areas of the plate, specifically:

[0020] When the deformation of the region is less than or equal to the first threshold:

[0021] T x =250℃;

[0022] When the deformation of the region is greater than the first threshold and less than the second threshold:

[0023] If σ s ≥260MPa, T x =T0-R / 2;

[0024] If 220MPa≤σ s <260MPa,T x =280℃;

[0025] When the deformation of the region is greater than or equal to the first threshold:

[0026] If σ s ≥ 260 MPa, T x = T0 - R / 4;

[0027] If 220 MPa ≤ σ s <260 MPa, T x = 330 °C;

[0028] Among them, T x represents the spinning temperature.

[0029] Preferably, the first threshold is 10% of the original size of this area, and the second threshold is 30% of the original size of this area.

[0030] Preferably, the starting temperature T0 of the temperature-controlled rolling ranges from 150 °C to 350 °C.

[0031] Preferably, the value range of R is 30 - 40.

[0032] The advantages of the present invention compared with the prior art are as follows:

[0033] In view of the performance strengthening characteristics of the aluminum-magnesium-scandium alloy, the present invention proposes a high-performance maintaining spinning forming method for large-thickness 5B70 aluminum-magnesium-scandium alloy. By analyzing the mechanical properties of 5B70 plates and the rolling forming system, the preheating temperature for the spinning forming of the plates is determined, and different spinning processing temperatures are adopted for different deformation amount regions. During the forming process, the deterioration trend of the material is effectively inhibited, and the high mechanical properties of the spun parts are maintained, realizing the high-performance spinning forming of large integral 5B70 cabin structures. Brief Description of the Drawings

[0034] Figure 1 is a schematic flow chart of the high-performance spinning forming method for the large-thickness 5B70 sealed cabin of the present invention;

[0035] Figure 2 is a schematic diagram of the typical mechanical properties of the spun parts in the embodiment of the present invention;

[0036] Figure 3 is a schematic diagram of the fracture morphology of the spun parts in the embodiment of the present invention;

[0037] Figure 4 is a schematic diagram of the EBSD image and grain boundary data of the spun parts before annealing in the embodiment of the present invention;

[0038] Figure 5 is a schematic diagram of the EBSD image and grain boundary data of the spun parts after annealing in the embodiment of the present invention. Detailed Embodiments

[0039] The present invention will be described in detail below, and its features and advantages will become clearer and more definite with these descriptions.

[0040] The present invention provides a high-performance spinning forming method for a large-thickness 5B70 sealed cabin body, as Figure 1 shown, including the following steps:

[0041] S1 Obtain a 5B70 sheet to be spin-formed by rolling, and acquire the rolling parameters and mechanical property parameters of the sheet;

[0042] Specifically, the rolling process includes successively performing hot rolling and controlled-temperature rolling on a 5B70 ingot. Hot rolling is carried out above the recrystallization temperature of the sheet, and controlled-temperature rolling controls the starting temperature and ending temperature of rolling to ensure the mechanical properties of the sheet.

[0043] Furthermore, the yield strength of the 5B70 sheet to be spin-formed obtained by rolling is greater than or equal to 220 MPa.

[0044] Furthermore, the rolling parameters are the starting temperature T0 of the controlled-temperature rolling of the sheet and the percentage R% of the total deformation of the ingot during the controlled-temperature rolling in the total deformation of the rolling process; the mechanical property parameter is the yield strength σ of the 5B70 sheet to be spin-formed s .

[0045] In a specific embodiment, the value range of the starting temperature T0 of the controlled-temperature rolling is 150 °C to 350 °C; the value range of R is 30 to 40.

[0046] S2 Determine the preheating temperature according to the rolling parameters and mechanical property parameters of the sheet, and uniformly preheat the sheet with the preheating temperature;

[0047] Specifically, when σ s ≥ 260 MPa, T t = T0 - R / 2;

[0048] When 220 MPa ≤ σ s < 260 MPa, T t = 250 °C;

[0049] Wherein, T t represents the preheating temperature.

[0050] Furthermore, during the preheating process, thermocouples are arranged at intervals of 500 mm along the spinning part sheet to detect the surface temperature of the sheet, and holes are drilled at the center, with at least 1 thermocouple arranged to monitor the temperature at 1 / 2 thickness of the sheet. After all the thermocouples indicate the preset temperature, immediately end the preheating of the sheet.

[0051] S3 determines the spinning processing temperature corresponding to each region according to the spinning deformation amount of different regions of the sheet, the rolling parameters and mechanical property parameters of the sheet, and performs spinning forming on the preheated sheet.

[0052] Specifically, the deformation amount of each region of the sheet during the spinning forming process is obtained through simulation.

[0053] When the deformation amount of the region is less than or equal to the first threshold:

[0054] T x = 250°C;

[0055] When the deformation amount of the region is greater than the first threshold and less than the second threshold:

[0056] If σ s ≥ 260 MPa, T x = T0 - R / 2;

[0057] If 220 MPa ≤ σ s <260 MPa, T x = 280°C;

[0058] When the deformation amount of the region is greater than or equal to the first threshold:

[0059] If σ s ≥ 260 MPa, T x = T0 - R / 4;

[0060] If 220 MPa ≤ σ s <260 MPa, T x = 330°C;

[0061] Among them, T x represents the spinning processing temperature.

[0062] Furthermore, the first threshold is 10% of the original size of this region, and the second threshold is 30% of the original size of this region.

[0063] In a specific embodiment, the thickness is selected as the original size for calculating the deformation amount.

[0064] To fully illustrate the rationality and reliability of the method of the present invention, the research and analysis process of the method of the present invention is described as follows:

[0065] First, according to the sheet rolling process and the mechanical properties of the sheet, the main strengthening mechanism of the sheet is analyzed.

[0066] The production process flow of sheet production is ingot heating → hot rolling → controlled rolling → flatness detection → pre-stretching → sawing → detection.

[0067] The metallographic structure of the sheet shows that the sheet structure is a deformed band structure evenly distributed along the rolling direction. Transmission microstructure analysis shows that a large number of dislocations in the deformed matrix are tangled at both grain boundaries and within grains, forming a large number of dislocation wall interfaces. The dislocation walls within the grains divide the grains into smaller-sized dislocation cell blocks. The dislocations are rearranged around the cell blocks, forming a large number of small-angle sub-boundaries. This microstructure morphology is a typical feature of the material with excellent mechanical properties.

[0068] During the production process of the sheet, rolling is carried out in two stages. The first stage is normal rolling, and the second stage is temperature-controlled rolling. The total processing rate of the second-stage rolling is controlled within the range of 30% - 40%. The start temperature and end temperature of the second-stage rolling need to be controlled in a certain way at the production site. Due to the different sheet thicknesses and the different total deformation amounts from the ingot to the sheet, the deformation amount of the temperature-controlled rolling also changes accordingly. Then, due to the difference in the flatness of each sheet during the production process, the tensile deformation amounts during the actual room-temperature leveling process of the sheets are also different.

[0069] For the finished sheets with a thickness in the range of 30 - 70 mm, in the same direction, for example, in the transverse direction of the sheet, the tensile strength varies between 375 - 420 MPa, the yield strength varies between 230 - 290 MPa, and the elongation varies between 12% - 22%.

[0070] Both the medium-temperature rolling and room-temperature leveling processes can improve the mechanical properties of the 5B70 material to varying degrees, but different processes have significant differences in the improvement amplitude of the material properties and the influence on the performance stability after subsequent spinning forming. This results in different mechanical properties of the material sheets, or different properties of the sheets with the same mechanical properties after spinning forming in the same process. Furthermore, it may lead to the situation that the spun parts either cannot meet the requirements of the cabin structure for high yield strength (yield strength ≥ 220 MPa), or cannot meet the requirements of the entire cabin structure for performance uniformity (the mechanical property deviation of the spun parts in the whole area ≤ 10%).

[0071] To ensure the lightweight degree and structural stability of the spacecraft cabin structure. It is required that during the manufacturing process of the spun blank for the cabin, first, the material should maintain a high yield strength to resist various force loads; then, the material should be regulated to have uniform global properties, so that the overall structure is stressed stably and does not undergo distortion.

[0072] During the forming process from the sheet to the spun part, due to the complex folded bus configuration of the cabin structure, the deformation degrees of the materials at different bus heights are different.

[0073] Thus, by analyzing the sheet rolling process and the typical microstructure of the sheet, a spinning forming temperature regime is formulated. Under different mechanical properties and different property stabilities of the sheet, for the spinning forming with different deformation amounts in each region, by regulating the forming temperature, the goals of high mechanical properties and high property uniformity of the spun parts are achieved, laying a performance foundation for the stable load-bearing of the cabin structure.

[0074] Example of the actual operation process:

[0075] The first step: Analyze the actual deformation parameters of sheet rolling, including the total deformation amount, the deformation amount in medium-temperature rolling, the starting rolling and medium rolling temperatures in medium-temperature rolling, and the deformation amount of room-temperature leveling.

[0076] The second step: Take the starting rolling temperature in medium-temperature rolling as the temperature reference T0; the deformation amount in medium-temperature rolling as the performance prediction reference parameter, and the deformation amount of room-temperature leveling as the performance instability factor parameter.

[0077] The third step: Take samples from the sheet body. At T0 ± 30 °C, take no less than three groups of different temperatures, and perform full annealing on the sheet. Then process test bars and test the mechanical properties at room temperature.

[0078] The fourth step: For a typical cabin structure, trial-produce a spun part with a temperature reference of T1, and then perform a full dissection. At T0 ± 30 °C, take no less than three groups of different temperatures, and perform full annealing on the samples taken. Then process test bars and test the mechanical properties at room temperature. Test the global mechanical properties of the spun part at different busbar heights, and observe the typical microstructure morphology of the spun part under different deformation amounts.

[0079] For example: Dissect and analyze a certain spun part with a folded busbar, test the global mechanical properties of the spun part trial-produced at temperature T1 after full annealing at different temperatures, analyze the mechanical properties, and summarize the changing trends of the properties of such spun parts with different deformation amounts and different annealing temperatures. The typical results of a certain spun part are as follows Figure 2As shown in (a) to (d), the following characteristics can be summarized from the performance results: (1) The strength of the central region is generally lower than that of the large-mouth region samples; (2) The strength of the transverse samples is slightly lower than that of the longitudinal samples, and the strength of the transverse samples in the central region is mostly lower than the standard value of 220 MPa; (3) The strength of the samples does not show corresponding regular changes with the change of the annealing temperature. Regarding the first point, this is actually related to the deformation amount of the samples. The thickness of the spun parts in the central region is thicker than that in the large-mouth region, indicating that the deformation amount in the thickness direction is less, and the work-hardening effect obtained during the hot spinning process is also less. Therefore, the strength of the central region is lower than that of the large-mouth region. Regarding the second point, due to the characteristics of the spinning deformation, the length of the original sheet in the arc direction of spinning (here it is the transverse direction) decreases, that is, there is a certain compression, which is not conducive to and maintaining the integrity of the fiber structure. In the busbar direction of spinning, the sheet is stretched, that is, the longitudinal tensile samples are in tensile deformation during the spinning process, and the deformation is more uniform. Therefore, the strength of the longitudinal samples is slightly higher than that of the transverse samples, but the difference is not significant. Adding the difference in the deformation amount between the central region and the large-mouth region, the transverse samples in the central region are the lowest in overall performance.

[0080] There is no regular connection between the strength of the samples and the annealing temperature. This indicates that the reduction of mechanical properties is related to the excessive local temperature during spinning deformation. When the local temperature during deformation is too high, the mechanical properties have already been lost. In the subsequent annealing, the highest annealing temperature is 350 °C, and this temperature is very likely not to reach the local maximum temperature during the spinning process. Since the local high temperature during the spinning process has caused the softening of the material and determined the properties of the material, the subsequent annealing will not have a new impact on the properties. Therefore, the strength of the samples does not change due to different annealing temperatures.

[0081] Step 5: Analyze the fracture morphologies of typical specimens with different mechanical properties.

[0082] The fracture of the tensile samples was analyzed by scanning electron microscopy. The scanning electron microscopy results are as Figure 3 shown in (a) to (i), where: (a) unannealed; (b) annealed at 200 °C; (c) annealed at 220 °C; (d) annealed at 240 °C; (e) annealed at 260 °C; (f) annealed at 280 °C; (g) annealed at 300 °C; (h) annealed at 320 °C; (i) annealed at 350 °C;

[0083] When there are undulations on the fracture of the samples, the fracture surface is relatively rough, and there are dimples of different depths inside the fracture, which indicates that the samples have good toughness and the work-hardening effect is not strong. As Figure 3 (a) and Figure 3 (e) have slightly more dimples than the other images. This is consistent with the lower yield strength results of these two samples in the tensile data.

[0084] When a small amount of flaky texture is found on the fracture surface, this is a characteristic of cleavage fracture. It indicates that the work hardening degree of this sample is slightly higher than that of other samples, but the degree is limited. For example, Figure 3 (c), Figure 3 (g), Figure 3 (h) and Figure 3 (i) can correspond to its slightly higher yield strength.

[0085] Similarly, if the overall fracture surface of the sample is relatively flat, it indicates that there is a transgranular fracture behavior in the sample, and the brittle component of the fracture is higher. The morphology of the fracture surface indicates a higher work hardening level in the sample. For example, when the annealing temperature increases, the number of dimples in the fracture surface increases, and the fracture surface becomes uneven, which indicates that after annealing at a higher temperature, a certain amount of work hardening is eliminated and the toughness is increased.

[0086] Step 6: Analyze the typical microstructure morphology of the spun parts.

[0087] Taking the samples taken from a typical area of a certain spinning as an example, its EBSD images and grain boundary data are as shown in Figure 4 (a), ~(d), where Figure 4 (a), (b) are the original samples in the central area, and 4(c), (d) are the original samples in the large-mouth area. The overall grains show a flat and long spindle shape. There are some fine recrystallized grains on the grain boundaries. At the same time, a small amount of recrystallized grain nucleation can also be seen inside the large grains. Figure 4 (c) shows that most of the grain boundaries in this sample are small-angle grain boundaries, and the average grain boundary angle is 9.15°. The grains in the large-mouth area sample are more slender ( Figure 4 (b)), indicating that the deformation amount of the large-mouth area sample by spinning is higher than that of the central area sample. Recrystallized grains appear both at the grain boundaries and inside the grains. It can be seen from Figure 4 (d) that the average grain boundary angle of this sample is 9.28°, and a large number of grain boundaries are still small-angle grain boundaries. Through the above results, it can be concluded that even without annealing, partial recrystallization has occurred in the spun samples in both regions. At the same time, the lower grain boundary angle indicates that there are a large number of substructures in the grains, which is the result of dynamic recovery, indicating that the local temperature during spinning is too high.

[0088] The results after annealing the large-mouth area transversely at 220°C and 240°C are as shown in Figure 5 (a)~(d), where, Figure 5 (a), (b) are the results after annealing at 220°C, Figure 5(c) and (d) Results after annealing at 240 °C. The overall EBSD morphologies of the following two samples are very similar. There are some small equiaxed grains in the fibrous grains. The fibrous grains of the large-mouth area sample are more slender than those of the central area sample, but the recrystallization degrees are close. The average grain boundary angles of the two large-mouth area samples are 9.44° and 9.95°, slightly higher than those of the original sample, but lower than those of the central area annealed sample. This indicates that the deformed structure of this group of samples is more than that of the central area annealed sample. In addition, there is no obvious increase in the grain boundary angle after annealing, indicating that there are no excess dispersed dislocations in the sample, and the deformed structure is retained in the form of substructure.

[0089] Step 7: Comprehensive analysis conclusion of the fully sectioned specimen.

[0090] Through the comprehensive analysis of the mechanical property results, tensile fracture results, and EBSD grain results, the following conclusions can be drawn: First, the scanning images of the fracture can basically correspond to the strength results of the samples. Although the differences between the fractures of different samples are not significant, the toughness differences of different samples can be basically judged based on information such as the number of dimples, dimple size, dimple ratio, and fracture flatness. This difference can basically match the tensile results of the samples. That is, the sample with more dimples has more toughness components in its fracture form, less work hardening effect is retained, and the recrystallization degree of the material is higher.

[0091] Second, it can be clearly seen from the EBSD results that the sample with more slender fibrous tissue has a larger amount of deformation. More deformation results in more deformed structure and higher mechanical properties in the sample. From the change in the grain boundary angle of EBSD, the recrystallized structure in the sample can be seen to vary with the annealing temperature. When annealing does not have a great impact on the microstructure of the material, all tissues are very fine and their sizes are close, and there is no phenomenon of recrystallized grain growth, it indicates that the fine recrystallized grains are the result of dynamic recrystallization, while static annealing-caused recrystallization will show the phenomenon of grain boundary bowing and growth. When no such changes are found, it proves that the actual deformation temperature of hot working is higher than the annealing temperature of the specimen. The recrystallized structure in the sample is mainly formed during the spinning process, and subsequent annealing only forms some substructures and does not have a great impact on the grain structure. There is also no obvious regular change in the performance differences between samples at different annealing temperatures and the annealing temperature. On the contrary, it proves that the actual deformation temperature of spin forming is lower than the annealing temperature.

[0092] Step 8:

[0093] Then, according to the plate rolling parameters, structure, and dislocation conditions, the preheating temperature of the spun part is designed.

[0094] During the preheating process of the spun parts, most of the work hardening caused by leveling the sheet at room temperature will be eliminated. When the preheating temperature is equal to the starting rolling temperature of medium-temperature rolling, part of the work hardening caused by medium-temperature rolling will be further eliminated. The greater the deformation amount of medium-temperature rolling, the higher the elimination ratio. Therefore, the preheating temperature of spinning is designed based on the actual deformation amount and measured performance of each sheet. The principle for selecting the preheating temperature is to raise the preheating temperature as much as possible while leaving a certain performance margin.

[0095] For example: The starting rolling temperature of medium-temperature rolling for a certain sheet is 330 °C, the deformation amount of medium-temperature rolling accounts for 40% of the total deformation amount, the yield strength of the sheet is 280 MPa, and the preheating temperature of the spun part is selected as 310 °C. Some unstable work hardening properties can be removed, and a certain toughness can be reserved for the spinning forming of the sheet.

[0096] The starting rolling temperature of medium-temperature rolling for a certain sheet is 330 °C, the deformation amount of medium-temperature rolling accounts for 40% of the total deformation amount, the yield strength of the sheet is 240 MPa, and the preheating temperature of the spun part is selected as 250 °C. At this time, it can be ensured that the mechanical properties of the sheet basically do not decrease after subsequent spinning processing.

[0097] The ninth step:

[0098] Finally, design the spinning forming temperature to ultimately ensure that the spun parts maintain their high mechanical properties.

[0099] Based on the above data and analysis conclusions, combined with the required deformation amount and deformation speed for precise size forming during the spinning process, corresponding deformation temperature parameters can be formulated in stages. In the area with a small deformation amount, the deformation temperature should be reduced as much as possible to prevent dynamic recrystallization. If the work hardening effect of the original sheet is eliminated and the newly introduced deformation amount is not enough to offset the loss caused by high-temperature dynamic recrystallization, the strength of the material will decrease.

[0100] In the area with a large deformation amount, a temperature regime similar to that of medium-temperature rolling is adopted for spinning processing. While maintaining the original properties of the sheet, the temperature should be raised as much as possible to ensure stable deformation and prevent cracking.

[0101] This research invented the spinning forming of high-performance 5B70 aluminum-magnesium-scandium alloy, and proposed a spinning forming method for maintaining high performance based on the rolling regime, microstructure, and dislocation conditions of the sheet, effectively suppressing the deterioration of the sheet properties during the spinning forming process.

[0102] The content not described in detail in the specification of the present invention belongs to the well-known technology of those skilled in the art.

Claims

1. A high-performance spinning forming method for a large-thickness 5B70 sealed cabin, characterized in that, It includes the following steps: (1) Obtain the 5B70 sheet to be spin-formed by rolling, and acquire the rolling parameters and mechanical property parameters of the sheet; In the step (1), the rolling process of the 5B70 sheet to be spin-formed includes hot rolling and controlled-temperature rolling of the 5B70 ingot in sequence. The hot rolling is carried out above the recrystallization temperature of the sheet, and the controlled-temperature rolling controls the starting temperature and the ending temperature of the rolling to ensure the mechanical properties of the sheet; The yield strength of the 5B70 sheet to be spin-formed obtained by rolling is greater than or equal to 220 MPa; In the step (1), the rolling parameters are the starting temperature of the temperature-controlled rolling of the sheet metal , and the percentage R% of the total deformation of the ingot during the temperature-controlled rolling in the total deformation during the rolling process; In the step (1), the mechanical property parameter is the yield strength of the 5B70 sheet to be spun formed ; (2) Determine the preheating temperature according to the rolling parameters and mechanical property parameters of the sheet, and uniformly preheat the sheet with the preheating temperature; In the step (2), determining the preheating temperature according to the rolling parameters and mechanical property parameters of the sheet is specifically as follows: When ≥ 260 MPa, ; When 220 MPa ≤ <260 MPa, ; Among them, represents the preheating temperature; (3) Determine the spin-forming temperature corresponding to each region according to the spin-forming deformation amount of different regions of the sheet, the rolling parameters and mechanical property parameters of the sheet, and carry out spin-forming on the preheated sheet; In the step (3), determining the spin-forming temperature corresponding to each region according to the deformation amount of different regions of the sheet is specifically as follows: When the deformation amount of the region is less than or equal to the first threshold: ； When the deformation amount of the region is greater than the first threshold and less than the second threshold: If ≥ 260 MPa, ; If 220 MPa ≤ <260 MPa, ; When the deformation amount of the region is greater than or equal to the second threshold: If ≥ 260 MPa, ; If 220 MPa ≤ <260 MPa, ; Among them, represents the temperature of spin forming.

2. The high-performance spinning forming method of a large-thickness 5B70 sealing cabin according to claim 1, characterized in that The first threshold is 10% of the original size of this region, and the second threshold is 30% of the original size of this region.

3. A high-performance spinning forming method for a large-thickness 5B70 sealed cabin according to claim 2, characterized in that, The value range of the starting temperature T0 of the controlled-temperature rolling is 150°C to 350°C.

4. A high-performance spinning forming method for a large-thickness 5B70 sealed cabin according to claim 2, characterized in that The value range of R is 30 to 40.

Images