CN116159916A - High-performance spin forming method for large-thickness 5B70 sealed cabin - Google Patents

High-performance spin forming method for large-thickness 5B70 sealed cabin Download PDF

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CN116159916A
CN116159916A CN202211634795.2A CN202211634795A CN116159916A CN 116159916 A CN116159916 A CN 116159916A CN 202211634795 A CN202211634795 A CN 202211634795A CN 116159916 A CN116159916 A CN 116159916A
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rolling
temperature
plate
spinning
forming
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沈晓宇
赖小明
易卓勋
王博
陈少君
张斌
张玉良
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Beijing Satellite Manufacturing Factory Co Ltd
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Beijing Satellite Manufacturing Factory Co Ltd
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/14—Spinning
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B45/00—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
    • B21B45/004—Heating the product
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D37/00—Tools as parts of machines covered by this subclass
    • B21D37/16—Heating or cooling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B2001/225—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length by hot-rolling

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

The invention provides a high-performance spinning forming method of a large-thickness 5B70 sealed cabin body, which comprises the following steps: (1) Obtaining a 5B70 plate to be spin-formed by rolling, and obtaining rolling parameters and mechanical property parameters of the plate; (2) Determining a preheating temperature according to the rolling parameters and the mechanical property parameters of the plate, and uniformly preheating the plate by adopting the preheating temperature; (3) And determining spinning processing temperatures corresponding to the areas according to the spinning deformation of the different areas of the plate, the rolling parameters and the mechanical property parameters of the plate, and carrying out spinning forming on the preheated plate. According to the invention, through analysis of the mechanical property of 5B70 and a rolling forming system, the preheating temperature of the spinning forming of the plate is determined, and different spinning processing temperatures are adopted for areas with different deformation amounts, so that the degradation of the performance of the plate in the spinning forming process is effectively inhibited, the overall high performance of the sealed cabin body after the spinning forming can be ensured, and the sealed cabin body has a good service effect.

Description

High-performance spin forming method for large-thickness 5B70 sealed cabin
Technical Field
The invention belongs to the technical field of aluminum-magnesium-scandium alloy spin forming, and particularly relates to a high-performance spin forming method of a large-thickness 5B70 sealed cabin.
Background
Along with the improvement of the requirement of the light weight of the sealed cabin of the spacecraft, the 5A06 aluminum alloy has lower yield limit as a material for the traditional main application of the sealed cabin, and can not adapt to the development requirement of the novel sealed cabin structure. Therefore, the novel aluminum-magnesium-scandium 5B70 alloy is applied to a sealed cabin structure, and the high bearing and light weight level of the cabin structure is improved by improving the yield limit of materials.
Scandium of the 5B70 aluminum-magnesium-scandium alloy firstly reduces the grain size of the aluminum alloy to 20-30 mu m through obviously refining an as-cast structure; then uniformly precipitating A1 which is coherent with the Al matrix 3 Sc particles can produce precipitation strengthening; and A1 is distributed in a dispersed manner 3 The Sc particles can strongly pin the dislocation, prevent the alloy from recrystallization, and generate obvious substructure reinforcement.
In the spinning forming process of the 5B70 aluminum-magnesium-scandium alloy, the deformation is small, the forming temperature is high, crystal grains have a growing trend, dislocation has an annihilation trend, and the following problems exist: the strain strengthening and strain rate strengthening effects are weakened, and the yield strength and the tensile strength of the material are lost after the material is heated and spun and formed.
Disclosure of Invention
The invention solves the technical problems that: the high-performance spinning forming method for the large-thickness 5B70 sealed cabin body overcomes the defects of the prior art, effectively inhibits the degradation trend of materials, and keeps the higher mechanical property of the spinning piece.
The technical scheme of the invention is as follows:
a high-performance spin forming method of a large-thickness 5B70 sealed cabin body comprises the following steps:
(1) Obtaining a 5B70 plate to be spin-formed by rolling, and obtaining rolling parameters and mechanical property parameters of the plate;
(2) Determining a preheating temperature according to the rolling parameters and the mechanical property parameters of the plate, and uniformly preheating the plate by adopting the preheating temperature;
(3) And determining spinning processing temperatures corresponding to the areas according to the spinning deformation of the different areas of the plate, the rolling parameters and the mechanical property parameters of the plate, and carrying out spinning forming on the preheated plate.
Preferably, in the step (1), the rolling process of the 5B70 plate to be spin-formed includes sequentially performing hot rolling and temperature-controlled rolling on the 5B70 ingot, the hot rolling is performed above the recrystallization temperature of the plate, and the temperature-controlled rolling is performed to control the initial temperature and the final temperature of the rolling so as to ensure the mechanical properties of the plate.
Preferably, the yield strength of the 5B70 plate to be spin-formed obtained by rolling is 220MPa or more.
Preferably, in the step (1), the rolling parameter is the initial temperature T of the controlled temperature rolling of the plate 0 And the total deformation of the cast ingot in the temperature-controlled rolling process accounts for the percentage R% of the total deformation in the rolling process.
Preferably, in the step (1), the mechanical property parameter is the yield strength sigma of the 5B70 plate to be spin formed s 。
Preferably, in the step (2), the preheating temperature is determined according to the rolling parameters and the mechanical performance parameters of the plate, specifically:
when sigma is s T when the pressure is more than or equal to 260MPa t ＝T 0 -R/2；
When 220MPa is less than or equal to sigma s T is less than 260MPa t ＝250℃；
Wherein T is t Indicating the preheat temperature.
Preferably, in the step (3), the spinning temperature corresponding to each region is determined according to the deformation of different regions of the plate, specifically:
when the deformation amount of the region is equal to or less than a first threshold value:
T x ＝250℃；
when the deformation amount of the region is larger than the first threshold value and smaller than the second threshold value:
if sigma s ≥260MPa，T x ＝T 0 -R/2；
If 220MPa is less than or equal to sigma s ＜260MPa，T x ＝280℃；
When the deformation amount of the region is equal to or larger than a first threshold value:
if sigma s ≥260MPa，T x ＝T 0 -R/4；
If 220MPa is less than or equal to sigma s ＜260MPa，T x ＝330℃；
Wherein T is x The spin-forming temperature is indicated.
Preferably, the first threshold is 10% of the original size of the region, and the second threshold is 30% of the original size of the region.
Preferably, the initial temperature T of the temperature-controlled rolling 0 The value range of (2) is 150-350 ℃.
Preferably, the value range of R is 30 to 40.
Compared with the prior art, the invention has the advantages that:
aiming at the characteristic of strengthening the performance of the aluminum-magnesium-scandium alloy, the invention provides a high-performance retaining spinning forming method of the large-thickness 5B70 aluminum-magnesium-scandium alloy, which is characterized in that the preheating temperature of the spinning forming of the 5B70 plate is determined by analyzing the mechanical property and the rolling forming system of the 5B70 plate, and different spinning processing temperatures are adopted for different deformation areas, so that the degradation trend of the material is effectively restrained in the forming process, the higher mechanical property of a spinning piece is maintained, and the high-performance spinning forming of the large-scale integral 5B70 cabin structure can be realized.
Drawings
FIG. 1 is a schematic flow diagram of a high performance spin forming process for a large thickness 5B70 sealed capsule of the present invention;
FIG. 2 is a schematic view of typical mechanical properties of a spin-formed article according to an embodiment of the present invention;
FIG. 3 is a schematic view of fracture morphology of a spin-formed article according to an embodiment of the present invention;
FIG. 4 is a schematic representation of EBSD image and grain boundary data before annealing of a spin-formed article according to an embodiment of the present invention;
FIG. 5 is a schematic representation of EBSD image and grain boundary data after annealing of a spin-formed article according to an embodiment of the present invention.
Detailed Description
The features and advantages of the present invention will become more apparent and clear from the following detailed description of the invention.
The invention provides a high-performance spinning forming method of a large-thickness 5B70 sealed cabin, which is shown in figure 1 and comprises the following steps:
s1, obtaining a 5B70 plate to be spin-formed through rolling, and obtaining rolling parameters and mechanical property parameters of the plate;
specifically, the rolling process comprises the steps of sequentially carrying out hot rolling and temperature control rolling on a 5B70 cast ingot, wherein the hot rolling is carried out above the recrystallization temperature of the plate, and the temperature control rolling is used for controlling the initial temperature and the final temperature of the rolling so as to ensure the mechanical properties of the plate.
Further, the yield strength of the 5B70 plate to be spin-formed obtained by rolling is more than or equal to 220MPa.
Further, the rolling parameter is the initial temperature T of the temperature-controlled rolling of the plate 0 And the total deformation of the cast ingot in the temperature-controlled rolling process accounts for the percentage R of the total deformation in the rolling process; the mechanical property parameter is the yield strength sigma of the 5B70 plate to be spin formed s 。
In one embodiment, the initial temperature T of the controlled rolling 0 The value range of (2) is 150-350 ℃; r has a value ranging from 30 to 40.
S2, determining a preheating temperature according to the rolling parameters and the mechanical property parameters of the plate, and uniformly preheating the plate by adopting the preheating temperature;
in particular, when sigma s T when the pressure is more than or equal to 260MPa t ＝T 0 -R/2；
When 220MPa is less than or equal to sigma s T is less than 260MPa t ＝250℃；
Wherein, the liquid crystal display device comprises a liquid crystal display device,T t indicating the preheat temperature.
Further, in the preheating process, a position is arranged at intervals of 500mm along the spinning piece plate by a thermocouple, the surface temperature of the plate is detected, a hole is punched in the center, the position of the thermocouple is not smaller than 1 position, and the temperature of the plate at the 1/2 thickness position is monitored. After all thermocouples show temperature to reach preset temperature, the preheating of the plate is finished immediately.
S3, determining spinning processing temperatures corresponding to the areas according to spinning deformation of different areas of the plate, rolling parameters and mechanical property parameters of the plate, and carrying out spinning forming on the preheated plate.
Specifically, the deformation of each region of the plate in the spinning forming process is obtained through simulation.
When the deformation amount of the region is equal to or less than a first threshold value:
T x ＝250℃；
when the deformation amount of the region is larger than the first threshold value and smaller than the second threshold value:
if sigma s ≥260MPa，T x ＝T 0 -R/2；
If 220MPa is less than or equal to sigma s ＜260MPa，T x ＝280℃；
When the deformation amount of the region is equal to or larger than a first threshold value:
if sigma s ≥260MPa，T x ＝T 0 -R/4；
If 220MPa is less than or equal to sigma s ＜260MPa，T x ＝330℃；
Wherein T is x The spin-forming temperature is indicated.
Further, the first threshold is 10% of the original size of the region, and the second threshold is 30% of the original size of the region.
In one embodiment, the thickness is selected as the original dimension for deformation calculation.
In order to fully illustrate the rationality and reliability of the method of the invention, the following description is made of the process of investigation and analysis of the method of the invention:
firstly, according to the plate rolling process and the plate mechanical property, analyzing a main plate strengthening mechanism.
The production process flow of the plate production comprises ingot heating, hot rolling, temperature control rolling, unevenness detection, prestretching, sawing and detection.
The metallographic structure of the plate shows that the plate structure is a deformation zone structure which is uniformly distributed along the rolling direction, and the transmission microscopic structure analysis shows that a large number of dislocation in the deformation matrix are intertwined in the crystal boundary and the crystal grain to form a large number of dislocation wall interfaces, and the dislocation wall in the crystal grain divides the crystal grain into dislocation cell blocks with smaller sizes. Dislocations rearrange around the bulk of the cell to form a large number of small angle subgrain boundaries, a tissue morphology typical of materials with excellent mechanical properties.
In the production process of the plate, rolling is carried out in two sections, the first section is normally rolled, and the second section is subjected to temperature control rolling. The total rolling working rate of the second section is controlled within the range of 30% -40%. The production site needs to control the starting temperature and the ending temperature of the second section of rolling in a certain mode. Because the thickness of the plates is different, the total deformation from the ingot casting to the plates is different, and the temperature control rolling deformation is also changed. Then, since the flatness of each sheet of sheet is different in the production process, the tensile deformation amount in the room temperature leveling process actually adopted by the sheet is also different.
The finished plate with the thickness ranging from 30 mm to 70mm has tensile strength ranging from 375 MPa to 420MPa, yield strength ranging from 230 MPa to 290MPa and elongation ranging from 12% to 22% in the same direction, such as the transverse direction of the plate.
The mechanical properties of the 5B70 material can be improved to different degrees in the two working procedures of medium-temperature rolling and room-temperature leveling, but different processes have larger differences in the improvement range of the material properties and the influence of the performance stability after the subsequent spinning forming. Therefore, the mechanical properties of the material plates are different, or the properties of the plates with the same mechanical properties are different after spinning forming in the same process. And further, the spinning piece can not meet the requirement of the cabin body structure on high yield strength (the yield strength is more than or equal to 220 MPa) or the requirement of the whole cabin structure on performance uniformity (the overall mechanical property deviation of the spinning piece is less than or equal to 10%).
And the lightweight degree and the structural stability of the spacecraft cabin structure are ensured. The manufacturing process of the spinning blank used as the cabin body is required, firstly, the high yield strength of the material is required to be maintained so as to resist various force loads; and then the material to be regulated has uniform global performance, so that the whole structure is stable in stress and free from distortion.
In the forming process from the plate to the spinning piece, the cabin body is in a complex folded bus configuration, so that the deformation degree of materials at different bus heights is different.
Therefore, a spinning forming temperature system is established by analyzing the plate rolling process and the plate typical structure. Under the conditions of different mechanical properties and different performance stability of the plate, the spinning forming of different deformation amounts of each region is realized, and the high mechanical property and high performance uniformity targets of the spinning forming piece are realized by regulating and controlling the forming temperature, so that a performance foundation is laid for stable bearing of the cabin structure.
Actual operation procedure example:
the first step: and analyzing actual deformation parameters of plate rolling, wherein the actual deformation parameters comprise total deformation, medium-temperature rolling starting and medium-temperature rolling temperature and room-temperature leveling deformation.
And a second step of: taking the starting temperature of medium-temperature rolling as a temperature reference T 0 The method comprises the steps of carrying out a first treatment on the surface of the The medium-temperature rolling deformation is used as a performance estimation reference parameter, and the room-temperature leveling deformation is used as a performance instability factor parameter.
And a third step of: sampling at the plate body, at T 0 And (3) taking at least three groups of different temperatures at the temperature of +/-30 ℃ to completely anneal the plate. And then processing the test bar and testing the room temperature mechanical property.
Fourth step: for a typical cabin structure, T is adopted 1 The preform was pre-fabricated with a temperature reference and then subjected to total cross-sectional analysis. By T 0 Taking at least three groups of different temperatures at +/-30 ℃, and carrying out complete annealing on the sampled products. And then processing the test bar and testing the room temperature mechanical property. And testing the overall mechanical properties of spinning parts at different bus heights, and observing the typical tissue morphology of the spinning parts at different deformation amounts.
For example: performing a section analysis on a certain folded busbar spinning piece, and testing by T 1 Temperature-trial-produced spinning piece to avoidAnd (3) analyzing the mechanical properties of the whole domain mechanical properties after the same-temperature complete annealing, and summarizing the variation trend of the performance of the spinning piece along with different deformation amounts and different annealing temperatures. Typical results for a certain spun part are shown in fig. 2 (a) - (d), from which the following features can be summarized: (1) the intensity of the central zone is generally lower than that of the large mouth zone sample; (2) The strength of the transverse sample is slightly lower than that of the longitudinal sample, and the strength of the transverse sample in the central area is mostly lower than the standard value of 220 MPa; (3) The sample strength did not change with the change in annealing temperature with a corresponding change in regularity. With respect to the first point, this is in fact related to the amount of deformation of the sample. The thickness of the spinning member in the central region is thicker than that in the large-mouth region, which means that the deformation amount in the thickness direction is smaller, and the work hardening effect obtained in the hot spinning process is smaller, so that the strength of the central region is lower than that in the large-mouth region. Regarding the second point, because of the nature of the spin-forming deformation, the length of the original sheet material in the direction of the spin-formed arc (here, transverse) is reduced, i.e., there is some compression, which is detrimental to and maintains the integrity of the fibrous structure. In the direction of the spinning generatrix, the plate is elongated, namely the longitudinal stretching sample is stretched and deformed in the spinning process, and the deformation is more uniform. The strength of the longitudinal samples was slightly higher than that of the transverse samples, but the differences were not great. And superposing the difference between the central area and the large opening area in deformation, wherein the transverse sample in the central area is the position with the lowest global performance.
And there is no regular relation between the strength of the sample and the annealing temperature. It is explained that the decrease in mechanical properties is related to the local temperature being too high during the spinning deformation, which has caused a loss of mechanical properties. In the subsequent anneals, the highest annealing temperature is 350 ℃, which is likely to not reach the local maximum temperature during spinning. Since the local high temperature of the spinning process has caused softening of the material, the performance of the material is determined, and the subsequent annealing does not have a new effect on the performance. The strength of the sample does not change due to the difference in annealing temperature.
Fifth step: and analyzing fracture morphology of the test pieces with different typical mechanical properties.
Scanning electron microscope analysis is carried out on the fracture of the tensile sample, and the scanning electron microscope results are shown in fig. 3 (a) - (i), wherein: (a) not annealed; (b) annealing at 200 ℃; (c) 220 ℃ annealing; (d) 240 ℃ annealing; (e) annealing at 260 ℃; (f) annealing at 280 ℃; (g) 300 ℃ annealing; (h) 320 ℃ annealing; (i) 350 ℃ annealing;
when the fracture of the sample has fluctuation, the surface of the fracture is rough, and the inside of the fracture has tough pits with different depths, which indicates that the sample has better toughness and weak work hardening effect. The number of dimples as in fig. 3 (a) and 3 (e) is slightly greater than the other images. Consistent with the lower yield strength results of the two samples in the tensile data.
When the fracture finds a small amount of lamellar texture, this is characteristic of cleavage fracture. This sample was shown to work harden to a slightly higher degree than the other samples, but to a limited extent. As in fig. 3 (c), 3 (g), 3 (h) and 3 (i), it is possible to correspond to a slightly higher yield strength.
Similarly, if the whole fracture of the sample is smoother, the sample has a crystal-through fracture behavior, and the brittle component of fracture is higher. The morphology of the fracture indicated a higher level of work hardening in the sample. If the annealing temperature is increased, the number of ductile pits in the fracture increases, and the fracture becomes fluctuant, which means that the material eliminates certain work hardening after annealing at a higher temperature, and increases toughness.
Sixth step: analyzing the typical tissue morphology of the spinning piece.
Taking a sample taken in a spinning typical area as an example, the EBSD image and grain boundary data of the sample are shown in fig. 4 (a) and (d), wherein fig. 4 (a) and (b) are central area original samples, and fig. 4 (c) and (d) are large-mouth area original samples, and the whole crystal grain is in a prolate spindle shape. There are some fine recrystallized grains on the grain boundaries, and at the same time, a small amount of recrystallized grain nucleation can be seen inside the large grains. Fig. 4 (c) shows that most of the grain boundaries in this sample were small angle grain boundaries, and the average grain boundary angle was 9.15 °. The grains of the bulk sample were more elongated (fig. 4 (b)), indicating that the bulk sample was subjected to spinning with higher deformation than the center sample. Recrystallized grains appear at both grain boundaries and within the grains. It can be seen from fig. 4 (d) that the average grain boundary angle of the sample was 9.28 °, and a large number of grain boundaries remained as small angle grain boundaries. From the above results, it can be seen that the spun sample in both regions was partially recrystallized even without annealing, while the lower grain boundary angle indicated the presence of a large number of substructures in the grain, which is a result of dynamic recovery, indicating that the local temperature of spinning was too high.
The results of annealing the large-mouth region at 220 ℃ and 240 ℃ in the transverse direction are shown in fig. 5 (a) to (d), wherein fig. 5 (a) and (b) are the results of annealing the large-mouth region at 220 ℃ and fig. 5 (c) and (d) are the results of annealing the large-mouth region at 240 ℃ and are the whole EBSD morphology of the following two samples. The fiber grains of the large mouth area sample are more slender than the fiber grains of the central area sample, but the recrystallization degree is close. The average grain boundary angles for the two large mouth zone samples were 9.44 ° and 9.95 °, slightly higher than the original sample, but lower than the center zone annealed sample. This indicates that the deformed tissue of the set of samples is more than the central zone annealed samples. In addition, no significant rise in grain boundary angle was caused after annealing, indicating that no excessive threading dislocation was present in the sample and the deformed structure remained in the form of substructure.
Seventh step: and (5) comprehensively analyzing the conclusion of the full-section test piece.
The mechanical property result, the tensile fracture result and the EBSD crystal grain result are comprehensively analyzed. The following can be concluded: firstly, the scanned image of the fracture can basically correspond to the strength result of the sample, and although the fracture of different samples is not greatly different, the toughness difference of different samples can be basically judged according to the information such as the number of the ductile fossa, the size of the ductile fossa, the proportion of the ductile fossa, the smoothness of the fracture and the like. This difference can substantially correspond to the stretching results of the sample. That is, the samples with more ductile pits have more ductile components in fracture forms, the hardening effect is less retained, and the recrystallization degree of the material is higher.
Secondly, the EBSD result can obviously show that the deformation of the sample with longer fiber tissue is large, and the deformation of the sample is more due to the larger deformation, so that the deformation tissue in the sample is more, and the mechanical property is higher. From the grain boundary angle change of EBSD, it can be seen that the recrystallized structure in the sample varies with annealing temperature. When annealing does not have a great influence on the microstructure of the material, all the structures are very fine and the sizes are close, and the phenomenon that recrystallized grains grow is avoided, the fact that fine recrystallized grains are dynamic recrystallization results is indicated, the phenomenon that grain boundaries bow out and grow is caused by recrystallization caused by static annealing, and when no change is found, the fact that the actual deformation temperature of hot working is higher than the annealing temperature of a test piece is proved. The recrystallized structure in the sample is mainly formed in the spinning process, and the subsequent annealing only forms partial substructure without greatly influencing the grain structure. The difference in performance between samples at different annealing temperatures also did not change significantly from the annealing temperature. Otherwise, the actual deformation temperature of the spinning forming is lower than the annealing temperature.
Eighth step:
and then designing the preheating temperature of the spinning piece according to the rolling parameters, the organization and the dislocation conditions of the plate.
In the preheating process of the spinning piece, the work hardening generated by the room temperature leveling of most plates is eliminated, and when the preheating temperature is equal to the rolling starting temperature of the intermediate temperature rolling, the work hardening caused by partial intermediate temperature rolling is further eliminated. The larger the deformation amount of the intermediate-temperature rolling, the higher the elimination ratio. Therefore, the spinning preheating temperature is designed according to the actual medium-temperature rolling deformation and the actual measurement performance of each plate. The preheating temperature is selected according to the principle that the preheating temperature is increased as much as possible under the condition of a certain performance margin.
For example: the medium-temperature rolling starting temperature of a certain plate is 330 ℃, the medium-temperature rolling deformation amount accounts for 40% of the total deformation amount, the yield strength of the plate is 280MPa, and the preheating temperature of a spinning piece is 310 ℃. The partially unstable work hardening properties may be removed. And reserving certain toughness for spinning and forming the plate.
The medium-temperature rolling starting temperature of a certain plate is 330 ℃, the medium-temperature rolling deformation amount accounts for 40% of the total deformation amount, the yield strength of the plate is 240MPa, and the preheating temperature of the spinning piece is selected to be 250 ℃. At the moment, the mechanical properties of the plate are basically not reduced after the subsequent spinning processing.
Ninth step:
and finally, designing the spinning forming temperature, and finally ensuring that the spinning piece keeps higher mechanical property.
According to the data and analysis conclusion, the deformation quantity and the deformation speed required by the accurate forming of the size in the spinning process are combined, the corresponding phased deformation temperature parameter and the area with small deformation quantity can be formulated, the deformation temperature is reduced as much as possible, the dynamic recrystallization is prevented from being generated, the work hardening effect of the original plate is eliminated, the newly introduced deformation quantity is insufficient to offset the loss caused by the dynamic recrystallization at high temperature, and the strength of the material is reduced.
In the area with larger deformation, the spinning processing is carried out by adopting a temperature system similar to a medium-temperature rolling system, so that the original performance of the plate is kept, and meanwhile, the temperature is increased as much as possible, so that the deformation stability is ensured, and the cracking is avoided.
The invention provides a high-performance maintaining spinning forming method based on a plate rolling system, a plate structure and dislocation conditions, and effectively inhibits the degradation of the plate performance in the spinning forming process.
What is not described in detail in the present specification is a well known technology to those skilled in the art.

Claims (10)

1. The high-performance spinning forming method of the large-thickness 5B70 sealed cabin body is characterized by comprising the following steps of:
(1) Obtaining a 5B70 plate to be spin-formed by rolling, and obtaining rolling parameters and mechanical property parameters of the plate;
(2) Determining a preheating temperature according to the rolling parameters and the mechanical property parameters of the plate, and uniformly preheating the plate by adopting the preheating temperature;
(3) And determining spinning processing temperatures corresponding to the areas according to the spinning deformation of the different areas of the plate, the rolling parameters and the mechanical property parameters of the plate, and carrying out spinning forming on the preheated plate.
2. The method for forming a high-performance spin-on capsule with a large thickness 5B70 according to claim 1, wherein in the step (1), the rolling process of the 5B70 sheet to be spin-formed comprises sequentially hot-rolling and temperature-controlled rolling of the 5B70 ingot, the hot-rolling being performed above the recrystallization temperature of the sheet, and the temperature-controlled rolling being performed to control the initial temperature and the final temperature of the rolling so as to ensure the mechanical properties of the sheet.
3. The high-performance spinning forming method of the large-thickness 5B70 sealed cabin body according to claim 2, wherein the yield strength of the 5B70 plate to be spun formed obtained through rolling is more than or equal to 220MPa.
4. The method for high performance spin forming of a large thickness 5B70 sealed capsule according to claim 3, wherein in the step (1), the rolling parameter is the initial temperature T of the controlled temperature rolling of the sheet material 0 And the total deformation of the cast ingot in the temperature-controlled rolling process accounts for the percentage R% of the total deformation in the rolling process.
5. The method for high performance spin forming of a large thickness 5B70 sealed cabin according to claim 4, wherein in the step (1), the mechanical property parameter is the yield strength σ of the 5B70 plate to be spin formed s 。
6. The method for forming the high-performance spinning of the sealed cabin body with the large thickness 5B70 according to claim 5, wherein in the step (2), the preheating temperature is determined according to the rolling parameters and the mechanical property parameters of the plate, specifically:
when sigma is s T when the pressure is more than or equal to 260MPa t ＝T 0 -R/2；
When 220MPa is less than or equal to sigma s T is less than 260MPa t ＝250℃；
Wherein T is t Indicating the preheat temperature.
7. The method for forming a sealed cabin with high performance and high thickness 5B70 according to claim 6, wherein in the step (3), the spinning temperature corresponding to each region is determined according to the deformation of the different regions of the plate, specifically:
when the deformation amount of the region is equal to or less than a first threshold value:
T x ＝250℃；
when the deformation amount of the region is larger than the first threshold value and smaller than the second threshold value:
if sigma s ≥260MPa，T x ＝T 0 -R/2；
If 220MPa is less than or equal to sigma s ＜260MPa，T x ＝280℃；
When the deformation amount of the region is equal to or larger than a first threshold value:
if sigma s ≥260MPa，T x ＝T 0 -R/4；
If 220MPa is less than or equal to sigma s ＜260MPa，T x ＝330℃；
Wherein T is x The spin-forming temperature is indicated.
8. The high performance spin forming method of a high gauge 5B70 sealed capsule of claim 7, wherein the first threshold is 10% of the original size of the region and the second threshold is 30% of the original size of the region.
9. A high performance spin forming method of a large thickness 5B70 sealed capsule according to any of claims 2-8, wherein the temperature controlled rolling initiation temperature T 0 The value range of (2) is 150-350 ℃.
10. The high performance spin forming method of a large thickness 5B70 sealed capsule according to any one of claims 2 to 8, wherein R has a value in the range of 30 to 40.
CN202211634795.2A 2022-12-19 2022-12-19 High-performance spin forming method for large-thickness 5B70 sealed cabin Pending CN116159916A (en)

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN117531881A (en) * 2024-01-08 2024-02-09 四川省盛源鑫智能电气有限责任公司 Copper bar bending machine tool

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN117531881A (en) * 2024-01-08 2024-02-09 四川省盛源鑫智能电气有限责任公司 Copper bar bending machine tool
CN117531881B (en) * 2024-01-08 2024-04-26 四川省盛源鑫智能电气有限责任公司 Copper bar bending machine tool

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