CN113174500A - Method for improving O-state bending performance of 5083 alloy - Google Patents
Method for improving O-state bending performance of 5083 alloy Download PDFInfo
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Abstract
The invention belongs to the technical field of aluminum alloy, and particularly discloses a method for improving O-state bending performance of 5083 alloy, which comprises the following steps: adding the prepared raw materials into a smelting furnace for smelting, standing and refining, degassing, slagging off and filtering to obtain aluminum liquid, wherein the refining temperature is 730-2Per kg; casting aluminum liquid at the casting temperature of 710-720 ℃ and the casting speed of 45-55mm/min to form aluminum alloy ingots; carrying out homogenization heat treatment on the aluminum alloy cast ingot; after preheating, sequentially pass throughHot rough rolling for multiple passes and hot finish rolling for single pass are carried out to obtain a hot rolled blank with the thickness of 10.0-12.0 mm; cold rolling the hot rolled blank by adopting a large reduction ratio to obtain a cold rolled coil with the thickness of 3.0-5.0 mm; the 5083 alloy O-shaped plate prepared by the invention has 90-degree bending minimum relative bending radius of 0.5t, and the surface is uniform, smooth and fine after bending.
Description
Technical Field
The invention belongs to the technical field of aluminum alloy production, and particularly relates to a method for improving O-state bending performance of 5083 alloy.
Background
The 5083 aluminum alloy is a high-magnesium aluminum alloy, has good strength, corrosion resistance and machinability in non-heat-treatable alloys, has an attractive surface after anodization treatment and good arc welding performance, and is widely applied to marine applications such as ships, automobiles, aircraft weldments, subway light rails, pressure vessels requiring strict fire protection and the like.
The bending capability of an aluminum alloy plate during bending is usually measured by the minimum relative bending radius in aluminum processing, and the smaller the minimum relative bending radius is, the better the bending capability of the material is. When the material is bent, the outer layer is stretched and the inner layer is compressed on the fillet area, and when the thickness of the material is fixed, the smaller the inner r (the radius of the radian of the inner part in bending), the more serious the stretching and compression of the material are; when the tensile stress of the outer layer fillet exceeds the ultimate strength of the material, cracks or splits can develop. The structural design of the curved parts should therefore avoid excessively small curved fillet radii. When bent, the minimum relative bend radius refers to: the ratio of the minimum fillet radius to the blank thickness that the inner surface of the bending part can be bent under the condition of ensuring that the outer surface of the blank does not crack when being bent is expressed by rmin/t (t is the thickness). The smaller the value t, the better the bending performance of the plate. For example, a material with a minimum relative bend radius of 0.5t may have better bending capability than a material with a minimum relative bend radius of 1.5 t.
The existing standard for measuring the minimum relative bending radius of the bent aluminum alloy sheet has the following standard for the minimum relative bending radius of a 5083 aluminum alloy O-state sheet in GB/T3880.2-2012 (general industrial aluminum and aluminum alloy sheets and strip second part: mechanical property): when the thickness is 3.0-6.3mm, the minimum relative bending radius reaches 1.5t, and the product is qualified. However, in recent years, in actual production, the bending capabilities of a 5083 aluminum alloy plate material with a thickness of less than 3.0mm and a material with a thickness of more than 3.0mm are different, and when a bending die is replaced according to the thickness during bending, a thicker material can be prevented from cracking during bending, and if the same upper and lower bending dies are used for bending, the thicker 5083 material is liable to crack easily during bending. However, in actual bending, customers often pursue simplicity and convenience, and want to bend with the same bending die, so that the bending capability of a 5083 plate with the thickness of 3.0-5.0mm has a high requirement, otherwise, microcracks or cracks are easily generated during bending.
By analyzing the defects of a plurality of samples with 5083-0 state aluminum alloy bending cracking by using an OM optical microscope, an SEM scanning electron microscope and an EDS spectrometer, the following reasons for the 5083-O state aluminum alloy failure bending cracking are found: bending failure caused by nonmetal and metal inclusions, bending failure caused by coarse compounds, bending failure caused by coarse second phases, and bending failure caused by high performance due to incomplete recrystallization after annealing. The presence of any of the above-mentioned defects reduces the bending ability of the O-phase material of the 5083 aluminum alloy. In the past, how to obviously improve the bending capability of a 5083 aluminum alloy O-state material with the thickness of 3.0-5.0mm on the basis of national standards, particularly the minimum relative bending radius to 0.5t, is the research direction of technicians of aluminum processing enterprises.
Disclosure of Invention
Aiming at the defects of the prior art, the invention provides a method for improving the O-state bending performance of a 5083 alloy, and solves the problems in the background art.
A method for improving O-state bending performance of 5083 alloy comprises the following steps:
s1, preparing materials, namely preparing the following raw materials in percentage by weight for later use: si is less than or equal to 0.15 percent, Fe is less than or equal to 0.15 percent, Cu is less than or equal to 0.05 percent, Mn is 0.40 to 0.50 percent, Mg is 4.1 to 4.3 percent, Zn is less than or equal to 0.05 percent, Cr is 0.05 to 0.08 percent, Ti is less than or equal to 0.05 percent, other single impurities are less than 0.05 percent, the total amount of the impurities is less than 0.15 percent, and the balance is Al;
s2, smelting and refining, wherein the raw material prepared in the step S1 is added into a smelting furnace for smelting, then the molten aluminum is obtained after standing refining, degassing, slag skimming and filtering, the refining temperature is 730-2/kg；
S3, casting ingots, namely casting the aluminum liquid obtained in the step S2 into aluminum alloy ingots at the casting temperature of 710-720 ℃ and the casting speed of 55 +/-3 mm/min;
s4, carrying out homogenization heat treatment, cutting off the head and the tail of the aluminum alloy ingot obtained in the step S3, and milling the surface to obtain a pretreated alloy ingot;
s5, hot rolling, namely sequentially carrying out multi-pass hot rough rolling and single-pass hot finish rolling on the preprocessed alloy ingot obtained in the step S4 to obtain a hot rolled blank with the thickness of 10.0-12.0mm, wherein the final hot rolling temperature is more than or equal to 320 ℃;
s6, cold rolling, namely, cold rolling the hot rolled blank obtained in the step S5 by adopting a high reduction rate to obtain a cold rolled coil with the thickness of 3.0-5.0mm, and controlling the total reduction rate of the cold rolling to be more than 50%;
s7, annealing, namely performing high-temperature rapid annealing on the cold-rolled coil obtained in the step S6 on a continuous annealing line, and keeping the temperature for 5-10min to obtain an aluminum alloy coil;
and S8, straightening and slitting the aluminum alloy coiled material obtained in the step S7 by transverse shearing to obtain a finished plate.
In the present invention, the temperature of the homogenization heat treatment in the step S4 is 520-530 ℃, and the time of the homogenization heat treatment is 24 h.
In the invention, in the step S5, the hot rough rolling is performed for 15 passes, the average rolling reduction is 42mm, and the thickness of the plate after the hot rough rolling is 20.0-24.0 mm.
In the present invention, in the step S5, the reduction ratio of the finish hot rolling is 50%.
In the present invention, the annealing temperature in the step S7 is 460-480 ℃.
Compared with the prior art, the invention has the following beneficial effects:
1. in the aspect of chemical composition optimization, the invention reduces the percentage content of Mn and Cr elements in national standard chemical compositions of 5083 aluminum alloy to lower limits (the ranges of Mn and Cr in the chemical compositions of 5083 aluminum alloy in GB/T3190-2020 are respectively 0.4-1.0 percent and 0.05-0.25 percent) by reducing the content of Mn and Cr, and the Al generated in casting is reduced with higher probability in chemical composition distribution ratio7Cr and Al6The amount of metal compounds such as Mn and the like produced, and the impurities Fe, Zn, Cu and the like in the ingot are reduced by melt purification, thereby reducing the impurity elementsThe influence of elements on the plasticity of the finished product aluminum alloy is beneficial to improving the bending performance of the finished product 5083 aluminum alloy;
2. in the casting process, the lower casting temperature means Al7Cr and Al6The Mn intermetallic compound has good thermodynamic growth conditions at the stage before the solidification of the aluminum liquid; at the same time, the casting speed is slow and Al is provided7Cr and Al6Sufficient growth time of the Mn compound; meanwhile, the redistribution of the solute is more obvious due to the low casting speed, and the solute elements which are locally enriched provide more sufficient forming conditions; therefore, casting is controlled and prevented with 5083 alloy Al7Cr and Al6The generation of Mn intermetallic compound requires strict control of temperature range, so that the whole solidification process can rapidly pass through Al7Cr and Al6A temperature interval for the formation of the Mn compound; the invention effectively controls Al by controlling the casting temperature and improving the casting speed7Cr and Al6Generation of Mn intermetallic compounds; wherein Al is avoided by controlling the casting temperature7Cr and Al6Mn intermetallic compound grows before the solidification of aluminum liquid, so as to achieve the purposes of casting and reducing Al7Cr and Al6The purpose of the Mn intermetallic compound;
3. according to the invention, through homogenization heat treatment, microsegregation of an ingot structure is eliminated to the maximum extent, the uniformity of the ingot structure and the grain refinement effect are ensured, and after the homogenization heat treatment, a second phase is dispersed and precipitated in a matrix; the key point of the homogenization heat treatment is that the size of the second phase compound in the matrix is changed, the second phase in the ingot is subjected to high-temperature homogenization and heat preservation for 24 hours, the average size of the second phase compound after the homogenization heat treatment is less than 10 micrometers and almost less than 20 micrometers, and the cutting effect of coarse compounds on the matrix during bending in the later period is reduced, so that the bending cracking caused by stress concentration at the bending part due to the coarse compounds is avoided.
4. In the hot rolling process, a large-pass reduction process is adopted, so that the core of the hot rolled plate can be uniformly deformed, the coarse second phase can be fully crushed, and the coarse second phase of the core of the aluminum alloy blank can be fully crushed through the subsequent single-pass 50% large reduction rate finish rolling; in the cold rolling process, the total processing rate from the hot rolling blank to the cold rolling finished plate is more than 50 percent, which is beneficial to the grain refinement after recrystallization annealing;
5. in the recrystallization annealing process, the yield ratio of the O-state 5083 aluminum alloy plate is effectively reduced and the strain hardening index of the material is improved by a rapid high-temperature annealing mode; on the other hand, the problem of 'non-back-out' caused by lower annealing temperature is avoided, so that the bending capability is low.
In a word, the invention effectively improves the bending property of 5083 aluminum alloy in an O state by controlling the existence of intermetallic compounds Al7Cr and Al6Mn in the ingot, thinning coarse second phases and grains of the aluminum alloy plate, reducing the yield ratio in the mechanical property of the material and the like, realizes the requirement that 90-degree bending of a 5083 aluminum alloy O-state plate with the thickness of 3.0-5.0mm reaches the minimum bending radius of 0.5t, and ensures that the bent surface of a finished plate is uniform, fine, free of crack characteristics and smooth.
Detailed Description
The technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all of the embodiments.
Example 1
A method for improving O-state bending performance of 5083 alloy is characterized by comprising the following steps:
s1, preparing materials, namely preparing the following raw materials in percentage by weight for later use: si is less than or equal to 0.15 percent, Fe is less than or equal to 0.15 percent, Cu is less than or equal to 0.05 percent, Mn is 0.40 percent, Mg is 4.3 percent, Zn is less than or equal to 0.05 percent, Cr is 0.05 percent, Ti is less than or equal to 0.05 percent, other single impurities are less than 0.05 percent, the total amount of the impurities is less than 0.15 percent, and the balance is Al;
s2, smelting and refining, wherein the raw materials prepared in the step S1 are added into a smelting furnace to be smelted, then the smelted raw materials are subjected to standing refining, degassing, slag skimming and filtering to obtain molten aluminum, the refining temperature is 730 ℃, the online purification treatment requires that the hydrogen content measured by a launder after degassing is less than or equal to 0.1mL/100gAl, and the inclusion content of the melt of the online launder is less than 0.04mm2/kg；
S3, casting ingots, namely casting the aluminum liquid obtained in the step S2 into aluminum alloy ingots at the casting temperature of 710 ℃ and the casting speed of 55 +/-3 mm/min;
s4, carrying out homogenization heat treatment, cutting off the head and the tail of the aluminum alloy ingot obtained in the step S3 after the homogenization heat treatment, and milling the surface to obtain a pretreated alloy ingot, wherein the temperature of the homogenization heat treatment is 530 ℃, and the time of the homogenization heat treatment is 24 hours;
s5, hot rolling, namely preheating the pretreated alloy ingot obtained in the step S4, then carrying out 15-pass hot rough rolling to obtain a plate with the thickness of 20.0mm, wherein the average reduction is 42mm, then carrying out single-pass hot finish rolling to obtain a hot rolled blank with the thickness of 10.0mm, wherein the hot rolling final temperature is more than or equal to 320 ℃, and the reduction rate of the hot finish rolling is 50%;
s6, cold rolling, namely, cold rolling the hot rolled blank obtained in the step S5 to a cold rolled coil with the thickness of 3.0mm by adopting a large reduction rate;
s7, annealing, namely, performing high-temperature rapid annealing on the cold-rolled coil obtained in the step S6 on a continuous annealing line, wherein the heat preservation time is 10min, so as to obtain an aluminum alloy coil, and the annealing temperature is 460 ℃;
and S8, straightening and slitting the aluminum alloy plate coil obtained in the step S7 through cross shearing to obtain a finished plate.
Example 2
A method for improving O-state bending performance of 5083 alloy is characterized by comprising the following steps:
s1, preparing materials, namely preparing the following raw materials in percentage by weight for later use: si is less than or equal to 0.15 percent, Fe is less than or equal to 0.15 percent, Cu is less than or equal to 0.05 percent, Mn is 0.50 percent, Mg is 4.1 percent, Zn is less than or equal to 0.05 percent, Cr is 0.08 percent, Ti is less than or equal to 0.05 percent, other single impurities are less than 0.05 percent, the total amount of the impurities is less than 0.15 percent, and the balance is Al;
s2, smelting and refining, wherein the raw materials prepared in the step S1 are added into a smelting furnace to be smelted, then the smelted raw materials are subjected to standing refining, degassing, slag skimming and filtering to obtain molten aluminum, the refining temperature is 740 ℃, the online purification treatment requires that the hydrogen content measured by a launder after degassing is less than or equal to 0.1mL/100gAl, and the inclusion content of the melt of the online launder is less than 0.04mm2/kg；
S3, casting ingots, namely casting the molten aluminum obtained in the step S2 into aluminum alloy ingots at the casting temperature of 720 ℃ and the casting speed of 55 +/-3 mm/min;
s4, carrying out homogenization heat treatment, namely cutting off the head and the tail of the aluminum alloy cast ingot obtained in the step S3 after the homogenization heat treatment, and milling the surface to obtain a pretreated alloy ingot, wherein the temperature of the homogenization heat treatment is 520 ℃, and the time of the homogenization heat treatment is 24 hours;
s5, hot rolling, namely preheating the pretreated alloy ingot obtained in the step S4, then carrying out 15-pass hot rough rolling to obtain a plate with the thickness of 24.0mm, wherein the average reduction is 42mm, then carrying out single-pass hot finish rolling to obtain a hot rolled blank with the thickness of 12.0mm, wherein the hot rolling final temperature is more than or equal to 320 ℃, and the reduction rate of the hot finish rolling is 50%;
s6, cold rolling, namely, cold rolling the hot rolled blank obtained in the step S5 to a cold rolled coil with the thickness of 5.0mm by adopting a large reduction ratio;
s7, annealing, namely, performing high-temperature rapid annealing on the cold-rolled coil obtained in the step S6 on a continuous annealing line, wherein the heat preservation time is 5-10min, so as to obtain an aluminum alloy plate, and the annealing temperature is 480 ℃;
s8, straightening and slitting the aluminum alloy plate obtained in the step S7 by transverse shearing to obtain a finished plate,
example 3
A method for improving O-state bending performance of 5083 alloy is characterized by comprising the following steps:
s1, preparing materials, namely preparing the following raw materials in percentage by weight for later use: si is less than or equal to 0.15 percent, Fe is less than or equal to 0.15 percent, Cu is less than or equal to 0.05 percent, Mn is 0.45 percent, Mg is 4.2 percent, Zn is less than or equal to 0.05 percent, Cr is 0.06 percent, Ti is less than or equal to 0.05 percent, other single impurities are less than 0.05 percent, the total amount of the impurities is less than 0.15 percent, and the balance is Al;
s2, smelting and refining, namely adding the raw materials prepared in the step S1 into a smelting furnace for smelting, standing and refining, degassing, slagging off and filtering to obtain molten aluminum, wherein the refining temperature is 735 ℃, the hydrogen content measured by a launder is controlled to be less than or equal to 0.1mL/100gAl in the degassing process, and the impurity content in the launder is controlled to be less than 0.04mm2/kg；
S3, casting ingots, namely casting the aluminum liquid obtained in the step S2 into aluminum alloy ingots at the casting temperature of 735 ℃ and the casting speed of 55 +/-3 mm/min;
s4, carrying out homogenization heat treatment, namely cutting off the head and the tail of the aluminum alloy cast ingot obtained in the step S3 after the homogenization heat treatment, and milling the surface to obtain a pretreated alloy ingot, wherein the temperature of the homogenization heat treatment is 525 ℃, and the time of the homogenization heat treatment is 24 hours;
s5, hot rolling, namely preheating the pretreated alloy ingot obtained in the step S4, then carrying out 15-pass hot rough rolling to obtain a plate with the thickness of 23.0mm, wherein the average reduction is 42mm, then carrying out single-pass hot finish rolling to obtain a hot rolled blank with the thickness of 11.5mm, wherein the hot rolling final temperature is more than or equal to 320 ℃, and the reduction rate of the hot finish rolling is 50%;
s6, cold rolling, namely, cold rolling the hot rolled blank obtained in the step S5 to a cold rolled coil with the thickness of 4.0mm by adopting a large reduction rate;
s7, annealing, namely, performing high-temperature rapid annealing on the cold-rolled plate obtained in the step S6 on a continuous annealing line, wherein the heat preservation time is 5-10min, so as to obtain an aluminum alloy plate, and the annealing temperature is 470 ℃;
and S8, straightening and slitting the aluminum alloy coiled material obtained in the step S7 by transverse shearing to obtain a finished plate.
Comparative tests, wherein the following example is based on example 1, four comparative examples are respectively provided on the basis of example 1, and the four comparative examples are respectively compared with the mechanical property and the bending property of a finished plate prepared when the contents of Fe, Mn and Cr, the casting temperature, the annealing temperature and the homogenization heat treatment temperature are changed;
comparative example 1
Comparative example 1 is an embodiment based on example 1, and comparative example 1 is different from example 1 in the content of Fe, Mn, and Cr in step S1, specifically, 0.30% of Fe, 0.80% of Mn, and 0.15% of Cr, and the remaining process parameters are the same.
Comparative example 2
Comparative example 2 is an embodiment based on example 1, and comparative example 2 is different from example 1 in that the casting temperature of the molten aluminum in step S3 is 680 ℃, and the rest of the process parameters are the same.
Comparative example 3
Comparative example 3 is an embodiment based on example 1, and comparative example 3 is different from example 1 in that the annealing temperature is 340 ℃ in step S7, and the remaining process parameters are the same.
Comparative example 4
Comparative example 4 is an embodiment based on example 1, and comparative example 4 is different from example 1 in that the homogenization heat treatment temperature of step S4 is 450 ℃, and the remaining process parameters are the same.
The mechanical properties and bending properties of the finished plates prepared in the foregoing examples 1 to 3 and comparative examples 1 to 3 were tested, and the test results are shown in the following table:
the experimental data show that:
as can be seen from the comparative example 1, when the contents of Mn, Cr and Fe in the 5083 aluminum alloy are higher, the tensile strength and the yield strength of the material are higher after the same annealing, the elongation rate and the strain hardening index representing plasticity are reduced, the yield ratio of the material is higher, and the minimum bending is cracked at 0.5t when the material is bent at 90 degrees;
comparative example 2 shows that the mechanical properties of the material are not substantially different from those of example 1, all parameters are basically consistent, but flaw detection inspection is carried out on a low-casting-temperature cast ingot, a 5083 cast ingot with a low casting temperature cannot reach the A-grade standard, more impurities of Mn and Cr compounds are found, the material shows microcracks after 90-0.5 t bending, and the stress concentration caused by the impurities of the Mn and Cr compounds is analyzed;
as can be seen from the comparative example 3, when the annealing temperature is lower, the yield ratio is larger no matter the tensile strength or the yield strength is higher, the plasticity is lower, so that the bending cracking is caused after the bending of 90 degrees to 0.5 t;
as can be seen from comparative example 4, when the homogenization heat treatment temperature is lower, the yield strength of 5083 after annealing is higher, and the plasticity is properly lowered.
SEM scanning electron microscope analysis comparison of the ingot prepared in the example 4 at the homogenization heat treatment temperature of 450 ℃ and the homogenization heat treatment temperature of 520 ℃ and 530 ℃ provided by the invention shows that the second phase has the following characteristics:
from the above table of the effect of different homogenization heat treatment processes on the size of the 5083 ingot second phase, comparative example 4, which had two side effects, had a larger internal second phase after homogenization heat treatment at 450 ℃: on one hand, the cutting effect is exerted on the continuity of the matrix, namely, the larger second phase is easy to break the continuity of the matrix when deformed; on the other hand, stress concentration tends to occur in a large second phase during bending, and microcracks tend to occur.
In summary, the comprehensive performance and analysis of the examples and comparative examples show that the method for preparing the 5083 alloy plate with the thickness of 3.0-5.0mm in the O state by the invention completely avoids the reasons of the final material through a series of processes such as component optimization, smelting refining purification treatment, casting temperature and speed control, high-temperature lengthening time homogenization heat treatment, high-reduction rough rolling, high-machining-rate hot finish rolling, cold rolling with the total cold rolling processing rate of more than 50%, high-temperature short-time rapid annealing and the like: bending failure caused by nonmetal and metal inclusions, bending failure caused by coarse compounds, bending failure caused by coarse second phases, bending failure caused by incomplete recrystallization after annealing, and other potential bending failure factors, and the bending capability of the 5083 aluminum alloy O-state plate is well improved.
The above description is only for the preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art should be considered to be within the technical scope of the present invention, and the technical solutions and the inventive concepts thereof according to the present invention should be equivalent or changed within the scope of the present invention.
Claims (5)
1. A method for improving O-state bending performance of 5083 alloy is characterized by comprising the following steps:
s1, preparing materials, namely preparing the following raw materials in percentage by weight for later use: si is less than or equal to 0.15 percent, Fe is less than or equal to 0.15 percent, Cu is less than or equal to 0.05 percent, Mn is 0.40 to 0.50 percent, Mg is 4.1 to 4.3 percent, Zn is less than or equal to 0.05 percent, Cr is 0.05 to 0.08 percent, Ti is less than or equal to 0.05 percent, other single impurities are less than 0.05 percent, the total amount of the impurities is less than 0.15 percent, and the balance is Al;
s2, smelting and refining, wherein the raw material prepared in the step S1 is added into a smelting furnace for smelting, then the molten aluminum is obtained after standing and refining, degassing, slag skimming and filtering, the refining temperature is 730-2/kg；
S3, casting ingots, namely casting the aluminum liquid obtained in the step S2 at the casting temperature of 710-720 ℃ and the casting speed of 55 +/-3 mm/min to form aluminum alloy ingots;
s4, carrying out homogenization heat treatment, cutting off the head and the tail of the aluminum alloy ingot obtained in the step S3, and milling the surface to obtain a pretreated alloy ingot;
s5, hot rolling, namely preheating the pretreated alloy ingot obtained in the step S4, and then sequentially carrying out multi-pass hot rough rolling and single-pass hot finish rolling to obtain a hot rolled blank with the thickness of 10.0-12.0mm, wherein the final hot rolling temperature is more than or equal to 320 ℃;
s6, cold rolling, namely, cold rolling the hot rolled blank obtained in the step S5 by adopting a high reduction rate to obtain a cold rolled coil with the thickness of 3.0-5.0mm, and controlling the total reduction rate of the cold rolling to be more than 50%;
s7, annealing, namely performing high-temperature rapid annealing on the cold-rolled coil obtained in the step S6 on a continuous annealing line, and keeping the temperature for 5-10min to obtain an aluminum alloy coil;
and S8, straightening and slitting the aluminum alloy coiled material obtained in the step S7 by transverse shearing to obtain a finished plate.
2. The method of improving the O-temper bending performance of a 5083 alloy of claim 1, wherein: the temperature of the homogenization heat treatment in the step S4 is 520-530 ℃, and the heat preservation time of the homogenization heat treatment is 24 h.
3. The method of improving the O-temper bending performance of a 5083 alloy of claim 1, wherein: in the step S5, the hot rough rolling is performed for 15 passes, the average rolling reduction is 42mm, and the thickness of the plate after the hot rough rolling is 20.0-24.0 mm.
4. The method of improving the O-temper bending performance of a 5083 alloy of claim 3, wherein: in step S5, the hot finish rolling has a single pass reduction of 50%.
5. The method of improving the O-temper bending performance of a 5083 alloy of claim 1, wherein: the annealing temperature in the step S7 is 460-480 ℃.
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Cited By (4)
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| CN113862498A (en) * | 2021-08-19 | 2021-12-31 | 河南泰鸿新材料有限公司 | High-strength aluminum plate for cargo vehicle oil tank and production method thereof |
| CN114182117A (en) * | 2021-12-09 | 2022-03-15 | 东北轻合金有限责任公司 | Manufacturing method of hot-rolled 5083 aluminum alloy O-state plate |
| CN114457265A (en) * | 2022-01-28 | 2022-05-10 | 河南明晟新材料科技有限公司 | High-strength high-fatigue-performance 6-series aluminum alloy, gas cylinder and preparation method of gas cylinder |
| CN115747535A (en) * | 2022-09-07 | 2023-03-07 | 河南明晟新材料科技有限公司 | Manufacturing method for improving edge covering performance of 6016 automobile stamping plate |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113862498A (en) * | 2021-08-19 | 2021-12-31 | 河南泰鸿新材料有限公司 | High-strength aluminum plate for cargo vehicle oil tank and production method thereof |
| CN114182117A (en) * | 2021-12-09 | 2022-03-15 | 东北轻合金有限责任公司 | Manufacturing method of hot-rolled 5083 aluminum alloy O-state plate |
| CN114182117B (en) * | 2021-12-09 | 2022-08-26 | 东北轻合金有限责任公司 | Manufacturing method of hot-rolled 5083 aluminum alloy O-state plate |
| CN114457265A (en) * | 2022-01-28 | 2022-05-10 | 河南明晟新材料科技有限公司 | High-strength high-fatigue-performance 6-series aluminum alloy, gas cylinder and preparation method of gas cylinder |
| CN115747535A (en) * | 2022-09-07 | 2023-03-07 | 河南明晟新材料科技有限公司 | Manufacturing method for improving edge covering performance of 6016 automobile stamping plate |
| CN115747535B (en) * | 2022-09-07 | 2023-10-03 | 河南明晟新材料科技有限公司 | Manufacturing method for improving edge covering performance of 6016 automobile stamping plate |
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