CN114700366B - Al-Mg alloy thin plate and rolling method for reducing earing rate of Al-Mg alloy thin plate - Google Patents
Al-Mg alloy thin plate and rolling method for reducing earing rate of Al-Mg alloy thin plate Download PDFInfo
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- CN114700366B CN114700366B CN202210632213.0A CN202210632213A CN114700366B CN 114700366 B CN114700366 B CN 114700366B CN 202210632213 A CN202210632213 A CN 202210632213A CN 114700366 B CN114700366 B CN 114700366B
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- 239000000956 alloy Substances 0.000 title claims abstract description 68
- 238000000034 method Methods 0.000 title claims abstract description 62
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 60
- 238000005096 rolling process Methods 0.000 title claims abstract description 49
- 229910018134 Al-Mg Inorganic materials 0.000 title claims abstract description 46
- 229910018467 Al—Mg Inorganic materials 0.000 title claims abstract description 46
- 238000005097 cold rolling Methods 0.000 claims abstract description 52
- 238000005098 hot rolling Methods 0.000 claims abstract description 42
- 238000000137 annealing Methods 0.000 claims abstract description 32
- 230000008569 process Effects 0.000 claims abstract description 32
- 230000009467 reduction Effects 0.000 claims abstract description 26
- 238000001816 cooling Methods 0.000 claims description 13
- 238000012545 processing Methods 0.000 claims description 7
- 238000004519 manufacturing process Methods 0.000 abstract description 10
- 239000000047 product Substances 0.000 description 32
- 229910000838 Al alloy Inorganic materials 0.000 description 11
- 229910000861 Mg alloy Inorganic materials 0.000 description 11
- 239000000126 substance Substances 0.000 description 11
- 239000000203 mixture Substances 0.000 description 10
- 229910052782 aluminium Inorganic materials 0.000 description 9
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 9
- 239000011777 magnesium Substances 0.000 description 7
- 238000005266 casting Methods 0.000 description 6
- 239000000463 material Substances 0.000 description 6
- 230000003647 oxidation Effects 0.000 description 6
- 238000007254 oxidation reaction Methods 0.000 description 6
- 230000000052 comparative effect Effects 0.000 description 5
- 238000010438 heat treatment Methods 0.000 description 5
- 238000009749 continuous casting Methods 0.000 description 4
- 239000012535 impurity Substances 0.000 description 4
- 230000001276 controlling effect Effects 0.000 description 3
- 230000007547 defect Effects 0.000 description 3
- 230000004927 fusion Effects 0.000 description 3
- 238000003801 milling Methods 0.000 description 3
- 238000010899 nucleation Methods 0.000 description 3
- 230000006911 nucleation Effects 0.000 description 3
- 238000004321 preservation Methods 0.000 description 3
- 230000002829 reductive effect Effects 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 230000002401 inhibitory effect Effects 0.000 description 2
- 229910052749 magnesium Inorganic materials 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
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- 229910001234 light alloy Inorganic materials 0.000 description 1
- 230000000670 limiting effect Effects 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
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- 238000003672 processing method Methods 0.000 description 1
- 238000002310 reflectometry Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
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Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/56—Elongation control
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B2003/001—Aluminium or its alloys
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- Chemical & Material Sciences (AREA)
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- Mechanical Engineering (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Metal Rolling (AREA)
Abstract
The invention provides an Al-Mg alloy sheet and a rolling method for reducing the earing rate of the Al-Mg alloy sheet, wherein the rolling method comprises the following steps of: carrying out hot rolling and primary cold rolling treatment on the Al-Mg alloy cast ingot in sequence to obtain an Al-Mg alloy sheet; wherein the total rolling reduction rate of hot rolling is controlled to be more than or equal to 95 percent, the hot finishing rolling temperature of hot rolling is controlled to be 220 to 300 ℃, and the total rolling reduction rate of primary cold rolling is controlled to be more than or equal to 90 percent. The method of the invention can effectively solve the problem of high earing rate of the Al-Mg alloy sheet with higher purity, so that the product can have better surface performance, deep drawing performance and strength on the premise of keeping the earing rate lower. The method has strong applicability to production equipment, and the working procedures of hot rolling, cold rolling, annealing and the like in the process can adopt conventional production equipment without increasing equipment investment, so that the cost is lower and the universality is better.
Description
Technical Field
The invention relates to the field of aluminum alloy sheets, in particular to an Al-Mg alloy sheet and a rolling method for reducing the earing rate of the Al-Mg alloy sheet.
Background
In the industries of packaging, lighting, building, automobile, battery and the like, in order to ensure high surface property, high reflectivity and high finish of products and reduce the reduction of surface quality caused by the anodic oxidation process of alloy compound phases, the purity of the selected aluminum alloy material is generally higher and the impurity content is lower. Meanwhile, a large part of parts required by the industries are cylindrical deep-drawing parts, and are required to be manufactured by a deep-drawing process of multiple passes, so that the materials are required to have excellent deep-drawing performance. Moreover, under actual use conditions, the material is required to have high strength. Therefore, the performance requirements of such materials at present need to have high surface property, high deep drawing property and high strength. Generally, in order to ensure the surface performance of the aluminum material after anodic oxidation, the reduction of the content of impurity elements Fe and Si is a main means. Meanwhile, by adding solid solution element Mg and reasonably controlling the content of Mg, the strength of the alloy plate can be improved and the alloy plate still has excellent surface property.
The lug making in the deep drawing process of the aluminum alloy plate is closely related to the texture of the plate. The cubic texture caused the sheet to develop 4 lugs in the 0/90 orientation to the rolling direction after deep drawing, while the sheet with a strong rolling texture caused it to develop lugs in the approximately 45 orientation to the rolling direction. Moreover, it has been shown by research that the influence of alloy elements and contents on the texture is more complex, but the general trend is that the purer the alloy, i.e. the less impurities, the more easily the pure metal type rolling texture is formed, and the stronger the cubic texture after annealing is (reference: shenjian, zhang Xinming. Texture and anisotropy of aluminum sheet for deep drawing [ J ]. Light alloy processing technique, 1994, 22 (7): 27-33+ 40.).
How to reduce the earing rate of Al-Mg series alloy materials with higher purity is a technical problem, but at present, no processing method for the products is available. Patents CN200510009793, CN200810230639, CN201210502214, CN201711126422, CN201880061110, CN201911316096, CN202010233523, CN202110253793 and the like all disclose methods for controlling the earing ratio of aluminum alloy sheets, but all the methods are directed to alloy products containing higher elements such as Mn, cu, cr, fe and the like. However, it has been found that if there are a large amount of other solid solution elements such as Mg, mn and Cu in the matrix of the aluminum alloy material, the matrix will show a completely different structure property evolution law from that of high purity aluminum (refer to R. Kalsar, R. Madhavan, R.K. Ray, S. Suwa. Texture transformation in Al-Mg alloys: effect of magnesium [ J ]. Photocosmetic Magazine, 2020, 100 (16): 2143-2164.). Therefore, it is necessary to provide a new rolling method for a high-purity Al — Mg alloy material, which can provide a product with a lower earing ratio.
Disclosure of Invention
Al-Mg alloys are a class of non-heat treatable strengthened aluminum alloys. In order to control the deep drawing performance of the product and the surface quality after anodic oxidation, the sheet products are generally supplied in the states of O, H1X, H2X, H3X and the like (refer to GB/T16475-2008 deformed aluminum and aluminum alloy state codes).
In the aluminum processing industry, al-Mg alloy sheet products generally have two process routes, one is an ingot casting-hot rolling process route, and the other is a continuous casting-cold rolling process route. The casting ingot-hot rolling process is used for producing Al-Mg alloy casting ingots by semi-continuous casting, and then producing Al-Mg alloy sheets by homogenizing heat treatment, hot rolling, cold rolling, annealing and other processes.
The chemical components of the Al-Mg alloy have important influence on the subsequent processing technology, and Al-Mg alloy sheet products with different chemical components need to adopt different production process routes. The present inventors have found that, for a higher purity Al — Mg alloy material, for example, the following Al — Mg alloys: the alloy material is characterized by taking Mg as a main alloy element, wherein the content of Mg is lower and is only 0 to 6wt%, and the alloy material also comprises alloy elements such as Mn, cu, cr, zn, ti and the like, the content of the alloy elements is lower and is only 0 to 0.3wt%, and inevitable trace impurity elements such as Fe, si and the like. The Al-Mg series alloy has less second phase particles, and grains which are nucleated and grow by a PSN mechanism in the recrystallization process tend to form random textures, so when the material is processed into a thin plate by a rolling process, a very strong cubic texture is easy to form in the subsequent annealing process. The strong cubic texture formed during this annealing process is the root cause for the 0/90 earing. Furthermore, in the case of a high-purity Al — Mg alloy, the cubic texture is difficult to weaken in the subsequent cold working process, which results in a high earing ratio in the 0 °/90 ° direction of the product, generally 5% or more, and sometimes even more than 10%, when producing such products in the H1X, H2X, and H3X state (see GB/T16475-2008 wrought aluminum and aluminum alloy state codes). Such higher earing products can result in higher scrap rates for downstream customers in subsequent parts manufacturing, thereby significantly reducing the market competitiveness of such products.
Further, the present invention is directed to an Al — Mg alloy thin plate and a rolling method for reducing the earing rate of the Al — Mg alloy thin plate, which solve the problem of high earing rate after rolling of a high-purity Al — Mg alloy material in the prior art. In order to achieve the above object, according to one aspect of the present invention, there is provided a rolling method for reducing a earing ratio of an Al — Mg-based alloy thin plate, the rolling method including the steps of: carrying out hot rolling and primary cold rolling treatment on the Al-Mg alloy cast ingot in sequence to obtain an Al-Mg alloy sheet; wherein the total rolling reduction rate of hot rolling is controlled to be more than or equal to 95 percent, the hot finishing rolling temperature of hot rolling is controlled to be 220 to 300 ℃, and the total rolling reduction rate of primary cold rolling is controlled to be more than or equal to 90 percent.
Based on the method, the nucleation and growth of the cubic texture in the high-purity Al-Mg alloy sheet can be more effectively inhibited. The cold-rolled Al-Mg alloy sheet with a lower cubic texture proportion can be obtained after one-time cold rolling treatment. And the cold-rolled Al-Mg alloy sheet can still keep a lower cubic texture proportion in the subsequent annealing and other conventional processing processes, so that the proportion of the cubic textures of O-state and H1X-state sheet products can be more effectively inhibited, and the earing rate of the products can be more effectively reduced. Meanwhile, the defects of the product after anodic oxidation can be effectively avoided, so that the surface quality of the product is ensured.
The production process of the Al — Mg alloy sheet includes casting, homogenization heat treatment, hot rolling, cold rolling, intermediate annealing, and the like. In the prior art, the preparation of the Al-Mg alloy sheet can adopt an O state process, an H1X process, an H2X process or an H3X process. The process comprises the steps of hot rolling and primary cold rolling, and the invention mainly has the beneficial effects of effectively inhibiting the formation of cubic texture and reducing earing in the direction of 0 DEG/90 DEG by controlling the technological parameters of the hot rolling and the primary cold rolling in the process. The hot rolling total reduction rate is more than 95%, the hot finishing temperature is 220-300 ℃, the cold rolling total reduction rate is more than 90%, and the three conditions are none. Based on the cooperative action of the three parameters, the high-purity Al-Mg alloy sheet processed by the method can simultaneously take the excellent performances into consideration, the earing rate can be controlled below 3 percent, and the high-purity Al-Mg alloy sheet has excellent surface performance and high strength.
In a word, the rolling method can effectively solve the problem of high earing rate of the Al-Mg alloy sheet with higher purity, so that the product can also have better surface property, deep drawing property and strength on the premise of keeping the earing rate lower. Secondly, in the subsequent annealing process, the proportion of the cubic texture of the plate in an annealing state can still be kept at a lower level within a larger annealing temperature and time range, namely, the process window of the method is wider, and the performance of the produced product, particularly the stability of the earing rate is high. Thirdly, the method has strong applicability to production equipment, and the process equipment of hot rolling, cold rolling, annealing and the like involved in the process can adopt conventional production equipment without increasing equipment investment, so that the cost is lower and the universality is better.
Further, in a preferred embodiment, the invention is a hot rolling method of an Al-Mg alloy ingot with a thickness of 400 to 700mm, the open rolling temperature of the hot rolling is controlled to be 400 to 550 ℃, and the pass of the hot rolling is controlled to be 15 to 30. Based on the above, the Al-Mg alloy sheet can have better performance uniformity, so that the Al-Mg alloy sheet can have lower earing rate, better surface performance and higher strength.
Preferably, after hot rolling, the hot rolled coil after hot rolling is cooled to below 100 ℃ (preferably 20 to 25 ℃) and then subjected to cold rolling for the first time. The cooling can be natural cooling or forced cooling. Thus, the nucleation and growth of the cubic texture in the high-purity Al-Mg alloy thin plate can be further effectively inhibited. Therefore, on the basis of effectively reducing the earing rate of the product, the defect of the product after anodic oxidation can be more effectively avoided, and the surface quality of the product is ensured. More preferably, the number of passes in the first cold rolling process is controlled to be 4 to 10.
In a preferred embodiment, after the first cold rolling, the rolling method further includes: and sequentially carrying out intermediate annealing, secondary cold rolling and finished product annealing on the cold-rolled coil subjected to the primary cold rolling. For Al-Mg alloy with higher purity, the treatment temperature of intermediate annealing can be kept above the recrystallization temperature of the alloy, and is preferably controlled within the range of 300 to 360 ℃; the treatment time is controlled within the range of 0.5 to 6 h. Thus, the invention can obtain O-state products with the earing rate of less than 3 percent. Furthermore, after the intermediate annealing, the sample is subjected to secondary cold rolling, the reduction rate of the secondary cold rolling is kept between 15 and 50 percent, the number of rolling passes is 1 to 5, so that the H1X-state product is further obtained, and the earing rate is below 3 percent.
In order to achieve the above object, according to another aspect of the present invention, there is provided an Al — Mg alloy thin plate obtained by the rolling method for reducing the earing ratio of an Al — Mg alloy thin plate.
Based on the reasons, the invention creatively controls the operating parameters in the hot rolling and one-time cold rolling processes within the range, thereby more effectively inhibiting the nucleation and growth of the cubic texture in the Al-Mg series alloy sheet material with higher purity. Based on the method, the cold-rolled Al-Mg alloy sheet with lower cubic texture proportion can be obtained after one-time cold rolling treatment. And the cold-rolled Al-Mg alloy sheet can still keep a lower cubic texture proportion in the subsequent annealing and other processing processes, so that the proportion of the cubic textures of O-state and H1X-state sheet products can be more effectively inhibited, the composition proportion of each texture in the sheet can be more reasonably controlled, and the earing rate of the product can be more effectively reduced. Meanwhile, the defects generated after the anodic oxidation can be effectively avoided, so that the surface quality of the product is ensured.
Further, the present invention can obtain an Al-Mg alloy sheet having a earing ratio of 3% or less in an O state and an H1X state, and the product has both excellent surface properties and high strength.
Detailed Description
It should be noted that the embodiments and features of the embodiments in the present application may be combined with each other without conflict. The present invention will be described in detail with reference to examples.
The present application is described in further detail below with reference to specific examples, which should not be construed as limiting the scope of the invention as claimed.
And (4) performance testing: the invention relates to a method for testing the forming performance of a metal sheet according to GB/T15825.7-2008, part 7: the lug test detects the lug making rate of the sheet.
Example 1:5150-H12 Rolling production
Fusion casting and chemical composition control: adopting a DC semi-continuous casting mode to cast and form a 5150 alloy ingot with the thickness of 560mm, wherein the chemical composition of the ingot is controlled according to the standard of GB/T3190-2008 deformed aluminum and aluminum alloy chemical composition. The thickness of the cast ingot is changed to 520mm after the surface milling, and then the hot rolling process is carried out.
(II) hot rolling: and (3) carrying out heat preservation on the cast ingot at 530 ℃ for 12h, then starting hot rolling, and rolling the cast ingot into a hot rolled coil of 12mm by 22 passes, wherein the total hot rolling reduction rate is 97.7%, the initial rolling temperature is 450-500 ℃, and the hot final rolling temperature is controlled to be 260-270 ℃.
(III) cooling the hot-rolled coil: and (4) rolling the hot rolled coil, and naturally cooling to room temperature (20 to 25 ℃).
(IV) primary cold rolling: and cooling the hot-rolled coil to room temperature, and then carrying out cold rolling for 6 passes to obtain a cold-rolled coil with the thickness of 0.8mm, wherein the total cold-rolling reduction rate is 93.3%.
(V) intermediate annealing: annealing the cold-rolled coil for 7 to 12h at 330 ℃ in a box-type annealing furnace, wherein the heating time is 5 to 10h.
(VI) secondary cold rolling: the annealed sheet is subjected to cold rolling for 1 pass to be in an H12 state, the thickness of a finished product is 0.64mm, and the total reduction rate of the cold rolling is 20%.
The earing rate of the 5150-H12 thin plate with the thickness of 0.64mm produced by the process is 2.8 percent.
Comparative example 1:5150-H12 Rolling production
Fusion casting and chemical composition control: adopting a DC semi-continuous casting mode to cast and form a 5150 alloy ingot with the thickness of 560mm, wherein the chemical composition of the ingot is controlled according to the standard of GB/T3190-2008 deformed aluminum and aluminum alloy chemical composition. The thickness of the cast ingot is changed to 520mm after the surface milling, and then the cast ingot enters a hot rolling procedure.
(II) hot rolling: and (3) carrying out heat preservation on the cast ingot at 530 ℃ for 12h, then starting hot rolling, rolling the cast ingot into a hot rolled coil with the thickness of 12mm through 25 passes, wherein the total hot rolling reduction rate is 97.7%, and the hot finishing temperature is controlled to be 310-320 ℃.
(III) cooling the hot-rolled coil: and naturally cooling the hot-rolled coil to room temperature after rolling.
(IV) primary cold rolling: and cooling the hot-rolled coil to room temperature, and then carrying out cold rolling for 6 passes to obtain a cold-rolled coil with the thickness of 0.8mm, wherein the total cold-rolling reduction rate is 93.3%.
(V) intermediate annealing: and annealing the cold rolled coil for 7 to 12h at 330 ℃ by a box annealing furnace, wherein the heating time is 5 to 10h.
(VI) secondary cold rolling: the annealed sheet is subjected to cold rolling for 1 pass to be in an H12 state, the thickness of a finished product is 0.64mm, and the total reduction rate of the cold rolling is 20%.
The earing rate of the 5150-H12 thin plate with the thickness of 0.64mm produced by the process is more than 4 percent, and even reaches 8 percent. The process of comparative example 1 differs from example 1 in that the hot final rolling temperature of the hot rolling (II) is controlled at a higher temperature, and the microstructure of the hot rolled coil already contains a higher proportion of recrystallized grains, which increases the tendency of the sheet to form cubic texture during subsequent annealing, resulting in an increased earing ratio of the H12 temper product in the 0/90 direction.
Comparative example 2:5150-H12 Rolling production
Fusion casting and chemical composition control: adopting a DC semi-continuous casting mode to cast and form a 5150 alloy ingot with the thickness of 560mm, wherein the chemical composition of the ingot is controlled according to the standard of GB/T3190-2008 deformed aluminum and aluminum alloy chemical composition. The thickness of the cast ingot is changed to 520mm after the surface milling, and then the hot rolling process is carried out.
(II) hot rolling: and (3) carrying out heat preservation on the cast ingot at 530 ℃ for 12h, then starting hot rolling, rolling the cast ingot into a hot rolled coil with the thickness of 7.8 mm through 24 passes, wherein the total hot rolling reduction rate is 98.5%, and the hot finish rolling temperature is controlled to be 260-270 ℃.
(III) cooling the hot-rolled coil: and naturally cooling the hot-rolled coil to room temperature after rolling.
(IV) primary cold rolling: and cooling the hot-rolled coil to room temperature, and then carrying out cold rolling for 6 passes to obtain a cold-rolled coil with the thickness of 0.8mm, wherein the total cold-rolling reduction rate is 89.7%.
(V) intermediate annealing: and annealing the cold rolled coil for 7 to 12h at 330 ℃ by a box annealing furnace, wherein the heating time is 5 to 10h.
(VI) secondary cold rolling: the annealed plate is subjected to 1-pass cold rolling to be in an H14 state, the thickness of a finished product is 0.48mm, and the total cold rolling reduction rate is 40%.
The sheet of 5150-H12 with the thickness of 0.48mm produced by the process has the earing rate of more than 4 percent. The main process difference of comparative example 2 compared to example 1 is that the reduction ratios of (two) hot rolling, (four) primary cold rolling and (six) secondary cold rolling are different. Comparative example 2 increased the total rolling reduction and the total rolling reduction of the second cold rolling, while decreasing the total rolling reduction of the first cold rolling step before annealing. Under the condition of the process combination, the cubic texture proportion in the plate before annealing cannot be reduced to a certain limit, so that the cubic texture proportion is greatly increased after the (five) intermediate annealing, and even if the total reduction rate of the subsequent (six) secondary cold rolling is increased, the cubic texture proportion of the final product is still larger, so the earing rate is also higher.
The present invention has been described in terms of the preferred embodiment, and it is not intended to be limited to the embodiment. Any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention should be included in the protection scope of the present invention.
Claims (3)
1. A rolling method for reducing the earing rate of an Al-Mg alloy thin plate, which is characterized by comprising the following steps: carrying out hot rolling and primary cold rolling treatment on the Al-Mg alloy cast ingot in sequence to obtain the Al-Mg alloy sheet; wherein,
controlling the total rolling reduction rate of the hot rolling to be more than or equal to 97.7 percent, the hot finishing rolling temperature of the hot rolling to be 220-300 ℃, and the total rolling reduction rate of the primary cold rolling to be more than or equal to 93.3 percent;
after the hot rolling, cooling the hot rolled coil after the hot rolling to below 100 ℃ and then performing the primary cold rolling;
after the one cold rolling, the rolling method further includes: sequentially carrying out intermediate annealing, secondary cold rolling and finished product annealing on the cold-rolled coil subjected to the primary cold rolling, wherein in the intermediate annealing process, the processing temperature is 300-360 ℃, and the processing time is 0.5-6 h;
the Al-Mg alloy cast ingot is a 5150 alloy cast ingot;
the thickness of the Al-Mg alloy cast ingot is 400 to 700mm; the hot rolling temperature is 400-550 ℃, and the hot rolling pass is 15-30;
the earing rate of the Al-Mg alloy sheet is less than or equal to 3 percent.
2. The rolling method for reducing the earing of an Al-Mg alloy thin plate as set forth in claim 1, wherein the total reduction rate of the secondary cold rolling is controlled to be 15 to 50%.
3. An Al-Mg alloy thin plate obtained by the rolling method for reducing the earing ratio of an Al-Mg alloy thin plate according to claim 1 or 2.
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| CN114700366A (en) | 2022-07-05 |
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