CN111910111A - Preparation method of aluminum-magnesium-manganese-copper alloy plate for thinning and drawing can body - Google Patents
Preparation method of aluminum-magnesium-manganese-copper alloy plate for thinning and drawing can body Download PDFInfo
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Abstract
The invention belongs to the technical field of metal processing, and particularly relates to an aluminum-magnesium-manganese-copper alloy for an ironing can body and a preparation method of a plate thereof. The alloy comprises the following components in percentage by mass: 1.10 to 1.40 percent of Mg, 0.80 to 1.10 percent of Mn, 0.20 to 0.40 percent of Cu, 0.20 to 0.50 percent of Fe, 0.18 to 0.4 percent of Si, and the balance of Al and inevitable impurities. The preparation method of the aluminum alloy plate comprises the following steps: sequentially smelting, casting and milling the aluminum alloy to obtain an aluminum alloy ingot; carrying out two-stage homogenization heat treatment on the aluminum alloy cast ingot; carrying out hot rolling on the aluminum alloy cast ingot to obtain a hot rolled plate; and cold rolling the hot rolled plate to obtain the aluminum alloy plate. The strength and the elongation of the prepared plate are obviously improved, and the can manufacturing process of the thin can body with the thickness of less than 0.26mm can body can be met.
Description
Technical Field
The invention belongs to the technical field of metal processing, and particularly relates to an aluminum-magnesium-manganese-copper alloy for an ironing can body and a preparation method of a plate thereof.
Background
The 3XXX aluminum alloy sheet for the ironing can body is a raw material for manufacturing the ironing can body, and is a thin sheet having a thickness of 0.4mm or less. The white can body of the thinning and drawing can, namely the commonly known pop can, is formed by blanking and punching a cup, thinning and drawing for multiple times, punching and forming the bottom of the can, cleaning and baking. Since the can is a container for hermetically storing a liquid, the liquid such as carbonated beverage and beer stored therein contains carbon dioxide dissolved therein to form carbonic acid, and the carbonic acid is decomposed into carbon dioxide under vibration or increased temperature to increase the pressure in the can, and if the strength of the can body material is insufficient, the can body may be inverted or broken. Therefore, the aluminum alloy plate for the ironing can body has higher requirement on strength, and 3104 aluminum alloy is generally used at home and abroad. In addition, the can making process of the pop can comprises the steps of deep drawing, thinning and deep drawing and the like, the deformation amount is large, the deformation rate is high, the forming performance of the plate is extremely high, the forming performance of the plate is easily reduced by simply improving the strength of the plate, and the can making requirement cannot be met.
In order to reduce the amount of aluminum used for a single can and save cost, 3104 aluminum alloy plates for can bodies are always improved in strength, and then are thinned. At present, the thickness of 3104 aluminum alloy plates for can bodies, which are mainstream in China, is reduced to 0.265-0.27mm, and the yield strength also reaches 250 MPa. On the basis, the sheet material is continuously thinned, so that the sheet material strength is further improved, and the sheet material forming performance is improved. Therefore, the conventional sheet material for a can body cannot satisfy the can manufacturing requirements of the can body material of 0.26mm or less.
Disclosure of Invention
The invention aims to provide an aluminum-magnesium-manganese-copper alloy for a thin can body with reduced thickness, improved strength and higher forming capability and a preparation method of the sheet material, and solves the problem that the sheet material in the prior art cannot meet the can body material can making requirement below 0.26 mm.
In order to achieve the purpose, the invention adopts the following technical scheme:
an aluminum-magnesium-manganese-copper alloy plate for an ironing can body comprises the following components in percentage by mass: 1.10 to 1.40 percent of Mg, 0.80 to 1.10 percent of Mn, 0.20 to 0.40 percent of Cu, 0.20 to 0.50 percent of Fe, 0.18 to 0.4 percent of Si, and the balance of Al and inevitable impurities.
The preparation method of the aluminum-magnesium-manganese-copper alloy plate for the reduction drawing of the can body comprises the following steps:
step S1, sequentially smelting, casting and milling the aluminum alloy to obtain an aluminum alloy ingot;
step S2, carrying out two-stage homogenization heat treatment on the aluminum alloy ingot; the treatment temperature of the first-stage homogenization heat treatment is 550-610 ℃, and the treatment time is 4-12 h; the treatment temperature of the second-stage homogenization heat treatment is 500-540 ℃, and the treatment time is 12-36 h;
step S3, carrying out hot rolling on the aluminum alloy cast ingot subjected to the two-stage homogenization heat treatment to obtain a hot rolled plate, wherein the hot rolling finishing temperature is 330-360 ℃, and the thickness of the hot rolled plate is 1.8-2.2 mm;
step S4, cold rolling the hot rolled plate to obtain the aluminum alloy plate, wherein the cold rolling times of the hot rolled plate are 4-6 times, the reduction of each time is 30-45%, the total cold rolling rate of the hot rolled plate is 88-90%, and the final cold rolling temperature is 120-180 ℃.
Further, the aluminum alloy comprises the following components in percentage by mass: 1.29 to 1.40 percent of Mg, 0.93 to 1.10 percent of Mn, 0.26 to 0.40 percent of Cu, 0.20 to 0.34 percent of Fe, 0.31 to 0.4 percent of Si, and the balance of Al and inevitable impurities.
The preparation method of the aluminum-magnesium-manganese-copper alloy plate with the limited components comprises the following steps:
step S100, sequentially smelting, casting and milling the aluminum alloy to obtain an aluminum alloy ingot;
step S200, carrying out two-stage homogenization heat treatment on the aluminum alloy ingot, wherein the treatment temperature of the first-stage homogenization heat treatment is 590-610 ℃, and the treatment time is 6-12 h; the treatment temperature of the second-stage homogenization heat treatment is 500-540 ℃, and the treatment time is 12-36 h;
step S300, carrying out hot rolling on the aluminum alloy cast ingot subjected to the two-stage homogenization heat treatment to obtain a hot rolled plate, wherein the hot rolling finishing temperature is 340-360 ℃, and the thickness of the hot rolled plate is 1.8-2.2 mm;
step S400, the hot rolled plate is subjected to cold rolling to obtain an aluminum alloy plate, the number of times of cold rolling of the hot rolled plate is 4-6, the reduction of each time is 30-45%, the total cold rolling rate of the hot rolled plate is 88-90%, and the final cold rolling temperature is 120-180 ℃.
When the aluminum alloy ingot is subjected to two-stage homogenization heat treatment in the step 200, the treatment temperature of the first-stage homogenization heat treatment is 590-600 ℃, and the treatment time is 7-10 h; the treatment temperature of the second-stage homogenization heat treatment is 510-530 ℃, and the treatment time is 15-20 h.
In the step 300, the hot rolling finishing temperature of the aluminum alloy cast ingot after the two-stage homogenization heat treatment is 340-350 ℃, and the thickness of a hot rolled plate is 1.9-2.1 mm; cubic texture strength of hot rolled sheet: 30 to 50.
In the step 400, the cold rolling finishing temperature of the aluminum alloy plate obtained by cold rolling the hot rolled plate is 150-170 ℃.
The thickness of the aluminum alloy plate is 0.20-0.26mm, the cubic texture strength of the aluminum alloy plate is 3-6, the S texture strength of the aluminum alloy plate is 10-13, the AlMnSi phase in the aluminum alloy plate accounts for 2.5-4% of the area percentage of all phases in the aluminum alloy plate, after the aluminum alloy plate is baked through a coating, the tensile strength is 310-340 MPa, the yield strength is 275-305 MPa, the elongation of the aluminum alloy plate is 6-9%, and the earing rate of the aluminum alloy plate is 0.5-3%.
Al in the aluminum alloy plate12(FeMn)3The area of the diffraction peak of the Si phase accounts for Al in the aluminum alloy plate6Diffraction peak area of FeMn phase and Al12(FeMn)3The sum of diffraction peak areas of the Si phase is more than 80%; al (Al)12(FeMn)3The equivalent circle diameter of the Si phase is 0.1 μm to 8 μm.
Al having equivalent circle diameter of 2 μm to 4 μm12(FeMn)3The area of Si phase accounts for all Al in the aluminum alloy plate12(FeMn)340-60% of the area of the Si phase.
The invention has the beneficial technical effects that: according to the invention, by controlling the components of the aluminum alloy and the processing method of the aluminum alloy plate, the obtained aluminum alloy plate is baked by the coating, and has the tensile strength of 310-340 MPa, the yield strength of 275-305 MPa, the elongation of 6-9% and the earing rate of 0.5-3%. Compared with the prior art, the strength and the elongation of the sheet material are obviously improved, the can forming performance and the can forming rate are kept unchanged, and the can forming process of the thin can body with the thickness of less than 0.26mm can be met.
Drawings
FIG. 1 is a metallographic structure of an aluminum alloy plate according to comparative example No. 15 of the present invention; large-sized compounds are in circles;
FIG. 2 shows a metallographic structure of an aluminum alloy sheet according to example 1 of the present invention;
FIG. 3 is an XRD diffraction pattern of comparative example 14# of the present invention;
FIG. 4 is an XRD diffraction pattern of example 1 of the present invention;
FIG. 5 is a graph of ODF (distribution function) of comparative example 18# of the present invention;
FIG. 6 is a diagram of ODF (distribution function) for the 1# embodiment of the present invention;
FIG. 7 is a scanning electron microscope observation of the aluminum alloy ingots of comparative example No. 22 and example No. 1 of the present invention after the second-stage homogenization heat treatment;
FIG. 8 is a photograph of the hot rolled plate grain structure after the aluminum alloy ingots according to comparative example No. 22 and example No. 1 of the present invention were subjected to the second-stage homogenization heat treatment.
Detailed Description
For further disclosure, but not limitation, the present invention is described in further detail below with reference to examples.
The aluminum-magnesium-manganese-copper alloy for the ironing can body and the plate thereof comprise the following components in percentage by mass: 1.10 to 1.40 percent of Mg, 0.80 to 1.10 percent of Mn, 0.20 to 0.40 percent of Cu, 0.20 to 0.50 percent of Fe, 0.18 to 0.4 percent of Si, and the balance of Al and inevitable impurities. Preferably, the aluminum alloy comprises the following components in percentage by mass: 1.29 to 1.40 percent of Mg, 0.93 to 1.10 percent of Mn, 0.26 to 0.40 percent of Cu, 0.20 to 0.34 percent of Fe, 0.31 to 0.4 percent of Si, and the balance of Al and inevitable impurities.
Mn is a strengthening element in the alloy, and when the Mn is less than 0.93%, the alloy sheet cannot obtain the required strength and does not have enough AlFeMn compound; if the content of the Mn element is higher than 1.1%, a large amount of AlFeMn compounds with larger sizes can appear in the alloy, so that the forming performance of the plate is reduced; meanwhile, the excessive Mn element also causes the number of AlFeMn phases in the alloy ingot to be increased sharply, compared with the situation that the number of Si element is small, the AlFeMn phase is not completely converted into alpha phase (Al) in the homogenization process12(FeMn)3Si phase), which causes a decrease in the α -phase transformation ratio, affects the ironing performance of the sheet material, and eventually leads to failure in can making.
Fe element is a strengthening element in the alloy, and when Fe element is less than 0.20%, the alloy sheet cannot obtain the required strength, and there is not enough AlFeMn compound. If the Fe element content is higher than 0.34%, a large amount of AlFeMn compounds with larger sizes can appear in the alloy, so that the sheet forming performance is reduced, and can making cannot be finished.
Si is a strengthening element in the alloy and is an essential element for converting an AlFeMn phase into an alpha phase in the homogenization heat treatment process of the alloy ingot. The quantity and the appearance of the alpha phase are main regulating and controlling factors for improving the thinning and drawing performance of the plate. If the content of the Si element is lower than 0.18 percent, the ingot cannot obtain enough alpha phase in the homogenization process; if the content of the Si element is higher than 0.4%, the obtained alpha phase has a large size, the mechanical property of the plate is reduced, and can making cannot be completed.
Mg is a strengthening element in the alloy, and the performance of the alloy plate is improved mainly through solid solution strengthening. When the content of Mg element is lower than 1.29 percent, the strength of the plate can not meet the requirement; when the Mg element is more than 1.40%, the rolling property of the plate becomes poor, which is not favorable for the production.
The Cu element is a strengthening element in the alloy, and can perform aging strengthening by utilizing the rolling temperature after cold rolling and the temperature in the forming and baking process of the tank body. If the content of the Cu element is lower than 0.26%, the strength of the plate cannot meet the requirement; if the Cu content is higher than 0.40%, the formability of the plate is seriously reduced, and the can making process cannot be completed.
The preparation method of the aluminum alloy plate comprises the following steps:
(1) sequentially smelting, casting and milling an aluminum alloy to obtain an aluminum alloy ingot;
(2) carrying out two-stage homogenization heat treatment on the aluminum alloy ingot, wherein the treatment temperature of the first-stage homogenization heat treatment is 590-610 ℃, and the treatment time is 6-12 h; the treatment temperature of the second-stage homogenization heat treatment is 500-540 ℃, and the treatment time is 12-36 h;
preferably, when the aluminum alloy ingot is subjected to two-stage homogenization heat treatment, the treatment temperature of the first-stage homogenization heat treatment is 590-600 ℃, and the treatment time is 7-10 h; the treatment temperature of the second-stage homogenization heat treatment is 510-530 ℃, and the treatment time is 15-20 h.
The reason for choosing the homogenization heat treatment process is mainly to control the proportion and morphology of the alpha phase. The alpha phase is an AlFeMnSi quaternary phase and is transformed from an as-cast AlFeMn phase and a Si element dissolved in the matrix together in the high-temperature homogenization process. The hardness of the alpha phase is higher than that of AlFeMn phase, and in the process of manufacturing the pop can, the alpha phase with the size of 2-4 mu m can effectively scrape impurity deposits such as aluminum ash on the surface of a thinning and drawing die, and is the most important compound in the process of manufacturing the pop can. If the first-stage homogenization temperature is lower than 590 ℃, the process of converting the AlFeMn phase into the alpha phase is obviously slowed down, so that the production efficiency is reduced, and the cost is increased; if the first-stage homogenization heat treatment time is less than 6h, a certain amount of AlFeMn phase at the central part of the ingot is not fully converted into an alpha phase, so that the thinning and drawing performance of the plate is reduced; if the first-stage homogenization heat treatment time is longer than 12 hours, the alpha phase obtained by conversion is agglomerated and spheroidized, and is not beneficial to crushing in the subsequent rolling process, so that the strengthening effect of the alpha phase on the plate is reduced, and the can making process is more difficult to complete. It can be seen from the examples and comparative examples of the present invention that the proportion of broken cans of the sheet is significantly increased when the compound having an equivalent circle diameter > 8 μm starts to appear in the sheet.
And after the first-stage homogenization heat treatment is finished, transferring the aluminum alloy ingot into a heat preservation furnace for second-stage homogenization heat treatment, wherein the furnace temperature is 500-540 ℃, and the heat preservation is carried out for 12-36 h. The purpose of heat preservation is to separate out AlMnSi phase in the alloy, the AlMnSi phase is submicron needle phase, and can be crushed into nano-scale fine particles in the subsequent rolling process, the AlMnSi has certain strengthening effect, and can pin recrystallization grain boundary, prevent recrystallization grain growth, refine hot rolling structure and further improve the strength of the plate, and the embodiment and the comparative example of the patent can know that the AlMnSi phase in the aluminum alloy plate accounts for more than 2.5 percent of the area percentage of the whole phase in the aluminum alloy plate, and can play a sufficient strengthening role, preferably, the AlMnSi phase accounts for 2.5 to 4 percent of the area percentage of the whole phase in the aluminum alloy plate.
(3) Directly hot rolling the aluminum alloy ingot subjected to the two-stage homogenization heat treatment to obtain a hot rolled plate, wherein the final hot rolling temperature is 340-360 ℃, and the thickness of the hot rolled plate is 1.8-2.2 mm; preferably, the hot rolling finishing temperature of the aluminum alloy ingot subjected to the two-stage homogenization heat treatment is 340-350 ℃, and the thickness of the hot rolled plate is 1.9-2.1 mm.
The direct rolling after the heat treatment at 500-530 ℃ is selected to ensure that the hot finish rolling temperature of the plate is 340-360 ℃ after hot rolling, so that the hot rolled plate can be ensured to have enough temperature for self annealing after being rolled, a higher recrystallized cubic texture is obtained, and the cubic texture crystal grain accounts for 17-20% in the hot rolled plate. In the subsequent cold rolling process, the cubic textures and the rolling textures generated in the cold rolling process are kept in a certain composition ratio, so that the earing rate is ensured to be 0.5-3%.
As can be seen from the comparative examples and examples of the present invention, the earing ratio can be controlled to 3% or less in general when the strength of the cubic texture in the aluminum alloy sheet is 3 to 6 and the strength of the S texture is 10 to 13. However, if the hot rolling start temperature is higher than 530 ℃, the aluminum can be seriously adhered to the roller during the hot rolling process of the plate, so that the plate is scrapped. The thickness of the hot rolled plate is selected to be 1.8mm-2.2mm so as to ensure that the total cold rolling rate is controlled to be about 88% -90% in the subsequent cold rolling process, thereby controlling the number of the rolling textures generated in the cold rolling process, keeping a certain composition proportion with the recrystallization cube texture, and ensuring that the earing rate is below 3%.
(4) Cold rolling the hot rolled plate to obtain an aluminum alloy plate, wherein the cold rolling times of the hot rolled plate are 4-6 times, the reduction of each time is 30-45%, the total cold rolling rate of the hot rolled plate is 88-90%, and the final cold rolling temperature is 120-180 ℃; preferably, the cold rolling finishing temperature of the aluminum alloy plate obtained by cold rolling the hot rolled plate is 150-170 ℃. The reduction of 30-45% per pass is selected because the risk of plate rolling cracking is increased if the reduction of a single pass is more than 45%; if the single-pass reduction is less than 30%, the plate cannot be rolled to 0.20-0.26mm in 4-6 passes, the production efficiency is seriously reduced, the cold rolling finishing temperature of the plate cannot reach more than 120 ℃, the aging strengthening effect of the Cu element is insufficient, and the plate performance cannot meet the requirements.
According to the aluminum alloy component and the preparation method of the aluminum alloy plate, the thickness of the aluminum alloy plate can be reduced to 0.20-0.26mm, the tensile strength of the aluminum alloy plate can be increased to 310-340 MPa after the aluminum alloy plate is baked by a coating, the yield strength of the aluminum alloy plate can be increased to 275-305 MPa, the elongation is kept to be 6-9%, the earing rate is 0.5-3%, and the requirement of industrial can making can be met.
Examples and comparative examples
Table 1 shows the compositions of the aluminum alloys used in examples and comparative examples, excluding Al and other unavoidable impurities, and their mass percentages.
TABLE 1 compositions and mass percents of aluminum alloys in examples and comparative examples
3104 aluminum alloy ingots are cast according to the aluminum alloy provided in table 1, the aluminum alloy ingots are subjected to a first-stage homogenization heat treatment at 600 ℃ for 6 hours, then the aluminum alloy ingots are cooled to 500 ℃ and are subjected to a second-stage homogenization heat treatment at 12 hours, the aluminum alloy ingots are subjected to hot rolling after the heat treatment, the final hot rolling temperature is 340 ℃, the hot rolling is carried out after winding, and the hot rolled plate is cooled by blowing, wherein the thickness of the hot rolled plate is 2.2 mm. And (3) carrying out 4-pass cold rolling on the hot rolled plate, wherein the cold rolling reduction of each pass is 40-45%, the cold rolling finishing temperature is 160 ℃, and the aluminum alloy plate is obtained after cold rolling, and the thickness of the aluminum alloy plate is 0.20-0.26 mm. Table 2 shows the yield strength, elongation and can making evaluation results of the aluminum alloy sheets prepared from the aluminum alloys in table 1 by the above-mentioned processing techniques.
TABLE 2 mechanical Property results for aluminum alloy sheets
As can be seen from tables 1 and 2, when the Mn content is higher than the range required by the present invention, the deformation capability of the sheet material is insufficient due to the coarse compounds in the sheet material, and can not be successfully formed; when the Mn content is less than the range required by the present invention, the sheet strength is insufficient to cause insufficient can body pressure resistance. When the Mg content is higher than the range required by the invention, the rolling capability of the plate is reduced, and the plate cannot be rolled and prepared according to the established process; when the Mg content is less than the range required by the present invention, the sheet strength is insufficient to cause insufficient can body pressure resistance. When the Cu content is higher than the range required by the invention, the tendency that the Cu element is precipitated to form a dispersed phase with poor strengthening effect is increased, so that the strength of the plate is insufficient, and the pressure resistance of the tank body is insufficient; when the Cu content is less than the required range of the present invention, the sheet strength is insufficient to cause insufficient can body pressure resistance. When the Fe content is higher than the range required by the invention, the deformation capability of the sheet is insufficient due to the coarse compounds in the sheet, and the can making cannot be successful; when the Fe content is less than the required range of the present invention, the insufficient strength of the sheet results in insufficient pressure resistance of the can body. When the Si content is higher than the required range of the invention, the alpha phase in the plate is thick, so that the deformation capability is insufficient, the tank bottom can not be formed, and the tank making can not be successful; when the Si content is lower than the required range of the invention, the insufficient strength of the plate leads to insufficient pressure resistance of the tank body, and the insufficient amount of the alpha phase in the plate leads to the failure of cleaning the surface of the die, thereby causing the serious pull mark on the surface of the tank body. According to the invention, by controlling the chemical composition of the alloy, on the basis that the aluminum alloy plate for the can body is thinned to 0.20-0.26mm, the strength of the aluminum alloy plate is improved, the elongation of the material and the forming performance of the can body are kept, and the manufacturing requirement of the aluminum alloy plate for the can body of 0.20-0.26mm is met.
Table 3 shows process parameters of examples and comparative examples of 0.20mm to 0.26mm aluminum alloy sheets for can bodies prepared by different processing methods based on the aluminum alloy composition of example No. 1 in Table 1. Among them, the example # 1 in table 3 is still the example # 1 in table 1, and is a reference example in not only the alloy composition research design but also the machining process research design, and thus is presented again in table 3, which facilitates the comparison of the machining processes. In order to facilitate identification of compositions and processes of different examples and comparative examples throughout the text, numbers of examples and comparative examples generated subsequently in table 3 for studying the effects of different processes on the structure and performance of the aluminum alloy sheet are accumulated on the basis of table 1, so that examples 13 are started, and comparative examples 14# -24 are generated subsequently. The compositions of the aluminum alloys of examples # 13 to # 24 and comparative examples are the compositions of the aluminum alloy of example # 1, but the processing techniques are different from those of example # 1 in Table 3.
TABLE 3 examples and comparative examples of different working processes
Table 4 shows the mechanical properties, earing ratios and can making evaluation tables of the aluminum alloy sheets obtained by using the aluminum alloy ingots prepared from the aluminum alloy of example # 1 in table 1 and performing the different processing techniques in table 3.
TABLE 4 aluminum alloy sheet Properties and evaluation tables obtained by different processing techniques in TABLE 3
From table 3 and table 4, it can be compared: under the condition that the primary homogenization temperature is 590-600 ℃, when the primary homogenization time is longer than the range of the invention (comparative example No. 15), the alpha phase in the aluminum alloy is too large in size, so that the sheet earing rate is improved, the mechanical property and the forming property of the sheet are also reduced, and the can making is failed (as shown in figures 1 and 2); by counting the compounds of the metallographic photograph of the 1# example and the 15# comparative example, it can be found that: the compounds of example # 1 all had equivalent circle diameters of 8 μm or less, and the area of the α phase, which was effective in cleaning the mold, of 2 μm to 4 μm was 40% of the area of all the compounds. In the 15# embodiment, because the first-stage homogenization time is too long, the alpha phase in the aluminum alloy is agglomerated and grown, and the grown alpha phase particles are difficult to break in the rolling process, a compound with the equivalent circle diameter of more than 8 μm appears in the aluminum alloy plate, and the area of the alpha phase with the equivalent circle diameter of 2 μm-4 μm accounts for only 35% of the area of all the compounds. The increase in the amount of large-sized compounds and the decrease in the amount of small-sized compounds capable of cleaning the mold together cause problems of low elongation and severe tank breakage in the can manufacturing thereof.
When the first-stage homogenization time is less than the range of the invention (comparative example No. 14), the alpha phase conversion rate in the aluminum alloy is insufficient, the mold cleaning effect cannot be achieved, the surface of the can body is excessively drawn, and the can manufacturing is also judged to be unqualified. As can be seen from FIGS. 3 and 4, the diffraction peak of the alpha phase of example No. 1 is significantly higher than that of Al6The diffraction peak of the FeMn phase shows that the content of the alpha phase in the aluminum alloy is high. The peak areas of the diffraction peaks are measured and compared, so that the proportion of the alpha phase in the 1# embodiment in the total compound reaches 80 percent; in the comparative example No. 14, Al6The fact that the diffraction peak of FeMn phase is strong and the diffraction peak of α phase is weak indicates that the α phase transformation is small, only about 40%, in the first-stage homogenization heat treatment process of comparative example # 14. Therefore, the mould can not be cleaned during can manufacturing, so that the surface of the can body is drawn and scratched, and the can is broken in severe cases.
When the hot rolling finishing temperature is lower than the range of the invention (comparative example No. 16), the strength of the recrystallized texture of the aluminum alloy sheet after rolling is lower, and the balance between the recrystallized texture and the rolled texture can not be kept after cold rolling, so that the earing rate is higher. When the hot rolling finishing temperature is higher than the range of the invention (No. 17 comparative example), the recrystallized grain size after the plate is hot rolled and rolled is obviously larger than that of the sample of the No. 1 comparative example, the fine grain strengthening effect brought by the larger grain size is insufficient, the strength of the plate is reduced, and the pressure resistance requirement after can making cannot be met.
When the hot finish rolling thickness is higher than the range of the invention (comparative example No. 18), the cold rolling rate of the aluminum alloy plate is increased, so that the rolling texture is improved (as shown in figure 5), the S texture strength of the rolling texture is more than 18, and the cube texture strength is only about 1.7, so the earing rate of the comparative example No. 18 is higher; in contrast, as can be seen from the ODF diagram (fig. 6) of the # 1 embodiment, the strength of the S texture of the plate is only about 12.3, while the strength of the cube texture is more than 3.3, and the ears formed by the S texture and the cube texture can fill up the gaps, so that the total ear making rate of the plate is reduced, and the requirement of can making is met.
When the hot finish rolling thickness is less than the range of the present invention (comparative example No. 19), the cold rolling rate of the sheet is reduced, the work hardening degree is insufficient, the strength of the sheet is reduced, and the pressure resistance of the can body cannot meet the requirement. When the cold rolling finishing temperature is lower than the range of the invention (comparative example No. 20), the Cu element precipitation strengthening effect is insufficient, the plate strength is reduced, and the pressure resistance of the can body cannot meet the requirement. When the cold rolling rate was increased and the cold rolling passes were reduced (comparative example # 21), the single pass deformation was too large, resulting in severe wrinkles in the center and edge regions of the plate and failure to successfully roll the plate. When the holding time of the aluminum alloy ingot in the second-stage homogenization heat treatment is less than 12h (comparative example No. 22), the number of AlMnSi phases precipitated in the ingot is small (as shown in figure 7), the pinning recrystallization grain boundary effect and the second-phase strengthening effect are weak, the grain size of the plate is coarse (as shown in figure 8), and the performance of the plate cannot reach the standard. From the compound statistics, the area percentage of the AlMnSi phase in the 1# example exceeds 2.5%, while the area percentage of the AlMnSi phase in the 22# example is only 1.9%. When the holding temperature of the ingot before hot rolling is lower than 500 ℃ (comparative example No. 23), the number of AlMnSi phases precipitated in the ingot is still insufficient due to the lower temperature, so that the performance of the plate cannot reach the standard.
The second-stage homogenization heat treatment temperature is higher (comparative example No. 24), although enough AlMnSi phase can be precipitated, the temperature of the cast ingot is higher during the initial rolling, so that aluminum is adhered to the surface of the roller, the smooth operation of the rolling process is seriously influenced, and the surface defects and even the scrapping of the cast ingot are easily caused.
The results of the above examples and comparative examples show that the aluminum alloy sheet for can bodies of 0.20-0.26mm can be prepared by further controlling the preparation processing technique of the alloy on the basis of controlling the alloy components of the invention.
Claims (10)
1. The aluminum-magnesium-manganese-copper alloy plate for the reduction drawing of the can body is characterized by comprising the following components in percentage by mass: 1.10 to 1.40 percent of Mg, 0.80 to 1.10 percent of Mn, 0.20 to 0.40 percent of Cu, 0.20 to 0.50 percent of Fe, 0.18 to 0.4 percent of Si, and the balance of Al and inevitable impurities.
2. A method of making an aluminum magnesium manganese copper alloy sheet for an ironed can body according to claim 1, comprising the steps of:
(1) sequentially smelting, casting and milling the aluminum alloy to obtain an aluminum alloy ingot;
(2) carrying out two-stage homogenization heat treatment on the aluminum alloy cast ingot;
(3) carrying out hot rolling on the aluminum alloy ingot subjected to the two-stage homogenization heat treatment to obtain a hot rolled plate, wherein the final hot rolling temperature is 330-360 ℃, and the thickness of the hot rolled plate is 1.8-2.2 mm;
(4) the hot rolled plate is subjected to cold rolling to obtain an aluminum alloy plate, the number of cold rolling passes of the hot rolled plate is 4-6, the reduction of each pass is 30-45%, the total cold rolling rate of the hot rolled plate is 88-90%, and the final cold rolling temperature is 120-180 ℃.
3. The method of claim 2, wherein: the two-stage homogenization heat treatment in the step (2) is specifically as follows: the treatment temperature of the first-stage homogenization heat treatment is 550-610 ℃, and the treatment time is 4-12 h; the treatment temperature of the second-stage homogenization heat treatment is 500-540 ℃, and the treatment time is 12-36 h.
4. The aluminum-magnesium-manganese-copper alloy plate for the reduction drawing of the can body is characterized by comprising the following components in percentage by mass: 1.29 to 1.40 percent of Mg, 0.93 to 1.10 percent of Mn, 0.26 to 0.40 percent of Cu, 0.20 to 0.34 percent of Fe, 0.31 to 0.4 percent of Si, and the balance of Al and inevitable impurities.
5. A method of making an aluminum magnesium manganese copper alloy sheet for an ironed drawn can body according to claim 4, comprising the steps of:
(1) sequentially smelting, casting and milling the aluminum alloy to obtain an aluminum alloy ingot;
(2) carrying out two-stage homogenization heat treatment on the aluminum alloy ingot, wherein the treatment temperature of the first-stage homogenization heat treatment is 590-610 ℃, and the treatment time is 6-12 h; the treatment temperature of the second-stage homogenization heat treatment is 500-540 ℃, and the treatment time is 12-36 h;
(3) carrying out hot rolling on the aluminum alloy ingot subjected to the two-stage homogenization heat treatment to obtain a hot rolled plate, wherein the final hot rolling temperature is 340-360 ℃, and the thickness of the hot rolled plate is 1.8-2.2 mm;
(4) the hot rolled plate is subjected to cold rolling to obtain an aluminum alloy plate, the number of cold rolling passes of the hot rolled plate is 4-6, the reduction of each pass is 30-45%, the total cold rolling rate of the hot rolled plate is 88-90%, and the final cold rolling temperature is 120-180 ℃.
6. The preparation method according to claim 5, characterized in that when the aluminum alloy ingot in the step (2) is subjected to two-stage homogenization heat treatment, the treatment temperature of the first-stage homogenization heat treatment is 590-600 ℃, and the treatment time is 7-10 h; the treatment temperature of the second-stage homogenization heat treatment is 510-530 ℃, and the treatment time is 15-20 h.
7. The production method according to claim 5, wherein the hot rolling finishing temperature of the hot rolling of the aluminum alloy ingot after the two-stage homogenization heat treatment in step (3) is 340 ℃ to 350 ℃, and the thickness of the hot rolled sheet is 1.9mm to 2.1 mm; cubic texture strength of hot rolled sheet: 30 to 50.
8. The production method according to claim 5, wherein the cold rolling finish temperature of the aluminum alloy sheet obtained by cold rolling the hot-rolled sheet in the step (4) is 150 ℃ to 170 ℃.
9. The preparation method of claim 5, wherein the aluminum alloy plate has a thickness of 0.20-0.26mm, a yield strength of 275MPa-305MPa, a tensile strength of 310MPa-340MPa, an elongation of 6-9% after baking of the coating, a cubic texture strength of 3-7, and a earing rate of 0.5-3%.
10. The production method according to claim 5, wherein the Al having an equivalent circle diameter of 2 μm to 4 μm12(FeMn)3The area of Si phase accounts for all Al in the aluminum alloy plate12(FeMn)340-60% of the area of the Si phase; al in the aluminum alloy plate12(FeMn)3The area of the diffraction peak of the Si phase accounts for Al in the aluminum alloy plate6Diffraction peak area of FeMn phase and Al12(FeMn)3The sum of diffraction peak areas of the Si phase is more than 80%; al (Al)12(FeMn)3The equivalent circle diameter of the Si phase is 0.1-8 μm; the AlMnSi phase in the aluminum alloy plate accounts for 2.5-5% of the area percentage of the whole phase in the aluminum alloy plate.
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