JP2008303449A - Aluminum alloy sheet for forming, and method for producing aluminum alloy sheet for forming - Google Patents

Aluminum alloy sheet for forming, and method for producing aluminum alloy sheet for forming Download PDF

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JP2008303449A
JP2008303449A JP2007153937A JP2007153937A JP2008303449A JP 2008303449 A JP2008303449 A JP 2008303449A JP 2007153937 A JP2007153937 A JP 2007153937A JP 2007153937 A JP2007153937 A JP 2007153937A JP 2008303449 A JP2008303449 A JP 2008303449A
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mpa
aluminum alloy
baking
forming
proof stress
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JP2007153937A
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Akira Hibino
Toshio Komatsubara
Akira Tajiri
Takeshi Takada
小松原俊雄
日比野旭
田尻彰
高田健
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Furukawa Sky Kk
Nippon Steel Corp
古河スカイ株式会社
新日本製鐵株式会社
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Abstract

<P>PROBLEM TO BE SOLVED: To provide an aluminum alloy sheet for forming, in which a performance balance that baking hardenability is excellent, and change over time at normal temperature is small after production, can be optimally constructed, and to provide a method for producing the same. <P>SOLUTION: An aluminum alloy rolled sheet composed of an Al-Mg-Si-based or Al-Mg-Si-Cu-based alloy is subjected to artificial preliminary aging treatment, so as to control the quantity and quality of a cluster II to suitable levels, thus the 0.2% proof stress of the material is beforehand controlled to &ge;140 MPa, the material is subjected to 2% stretching in an aging period at ordinary temperature (0 to 45&deg;C) at least within three months, and, after coating/baking at 170&deg;C&times;20 min, 0.2% proof stress is &ge;240 MPa, and particularly high coating/baking strength in which the degree of increase by the coating/baking is &ge;80 MPa can be achieved. <P>COPYRIGHT: (C)2009,JPO&amp;INPIT

Description

  The present invention relates to an aluminum alloy plate for forming and a method for producing the same, and in particular, an Al-Mg-Si-based or Al-Mg-Si-Cu-based forming process that is used after being subjected to forming process or paint baking depending on the application. The present invention relates to an aluminum alloy plate and a method for producing the same.
Conventionally, as a body sheet of an automobile, a cold rolled steel sheet has been mainly used, but recently, an aluminum alloy rolled sheet is frequently used from the viewpoint of reducing the weight of the vehicle body. By the way, since the body sheet of an automobile is used after being subjected to press working, it is required that the formability is excellent and that a Ruders mark is not generated during the forming process.
In addition, it is essential to have high strength, and since it is usually used after being baked, it is required to have a characteristic (bake hardenability, i.e., BH property) that provides high strength after baking (also called baking). The
In addition, in order to satisfy the moldability such as press formability, shape freezing property, hemmability, and bake hardenability in a well-balanced manner, the material changes from room temperature to aging, that is, due to natural aging. It is very important to suppress performance deterioration, particularly strength reduction after baking.
  Conventionally, as an aluminum alloy for such an automobile body sheet, in addition to an Al-Mg alloy, it has a relatively low strength and excellent formability at the time of molding before coating baking, Aging Al-Mg-Si alloy, aging Al-Mg-Si-Cu alloy, which has the advantage that it is aged by heating and has the advantage that the strength after baking is high, and has the advantage that it does not easily generate Luders marks. Alloys are mainly used.
  Patent Document 1, which has studied to improve the formability and bake hardenability of this aging Al—Mg—Si based alloy and aging Al—Mg—Si—Cu based alloy and to suppress room temperature aging, A heat treatment is proposed in which the material is kept at a certain temperature range (50 ° C. to 150 ° C.) after being subjected to normal temperature aging as short as possible after the treatment.
  Further, in Patent Document 2, stable clusters are easily formed by holding treatment or reheating treatment, and the stability of the clusters is improved, the change with time after the plate is manufactured is suppressed, and good moldability is ensured. In addition, by applying a stabilization treatment to obtain sufficient bake hardenability, the time-dependent change at room temperature after manufacturing the plate is reduced, and the β ”phase in paint baking is finer, and the bake hardenability is improved. The manufacturing method of was disclosed.
  Focusing on the problem that increasing the amount of stable cluster formation in the method disclosed in Patent Document 2 means a decrease in the degree of supersaturation of the solute element and reducing the amount of β ″ phase formation. Reference 3 describes that a restoration process for re-solidifying clusters formed by natural aging during the standing time after solution treatment and air cooling and re-establishing the amount of solute elements is performed in a temperature range corresponding to the standing time. In addition, an aluminum alloy plate suitable for use in an automobile body has been disclosed, which is excellent in moldability and paint bake hardenability.
On the other hand, Patent Document 4 and Patent Document 5 disclosed a method for producing a general-purpose aluminum alloy plate for forming that performs solution treatment (high temperature) treatment and stabilization treatment after quenching.
Japanese Patent No. 3207413 (Japanese Patent Laid-Open No. 04-147951) JP-A-6-272000 JP-A-9-143645 Japanese Patent No. 2613466 (Japanese Patent Laid-Open No. 02-205660) Japanese Patent No. 3359428 (Japanese Patent Laid-Open No. 08-049052)
  Recently, for aging Al-Mg-Si-based and Al-Mg-Si-Cu-based alloy plates for automobile body sheets, a higher strength level than ever has been achieved in order to reduce the material thickness and reduce costs. At the same time, it is required to be a material with as little strength deterioration as possible even after aging at room temperature. In addition, with regard to paint baking, there is an increasing tendency to lower the baking temperature and shorten the baking time. ing.
  The needs for automobile body seats are extremely acute and urgent issues in relation to the social background, where environmental quality, including measures against global warming, is the highest quality requirement for automobiles. In order to achieve this, material design that is not only based on empirical data but also focused on the physical behavior of the material to achieve precise purposes is required, and particularly high bake hardenability (BH properties) is emphasized. In addition, it is necessary to meet the demand for suppressing deterioration in strength after baking after painting due to aging at room temperature, and to achieve this with an optimal performance balance at a reasonable cost.
From this point of view, the aging Al-Mg-Si-based and Al-Mg-Si-Cu-based alloy sheets obtained by the manufacturing methods disclosed in Patent Documents 1 to 5 are immediately after manufacturing (room temperature aging 1 month). Less), after high-strength, 0.2% proof stress 240MPa or higher and 80MPa or more of the increase is obtained, if left at room temperature for a long time (1 month or longer), Deterioration in strength (increased by 0.2% proof stress less than 80 MPa) has occurred, and bake hardenability (BH properties) and room temperature aging cannot be sufficiently balanced at the level according to the above needs.
For example, in the manufacturing methods disclosed in Patent Document 2 and Patent Document 3, although attention has been paid to clusters generated in an aluminum alloy matrix, a specific request for realizing appropriate characteristics at a reasonable cost is specifically described. I was not satisfied.
Further, for example, according to the method for producing an aluminum alloy plate disclosed in Patent Document 4, after the solution treatment (high temperature) treatment, it is quenched into a temperature range of 50 to 130 ° C. and kept at 50 to 150 ° C. for 1 to 96 hours. It is said that the strength and formability are improved by applying the treatment, but No. 1 shown in Table 3 of Patent Document 4 is shown. No. 10, although the stabilization process is performed at 100 ° C. or higher for 48 hours, the post-baking proof stress is 22.3 kg / mm 2 (218.7 MPa) or lower, and the 0.2% proof stress is 240 MPa or higher after paint baking. It does not meet your needs.
Furthermore, the aluminum alloy sheet for forming disclosed in Patent Document 5 is subjected to a solution treatment, and is cooled to a temperature range of 50 to 80 ° C. at 100 ° C./min or more. Is held for a time within a range such that the proof stress is 100 N / mm 2 or less, and subsequently subjected to stabilization treatment at 85 to 150 ° C. for 0.5 to 50 hours, the quenching temperature is set to 60 ° C., Production number 1 (alloy symbol A1) shown in Tables 2 and 3 subjected to stabilization treatment at 100 ° C. for 18 hours has a small change over time in yield strength due to normal temperature aging after production, and on the first day after production, 0.2% proof stress of baking after material 180 ° C. × 30min at 40 days are each 211N / mm 2, 209N / mm 2, able to satisfy the needs of still 0.2% proof stress 240MPa or more after baking Can not
  The present invention has been made against the background of the above circumstances, an aluminum alloy sheet for forming and capable of optimally constructing a performance balance of excellent bake hardenability and little change with time at room temperature after manufacture, and a method for manufacturing the same The purpose is to provide.
  As a result of repeated studies by the present inventors in order to solve the above-described problems, the structure of the final plate of the Al-Mg-Si-based or Al-Mg-Si-Cu-based alloy is preliminarily used as a material structure by high-temperature pre-aging. It has been found that an aluminum alloy sheet having high paint bake strength can be obtained by adjusting so that the cluster II is sufficiently generated therein, and the present invention has been made.
Here, clusters are generally divided into two types, cluster I and cluster II. As a feature thereof, the cluster I is an atomic group of Mg and Si formed mainly at a holding temperature of less than 70 ° C., and this exists stably even at the coating baking temperature.
Cluster II is a group of Mg and Si atoms similar to cluster I, but changes into precipitates effective for improving strength at the coating baking temperature.
  That is, the aluminum alloy sheet for forming according to the present invention is obtained from an aluminum alloy ingot made of an Al-Mg-Si or Al-Mg-Si-Cu alloy through a rolling process and a heat treatment process including heating and cooling. A rolled plate having a plate thickness, and after the solution treatment on the rolled plate, the material is 0.2% proof stress 140 MPa or more in advance by artificial preliminary aging treatment, and the normal temperature (0 to 45 ° C.) aging period within at least 3 months After the material is stretched by 2%, the 0.2% proof stress after coating baking at 170 ° C. × 20 min is 240 MPa or more, and the increase due to coating baking is 80 MPa or more.
  In addition, the aluminum alloy sheet for forming according to the present invention is obtained from an aluminum alloy ingot made of an Al-Mg-Si-based or Al-Mg-Si-Cu-based alloy through a rolling process and a heat treatment process including heating and cooling. A rolled plate having a thickness is formed. After the solution treatment, the material is 0.2% proof stress of 140 MPa or more in advance by an artificial preliminary aging treatment, and by a differential scanning calorimeter (DSC). In the measurement, the maximum exothermic peak height is set to 0.09 W / g or less, and the 0.2% proof stress after painting and baking of the material is 240 MPa or more during the normal temperature (0 to 45 ° C.) aging period of at least 3 months. Thus, the increase in coating baking has a high coating baking strength of 90 MPa or more.
The structure and configuration of the cluster II are not necessarily constant, and the bake hardenability and formability of the material are affected depending on the structure and configuration of the cluster II.
Therefore, by restricting the maximum exothermic peak height in DSC measurement to 0.09 W / g or less, the structure and configuration of cluster II can be adjusted to obtain high-performance bake hardenability and formability prevention effect. it can.
After performing the solution treatment at 480 ° C. or higher, after cooling at a cooling rate of 100 ° C./min (min) or higher to a temperature range of 80 ° C. or higher and 150 ° C. or lower, the alloy plate is heated at a temperature range of 80 ° C. or higher and 150 ° C. or lower. Cluster II can be generated by a process of retaining so that the 2% proof stress is 140 MPa or more.
By retaining the material in a temperature range of 80 ° C. or more and 150 ° C. or less, the generation amount of cluster II that is a factor contributing to the strength becomes dominant, and the formation of cluster II brings matching strain in the structure, and the strength is increased. To rise.
Moreover, when the production amount reaches a certain level or more, the change with time at room temperature is suppressed by the interaction between the cluster II and the pores, and the deterioration of the strength after coating baking due to the room temperature with time can be minimized.
After performing the solution treatment at 480 ° C. or higher, after cooling at a cooling rate of 100 ° C./min (min) or higher in a temperature range of 70 ° C. or higher and 90 ° C. or lower, the temperature range of 70 ° C. or higher and lower than 90 ° C. is 10 minutes or lower. Degradation of formability can be prevented by the cluster II generated at a relatively low temperature by the retention process.
If this residence time is 10 minutes or more, high-performance bake hardenability may not be obtained.
Next, reheating to a temperature range of 90 ° C. or higher and 150 ° C. or lower is performed again. The temperature rising rate is preferably a temperature rising rate of 10 ° C./min or more.
By staying in a relatively high temperature range of 90 ° C. or more and 150 ° C. or less, the 0.2% proof stress of the material is set to 140 MPa or more, and a more stable Cluster II structure / configuration can be obtained.
Moreover, if the maximum exothermic peak height is adjusted to 0.09 W / g or less by DSC measurement, it will be 0. 0 after coating and baking of the material at room temperature (0 to 45 ° C.) over a period of at least 3 months. The 2% proof stress is 240 MPa or more, and a high paint bake strength with an increase of 90 MPa or more can be obtained.
In the case where higher strength is emphasized, the preliminary aging temperature is preferably adjusted to the high temperature side so that the maximum exothermic peak height is 0.06 W / g or less. Further, when emphasizing prevention of moldability deterioration, it is preferable to set the artificial preliminary aging temperature to 130 ° C. or lower.
  The aluminum alloy for forming contains Mg 0.2 to 1.5% (mass%, the same shall apply hereinafter), Si 0.3 to 2.0%, Mn 0.03 to 0.6%, Cr 0.01 to 0 Ti0 allowed to accompany B of .4%, Zr 0.01-0.4%, V 0.01-0.4%, Fe 0.03-1.0%, 0.0001% -0.0500% An aluminum alloy containing one or more selected from 0.005 to 0.2%, with the balance being Al and inevitable impurities. Furthermore, you may contain 1 type or 2 types of Zn0.03-2.5%, Cu0.05-1.5%.
  Bake hardenability (BH), moldability, and change with time can be comprehensively adjusted for a thin automobile body sheet.
[Action]
According to the aluminum alloy sheet for forming according to the present invention, particularly high paint bake strength can be realized by adjusting the amount and quality of the cluster II to an appropriate level by artificial preliminary aging treatment.
The aluminum alloy sheet for forming according to the present invention is particularly emphasized in the balance between formability and strength, excellent in bake hardenability, high in strength after baking, and with little change over time at room temperature. Excellent performance with less paint bake hardenability.
Moreover, according to the manufacturing method of the aluminum alloy plate for forming according to the present invention, the aluminum alloy plate for forming having excellent performance as described above can be manufactured reliably and stably on a mass production scale.
Accordingly, the aluminum alloy sheet for forming according to the present invention is suitable for a body sheet for thin-walled automobiles because the bake hardenability (BH), formability and aging change are comprehensively adjusted.
The aluminum alloy plate in the method for producing an aluminum alloy plate for forming according to the present invention may basically be an Al-Mg-Si alloy or an Al-Mg-Si-Cu alloy, and its specific composition Is not particularly restricted.
Usually, it contains Mg 0.2 to 1.5% (mass%, the same shall apply hereinafter), Si 0.3 to 2.0%, Mn 0.03 to 0.6%, Cr 0.01 to 0.4%, Zr0 0.01 to 0.4%, V 0.01 to 0.4%, Fe 0.03 to 1.0%, 0.0001% to 0.0500% Ti allowed to accompany B 0.005 to 0.00%. It is preferable to use, as a raw material, an aluminum alloy containing one or more selected from 2%, with the balance being Al and inevitable impurities. Furthermore, you may contain 1 type or 2 types of Zn0.03-2.5%, Cu0.05-1.5%.
The reasons for limiting the components of this material alloy will be described below.
Mg:
Mg is an alloy element that is a basic alloy of the system targeted by the present invention, and contributes to strength improvement in cooperation with Si. If the Mg content is less than 0.2%, the amount of β "phase that contributes to strength improvement by precipitation hardening during baking is reduced, so that sufficient strength improvement cannot be obtained, while if it exceeds 1.5%, it is coarse. Mg-Si based intermetallic compounds are produced, and the formability, particularly bending workability, is reduced, so the Mg content is within the range of 0.2 to 1.5%. In order to improve the workability, the Mg content is preferably in the range of 0.3 to 0.9%.
Si:
Si is also an alloy element that is fundamental in the alloy of the present invention, and contributes to strength improvement in cooperation with Mg. In addition, Si is produced as a crystallized product of metal Si at the time of casting, and the periphery of the metal Si particles is deformed by processing and becomes a recrystallization nucleus generation site during solution treatment. It also contributes to If the amount of Si is less than 0.3%, the above effect cannot be obtained sufficiently. On the other hand, if it exceeds 2.0%, coarse Si particles and coarse Mg-Si based intermetallic compounds are produced, and formability, particularly This causes a decrease in bending workability. Therefore, the Si amount is set in the range of 0.3 to 2.0%. In order to obtain a better balance between press formability and bending workability, the Si content is preferably in the range of 0.5 to 1.3%.
Mn, Cr, Zr, V
These elements are effective in improving strength, crystal grain refinement, or improving aging (bake hardenability), and any one or more of them are added.
When the Mn content is less than 0.03%, or the Cr content is less than 0.01%, or the Zr content is less than 0.01%, and the V content is less than 0.01%, If the Mn content exceeds 0.6% or the Cr, Zr, and V contents exceed 0.4%, the above effect is not only saturated. , A large number of intermetallic compounds may be produced, which may adversely affect the formability, particularly hem bendability. Therefore, Mn is in the range of 0.03 to 0.6%, and Cr, Zr, and V are each 0.01%. Within the range of ~ 0.4%.
Fe
Fe is an element effective for strength improvement and crystal grain refinement.
If its content is less than 0.03%, a sufficient effect cannot be obtained. On the other hand, if it exceeds 1.0%, moldability, particularly bending workability, may be deteriorated. Within the range of 0.0%.
Ti
To make the ingot structure fine, 0.005% to 0.200% Ti may be added alone or together with B0.0001% to 0.0500%. If the Ti addition amount exceeds 0.200% and the B addition amount exceeds 0.0500%, coarse crystallized matter is generated, and the moldability may be lowered. On the other hand, when Ti is less than 0.005% and less than B0.0001%, the effect of refining the structure of the ingot is small. Further, if Ti exceeds 0.200%, coarse crystallized substances are generated and the moldability is impaired, and if B exceeds 0.05%, coarse intermetallic compounds are generated and the moldability is impaired. Therefore, 0.005% to 0.2% Ti, which is allowed to accompany 0.0001% to 0.0500% B, can be added.
Furthermore, the addition of Sc is also effective for making the ingot structure finer, and there is no particular problem even if Sc is added within the range of 0.01 to 0.2%.
Zn
Zn is an element that contributes to strength improvement through improvement in aging and is effective in improving surface treatment.
If the added amount of Zn is less than 0.03%, the above effect cannot be obtained sufficiently. On the other hand, if the added amount exceeds 2.5%, the moldability and the corrosion resistance deteriorate, so the added amount when adding Zn is 0.03. Within the range of ~ 2.5%.
Cu
Cu is an element that may be added to improve strength and formability. For the purpose of improving the strength and formability, the addition amount when adding Cu is 0.05% or more.
However, if the amount exceeds 1.5%, the corrosion resistance (intergranular corrosion resistance, yarn rust resistance) deteriorates, so the Cu content is restricted to 1.5% or less. In addition, when it is necessary to further improve the corrosion resistance, the Cu content is preferably 1.0% or less, and when the corrosion resistance is particularly important, the Cu content is desirably regulated to 0.05% or less.
In addition, in aging Al-Mg-Si alloys and aging Al-Mg-Si-Cu alloys, trace amounts of Ag, In, Cd, Be, or Sn which are high temperature aging promoting elements or normal temperature aging inhibiting elements are added. Sometimes.
Even in the aluminum alloy sheet for forming according to the present invention, addition of these elements is allowed if added in a trace amount, and if it is 0.3% or less, the intended purpose is not particularly impaired.
  In addition to the above elements, basically, Al and inevitable impurities may be used.
Next, a method for producing the aluminum alloy plate for forming according to the present invention will be described.
In the method for producing an aluminum alloy sheet for forming according to the present invention, an alloy having the component composition as described above is melted in accordance with a conventional method and cast by a normal casting method such as a DC casting method.
Next, the obtained ingot is subjected to heat treatment and rolling in one of the following steps, for example, to obtain a required plate thickness.
1. Homogenization process ⇒ Hot rolling process ⇒ Cold rolling process ⇒ Intermediate annealing process ⇒ Cold rolling process 2. Homogenization process ⇒ Hot rolling process ⇒ Annealing process ⇒ Cold rolling process Homogenization process ⇒ Hot rolling process ⇒ Cold rolling process
That is, in the method for producing an aluminum alloy sheet for forming according to the present invention, the process of setting the ingot to the required plate thickness may be in accordance with a conventional method, and the conditions are not particularly limited.
In general, it is subjected to a hot rolling step after being cooled at a homogenization temperature of 480 ° C. or more, a holding time of 1 h to 48 h, and a cooling rate of 3 ° C./min or more as necessary. In batch-type intermediate annealing with a hot rolling start temperature of 250 ° C. or more and 590 ° C. or less, an end temperature of 150 ° C. or more and 350 ° C. or less, and a slow temperature increase and cooling rate (approximately 5 to 60 ° C./hr), an annealing temperature of 300 to 450 is used. In a continuous annealing line (CAL method) having a high temperature and a cooling rate (approximately 2 to 100 ° C./sec), a annealing temperature of 400 to 590 ° C., a holding time of 0 seconds to 10 minutes, etc. Is implemented.
  Further, as will be described later, in the method of manufacturing an aluminum alloy plate for forming according to the present invention, since the solution treatment is performed at a high temperature, the finally obtained aluminum alloy plate for forming processing can be improved in paint bake hardenability and formability. The effect of the previous process is very small.
Next, after making the ingot a required plate thickness, solution treatment is performed at a temperature of 480 ° C. or higher.
This solution treatment is an important process for solid-dissolving Mg2Si, simple substance Si, etc. in the matrix, thereby imparting bake hardenability and improving the strength after paint baking. This process also contributes to lowering the distribution density of the second phase particles by solid solution of Mg2Si, simple substance Si particles, etc., and improving ductility and bendability. This is also an important process for obtaining crystal orientation and obtaining good moldability.
  When the solution treatment temperature is less than 480 ° C., it is considered advantageous for suppressing the change over time at room temperature. Not only does this become impossible, but ductility and bendability also deteriorate significantly, so the solution treatment temperature needs to be 480 ° C. or higher. In particular, when emphasizing the solution effect, the solution treatment temperature is preferably 540 ° C. or higher. On the other hand, the upper limit of the solution treatment temperature is not particularly defined, but it is usually preferably 590 ° C. or less in consideration of the possibility of eutectic melting and coarsening of recrystallized grains. The solution treatment time is not particularly limited. However, if it exceeds 5 minutes, the solution effect is saturated, not only the economic efficiency is impaired, but also the crystal grains may be coarsened. Is preferably within 5 minutes.
In the manufacturing method of the aluminum alloy plate for forming according to the present invention, the solution can be cooled to a temperature range of 80 to 150 ° C. at a cooling rate of 100 ° C./min or more after the solution treatment.
Here, if the cooling rate after the solution treatment is less than 100 ° C./min, Mg2Si or simple substance Si precipitates in the grain boundary during cooling, and at the same time, the formability, particularly heme workability is lowered, and at the same time, bake hardening. As a result, the strength is lowered and it is not possible to expect a sufficient strength improvement during painting baking.
Moreover, when it cools to the temperature range below 80 degreeC, the cluster I or the low temperature cluster II may be formed, and there exists a possibility that bake hardenability may fall. In addition, when the material is retained at a temperature exceeding 150 ° C., grain boundary precipitation is likely to occur, and the moldability and hemmability may be deteriorated. Furthermore, since there is a concern about a decrease in bake curability due to aging at room temperature, the temperature is set to 150 ° C. or lower. From the balance of moldability and bake hardenability, 130 ° C. or lower is preferable.
In the manufacturing method of the aluminum alloy sheet for forming according to the present invention, the 0.2% proof stress of the material can be made 140 MPa or more in advance by an artificial preliminary aging treatment after the solution treatment.
After the solution treatment, cooling is performed at a cooling rate of 100 ° C./min or higher in a temperature range of 80 ° C. or higher and 150 ° C. or lower, and the material is retained in the temperature range of 80 ° C. or higher and 150 ° C. or lower in the metal structure. A precipitate called Cluster II is produced.
  By causing the material to stay in a temperature range of 80 ° C. or higher and 150 ° C. or lower, the formation of cluster II causes an alignment strain in the structure, and the strength increases. Moreover, when the production amount (density) reaches a certain level or more, the short-time bake hardenability is remarkably improved, and high paint bake strength that cannot be obtained by a general production method can be obtained. Further, due to the interaction between the high-density cluster II and the pores and the reduction of the degree of supersaturation, the change with time at room temperature can be suppressed, and the deterioration of the strength after baking with coating due to the room temperature can be minimized.
In the manufacturing method of the aluminum alloy sheet for forming according to the present invention, after the solution treatment at 480 ° C. or higher, cooling is performed at a cooling rate of 100 ° C./min (min) or higher in a temperature range of 70 ° C. or higher and 90 ° C. or lower. You can also.
By cooling at this cooling rate, precipitation at the grain boundary can be prevented, and deterioration of formability and hemmability can be suppressed.
When it hardens below 70 degreeC, there exists a possibility that the fall of bake sclerosis | hardenability may become large. On the other hand, when directly quenching in a temperature range of 90 ° C. or higher, there is a possibility that a decrease in moldability becomes large. If the residence time exceeds 10 minutes, high-performance bake hardenability may not be obtained.
Further, a treatment for retaining the 0.2% proof stress at 140 MPa or higher in a temperature range of 90 ° C. or higher and 150 ° C. or lower is performed.
In order to obtain a higher performance bake hardenability, the first stage comparative low temperature preliminary aging is performed, and then the higher temperature second stage preliminary aging is performed.
As described above, the higher the preliminary aging temperature is, the more stable the cluster II structure and configuration are obtained, and these tend to shift to the β ″ phase that contributes to strength at the time of paint baking, so that high strength is obtained after paint baking. .
In addition, a large amount of stable cluster II exists as a result of retention so that the 0.2% proof stress is 140 MPa or more, and the maximum exothermic peak is observed between 220 ° C. and 350 ° C. in the DSC measurement. Is 0.09 W / g or less. As a result, it is possible to minimize the deterioration of the bake hardenability due to the aging of the room temperature due to the interaction between a large amount of the stable cluster II and pores and the reduction of the degree of supersaturation. ) It is possible to obtain a high paint bake strength with a 0.2% proof stress after painting and baking of the material of 240 MPa or more and an increase of 90 MPa or more during the aging period. When emphasizing the balance with formability, the second stage preliminary aging is preferably performed at 90 to 130 ° C.
  In the aluminum alloy sheet for forming according to the present invention, for the sake of convenience, as a typical condition, it is defined by a proof stress value or the like when “the material is stretched 2% and then baked at 170 ° C. for 20 minutes”. However, this rule does not mean that the aluminum alloy sheet for forming according to the present invention is used only under the paint baking conditions. In other words, any one may be applied as long as it is within the range of general conditions of coating baking at 140 to 230 ° C. for about 10 to 120 minutes after stretching in the range of 0 to 5%. Of course, in that case, it is necessary to experimentally obtain a proof stress value corresponding to each paint baking condition.
  Examples of the present invention will be described below together with comparative examples. The following examples are for explaining the effects of the present invention, and the processes and conditions described in the examples do not limit the technical scope of the present invention. The following example is an example showing the effect.
  Alloys of alloy symbols A1 to A4 within the composition (mass%) range shown in Table 1 were melted in accordance with conventional methods and cast into slabs by DC casting.
Each obtained slab was homogenized at 530 ° C. for 5 hours. After the homogenization treatment, a plate having a thickness of 1 mm was formed in the hot rolling process and the cold rolling process. Then, the process of this invention was given with respect to the obtained raw material on the manufacturing conditions shown in Table 2. In addition, the average cooling rate cooled to the 80-150 degreeC temperature range after the solution treatment shown in Table 2, or the 70-90 degreeC temperature range is 500 degrees C / min. Moreover, the temperature rising time from the temperature of the aging treatment 1 of Example 2 to the temperature of the aging treatment 2 is within 5 minutes.
In the production conditions shown in Table 2, production number 1, production number 2, production number 3, production number 4, and production number 5 are invention examples, production number 6, production number 7, and production number 8 are comparative examples.
Various characteristics evaluation was performed about each board obtained as mentioned above.
In the characteristic evaluation, after standing at room temperature (25 ° C.) for 10 days in consideration of aging at room temperature, a tensile test is performed to obtain a 0.2% proof stress value (YS1) as mechanical strength, and strength after baking. A 0.2% proof stress value (ABYS1) was measured. Further, after standing at room temperature (25 ° C.) for 90 days, 0.2% proof stress value was measured as mechanical strength (YS2), and 0.2% proof stress value (ABYS2) was measured as strength after baking. . YS2-YS1 was used as an index for evaluation of changes over time. An increase in 0.2% proof stress after paint baking was evaluated by ABYS1-YS1 and ABYS2-YS2.
Further, for each plate left at room temperature (25 ° C.), the overhang height was measured as moldability evaluation.
Overhang test:
A masking film was pasted on both sides of a 1 mm plate having a size of 200 mm × 200 mm, and in order to further improve lubrication, it was subjected to a bulge test in a state where wax was applied, and the maximum bulge height was examined. A punch having a ball head punch diameter of 100 mm was used.
  After that, each plate left at room temperature (25 ° C.) for 10 days and 90 days is stretched by 2%, and then subjected to a coating baking process of 170 ° C. × 20 minutes, and each plate after baking is subjected to a tensile test, The 0.2% proof stress value was measured as the mechanical strength and used as an index for bake hardenability (BH property) evaluation.
Specifically, the coating baking process is performed using a material added with 2% stretch, and an average temperature increase rate of about 80 ° C./min in an oil bath from normal temperature (from 0 ° C. to 45 ° C., usually 20 ° C.) to 170 ° C. After heating to 170 ° C and holding at this temperature for 20 minutes, take it out from the oil bath and let it cool naturally (normally about 50 ° C / min.) Until it reaches 50 ° C or less in a normal temperature environment (about 20 ° C) I went there.
Here, 2% stretch was applied in the paint baking process because the material stayed at an automobile maker, and after the aging at room temperature, the strain generated after pressing during the press-assembly-painting manufacturing process was experimentally tested. It is a simulation.
Since the proof stress value varies depending on the state of the material and the coating baking condition, it is often necessary to stretch the coating baking process in order to generally approximate the state of the material to be subjected to coating baking in an automobile manufacturer.
The results of the above various evaluations are shown in Table 3 as the material performance of the final plate.
  The DSC measurement in Table 3 uses a Diamond DSC manufactured by PerkinElmer, the sample weight is about 50 mg, 99.99% high-purity aluminum is used as a reference (reference material), and the heating rate is 40 ° C./min. The temperature range was 20 ° C. to 500 ° C., and the exothermic and endothermic peak heights were measured based on the baseline measured using a reference (no exothermic and endothermic peaks). The horizontal axis represents temperature, and the vertical axis represents heat energy index (W / g) of heat generation and endotherm.
As shown in Tables 1 to 3, production numbers 1 to 5 are all within the range specified by the present invention for the component composition of the alloy, and the manufacturing process conditions are also within the range specified by the present invention. The aluminum alloy plates for forming with the production numbers 1 to 5 have a high bake hardenability, exhibit a sufficient bake hardenability at the time of paint baking, and the material strength (proof stress) changes over time for 3 months. The maximum is 12 MPa of production number 4 and is small.
Therefore, those with production numbers 1 to 5 can be suitably used for automobile body sheets where bake hardenability (BH) and formability are important.
  Specifically, production number 1 has a 0.2% proof stress of 142 MPa (10 days at room temperature) after production and before baking, and a 0.2% proof stress of 152 MPa at 90 days at room temperature. The condition that the 0.2% proof stress is 140 MPa or more is satisfied. Further, after the material is stretched by 2%, it is 0.2% proof stress after coating baking at 170 ° C. for 20 minutes {hereinafter referred to as “baking curability (BH)”. } Is 250 (90-day lapse, 10-day lapse) MPa, satisfying the condition of 240 MPa or more, and the increase in yield strength due to paint baking is as large as 108 MPa (10-day lapse) and 98 MPa (90-day lapse). The condition of the present invention in which the minute is 80 MPa or more is satisfied. The overhang height was 36.7 (90 days elapsed) to 36.9 (10 days elapsed) mm, and sufficient moldability was exhibited. Also, after standing at room temperature (25 ° C.) for 10 days, a tensile test was performed to measure a 0.2% proof stress value (YS1), and after leaving at room temperature (25 ° C.) for 90 days, a 0.2% proof stress value was obtained. The (YS2-YS1) value, which was used as an index for evaluation of the change with time based on the measured value (YS2), was as extremely low as 10 MPa, and the aging property was good.
In addition, this production number 1 was manufactured at a temperature of 560 ° C. or higher and then cooled at an average cooling rate of 500 ° C./min, and a residence temperature of aging treatment 1 was 102 ° C.
Therefore, production number 1 is a temperature range of 80 ° C. or higher and 150 ° C. or lower after cooling at a cooling rate of 100 ° C./min (min) or higher in a temperature range of 80 ° C. or higher and 150 ° C. or lower after solution treatment at 480 ° C. or higher. Thus, it was manufactured under the condition that the 0.2% proof stress of the alloy plate is retained so as to be 140 MPa or more.
After performing the solution treatment at 480 ° C. or higher, after cooling at a cooling rate of 100 ° C./min (min) or higher to a temperature range of 80 ° C. or higher and 150 ° C. or lower, the alloy plate is heated to 0 ° C. or higher and 150 ° C. or lower. It was manufactured by satisfying the condition that the 2% proof stress was retained to be 140 MPa or more.
Therefore, production number 1 corresponds to the implementation of the method for producing an aluminum alloy sheet for forming according to the present invention.
  In production number 2, the 0.2% yield strength after production and before baking is 151 MPa (room temperature aging 10 days), the room temperature aging 90 days 0.2% proof stress is 152 MPa, and 0.2% of the material in advance. The condition that the proof stress is 140 MPa or more is satisfied. In the DSC measurement results after 90 days, the maximum exothermic peak height is 0.045 W / g when the measurement temperature range is 20 ° C. to 500 ° C., and the maximum exothermic peak height is 0.09 W / g. The following conditions are satisfied. Furthermore, the bake hardenability (BH) after baking at 170 ° C. for 20 min after 2% stretching is 258 (90-day aging) to 259 (10-day aging) MPa, and room temperature (0 to 45 ° C.) within 3 months. The condition that the 0.2% proof stress after painting and baking of the material is 240 MPa or more during the aging period is satisfied. Further, the increase in yield strength due to paint baking is as large as 108 MPa (10 days elapsed) and 98 MPa (90 days elapsed), the increase is 80 MPa or more, the present invention conditions are satisfied, and the increase is 90 MPa or more. Is satisfied.
  In the production number 2, the overhang height was 37.1 (90 days elapsed) to 37.3 (10 days elapsed) mm, and sufficient moldability was exhibited. Also, after standing at room temperature (25 ° C.) for 10 days, a tensile test was performed to measure a 0.2% proof stress value (YS1), and after leaving at room temperature (25 ° C.) for 90 days, a 0.2% proof stress value was obtained. The (YS2-YS1) value, which was used as an index for evaluation of the change with time based on the measured value (YS2), was as extremely low as 9 MPa, and the change over time was good.
  In addition, since the retention temperature of the aging treatment 1 after the solution treatment is 81 ° C. and the residence time is 0.03 hours, the production number 2 is said to be retained in a temperature range of 80 ° C. or more and 150 ° C. or less. The conditions were fulfilled, and at the same time, the conditions of staying for 10 minutes or less in a temperature range of 70 ° C. or more and less than 90 ° C. were fulfilled. Furthermore, the aging treatment 2 after the aging treatment 1 was also performed under the condition that the temperature was 103 ° C. and the residence time was 12 hours, and the residence was performed in a temperature range of 90 ° C. or more and 150 ° C. or less.
Further, in production number 3, the 0.2% proof stress after production and before paint baking is 159 MPa (10 days at room temperature), the 0.2% proof stress at 90 days at room temperature is 162 MPa, and 0.2% of the material in advance. The condition that the% proof stress is 140 MPa or more is satisfied. Also, after stretching the material by 2%, after baking at 170 ° C. for 20 minutes, the 0.2% proof stress is 242 (90 days elapsed, 10 days elapsed) MPa, satisfying the condition of 240 MPa or more, and by coating baking The increase in yield strength is as large as 83 MPa (10 days elapsed) and 80 MPa (90 days elapsed), and the increase is 80 MPa or more.
Further, the overhang height was 37.3 (90 days elapsed) to 37.6 (10 days elapsed) mm, and sufficient moldability was exhibited. Also, after standing at room temperature (25 ° C.) for 10 days, a tensile test was performed to measure a 0.2% proof stress value (YS1), and after leaving at room temperature (25 ° C.) for 90 days, a 0.2% proof stress value was obtained. The (YS2-YS1) value, which was used as an index for evaluation of the change with time by the numerical value obtained as the measured (YS2), was as extremely small as 3 MPa, and the aging property was good.
In addition, this production number 3 is cooled at an average cooling rate of 500 ° C./min after performing a solution treatment at 560 ° C. or higher, and is manufactured as a residence temperature of 83 ° C. and a residence time of 42 hours in the aging treatment 1 after the solution treatment. The condition of retaining in a temperature range of 80 ° C. or higher and 150 ° C. or lower was implemented.
Therefore, production number 3 corresponds to the implementation of the method for producing an aluminum alloy sheet for forming according to the present invention.
Furthermore, in the production number 4, the 0.2% proof stress after production and before baking is 155 MPa (normal temperature aging 10 days), the 0.2% proof stress 90 days at normal temperature 90 days is 167 MPa. The condition that the% proof stress is 140 MPa or more is satisfied. In addition, after stretching the material by 2%, after baking at 170 ° C. for 20 minutes, the 0.2% proof stress is 260 MPa (10 days elapsed) and 261 MPa (90 days elapsed), satisfying the condition of 240 MPa or more. The increase in the yield strength due to baking is as large as 105 MPa (10-day lapse) and 94 MPa (90-day lapse), and the conditions of the present invention in which the increase is 80 MPa or more are satisfied.
Further, the overhang height was 36.5 (90 days elapsed) to 36.7 (10 days elapsed) mm, and sufficient moldability was exhibited. Also, after standing at room temperature (25 ° C.) for 10 days, a tensile test was performed to measure a 0.2% proof stress value (YS1), and after leaving at room temperature (25 ° C.) for 90 days, a 0.2% proof stress value was obtained. The (YS2-YS1) value, which was used as an index for evaluation of the change with time by the numerical value obtained as the measured (YS2), was as small as 12 MPa, and the aging property was good.
  In addition, this production number 4 was cooled at an average cooling rate of 500 ° C./min after solution treatment at 560 ° C. or higher, gradually cooled from 120 ° C. to 80 ° C. at 1 ° C./h after solution treatment, and then cooled to 80 ° C. Manufactured by satisfying the condition of staying in a temperature range of 150 ° C. or less, this production number 4 is produced by carrying out the method for producing an aluminum alloy plate for forming according to the present invention, and is suitable for automobile body seats. It corresponds to the aluminum alloy plate for forming process of the present invention that can be used.
Furthermore, in production number 5, the 0.2% proof stress after production and before painting and baking is 160 MPa (room temperature aging 10 days), the 0.2% proof stress 90 days at room temperature aging is 168 MPa. The condition that the% proof stress is 140 MPa or more is satisfied. Also, after stretching the material by 2%, after baking at 170 ° C. for 20 minutes, the 0.2% proof stress is 249 MPa (10 days elapsed) and 248 MPa (90 days elapsed), satisfying the condition of 240 MPa or more. The increase in the yield strength due to baking is 89 MPa (10-day lapse) and 80 MPa (90-day lapse), and the conditions of the present invention in which the increase is 80 MPa or more are satisfied.
Further, the overhang height was 36.9 (90 days elapsed) to 37.2 (10 days elapsed) mm, and sufficient moldability was exhibited. Also, after standing at room temperature (25 ° C.) for 10 days, a tensile test was performed to measure a 0.2% proof stress value (YS1), and after leaving at room temperature (25 ° C.) for 90 days, a 0.2% proof stress value was obtained. The (YS2-YS1) value, which was used as an index for evaluation of the change with time by the numerical value obtained as the measured (YS2), was as small as 8 MPa, and the change with time was good.
  In addition, this production number 5 was cooled at an average cooling rate of 500 ° C./min after solution treatment at 560 ° C. or higher, and after the solution treatment, gradually cooled from 88 ° C. to 80 ° C. at 80 ° C./h to 80 ° C. It is manufactured while satisfying the condition of retaining in a temperature range of 150 ° C. or less, and this production number 5 corresponds to the implementation of the method for producing an aluminum alloy sheet for forming according to the present invention.
On the other hand, with regard to the production numbers 6 and 7, the alloy composition was within the range defined by the present invention, and the aging treatment 1 was performed under the production process conditions. However, in the production number 6, the condition that the retention temperature of the aging treatment 1 after the solution treatment is 70 ° C. and is retained in the temperature range of 80 ° C. or more and 150 ° C. or less is not implemented. It does not correspond to the method of manufacturing the aluminum alloy plate for forming according to the invention.
In addition, since sufficiently stable high temperature cluster II generation processing has not been implemented in advance, the balance is lost and the bake hardenability (BH) is reduced to 226 MPa, which satisfies the conditions of the aluminum alloy sheet for forming according to the present invention. Therefore, it is unsuitable for automobile body sheets where bake hardenability (BH) is important.
  On the other hand, in the production number 7, as the aging treatment 1 after the solution treatment, the treatment is allowed to stand at room temperature of 15 to 30 ° C., and the treatment for staying in the temperature range of 80 ° C. to 150 ° C. is not performed. No. 7 does not correspond to the implementation of the manufacturing method of the aluminum alloy plate for forming according to the present invention. As a result, a large amount of cluster I is produced, and the bake hardenability (BH) is greatly reduced to 136 MPa, which does not satisfy the conditions of the aluminum alloy sheet for forming according to the present invention. Therefore, the bake hardenability (BH) is low. It is not suitable for car body seats that are important.
On the other hand, in production number 8, the alloy component composition is within the range specified in the present invention, and the residence temperature of aging treatment 1 after solution treatment is 90 ° C., and the temperature range is 80 ° C. or more and 150 ° C. or less. The process to make it stay is performed. However, the 0.2% proof stress after manufacturing and before baking is 128 MPa (10 days at room temperature), and the 0.2% proof stress of the alloy plate is 140 MPa or higher in the temperature range of 80 ° C. or higher and 150 ° C. or lower. The condition of the present invention to be retained is not satisfied.
Production No. 8 has a bake hardenability (BH) of 215 MPa and does not satisfy the conditions of this invention in which the 0.2% proof stress is 240 MPa or more after baking at 170 ° C. for 20 minutes. Therefore, it cannot be applied to an automobile body sheet where bake hardenability (BH) is important.
  The forming aluminum alloy sheet and the forming aluminum alloy sheet manufacturing method according to the present invention are such that the strength of the material before baking is higher than that of a normal material during a short period of normal temperature (for example, 15 days after manufacture). Therefore, it is within the allowable range of molding of automobile body sheet materials, and is especially suitable for automobile body sheets that emphasize strength after paint baking.

Claims (7)

  1. An aluminum alloy ingot made of an Al-Mg-Si-based or Al-Mg-Si-Cu-based alloy is subjected to a rolling process and a heat treatment process including heating and cooling to obtain a rolled sheet having a required thickness. Then, after the solution treatment, the material is made to have a 0.2% proof stress of 140 MPa or more in advance by an artificial preliminary aging treatment, and after stretching the material by 2% during a normal temperature (0 to 45 ° C.) time period within at least 3 months, 170 An aluminum alloy sheet for forming, which has a 0.2% proof stress of 240 MPa or more after baking at 20 ° C. for 20 minutes.
  2. The aluminum alloy sheet for forming according to claim 1, wherein the 0.2% yield strength increase due to paint baking is 80 MPa or more.
  3. 2. A high scanning baking strength with a maximum baking peak of 0.09 W / g or less and an increase due to coating baking of 90 MPa or more as measured by a differential scanning calorimeter (DSC). Aluminum alloy plate for forming.
  4. Mg 0.2-1.5% (mass%, the same shall apply hereinafter), Si 0.3-2.0%, Mn 0.03-0.6%, Cr 0.01-0.4%, Zr0.01 Ti 0.005 to 0.2% allowed to accompany B of ~ 0.4%, V 0.01 to 0.4%, Fe 0.03 to 1.0%, 0.0001% to 0.0500% The aluminum alloy plate for forming according to any one of claims 1 to 3, comprising one or more selected from among the above, with the balance comprising Al and inevitable impurities.
  5. The aluminum alloy plate for forming according to any one of claims 1 to 4, comprising one or two of Zn 0.03-2.5% and Cu 0.05-1.5%.
  6. After performing the solution treatment at 480 ° C. or higher, after cooling at a cooling rate of 100 ° C./min (min) or higher to a temperature range of 80 ° C. or higher and 150 ° C. or lower, the alloy plate is heated at a temperature range of 80 ° C. or higher and 150 ° C. or lower. The method for producing an aluminum alloy sheet for forming according to claim 1, wherein the 2% proof stress is retained so as to be 140 MPa or more.
  7. After performing the solution treatment at 480 ° C. or higher, after cooling at a cooling rate of 100 ° C./min (min) or higher in a temperature range of 70 ° C. or higher and 90 ° C. or lower, the temperature range of 70 ° C. or higher and lower than 90 ° C. is 10 minutes or lower. The manufacturing method of the aluminum alloy plate for shaping | molding of Claim 3 which makes it retain so that the 0.2% yield strength of an alloy plate may become 140 Mpa or more again in the temperature range of 90 to 150 degreeC.
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CN102732759A (en) * 2011-03-31 2012-10-17 株式会社神户制钢所 Aluminum alloy plate for formation processing and manufacturing method thereof
JP2014218734A (en) * 2013-04-09 2014-11-20 株式会社神戸製鋼所 Aluminum alloy sheet for press molding, manufacturing method therefor and press molded body thereof
KR101476284B1 (en) * 2014-09-30 2014-12-24 유선상 Al-Si-Mg Aluminum alloy and manufacturing method thereof
WO2015151907A1 (en) * 2014-03-31 2015-10-08 株式会社神戸製鋼所 Aluminum alloy plate having excellent moldability and bake finish hardening properties
WO2015151908A1 (en) * 2014-03-31 2015-10-08 株式会社神戸製鋼所 Aluminum alloy plate having excellent moldability and bake hardening properties
JP2015196853A (en) * 2014-03-31 2015-11-09 株式会社神戸製鋼所 Aluminum alloy sheet excellent in moldability and coating/baking hardenability
JP2015196854A (en) * 2014-03-31 2015-11-09 株式会社神戸製鋼所 Aluminum alloy sheet excellent in moldability and coating/baking hardenability
CN105506408A (en) * 2015-12-18 2016-04-20 百色学院 Die casting aluminum alloy for automobile plates and production technology of die casting aluminum alloy
EP2964800B1 (en) 2013-03-07 2017-08-09 Aleris Aluminum Duffel BVBA Method of manufacturing an al-mg-si alloy rolled sheet product with excellent formability
CN109666824A (en) * 2019-01-29 2019-04-23 中铝材料应用研究院有限公司 High-intensitive Al-Mg-Si-Mn wrought aluminium alloy and preparation method thereof

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EP2964800B1 (en) 2013-03-07 2017-08-09 Aleris Aluminum Duffel BVBA Method of manufacturing an al-mg-si alloy rolled sheet product with excellent formability
JP2014218734A (en) * 2013-04-09 2014-11-20 株式会社神戸製鋼所 Aluminum alloy sheet for press molding, manufacturing method therefor and press molded body thereof
WO2015151907A1 (en) * 2014-03-31 2015-10-08 株式会社神戸製鋼所 Aluminum alloy plate having excellent moldability and bake finish hardening properties
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JP2015196853A (en) * 2014-03-31 2015-11-09 株式会社神戸製鋼所 Aluminum alloy sheet excellent in moldability and coating/baking hardenability
JP2015196854A (en) * 2014-03-31 2015-11-09 株式会社神戸製鋼所 Aluminum alloy sheet excellent in moldability and coating/baking hardenability
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WO2015151908A1 (en) * 2014-03-31 2015-10-08 株式会社神戸製鋼所 Aluminum alloy plate having excellent moldability and bake hardening properties
KR101476284B1 (en) * 2014-09-30 2014-12-24 유선상 Al-Si-Mg Aluminum alloy and manufacturing method thereof
CN105506408A (en) * 2015-12-18 2016-04-20 百色学院 Die casting aluminum alloy for automobile plates and production technology of die casting aluminum alloy
CN109666824A (en) * 2019-01-29 2019-04-23 中铝材料应用研究院有限公司 High-intensitive Al-Mg-Si-Mn wrought aluminium alloy and preparation method thereof

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