JP5435914B2 - Method for producing aluminum alloy plate for cold press forming, method for cold press forming aluminum alloy plate, and aluminum alloy cold press formed product - Google Patents

Method for producing aluminum alloy plate for cold press forming, method for cold press forming aluminum alloy plate, and aluminum alloy cold press formed product Download PDF

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JP5435914B2
JP5435914B2 JP2008226006A JP2008226006A JP5435914B2 JP 5435914 B2 JP5435914 B2 JP 5435914B2 JP 2008226006 A JP2008226006 A JP 2008226006A JP 2008226006 A JP2008226006 A JP 2008226006A JP 5435914 B2 JP5435914 B2 JP 5435914B2
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aluminum alloy
heat treatment
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cold press
heating
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JP2009161851A (en
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旭 日比野
幸司 一谷
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株式会社Uacj
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  The present invention relates to an Al-Mg-Si-based aluminum alloy plate used for forming processing, particularly cold press forming or paint baking, a manufacturing method thereof, and a cold press forming method using the same. Al-Mg-Si suitable for use in various parts and parts of automobiles, ships, aircraft, etc., building materials, structural materials, other various machinery and appliances, home appliances and parts thereof, especially automobile body sheets and body panels This is about the aluminum alloy plate.

Conventionally, cold rolled steel sheets have been mainly used as body seats for automobiles. Recently, however, reduction of CO 2 emissions has been demanded from the viewpoint of global warming suppression. As a result of recognition, the use of rolled aluminum alloy sheets is increasing. By the way, since the formability of an aluminum alloy rolled sheet is generally inferior to that of a cold-rolled steel sheet, it is an obstacle to expanding its use. In order to improve the formability of the rolled aluminum alloy sheet, improvement of the formability of the material itself and a device for the forming method are strongly demanded.

  Further, in this type of application, since it is usually used after being subjected to paint baking, a characteristic (bake hardenability, that is, BH property) capable of obtaining high strength after paint baking is required.

  Patent Documents 1 and 2 propose applying a warm deep drawing method in order to improve the formability of an aluminum alloy plate. Certainly, the warm forming method can improve the deep drawability of the aluminum alloy sheet, but there are some problems if large-scale industrial production is assumed.

That is, as a feature of the warm deep drawing method, it is required to perform deep drawing while the flange portion is heated and the punch portion is cooled.
1. It is necessary to provide the press machine with heating and cooling functions for the aluminum alloy sheet. Compared with cold press forming, the total forming time is longer, resulting in lower production efficiency and lower forming costs. To increase.
2. Since the molding is performed warmly, the usual cold forming lubricating oil cannot be used, and therefore, it is necessary to develop a new lubricating oil.
3. The configuration of the press machine becomes complicated and requires high equipment costs.
4). As press machines become more complex, concerns about quality control arise.
There are problems such as.

  By the way, the warm deep drawing method is to locally heat and soften a portion having a high degree of processing with respect to the aluminum alloy plate blank at the time of forming, so if it is caught at the time of forming, the aluminum alloy plate blank It can be said that it is intended to improve the formability by partially imparting a strength difference to the other, but in the same way, other strengths that are intended to improve the formability by giving a strength difference to the aluminum alloy sheet blank. As a method, a method in which a blank is subjected to local heat treatment in advance is known (for example, Patent Document 3). This method is particularly suitable for age-hardening alloys such as Al-Mg-Si alloys, which are mainly used for automobile body sheets, in which solid solution precipitation occurs in the matrix due to heat treatment and the strength changes greatly. It is considered effective.

  Here, in the technique disclosed in Patent Document 3, while an Al—Mg—Si based alloy sheet that is shipped after being solution-treated by an aluminum rolling manufacturer is held at room temperature, Mg and Si can be obtained by aging at room temperature. It is possible to give a strength difference in the blank by utilizing the fact that extremely fine precipitates consisting of uniform precipitates in the matrix and the strength is improved compared to immediately after the solution treatment. Is going. That is, in the technique of Patent Document 3, the above-described precipitate formed at room temperature is easily re-solidified by short-time heating at a relatively low temperature of 250 ° C. or more, and the strength of the heated portion is reduced. By utilizing this, it is said that a partial strength difference can be imparted to the aluminum alloy plate by a relatively low-cost and short-time treatment.

By the way, the technique disclosed in Patent Document 3 is a technique for improving formability on the premise that a blank of an aluminum alloy plate is press-molded in a state where the periphery is clamped and the periphery is completely fixed. In the blank surface, the area directly under the punch to which the punch hits during press molding is heated and softened except for the area to which the shoulder of the punch hits to improve the formability. However, in this case, the strain is concentrated in the region immediately below the softened punch, and it has been found that there is a problem in that the thickness of the molded product is insufficient due to significant local thickness reduction in this portion. Further, since press molding is performed with the periphery completely fixed by a clamp, there is a disadvantage in that material inflow from the peripheral wrinkle pressing portion is not allowed at all, and thus the width of improvement in formability is limited. Further, in the case of a body sheet for automobiles, after press molding, bending (hem processing) is often performed in the peripheral portion of the molded product. In other words, the center part of the plate is heated, and the peripheral part of the plate remains in an aging-precipitated state due to normal temperature aging, and the bending workability is remarkably deteriorated in that part, and cracks are generated in the bent part. There was a problem.
JP-A-4-351229 JP 2006-205244 A JP 2000-117338 A

  In forming the Al—Mg—Si based alloy plate according to the conventional technique as described above, it has been difficult to sufficiently satisfy the formability and other performances required for the recent automobile body sheet.

  That is, recently, a high designability is required for the shape of an automobile panel, and accordingly, a material having a higher formability than that of a conventional material is required, and a material having a particularly high drawability is required. Of course, it is required to improve not only the formability index such as drawability but also the bendability (hem workability) and the deterioration of strength, etc. Although high productivity of the forming process is required, the conventional Al-Mg-Si alloy plate forming method is still insufficient in these respects.

  The present invention has been made against the background of the above circumstances, and it is possible to achieve both the securing of the high formability of the Al-Mg-Si based aluminum alloy sheet and the maintenance of the high productivity of the forming process, and other required characteristics. It is an object of the present invention to provide an aluminum alloy plate excellent in formability, a manufacturing method thereof, and a press forming method, which can skillfully utilize the difference in material strength without causing deterioration of the material. .

  Specifically, the press part around the drawing in cold drawing, based on the technology that gives a difference in strength in the surface by partial heat treatment (restoration treatment) in advance to the aluminum alloy sheet blank. In order to allow material inflow from the material, the material flow from the periphery of the blank is promoted by performing cold deep drawing on the blank that has been optimized by appropriately adjusting the heating site by partial reconstitution heat treatment. This makes it possible to produce molded products with a uniform plate thickness and deep drawing, and at the same time facilitating bending work performed on the periphery of the molded product, while maintaining paint bake hardenability in the heating section. However, an object of the present invention is to make the heat treatment performed in advance a short-time treatment so as not to impair the high production efficiency of the conventional cold press forming.

  As a result of repeated various experiments and studies to solve the above-mentioned problems, the present inventors have drawn aged aluminum alloy sheets, that is, aluminum alloy sheets subjected to room temperature aging or artificial aging after solution treatment. It is important to optimally select the heating part in the partial restoration heat treatment so as to improve the workability and bending workability, and the heating ultimate temperature in this partial restoration heat treatment, the temperature rise rate during heating, By optimizing the cooling rate after heating, the part can be softened efficiently in a very short time by restoring it, the bendability can be improved, and high paint bake hardenability can be imparted As a result, the present inventors have found that this is possible.

  Here, the term “restore” means that the age-hardening type aluminum alloy is rapidly cooled after solution treatment, and the alloy element is supersaturated at room temperature, and then held at room temperature or slightly higher temperature in the matrix. It means a phenomenon in which after a very fine precipitate is deposited to improve the strength and then heated to a temperature higher than the holding temperature for a short time, the fine precipitate is re-dissolved to reduce the strength. And in order to cause such a phenomenon, the process which heats the material after holding | maintenance after a solution treatment is called the restoration | repair heat processing. Here, the partial restoration heat treatment is to selectively heat only a predetermined portion (region) in the plane of the aluminum alloy sheet blank for the purpose of improving formability and bendability. It means a process of restoring and softening only the predetermined part.

Specifically, the manufacturing method of the aluminum alloy sheet for cold press forming according to the first aspect of the invention uses an Al—Mg—Si-based aluminum alloy rolled sheet rolled to a predetermined sheet thickness as a raw material, and is 480 to 590 ° C. After the solution treatment at a temperature within the range of, the area to be sandwiched between wrinkle pressers during cold press molding is further cured by age hardening so that the 0.2% proof stress is 90 MPa or more. The part to be pressed against the heating part is determined as a non-heated part, and as a partial restoration heat treatment for the heating part, before cold press molding, the temperature is increased from 30 ° C./min to 150 ° C. to 350 ° C. After heating to a temperature within the range, holding at the temperature within the range for 5 minutes or less (including 0 seconds), and then cooling to a temperature of 100 ° C. or less at a cooling rate of 30 ° C./min or more. The non-heated part and the additive Difference 0.2% proof stress after cold cooling parts - the value of [(0.2% proof stress of the non-heated part) (0.2% proof stress of the heated part)] as above 10 MPa, the heating section 0.2 An aluminum alloy plate having a% proof stress of 141 MPa or less is obtained .
Here, the value of 0.2% yield strength difference [(0.2% yield strength of non-heated portion) − (0.2% yield strength of heated portion)] is 0.2% yield strength (MPa) of non-heated portion. ) Means a value obtained by subtracting 0.2% proof stress (MPa) of the heating part.

Furthermore, the invention of claim 2 is the method for producing an aluminum alloy sheet for cold press forming according to claim 1 , wherein the partial restoring heat treatment is used to obtain the tensile strength of the non-heated part and the 0.2% yield strength of the heated part. The value of [(tensile strength of the non-heated part) − (0.2% proof stress of the heated part)] is increased by 20 MPa or more before and after the partial restoration heat treatment.
Here, the difference between the tensile strength of the non-heated part and the 0.2% yield strength of the heated part [(tensile strength of the non-heated part) − (0.2% yield strength of the heated part)] It means a value obtained by subtracting a value of 0.2% proof stress (MPa) of a heated part from a value of tensile strength (MPa).

The invention of claim 3 is a method of performing cold press forming using an aluminum alloy plate for cold press forming manufactured by the method described in claim 1 or 2. Then, after the partial restoration heat treatment, cold press molding is performed before the standing period at room temperature passes 30 days.

Further, the cold press forming method of the aluminum alloy plate of the invention of claim 4 is an aluminum alloy plate for cold press forming manufactured by the method of claim 1 or claim 2. Using the aluminum alloy before the strength of the heated portion returns to the state before the partial reconstitution heat treatment by aging precipitation during holding at room temperature after the partial reconstitution heat treatment. A sheet blank is cold-press formed.

And also the invention of請Motomeko 5, claim 1, in cold press forming method for an aluminum alloy sheet according to any one of claims 2, to the heating part in the partial reversion heating treatment, the aluminum alloy plate Of the blank, the portion outside the region where the punch shoulder is in contact during press molding is included, and the portion to be bent after molding is included.

Furthermore, the invention of claim 6 is the cold press forming method of the aluminum alloy sheet according to any one of claims 1 and 2 , wherein the heating part in the partial restoration heat treatment is provided with an aluminum alloy during press forming. All the area | regions inside the area | region which a punch shoulder part contacts among board blanks, or one area | region or two areas or more of arbitrary shapes in this area | region are characterized by the above-mentioned.

The invention of claim 7 is a molded product obtained by the cold press forming method of an aluminum alloy plate according to any one of claims 3 and 4, and after the partial restoration heat treatment The proof stress value of the heating part is improved by 20 MPa or more by the artificial aging treatment performed before 30 days have passed.

The method for producing an aluminum alloy plate for cold press forming according to claim 8 is the method for producing an aluminum alloy plate for cold press forming according to any one of claims 1 and 2 , wherein: -As Mg-Si based aluminum alloy plate, Mg 0.2-1.5%, Si 0.3-2.0%, and Fe 0.03-1.0%, Mn 0.03-0.6%, Cr 0.01-0.4%, Zr 0.01-0.4%, V 0.01-0.4%, Ti 0.005-0.3%, Zn 0.03-2.5%, Cu 0.01-1 It is characterized by using an aluminum alloy plate containing one or more selected from 5%, the balance being Al and inevitable impurities.

In addition, as an aspect relevant to the present invention, there are the following aspects (1) to (8).
(1) In a cold press forming method to which a process of cold press forming using a punch is performed by pressing an end of an Al-Mg-Si aluminum alloy sheet blank which has been aged by normal temperature aging, Among the aluminum alloy plate blanks, all or a smaller part of the outer part than the region where the punch shoulder is in contact at the time of press forming is determined as a heating part, and the part other than the heating part is not By defining the heating part and heating the heating part rapidly, the aging precipitate is temporarily dissolved and softened, and by not heating the non-heating part, the strength of the heating part is compared with the strength of the non-heating part. After that, a partial recovery heating process is performed in which the temperature of the heating part is rapidly cooled to room temperature, and then the heating part is strengthened by aging precipitation while maintaining the room temperature. In but before returning to the state before the partial reversion heating treatment, characterized in that the aluminum alloy sheet blank to cold press molding, cold press forming method for an aluminum alloy plate.
(2) After the solution treatment, artificial aging at 140 ° C. or lower is applied, or aging treatment is performed by combining aging at normal temperature and artificial aging at 140 ° C. or lower, and in a sub-aging state, and 0.2% proof stress Cold press forming method using an Al-Mg-Si based aluminum alloy plate having a value of 90 MPa or more, pressing the end of the aluminum alloy plate blank and applying a cold press forming using a punch In the aluminum alloy plate blank, the whole or a part smaller than the region outside the region where the punch shoulder is in contact during press molding is defined as a heating portion, and other than the heating portion. The part is defined as a non-heated part, and by rapidly heating the heated part, the aging precipitates are temporarily dissolved and softened, and the non-heated part is added. By doing so, after the strength of the heated part is reduced compared to the strength of the non-heated part, a partial restoration heat treatment is performed in which the temperature of the heated part is rapidly cooled to room temperature, and then by aging precipitation while maintaining the room temperature. A method of cold press forming an aluminum alloy plate, wherein the aluminum alloy plate blank is cold press formed before the strength of the heating part returns to the state before heating.
(3) In the cold press forming method of the aluminum alloy plate according to the above aspect (1) or (2),
  As the partial restoration treatment, after heating to a temperature in the range of 150 to 350 ° C. at a temperature increase rate of 30 ° C./min or more and holding for 5 minutes or less (including 0 seconds) at the temperature in the range A method for cold press forming an aluminum alloy plate, characterized by cooling to a temperature of 100 ° C. or lower at a cooling rate of 30 ° C./min or higher.
(4) In the cold press forming method of the aluminum alloy plate according to the above aspect (1) or (2),
  As the partial restoration heat treatment, heating is performed at a temperature rising rate of 50 ° C./min or more to a temperature within the range of 180 to 350 ° C., and the temperature within the range is maintained for 5 minutes or less (including 0 seconds). After that, it is cooled to a temperature of 100 ° C. or less at a cooling rate of 50 ° C./min or more, so that the difference between the tensile strength of the heated part and the 0.2% proof stress of the non-heated part is measured before and after the partial restoration heat treatment. A method for cold press forming an aluminum alloy plate, characterized by increasing the pressure by 20 MPa or more.
(5) In the cold press forming method of the aluminum alloy plate according to any one of the above aspects (1) to (4),
  In the heating part in the partial restoration heat treatment, the part of the aluminum alloy sheet blank that is to be bent after forming out of the part outside the region where the punch shoulder is in contact during press forming is included. A method for cold press forming an aluminum alloy sheet.
(6) In the cold press forming method of the aluminum alloy plate according to any one of the above aspects (1) to (4),
  All regions inside the region where the punch shoulder portion of the aluminum alloy plate blank contacts with the heating part in the partial restoration heat treatment at the time of press forming, or one region or two regions of any shape in this region A method for cold press forming an aluminum alloy plate, comprising:
(7) A molded article obtained by the cold press molding method of an aluminum alloy plate according to any one of the above aspects (1) to (6),
  An aluminum alloy cold press-formed product characterized in that the yield strength value of the heated portion is improved by 20 MPa or more by an artificial aging treatment that is performed before 30 days have elapsed after the partial restoration heat treatment.
(8) In the cold press forming method of the aluminum alloy plate according to any one of the above aspects (1) to (7),
  As an Al-Mg-Si-based aluminum alloy plate, it contains Mg 0.2-1.5%, Si 0.3-2.0%, and Fe 0.03-1.0%, Mn 0.03-0.6% Cr 0.01-0.4%, Zr 0.01-0.4%, V 0.01-0.4%, Ti 0.005-0.3%, Zn 0.03-2.5%, Cu 0.01- A method for cold press forming an aluminum alloy plate, comprising using an aluminum alloy plate containing one or more selected from 1.5% and the balance being Al and inevitable impurities.

  According to the present invention, Al-Mg-Si based aluminum alloy sheet aged at room temperature after solution treatment, or Al after sublimation by solution aging or artificial aging or a combination of room temperature aging and artificial aging. -The wrinkle holding part of the Mg-Si based aluminum alloy plate is heated (partial recovery heat treatment) to make the part a low-strength part due to the restoration phenomenon, giving a strength difference between the punch shoulder part which is not heated By doing so, it is possible to improve the press formability. Moreover, since such partial restoration heat treatment is performed as a separate process prior to cold press forming, press forming itself can be performed at a high speed by a conventional cold press machine, and thus warm. There is no increase in equipment cost or reduction in production efficiency of the press machine as in the case of forming, and there is no need for special lubricating oil.

  In addition, according to the present invention, the shape freezing property of the molded product is improved by reducing the strength of the wrinkle-pressing portion, and the portion that has become low strength due to the restoration phenomenon has a high curing speed at the time of paint baking, and the strength rapidly recovers. Therefore, high paint bake hardenability (BH property) can be obtained, so that strength deterioration after paint bake can be prevented, and furthermore, by selecting the heating region to be restored optimally, It is also possible to improve the bending workability.

  The aluminum alloy plate used in the present invention is basically an Al-Mg-Si aluminum alloy plate that has been subjected to a solution treatment at a high temperature and then aged by normal temperature aging, or at a high temperature. After solution treatment, artificial aging or an aging treatment combining room temperature aging and artificial aging is performed to assume a sub-aging state. Therefore, the present invention will be described in detail with the main items divided into items.

<Method for producing aluminum alloy sheet for cold press forming>
First, the manufacturing method of the aluminum alloy plate for cold press forming will be explained. Basically, the material of the aluminum alloy blank formed by the forming method of the present invention is a method generally adopted in the aluminum alloy manufacturing industry. Can be manufactured.

  That is, an aluminum alloy melt adjusted to a predetermined component is cast by appropriately selecting a normal melting casting method. Here, the normal melt casting method includes, for example, a semi-continuous casting method (DC casting method), a thin plate continuous casting method (roll casting method, etc.) and the like. Next, the aluminum alloy ingot is subjected to homogenization at a temperature of 480 ° C. or higher. Homogenization treatment mitigates microsegregation of alloying elements during solidification of molten metal, and in the case of containing various transition elements including Mn / Cr, dispersed particles of intermetallic compounds mainly composed of these, This is a process necessary for uniformly and densely depositing in the matrix. The heating time for the homogenization treatment is usually 1 hour or more, and is usually terminated within 48 hours for economic reasons. However, since the heating temperature in this homogenization treatment is close to the heat treatment temperature for heating to the hot rolling start temperature before hot rolling, it is also possible to perform the homogenization processing together with the heat treatment before hot rolling. Before or after this homogenization treatment step, after appropriate chamfering, hot rolling is started in a temperature range of 300 to 590 ° C., and then cold rolling is performed to obtain an aluminum alloy plate having a predetermined thickness. To manufacture. In the middle of hot rolling, in the middle of hot rolling and cold rolling, or in the middle of cold rolling, intermediate annealing may be performed as necessary.

Next, a solution treatment is performed on the aluminum alloy sheet after the cold rolling. This solution treatment is an important step for solid-dissolving Mg 2 Si, 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 Mg 2 Si, simple substance Si particles, etc., and improving ductility and bendability, and also good molding by recrystallization. This is also an important process for obtaining good performance. In order to exhibit these effects, treatment at 480 ° C. or higher is necessary. If the solution treatment temperature exceeds 590 ° C., eutectic melting may occur, so the temperature is set to 590 ° C. or less.

  Here, the solution treatment can be efficiently performed by continuously passing the cold rolled sheet wound in a coil shape through a continuous annealing furnace having a heating zone and a cooling zone. In such a continuous annealing furnace, the aluminum alloy sheet is heated to a high temperature of 480 ° C. or more and 590 ° C. or less when passing through the heating zone, and then rapidly cooled when passing through the cooling zone. Through such a series of treatments, Mg and Si, which are the main alloying elements of the alloy targeted by the present invention, were once dissolved in the matrix at a high temperature, and then rapidly cooled, thereby becoming supersaturated at room temperature. It becomes a state.

<Aging between solution treatment and restoration heat treatment>
In order to give a difference in strength between the heated part and non-heated part of the plate by partial restoration heat treatment, a certain amount of clusters or fine precipitation is caused by room temperature aging (natural aging) during the room temperature standing period after solution treatment. If such clusters or fine precipitates are not generated, there is no recovery phenomenon even in the heating part in the subsequent partial recovery heat treatment, and the partial recovery heat treatment The strength reduction of the heating part is not realized. Therefore, after the solution treatment, it is necessary to leave at room temperature for one day or more before performing the partial restoration heat treatment. In general, the normal temperature standing period from the solution treatment at the material maker to the molding at the molding maker is 10 days or more. The normal temperature aging progresses early in the initial stage, but after about half a year, it becomes difficult to proceed further, so there is no particular upper limit for the normal temperature standing period before the restoration heat treatment. Here, room temperature specifically means a temperature within the range of 0 to 40 ° C.

  In the above description, only the normal temperature aging was described for the aging after the solution treatment, but in the present invention, the aging after the solution treatment and the artificial aging were performed in combination with the normal aging and the artificial aging. Even in such a case, the strength difference can be imparted to the alloy plate blank by the subsequent partial restoration heat treatment. When artificial aging is performed, the strength of the entire alloy sheet blank before partial reheating can be increased earlier than in the case of room temperature aging alone. However, the temperature of artificial aging must be 140 ° C. or less, and the aluminum alloy plate must be in a sub-aging state after the artificial aging treatment. When the temperature of artificial aging exceeds 140 ° C., the precipitate composed of Mg and Si becomes coarse, so that the precipitate is easily solidified in a short time in the subsequent partial recovery heat treatment. It does not melt, so it takes a long time for softening due to restoration, impairing the productivity of press molding. Further, even under conditions of 140 ° C. or lower, when the artificial aging is performed for a long time and the peak aging or the overaging state after this is reached, the precipitates composed of Mg and Si are also coarsened and partially In the heat recovery heat treatment, it does not easily dissolve, and it takes a long time for the recovery. From such a viewpoint, a more preferable artificial aging temperature is less than 100 ° C.

  In the present invention, it is desirable that the proof stress value (0.2% proof stress) is in the range of 90 MPa or more as the material strength immediately after the aging as described above is performed and the next partial restoration heat treatment is performed. If it is less than this value, the strength will be insufficiently reduced at the part that is restored by heating in the subsequent partial restoration heat treatment, so that a sufficient strength difference cannot be imparted and molding is performed. It is difficult to sufficiently improve the property. More preferably, it is desirable that the proof stress value is 110 MPa or more.

<Partial restoration heat treatment>
The most important feature of the present invention is that the Al-Mg-Si-based aluminum alloy sheet aged as described above is subjected to a partial (two-dimensional in-plane location) before cold press forming. As a partial, not a degree meaning) heating (restoring heat treatment), and after cooling at room temperature, the strength difference between the heated part and the non-heated part by the partial restoring heat treatment (0.2%) The difference in yield strength is 10 MPa or more.

  Here, it is known that the deep drawing forming limit is determined by the magnitude relationship between the breaking strength of the punch shoulder and the inflow resistance of the wrinkle holding portion (flange). Aluminum alloy sheets for automobile body sheets are usually left at room temperature from material solution treatment at the manufacturer to press forming by the user, but Al-Mg-Si alloys are age-precipitation hardening type alloys. Therefore, if the room temperature storage period is long, the material strength increases due to room temperature aging during the room temperature storage period. If it is going to be cold press-molded as it is, the inflow resistance of the wrinkle holding part is large, and the press formability is lowered.

  However, if heat treatment is performed for a short time before cold press forming, clusters and fine precipitates formed by room temperature aging (or artificial aging, or a combination of room temperature aging and artificial aging) will decompose and re- Since it is dissolved, a restoring phenomenon of strength reduction occurs in the heated portion. The present invention exactly utilizes such a phenomenon, and the strength reduction amount in that case requires 10 MPa or more.

  That is, the heated part whose strength has been reduced by 10 MPa or more is applied to the wrinkle holding part, and the non-heated part that remains high in strength by normal temperature aging (or artificial aging, or a combination of normal temperature aging and artificial aging) is applied to the punch shoulder, By performing the intermediate press forming, not only the press formability is improved, but also the hem workability and the strength reduction after the coating baking in the heating part can be prevented. In order to further improve the press formability, it is preferable that the difference in strength between the heated portion and the non-heated portion of the plate is 20 MPa or more.

  Furthermore, as a result of further detailed studies by the present inventors, it is essentially effective to expand the difference between the tensile strength of the non-heated part and the yield strength of the heated part at room temperature by 20 MPa or more before and after partial restoration heating. It became clear that. This is because, by giving such a large difference in strength, the material inflow resistance (the proof strength of the wrinkle holding portion) from the wrinkle holding portion, whose strength has been relatively reduced during the drawing process, is reduced. This is because the material strength (tensile strength) of the portion corresponding to the strong punch shoulder can withstand a larger inflow of material, and as a result, deep drawing is possible. As described above, the difference between the tensile strength in the non-heated part and the proof stress in the heated part, which is more important in improving the drawability, can be expanded before and after partial restoration heating. It has been found that it is effective in improving the deep drawability of the alloy plate. In addition, when the increase in the difference between the tensile strength of the non-heated part at room temperature and the proof stress of the heated part before and after the partial restoration heat treatment is less than 20 MPa, the improvement in moldability cannot be sufficiently obtained.

  Here, the tensile strength and proof strength in the state before the partial restoration heat treatment can be considered to be almost uniform in the alloy blank, and the tensile test piece is sampled from an arbitrary position of the alloy plate blank. The tensile strength and the proof strength obtained by performing the above can be regarded as the tensile strength of the non-heated portion and the proof strength of the heated portion before the partial restoration heat treatment, respectively. On the other hand, in the state after the partial restoration heat treatment, the strength is different between the heated part and the non-heated part, so it is necessary to collect a tensile test piece from each part and perform a tensile test. Here, the non-heated part means a part (region) that is not intended to decrease the strength due to the partial restoration heat treatment, but the performance of the partial restoration heat treatment apparatus and the temperature reached in the partial restoration heat treatment Depending on the temperature, the temperature of the non-heated part may rise to some extent due to heat transfer and residual heat from the heating part. When the partial restoration heat treatment is performed in an ideal manner that does not substantially raise the temperature in the non-heated part, the tensile strength of the non-heated part is equivalent to that before the partial restoration heat treatment. In this case, the decrease in the yield strength in the heating part is an increment before and after the partial restoration heat treatment of the difference between the tensile strength of the non-heating part and the yield strength of the heating part at room temperature. On the other hand, depending on the method and conditions of partial recovery heating, the temperature of the non-heated part rises to some extent in the partial recovery heating process, and a slight recovery occurs, and the tensile strength of the non-heated part May decrease slightly. However, even in such a case, as specified in the present invention, if the increase before and after the partial restoration heat treatment about the difference between the tensile strength of the non-heated part and the proof stress of the heated part at room temperature is 20 MPa or more, The press formability of the alloy plate blank can be substantially improved by the partial restoration heat treatment. This is the reason why the increase in the tensile strength of the non-heated part and the difference in yield strength of the heated part before and after the partial restoration heat treatment at room temperature was used as an index in the present invention.

<Details about the part to be subjected to the partial restoration heat treatment>
Next, the part to be heated and the part not to be heated in the partial restoration heat treatment will be described in more detail.

  Basically, as described above, the heating part is selected so that the heated part with low strength hits the wrinkle holding part and the non-heated part with high strength hits the shoulder of the punch, but press forming for deep drawing 1 is schematically shown in FIG. 1, and a portion where partial restoration heating is performed will be described with reference to FIG. In FIG. 1, reference numeral 1 denotes a die, 2 denotes a punch, 3 denotes a shoulder of the punch 2, 4 denotes a wrinkle presser, and 5 denotes an aluminum alloy plate blank. In FIG. 1, in the partial restoration heat treatment, a region A (wrinkle presser 4) that is a portion outside the region B with which the punch shoulder 3 contacts in the aluminum alloy sheet blank 5 during press forming. It is effective to soften all or a smaller part of the side region) as a heating part. As a special case, one or two or more shapes that are partially deepened in the region C inside the region B with which the punch shoulder 3 is in contact (for example, described later) In Example 4 and FIG. 6), as defined in claim 14, one region or two or more regions having an arbitrary shape optimized corresponding to the shape in the region C may be added as a heating unit. It is effective to obtain a good molded product by press molding.

  This invention also solves the problem of low bending workability of molded products, which has been a problem in the prior art where partial heat treatment was applied to an alloy plate blank aged at room temperature to improve formability. Is done. In other words, this is a problem in panels that require bending after forming, but bending after press forming is often a part outside the region B where the punch shoulder is in contact. This can be solved by selectively adding a part to be bent after press molding as a heating part by utilizing that applied to a part of the region A. Item 13 defines. Here, the restoration heat treatment also has the effect of greatly improving the bending workability that has been greatly deteriorated due to normal temperature aging, so that the above-described effects can also be obtained.

<Detailed conditions for partial restoration heat treatment>
As conditions for the partial restoration heat treatment, in claims 6 and 11, heating is performed at a temperature rising rate of 30 ° C./min or more to a temperature in the range of 150 to 350 ° C., and the temperature in the range is 5 After holding for less than a minute (including 0 seconds), it is stipulated to cool to a temperature of 100 ° C. or less at a cooling rate of 30 ° C./min or more. explain.

  In the case of an Al—Mg—Si-based aluminum alloy, the reduction in strength at the heating site as described above by partial recovery heat treatment is heating within 5 minutes in the temperature range of 150 ° C. to 350 ° C. Can be achieved.

  Moreover, in order to make the intensity difference between the heated part and the non-heated part due to the partial restoration heat treatment 10 MPa or more, a rapid temperature increase, specifically, a temperature increase rate of 30 ° C./min or more is required. If the rate of temperature rise is 30 ° C./min or less, the rate of strength reduction due to restoration decreases, and conversely the rate of strength increase due to aging increases, so that a difference in strength can be imparted between the heated part and the non-heated part. It becomes difficult. For the same reason, the heating rate is preferably 50 ° C./min or more, more preferably 100 ° C./min or more.

  Here, when the heating attainment temperature is lower than 150 ° C., it is difficult to give a difference in strength between the heating part and the non-heating part because the rate of strength reduction due to restoration is small. On the other hand, if the temperature reached by heating exceeds 350 ° C., grain boundary precipitation becomes violent and the ductility is lowered.

  The holding time at the reached temperature is within 5 minutes (including the case where the holding time is zero = there is cooling immediately after reaching the predetermined temperature without staying). If the holding time at the ultimate temperature exceeds 5 minutes, the rate of strength reduction due to restoration decreases, and conversely the rate of strength increase due to aging increases, so it becomes difficult to reduce the strength of the heated part, and productivity Is also inhibited.

  Further, in the cooling process after the partial restoration heat treatment, it is necessary to rapidly cool to 100 ° C. Specifically, when the cooling rate to 100 ° C. is less than 30 ° C./min, grain boundary precipitation is likely to occur during cooling, and the ductility of the material is reduced. For the same reason, the cooling rate is preferably 50 ° C./min or more, more preferably 100 ° C./min or more. On the other hand, if the material temperature after cooling exceeds 100 ° C., age hardening occurs, making it difficult to reduce the strength of the heated portion. Therefore, it was decided to cool to 100 ° C. or lower after the partial restoration heat treatment.

  On the other hand, as a condition of the partial restoration heat treatment for increasing the difference between the tensile strength of the non-heated part at room temperature and the proof stress of the heated part by 20 MPa or more before and after the partial restoration heat treatment, Is heated to a temperature in the range of 180 to 350 ° C. at a temperature rising rate of 50 ° C./min or more, held at the temperature in the range for 5 minutes or less (including 0 seconds), and then 50 ° C. / It is supposed to cool to a temperature of 100 ° C. or less at a cooling rate of at least minutes. The reason for this definition is as follows.

  That is, in order to increase the difference between the tensile strength of the non-heated part at room temperature and the proof stress of the heated part by 20 MPa or more before and after the partial restoration heating process, the temperature of the region (heating part) heated by the partial restoration heating process Is preferably in the range of 180 ° C. or higher and 350 ° C. or lower. When the temperature reached by heating is less than 180 ° C., when compared with the productivity of the cold press, the heat treatment in a short time that does not impair the productivity does not sufficiently restore, and the material strength of the heating part is Does not drop sufficiently. For this reason, the difference between the tensile strength of the non-heated part at room temperature and the proof stress of the heated part does not increase by 20 MPa or more before and after the partial restoration heat treatment, and the improvement of the formability of the alloy plate by the partial restoration heat treatment is insufficient. Become. In addition, when the temperature reached by heating is higher than 350 ° C., the aging proceeds so that the fine precipitates composed of Mg and Si are dissolved in an extremely short time, and then the fine precipitates composed of Mg and Si are immediately precipitated. It hardens again. Since this aging continues even during the subsequent cooling, even when the partial restoration heat treatment time is set to an extremely short time, the decrease in strength after cooling becomes low. Further, since grain boundary precipitation occurs simultaneously with the restoration phenomenon, the elongation is remarkably lowered, and cracking is likely to occur during press molding, so that the moldability is not substantially improved. On the other hand, when the temperature reached by heating is not lower than 180 ° C. and lower than 350 ° C., it is possible to effectively impart a difference in strength to the blank with high efficiency that does not impair the productivity of press molding.

  Here, the heating ultimate temperature in the partial restoration heat treatment can be further divided into two temperature ranges according to the rate of change with time in the strength of the heating portion.

  That is, when the heating attainment temperature is 250 ° C. or more and 350 ° C. or less, the fine precipitates composed of Mg and Si are dissolved in a short time within a few seconds, and the restoration is completed, and then cooled to room temperature at a predetermined cooling rate. Immediately after, the tensile strength of the non-heated part at room temperature and the yield strength difference of the heated part increase by 20 MPa or more before and after the partial restoration heat treatment. However, when restoration heating is performed in this temperature range, many atomic vacancies remain at room temperature after cooling. This atomic vacancy promotes the diffusion of Mg and Si while maintaining the room temperature in the part subjected to the partial reconstitution heat treatment, and accelerates the formation of fine precipitates at room temperature. It will quickly return to the state before the restoration heat treatment after being left for several days. This atomic vacancy density increases as the heating temperature increases, and with increasing atomic vacancy density, the increase in yield strength at room temperature is accelerated. Such rapid changes in strength distribution cause incompatibility with pre-optimized press molding conditions, and often cause shape defects and poor appearance in press molded products. In order to produce a molded product, it is preferable to perform press molding while keeping the room temperature after the partial restoration heat treatment as short as possible. On the other hand, when the restoration heat treatment is performed in a temperature range of 180 ° C. or more and less than 250 ° C., the restoration is completed within a short time so as not to impair this compared with the productivity of the cold press. In addition, the density of atomic vacancies at room temperature after cooling is sufficiently low, and the increase in the proof stress over time during the room temperature holding period after the partial restoration heat treatment is sufficiently small. Therefore, when the partial restoration heat treatment is performed within such a temperature range, it is possible to stably produce a good molded product even when kept at room temperature for several days. Therefore, if importance is attached to the schedule of the production process, the partial reconstitution heat treatment is performed so that after the partial reconstitution heat treatment, the blank can be held at room temperature for several days before being pressed. Is preferably 180 ° C. or higher and lower than 250 ° C. Here, in order to stably produce a good molded product, the amount of increase in the proof stress value of the heating part in the partial restoration heat treatment from immediately after the partial restoration heat treatment to the fifth day is set to 50 MPa or less, more preferably 30 MPa or less.

  The holding time at the ultimate temperature for increasing the difference between the tensile strength of the non-heated part at room temperature and the proof stress of the heated part by 20 MPa or more before and after the partial restoration heat treatment is also within 5 minutes (zero holding time). = Including the case of cooling immediately without substantially holding). Similarly, in order to increase the difference between the tensile strength of the non-heated part at room temperature and the proof stress of the heated part by 20 MPa or more before and after the partial restoration heat treatment, the temperature increase rate in the partial restoration heat treatment is 50 ° C./min. It is desirable to set it above. If the rate of temperature increase is less than 50 ° C./min, the re-solution of ultrafine precipitates will progress during the temperature increase, and the recovery will be completed during the temperature increase or during heating and holding, and precipitation will continue. As a result, it is difficult to effectively reduce the yield strength of the heated part, and therefore, the yield strength difference between the non-heated part and the heated part at room temperature is improved by 20 MPa or more before and after the partial restoration heat treatment. It becomes difficult. Furthermore, it is desirable that the cooling rate of the heating portion after the partial restoration heat treatment is 50 ° C./min or more. When the cooling rate is less than 50 ° C./min, the strength improvement due to aging proceeds during cooling, and it becomes difficult to effectively reduce the yield strength of the heated part. It becomes difficult to increase the difference between the tensile strength and the yield strength of the heated portion by 20 MPa or more before and after the partial restoration heat treatment.

  In addition, the specific means for partially heating the blank is not particularly limited as the partial restoration heat treatment, but for example, a heated metal ridge is brought into contact with the portion corresponding to the wrinkle holding portion during press molding. Or a method of heating only that portion with hot air can be applied.

  Here, if the partial restoration heat treatment as described above is performed, the shape freezing property of the molded product is improved due to the strength reduction of the wrinkle holding part, and the part that has become low strength due to the restoration phenomenon is the curing rate during paint baking. Since the strength is rapidly recovered, high paint bake hardenability (BH property) is obtained, and strength deterioration after baking is eliminated. This is because the clusters formed by aging at room temperature are once solid-dissolved by heating by partial restoration heat treatment, and then the coating baking is performed, so that larger size precipitates that contribute more effectively to strength improvement are dense. This is because it is formed. On the other hand, if the coating baking is performed in a state where the clusters formed by normal temperature aging remain, the clusters usually dissolve once at a heating temperature of less than 180 ° C., and then contribute more effectively to improving the strength. Since precipitation of large-size precipitates starts, heating and holding for a short period of time of about 20 minutes for coating baking lowers the degree of curing, and high coating baking curability cannot be obtained. On the other hand, in the molded product obtained by performing the partial restoration heat treatment of the present invention, the partial restoration heat treatment is performed by a paint baking process (corresponding to artificial aging) performed within 30 days after the partial restoration heat treatment. The proof stress of the heated portion is improved by 20 MPa or more, and the molded article can be given the rigidity required as a body panel. This is defined in claim 15.

<Normal temperature storage from partial restoration heat treatment to cold press forming>
The process from the partial restoration heat treatment to the cold press forming process is allowed to stand at room temperature, and the room temperature standing period is preferably within 30 days as defined in claim 8. If the room temperature standing time after partial restoration treatment exceeds 30 days, the strength of the part reduced by heating and restoration will increase due to new room temperature aging, and the strength difference between the heated part and non-heated part of the plate will be reduced. , High press formability may not be obtained. In order to reliably suppress the normal temperature aging, it is preferable that the normal temperature is kept within 72 hours, preferably within 24 hours, which is advantageous from the viewpoint of productivity.

  In addition, as the period of standing at room temperature from partial restoration heat treatment to cold press forming, more substantially, the strength of the part softened by partial restoration heat treatment returns to the original strength before treatment. It is the period during which it is not. Further, a substantially preferable state is a period in which the difference between the tensile strength of the non-heated part at room temperature and the proof stress of the heated part is maintained at 20 MPa or more after the partial restoration heat treatment. In addition, it is preferable to implement the oiling process required for normal press molding during this room temperature standing period or immediately before performing press molding.

<Component composition of aluminum alloy plate>
The aluminum alloy plate for forming according to the present invention may basically be an Al-Mg-Si alloy, and its specific component composition is not particularly limited. An alloy having a component composition as defined in Item 18, that is, containing Mg 0.2 to 1.5%, Si 0.3 to 2.0%, Fe 0.03 to 1.0%, Mn 0.03 to 0.00. 6%, Cr 0.01-0.4%, Zr 0.01-0.4%, V 0.01-0.4%, Ti 0.005-0.3%, Zn 0.03-2.5%, Cu 0. It is preferable to use, as a material, an aluminum alloy containing one or more selected from 01 to 1.5%, with the balance being Al and inevitable impurities.

  The reasons for limiting the component composition of the material alloy defined in claims 16 to 18 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 1.4%.

  The above Mg and Si are basic alloy elements as an Al—Mg—Si-based aluminum alloy, but Fe 0.03 to 1.0%, Mn 0.03 to 0.6%, Cr 0.01 to 0.4%, Zr 0.01-0.4%, V 0.01-0.4%, Ti 0.005-0.3%, Zn 0.03-2.5%, Cu 0.01-1.5% One or two or more selected from among them are included. The reason for these additions and the reason for limiting the addition amount are as follows.

Ti, V:
Ti is an element effective for improving the strength and preventing corrosion by refining the ingot structure, and V is an element effective for improving the strength and preventing corrosion. If the Ti content is less than 0.005%, a sufficient effect cannot be obtained. On the other hand, if the Ti content exceeds 0.3%, the effects of refinement of the ingot structure and corrosion protection due to the addition of Ti are saturated. If V is less than 0.01%, a sufficient effect cannot be obtained. On the other hand, if it exceeds 0.4%, the anticorrosive effect by addition of V is saturated. If the upper limit is exceeded, coarse Ti or V-based intermetallic compounds increase, which leads to a decrease in formability and hemmability.

Mn, Cr, Zr:
These elements are effective for improving the strength, refining crystal grains, or improving aging (bake hardenability). If the Mn content is less than 0.03% or the Cr and Zr contents are each less than 0.01%, the above effect cannot be obtained sufficiently, while the Mn content exceeds 0.6%. If the Cr, Zr content exceeds 0.4%, not only the above effects will be saturated, but also 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 and Zr are in the range of 0.01 to 0.4%, respectively.

Fe:
In general aluminum alloys, Fe is usually contained as an inevitable impurity in an amount of less than 0.03%. On the other hand, Fe is an element effective for strength improvement and crystal grain refinement, and in order to exert these effects, Fe may be positively added by 0.03% or more. However, if the content is less than 0.03%, a sufficient effect cannot be obtained. On the other hand, if it exceeds 1.0%, the formability, particularly the bending workability, may be lowered. Therefore, Fe is actively added. In this case, the amount of Fe was set in the range of 0.03 to 1.0%.

Zn:
Zn is an element that contributes to strength improvement through aging improvement and is effective in improving surface treatment properties. However, if the amount of Zn is less than 0.03%, the above effect cannot be obtained sufficiently, while 2.5 If it exceeds 50%, the moldability and the corrosion resistance decrease, so the Zn content is set in the range of 0.03 to 2.5%.

Cu:
Cu is an element added for improving formability and strength, and 0.01% or more is added for the purpose of improving formability and strength. However, if the Cu content 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 importance is attached to strength improvement, the Cu content is preferably 0.4% or more, and when it is desired to further improve the corrosion resistance, the Cu content is preferably 1.0% or less. Furthermore, when importance is attached to corrosion resistance, it is preferable not to add Cu positively and to regulate the amount of Cu to 0.01% or less.

  Moreover, in general Al alloy, B may be added simultaneously with the above-mentioned Ti for refining the ingot structure. By adding B together with Ti, the ingot structure can be refined and stabilized. The effect becomes more remarkable. In the case of this invention, it is permissible to add 500 ppm or less of B together with Ti.

  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.

[Example 1]
Each aluminum alloy shown in A1 to A6 of Table 1 was dissolved and the components were adjusted, and then cast by a DC casting method to produce an aluminum alloy ingot. The ingot was subjected to soaking at 530 ° C. for 10 hours, and then subjected to hot rolling and cold rolling according to a conventional method to obtain an alloy plate having a thickness of 1 mm. Thereafter, a solution treatment was performed at 530 ° C., followed by rapid cooling to room temperature. After solution treatment and rapid cooling, it was left at room temperature for 60 days. Thereafter, a partial restoring heat treatment was applied to the wrinkle holding portion of the drawing molding under the heating conditions shown in Table 2. After the whole plate is cooled to room temperature, the strength (tensile strength and 0.2% yield strength), limit drawing ratio (LDR), and coating bake strength of the heated portion within 24 hours of standing at room temperature. Was measured. Furthermore, the hemming property of the heating part was also evaluated within 24 hours at room temperature.

LDR (limit drawing ratio) test:
The punch diameter (P) was 32 mmφ, the wrinkle pressure was 150 kg, the blank diameter size was variously changed, and the maximum drawable blank diameter (D) was obtained by LDR = D / P. Johnson Wax ™ was applied to both sides of the plate as a lubricant.

Paint bake strength:
After stretching 2% using a JIS No. 5 test piece, a baking treatment (baking) was performed at 170 ° C. for 20 minutes, a tensile test was performed, and a 0.2% proof stress value was measured as mechanical strength.

Hem processability evaluation:
After stretching 5% using a bending test piece, 180 ° contact bending was performed, and the presence or absence of cracks was visually observed. Here, a circle indicates that there is no crack, and a cross indicates that there is a crack.

  All the alloys A1 to A6 shown in Table 1 are within the component composition range defined in claims 16 to 18 of the present invention.

  Sample No. in Table 2 1-No. Nos. 5 are examples of the present invention. 6-No. 9 is a comparative example.

  In all the examples of the present invention, the difference in strength between the non-heated part and the heated part (difference in 0.2% proof stress) is +12 or more, and the LDR is 2.09 or more, and the hemming property is also good. The strength after baking is also high.

  On the other hand, the LDR was particularly inferior in the comparative example. Among them, the test material No. 6, no. 7, no. In No. 8, since the heating conditions of the partial restoration heat treatment are out of the scope of the present invention, the strength of the heated portion is high, the strength of the non-heated portion is low, and the strength reversal phenomenon occurs compared to the invention example, and the Since the strength of the part was high and the strength of the punch shoulder was low, the LDR was greatly reduced. Furthermore, sample No. 7, no. In 8, the hemmability was also deteriorated. Specimen No. No. 9 is a comparative example obtained by cold pressing a strength uniform plate without partial restoration heat treatment. Compared to 1, LDR and strength after baking were inferior.

[Example 2]
The second embodiment is mainly for explaining the effects of the methods according to claims 7 and 12 in terms of process. However, examples that fall outside the conditions defined in claims 7 and 12 but fall within the conditions defined in claims 6 and 11 are also described for reference. Here, an example satisfying the conditions defined in claims 7 and 12 is referred to as “second invention example”, and the conditions defined in claims 6 and 11 are satisfied. 7. An example that does not satisfy the conditions defined in claim 12 is referred to as a “first invention example”, and an example that does not satisfy any of the conditions is referred to as a “comparative example”.

  The aluminum alloys shown in B1 to B3 in Table 3 were melted and then cast by a DC casting method to produce aluminum alloy ingots having chemical components shown in Table 3. The ingot was subjected to soaking at 530 ° C. for 10 hours, and then subjected to hot rolling and cold rolling according to a conventional method to obtain an alloy plate having a thickness of 1 mm. Thereafter, a solution treatment was performed at 530 ° C., followed by rapid cooling to room temperature.

  Thereafter, under the conditions shown in Tables 4 and 5, aging treatment at room temperature, artificial aging, or a combination of both was performed. Tensile test pieces (JIS No. 5 test piece shape) are taken from this alloy plate so that the tensile direction is perpendicular to the rolling direction, and a tensile test is performed to examine mechanical properties (tensile strength, yield strength, elongation). The results are shown in Tables 4 and 5. The alloy plate was subjected to a partial restoration heat treatment by the method described below and then subjected to a formability evaluation test.

  First, a disc blank for formability evaluation of a predetermined size was produced from this alloy plate. As shown in FIG. 2, the region of 55.7 mmφ in the center of this disk sample (blank 5) was designated as a non-heating part Q, and the surrounding area was designated as a heating part P, and a partial restoration heat treatment was performed. This heating part is all the part outside the region where the shoulder 3 of the punch 2 is in contact during press molding. As a specific method of this partial restoration heat treatment, the disk blank 5 was sandwiched between the upper board 6 and the lower board 7 of the partial restoration heat treatment apparatus having a shape schematically shown in FIG. . In FIG. 3, each of the upper board 6 and the lower board 7 is a non-heating part 8 whose central part is cooled by water cooling, and the surrounding part is a heating part 9 incorporating a heater. Tables 4 and 5 show the heating arrival temperature, heating time, temperature increase rate, and cooling rate conditions in the heating section at this time.

  About the disk blank which performed the partial reconstruction heat processing on these conditions, while using for the moldability evaluation test demonstrated below, about the disk blank of each condition, the small tensile test piece 10 of the shape shown in FIG. Samples are taken from both the heating part P and the non-heating part Q (the sampling position is shown in FIG. 5) and subjected to a tensile test, the proof stress of the non-heating part Q and the heating part P is examined, and the results are shown in Tables 6 and 7 Indicated. The strength evaluation of each part after the partial restoration heat treatment was performed as soon as possible after the partial restoration heat treatment, substantially within 5 hours after the partial restoration heat treatment. Moreover, in order to confirm the time-dependent change of the proof stress value in the heating part of the disk blank which performed the partial reconstruction heat processing on each condition, from the heating part of the disk blank which passed 1 day and 5 days after the partial reconstruction heating process. Similarly, a tensile test piece was collected and immediately subjected to a tensile test. The proof stress value after each time passage was examined, and the results are shown in Tables 6 and 7. Furthermore, after performing partial restoration heat treatment, after holding the disc blank at room temperature for the same time as the time until the moldability evaluation test is performed, a small tensile test piece is removed from both the heating part and the non-heating part. After sampling (sampling position is shown in FIG. 5) and pre-applying 2% deformation by simulating press molding, artificial aging was performed at 170 ° C. for 20 minutes corresponding to the coating baking process. Tensile tests were performed on these test pieces, the proof stress values at each part were measured, and increments of the proof stress values at each part due to the heat treatment corresponding to the paint baking process are shown in Tables 6 and 7. Furthermore, after the partial restoration heat treatment is performed, in addition to the time until the moldability evaluation test is performed, the disk blank is held at room temperature for 3 days, and then a small tensile test piece is heated from the heating portion of the disk blank. After applying 5% tensile deformation, the parallel part of the test piece was cut out and subjected to a bendability evaluation test by the following method. That is, first, after bending at a bending radius of 0.8 mm until the angle is 90 °, a line perpendicular to the tensile direction located at the center of the parallel part of the test piece is bent to a 90 ° angle, and further bent to an angle of 135 ° Assuming that the inner panel is inserted inside, a plate having a thickness of 1.0 mm was inserted, and the plate was folded to an angle of 180 ° so as to sandwich the plate and brought into close contact. The outside of the bent portion was confirmed with a loupe, and it was judged that the bending workability was good when no cracks occurred, and the bending workability was judged poor when the cracks occurred.

  The moldability evaluation test was carried out by a cylindrical deep drawing test after holding the disc blank at room temperature for the time shown in Tables 6 and 7 after the partial restoration heat treatment. The punch used in this test had a punch diameter of 50 mm and a punch angle radius of 5.0 mm, and the die had a die inner diameter of 53.64 mm and a die shoulder radius of 13.0 mm. As conditions for the deep drawing test, the punching speed was 180 mm / min, the wrinkle holding force was 150 kg, and Johnson Wax (trademark) was used as the lubricant. A deep drawing test was performed on the alloy plate blank subjected to the partial restoration heat treatment. When three or more of the five sheets could be drawn, the diameter of the disk was increased by 0.5 mm and the deep drawing test was performed again. went. By repeating this, the diameter of the maximum disk that can be drawn was determined, and this numerical value was divided by the punch diameter of 50 mm to determine the limit drawing ratio LDR. Moreover, LDR was calculated | required also about the original plate which does not perform a partial reconstruction heat processing for the comparison, and the result of these cylindrical deep drawing tests was shown in Table 5. Here, by performing the partial restoration heat treatment, it was judged that the moldability was substantially improved by the partial restoration heat treatment when the LDR increased by 0.1 or more compared to the case where this treatment was not performed. .

  Conditions 1 to 4 are obtained by subjecting the alloy B1 to a partial restoration heat treatment or the like under the conditions within the scope of the inventions of claims 7 and 12 (second invention example). In any case, the difference between the tensile strength of the non-heated part and the proof stress of the heated part at room temperature increased by 20 MPa or more before and after the partial restoration heat treatment. For this reason, even in the moldability evaluation test, the LDR was improved by 0.1 or more as compared with the case where partial restoration heating was not performed, and a practically effective moldability improvement effect was recognized. In addition, it was also confirmed that there was an improvement in yield strength of 20 MPa or more in the heating section after the heat treatment equivalent to the paint baking treatment, and it was found that the strength level required for the automobile body sheet could be secured. Furthermore, the time-dependent change in the proof stress value of the heated part after the partial restoration heat treatment is gradual, and the increment of the proof stress value until the fifth day after the partial restoration heat treatment is stable at 50 MPa or less. It was confirmed that a good molded product having no defects can be stably produced. Furthermore, it was confirmed that the bending processability of the heating part in the partial restoration heat treatment is good, and that the bending process is facilitated by setting the bending part of the press-formed product as the heating part.

  On the other hand, the condition 5 is that the temperature reached in the partial restoration heat treatment is such that the difference between the tensile strength of the non-heated part and the yield strength of the heated part at room temperature is 20 MPa or more due to the partial restoration heat treatment. This is an example (first invention example) lower than the temperature range of the inventions of claims 7 and 12. In this case, the softening effect by sufficient restoration | restoration in a heating part was not acquired, but the increment became less than 20 MPa. For this reason, it has been found that the LDR obtained in the moldability evaluation test does not sufficiently improve as compared with the case where the partial restoration heat treatment is not performed.

  Condition 6 is a comparative example in which the temperature reached by heating in the partial restoration heat treatment is higher than the range of the present invention. In this case, the aging precipitation immediately proceeds immediately after the restoration is completed in a short time in the heating part, thereby improving the yield strength of the heating part, and as a result, the tensile strength of the non-heating part at room temperature and the heating part. The difference from the yield strength by the partial restoration heat treatment is less than 20 MPa, so the LDR obtained in the moldability evaluation test is equivalent to the case where the partial restoration heat treatment is not performed, and the moldability is not improved. It has been found that since the grain boundary precipitation occurs by heating at this temperature, the bending workability is greatly deteriorated and the molded product cannot be bent. In this case, the increase in the proof stress due to the artificial aging after molding in the heating portion is 20 MPa or less, and the strength required for the body panel cannot be ensured.

  The condition 7 is that the rate of temperature increase in partial recovery heating is such that the difference between the tensile strength of the non-heated part and the proof stress of the heated part at room temperature is 20 MPa or more due to the partial recovery heat treatment. This is an example (first invention example) lower than the temperature range of the invention of claim 12. In this case, the aging precipitation proceeds following the restoration in the middle of the mild temperature rise in the heating section and in the middle of the heating reaching temperature, and as a result, the tensile strength and heating of the non-heating section at room temperature. The difference from the yield strength of the part due to the partial restoration heat treatment was less than 20 MPa. Therefore, the improvement of LDR of 0.1 or more was not seen, and the sufficient improvement effect of the moldability by the partial restoration heat treatment was not recognized.

  The condition 8 is that the cooling rate in the partial restoration heat treatment is such that the difference between the tensile strength of the non-heated part and the proof stress of the heated part at room temperature is 20 MPa or more due to the partial restoration heat treatment. This is an example (first invention example) lower than the scope of the invention of claim 12. In this case, in the heating part, it softens once by restoration, but aging precipitation progresses during the slow cooling after heating and hardens again. As a result, the tensile strength and heating of the non-heating part at room temperature The difference from the yield strength of the part due to the partial restoration heat treatment was less than 20 MPa. Therefore, the improvement of LDR of 0.1 or more was not seen, and the sufficient improvement effect of the moldability by the partial restoration heat treatment was not recognized.

  Conditions 9 and 10 are examples in which a partial restoration heat treatment or the like was performed under the conditions within the scope of the inventions of claim 7 and claim 12 after the aging treatment combining room temperature aging and artificial aging (second invention example). It is. In any case, the difference between the tensile strength of the non-heated part at room temperature and the proof stress of the heated part increased by 20 MPa or more before and after the partial restoration heat treatment, and therefore LDR performed the partial restoration heat treatment in the moldability evaluation test. Compared with the case where there is no material, it was improved by 0.1 or more, and a practically effective moldability improving effect was recognized. In addition, after heat treatment corresponding to the paint baking treatment, it was confirmed that there was an improvement in proof stress of 20 MPa or more in the heating part, and the necessary strength level for the automobile body sheet could be secured. Furthermore, the change over time in the proof stress value of the heated part after the partial reconstitution heat treatment is gradual, and the increment of the proof stress value until the fifth day after the partial reconstitution heat treatment is stable at 50 MPa or less. Or it turned out that the favorable molded product without an external appearance defect can be manufactured stably. Furthermore, it was confirmed that the bending workability of the heating part is improved by the partial restoration heat treatment, and that bending can be performed by setting the bending part for the press-formed product as the heating part.

  On the other hand, Condition 11 is a comparative example in which the proof stress before performing the partial restoration heat treatment is less than the range of the present invention although the aging is performed at normal temperature. In this case, even if the partial restoration heat treatment or the like performed thereafter is performed under the conditions of the scope of the present invention, a sufficient decrease in yield strength cannot be obtained in the heating portion in the partial restoration heat treatment, and therefore, non-heating at room temperature. The difference between the tensile strength of the part and the yield strength of the heated part is less than 20 MPa, and the LDR obtained in the formability evaluation test is only slightly increased from the case where the partial restoration heat treatment is not performed. In addition, a substantial formability improvement effect by the partial restoration heat treatment was not recognized.

  Results similar to those obtained for these alloys B1 were also obtained for the alloys B2 which are Al—Mg—Si—Cu based alloys. That is, all of the conditions 12 to 15 performed on the alloy B2 were obtained by performing a partial restoration heat treatment or the like under the conditions within the scope of the inventions of claims 7 and 12. The difference between the tensile strength of the heating part and the proof stress of the heating part increased by 20 MPa or more before and after the partial restoration heat treatment. For this reason, in the moldability evaluation test, LDR was improved by 0.1 or more compared to the case where the partial restoration heat treatment was not performed, and a practically effective moldability improving effect was recognized. In this case, after the heat treatment equivalent to the paint baking process, it is also confirmed that there is an improvement in the proof stress of 20 MPa or more in the heating part, and it is possible to secure a necessary strength level for the automobile body sheet, and further, Yield value changes gradually over time, and the increment of the proof stress value up to the fifth day after the restoration process is stable at 50 MPa or less, and a stable molded product having no shape defect or appearance defect is stably produced in press molding. Turned out to be possible. Furthermore, in this case, it is confirmed that the bending processability of the heating part in the partial restoration heat treatment is good, and that the bending process of the molded product becomes easy by setting the bending part of the press-molded product as the heating part. It was.

  On the other hand, the condition 16 performed on the alloy B2 is that the heating arrival temperature in the partial restoration heat treatment is an increase in the difference between the tensile strength of the non-heated part and the proof stress of the heated part at room temperature by 20 MPa or more. This is an example (first invention example) that is lower than the temperature range of the inventions of claims 7 and 12. In this case, the softening effect due to sufficient restoration cannot be obtained in the heating part, and the increment is less than 20 MPa. Therefore, the LDR obtained in the moldability evaluation test is sufficient as compared with the case where the partial restoration heating treatment is not performed. It turns out that it does not improve.

  Moreover, the conditions 17 and 18 performed about the alloy B2 are comparative examples whose heating attainment temperature in a partial reconstruction heat processing is higher than the range of this invention. In this case, the aging precipitation immediately proceeds immediately after the restoration is completed in a short time in the heating part, thereby improving the yield strength of the heating part, and as a result, the tensile strength of the non-heating part at room temperature and the heating part. The increment by the partial restoration heat treatment of the difference from the proof stress was less than 20 MPa. Therefore, the LDR obtained in the formability evaluation test is almost the same as the case where the partial restoration heat treatment is not performed, and it is confirmed that the formability is not substantially improved, and the grain boundary precipitation is caused by heating at this temperature. Therefore, it was found that the bending workability is greatly deteriorated and the molded product cannot be bent. Furthermore, it was found that the increase in the proof stress value due to artificial aging after molding in the heating part is 20 MPa or less, and the strength required for the body panel cannot be ensured.

  The condition 19 performed for the alloy B2 is a comparative example in which the heating time in the partial restoration heat treatment is longer than the range of the present invention. In this case, in the heating part, the restoration is completed during heating and once softens, but then gradually hardens as aging precipitation proceeds, and as a result, the tensile strength of the non-heating part and the proof stress of the heating part at room temperature. The difference before and after the partial restoration heat treatment became negative. Therefore, the LDR obtained in the moldability evaluation test was lower than that in the case where the partial restoration heat treatment was not performed. Further, in this case, it was found that the bending workability after the heating part was molded was poor and the molded product could not be bent.

  On the other hand, the condition 20 performed for the alloy B2 is a comparative example in which the proof stress and the tensile strength before the partial restoration heat treatment are less than the range of the present invention although the aging is performed at normal temperature. In this case, even if the partial restoration heat treatment, etc. performed thereafter are performed under the conditions within the scope of the inventions of claims 7 and 12, sufficient reduction in yield strength can be obtained in the heated portion in the partial restoration heat treatment. Therefore, the increase in the difference between the tensile strength of the non-heated part at room temperature and the proof stress of the heated part is less than 20 MPa, and the LDR obtained in the moldability evaluation test is subjected to the partial recovery heating process. It was found that the effect of improving the formability by the partial restoration heat treatment was not substantially observed.

  Furthermore, the conditions 21 and 22 performed on the alloy B3 were partially reheated under the conditions within the scope of the inventions of claims 7 and 12 after performing normal temperature aging or artificial aging according to the conditions within the scope of the present invention. This is an example of the treatment (second invention example), in which the difference between the tensile strength of the non-heated part and the proof stress of the heated part at room temperature increased by 20 MPa or more before and after the partial restoration heat treatment. For this reason, the moldability evaluation test was also improved by 0.1 or more as compared with the case where the LDR did not perform partial restoration heating, and a practically effective moldability improvement effect was recognized. In addition, after heat treatment corresponding to the paint baking treatment, it was confirmed that there was an improvement in proof stress of 20 MPa or more in the heating part, and the necessary strength level for the automobile body sheet could be secured. Furthermore, the increase in the proof stress value until the fifth day after the partial restoration heat treatment is stable at 50 MPa or less, and it is confirmed that a good molded product having no shape defect or appearance defect can be stably produced in press molding. It was done. Furthermore, it was confirmed that the bending workability of the heating part in the partial restoration heat treatment was good, and that bending work was facilitated by setting the bending part of the press-formed product as the heating part.

[Example 3]
Table 4 shows the aging conditions after the solution treatment, the ultimate temperature, the heating time, the heating rate, and the cooling rate in the partial recovery heating process using the rolled sheet of the alloy B1 used in Example 2 as a test material. As the same condition as the condition 2 shown in the above, solution treatment, aging, and partial restoration heat treatment were performed. However, in Example 3, the partial restoration heat treatment was performed by changing various regions of the heating part and the non-heating part in the partial restoration heat treatment as shown in Table 8. Three days after the partial restoration process, the blank subjected to the partial restoration heat treatment in each region condition was subjected to a cylindrical deep drawing test under the same conditions as in Example 1 to obtain LDR. Shown in.

  Condition 1, which is a comparative example, is an example in which there is no heating region, that is, substantially no partial restoration heat treatment was performed. In this case, the LDR was 2.01. Moreover, Condition 2 as a comparative example is an example in which the entire surface of the blank was used as a heating part, and the LDR increased only slightly to 2.02, and a sufficient moldability improvement effect was not obtained.

  Furthermore, Condition 3, which is a comparative example, is an example in which the entire portion (region B in FIG. 1) that contacts the punch shoulder during molding and the entire outer portion (region A in FIG. 1) are used as the heating unit. In this case, the strength of the punch shoulder portion is reduced, and breakage is likely to occur at this portion. Therefore, the LDR is only 2.01, and it has been found that the moldability is not improved.

  Further, Condition 4 as a comparative example is an example in which a part (region B in FIG. 1) that contacts the punch shoulder at the time of molding and the entire outer part (region A in FIG. 1) are used as a heating unit. In this case, it was confirmed that the strength of the punch shoulder portion was lowered and breakage was likely to occur at this portion, so that the LDR was only 2.02, and the moldability was not improved.

  On the other hand, Condition 5 which is an example of the present invention is an example in which the entire outer portion (region A in FIG. 1) of the portion (region B in FIG. 1) that comes into contact with the punch shoulder at the time of molding is used as the heating unit. In this case, the strength of the portion that comes into contact with the blank punch shoulder is higher than that of the outer portion. Therefore, the LDR was 2.26, which was confirmed to be effectively increased by 0.1 or more as compared with the case where the partial restoration heat treatment was not performed, and it was confirmed that the moldability was improved.

  In addition, conditions 6 and 7 which are examples of the present invention are examples in which a part of the outer portion of the portion (region B in FIG. 1) that comes into contact with the punch shoulder during molding is a heating portion. The strength of the portion that comes into contact with the punch shoulder in the blank is higher than that of a partial region of the outer portion. For this reason, LDR was 2.25 and 2.23, respectively, and compared with the case where partial restoration heat treatment was not performed, it was effectively increased by 0.1 or more, and it was confirmed that the moldability was improved. .

[Example 4]
Using the rolled sheet of alloy B1 used in Example 2 as a test material, the aging conditions after solution treatment, the heating ultimate temperature, the heating time, the heating rate, and the cooling rate conditions in the partial restoration heating process are shown in Table 4 respectively. As the same condition as the condition 2 shown in the above, solution treatment, aging, and partial restoration heat treatment were performed. However, in Example 4, the shape of the punch used for press molding was made different from those in the above examples. That is, as shown in FIG. 6, a two-stage cylindrical punch 2 having two-stage punch shoulder portions 3A and 3B is used. Here, the first stage of the punch 2 has a punch shoulder part 3A having a size of φ50 mm and 5 mmR, and the second stage of the punch 2 has a punch shoulder part 3B having a size of φ25 mm and 5 mmR. Further, the die corresponds to the shape of the two-stage punch 2, and the disc blank 5 is press-formed with such a two-stage punch 2 and a die.

  At this time, as an example of the present invention, a region A outside the region B that will be in contact with the punch shoulder portion 3A on the one-step surface at the time of molding is used as a heating unit in partial recovery heating, and a region C inside the region B Of these, the outer region A ′ of the region B ′ that would be in contact with the punch shoulder 3B was also added as a heating portion, and a partial restoration heat treatment was performed. On the other hand, as a comparative example, the partial restoration heat treatment was performed using only the region A outside the region B that would be in contact with the punch shoulder portion 3A on the one-step surface during molding as a heating part in the partial restoration heat treatment. About the blank which performed these 2 types of partial decompression | restoration heat processing of this invention example and a comparative example, the press molding was performed using these punches and die | dyes 3 days after a partial reconstruction heat processing. As a result, in the example of the present invention, it was possible to produce a two-stage cylindrical molded product without breaking in the middle, but in the comparative example, the fracture occurred at a site corresponding to the punch shoulder 3B of the molded product. Oops.

In order to demonstrate the heating part and non-heating part at the time of performing partial restoration | repair heat processing by this invention, it is typical sectional drawing which shows the condition of the press molding of an aluminum alloy plate in steps. FIG. 6 is a schematic diagram for illustrating a heating part and a non-heating part during a partial restoration process in Example 2. It is a typical perspective view of the partial reconstruction heat processing apparatus used in Example 2. FIG. 6 is a plan view showing the shape and dimensions of a tensile test piece collected in Example 2. FIG. In Example 2, it is a top view which shows the tensile test piece collection position from the heating part and non-heating part of the blank which performed the partial reconstruction heat processing. It is typical sectional drawing which shows the position of the heating part and non-heating part in the partial reconstruction process with respect to the punch of 2 steps | paragraph shape of the press used in Example 4, and the blank in that case.

Explanation of symbols

1 Die 2 Punch 3, 3A, 3B Punch shoulder 4 Wrinkle presser 5 Blank P Heating part Q Non-heating part

Claims (8)

  1. After using a rolled Al-Mg-Si aluminum alloy sheet rolled to a predetermined thickness as a raw material and subjecting it to a solution treatment at a temperature in the range of 480 to 590 ° C, the 0.2% yield strength is 90 MPa or more. In this way, the region to be pinched by the wrinkle presser at the time of cold press forming is determined as the heating portion, and the portion to be pressed against the punch shoulder portion is determined as the non-heating portion, and partial restoration to the heating portion is performed. As the heat treatment, before cold press forming, the temperature is raised to a temperature in the range of 150 to 350 ° C. at a temperature rising rate of 30 ° C./min or more, and the temperature within the range is 5 minutes or less (including 0 seconds). After holding, a treatment of cooling to a temperature of 100 ° C. or lower at a cooling rate of 30 ° C./min or higher is performed, and a difference in 0.2% proof stress after cooling at room temperature between the non-heated portion and the heated portion [( 0.2% proof stress of non-heated part)-(0 of heated part) The value of 2% proof stress)] as the above 10 MPa, 0.2% proof stress of the heated part is characterized in that to obtain the following aluminum alloy plate 141MPa, a manufacturing method of an aluminum alloy sheet for cold press forming.
  2. In the manufacturing method of the aluminum alloy plate for cold press forming of Claim 1,
    By the partial reversion heating treatment, the difference between the 0.2% proof stress of the tensile strength and the heating portion of the non-heated part - the value of [(tensile strength of the non-heated part) (0.2% proof stress of the heated part)] Is increased by 20 MPa or more before and after the partial restoration heat treatment, and a method for producing an aluminum alloy plate for cold press forming.
  3. A method for performing cold press forming using an aluminum alloy sheet for cold press forming manufactured by the method according to claim 1;
    A cold press forming method of an aluminum alloy sheet, wherein cold press forming is performed before the standing period at room temperature has passed 30 days after the partial restoration heat treatment.
  4. A method for performing cold press forming using an aluminum alloy sheet for cold press forming manufactured by the method according to claim 1;
    The aluminum alloy plate is characterized in that the aluminum alloy plate blank is cold-press formed before the strength of the heating part returns to the state before the partial restoration heat treatment during holding at room temperature after the partial restoration heat treatment. Cold press molding method.
  5. In the manufacturing method of the aluminum alloy plate for cold press forming according to any one of claims 1 and 2 ,
    In the heating part in the partial restoration heat treatment, the part of the aluminum alloy sheet blank that is to be bent after forming out of the part outside the region where the punch shoulder is in contact during press forming is included. A method for producing an aluminum alloy plate for cold press forming .
  6. In the manufacturing method of the aluminum alloy plate for cold press forming according to any one of claims 1 and 2 ,
    All regions inside the region where the punch shoulder portion of the aluminum alloy plate blank contacts with the heating part in the partial restoration heat treatment at the time of press forming, or one region or two regions of any shape in this region The manufacturing method of the aluminum alloy plate for cold press forming characterized by including these.
  7. A molded article obtained by the cold press molding method of an aluminum alloy plate according to any one of claims 3 and 4 ,
    An aluminum alloy cold press-formed product characterized in that the yield strength value of the heated portion is improved by 20 MPa or more by an artificial aging treatment that is performed before 30 days have elapsed after the partial restoration heat treatment.
  8. In the manufacturing method of the aluminum alloy plate for cold press forming according to any one of claims 1 and 2 ,
    As an Al-Mg-Si-based aluminum alloy, it contains Mg 0.2-1.5% (mass%, the same shall apply hereinafter), Si 0.3-2.0%, Fe 0.03-1.0%, Mn 0. 03-0.6%, Cr 0.01-0.4%, Zr 0.01-0.4%, V 0.01-0.4%, Ti 0.005-0.3%, Zn 0.03-2.5 %, Cu containing 0.01 to 1.5% of one or more selected from the group consisting of Al and unavoidable impurities, and an aluminum alloy plate is used. A method for producing an aluminum alloy sheet for hot press forming.
JP2008226006A 2007-12-11 2008-09-03 Method for producing aluminum alloy plate for cold press forming, method for cold press forming aluminum alloy plate, and aluminum alloy cold press formed product Active JP5435914B2 (en)

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EP20080021178 EP2075348B1 (en) 2007-12-11 2008-12-05 Method of manufacturing an aluminum alloy sheet for cold press forming and cold press forming method for aluminum alloy sheet
US12/331,889 US8273196B2 (en) 2007-12-11 2008-12-10 Aluminum alloy sheet for cold press forming, method of manufacturing the same, and cold press forming method for aluminum alloy sheet
CN 200810107481 CN101514436B (en) 2007-12-11 2008-12-11 Aluminum alloy sheet for cold press forming, method of manufacturing the same, and cold press forming method for aluminum alloy sheet
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