JP2010159489A - Method for molding 7,000 series aluminum alloy material, and formed product molded by the same - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a molding method where a 7,000 series aluminum alloy material is easily and surely molded to obtain a formed product having high strength. <P>SOLUTION: The method for forming the 7,000 series aluminum alloy material includes: a stage where the 7,000 series aluminum alloy material having a composition containing, by mass, 2.0 to 10% Zn, 0.10 to 5.0% Mg, ≤5.0% Cu, ≤1.5% Mn, ≤1.0% Si, ≤1.0% Fe, ≤0.50% Cr, ≤0.50% Zr and ≤0.30% Ti, and the balance aluminum with inevitable impurities is subjected to solution treatment; a stage where the material is molded in a die; and a stage where quenching treatment is performed to ≤250°C in the die. <P>COPYRIGHT: (C)2010,JPO&INPIT

Description

The present invention relates to a 7000 series aluminum alloy plate material for molding a molded product requiring high strength such as a body sheet of an automobile or various housings, an automobile part such as a bumper or a stehan beam, and a two-wheel frame. As described above, a molding method of a material such as a 7000 series aluminum alloy extruded material for molding a molded product that applies bending or expansion / contraction to the extruded tube or the extruded profile, and a molding method of the 7000 series aluminum alloy material It relates to molded processed products.
Here, the molding process means all processes that are three-dimensionally processed by a mold, such as press molding, hydroforming (hydraulic molding), bulge molding, and superplastic molding (hot blow molding). .

  In recent years, as an energy-saving measure for environmental protection, for example, in automobiles, members such as bodies, sheets, and various housings, in order to achieve weight reduction while ensuring the conventional strength, the material of the above members is replaced with steel plates, Al-Mg-Si (6000 series) or Al-Zn-Mg (-Cu) (7000 series) aluminum alloy sheets that are lightweight and have excellent hardness and corrosion resistance are used (see Patent Document 1). ).

  However, the 7000 series aluminum alloy sheet used for the above member has a very high cold press formability because the strength increase due to room temperature aging after the solution treatment is remarkably large. As a result, the degree of freedom in designing the press-formed product is limited, and the yield of the press-formed product is also reduced.

  Furthermore, since the 7000 series aluminum alloy material has a higher quenching sensitivity than the 6000 series aluminum alloy material, the strength may decrease if the cooling rate in the quenching process after the solution treatment process is slow.

JP 2000-96175 A

  Therefore, the present invention obtains a high-strength molded product having a proof stress of 160 MPa or more even after the coating baking process in a 7000 series aluminum alloy material that has low cold-formability and is extremely difficult to cool during quenching. Is to be able to.

As the first feature,
Zn: 2.0% by mass (hereinafter referred to as “%”) or more, 10% or less, Mg: 0.10% or more, 5.0% or less, Cu: 5.0% or less, Mn: 1.5% Hereinafter, Si: 1.0% or less, Fe: 1.0% or less, Cr: 0.50% or less, Zr: 0.50% or less, Ti: 0.30% or less, the balance being aluminum and inevitable For 7000 series aluminum alloy material consisting of mechanical impurities,
Performing a solution treatment; and
The process of molding in the mold,
A quenching step of rapidly cooling to room temperature with the mold is included.

  Therefore, a high-strength 7000 series aluminum alloy material can be easily and reliably formed into a predetermined shape.

In addition, in the 7000 series aluminum alloy sheet used in the forming process, Zn contributes to the improvement of the strength. If the content is less than 2.0%, the strength is insufficient. Cracks occur, making it impossible to produce press-formed products. Therefore, the content is optimally 2.0% or more and less than 8.0%. Mg contributes to improvement of strength in the presence of Zn. If the content is less than 0.10%, the strength is insufficient. Can no longer be manufactured. Therefore, the content is suitably 0.10% or more and less than 5.0%, and more preferably 1.0% or more and 3.0% or less. Cu contributes to the improvement of strength, and if its content exceeds 5.0%, ingot cracking occurs and it becomes impossible to produce a press-formed product. Therefore, the content is suitably 5.0% or less, and more preferably 1.0% or more and 3.0% or less. Mn contributes to the improvement of strength by refining crystal grains. If the content exceeds 1.5%, ingot cracking occurs and it becomes impossible to produce a press-formed product. Therefore, the content is suitably 1.5% or less, and more preferably 0.8% or less. Si and Fe contribute to the improvement of strength, and if the content exceeds 1.0%, cracking occurs during press molding. Therefore, the content is suitably 1.0% or less, and more preferably 0.5% or less. Further, if the content is less than 0.03%, it is necessary to use an expensive high-purity aluminum ingot, which causes an increase in cost, so 0.03% or more is desirable. Cr, Zr and Ti each contribute to improvement in strength by refining crystal grains. When the content ratio exceeds 0.50% for Cr and Zr and exceeds 0.30% for Ti, ingot cracking and heat Interlaminar cracks are likely to occur, and coarse intermetallic compounds are likely to be produced, resulting in deterioration of molding processability. Therefore, the content is suitably 0.5% or less for Cr and Zr, 0.30% or less for Ti, and 0.3% or less for Cr and Zr, and 0.2% or less for Ti. is there.
In the present invention, among the elements defining the component range, except for Cu, only “below” is described, but this also includes 0.

And before performing a shaping | molding process, the process of performing a solution treatment, the process of performing a shaping | molding process within a metal mold | die, and the process of quenching rapidly cooled to 250 degrees C or less during a shaping | molding process are included.
In addition, it is common to the second and third features to be described later. However, if the quenching is completed at a temperature exceeding 250 ° C., quenching becomes insufficient, the molding processability deteriorates, and natural and artificial aging thereafter. It becomes difficult to obtain sufficient strength.

As the second feature,
For the 7000 series aluminum alloy material having the chemical component of the first characteristic,
It includes a step of performing a solution treatment, a step of quenching to 250 ° C. or less, and a step of molding in a mold within 120 hours after quenching.
Here, if the time until quenching after quenching exceeds 120 hours, the strength becomes too high due to natural aging, and molding becomes difficult. Therefore, it is preferably within 12 hours, and more preferably within 2 hours.

As the third feature,
For the 7000 series aluminum alloy material having the chemical component of the first characteristic,
It includes a step of performing a solution treatment, a step of performing molding in a heated mold, and a step of releasing from the mold and quenching to 250 ° C. or lower.
Quenching in this case may be performed by a mold different from the mold used in the molding process, or may be forced air cooling such as air blow or mist cooling, and any means that can provide a quenching effect is suitably employed.

The solution treatment conditions of the first, second, and third characteristics are desirably performed at a temperature of 400 ° C. or higher and lower than the melting point. If the temperature is lower than 400 ° C., sufficient strength cannot be obtained. A more desirable range is 450 ° C. or higher.
The solution treatment time can be appropriately set according to the solution treatment temperature as long as the effect of solution treatment is obtained. For example, if it is close to the melting point, the effect of solution treatment can be obtained even if it is 1 second, but if a time that satisfies the entire solution treatment temperature range is set, 5 seconds or more and 600 seconds or less are adopted. If it is less than 5 seconds, sufficient strength is difficult to obtain, and if it exceeds 600 seconds, the manufacturing cost increases. Therefore, 450 degreeC or more is more desirable.
Then, the forming process may be performed after the solution treatment is performed a plurality of times. For example, the material having undergone the first solution treatment is subjected to the second solution treatment after being cooled to room temperature, whereby the required strength and moldability can be easily obtained even if the second holding time is short. In this case, the cooling after the solution treatment is defined only for the cooling temperature during the molding process in the solution treatment of the first characteristic, and only the cooling temperature immediately before the molding process is defined in the solution treatment of the second characteristic. In the solution treatment having the feature 3, the required performance can be obtained if only the cooling rate after the molding process is defined.

In addition, in the heating of the mold having the third feature, it is desirable that the heating temperature is 400 ° C. or higher and lower than the melting point of the 7000 series aluminum alloy material.
When the temperature is lower than 400 ° C., precipitation of a solid solution element occurs during the molding process, and the moldability deteriorates and the strength after the molding process decreases.

  Further, in quenching, it is desirable that the cooling temperature from 400 ° C. to 250 ° C. is rapid cooling of 20 ° C./second or more. In addition, there exists a possibility that intensity | strength may fall that the cooling rate in this temperature range is less than 20 degree-C / sec. Therefore, it is more desirable that it is 40 ° C / second or more.

Next, a desirable manufacturing method of the alloy material up to the solution treatment will be described below. The following production methods are given as examples, and the present invention is not limited to the following methods.
Mainly, casting, homogenization, hot working, and cold working processes are employed.
Here, in the case of a plate material, hot rolling is generally used for hot working, and cold rolling is generally used for cold working. However, cold rolling is not necessarily required.
In the case of an extruded material, extrusion is generally used for hot working and drawing is generally used for cold working. However, the solution treatment is often performed in the extrusion without drawing.
Further, the ingot is formed by a DC casting method, and the homogenization heat treatment is preferably performed at a temperature of 430 ° C. or higher and lower than the melting point for 2 hours or longer and 100 hours or shorter. Here, if the temperature of the homogenization heat treatment is less than 430 ° C., cracks are likely to occur during the molding process. If the time for the homogenization heat treatment is less than 2 hours, the strength is insufficient, and if it exceeds 100 hours, the production cost may be remarkably increased.

  Moreover, it is preferable that the start temperature of hot processing is 400 degreeC or more and less than melting | fusing point. Here, if the start temperature of hot working is less than 400 ° C., it takes a lot of working time, which may increase the manufacturing cost.

  Then, intermediate annealing may be performed after hot working and before cold working or in the middle of cold working. 30% to 70% of the cold working rate after hot working is preferable when intermediate annealing is performed after intermediate annealing, and when intermediate annealing is not performed. The higher the cold working rate, the higher the strength due to the effect of crystal grain refinement. However, there is a risk that the manufacturing cost will increase due to a decrease in yield such as the occurrence of ear cracks in the forming process. Therefore, the final cold working rate is optimally 30 to 70% in order to prevent ear cracks in the molded product.

  As described above, based on the first, second, and third characteristics, a molded product manufactured by a method for forming a 7000 series aluminum alloy material has a high strength with a proof stress of 160 MPa or more after painting and baking. can do.

  Furthermore, the fourth characteristic is that the 7000 series aluminum alloy material is a rolled material in consideration of the first, second, and third characteristics.

  Furthermore, the fifth feature is that, based on the first, second, and third features, the 7000 series aluminum alloy material is an extruded material.

  Furthermore, the sixth feature is that the molded product is molded by a method of forming a 7000 series aluminum alloy material in consideration of the first, second, third, fourth, and fifth features.

  The present invention can be applied by simply and reliably forming a 7000 series aluminum alloy material in, for example, automobile body seats or members such as various housings, automobile parts such as bumpers and stehan beams, and two-wheel frames. Since it is possible to achieve weight reduction while ensuring the required strength, it has an excellent effect that can greatly contribute to environmental protection from the viewpoint of energy saving.

  Examples of the present invention will be described below. In addition, this Example is for showing one preferable embodiment of this invention, Comprising: This invention is not restrict | limited by this.

Therefore, examples of the aluminum alloy having the components shown in Table 1 (E1 to E19) and comparative examples (C1 to C11) described in the table are compared with press formability and mechanical strength (tensile strength before and after the coating baking process). , Yield strength, and elongation) were compared to confirm the effect of the present invention.

First, the aluminum alloy sheet material to be formed was ingoted by DC casting of aluminum alloys (E1 to E19) having the components shown in Table 1, and subjected to homogenization heat treatment at 480 ° C. for 10 hours.
Next, hot rolling to a plate thickness of 3 mm was performed after heating to 480 ° C.
And while performing the intermediate annealing for 2 hours at 480 degreeC, after cooling in a furnace to room temperature, it cold-rolled to plate | board thickness 1mm.
Furthermore, it was set as the aluminum alloy board | plate material which cut | disconnects to board thickness 1mm, board width 200mm, and length 250mm and uses for a shaping | molding process.

In addition, when examining the press formability regarding the presence or absence of the generation | occurrence | production of a crack, the shaping | molding process of the said aluminum alloy plate material was performed as follows.
First, as a first forming method, a molybdenum disulfide release agent is applied in advance to an aluminum alloy sheet, and then the aluminum alloy sheet is heated by an iron heating device composed of an upper mold and a lower mold. After heating at ℃ / second and holding at 480 ° C for 300 seconds (including heating time) for solution treatment, it is clamped and fixed between the upper and lower dies constituting the mold at 50 ° C At the same time as the press molding, the mold is rapidly cooled and quenched in the same mold to produce a U-shaped press molded product having a rectangular bottom surface.
Next, as a second forming method, the aluminum alloy sheet is heated in advance with an iron heating device composed of an upper mold and a lower mold at a heating rate of 15 ° C./second, and a solution treatment is performed. Therefore, after holding at 480 ° C. for 300 seconds (including the temperature rising time), after quenching by quenching to 50 ° C. rapidly (cooling rate: 40 ° C./second) in the material nipping cooling device, room temperature after 10 minutes of quenching A press-formed product having a rectangular U-shaped cross-section having a rectangular bottom surface is produced by press-molding using a low-viscosity lubricating oil while being sandwiched and fixed between an upper die and a lower die constituting the mold.
Further, as a third forming method, a molybdenum disulfide release agent is applied to the aluminum alloy sheet in advance, and then the aluminum alloy sheet is heated by an iron heating device composed of an upper mold and a lower mold. While heating at a rate of 15 ° C./second and holding at 480 ° C. for 300 seconds (including the temperature rising time) for solution treatment, it is sandwiched between the upper die and the lower die constituting the mold set at 480 ° C. It is fixed and press-molded, and the press-molded product is taken out once. The press-molded product is placed in a mold composed of an upper mold and a lower mold at room temperature, rapidly cooled (40 ° C./second) and quenched, and a U-shaped press having a rectangular bottom surface. A molded product is produced.

  In addition, the press-formed product was examined for formability regarding the presence or absence of forming cracks, and a rectangular test piece was cut out from the bottom surface of the press-formed product according to JIS Z2241, JIS No. 5 test piece. After press molding, after aging at 20 ° C. for 1 week at room temperature, the coating was baked and cured at 180 ° C. for 10 minutes, and the mechanical properties were examined.

The results of the first molding process (Table 2) and Examples (E1 to E19) show good moldability without cracking in the press-molded product, and are 160 MPa or more before and after the coating baking process. It was confirmed to show high strength mechanical properties such as having proof stress.

Next, in the homogenization heat treatment performed in manufacturing the aluminum alloy sheet, the formability and mechanical properties with respect to the homogenization heat treatment temperature and the homogenization heat treatment time were examined. Therefore, the homogenization heat treatment temperature and the homogenization time of Examples (E22 to E29) and Comparative Examples (C13 to C17) in the homogenization heat treatment were set to the conditions shown in Table 3 below.
In addition, the test piece which examines about the homogenization heat processing produced the test piece as mentioned above (other than the homogenization process) using the aluminum alloy which has a component of Example E1.

The results of the first molding method (Table 4) and Examples (E22 to E29) show good molding processability without causing cracks in the press-formed product, and 160 MPa or more before and after the paint baking process. It was confirmed that it exhibits high-strength mechanical properties such as

Next, in the hot rolling performed in manufacturing the aluminum alloy sheet, the formability and mechanical properties with respect to the hot rolling start temperature were examined. Therefore, the homogenization heat treatment temperature and the homogenization time of Examples (E30 to E32) and Comparative Examples (C18, C19) in the homogenization heat treatment were set to the conditions shown in Table 5 below.
In addition, the test piece which investigates about hot rolling temperature performed press molding using the aluminum alloy which has a component of Example E1, and produced the test piece as mentioned above (other than hot rolling temperature).

The results of the third press-molding method (Table 6) and Examples (E30 to E32) show good moldability without causing cracks in the press-molded product, and are 160 MPa or more before and after the coating baking process. It was confirmed that it exhibits high-strength mechanical properties such as

Next, in the solution treatment performed in manufacturing the aluminum alloy sheet, the formability and mechanical properties with respect to the solution treatment temperature and the solution treatment time were examined. Therefore, the solution treatment temperature and the solution treatment time of the examples (E34 to E41) and the comparative examples (C20, C21) in the solution treatment were set to the conditions shown in Table 7 below.
In addition, the test piece which considers about a solution treatment produced the test piece as mentioned above using the aluminum alloy which has a component of Example E1 (except solution treatment conditions).

The results of the third forming method (Table 8) and Examples (E34 to E41) show good forming workability without causing cracks in the press-formed product, and 160 MPa or more before and after the paint baking process. It was confirmed to exhibit high-strength mechanical properties having a yield strength of.

Next, in the cooling after the solution treatment performed in manufacturing the aluminum alloy sheet, the formability and mechanical properties with respect to the cooling rate conditions were examined. Therefore, the cooling conditions, mold temperature (° C.) and cooling rate conditions (° C./second) of the examples (E42 to E45) and the comparative examples (C26, C27) in the cooling after the solution treatment are the conditions shown in Table 9 below. Set to.
In addition, the test piece which considers about the cooling after solution treatment processed the test piece similarly as mentioned above using the aluminum alloy which has a component of Example E1 (other than cooling conditions).

The results of the second forming method (Table 10) and Examples (E42 to E45) show good forming workability without causing cracks in the press-formed product, and 160 MPa or more before and after the paint baking process. It was confirmed that it exhibits high-strength mechanical properties such as

Next, in order to verify the influence of the forming processability method, the forming processability and mechanical properties were examined using aluminum alloy plates having chemical components E1 and E4.
These alloys were ingoted by DC casting and subjected to a homogenization heat treatment at 470 ° C. for 12 hours. Next, hot rolling was performed as it was from the homogenization treatment temperature to obtain a plate thickness of 6 mm. And after performing the intermediate annealing for 1 hour at 360 degreeC, it cold-rolled to plate | board thickness 2mm. Furthermore, it was cut into a plate thickness of 2 mm, a plate width of 200 mm, and a length of 250 mm to obtain an aluminum alloy plate material used for press forming.

As a result of the first to third molding methods (component E1 is Table 13 and component E4 is Table 14), all show good moldability without causing cracks in the press-formed product, and paint baking treatment It was confirmed that high strength mechanical properties such as having a proof stress of 160 MPa or more were exhibited before and after.

Next, in order to verify the conditions of the first and third forming methods, an aluminum alloy having an E1 chemical component was ingoted by DC casting, and subjected to a homogenization heat treatment at 470 ° C. for 12 hours. Next, hot rolling was performed as it was from the homogenization treatment temperature to obtain a plate thickness of 6 mm, followed by cold rolling to a plate thickness of 2 mm. Furthermore, it was cut into a plate thickness of 2 mm, a plate width of 200 mm, and a length of 250 mm to obtain an aluminum alloy plate material used for press forming.
After previously applying a release agent to the aluminum alloy sheet, the aluminum alloy sheet was subjected to a solution treatment by heating with a heating device under the conditions shown in Table 13,
Regarding the first molding method, a cross section having a bottom surface, which is molded and quenched by press molding in the same mold and cooling under the conditions shown in Table 13 (cooling rate measured at 400 to 250 ° C.). A U-shaped press-molded product was produced.
Regarding the third molding method, press molding is performed in a mold at 420 ° C., and cooling is performed under the conditions shown in Table 13 after mold release (cooling rate is measured at 400 to 250 ° C.), thereby forming and quenching. This was carried out to produce a U-shaped press-formed product having a bottom surface. The condition of E55 is a condition in which a solution treatment for 120 s is performed at 470 ° C. in advance, and a water-cooled (1000 ° C./s) material is re-solution treated.

As a result of the first and third molding methods (Table 14 for the first molding method and Table 15 for the third molding method), Examples (E56 to E63) show that cracks occur in the press-formed product. It was confirmed that the film exhibited good molding processability with no mechanical properties, and exhibited high strength mechanical properties such as having a proof stress of 160 MPa or more before and after the coating baking process.
However, in the comparative examples (C29 to C34), since the solution treatment temperature is too high, the press cracking due to local melting or the solution treatment is performed at a low temperature or too short time, resulting in a decrease in ductility due to lack of solid solution of solute elements. occured.

Next, in order to verify the influence of the room temperature aging time of the second forming method, an aluminum alloy having a chemical component of E1 was ingoted by DC casting and subjected to homogenization heat treatment at 470 ° C. for 12 hours. Next, hot rolling was performed as it was from the homogenization treatment temperature to obtain a plate thickness of 6 mm, followed by cold rolling to a plate thickness of 2 mm. Furthermore, it was cut into a plate thickness of 2 mm, a plate width of 200 mm, and a length of 250 mm to obtain an aluminum alloy plate material used for press forming.
The aluminum alloy sheet was subjected to solution treatment by heating at 470 ° C. to 90 s with a heating device, and then rapidly cooled (cooling rate of 400 to 250 ° C. at 50 ° C./second) to room temperature, and then quenched. The punch radius of the cross-sectional U-shape having a bottom surface: R (mm) by changing the time and press-molding using a low-viscosity lubricant while being clamped and fixed between the upper mold and the lower mold constituting the mold A press-molded product was produced using a mold having different dies.

As a result, the examples (E64 to 68) exhibited molding processability without causing cracks in the molded product, although depending on the punch press radius.
However, in Comparative Example (C35), since the room temperature aging time was too long, cracks occurred in the molded product even when the punch press radius was 15 mm.

Next, for the first, second, and third molding methods, the moldability was examined using extruded shapes. An aluminum alloy having a chemical component of E1 was ingoted by DC casting and subjected to a homogenization heat treatment at 470 ° C. for 15 hours. Next, an L-shaped extruded material having a plate thickness of 2.5 mm and a side of 40 mm was produced by hot extrusion, cut into a length of 400 mm, and subjected to bending workability by press molding. Both ends of a 400 mm extruded profile were 50 mm at a bending angle of 30 ° and a bending radius of 15 mm, and the presence or absence of cracks in the bent portion and the mechanical properties of the central portion were investigated.
After the aluminum alloy profile was subjected to solution treatment with a heating device under the conditions shown in Table 17,
Regarding the first molding method, press molding and cooling under the conditions shown in Table 17 (cooling rate measured at 400 to 250 ° C.) are performed in the same mold to perform molding and quenching. Produced.
Regarding the 2nd shaping | molding processing method, after cooling on the conditions of Table 17 (cooling rate is measured at 400-250 degreeC), the press molding product was produced by press-molding 10 minutes after room temperature.
Regarding the third molding method, press molding is performed in a mold at 450 ° C., and cooling is performed under the conditions shown in Table 17 after mold release (cooling rate is measured at 400 to 250 ° C.), thereby forming and quenching. Implemented and produced a press-formed product.

Results of the first, second, and third molding methods (Table 18 for the first molding method, Table 19 for the second molding method, and Table 20 for the third molding method), Examples (E69 to E69) E74) has been confirmed to exhibit good formability without causing cracks in press-formed products, and to exhibit high-strength mechanical properties such as having a proof stress of 160 MPa or more before and after the coating baking process. It was.
However, in the comparative examples (C36 to C41), since the solution treatment temperature was too high, press cracks caused by local melting and press treatment due to insufficient solid solution of solute elements caused press cracks due to local melting and solution treatment was too low.

  The present invention can easily and reliably form a lightweight and high-strength aluminum alloy material on a member that requires light weight and strength such as an automobile fender or bumper. It can be applied to any member that is lightweight and requires high strength.

Claims (9)

Zn: 2.0% by mass (hereinafter referred to as “%”) or more, 10% or less, Mg: 0.10% or more, 5.0% or less, Cu: 5.0% or less, Mn: 1.5% Hereinafter, Si: 1.0% or less, Fe: 1.0% or less, Cr: 0.50% or less, Zr: 0.50% or less, Ti: 0.30% or less, the balance being aluminum and inevitable For 7000 series aluminum alloy material consisting of mechanical impurities,
Performing a solution treatment; and
The process of molding in the mold,
A method for forming a 7000 series aluminum alloy material, comprising a quenching step up to 250 ° C. or less with the mold. A method of forming a 7000 series aluminum alloy material having the chemical component according to claim 1,
For the 7000 series aluminum alloy material,
Performing a solution treatment; and
A step of quenching to 250 ° C. or less;
A method of forming a 7000 series aluminum alloy material, comprising a step of forming a mold in a mold within 120 hours after the quenching. A method of forming a 7000 series aluminum alloy material having the chemical component according to claim 1,
For the 7000 series aluminum alloy material,
Performing a solution treatment; and
A step of performing molding in a heated mold;
A method for forming a 7000 series aluminum alloy material, comprising a step of releasing from the mold and quenching to 250 ° C. or less.   3. A method for forming a 7000 series aluminum alloy material according to claim 1, wherein the solution treatment is performed at a temperature of 400 ° C. or higher and lower than the melting point.   In the solution treatment and heating of the mold according to claim 3, the solution treatment is performed at a temperature of 400 ° C. or higher and lower than the melting point, and the mold is heated at a temperature of 400 ° C. or higher and lower than the melting point. A forming method of a 7000 series aluminum alloy material.   The method for forming a 7000 series aluminum alloy material according to any one of claims 1 to 5, wherein in the quenching, a cooling temperature from 400 ° C to 250 ° C is set to 20 ° C / second or more.   The method for forming a 7000 series aluminum alloy material according to any one of claims 1 to 6, wherein the 7000 series aluminum alloy material is a rolled material.   The method for forming a 7000 series aluminum alloy material according to any one of claims 1 to 6, wherein the 7000 series aluminum alloy material is an extruded material.   A molded article formed by the method for molding a 7000 series aluminum alloy material according to any one of claims 1 to 8.