JP2009299104A5

JP2009299104A5 -

Info

Publication number: JP2009299104A5
Application number: JP2008152447A
Authority: JP
Filing date: 2008-06-11
Publication date: 2010-05-06
Anticipated expiration: 2028-06-11

Description

具体的には、請求項１の発明の高温成形方法は、Ｃｕを実質的に含有しないＡｌ−Ｍｇ−Ｓｉ系合金板を成形用素材とし、その合金板について、４８０℃以上の温度域で成形加工を施した後、２℃／ｓｅｃ以上の冷却速度で、２００℃以下５０℃以上の温度域まで冷却し、引続き直ちに１４０〜２４０℃の範囲内の温度に、１５分以下１秒以上保持する予備時効処理を行なうことを特徴とするものである。 Specifically, the high temperature forming method of the invention of claim 1 uses an Al— Mg—Si based alloy plate substantially free of Cu as a forming material, and the alloy plate is formed in a temperature range of 480 ° C. or higher. After processing, it is cooled to a temperature range of 200 ° C. or lower and 50 ° C. or higher at a cooling rate of 2 ° C./sec or higher, and then immediately maintained at a temperature within the range of 140 to 240 ° C. for 15 minutes or shorter and 1 second or longer. Preliminary aging treatment is performed.

また請求項２の発明は、Ｃｕを含むＡｌ−Ｍｇ−Ｓｉ系合金板を成形用素材とし、その合金板について、４８０℃以上の温度域で成形加工を施した後、２℃／ｓｅｃ以上の冷却速度で、２００℃以下の温度域まで冷却し、引続き直ちに１４０〜２４０℃の範囲内の温度に、１５分以下１秒以上保持する予備時効処理を行なうことを特徴とするものである。 The invention of claim 2 uses an Al- Mg-Si alloy plate containing Cu as a forming material, and the alloy plate is formed at a temperature range of 480 ° C or higher, and then 2 ° C / sec or higher. It is characterized in that it is cooled to a temperature range of 200 ° C. or lower at a cooling rate, and then a preliminary aging treatment is performed immediately at a temperature in the range of 140 to 240 ° C. for 15 minutes or less and 1 second or longer.

さらに請求項３の発明は、Ｍｇ０．３〜１．２％、Ｓｉ０．４〜１．６％、Ｆｅ０．０１〜０．４％を含有し、さらにＭｎ０．０１〜１．３％、Ｃｒ０．０１〜０．３％、Ｚｒ０．０１〜０．３％、Ｓｃ０．０１〜０．５％、Ｖ０．０１〜０．３％のうちから選ばれた１種または２種以上を含有し、残部がＡｌおよび不可避的不純物よりなるＡｌ−Ｍｇ−Ｓｉ系合金板を成形用素材とし、その合金板について、４８０℃以上の温度域で成形加工を施した後、２℃／ｓｅｃ以上の冷却速度で、２００℃以下５０℃以上の温度域まで冷却し、引続き直ちに１４０〜２４０℃の範囲内の温度に、１５分以下１秒以上保持する予備時効処理を行なうことを特徴とするものである。 Further, the invention of claim 3 contains Mg 0.3 to 1.2%, Si 0.4 to 1.6%, Fe 0.01 to 0.4%, Mn 0.01 to 1.3%, Cr 0. Containing one or more selected from 01 to 0.3%, Zr 0.01 to 0.3%, Sc 0.01 to 0.5%, V 0.01 to 0.3%, An Al- Mg-Si based alloy plate, the balance of which is Al and inevitable impurities, is used as a forming material, and the alloy plate is subjected to forming processing in a temperature range of 480 ° C or higher, and then a cooling rate of 2 ° C / sec or higher. Then, it is cooled to a temperature range of 200 ° C. or lower and 50 ° C. or higher, and then a preliminary aging treatment is performed immediately at a temperature in the range of 140 to 240 ° C. for 15 minutes or shorter and 1 second or longer.

またさらに請求項４の発明は、Ｍｇ０．３〜１．２％、Ｓｉ０．４〜１．６％、Ｆｅ０．０１〜０．４％、Ｃｕ０．０１〜１．０％を含有し、さらにＭｎ０．０１〜１．３％、Ｃｒ０．０１〜０．３％、Ｚｒ０．０１〜０．３％、Ｓｃ０．０１〜０．５％、Ｖ０．０１〜０．３％のうちから選ばれた１種または２種以上を含有し、残部がＡｌおよび不可避的不純物よりなるＡｌ−Ｍｇ−Ｓｉ系合金板を成形用素材とし、その合金板について、４８０℃以上の温度域で成形加工を施した後、２℃／ｓｅｃ以上の冷却速度で、２００℃以下の温度域まで冷却し、引続き直ちに１４０〜２４０℃の範囲内の温度に、１５分以下１秒以上保持する予備時効処理を行なうことを特徴とするものである。 Furthermore, the invention of claim 4 contains Mg 0.3-1.2%, Si 0.4-1.6%, Fe 0.01-0.4%, Cu 0.01-1.0%, and further Mn0 .01 to 1.3%, Cr 0.01 to 0.3%, Zr 0.01 to 0.3%, Sc 0.01 to 0.5%, V 0.01 to 0.3%. An Al- Mg-Si based alloy plate containing one or more types, the balance being Al and inevitable impurities was used as a forming material, and the alloy plate was formed in a temperature range of 480 ° C or higher. After that, it is cooled to a temperature range of 200 ° C. or lower at a cooling rate of 2 ° C./sec or higher, and then a preliminary aging treatment is performed immediately at a temperature within the range of 140 to 240 ° C. for 15 seconds or shorter for 1 second or longer. It is a feature.

Ｃｕ：
Ｃｕは人工時効処理を兼ねた塗装焼付け処理時に析出するＭｇ_２Ｓｉを微細かつ均一にする効果があり、そのためＣｕを添加することにより、塗装焼付け処理における耐力上昇幅が増大する。さらに、Ｃｕの添加は、高温成形後に５０℃未満の温度域まで冷却した際に形成される低温クラスタと称されるＭｇとＳｉからなる極微細析出物の形成を遅らせる効果がある。後に詳細に説明するように、この低温クラスタが析出してしまえば、塗装焼付け処理時の時効による効果が抑制されてしまい、耐力の上昇幅が大幅に低下するが、Ｃｕを添加すれば低温クラスタの形成が遅れるため、耐力の上昇幅の低下を抑えることが可能となる。そこで請求項２、請求項４の各発明の高温成形方法の場合は、Ｃｕを積極的に添加したＡｌ−Ｍｇ−Ｓｉ系合金を用いることとした。ここでＣｕを添加した場合には、前述のように低温クラスタの形成が遅れるため、高温成形後の冷却終了温度を５０℃以下の低温としても、この冷却終了温度での保持時間が短時間であれば、塗装焼付け処理時の時効による耐力の向上幅が低下するようなことがない。この場合、冷却終了温度での保持時間は１時間以内であればよいが、高温成形後の曲げ加工性の向上と塗装焼付け処理時の耐力の上昇とをより充分に図るため、および生産性をより高めるためには、保持時間を５分以内とすることが好ましい。なおＣｕの添加量が０．０１％未満では、Ｃｕ添加による上述の効果が充分に得られず、一方Ｃｕの添加量が１．０％を越えれば、成形品の耐食性が大幅に低下してしまい、自動車ボディパネル等の腐食環境に曝される部材として不適当となるから、Ｃｕを添加する場合のＣｕ量は、請求項４に示すように０．０１〜１．０％の範囲内とした。なおＣｕを積極的に添加しない請求項３の発明の場合も、不純物として０．０１％未満のＣｕが含まれることがあることはもちろんである。 Cu:
Cu has the effect of making Mg ₂ Si precipitated during the paint baking process also serving as an artificial aging process fine and uniform. Therefore, the addition of Cu increases the yield strength increase in the paint baking process. Furthermore, the addition of Cu has the effect of delaying the formation of ultrafine precipitates composed of Mg and Si, which are called low temperature clusters formed when cooled to a temperature range below 50 ° C. after high temperature molding. As will be described in detail later, if this low temperature cluster is precipitated, the effect due to aging during the coating baking process is suppressed, and the increase in the yield strength is greatly reduced. However, if Cu is added, the low temperature cluster is reduced. Therefore, it is possible to suppress a decrease in the increase in the yield strength. Therefore, in the case of the high temperature forming method of each invention of claims 2 and 4, an Al-Mg-Si alloy to which Cu is positively added is used. When Cu is added here, the formation of low-temperature clusters is delayed as described above, so even if the cooling end temperature after high-temperature forming is set to a low temperature of 50 ° C. or less, the holding time at this cooling end temperature is short. If there is, the improvement width of the proof stress due to aging during the paint baking process is not reduced. In this case, the holding time at the cooling end temperature may be 1 hour or less, but in order to sufficiently improve the bending workability after high-temperature forming and increase the yield strength during the coating baking process, and improve productivity. In order to further increase, the holding time is preferably within 5 minutes. In addition, if the addition amount of Cu is less than 0.01%, the above-described effects due to the addition of Cu cannot be sufficiently obtained. On the other hand, if the addition amount of Cu exceeds 1.0%, the corrosion resistance of the molded product is greatly reduced. Therefore, since it becomes unsuitable as a member exposed to a corrosive environment such as an automobile body panel, the amount of Cu when Cu is added is within the range of 0.01 to 1.0% as shown in claim 4. did. In the case of the invention of claim 3 in which Cu is not actively added, it is needless to say that less than 0.01% of Cu may be contained as an impurity.

以上の各元素のほかは、基本的には不可避不純物およびＡｌとすればよいが、鋳塊組織を微細にするためにＴｉ０．０１〜０．１５％を、単独あるいはＢ０．０００１〜０．０５％とともに添加することは許容される。但し、Ｔｉ添加量が０．１０％を越え、かつＢ添加量が０．０１％を越えれば、鋳造時にこれらを主成分とする粗大な化合物が晶出して、材料の特性ならびに靭性が大幅に低下してしまい、またＴｉ添加量が０．１５％を越えれば、鋳造時にＴｉＡｌ_３の粗大化合物が晶出し、材料の延性ならびに靭性が大幅に低下してしまう。さらにＢ添加量が０．０５％を越えれば、鋳造時にＴｉＢ_２の粗大化合物が晶出し、材料の延性ならびに靭性が大幅に低下してしまう。そこでＴｉを単独で添加する場合のＴｉ添加量は０．１５％以下とすることが好ましく、またＴｉをＢとともに添加する場合のＴｉ量は０．１０％以下、Ｂ量は０．０１％以下とすることが好ましい。 In addition to the above elements, basically, inevitable impurities and Al may be used. However, in order to make the ingot structure fine, Ti 0.01 to 0.15% is used alone or B0.0001 to 0.05. % Is acceptable. However, if the Ti addition amount exceeds 0.10% and the B addition amount exceeds 0.01%, coarse compounds mainly composed of these crystallize during casting, and the characteristics and toughness of the material are greatly increased. If the Ti addition amount exceeds 0.15%, a coarse compound of TiAl ₃ crystallizes during casting, and the ductility and toughness of the material are greatly reduced. In addition exceeds B addition amount of 0.05%, crude large compound of TiB ₂ at the time of casting is crystallized, ductility and toughness of the material is greatly reduced. Therefore, the Ti addition amount when adding Ti alone is preferably 0.15% or less, and the Ti amount when adding Ti together with B is 0.10% or less, and the B amount is 0.01% or less. It is preferable that

また成形品を室温で１０日間保持した後の塗装焼付け処理に相当する時効処理を行なう前の成形品の耐力値と、塗装焼付け処理に相当する時効処理を行なった後の成形品の耐力値を比較して、３０ＭＰａ以上の耐力値の向上があった場合には、塗装焼付け処理により充分な耐力値の向上があるものと判定した。また塗装焼付け処理に相当する時効後の成形品の耐力値が１７０ＭＰａ以上の場合に、ボディシートとして適用が可能であると判定した。さらに総合的な判断として、曲げ加工性が良好でかつこれら二つの耐力値の判定基準を満たす場合に、ボディパネル用の成形品として、より適していると判定した。
これらの試験結果、判定結果を表２に示す。 Also, the yield strength value of the molded product before the aging treatment corresponding to the paint baking process after holding the molded article at room temperature for 10 days and the proof stress value of the molded product after the aging treatment equivalent to the paint baking process are given. In comparison, when there was an improvement in the yield strength of 30 MPa or more, it was determined that there was a sufficient improvement in the yield strength by the coating baking process. Moreover, when the proof stress value of the molded product after aging corresponding to the paint baking process was 170 MPa or more, it was determined that the product can be applied as a body sheet. Furthermore, as a comprehensive judgment, when the bending workability was good and the judgment criteria of these two proof stress values were satisfied, it was judged that it was more suitable as a molded product for a body panel.
These test results and determination results are shown in Table 2.

本発明例の合金１〜５は、いずれもこの発明で規定する成分組成の範囲内の合金を用い、この発明で規定する条件にて高温成形およびその後の冷却、予備時効処理を行なったものである。これらの本発明例では、高温成形後１０日間室温保持後に行なった曲げ加工において、曲げ部の外側で割れが生じることはなく、良好な曲げ性を示した。また高温成形後１０日間室温保持後において、塗装焼付け処理相当の時効後の耐力は、塗装焼付け処理相当の時効前の耐力と比較して３０ＭＰａ以上向上していて、塗装焼付け処理相当の時効により充分な耐力値の上昇が認められ、なおかつ塗装焼付け処理相当の時効処理後耐力として、１７０ＭＰａ以上の高い耐力値が得られた。 Alloys 1 to 5 in the examples of the present invention are all alloys in the range of the component composition defined in the present invention, and subjected to high temperature forming, subsequent cooling and pre-aging treatment under the conditions defined in the present invention. is there. In these examples of the present invention, in bending performed after holding at room temperature for 10 days after high temperature molding, cracks did not occur outside the bent portion, and good bendability was exhibited. In addition, after holding at room temperature for 10 days after high-temperature molding, the yield strength after aging equivalent to the paint baking process is improved by 30 MPa or more compared to the pre-aging resistance equivalent to the paint baking process. such increase in proof stress was recognized, as yet aging treatment after strength of paint baking equivalent, high it has proof stress on 170MPa or more was obtained.

これらの合金板について、次に説明する条件で高温ブロー成形およびその後の冷却、予備時効処理を行なった。高温ブロー成形については、前述の実施例１の場合と同様に、平面部が３００ｍｍ×３００ｍｍの大きさで、高さが８０ｍｍのフランジ付き角筒形状の成形品が得られる金型を用い、実施例１の場合と同様に高温ブロー成形機にセットした合金板の片側からガス圧を付与して、ガス圧を１気圧から１０気圧まで１分間で昇圧して、１０気圧の状態で１分間保持し、合計２分間の高温成形を行なった後に、ガス圧を１気圧まで減圧する方法を適用した。具体的な成形条件としては、先ず予備加熱として、合金板を所定の成形温度まで１０℃／ｓｅｃの昇温速度で加熱後、合金板を成形機にセットした。その後、実施例１の場合と同様に所定の成形温度で成形を完了させた後、所定の冷却速度にて、所定の冷却終了温度まで冷却後、直ちに所定の予備時効処理温度にて所定時間予備時効処理を行ない、室温まで冷却した。このような実施例のプロセスについて、成形温度、冷却速度、冷却終了温度、予備時効処理温度、予備時効処理時間、予備時効後に曲げ加工および塗装焼付け相当処理を行なうまでに経過した日数の条件を、表４にまとめて示す。 These alloy plates were subjected to high temperature blow molding, subsequent cooling, and pre-aging treatment under the conditions described below. As with the case of Example 1 described above, high-temperature blow molding is performed using a mold that can obtain a flanged square tube-shaped molded product having a plane portion of 300 mm × 300 mm and a height of 80 mm. As in the case of Example 1, gas pressure is applied from one side of the alloy plate set in the high-temperature blow molding machine, and the gas pressure is increased from 1 atm to 10 atm in 1 minute and held at 10 atm for 1 minute. Then, after performing high temperature molding for a total of 2 minutes, a method of reducing the gas pressure to 1 atm was applied. As specific forming conditions, first, as preheating, the alloy plate was heated to a predetermined forming temperature at a heating rate of 10 ° C./sec, and then the alloy plate was set in a forming machine. After that, after completion of molding at a predetermined molding temperature in the same manner as in Example 1, after cooling to a predetermined cooling end temperature at a predetermined cooling rate, immediately preliminarily for a predetermined time at a predetermined preliminary aging temperature. An aging treatment was performed and the mixture was cooled to room temperature. Regarding the process of such an example , the molding temperature, cooling rate, cooling end temperature, preliminary aging treatment temperature, preliminary aging treatment time, conditions for the number of days that have passed before the preparatory aging and bending baking and equivalent processing are performed, Table 4 summarizes the results.

比較例である条件１の場合は、成形温度がこの発明で規定する範囲よりも低く、そのため、マトリックス中に未固溶のＭｇおよびＳｉが多数存在し、Ｍｇ、Ｓｉの固溶量が少なくなったため、高温成形後の曲げ性が不良となり、また塗装焼付け処理相当の時効処理による耐力の上昇が少なかった。これに対し本発明例である条件２、３、４の場合は、いずれも成形温度がこの発明で規定する範囲内であり、この場合は曲げ性、耐力値ともに良好となった。 If condition 1 is a comparative example is lower than the range of the molding temperature is stipulated in the present invention, therefore, there are many Mg and Si undissolved in the matrix, Mg, dissolved amount of Si Because of the decrease, the bendability after high-temperature molding became poor, and the increase in yield strength due to the aging treatment equivalent to the paint baking treatment was small. On the other hand, in the cases 2, 3, and 4 which are examples of the present invention, the molding temperature is within the range specified by the present invention, and in this case, both the bendability and the proof stress are good.

また比較例である条件８は、特にＣｕを含有しないＡｌ−Ｍｇ−Ｓｉ系合金を用いて、高温成形後の冷却終了温度の条件がこの発明で規定する冷却終了温度を越えたものである。この場合は、引続いて行なわれる予備時効処理温度に移行する間に結晶粒界上に粗大なＭｇ_２Ｓｉ粒子が多数析出し、この粒界上の析出粒子がその後に行なわれる曲げ加工時に割れの起点となって、曲げ性が大幅に低下した。これに対し本発明例である条件９、条件１０および条件１１は、同様にＣｕを含有しないＡｌ−Ｍｇ−Ｓｉ系合金を用い、高温成形後の冷却終了温度の条件をはじめとするすべての条件をこの発明の範囲内としたものであり、これらの場合は、曲げ性、耐力ともに良好であった。一方、比較例である条件１２は、Ｃｕを含有しないＡｌ−Ｍｇ−Ｓｉ系合金を用い、高温成形後の冷却終了温度が請求項２の発明で規定する範囲よりも低かったものであり、この場合は、冷却終了温度である４０℃付近の温度域でＭｇとＳｉよりなる低温クラスタが多数形成され、その低温クラスタはその後の塗装焼付け処理に相当する時効によって耐力の増加に寄与する微細なＭｇ_２Ｓｉ析出物には直接変化しないため、塗装焼付け処理に相当する時効処理による耐力の上昇が小さくなってしまった。 In addition, Condition 8 as a comparative example is that in which an Al—Mg—Si based alloy not containing Cu is used, and the condition of the cooling end temperature after the high temperature forming exceeds the cooling end temperature defined in the present invention. In this case, a large number of coarse Mg ₂ Si particles are precipitated on the grain boundaries during the transition to the subsequent pre-aging temperature, and the precipitated particles on the grain boundaries are cracked during the subsequent bending process. As a starting point, the bendability was greatly reduced. In contrast an invention example condition 9, Condition 10 and Condition 11, using the Al-Mg-Si based alloy containing no similarly Cu, the all the other internationalization condition of the cooling end temperature after the high temperature molding It is obtained by the condition in the range of inventions of this, in these cases, bendability was good in strength both. On the other hand, Condition 12, which is a comparative example, uses an Al—Mg—Si-based alloy that does not contain Cu, and the cooling end temperature after high-temperature forming is lower than the range defined in the invention of claim 2. In this case, a large number of low-temperature clusters composed of Mg and Si are formed in the temperature range around 40 ° C. that is the cooling end temperature, and the low-temperature clusters are fine Mg that contributes to an increase in yield strength by aging corresponding to the subsequent coating baking process. _{Since 2} Si precipitates do not change directly, the increase in yield strength due to the aging treatment corresponding to the coating baking treatment has been reduced.

Claims

Ｃｕを実質的に含有しないＡｌ−Ｍｇ−Ｓｉ系合金板を成形用素材とし、その合金板について、４８０℃以上の温度域で成形加工を施した後、２℃／ｓｅｃ以上の冷却速度で、２００℃以下５０℃以上の温度域まで冷却し、引続き直ちに１４０〜２４０℃の範囲内の温度に、１５分以下１秒以上保持する予備時効処理を行なうことを特徴とする、Ａｌ−Ｍｇ−Ｓｉ系合金板の高温成形方法。 An Al— Mg—Si based alloy plate that does not substantially contain Cu is used as a forming material, and the alloy plate is subjected to forming processing in a temperature range of 480 ° C. or higher, and at a cooling rate of 2 ° C./sec or higher. Al-Mg-Si, characterized in that it is cooled to a temperature range of 200 ° C or lower and 50 ° C or higher, and then immediately subjected to a pre-aging treatment at a temperature within the range of 140 to 240 ° C and held for 15 seconds or shorter for 1 second or longer. Method for high-temperature forming of an alloy plate.

Ｃｕを含むＡｌ−Ｍｇ−Ｓｉ系合金板を成形用素材とし、その合金板について、４８０℃以上の温度域で成形加工を施した後、２℃／ｓｅｃ以上の冷却速度で、２００℃以下の温度域まで冷却し、引続き直ちに１４０〜２４０℃の範囲内の温度に、１５分以下１秒以上保持する予備時効処理を行なうことを特徴とする、Ａｌ−Ｍｇ−Ｓｉ系合金板の高温成形方法。 An Al— Mg—Si based alloy plate containing Cu is used as a forming material, and the alloy plate is subjected to forming processing at a temperature range of 480 ° C. or higher, and then at a cooling rate of 2 ° C./sec. A method of high-temperature forming an Al-Mg-Si alloy sheet, characterized by performing a pre-aging treatment that is cooled to a temperature range and then immediately maintained at a temperature in the range of 140 to 240 ° C for 15 seconds or less for 1 second or longer. .

Ｍｇ０．３〜１．２％（ｍａｓｓ％、以下同じ）、Ｓｉ０．４〜１．６％、Ｆｅ０．０１〜０．４％を含有し、さらにＭｎ０．０１〜１．３％、Ｃｒ０．０１〜０．３％、Ｚｒ０．０１〜０．３％、Ｓｃ０．０１〜０．５％、Ｖ０．０１〜０．３％のうちから選ばれた１種または２種以上を含有し、残部がＡｌおよび不可避的不純物よりなるＡｌ−Ｍｇ−Ｓｉ系合金板を成形用素材とし、その合金板について、４８０℃以上の温度域で成形加工を施した後、２℃／ｓｅｃ以上の冷却速度で、２００℃以下５０℃以上の温度域まで冷却し、引続き直ちに１４０〜２４０℃の範囲内の温度に、１５分以下１秒以上保持する予備時効処理を行なうことを特徴とする、Ａｌ−Ｍｇ−Ｓｉ系合金板の高温成形方法。 Mg 0.3 to 1.2% (mass%, the same shall apply hereinafter), Si 0.4 to 1.6%, Fe 0.01 to 0.4%, Mn 0.01 to 1.3%, Cr 0.01 0.3%, containing Zr0.01~0.3%, Sc0.01~0.5%, 1 or more kinds selected from among V 0.01 to 0.3%, the balance An Al —Mg—Si based alloy plate made of Al and inevitable impurities is used as a forming material, and the alloy plate is formed at a temperature range of 480 ° C. or higher and then cooled at a cooling rate of 2 ° C./sec or higher. The pre-aging treatment is carried out by cooling to a temperature range of 200 ° C. or lower and 50 ° C. or higher, and then immediately holding at a temperature within the range of 140 to 240 ° C. for 15 minutes or shorter for 1 second or longer. A high-temperature forming method for Si-based alloy plates.

Ｍｇ０．３〜１．２％、Ｓｉ０．４〜１．６％、Ｆｅ０．０１〜０．４％、Ｃｕ０．０１〜１．０％を含有し、さらにＭｎ０．０１〜１．３％、Ｃｒ０．０１〜０．３％、Ｚｒ０．０１〜０．３％、Ｓｃ０．０１〜０．５％、Ｖ０．０１〜０．３％のうちから選ばれた１種または２種以上を含有し、残部がＡｌおよび不可避的不純物よりなるＡｌ−Ｍｇ−Ｓｉ系合金板を成形用素材とし、その合金板について、４８０℃以上の温度域で成形加工を施した後、２℃／ｓｅｃ以上の冷却速度で、２００℃以下の温度域まで冷却し、引続き直ちに１４０〜２４０℃の範囲内の温度に、１５分以下１秒以上保持する予備時効処理を行なうことを特徴とする、Ａｌ−Ｍｇ−Ｓｉ系合金板の高温成形方法。 Mg 0.3 to 1.2%, Si 0.4 to 1.6%, Fe 0.01 to 0.4%, Cu 0.01 to 1.0%, further Mn 0.01 to 1.3%, Cr0 .01～0.3%, containing Zr0.01~0.3%, Sc0.01~0.5%, 1 or more kinds selected from among V 0.01 to 0.3% Then, an Al— Mg—Si based alloy plate consisting of Al and inevitable impurities is used as a forming material, and the alloy plate is formed at a temperature of 480 ° C. or higher and then cooled at 2 ° C./sec or higher. The Al—Mg—Si is characterized in that it is cooled to a temperature range of 200 ° C. or less at a rate and is immediately subjected to a pre-aging treatment at a temperature in the range of 140 to 240 ° C. for 15 minutes or less for 1 second or longer. Method for high-temperature forming of an alloy plate.

請求項１〜請求項４のいずれかの請求項に記載の高温成形方法によって製造された成形品であって、前記予備時効処理後、１５日以内に行なわれる曲げ加工での曲げ性が良好で、かつ前記予備時効処理後、１５日以内に行なわれる１７０℃×２０分の塗装焼付け処理により耐力が３０ＭＰａ以上高くなって、１７０ＭＰａ以上の耐力値を示すことを特徴とする、Ａｌ−Ｍｇ−Ｓｉ系合金からなる高温成形品。 It is a molded article manufactured by the high temperature molding method according to any one of claims 1 to 4, and has good bendability in bending performed within 15 days after the preliminary aging treatment. In addition, Al-Mg-Si is characterized in that the yield strength is increased by 30 MPa or more by a paint baking process at 170 ° C. for 20 minutes performed within 15 days after the preliminary aging treatment, and exhibits a yield value of 170 MPa or more. High-temperature molded product made of an alloy.