JP2001288523A - High formability aluminum alloy sheet and its producing method - Google Patents
High formability aluminum alloy sheet and its producing methodInfo
- Publication number
- JP2001288523A JP2001288523A JP2001003248A JP2001003248A JP2001288523A JP 2001288523 A JP2001288523 A JP 2001288523A JP 2001003248 A JP2001003248 A JP 2001003248A JP 2001003248 A JP2001003248 A JP 2001003248A JP 2001288523 A JP2001288523 A JP 2001288523A
- Authority
- JP
- Japan
- Prior art keywords
- elongation
- aluminum alloy
- proof stress
- alloy sheet
- tensile strength
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Landscapes
- Metal Rolling (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は高成形性アルミニウ
ム合金板およびその製造方法に係り、３方向の引張試験
で引張強さが９０N/mm2 以上、耐力が４５N/mm2 以上
で、全伸びが４０％以上で局部伸びが１０％以上を有す
るような高延性で局部伸びの優れた高成形性アルミニウ
ム合金板およびその製造方法を提供しようとするもので
ある。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a highly formable aluminum alloy sheet and a method for producing the same, and has a tensile strength of 90 N / mm 2 or more, a proof stress of 45 N / mm 2 or more, and a total elongation in a three-way tensile test. It is an object of the present invention to provide a highly ductile and highly formable aluminum alloy sheet excellent in local elongation and having a local elongation of at least 40% and a local elongation of 10% or more, and a method for producing the same.
【０００２】[0002]
【従来の技術】近年、自動車用アルミ合金板としてAl−
Mg合金が研究され且つ使用され、全伸びが３５％程度の
材料が得られているが、Mg量を増加しても局部伸びが増
加せず、また、加工硬化指数が高いため、成形途中で一
旦発生したシワが取りきれず、シワ重なりが発生したり
して特に非対称の深絞り成形品については鋼板に及ばな
いのが現状であり、従って、燃料タンクやタンクカバー
については一部で温間成形法でしか製造ができないのが
現状である。2. Description of the Prior Art In recent years, Al-
Mg alloys have been studied and used, and a material with a total elongation of about 35% has been obtained. However, even if the amount of Mg is increased, the local elongation does not increase, and the work hardening index is high. The wrinkles once generated cannot be removed, and wrinkle overlap occurs.In particular, the asymmetrical deep-drawing products do not reach the steel plate, and therefore some fuel tanks and tank covers are not warm. At present, it can only be manufactured by a molding method.
【０００３】なお純アルミ系で、引張強さや耐力を高く
しようとすることも一部に考えられ、また耐力が低いAl
−Fe系を採用することも一部に検討されているようであ
る。In some cases, it is considered that pure aluminum is used to increase the tensile strength and proof stress.
The adoption of -Fe system seems to be considered in some cases.
【０００４】[0004]
【発明が解決しようとする課題】アルミニウム合金板で
鋼板並みの成形性を得るには全伸びが４０％以上で、な
おかつ、局部伸び１０％以上で適度な強度が必要である
が一般に純度が高いと伸びが大きくなることが知られて
いて Al ９9.８％以上では伸びが４０％を超えるように
なるとしても引張強さや耐力がかなり低く、板材の取扱
い時の変形問題や成形品での加工硬化がAl−Mg系に比べ
て小さく、成形品が変形し易い等の問題がある。In order to obtain formability comparable to that of a steel sheet with an aluminum alloy sheet, it is necessary that the total elongation is 40% or more and the local elongation is 10% or more, and appropriate strength is obtained, but the purity is generally high. It is known that the elongation becomes large, and even if the elongation exceeds 40% at 99.8% or more of Al, the tensile strength and proof stress are considerably low, and there is a problem of deformation at the time of handling of a sheet material and processing of a molded product. There is a problem that the curing is smaller than that of the Al-Mg system and the molded product is easily deformed.
【０００５】なお、純アルミ系で引張強さや耐力を高く
しようとすると、一般に強度を確保し、伸びを犠牲にし
たＨ２４材が使用されるが伸びが低いため深絞りや張り
出し成形ができず、浅い絞り成形品に限定されてくるの
が実状である。また、耐力が低いAl−Fe系や純アルミ系
の板材では金型とのクリアランスが厳しい条件や複雑な
非対称の形状を成形する場合には板材が金型のコーナー
Ｒの小さい部分等の変曲部で塑性変形し易いため、材料
の流入が抑えられて局部的に板材の肉厚が減少し、絞り
切れが発生し易い欠点がある。[0005] In order to increase the tensile strength and proof stress of pure aluminum, H24 material is generally used to secure the strength and sacrifice the elongation. However, since the elongation is low, deep drawing and bulging cannot be performed. The reality is that it is limited to shallow drawn products. In addition, in the case of Al-Fe or pure aluminum-based sheet material having low proof stress, when the clearance with the mold is severe or when forming a complicated asymmetric shape, the sheet material may be inflected at a small corner R of the mold. Since plastic deformation is apt to occur in the portion, the inflow of the material is suppressed, the thickness of the plate material is locally reduced, and there is a disadvantage that the drawing is likely to be cut off.
【０００６】[0006]
【課題を解決するための手段】本発明者等は上記したよ
うな従来技術における課題を解消することについて検討
を重ねた結果、全伸びが４０％以上で、なおかつ局部伸
びが１０％以上を有し、また耐力を高めてより鋼板に近
いアルミニウム板材が必要であることを確認した。また
アルミ板の取り扱い時の変形や浅い絞り成形品の変形は
材料の耐力に起因するもので、材料の伸びを大きく損な
うことなく耐力を高められれば解決可能であることを見
出し、更に板材の伸びを高める方法としてAl−Fe系合金
でSi量を少なくコントロールすることにより、Ｏ材で全
伸び４０％以上局部伸び１０％以上を得ることを見出
し、更に材料の耐力を高める方法として、Ｏ材をスキン
パス圧延する方法やレベラーロールで繰り返し曲げ加工
する方法を検討したがスキンパス圧延法では耐力の向上
が大きい反面、伸びの低下が著しい。また、レベラーに
よる繰返し曲げは伸びの低下が比較的少ないものの、耐
力向上が５〜１０N/mm 2 と小さく、目的を満たさない。
本発明ではテンションレベラー等でＯ材コイルを１〜５
％引張り加工することにより、耐力を１５〜３０N/mm2
向上せしめ、伸びの減少を0.５〜４％に抑えて高耐力で
高延性の高成形性材を得ることに成功したものであっ
て、そのポイントは以下の如くである。Means for Solving the Problems The present inventors have described above.
To solve the problems in conventional technologies such as
As a result, the total elongation is 40% or more and the local elongation
10% or more, and with increased proof stress, closer to steel plate
It was confirmed that a new aluminum plate was necessary. Also
Deformation when handling aluminum plates and deformation of shallow drawn products
Due to the strength of the material, it greatly reduces the elongation of the material.
See if it can be solved if the proof stress can be increased without
Al-Fe alloy
By controlling the amount of Si low with
It is found that elongation of 40% or more and local elongation of 10% or more are obtained.
In addition, as a method to further increase the strength of the material,
Pass rolling method and repeated bending with leveler roll
To improve the yield strength by skin pass rolling method
However, the elongation is remarkably reduced. In addition, to leveler
Repeated bending causes a relatively small decrease in elongation,
Strength improvement is 5 to 10 N / mm TwoAnd small, does not meet the purpose.
In the present invention, the O material coil is set to 1 to 5 with a tension leveler or the like.
15-30N / mmTwo
With high yield strength by suppressing elongation reduction to 0.5-4%
It has succeeded in obtaining a high formability material with high ductility.
The points are as follows.
【０００７】（１） Fe：１.０〜2.０wt％およびTi：
0.００５〜0.１０wt％もしくはTi：0.００５〜0.１０wt
％およびＢ：0.０００５〜0.００２wt％を含有し、残部
がAlおよび不可避不純物からなり、該不純物中のSiを0.
１０wt％以下，Cuを0.０３wt％以下に規制したアルミニ
ウム合金板で、３方向の引張試験で引張強さが９０N/mm
2 以上、耐力４５N/mm2 以上で、全伸び４０％以上であ
り、かつ局部伸びが１０％以上を有することを特徴とし
た高成形性アルミニウム合金板。(1) Fe: 1.0 to 2.0 wt% and Ti:
0.005 to 0.10 wt% or Ti: 0.005 to 0.10 wt%
% And B: 0.0005 to 0.002 wt%, with the balance being Al and unavoidable impurities.
Aluminum alloy plate with less than 10 wt% and less than 0.03 wt% Cu, with tensile strength of 90N / mm in tensile test in three directions
2. A highly formable aluminum alloy sheet characterized by having a proof stress of 2 or more, a proof stress of 45 N / mm 2 or more, a total elongation of 40% or more, and a local elongation of 10% or more.
【０００８】（２） Fe：１.０〜2.０wt％および、更
にMg：0.０５〜0.３wt％またはMn：0.０５〜0.６wt％の
何れか１種または２種、Ti：0.００５〜0.１０wt％もし
くはTi：0.００５〜0.１０wt％およびＢ：0.０００５〜
0.００２wt％を含有し、残部がAlおよび不可避不純物か
らなり、該不純物中のSiを0.１０wt％以下，Cuを0.０３
wt％以下に規制したアルミニウム合金板で、３方向の引
張試験で引張強さが１００N/mm2 以上、耐力５５N/mm2
以上で、全伸び４０％以上であり、かつ局部伸びが１０
％以上を有することを特徴とした高成形性アルミニウム
合金板。(2) Fe: 1.0 to 2.0% by weight, and further Mg: 0.05 to 0.3% by weight or Mn: 0.05 to 0.6% by weight, Ti : 0.005 to 0.10 wt% or Ti: 0.005 to 0.10 wt% and B: 0.0005 to
0.002 wt%, the balance being Al and unavoidable impurities. Si in the impurities is 0.10 wt% or less and Cu is 0.03 wt%.
an aluminum alloy plate regulated below wt%, is 100 N / mm 2 or more tensile strength in the three directions of the tensile test, strength 55N / mm 2
As described above, the total elongation is 40% or more and the local elongation is 10%.
% Of a high formability aluminum alloy sheet characterized by having a content of at least 10%.
【０００９】（３） 上記（１）の鋳塊を４５０〜６２
０℃の温度で均熱処理し、通常の熱間圧延を施し、その
まま、冷間圧延を施した後、３００℃以上で中間焼鈍
し、またはそのまま、冷間圧延を６０％以上施した後、
３００℃以上の温度で最終焼鈍した後、テンションレベ
ラー等で１〜５％の永久伸びを付与して耐力を向上させ
て３方向での引張試験で引張強さが９０N/mm2 以上、耐
力４５N/mm2 以上で全伸び４０％以上であり、かつ、局
部伸びが１０％以上を有する高延性で局部伸びの優れた
高成形性アルミニウム合金板の製造方法。(3) 450-62
After soaking at a temperature of 0 ° C., performing normal hot rolling, performing cold rolling as it is, performing intermediate annealing at 300 ° C. or more, or performing cold rolling at 60% or more as it is,
After final annealing at a temperature of 300 ° C. or more, a permanent elongation of 1 to 5% is imparted by a tension leveler or the like to improve the proof stress, and the tensile strength is 90 N / mm 2 or more and the proof stress 45 N in a tensile test in three directions. A method for producing a highly formable aluminum alloy sheet having high ductility and excellent local elongation having a total elongation of at least 40% / mm 2 and a local elongation of at least 10%.
【００１０】（４） 上記した（２）の鋳塊を、上記
（３）の均熱処理、熱間圧延、冷間圧延、中間焼鈍また
はそのまま冷間圧延を６０％以上施した後、同様に最終
焼鈍し、テンションレベラー等による永久伸び付与によ
る耐力向上をなし、３方向での引張試験で引張強さが１
００N/mm2 以上、耐力５５N/mm2 以上で全伸び４０％以
上であり、かつ局部伸びが１０％を有せしめた高延性で
局部伸びの優れた高成形性アルミニウム合金板の製造方
法。(4) After subjecting the ingot of (2) to the soaking treatment, hot rolling, cold rolling, intermediate annealing or cold rolling as described in (3) above for 60% or more, the final Annealing and improvement of proof stress by giving permanent elongation by tension leveler, etc., and tensile strength of 1 in tensile test in 3 directions
00N / mm 2 or more, proof stress 55N / mm 2 or more in total elongation of 40% or more, and excellent process for producing a high formability aluminum alloy plate local elongation at high ductility local elongation was allowed Yes 10%.
【００１１】上記したような本発明における成分限定理
由は以下の如くである。 ・Fe：Feは強度および伸びを付与する重要な元素で１.
０％未満ではその効果が少なく、２％を超えると耐食性
を損なうので１.０〜2.０％とする。 ・Si：不純物としてのSiは鋳造時にFeやMnと化合して、
Al−Fe−Si系晶出物となり、局部伸びを阻害するので0.
１０％以下とする。 ・Cu：不純物としてのCuは強度を付与する元素であるが
Fe量が高い場合に耐食性を損なうので0.０３％以下とす
る。 ・MgおよびMn：強度付与元素である。特にMgは固溶して
強度を付与する元素であり、0.０５％未満ではその効果
が小さく、0.３％を超えると加工硬化度が大きくなって
局部伸びや全伸びが低下するので0.０５〜0.３％とす
る。Mnは化合物を微細に分散して強度を付与する元素で
あると共に焼鈍時に再結晶粒を微細化する効果があり、
0.０５％未満ではその効果が小さく、また0.６％を超え
ると局部伸びが減少するのでMn量は0.０５〜0.６％とす
る。 ・TiもしくはTiおよびＢ：鋳塊の鋳造組織を微細化し鋳
造割れを防止するために、Ti単独、またはTiとＢを複合
添加する。Ti単独の場合0.００５〜0.１０wt％、もしく
はTiとＢを複合添加する場合Ti：0.００５〜0.１０wt％
およびＢ：0.０００５〜0.００２wt％である。 ・他の不純物は、Znは0.３wt％以下、他の不純物は各々
0.１wt％以下とする。The reasons for limiting the components in the present invention as described above are as follows. Fe: Fe is an important element that gives strength and elongation 1.
If it is less than 0%, the effect is small, and if it exceeds 2%, the corrosion resistance is impaired, so the content is set to 1.0 to 2.0%.・ Si: Si as an impurity combines with Fe and Mn during casting,
It becomes an Al-Fe-Si crystallized substance and hinders local elongation.
10% or less.・ Cu: Cu as an impurity is an element that imparts strength.
If the Fe content is high, the corrosion resistance is impaired, so the content is made 0.03% or less. -Mg and Mn: Strength imparting elements. In particular, Mg is an element which gives strength by forming a solid solution, and if its content is less than 0.05%, its effect is small. 0.05 to 0.3%. Mn is an element that imparts strength by dispersing the compound finely and has the effect of refining recrystallized grains during annealing,
If it is less than 0.05%, the effect is small, and if it exceeds 0.6%, the local elongation decreases, so the Mn content is set to 0.05 to 0.6%. Ti or Ti and B: In order to refine the casting structure of the ingot and prevent casting cracks, Ti alone or a combination of Ti and B is added. 0.005 to 0.10 wt% when Ti alone or Ti and 0.005 to 0.10 wt% when combined with Ti and B
And B: 0.0005 to 0.002 wt%.・ As for other impurities, Zn is 0.3wt% or less, other impurities are each
0.1 wt% or less.
【００１２】また本発明における鋳造から引張矯正まで
の製造工程については以下の如くである。 （鋳造）鋳造法は特に限定されず、常法によって鋳塊を
作れば良く、ＤＣ鋳造法（半連続鋳造法）で連続鋳造法
でも良い。 （均熱処理）均熱処理は熱間圧延のための加熱処理で、
４５０℃未満ではAl−Fe化合物の均質化が不十分であ
り、一方６２０℃以上ではコストアップとなるので４５
０〜６２０℃とする。 （熱間圧延）常法によって３００℃以上の再結晶温度以
上で圧延を行う。 （冷間圧延）最終焼鈍前の冷延加工率は塑性加工異方性
を小さくするために重要で６０％未満では再結晶粒が粗
大となり、耐力の低下と成形加工時の肌荒れを生じ易く
なる。また冷延加工率が９０％を超えると塑性異方性が
大きくなり、圧延方向に対して４５°方向の伸びが大き
く、絞り加工時の耳率が大きくなるので６０〜９０％と
する。冷延率が９０％を超える場合は冷延途中で中間焼
鈍を施すことによってこの目標を達成できる。 （最終焼鈍）Ｏ材焼鈍するために行うものでバッチ焼鈍
では３００℃以上の温度で0.５〜３Hrで十分に再結晶さ
せる。なお、連続焼鈍では３５０℃以上の温度で１〜６
０秒の加熱を行って十分に再結晶させる。 （引張矯正）本発明の重要な工程でテンションレベラー
等で永久伸びを与えて耐力向上をはかるもので永久伸び
量が１％未満では耐力の向上が小さく、一方５％を超え
ると全伸びを低減するので１〜５％とする。ここでテン
ションレベラーとは、コイル状態で連続的に永久伸びを
生ずるように引張りながら、レベラーロールで繰り返し
曲げにより歪矯正をする設備をいう。The manufacturing steps from casting to straightening in the present invention are as follows. (Casting) The casting method is not particularly limited, and an ingot may be made by a conventional method, and a DC casting method (semi-continuous casting method) or a continuous casting method may be used. (Soaking heat treatment) Soaking heat treatment is a heat treatment for hot rolling.
If the temperature is lower than 450 ° C., the homogenization of the Al—Fe compound is insufficient, while if it is higher than 620 ° C., the cost is increased.
0 to 620 ° C. (Hot rolling) Rolling is performed at a recrystallization temperature of 300 ° C. or higher by a conventional method. (Cold rolling) The cold rolling work ratio before final annealing is important for reducing plastic working anisotropy. If it is less than 60%, recrystallized grains become coarse, and the yield strength tends to decrease and the surface becomes rough during forming. . If the cold-rolling rate exceeds 90%, the plastic anisotropy increases, the elongation in the 45 ° direction with respect to the rolling direction increases, and the ear ratio at the time of drawing increases. When the cold rolling ratio exceeds 90%, this target can be achieved by performing intermediate annealing during the cold rolling. (Final annealing) This is performed for annealing the O material. In batch annealing, recrystallization is sufficiently performed at a temperature of 300 ° C. or more at 0.5 to 3 hours. In the case of continuous annealing, 1 to 6 at a temperature of 350 ° C. or more.
Perform heating for 0 seconds to sufficiently recrystallize. (Tension straightening) In the important step of the present invention, a permanent elongation is given by a tension leveler or the like to improve the proof stress. When the elongation is less than 1%, the improvement of the proof stress is small, and when it exceeds 5%, the total elongation is reduced. Therefore, it is set to 1 to 5%. Here, the tension leveler refers to equipment that corrects distortion by repeatedly bending with a leveler roll while pulling the coil to continuously generate permanent elongation in a coil state.
【００１３】[0013]
【発明の実施の形態】本発明によるものの具体的な実施
態様について説明すると、先ず本発明者等が採用した発
明例合金およびその比較例合金は次の表１に示す如くで
ある。DESCRIPTION OF THE PREFERRED EMBODIMENTS The specific embodiments of the present invention will be described. First, the alloys of the invention and the comparative alloys adopted by the present inventors are as shown in Table 1 below.
【００１４】[0014]
【表１】 [Table 1]
【００１５】また上記したような各合金に対する製造条
件を要約して示すと、次の表２に示す如くである。The production conditions for each of the above alloys are summarized in Table 2 below.
【００１６】[0016]
【表２】 [Table 2]
【００１７】上記したような製造例および比較例につい
て説明すると、表２に示されたような製造 No.１〜６に
よるものは何れもその組成および製造プロセスの何れも
が本発明で規定する条件を満足した本発明例であり、こ
れらのものは表２に示すように引張強さ９０N/mm2 以
上、耐力４５N/mm2 、全伸び４０％以上を有し、局部伸
びも１０％以上で耐食性も良好である高耐力で高延性の
優れた高成形性材料である。ここで全伸びとは、板の引
張試験（ＪＩＳ５号試験片使用）において引張開始から
板破断時までの全伸び値を標点距離（初期長さ）で徐し
た値（％）をいう。局部伸びとは、板の引張試験（ＪＩ
Ｓ５号試験片使用）において最大荷重時から板破断時ま
での伸び値を標点距離（初期長さ）で徐した値（％）を
いう。引張強さは３方向の引張試験によるもので、３方
向とは圧延方向、圧延方向に直角な方向、圧延方向に対
して４５°方向を指し、一番低い値を示すものである。The production examples and comparative examples as described above will be described. In the case of Production Nos. 1 to 6 as shown in Table 2, all of the compositions and the production processes satisfy the conditions specified in the present invention. As shown in Table 2, these have an tensile strength of 90 N / mm 2 or more, a proof stress of 45 N / mm 2 , a total elongation of 40% or more, and a local elongation of 10% or more. It is a highly moldable material with good corrosion resistance and high yield strength and high ductility. Here, the total elongation refers to a value (%) obtained by reducing the total elongation value from the start of tension to the time of breaking of the plate by the gauge length (initial length) in a plate tensile test (using a JIS No. 5 test piece). Local elongation refers to the tensile test (JI
(Using S5 test piece) means a value (%) obtained by reducing the elongation value from the time of maximum load to the time of sheet breakage by the gauge length (initial length). Tensile strength is based on a tensile test in three directions. The three directions indicate a rolling direction, a direction perpendicular to the rolling direction, and a direction at 45 ° to the rolling direction, and show the lowest value.
【００１８】これに対し製造 No.７〜１１のものは何れ
も比較例であって、製造 No.７は組成が本発明で規定す
る範囲を満たすが製造プロセスで最終引張矯正量が規定
より小さく、耐力が低目で発明の強度範囲を満たさない
例である。また、製造 No.８，９，１０，１１は製造プ
ロセスが本発明で規定する範囲を満たすが組成範囲を満
たさない比較例で No.８はSi量が多めでAL−Fe−Si系化
合物の生成により、製品の伸びが低く、発明で規定する
範囲を満たしていない。さらに、 No.１０はCu量が多め
で製品の耐食性が劣り、使用上問題となる。また製造 N
o.９，１１はFe量が少なく、製品の伸びは満足している
が強度が不足しており、引張強さおよび耐力が共に発明
で規定する範囲を満たしていない。なお、 No.１２は組
成が範囲内であるが製造プロセスにおいて、引張矯正量
が大きすぎ、製品の伸びが低目となって発明で規定する
範囲を満たしていない。On the other hand, Production Nos. 7 to 11 are all comparative examples. In Production No. 7, the composition satisfies the range specified in the present invention, but the final tensile correction amount is smaller than specified in the manufacturing process. This is an example in which the proof stress is low and does not satisfy the strength range of the present invention. Production Nos. 8, 9, 10, and 11 are comparative examples in which the production process satisfies the range specified in the present invention but does not satisfy the composition range. Due to the formation, the product elongation is low and does not satisfy the range specified in the invention. In addition, No. 10 has a large amount of Cu and is inferior in corrosion resistance of the product, which causes a problem in use. Also manufacture N
In Nos. 9 and 11, the Fe content was small, the product elongation was satisfactory, but the strength was insufficient, and both the tensile strength and the proof stress did not satisfy the ranges specified in the invention. Although the composition of No. 12 was within the range, the amount of straightening in the production process was too large, and the elongation of the product was too low to satisfy the range specified in the invention.
【００１９】また自動車の燃料タンクの如く逆鞍型の複
雑形状の容器で、全体をとおして幅が６０〜８０cmで左
部分の寸法が深さ２０〜２５cm×長さ３０〜４０cm、中
央部分の寸法が深さ１０〜１５cm×長さ３０〜４０cm、
右部分の寸法が深さ１５〜２０cmの大型の容器を、上記
各製造 No.１〜１２と同じ条件で製造した板を用いてプ
レス加工したところ、製造 No.１〜６の条件のものは破
断することなく成形ができた。一方製造 No.７〜１２の
条件のものはプレス金型の肩部で破断が生じた。[0019] The inverted saddle-shaped container having a complicated shape, such as a fuel tank of an automobile, having a width of 60 to 80 cm, a left portion having a depth of 20 to 25 cm, a length of 30 to 40 cm, and a central portion. Dimensions are 10-15 cm deep x 30-40 cm long,
A large container with a depth of 15 to 20 cm in the right part was pressed using a plate manufactured under the same conditions as the above Nos. 1 to 12; Molding was possible without breaking. On the other hand, under the conditions of Production Nos. 7 to 12, breakage occurred at the shoulder of the press die.
【００２０】即ち、このような結果によるときは組成が
本発明の条件を満すと共に製造プロセスも本発明の要件
を満足することによって本発明の目的を的確に達成し得
るものであることが確認される。That is, according to the above results, it is confirmed that the object of the present invention can be accurately achieved by satisfying the requirements of the present invention and the composition satisfying the requirements of the present invention. Is done.
【００２１】[0021]
【発明の効果】上記したような本発明によれば引張強さ
９０N/mm2 以上、耐力４５N/mm2 以上、全伸び４０％以
上で局部伸び１０％以上と特に耐力と伸びが優れたアル
ミニウム合金板を得ることができる。このような本発明
によるアルミニウム合金板を非対称の深絞り成形部品や
難形状成形部品に使用することにより、鋼板でしか出来
なかった成形部材をアルミ化でき、軽量化、リサイクル
性に大きく寄与することが可能となるものであって、工
業的にその効果の大きい発明である。[Effect of the Invention] Tensile strength According to the present invention as described above 90 N / mm 2 or more, proof stress 45N / mm 2 or more, particularly yield strength and elongation and local elongation of 10% or more in total elongation of 40% or more excellent aluminum An alloy plate can be obtained. By using such an aluminum alloy sheet according to the present invention for asymmetric deep-drawing molded parts or difficult-to-form molded parts, it is possible to turn a molded member that could only be made of steel sheet into aluminum, to greatly contribute to weight reduction and recyclability. This is an invention which is industrially effective.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ テーマコート゛(参考） Ｃ２２Ｆ 1/00 ６８２ Ｃ２２Ｆ 1/00 ６８２ ６８３ ６８３ ６８５ ６８５Ｚ ６８６ ６８６Ａ ６９１ ６９１Ｂ ６９４ ６９４Ａ (72)発明者 水嶋 一光 愛知県稲沢市小池１丁目11番１号 日本軽 金属株式会社名古屋工場内 (72)発明者 田島 靖史 愛知県稲沢市小池１丁目11番１号 日本軽 金属株式会社名古屋工場内 (72)発明者 玉置 雄一 愛知県稲沢市小池１丁目11番１号 日本軽 金属株式会社名古屋工場内──────────────────────────────────────────────────続 き Continuation of the front page (51) Int.Cl. 7 Identification symbol FI Theme coat ゛ (Reference) Hikari 1-11-1 Koike, Inazawa City, Aichi Prefecture Nippon Light Metal Co., Ltd. Nagoya Plant (72) Inventor Yasushi Tajima 1-11-1 Koike Inazawa City, Aichi Prefecture Nippon Light Metal Co., Ltd. Nagoya Plant (72) Invention Person Yuichi Tamaki 1-11-1 Koike, Inazawa City, Aichi Prefecture Nippon Light Metal Co., Ltd. Nagoya Plant
Claims (4)
５〜0.１０wt％もしくはTi：0.００５〜0.１０wt％およ
びＢ：0.０００５〜0.００２wt％を含有し、残部がAlお
よび不可避不純物からなり、該不純物中のSiを0.１０wt
％以下，Cuを0.０３wt％以下に規制したアルミニウム合
金板で、３方向の引張試験で引張強さが９０N/mm2 以
上、耐力４５N/mm2 以上で、全伸び４０％以上であり、
かつ局部伸びが１０％以上を有することを特徴とした高
成形性アルミニウム合金板。1. Fe: 1.0 to 2.0 wt% and Ti: 0.00
5 to 0.10 wt% or Ti: 0.005 to 0.10 wt% and B: 0.0005 to 0.002 wt%, with the balance being Al and unavoidable impurities.
%, Cu is controlled to 0.03 wt% or less. The aluminum alloy plate has a tensile strength of 90 N / mm 2 or more, a proof stress of 45 N / mm 2 or more, and a total elongation of 40% or more in a three-way tensile test.
A highly formable aluminum alloy sheet having a local elongation of 10% or more.
0.０５〜0.３wt％またはMn：0.０５〜0.６ｗt％の何れ
か１種または２種、Ti：0.００５〜0.１０wt％もしくは
Ti：0.００５〜0.１０wt％およびＢ：0.０００５〜0.０
０２wt％を含有し、残部がAlおよび不可避不純物からな
り、該不純物中のSiを0.１０wt％以下，Cuを0.０３wt％
以下に規制したアルミニウム合金板で、３方向の引張試
験で引張強さが１００ N/mm2 以上、耐力５５N/mm2 以
上で、全伸び４０％以上であり、かつ局部伸びが１０％
以上を有することを特徴とした高成形性アルミニウム合
金板。2. Fe: 1.0 to 2.0 wt% and further Mg:
0.05 to 0.3 wt% or one or two of Mn: 0.05 to 0.6 wt%, Ti: 0.005 to 0.10 wt% or
Ti: 0.005 to 0.10 wt% and B: 0.0005 to 0.0
And 0.2% by weight of Si and 0.03% by weight of Cu in the impurities.
An aluminum alloy plate regulated below, is 100 N / mm 2 or more tensile strength in the three directions of the tensile test, in yield strength 55N / mm 2 or more, the total elongation is 40% or more, and local elongation is 10%
A highly formable aluminum alloy sheet characterized by having the above.
５〜0.１０wt％もしくはTi：0.００５〜0.１０wt％およ
びＢ：0.０００５〜0.００２wt％を含有し、残部がAlお
よび不可避不純物からなり、該不純物中のSiを0.１０wt
％以下，Cuを0.０３wt％以下に規制したアルミニウム合
金鋳塊を４５０〜６２０℃で均熱処理し、通常の熱間圧
延を施し、冷間圧延を施した後、３００℃以上で中間焼
鈍し、またはそのまま冷間圧延を６０％以上施した後、
３００℃以上の温度で最終焼鈍した後、テンションレベ
ラー等で１〜５％の永久伸びを付与して耐力を向上さ
せ、３方向の引張試験で引張強さが９０ N/mm2 以上、
耐力４５N/mm2 以上で、全伸び４０％以上であり、かつ
局部伸び１０％以上を有せしめたことを特徴とする高成
形性アルミニウム合金板の製造方法。3. Fe: 1.0 to 2.0 wt% and Ti: 0.00
5 to 0.10 wt% or Ti: 0.005 to 0.10 wt% and B: 0.0005 to 0.002 wt%, with the balance being Al and unavoidable impurities.
% Or less, and Cu is controlled to 0.03 wt% or less. The aluminum alloy ingot is soaked at 450 to 620 ° C, subjected to ordinary hot rolling, cold rolled, and then annealed at 300 ° C or more. Or after cold rolling as it is,
After the final annealing at a temperature of 300 ° C. or more, a permanent elongation of 1 to 5% is imparted by a tension leveler or the like to improve the proof stress, and the tensile strength in a three-way tensile test is 90 N / mm 2 or more.
A method for producing a highly formable aluminum alloy sheet, wherein a proof stress is 45 N / mm 2 or more, a total elongation is 40% or more, and a local elongation is 10% or more.
0.０５〜0.３wt％またはMn：0.０５〜0.６wt％の何れか
１種または２種、Ti：0.００５〜0.１０wt％もしくはT
i：0.００５〜0.１０wt％およびＢ：0.０００５〜0.０
０２wt％を含有し、残部がAlおよび不可避不純物からな
り、該不純物中のSiを0.１０wt％以下，Cuを0.０３wt％
以下に規制したアルミニウム合金鋳塊を４５０〜６２０
℃の温度で均熱処理し、通常の熱間圧延を施し、そのま
ま、冷間圧延を施した後、３００℃以上で中間焼鈍し、
またはそのまま、冷間圧延を６０％以上施した後、３０
０℃以上の温度で最終焼鈍し、テンションレベラーで１
〜５％の永久伸びを付与して耐力を向上させて３方向で
の引張試験で引張強さが１００N/mm2 以上、耐力５５N/
mm2 以上で全伸び４０％以上であり、かつ、局部伸びが
１０％以上を有せしめたことを特徴とする高延性で局部
伸びの優れた高成形性アルミニウム合金板の製造方法。4. Fe: 1.0-2.0 wt% and further Mg:
0.05 to 0.3 wt% or Mn: 0.05 to 0.6 wt%, one or two of them, Ti: 0.005 to 0.10 wt% or T
i: 0.005 to 0.10 wt% and B: 0.0005 to 0.0
And 0.2% by weight of Si and 0.03% by weight of Cu in the impurities.
Aluminum alloy ingot regulated below 450-620
Soak at a temperature of ℃, subjected to normal hot rolling, as it is, subjected to cold rolling, and then intermediate annealing at 300 ℃ or more,
Or, as it is, after cold rolling is performed for 60% or more, 30
Final annealing at a temperature of 0 ° C or higher, and 1
A tensile strength of 100 N / mm 2 or more in a tensile test in three directions and a proof stress of 55 N /
A method for producing a highly formable aluminum alloy sheet having high ductility and excellent local elongation, wherein the total elongation is 40% or more and the local elongation is 10% or more when mm 2 or more.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2001003248A JP3791337B2 (en) | 2000-02-01 | 2001-01-11 | Highly formable aluminum alloy plate and method for producing the same |
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2000-23739 | 2000-02-01 | ||
| JP2000023739 | 2000-02-01 | ||
| JP2001003248A JP3791337B2 (en) | 2000-02-01 | 2001-01-11 | Highly formable aluminum alloy plate and method for producing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2001288523A true JP2001288523A (en) | 2001-10-19 |
| JP3791337B2 JP3791337B2 (en) | 2006-06-28 |
Family
ID=26584620
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2001003248A Expired - Lifetime JP3791337B2 (en) | 2000-02-01 | 2001-01-11 | Highly formable aluminum alloy plate and method for producing the same |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3791337B2 (en) |
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2009215605A (en) * | 2008-03-10 | 2009-09-24 | Sumitomo Light Metal Ind Ltd | Aluminum alloy plate excellent in square-shell deep-drawability and production method thereof |
| JP2010013669A (en) * | 2008-07-01 | 2010-01-21 | Sumitomo Light Metal Ind Ltd | Aluminum alloy sheet having excellent corrosion resistance and formability |
| JP2014047367A (en) * | 2012-08-29 | 2014-03-17 | Kobe Steel Ltd | Aluminum hard foil for battery collector |
| JP2014065956A (en) * | 2012-09-27 | 2014-04-17 | Kobe Steel Ltd | Aluminum alloy foil for lithium battery outer packaging and its manufacturing method |
| JP2018178138A (en) * | 2017-04-03 | 2018-11-15 | 日本軽金属株式会社 | High strength aluminum alloy sheet excellent in moldability, flexure processability and dent resistance, and manufacturing method therefor |
| CN110709525A (en) * | 2017-12-05 | 2020-01-17 | 日本轻金属株式会社 | Aluminum alloy plate for battery cover for forming integrated explosion-proof valve and manufacturing method thereof |
| EP3842560A4 (en) * | 2018-08-23 | 2022-05-18 | Nippon Light Metal Company, Ltd. | Aluminum alloy sheet for battery lid for molding integrated explosion-proof valve and production method therefor |
| EP3842557A4 (en) * | 2018-08-23 | 2022-06-01 | Nippon Light Metal Company, Ltd. | Aluminum alloy sheet for battery lid for molding integrated explosion-proof valve and production method therefor |
| EP3842558A4 (en) * | 2018-08-23 | 2022-06-01 | Nippon Light Metal Co., Ltd. | Aluminum alloy sheet for battery lid for molding integrated explosion-proof valve and production method therefor |
-
2001
- 2001-01-11 JP JP2001003248A patent/JP3791337B2/en not_active Expired - Lifetime
Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2009215605A (en) * | 2008-03-10 | 2009-09-24 | Sumitomo Light Metal Ind Ltd | Aluminum alloy plate excellent in square-shell deep-drawability and production method thereof |
| JP2010013669A (en) * | 2008-07-01 | 2010-01-21 | Sumitomo Light Metal Ind Ltd | Aluminum alloy sheet having excellent corrosion resistance and formability |
| JP2014047367A (en) * | 2012-08-29 | 2014-03-17 | Kobe Steel Ltd | Aluminum hard foil for battery collector |
| JP2014065956A (en) * | 2012-09-27 | 2014-04-17 | Kobe Steel Ltd | Aluminum alloy foil for lithium battery outer packaging and its manufacturing method |
| JP2018178138A (en) * | 2017-04-03 | 2018-11-15 | 日本軽金属株式会社 | High strength aluminum alloy sheet excellent in moldability, flexure processability and dent resistance, and manufacturing method therefor |
| CN110709525A (en) * | 2017-12-05 | 2020-01-17 | 日本轻金属株式会社 | Aluminum alloy plate for battery cover for forming integrated explosion-proof valve and manufacturing method thereof |
| CN113174514A (en) * | 2017-12-05 | 2021-07-27 | 日本轻金属株式会社 | Aluminum alloy plate for battery cover for forming integrated explosion-proof valve and manufacturing method thereof |
| CN110709525B (en) * | 2017-12-05 | 2022-02-01 | 日本轻金属株式会社 | Aluminum alloy plate for battery cover for forming integrated circular explosion-proof valve and manufacturing method thereof |
| CN113174514B (en) * | 2017-12-05 | 2022-02-18 | 日本轻金属株式会社 | Aluminum alloy plate for battery cover for forming integrated explosion-proof valve and manufacturing method thereof |
| EP3842560A4 (en) * | 2018-08-23 | 2022-05-18 | Nippon Light Metal Company, Ltd. | Aluminum alloy sheet for battery lid for molding integrated explosion-proof valve and production method therefor |
| EP3842557A4 (en) * | 2018-08-23 | 2022-06-01 | Nippon Light Metal Company, Ltd. | Aluminum alloy sheet for battery lid for molding integrated explosion-proof valve and production method therefor |
| EP3842558A4 (en) * | 2018-08-23 | 2022-06-01 | Nippon Light Metal Co., Ltd. | Aluminum alloy sheet for battery lid for molding integrated explosion-proof valve and production method therefor |
Also Published As
| Publication number | Publication date |
|---|---|
| JP3791337B2 (en) | 2006-06-28 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US20070217943A1 (en) | Al-Mg Alloy Sheet with Excellent Formability at High Temperatures and High Speeds and Method of Production of Same | |
| WO1995022634A1 (en) | Method of manufacturing aluminum alloy plate for molding | |
| JP2008542526A (en) | Aluminum alloy plate and manufacturing method thereof | |
| WO2018011245A1 (en) | Method of making 6xxx aluminium sheets | |
| EP3740599A1 (en) | Method of making 6xxx aluminium sheets with high surface quality | |
| WO2020120267A1 (en) | Method of making 6xxx aluminium sheets with high surface quality | |
| TW201807210A (en) | Al-mg-Si-based alloy material, Al-Mg-Si-based alloy plate, and method for manufacturing Al-Mg-Si-based alloy plate | |
| WO2009098732A1 (en) | Aluminum alloy sheet for motor vehicle and process for producing the same | |
| JPH0747807B2 (en) | Method for producing rolled aluminum alloy plate for forming | |
| WO2018206696A1 (en) | Method of manufacturing an al-si-mg alloy rolled sheet product with excellent formability | |
| JP3791337B2 (en) | Highly formable aluminum alloy plate and method for producing the same | |
| JP2844411B2 (en) | Aluminum alloy sheet for superplastic forming capable of cold preforming and method for producing the same | |
| JPH10152762A (en) | Production of hard aluminum alloy sheet excellent in di workability | |
| JP5220310B2 (en) | Aluminum alloy plate for automobile and manufacturing method thereof | |
| JP2921820B2 (en) | Aluminum alloy sheet for superplastic forming capable of cold preforming and method for producing the same | |
| CN113474479A (en) | Method for producing a plate or strip from an aluminium alloy and plate, strip or shaped part produced thereby | |
| JPH08325664A (en) | High-strength heat treatment type aluminum alloy sheet for drawing and its production | |
| JP4237326B2 (en) | Method for producing aluminum alloy sheet excellent in formability and corrosion resistance | |
| JP2000160272A (en) | Al ALLOY SHEET EXCELLENT IN PRESS FORMABILITY | |
| JP3278130B2 (en) | Method for producing high-strength heat-treated aluminum alloy sheet for drawing | |
| TW201738390A (en) | Method for producing al-mg-Si alloy plate | |
| EP1141433A2 (en) | High strength aluminium alloy sheet and process | |
| JPH10219412A (en) | Manufacture of rolled aluminum alloy sheet excellent in external appearance characteristic after forming | |
| JP3587993B2 (en) | Manufacturing method of aluminum alloy sheet for deep drawing | |
| JP3180812B2 (en) | Method for producing Al-Fe alloy foil |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20040729 |
|
| A977 | Report on retrieval |
Free format text: JAPANESE INTERMEDIATE CODE: A971007 Effective date: 20050908 |
|
| RD02 | Notification of acceptance of power of attorney |
Free format text: JAPANESE INTERMEDIATE CODE: A7422 Effective date: 20051012 |
|
| RD04 | Notification of resignation of power of attorney |
Free format text: JAPANESE INTERMEDIATE CODE: A7424 Effective date: 20051014 |
|
| A521 | Written amendment |
Free format text: JAPANESE INTERMEDIATE CODE: A821 Effective date: 20051012 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20051213 |
|
| A521 | Written amendment |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20060131 |
|
| TRDD | Decision of grant or rejection written | ||
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 20060314 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20060327 |
|
| R150 | Certificate of patent or registration of utility model |
Free format text: JAPANESE INTERMEDIATE CODE: R150 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20100414 Year of fee payment: 4 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20110414 Year of fee payment: 5 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20120414 Year of fee payment: 6 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20120414 Year of fee payment: 6 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20130414 Year of fee payment: 7 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20130414 Year of fee payment: 7 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20140414 Year of fee payment: 8 |