JPH01259147A - Manufacture of al-cu-li-zr super plastic plate - Google Patents
Manufacture of al-cu-li-zr super plastic plateInfo
- Publication number
- JPH01259147A JPH01259147A JP8740188A JP8740188A JPH01259147A JP H01259147 A JPH01259147 A JP H01259147A JP 8740188 A JP8740188 A JP 8740188A JP 8740188 A JP8740188 A JP 8740188A JP H01259147 A JPH01259147 A JP H01259147A
- Authority
- JP
- Japan
- Prior art keywords
- rolling
- temperature
- hours
- superplastic
- treatment
- 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
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 22
- 238000005096 rolling process Methods 0.000 claims abstract description 27
- 229910000838 Al alloy Inorganic materials 0.000 claims abstract description 19
- 238000005097 cold rolling Methods 0.000 claims abstract description 14
- 238000000034 method Methods 0.000 claims description 22
- 238000005266 casting Methods 0.000 claims description 20
- 238000000137 annealing Methods 0.000 claims description 13
- 238000000265 homogenisation Methods 0.000 claims description 12
- 229910052782 aluminium Inorganic materials 0.000 claims description 9
- 239000012535 impurity Substances 0.000 claims description 9
- 238000001556 precipitation Methods 0.000 claims description 9
- 229910017539 Cu-Li Inorganic materials 0.000 claims description 3
- 238000001816 cooling Methods 0.000 claims description 3
- 238000002844 melting Methods 0.000 claims description 3
- 230000008018 melting Effects 0.000 claims description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims 4
- 238000010438 heat treatment Methods 0.000 abstract description 14
- 239000000463 material Substances 0.000 abstract description 12
- 229910052802 copper Inorganic materials 0.000 abstract description 2
- 230000000717 retained effect Effects 0.000 abstract 2
- 238000000151 deposition Methods 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 15
- 239000000956 alloy Substances 0.000 description 11
- 229910045601 alloy Inorganic materials 0.000 description 9
- 238000001953 recrystallisation Methods 0.000 description 6
- 229910001148 Al-Li alloy Inorganic materials 0.000 description 5
- 229910001093 Zr alloy Inorganic materials 0.000 description 4
- 238000012545 processing Methods 0.000 description 4
- 238000005482 strain hardening Methods 0.000 description 4
- 229910000905 alloy phase Inorganic materials 0.000 description 3
- 150000001875 compounds Chemical class 0.000 description 3
- 238000005098 hot rolling Methods 0.000 description 3
- 238000000465 moulding Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 230000002829 reductive effect Effects 0.000 description 2
- 229910017818 Cu—Mg Inorganic materials 0.000 description 1
- 229910019086 Mg-Cu Inorganic materials 0.000 description 1
- 239000012300 argon atmosphere Substances 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 238000005304 joining Methods 0.000 description 1
- 230000000670 limiting effect Effects 0.000 description 1
- 239000001989 lithium alloy Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 230000003068 static effect Effects 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
Landscapes
- Metal Rolling (AREA)
Abstract
Description
【発明の詳細な説明】
［産業上の利用分野］
本発明は超塑性変形が■ｆ能であるＡｌ−Ｌｉ系合金板
を製造する方法に関し、さらに詳しくは高温で変形速度
か極めて高いひずみ速度範囲て、超塑性変形か可能なＡ
ｌ−Ｃｕ−Ｌｉ−Ｚｒ系超塑性アルミニウム合金板を、
圧延で製造する方法に関するものである。[Detailed Description of the Invention] [Industrial Application Field] The present invention relates to a method for producing an Al-Li alloy plate capable of superplastic deformation, and more specifically, to a method for producing an Al-Li alloy plate capable of superplastic deformation. A range where superplastic deformation is possible
l-Cu-Li-Zr based superplastic aluminum alloy plate,
This relates to a method of manufacturing by rolling.
［従来の技術］
航空機用アルミニウム合金板は、機体の軽量化のために
、Ａｌ−Ｃｕ−Ｍｇ系の２０２４合金板やＡ Ｉ −Ｚ
−ｎ −Ｍ ｇ −Ｃｕ系の７０７５合金板から密度の
低いＡｌ−Ｌｉ系合金板に移行しつつある。[Prior Art] Aluminum alloy plates for aircraft are made of Al-Cu-Mg based 2024 alloy plates or AI-Z alloy plates in order to reduce the weight of aircraft bodies.
-n-Mg-Cu-based 7075 alloy plates are being replaced by low-density Al-Li-based alloy plates.
また、成形加工技術の面も、従来のロールフォーミンク
やプレス成形（板金加工）したものを組立て接合なとを
行う方法から一体化加工か可能な超塑性成形か取り入れ
られている。In addition, in terms of forming technology, superplastic forming, which allows for integrated processing, has been adopted from the conventional methods of assembling and joining products that have been roll-formed or press-formed (sheet metal processing).
超塑性成形法は、複雑な形状の製品を一度で成形するこ
とかできるため、部品の接合部か少なく、軽量化か可能
となり、また、組立て工数も少なく、製造コストの低減
をもたらす方法である。The superplastic molding method allows products with complex shapes to be molded in one go, making it possible to reduce the number of joints between parts and reduce weight.It also reduces the number of assembly steps and reduces manufacturing costs. .
このため超塑性変形かｒｉＪ能なＡｌ−Ｌｉ系合金材料
か要求されている。For this reason, an Al-Li alloy material that is capable of superplastic deformation is required.
従来、Ａｌ−Ｌｉ系合金としては、Ａｌ−Ｌｉ−Ｃｕ−
Ｍｇ−Ｚｒ系の８０９０合金とＡｌ−Ｃｕ−Ｌｉ−Ｚｒ
系の２０９０合金が、国際的に登録されている。このう
ちＡｌ−Ｌｉ−Ｃｕ−Ｍ ｇ −Ｚ ｒ系合金の超塑性
変形を得るために、均質化処理温度、熱間加工温度、中
間焼鈍温度および冷間加工度を規制する方法か提案され
ている。（特開昭６２−１７０４６２）
しかし、Ａ Ｉ−Ｃｕ−Ｌ ｉ−Ｚ ｒ系合金の超塑性
変形か得られる材料かなく、このようなな材料の開発が
強く要望されていた。Conventionally, Al-Li-Cu-
Mg-Zr based 8090 alloy and Al-Cu-Li-Zr
The 2090 alloy of the series is internationally registered. Among these, methods have been proposed to regulate the homogenization temperature, hot working temperature, intermediate annealing temperature, and degree of cold working in order to obtain superplastic deformation of Al-Li-Cu-Mg-Zr alloys. There is. (JP 62-170462) However, there is no material that can obtain superplastic deformation of AI-Cu-Li-Zr alloys, and there has been a strong demand for the development of such materials.
［発明が解決しようとする課題］
本発明は、変形速度か極めて筒い範囲で、超塑性変形が
得られるＡ Ｉ−Ｃｕ−Ｌ ｉ−Ｚ ｒ系合金材料を比
較的低温の熱間圧延で製造する方法を提供するものであ
る。[Problems to be Solved by the Invention] The present invention is directed to hot rolling an A I-Cu-L i-Zr alloy material that can obtain superplastic deformation at an extremely low deformation rate at a relatively low temperature. The present invention provides a method for manufacturing.
［課題を解決するための手段］
本発明による超塑性アルミニウム合金板の製造方法は、
前記目的を達成するため、下記のとおりに構成される。[Means for Solving the Problems] The method for manufacturing a superplastic aluminum alloy plate according to the present invention includes:
In order to achieve the above purpose, it is configured as follows.
（１） Ｃｕ ２．０−３．０ ％、 Ｌｉ１．
０−３．０ ％、Ｚ ｒ ０．０５〜０．２０％、Ｔ
ｉ ０．０１〜０．１０％を含有し、残部Ａｌおよび
不可避不純物からなるアルミニウム合金を、通常の鋳造
法で溶解、鋳造後、４５０〜５４０℃の温度において１
〜５０時間の均質化処理を行い、その後３００〜４５０
℃の温度で圧延し、５０％以上の冷間圧延を行うことを
特徴とするＡｌ−Ｃｕ−Ｌｉ−Ｚｒ系超塑性板の製造方
法。(1) Cu 2.0-3.0%, Li1.
0-3.0%, Z r 0.05-0.20%, T
An aluminum alloy containing 0.01 to 0.10% of i and the remainder consisting of Al and unavoidable impurities is melted and cast using a normal casting method, and then heated to 1% at a temperature of 450 to 540°C.
~50 hours of homogenization, then 300~450
A method for producing an Al-Cu-Li-Zr based superplastic plate, which comprises rolling at a temperature of 50% or more of cold rolling.
（２） Ｃｕ ２．０−３．０％、Ｌｉ １．０−
３．０％、Ｚ ｒ ０．０５〜０．２０％、Ｔ ｉ ０
．０１〜０．１０％を含有し、残部Ａｌおよび不可避不
純物からなるアルミニウム合金を、通常の鋳造法で溶解
し、鋳造後、４５０〜５４０℃の温度において１〜５０
時間の均質化処理を行い、その後３００〜４５０℃で１
〜５０時間の析出処理後、３００〜４５０℃の温度で圧
延し、５０％以上の冷間圧延を行うことを特徴とするＡ
ｌ−Ｃｕ−Ｌｉ−Ｚｒ系超塑性板の製造方法。(2) Cu 2.0-3.0%, Li 1.0-
3.0%, Z r 0.05-0.20%, T i 0
．． An aluminum alloy containing 0.01 to 0.10% and the balance consisting of Al and unavoidable impurities is melted by a normal casting method, and after casting, it is heated to 1 to 50% at a temperature of 450 to 540°C.
Homogenization treatment for 1 hour followed by 1 hour at 300-450℃
A characterized by rolling at a temperature of 300 to 450°C after precipitation treatment for ~50 hours to achieve cold rolling of 50% or more.
A method for manufacturing a l-Cu-Li-Zr based superplastic plate.
（３） Ｃｕ ２．０−３．０％、Ｌ’ｉ Ｌ、０
〜３．０％、Ｚ ｒ ０．０５〜０．２［］％、Ｔ ｉ
（１，１１１〜０．０１％を含有し、残部Ａｌおよび
不可避不純物からなるアルミニウム合金を、通常の鋳造
法で溶解し、鋳造後、４５０〜５４０℃の温度において
１〜５０時間の均質化処理を行った後、４８０ ℃以上
の温度で溶体化処理後、３００〜４５０℃の温度範囲ま
で冷却し、圧延を開始し、該圧延の途中で圧延を中断し
、１〜５０時間保持し析出処理した後、さらに３００〜
４５０℃の温度で圧延を継続した後、５０％以上の冷間
圧延を行うことを特徴とするＡｌ−Ｃｕ−Ｌｉ−Ｚｒ系
超塑性板の製造方法。(3) Cu 2.0-3.0%, L'i L, 0
~3.0%, Zr 0.05~0.2[]%, T i
(An aluminum alloy containing 1,111% to 0.01% and the remainder consisting of Al and unavoidable impurities is melted by a normal casting method, and after casting, it is homogenized at a temperature of 450 to 540°C for 1 to 50 hours. After performing solution treatment at a temperature of 480 °C or higher, cooling to a temperature range of 300 to 450 °C, rolling was started, rolling was interrupted in the middle of the rolling, and the rolling was held for 1 to 50 hours to undergo precipitation treatment. After that, another 300~
A method for producing an Al-Cu-Li-Zr based superplastic plate, which comprises continuing rolling at a temperature of 450°C and then cold rolling by 50% or more.
（４） Ｃｕ ２．０〜３．０％、Ｌｉ １．０−
３．０％、Ｚ ｒ ０．０５〜０．２０％、Ｔ ｉ ０
．０１〜０．１０％を含有し、残部Ａｌおよび不１−１
１避不純物からなるアルミニウム合金を、通常の鋳造法
で溶解し、鋳造後、４５０〜５４０℃で１〜５０時間保
持後３００〜４５０℃の温度まで冷却し、該温度範囲で
１〜５０時間の析出処理後、３００〜４５０℃の温度で
圧延し、ついで５０％以上の冷間圧延を行うことを特徴
とするＡｌ−Ｃｕ−Ｌｉ−
Ｚｒ系超塑性板の製造方法。(4) Cu 2.0-3.0%, Li 1.0-
3.0%, Z r 0.05-0.20%, T i 0
．． 01 to 0.10%, with the remainder being Al and Al.
1. An aluminum alloy consisting of avoided impurities is melted using a normal casting method, and after casting, it is held at 450 to 540°C for 1 to 50 hours, then cooled to a temperature of 300 to 450°C, and then heated in the temperature range for 1 to 50 hours. A method for producing an Al-Cu-Li-Zr based superplastic plate, which comprises rolling at a temperature of 300 to 450°C after precipitation treatment, and then cold rolling to a rate of 50% or more.
さらに上記方法の冷間圧延の前または途中に３００〜４
５０℃で１〜５０時間の中間焼鈍を行う方法あるいはさ
らに冷間圧延後に４５０℃以上で１分〜１時間最終焼鈍
する方法を含む。Furthermore, before or during the cold rolling of the above method, 30 to 4
This includes a method of performing intermediate annealing at 50° C. for 1 to 50 hours, or a method of final annealing at 450° C. or higher for 1 minute to 1 hour after cold rolling.
［作 用］
Ａｌ−Ｌｉ系超塑性制料は、従来の７４７５合金系超塑
性利料と材料り、動的再結晶により微細再結晶粒を形成
させ超塑性変形する性質をもつために、高温まで安定な
下部組織を有する材料か得られるのである。[Function] Al-Li-based superplastic material is different from the conventional 7475 alloy-based superplastic material, and has the property of forming fine recrystallized grains through dynamic recrystallization and superplastic deformation, so it can be used at high temperatures. A material with a stable substructure can be obtained.
本発明はＡ Ｉ−Ｃｕ−Ｌ ｉ−Ｚ ｒ系の熱間加工性
を向上させて圧延し、超塑性材料を得るための製造方法
に関するものであり、以下成分を限定した理由についで
述べる。The present invention relates to a manufacturing method for improving the hot workability of AI-Cu-Li-Zr-based material and rolling it to obtain a superplastic material, and the reasons for limiting the components will be described below.
Ｃｕ、超塑性成形後の合金相の強度向上効果かある。こ
の効果は２０％より少ないと得られず、３．０％より多
いと、Ｃｕの効果の密度か高いために航空機などの軽量
化に寄与することができない。これらのためＣｕを２．
０〜３．０％とした。Cu has the effect of improving the strength of the alloy phase after superplastic forming. This effect cannot be obtained if it is less than 20%, and if it is more than 3.0%, the density of the effect of Cu is too high and it cannot contribute to weight reduction of aircraft etc. For these reasons, 2.
The content was set at 0 to 3.0%.
Ｌに同じく合金相の強度向上と軽量化に効果かある。こ
の効果は１．０％より少ないと得られず、３．０％より
多いと鋳造時にその偏析か激しく、均質化熱処理によっ
ても容易に固溶しないため、熱間加工が困難である。Like L, it is effective in improving the strength and weight of the alloy phase. This effect cannot be obtained if the amount is less than 1.0%, and if it is more than 3.0%, it segregates violently during casting and does not dissolve easily even in homogenization heat treatment, making hot working difficult.
Ｚｒ；合金相の再結晶を抑制する効果がある。Zr: has the effect of suppressing recrystallization of the alloy phase.
０．０５％より少ないと最終焼鈍て再結晶が容易となり
、下部組織を安定化させることが困難となる。このため
超塑性成形か得られにくい。また、０．２０％を越える
と通常の鋳造法では巨大化合物を晶出しやすくなり、こ
れにより素材に圧延欠陥か生ずる。If it is less than 0.05%, recrystallization during final annealing becomes easy, making it difficult to stabilize the underlying structure. For this reason, it is difficult to obtain superplastic molding. Moreover, if it exceeds 0.20%, giant compounds tend to crystallize in normal casting methods, which causes rolling defects in the material.
Ｔｌ；素材合金に鋳造組織の微細化を与える効果がある
。この効果は０．０１％より少ないと得られず、０．１
０％より多いと巨大化合物か晶出しやすくなる。Tl: has the effect of giving the material alloy a finer casting structure. This effect cannot be obtained when the amount is less than 0.01%, and 0.1%
When the amount is more than 0%, giant compounds tend to crystallize.
次に製造条件についで述べる。Next, the manufacturing conditions will be described.
均質化処理。Homogenization process.
均質化処理はＣｕ、Ｌｉなとの溶質原子の粒界偏析を少
なくし、成分を均一化する効果かある。４５０℃未満で
はその効果か少なく、５４０℃を越えるとＺｒなとの再
結晶抑制元素か安定相として＋１７出し、それらの元素
のもつ効果か少なくなる。また、１時間未満では成分均
一化の効果が少なく、５０時間を越えるとその効果が飽
和するため、経済的な点て意味がない。４２０℃程度で
一旦ステップ加熱すると良い。The homogenization treatment has the effect of reducing grain boundary segregation of solute atoms such as Cu and Li and making the components uniform. Below 450°C, the effect is small, and above 540°C, recrystallization inhibiting elements such as Zr exhibit +17 as a stable phase, and the effects of these elements are reduced. Furthermore, if the time is less than 1 hour, the effect of homogenizing the components will be small, and if it exceeds 50 hours, the effect will be saturated, so it is economically meaningless. It is best to perform step heating once at about 420°C.
圧延温度；
圧延温度が３００〜４５０℃であるのはこの温度域かこ
のＡｌ−Ｃｕ−Ｌｉ系合金の
第２相（Ｔ Ｉ＜ Ａ ｌ ２ Ｌ ｉ Ｃｕ ＞、Ｔ
ｌ＜Ａｌ６Ｌｉ３Ｃｕ＞相）の析出温度であり、この温
度範囲で圧延すると安定な下部組織か形成される。Rolling temperature: The rolling temperature is 300 to 450°C because it is in this temperature range that the second phase of the Al-Cu-Li alloy (T I < Al 2 Li Cu >, T
This is the precipitation temperature of the <Al6Li3Cu> phase), and rolling in this temperature range forms a stable substructure.
冷間圧延２
冷間加工度か５０％以上なのは、これより少ないと安定
な下部組織か板面あるいは板厚方−］ 〇 −
向で均一に形成されにくいためである。Cold Rolling 2 The reason why the degree of cold working is 50% or more is because if it is less than this, it is difficult to form a stable substructure uniformly on the plate surface or in the thickness direction.
析出処理。Precipitation treatment.
３００−４５０℃ノ１〜５０時間の析出処理を３００〜
４５０℃での温度での圧延の前あるいは圧延の途中にイ
ー」うと、この圧延中に安定なト部組織が形成されやす
い。この場合は冷間圧延前の中間焼鈍を省くこともでき
る。300-450℃ precipitation treatment for 1-50 hours
If E is carried out before or during rolling at a temperature of 450° C., a stable top structure is likely to be formed during this rolling. In this case, intermediate annealing before cold rolling can be omitted.
溶体化処理；
鋳塊均質化熱処理後の冷却中に粒界上に析出した化合物
を再固溶させ、熱間加圧性を向上させるために行う。Solution treatment: Performed in order to solidify compounds precipitated on grain boundaries again during cooling after ingot homogenization heat treatment and improve hot pressability.
中間焼鈍。Intermediate annealing.
中間焼鈍を３００〜４５０℃で１〜５０時間実施するの
は、さらに積極的に第２相として析出させ、凝集化させ
、次の冷間圧延工程で加工ひずみを導入しやすくするた
めである。１時間未満では第２相の析出か不十分で、一
方、５０時間を越えると溶質原子が析出しすぎて、加工
ひずみが消滅しやすくなる。The reason why the intermediate annealing is performed at 300 to 450°C for 1 to 50 hours is to more actively precipitate and agglomerate as a second phase, thereby making it easier to introduce processing strain in the next cold rolling process. If the heating time is less than 1 hour, the second phase will not be sufficiently precipitated, whereas if the heating time exceeds 50 hours, solute atoms will precipitate too much, making it easier for the processing strain to disappear.
最終焼鈍；
一］］−
冷間用延数をそのまま超塑性変形させることかｎＪ能で
あるか、その昇温速度によっては昇温中に再結晶が進行
して、超塑性特性が低下する場合かある。この場合、予
め超塑性変形温度である ４５０℃以上に５９Ｃ／秒以
上の昇温速度で加熱処理することか自゛効である。また
、これ以上の温度に加熱することにより、下部組成を形
成させるために用いた第２相を再固溶させることができ
、超塑性変形中のキャビティの原因になる第２相か少な
くなり、超塑性特性を向上させることかできる。たたし
、この加熱処理か１分未満ではこれらの効果か少なく、
１時間を越えると静的再結晶を生し超塑性特性か低下し
やすい。Final annealing: 1]] - Depending on whether the cold elongation is directly subjected to superplastic deformation or nJ capacity, recrystallization progresses during temperature increase and the superplastic properties deteriorate depending on the temperature increase rate. There is. In this case, it is effective to heat the material in advance to a temperature of 450° C. or higher, which is the superplastic deformation temperature, at a heating rate of 59 C/sec or higher. In addition, by heating to a temperature higher than this, the second phase used to form the lower composition can be re-dissolved, and the amount of the second phase that causes cavities during superplastic deformation is reduced. It is possible to improve superplastic properties. However, if this heat treatment is done for less than 1 minute, these effects will be minimal.
If it exceeds 1 hour, static recrystallization occurs and the superplastic properties tend to deteriorate.
［実施例］
Ａｌ−２，４％Ｃｕ −２，２％Ｌ ｉ〜０．１２％Ｚ
ｒ〜０．０４％Ｔ１合金をアルゴン雰囲気中で溶解鋳造
後、鋳塊均質化熱処理条件を変えて熱間圧延を開始し、
６ｍｍ厚の板とした。熱間圧延開始温度は３００℃〜５
００℃まで変化さぜた。熱間圧延−］２−
後、中間焼鈍工程を入れ、冷間加工を行った。[Example] Al-2,4%Cu-2,2%Li~0.12%Z
After melting and casting r ~ 0.04% T1 alloy in an argon atmosphere, hot rolling was started by changing the ingot homogenization heat treatment conditions,
The plate was 6 mm thick. Hot rolling start temperature is 300℃~5
The temperature was changed to 00°C. Hot rolling-]2- After that, an intermediate annealing step was performed and cold working was performed.
又、最終焼鈍を行った場合もある。こうして製造した板
の製造条件と超塑性特性（伸び）の関係を表１に示す。In some cases, final annealing is also performed. Table 1 shows the relationship between the manufacturing conditions and superplastic properties (elongation) of the plates manufactured in this way.
引張試験は圧延方向に沿って採取した試験片を５００℃
で行った。引張の初期のひすみ速度は５、［ｉＸ １０
−’ ｓ−’である。伸びは標点間距離を１０ｍｍとし
て破断時の全伸びを求めた。評価は３００％以上を合格
とした。In the tensile test, test pieces taken along the rolling direction were heated to 500°C.
I went there. The initial strain rate in tension is 5, [iX 10
-'s-'. For elongation, the total elongation at break was determined with a gauge distance of 10 mm. An evaluation of 300% or higher was considered a pass.
＝ １４
［発明の効果］
本発明の製造方法によれば、以下のような効果か得られ
る。= 14 [Effects of the Invention] According to the manufacturing method of the present invention, the following effects can be obtained.
（１）本発明の方法により製造されたＡｌ−Ｃｕ−Ｌｉ
−Ｚｒ合金板は、非再結晶組織を有しているので、この
組織状態から変形速度を従来の超塑性アルミニウム合金
板（例えば７４７５など）よりも１桁大きくして、超塑
性変形をさせることができる。(1) Al-Cu-Li produced by the method of the present invention
- Since the Zr alloy plate has a non-recrystallized structure, it is possible to make the deformation rate one order of magnitude higher than that of conventional superplastic aluminum alloy plates (such as 7475) due to this structure to cause superplastic deformation. I can do it.
（２）本発明によれば高温の均質化熱処理と強度の冷間
加工を組合せ、あるいは更に、急速加熱による最終焼鈍
を行うことで、鋳造時の組織をこわすとともに、鋳造時
の粒界不純物を粒界から除去することができる。これに
よって、合金材の超塑性特性を向上させることかでき、
航空機や車輌および自動車などの複雑な形状の部品を容
易に製造することができる。(2) According to the present invention, by combining high-temperature homogenization heat treatment and intense cold working, or by further performing final annealing by rapid heating, the structure at the time of casting is destroyed and grain boundary impurities at the time of casting are removed. can be removed from grain boundaries. This can improve the superplastic properties of the alloy material,
Parts with complex shapes for aircraft, vehicles, automobiles, etc. can be easily manufactured.
Claims (6)
Ｚｒ０．０５〜０．２０％、Ｔｉ０．０１〜０．１０％
を含有し、残部Ａｌおよび不可避不純物からなるアルミ
ニウム合金を、通常の鋳造法で溶解、鋳造後、４５０〜
５４０℃の温度において１〜５０時間の均質化処理を行
い、その後３００〜４５０℃の温度で圧延し、５０％以
上の冷間圧延を行うことを特徴とするＡｌ−Ｃｕ−Ｌｉ
−Ｚｒ系超塑性板の製造方法。(1) Cu2.0-3.0%, Li1.0-3.0%,
Zr0.05-0.20%, Ti0.01-0.10%
After melting and casting an aluminum alloy containing aluminum with the remainder being Al and unavoidable impurities, it has a melting temperature of 450~
Al-Cu-Li characterized by performing homogenization treatment at a temperature of 540°C for 1 to 50 hours, then rolling at a temperature of 300 to 450°C, and performing cold rolling of 50% or more.
- A method for manufacturing a Zr-based superplastic plate.
Ｚｒ０．０５〜０．２０％、Ｔｉ０．０１〜０．１０％
を含有し、残部Ａｌおよび不可避不純物からなるアルミ
ニウム合金を、通常の鋳造法で溶解し、鋳造後、４５０
〜５４０℃の温度において１〜５０時間の均質化処理を
行い、その後３００〜４５０℃で１〜５０時間の析出処
理後、３００〜４５０℃の温度で圧延し、５０％以上の
冷間圧延を行うことを特徴とするＡｌ−Ｃｕ−Ｌｉ−Ｚ
ｒ系超塑性板の製造方法。(2) Cu2.0-3.0%, Li1.0-3.0%,
Zr0.05-0.20%, Ti0.01-0.10%
An aluminum alloy containing aluminum with the remainder being Al and unavoidable impurities is melted by a normal casting method, and after casting, the aluminum alloy is
Homogenization treatment for 1 to 50 hours at a temperature of ~540°C, followed by precipitation treatment for 1 to 50 hours at a temperature of 300 to 450°C, and rolling at a temperature of 300 to 450°C to achieve a cold rolling of 50% or more. Al-Cu-Li-Z characterized by
A method for producing an r-based superplastic plate.
Ｚｒ０．０５〜０．２０％、Ｔｉ０．０１〜０．１０％
を含有し、残部Ａｌおよび不可避不純物からなるアルミ
ニウム合金を、通常の鋳造法で溶解し、鋳造後、４５０
〜５４０℃の温度において１〜５０時間の均質化処理を
行った後、４６０℃以上の温度で溶体化処理後、３００
〜４５０℃の温度範囲まで冷却し、圧延を開始し、該圧
延の途中で圧延を中断し、１〜５０時間保持し析出処理
した後、さらに３００〜４５０℃の温度で圧延を継続し
た後、５０％以上の冷間圧延を行うことを特徴とするＡ
ｌ−Ｃｕ−Ｌｉ−Ｚｒ系超塑性板の製造方法。(3) Cu2.0-3.0%, Li1.0-3.0%,
Zr0.05-0.20%, Ti0.01-0.10%
An aluminum alloy containing aluminum with the remainder being Al and unavoidable impurities is melted by a normal casting method, and after casting, the aluminum alloy is
After homogenization treatment for 1 to 50 hours at a temperature of ~540 °C, after solution treatment at a temperature of 460 °C or more, 300 °C
After cooling to a temperature range of ~450 ° C., starting rolling, interrupting the rolling in the middle of the rolling, holding for 1 to 50 hours for precipitation treatment, and further continuing rolling at a temperature of 300 to 450 ° C., A characterized by cold rolling of 50% or more
A method for manufacturing a l-Cu-Li-Zr based superplastic plate.
Ｚｒ０．０５〜０．２０％、Ｔｉ０．０１〜０．１０％
を含有し、残部Ａｌおよび不可避不純物からなるアルミ
ニウム合金を、通常の鋳造法で溶解し、鋳造後、４５０
〜５４０℃で１〜５０時間保持後３００〜４５０℃の温
度まで冷却し、該温度範囲で１〜５０時間の析出処理後
、３００〜４５０℃の温度で圧延し、ついで５０％以上
の冷間圧延を行うことを特徴とするＡｌ−Ｃｕ−Ｌｉ−
Ｚｒ系超塑性板の製造方法。(4) Cu2.0-3.0%, Li1.0-3.0%,
Zr0.05-0.20%, Ti0.01-0.10%
An aluminum alloy containing aluminum with the remainder being Al and unavoidable impurities is melted by a normal casting method, and after casting, the aluminum alloy is
After being held at ~540°C for 1 to 50 hours, it is cooled to a temperature of 300 to 450°C, and after precipitation treatment in this temperature range for 1 to 50 hours, it is rolled at a temperature of 300 to 450°C, and then cold rolled by 50% or more. Al-Cu-Li- characterized by rolling
A method for manufacturing a Zr-based superplastic plate.
１〜５０時間の中間焼鈍を行う請求項（１）〜（４）の
いずれかに記載のＡｌ−Ｃｕ−Ｌ−Ｚｒ系超塑性板の製
造方法。(5) The Al-Cu-L-Zr superplastic according to any one of claims (1) to (4), wherein intermediate annealing is performed at 300 to 450°C for 1 to 50 hours before or during cold rolling. Method of manufacturing the board.
する請求項（１）〜（５）のいずれかに記載のＡｌ−Ｃ
ｕ−Ｌｉ−Ｚｒ系超塑性板の製造方法。(6) Al-C according to any one of claims (1) to (5), wherein the final annealing is performed at 450°C or higher for 1 minute to 1 hour after cold rolling.
A method for producing a u-Li-Zr superplastic plate.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63087401A JPH07116567B2 (en) | 1988-04-11 | 1988-04-11 | Method for producing A1-Cu-Li-Zr superplastic plate |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63087401A JPH07116567B2 (en) | 1988-04-11 | 1988-04-11 | Method for producing A1-Cu-Li-Zr superplastic plate |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH01259147A true JPH01259147A (en) | 1989-10-16 |
| JPH07116567B2 JPH07116567B2 (en) | 1995-12-13 |
Family
ID=13913853
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP63087401A Expired - Lifetime JPH07116567B2 (en) | 1988-04-11 | 1988-04-11 | Method for producing A1-Cu-Li-Zr superplastic plate |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH07116567B2 (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0571542A1 (en) * | 1991-02-15 | 1993-12-01 | Reynolds Metals Company | Low density aluminum lithium alloy |
| US9926620B2 (en) | 2012-03-07 | 2018-03-27 | Arconic Inc. | 2xxx aluminum alloys, and methods for producing the same |
| CN111500954A (en) * | 2020-04-29 | 2020-08-07 | 天津航天机电设备研究所 | Heat treatment process for large high-strength magnesium alloy thin-wall casting |
| CN115125422A (en) * | 2022-06-09 | 2022-09-30 | 烟台南山学院 | Corrosion-resistant high-toughness Al-Li-Cu-Zr-Er alloy plate and preparation method thereof |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| AU2013204114B2 (en) * | 2012-03-07 | 2016-04-14 | Arconic Inc. | Improved 2XXX aluminum alloys, and methods for producing the same |
| WO2013172912A2 (en) * | 2012-03-07 | 2013-11-21 | Alcoa Inc. | Improved aluminum-lithium alloys, and methods for producing the same |
| CN106480385B (en) * | 2016-12-12 | 2018-01-16 | 中南大学 | One kind improves the strong plasticity solid solution pre-treating method of aluminium lithium alloy thin plate and its heat treatment method |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6156269A (en) * | 1984-07-20 | 1986-03-20 | Kobe Steel Ltd | Manufacture of super plastic al-li alloy |
-
1988
- 1988-04-11 JP JP63087401A patent/JPH07116567B2/en not_active Expired - Lifetime
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6156269A (en) * | 1984-07-20 | 1986-03-20 | Kobe Steel Ltd | Manufacture of super plastic al-li alloy |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0571542A1 (en) * | 1991-02-15 | 1993-12-01 | Reynolds Metals Company | Low density aluminum lithium alloy |
| EP0571542A4 (en) * | 1991-02-15 | 1993-12-29 | Reynolds Metals Company Reynolds Metals Building | Low density aluminum lithium alloy |
| US9926620B2 (en) | 2012-03-07 | 2018-03-27 | Arconic Inc. | 2xxx aluminum alloys, and methods for producing the same |
| CN111500954A (en) * | 2020-04-29 | 2020-08-07 | 天津航天机电设备研究所 | Heat treatment process for large high-strength magnesium alloy thin-wall casting |
| CN115125422A (en) * | 2022-06-09 | 2022-09-30 | 烟台南山学院 | Corrosion-resistant high-toughness Al-Li-Cu-Zr-Er alloy plate and preparation method thereof |
| CN115125422B (en) * | 2022-06-09 | 2023-10-10 | 烟台南山学院 | Corrosion-resistant high-strength-toughness Al-Li-Cu-Zr-Er alloy plate and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH07116567B2 (en) | 1995-12-13 |
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