JPS616244A - High strength alloy for forming having fine grain and its manufacture - Google Patents
High strength alloy for forming having fine grain and its manufactureInfo
- Publication number
- JPS616244A JPS616244A JP12812084A JP12812084A JPS616244A JP S616244 A JPS616244 A JP S616244A JP 12812084 A JP12812084 A JP 12812084A JP 12812084 A JP12812084 A JP 12812084A JP S616244 A JPS616244 A JP S616244A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- strength
- forming
- high strength
- quenching
- 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
- Heat Treatment Of Nonferrous Metals Or Alloys (AREA)
- Shaping Metal By Deep-Drawing, Or The Like (AREA)
Abstract
Description
【発明の詳細な説明】
産業−■二の利用分野
本発明は高強度の成形加工用合金並びに製造法に関する
ものである。DETAILED DESCRIPTION OF THE INVENTION Industry - Second Field of Application The present invention relates to a high-strength forming alloy and a manufacturing method.
従来の技術
従来、引張強さ40k(1/11112前後の高強度合
金としてはJIS2014合金、2017合金、202
4合金等が知られている。これらの合金は高強度構造用
材料として広範囲に使用されているが、熱処理型の合金
であるため、高強度を付与するには焼入れ、焼もどし処
理が必要とされ、しかも焼入れに関しては水焼入れが必
要とされる。このため、焼入歪の除去等を含めて熱処理
コストの高い問題がある。Conventional technology Conventionally, high-strength alloys with a tensile strength of 40k (around 1/11112) include JIS2014 alloy, 2017 alloy, and 202
4 alloys are known. These alloys are widely used as high-strength structural materials, but since they are heat-treatable alloys, quenching and tempering treatments are required to impart high strength. Needed. Therefore, there is a problem in that the heat treatment cost is high, including the removal of quenching distortion.
発明が解決しようどする問題点
本発明は水焼入れを必要とせず、空冷でも焼入れ可能な
低コストの高強度成形加工用アルミニウム合金を得んと
するものである。Problems to be Solved by the Invention The present invention aims to provide a low-cost, high-strength forming aluminum alloy that does not require water quenching and can be quenched even by air cooling.
問題点を解゛するための手段
本発明は、M(13,5〜5.0%、Zn2,1〜3.
5%、Cu 0.05〜0.6%を必須成分とし、M
n 0.05〜0.40%、Q r 0.05〜0.2
5%、Zr0.05〜0.25%、V 0.05〜0.
25%のうちの1種以上を0.05〜0.6%含み、残
りアルミニウムと不純物よりなるアルミニウム合金であ
る。Means for Solving the Problems The present invention provides M(13.5 to 5.0%, Zn2.1 to 3.0%).
5%, Cu 0.05-0.6% as essential components, M
n 0.05-0.40%, Q r 0.05-0.2
5%, Zr 0.05-0.25%, V 0.05-0.
It is an aluminum alloy containing 0.05 to 0.6% of one or more of 25% aluminum and the remainder consisting of aluminum and impurities.
このような合金によれば強度が高く、結晶粒が微細で、
成形加工性にすぐれ、しかも空気焼入れで焼入可能な低
下コストの高強度成形加工用合金板を得ることが可能と
なる。Such alloys have high strength, fine grains,
It becomes possible to obtain a high-strength alloy plate for forming that has excellent forming processability and can be hardened by air quenching at a reduced cost.
各添加元素の限定理由を以下に示す。The reasons for limiting each additive element are shown below.
Mi):Millは主として合金の強度を高めるもので
あり、3.5〜5.0%の範囲とする。3.5%より少
ないと強度や成形性が十分でなく、5.0%をこえると
熱間加工性が極度に低下する。Mi): Mill mainly increases the strength of the alloy and is in the range of 3.5 to 5.0%. When it is less than 3.5%, strength and formability are insufficient, and when it exceeds 5.0%, hot workability is extremely reduced.
’;ln:ZnはM(Iと共存して合金に時効性を与え
、焼入後の室温時効により強度の向上を可能とするもの
であり、2.1〜3.5%の範囲とする。2.1%より
少ない場合には強度の向上が十分でなく、3.5%をこ
えると強度は著しく高くなるが、伸びが低下して成形性
が低下するばかりでなく、合金の熱間加工性が著しく低
下する。';ln: Zn coexists with M(I) to impart aging properties to the alloy, making it possible to improve strength through room temperature aging after quenching, and should be in the range of 2.1 to 3.5%. If it is less than 2.1%, the strength will not be improved sufficiently, and if it exceeds 3.5%, the strength will increase significantly, but not only will the elongation decrease and formability decrease, but the hot Workability is significantly reduced.
(:、U:(:、UはZnと同様に合金に時効性を与え
、焼入後の室温時効により強度を向上させる効果がある
。0.05%より少ない場合には強度向上の効果が少な
く、0.6%をこえると強度は著しく高くなるか熱間加
工性や成形性が低下する。(:, U: (:, Like Zn, U imparts aging properties to the alloy and has the effect of improving strength through room temperature aging after quenching. If it is less than 0.05%, there is no effect of improving strength. If the amount exceeds 0.6%, the strength will increase significantly or hot workability and moldability will decrease.
Mn、Cr、Zr、V:これらの元素は鋳塊の均質化処
理時に微細な金属間化合物として析出し、再結晶粒の微
細化と強度向上に有効である。添加量が下限未満の場合
には上記の効果が十分でなく、添加量の合計が上限をこ
えると焼入性が低下すると共に巨大な金属間化合物が晶
出する問題がある。Mn, Cr, Zr, V: These elements precipitate as fine intermetallic compounds during the homogenization treatment of the ingot, and are effective in making recrystallized grains finer and improving strength. When the amount added is less than the lower limit, the above effect is not sufficient, and when the total amount added exceeds the upper limit, there is a problem that the hardenability decreases and a huge intermetallic compound crystallizes.
なお、本発明においては、一般のアルミニウム合金と同
様にTi0.2%以下、30゜01%以下の添加は鋳造
組織を微細化し、熱間加工性の向上や品質向上に有効で
ある。In addition, in the present invention, as with general aluminum alloys, addition of Ti at 0.2% or less and 30°01% or less is effective in refining the casting structure and improving hot workability and quality.
本発明合金ですぐれた性能を得るには以下の製造工程を
とる。In order to obtain excellent performance with the alloy of the present invention, the following manufacturing steps are taken.
鋳塊を400〜520℃で一段または多段ソーキングを
行ない、鋳塊組織を均質化する。温度が下限未満の場合
には均質化効果が不十分であり、高強度や微細結晶粒が
得られない。The ingot is soaked in one or multiple stages at 400 to 520°C to homogenize the ingot structure. When the temperature is below the lower limit, the homogenization effect is insufficient, and high strength and fine crystal grains cannot be obtained.
温度が上限をこえると共晶融解の危険がある。If the temperature exceeds the upper limit, there is a risk of eutectic melting.
また、均質化時間は2〜48時間が適当で、2時間未満
では均質化効果が不十分であり、又、48時間を越えて
も結晶粒、強度、成形性等の特性は向上しない。Further, the homogenization time is suitably 2 to 48 hours; if it is less than 2 hours, the homogenization effect will be insufficient, and if it exceeds 48 hours, the properties such as crystal grains, strength, and moldability will not improve.
均質化処理時の無闇加工は350〜500℃で行なうこ
とが望ましく、下限未満では変形抵抗が高く熱部加工が
vA!lである。上限をこえると加工割れを生じ好まし
くない。It is desirable to carry out the dark processing during the homogenization treatment at a temperature of 350 to 500°C; below the lower limit, the deformation resistance is high and the hot part processing is vA! It is l. If the upper limit is exceeded, processing cracks may occur, which is not preferable.
熱間加工侵の冷間加工度は30%以上が望ましり、30
%未満の場合には微細結晶粒が得ら一5=
れない。The cold working degree of hot working corrosion is preferably 30% or more, and 30% or more is desirable.
If it is less than 5%, fine crystal grains cannot be obtained.
最終調質はT4処理(溶体化処理→焼入れ→室温時効)
する必要があり、430〜530℃で溶体化処理するこ
とが望ましい。Final tempering is T4 treatment (solution treatment → quenching → room temperature aging)
It is desirable to carry out solution treatment at 430 to 530°C.
溶体化処理温度が下限未満の場合には強度が十分でなく
、上限をこえると共晶融解の危険がある。焼入後の冷却
は水焼入れのような急冷を行なう必要はなく、5℃以上
空気焼入れ程度の冷却速度(10〜b
分に高強度を1りることが可能である。If the solution treatment temperature is below the lower limit, the strength will not be sufficient, and if it exceeds the upper limit, there is a risk of eutectic melting. Cooling after quenching does not require rapid cooling as in water quenching, and high strength can be achieved at a cooling rate of 5° C. or higher comparable to air quenching (10 to 10 b minutes).
従って、発明合金は連続焼入炉により低コストで焼入れ
処理することが可能である。Therefore, the invention alloy can be hardened at low cost in a continuous hardening furnace.
衷101 以下に実施例並びに比較例について述べる。101 Examples and comparative examples will be described below.
実施例1
表1に示した組成を有する合金鋳塊(30mm厚さ)を
480℃で16hr均賀化処理侵に420〜460℃で
3u+まで熱間圧延し、360℃x 2hrの中間焼鈍
を行なった後に冷間圧延により11BIIl板に圧延し
た。この11II冷間圧延板を480℃で2分の溶体化
処理後に平均冷却速度30℃/秒で室温まで強制空冷に
より冷却し、室温で30日時効後転諸性能を評価した。Example 1 An alloy ingot (30 mm thick) having the composition shown in Table 1 was heated at 480°C for 16 hours, hot rolled at 420 to 460°C to 3u+, and then subjected to intermediate annealing at 360°C x 2 hours. After this, it was rolled into a 11BII plate by cold rolling. This 11II cold-rolled plate was solution treated at 480° C. for 2 minutes, then cooled by forced air cooling to room temperature at an average cooling rate of 30° C./sec, and various performances after aging at room temperature for 30 days were evaluated.
表2に諸性能を示したが、発明合金は40k。Various performances are shown in Table 2, and the invention alloy is 40k.
/l!l12近い強度と微細結晶粒を有し、伸びやエリ
クセン値も^く成形性にすぐれている。/l! It has a strength close to l12 and fine crystal grains, and has excellent elongation and Erichsen value, and excellent formability.
比較例のNo、12、No、14〜16の各合金は伸び
やエリクセン値が高く成形性にすぐれているが強度が低
い。No、13合金は強度は高いが伸びやエリクセン値
が低く成形性に問題がある。No、17合金は焼入れ性
が悪く強度が低い。Comparative example alloys No. 12, No. 14 and No. 14 to 16 have high elongation and Erichsen value and excellent formability, but have low strength. Alloy No. 13 has high strength, but has low elongation and Erichsen value, and has problems with formability. Alloy No. 17 has poor hardenability and low strength.
表1 実施例の化学成分(%)
表21uTJ板の諸性能
9一
実施例2
表1に示した各合金を表3に示した製造条件で1mlに
圧延してT4処理を行なった。表4には焼入後に室温で
30日時効したT4板の諸性能を示す。Table 1 Chemical composition (%) of Examples Table 2 Various performances of 1uTJ plate 9 - Example 2 Each alloy shown in Table 1 was rolled to 1 ml under the manufacturing conditions shown in Table 3 and subjected to T4 treatment. Table 4 shows the various performances of the T4 plate aged for 30 days at room temperature after quenching.
良好な性能の得られるのは発明条件(NO11〜6)の
みであり、比較例(1’、lo、7〜12)では良好な
性能は得られない。Good performance was obtained only under the invention conditions (NOs 11 to 6), and good performance was not obtained under the comparative examples (1', lo, 7 to 12).
族311111IIT4板の製造条f[表4 1eml
’4板の諸+11能
本発明は、微細結晶粒をもった高強度の成形加工用に適
したアルミニウム合金が得られ、該合金は焼入れ竹に優
れ、連続焼入れ炉にて低コストで処理することができる
。Manufacturing method f of Group 311111IIT4 plate [Table 4 1eml
The present invention provides an aluminum alloy with fine grains suitable for high-strength forming processing, which is excellent in quenching bamboo and can be processed at low cost in a continuous quenching furnace. be able to.
Claims (2)
Cu10.05〜0.6%を必須成分とし、Mn0.0
5〜0.4%、Cr0.05〜0.25%、Zr0.0
5〜0.25%、V0.05〜0.25%のうち1種以
上を0.05〜0.6%含み、残りアルミニウムと不純
物よりなることを特徴とする空冷で焼入可能な微細結晶
粒高強度成形加工用合金。(1) Mg3.5-5.0%, Zn2.1-3.5%,
Cu10.05~0.6% is an essential component, Mn0.0
5-0.4%, Cr0.05-0.25%, Zr0.0
5 to 0.25%, V0.05 to 0.25%, and 0.05 to 0.6% of one or more of V0.05 to 0.25%, with the remainder consisting of aluminum and impurities, and is quenchable by air cooling. Alloy for high grain strength forming processing.
Cu0.05〜0.6%を必須成分とし、Mn0.05
〜0.4%、Cr0.05〜0.25%、Zr0.05
〜0.25%、V0.05〜0.25%のうち1種以上
を0.05〜0.6%含み、残りアルミニウムと不純物
よりなる合金を400〜520℃で均質化処理後に35
0〜500℃で熱間加工後、30%以上冷間加工し、4
30〜530℃で溶体化処理後に5℃/秒以上の冷却速
度で焼入れすることを特徴とする微細結晶粒高強度成形
加工用合金の製造法。(2) Mg3.5-5.0%, Zn2.1-3.5%,
Cu0.05-0.6% is an essential component, Mn0.05
~0.4%, Cr0.05~0.25%, Zr0.05
~0.25%, V0.05~0.25%, containing 0.05~0.6% of one or more of V0.05~0.25%, and the remaining aluminum and impurities after homogenization treatment at 400~520°C.
After hot working at 0 to 500℃, cold working by 30% or more,
A method for producing a fine-grained, high-strength forming alloy, which comprises solution treatment at 30 to 530°C and then quenching at a cooling rate of 5°C/sec or more.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP12812084A JPS616244A (en) | 1984-06-21 | 1984-06-21 | High strength alloy for forming having fine grain and its manufacture |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP12812084A JPS616244A (en) | 1984-06-21 | 1984-06-21 | High strength alloy for forming having fine grain and its manufacture |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS616244A true JPS616244A (en) | 1986-01-11 |
JPH0418019B2 JPH0418019B2 (en) | 1992-03-26 |
Family
ID=14976874
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP12812084A Granted JPS616244A (en) | 1984-06-21 | 1984-06-21 | High strength alloy for forming having fine grain and its manufacture |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS616244A (en) |
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS62290851A (en) * | 1986-06-09 | 1987-12-17 | Sky Alum Co Ltd | Manufacture of rolled aluminum alloy plate |
WO1999042627A1 (en) * | 1998-02-20 | 1999-08-26 | Corus Aluminium Walzprodukte Gmbh | Formable, high strength aluminium-magnesium alloy material for application in welded structures |
JP2016514209A (en) * | 2013-03-09 | 2016-05-19 | アルコア インコーポレイテッド | Heat-treatable aluminum alloy containing magnesium and zinc and method for producing the same |
EP3848476A1 (en) * | 2020-01-07 | 2021-07-14 | AMAG rolling GmbH | Sheet or strip made of a curable aluminium alloy, vehicle part manufactured from same, its use and a method for producing the sheet or strip |
EP3927860A4 (en) * | 2019-02-20 | 2022-11-23 | Howmet Aerospace Inc. | Improved aluminum-magnesium-zinc aluminum alloys |
-
1984
- 1984-06-21 JP JP12812084A patent/JPS616244A/en active Granted
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS62290851A (en) * | 1986-06-09 | 1987-12-17 | Sky Alum Co Ltd | Manufacture of rolled aluminum alloy plate |
WO1999042627A1 (en) * | 1998-02-20 | 1999-08-26 | Corus Aluminium Walzprodukte Gmbh | Formable, high strength aluminium-magnesium alloy material for application in welded structures |
JP2016514209A (en) * | 2013-03-09 | 2016-05-19 | アルコア インコーポレイテッド | Heat-treatable aluminum alloy containing magnesium and zinc and method for producing the same |
EP3927860A4 (en) * | 2019-02-20 | 2022-11-23 | Howmet Aerospace Inc. | Improved aluminum-magnesium-zinc aluminum alloys |
EP3848476A1 (en) * | 2020-01-07 | 2021-07-14 | AMAG rolling GmbH | Sheet or strip made of a curable aluminium alloy, vehicle part manufactured from same, its use and a method for producing the sheet or strip |
WO2021140163A1 (en) * | 2020-01-07 | 2021-07-15 | Amag Rolling Gmbh | Sheet or strip made of an aluminum alloy which can be hardened, a vehicle part made therefrom, a use, and a method for producing the sheet or strip |
CN115151667A (en) * | 2020-01-07 | 2022-10-04 | 亚马格轧制公司 | Plate or strip made of a hardenable aluminum alloy, vehicle part produced therefrom, use and method for producing a plate or strip |
Also Published As
Publication number | Publication date |
---|---|
JPH0418019B2 (en) | 1992-03-26 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP0646655B1 (en) | Method of manufacturing natural aging-retardated aluminum alloy sheet exhibiting excellent formability and excellent bake hardening ability | |
US5460666A (en) | Method of manufacturing natural aging-retardated aluminum alloy sheet | |
JPH0747808B2 (en) | Method for producing aluminum alloy sheet excellent in formability and bake hardenability | |
JPS6050864B2 (en) | Aluminum alloy material for forming with excellent bending workability and its manufacturing method | |
CN115216674B (en) | 7000 series aluminum alloy sheet for automobile and preparation method thereof | |
JPS616244A (en) | High strength alloy for forming having fine grain and its manufacture | |
JPH06340940A (en) | Aluminum alloy sheet excellent in press formability and baking hardenability and its production | |
JPH0257655A (en) | Foamable aluminum alloy having excellent surface treating characteristics and its manufacture | |
JPS61272342A (en) | Aluminum alloy sheet excelling in formability and baking hardening and its production | |
JPS6123751A (en) | Manufacture of al-li alloy having superior ductility and toughness | |
JPS61166938A (en) | Al-li alloy for expansion and its production | |
JPS61163232A (en) | High strength al-mg-si alloy and its manufacture | |
JPH04365834A (en) | Aluminum alloy sheet for press forming excellent in hardenability by low temperature baking and its production | |
JPS6410584B2 (en) | ||
JPH08269608A (en) | High strength aluminum alloy excellent in formability and corrosion resistance | |
JPS6220272B2 (en) | ||
JPH04304339A (en) | Aluminum alloy sheet for press forming excellent in balance between strength and ductility and baking hardenability and its production | |
JPH062092A (en) | Method for heat-treating high strength and high formability aluminum alloy | |
JPH0480979B2 (en) | ||
JPS61227157A (en) | Manufacture of al-li alloy for elongation working | |
JPS5831054A (en) | Aluminum alloy having superior strength and corrosion resistance and its manufacture | |
JPS63169353A (en) | Aluminum alloy for forming and its production | |
JPH04160131A (en) | Al-mg-si alloy plate excellent in strength and formability, and its manufacture | |
JPH07228957A (en) | Production of aluminum alloy sheet having excellent formability and quench-hardenability | |
JPS6296643A (en) | Superplastic aluminum alloy |