JP3161141B2 - Manufacturing method of aluminum alloy sheet - Google Patents
Manufacturing method of aluminum alloy sheetInfo
- Publication number
- JP3161141B2 JP3161141B2 JP06477593A JP6477593A JP3161141B2 JP 3161141 B2 JP3161141 B2 JP 3161141B2 JP 06477593 A JP06477593 A JP 06477593A JP 6477593 A JP6477593 A JP 6477593A JP 3161141 B2 JP3161141 B2 JP 3161141B2
- Authority
- JP
- Japan
- Prior art keywords
- temperature
- aluminum alloy
- annealing
- rolling
- cold rolling
- 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.)
- Expired - Fee Related
Links
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- Continuous Casting (AREA)
Description
【0001】[0001]
【産業上の利用分野】本発明はアルミニウム合金薄板の
製造方法に係り、成形性と強度に卓越し、しかも部分焼
鈍処理の温度範囲が広く作業性に優れたアルミニウム合
金薄板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 method for producing an aluminum alloy sheet, and provides a method for producing an aluminum alloy sheet having excellent formability and strength, a wide temperature range for partial annealing, and excellent workability. It is assumed that.
【0002】[0002]
【従来の技術】プレートフイン型熱交換器用のフイン
や、キャップ、アルミ缶、アルミ箔容器などを得るには
従来、A1000系合金およびこれにMnを含有せしめた
半硬質薄板が使用されている。特にプレートフイン型熱
交換器用フインは上記したA1000系合金の連続鋳造
圧延材を冷間圧延のみ、あるいは再結晶化中間焼鈍処理
後最終冷間圧延を施し、しかる後部分焼鈍を施して半硬
質薄板とし製造されていた。2. Description of the Related Art In order to obtain fins, caps, aluminum cans, aluminum foil containers and the like for plate fin type heat exchangers, conventionally, an A1000 series alloy and a semi-hard thin plate containing Mn therein have been used. In particular, fins for plate fin type heat exchangers are preferably made of the above-mentioned continuous cast rolled material of the A1000 series alloy only by cold rolling, or subjected to recrystallization intermediate annealing treatment and then subjected to final cold rolling, and then subjected to partial annealing to obtain a semi-hard thin plate. And was manufactured.
【0003】一方、特公昭61-21296においてはMg0.5%
を超え1.0%以下およびMnを0.05〜1.0%を含み、更
にFeとSiを特定の関係で含有し、残部がAlおよび不可避
不純物からなる薄板用アルミニウム合金が提案されてお
り、また製造された半硬質薄板に対して熱交換媒体の流
通する通液管外径に近似した孔を穿ちその周囲に張出し
部を形成し、該張出し部を外側にカール曲げする所謂フ
レア加工してプレートフインを成形することも図示説明
されている。On the other hand, in Japanese Patent Publication No. 61-21296, Mg 0.5%
Over 1.0% or less and Mn in a range of 0.05 to 1.0%, further containing Fe and Si in a specific relationship, the balance being Al and unavoidable impurities. Also, a so-called flare process is performed on the manufactured semi-rigid thin plate by forming a hole similar to the outer diameter of the liquid passage pipe through which the heat exchange medium flows, forming an overhang around the hole, and curling the overhang outward. It is also illustrated and described that the plate fin is formed by using the same.
【0004】[0004]
【発明が解決しようとする課題】上記したような従来技
術においては軽量化の要求から薄板の強度を高め、その
分板厚を薄くして軽量化に即応して来たが前記した従来
の半硬質薄板における強度向上には部分焼鈍処理時の加
熱軟化曲線には安定領域がないことから加熱温度範囲が
狭く、作業性に劣ると共に品質が安定しない不利があ
る。In the prior art as described above, the strength of the thin plate has been increased in response to the demand for weight reduction, and the thickness of the thin plate has been correspondingly reduced to reduce the thickness. In order to improve the strength of a hard thin plate, there is a disadvantage that the heating temperature range is narrow because the heating softening curve at the time of the partial annealing does not have a stable region, the workability is poor, and the quality is not stable.
【0005】また上記のようにして得られた薄板は伸び
が低下し、その結果フレア加工時に割れを生じ、またエ
リクセン値が低いので張出し高さを大きく採ることがで
きず、プレートフインの軽量化に対応する半硬質薄板と
して好ましい製品を得難い欠点がある。[0005] Further, the thin plate obtained as described above has a reduced elongation, and as a result, cracks occur during flaring, and the Erichsen value is low, so that the overhang height cannot be made large and the weight of the plate fin can be reduced. There is a disadvantage that it is difficult to obtain a product which is preferable as a semi-rigid thin plate corresponding to the above.
【0006】[0006]
【課題を解決するための手段】本発明は上記したような
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、連続鋳造圧延で過飽和に固溶したMnを有するアルミ
ニウム合金コイルを冷間圧延の途中で再結晶温度未満に
加熱保持して微細なAl−Mn系金属間化合物を析出させる
ことにより爾後の部分焼鈍処理において圧延組織内に生
じた再結晶初期組織の成長を抑制することができ、この
再結晶初期組織によって部分焼鈍時の加熱軟化曲線に安
定域を形成して強度を向上してもフレアに割れを生ぜし
めないようにしたものであって、以下の如くである。SUMMARY OF THE INVENTION The present invention has been studied to solve the problems in the prior art as described above, and an aluminum alloy coil having Mn dissolved in a supersaturated state by continuous casting and rolling is formed during cold rolling. By heating and holding at a temperature lower than the recrystallization temperature to precipitate a fine Al-Mn-based intermetallic compound, it is possible to suppress the growth of the recrystallization initial structure generated in the rolled structure in the subsequent partial annealing treatment. It is a structure in which a stable region is formed in a heating softening curve at the time of partial annealing by a recrystallization initial structure so that the flare is not cracked even when the strength is improved, and is as follows.
【0007】(1)Mn:0.05〜1wt%またはMn:0.0
5〜1wt%およびMg:0.05〜0.5wt%を含有し、更に
Ti:0.001〜0.1wt%、B:0.0001〜0.02wt%
およびZr:0.001〜0.1wt%の何れか1種または2種
以上を含有させ、残部がAlと不純物とからなる板厚20
mm以下の厚さに連続鋳造圧延して得られたアルミニウム
合金コイルに対し冷間圧延の途中で中間焼鈍処理を再結
晶温度未満で行い、しかる後最終冷間圧延後の部分焼鈍
も再結晶温度未満で行うことを特徴とするアルミニウム
合金薄板の製造方法。(1) Mn: 0.05 to 1 wt% or Mn: 0.0
5-1 wt% and Mg: 0.05-0.5 wt%, and
Ti: 0.001 to 0.1 wt%, B: 0.0001 to 0.02 wt%
And Zr: one or more of 0.001 to 0.1 wt%, the balance being Al and impurities having a thickness of 20
In the middle of cold rolling, the aluminum alloy coil obtained by continuous casting and rolling to a thickness of not more than mm is subjected to intermediate annealing at a temperature lower than the recrystallization temperature, and then the partial annealing after the final cold rolling is also performed at the recrystallization temperature. A method for producing an aluminum alloy sheet.
【0008】[0008]
【作用】上記したような本発明によるものは素材の成分
組成と、製板条件、特定中間焼鈍処理、最終冷間圧延お
よび部分焼鈍の如きより成り、これらは以下の如くであ
る。According to the present invention as described above, the composition of the raw material and the conditions such as sheet making conditions, specific intermediate annealing treatment, final cold rolling and partial annealing are as follows.
【0009】Mn:0.05〜1wt%. Mnは、中間焼鈍で、Al−Mn系の微細な金属間化合物とし
て析出し、爾後の部分焼鈍において亜結晶(再結晶初期
組織)の成長を抑制して軟化の停滞する温度範囲を形成
する。0.05%未満ではそうした作用が有効に得られ
ず、一方1%超えると上記軟化停滞温度範囲での伸びが
低下して加工性が劣化する。Mn: 0.05 to 1 wt%. Mn precipitates as an Al-Mn-based fine intermetallic compound in the intermediate annealing, and suppresses the growth of subcrystals (initial recrystallized structure) in the subsequent partial annealing to form a temperature range in which softening stagnates. If it is less than 0.05%, such an effect cannot be obtained effectively, while if it exceeds 1%, elongation in the above-mentioned softening stagnation temperature range is reduced, and workability is deteriorated.
【0010】Mg:0.05〜0.5wt%. Mgを添加することによって強度を向上するが0.05wt%
未満ではその効果が乏しく、好ましい強度向上、薄肉化
が得られない。一方0.5wt%を超えると冷間圧延時の硬
化が大となり、板歪の制御が困難となり、板が波状とな
るようなことがあって好ましくない。Mg: 0.05 to 0.5 wt%. The strength is improved by adding Mg, but 0.05wt%
If it is less than 30%, the effect is poor, and desirable strength improvement and thinning cannot be obtained. On the other hand, if it exceeds 0.5% by weight, the hardening during cold rolling becomes large, and it becomes difficult to control the plate distortion, and the plate may become wavy, which is not preferable.
【0011】上記以外の元素として、Fe、Si、Cu、Cr、
Znなどは不純物元素であり、FeおよびSiは0.5wt%ま
で、Cu、Cr、Znは0.3wt%までは本発明の中間焼鈍処理
による部分焼鈍時の熱軟化曲線に対する安定化効果を妨
げることがなく、本発明の目的達成を阻害しない。As elements other than the above, Fe, Si, Cu, Cr,
Zn and the like are impurity elements, Fe and Si up to 0.5% by weight, and Cu, Cr and Zn up to 0.3% by weight hinder the stabilizing effect on the thermal softening curve at the time of partial annealing by the intermediate annealing treatment of the present invention. It does not hinder the achievement of the object of the present invention.
【0012】また結晶微細化元素は鋳造に際して割れの
発生を防止するため適宜に添加されるものであって、例
えばTi:0.001〜0.1wt%、B:0.0001〜0.02
wt%、Zr:0.001〜0.1wt%の範囲で添加し、本発明
の技術目的を有効に達成せしめる。The crystal refining element is appropriately added to prevent the occurrence of cracks during casting. For example, Ti: 0.001 to 0.1 wt%, B: 0.0001 to 0.02
wt%, Zr: 0.001 to 0.1 wt%, to effectively achieve the technical object of the present invention.
【0013】次に製板条件について説明すると、除滓処
理等を施して溶製したAl−MnまたはAl−Mn−Mg合金溶湯
をハンター法、3C法、ハザレー法などの可動鋳型方式
で連続鋳造圧延して板厚20mm以下の板を得る。これは
鋳造に際して合金溶湯を急冷凝固せしめ、Mn元素を十分
に固溶させるためのものであって、板厚が20mm以上と
なると中間焼鈍処理で充分微細なAl−Mn系化合物を得難
く、爾後の部分焼鈍処理で強度に関し温度感受性の小さ
い中間焼鈍処理材が得られない。Next, the plate making conditions will be described. The molten Al-Mn or Al-Mn-Mg alloy which has been subjected to slag removal treatment or the like is continuously cast by a movable mold method such as a hunter method, a 3C method, or a Hazaret method. Rolling is performed to obtain a plate having a thickness of 20 mm or less. This is to rapidly solidify the molten alloy at the time of casting and to sufficiently solidify the Mn element. When the plate thickness exceeds 20 mm, it is difficult to obtain a sufficiently fine Al-Mn-based compound by intermediate annealing. In the partial annealing treatment, an intermediate annealing material having a low temperature sensitivity with respect to strength cannot be obtained.
【0014】上記のようにして得られた板厚20mm以下
の連続鋳造圧延板は、最終の所望厚さを考慮して冷間圧
延するが、該冷間圧延の工程中に少くとも1回再結晶温
度未満の温度で中間焼鈍処理する。この中間焼鈍処理前
の冷間圧延は部分焼鈍時の加熱軟化曲線に安定領域を得
るために必要であって、この冷間圧延量は例えば前記ハ
ンター法では圧下率で30%位あればよい。The continuous cast rolled plate having a thickness of 20 mm or less obtained as described above is cold-rolled in consideration of the final desired thickness, but is re-rolled at least once during the cold-rolling process. Intermediate annealing treatment is performed at a temperature lower than the crystallization temperature. The cold rolling before the intermediate annealing treatment is necessary to obtain a stable region in the heating softening curve at the time of the partial annealing, and the amount of the cold rolling may be, for example, about 30% as the rolling reduction in the Hunter method.
【0015】前記した再結晶温度未満における中間焼鈍
処理は上記処理前冷間圧延と相俟って連続鋳造圧延で過
飽和に固溶していたMn元素をAl−Mn系の微細化合物とし
て析出させ、爾後の部分焼鈍処理において圧延組織内に
生じた亜結晶の成長を抑制し、部分焼鈍時の加熱軟化曲
線に上述したような安定領域をつくると共に部分焼鈍材
の強度と加工性を向上させるためのものである。中間焼
鈍時に再結晶させるとフレア加工時にフレア時に肌荒れ
を起し、加工性が損われる。The intermediate annealing treatment at a temperature lower than the recrystallization temperature, together with the cold rolling before the treatment, precipitates the super-saturated solid solution Mn element as a fine Al-Mn compound by continuous casting and rolling. In order to suppress the growth of subcrystals generated in the rolled structure in the subsequent partial annealing treatment, to create the above-mentioned stable region in the heating softening curve during partial annealing, and to improve the strength and workability of the partially annealed material. Things. If recrystallization is performed during intermediate annealing, the surface becomes rough during flare during flaring, and the workability is impaired.
【0016】一般に再結晶温度は処理材の履歴によって
一定しないが、本発明の場合は350〜400℃位であ
るから、350℃以下とするのが確実で、好ましい。ま
たこの加熱下限温度は処理材の回復温度近傍で約250
℃であり、加熱時間は1〜24時間が適当である。In general, the recrystallization temperature is not constant depending on the history of the processing material. However, in the case of the present invention, the recrystallization temperature is about 350 to 400 ° C., so it is preferable and certainly set to 350 ° C. or less. The heating lower limit temperature is about 250 around the recovery temperature of the processing material.
C., and a suitable heating time is 1 to 24 hours.
【0017】上記のようにして中間焼鈍処理された板材
は所望の厚さまで冷間圧延され、その後部分焼鈍処理さ
れる。この最終冷間圧延の圧下率は部分焼鈍処理後の板
材品質を安定化するためには50%以上、好ましくは8
0%以上とするのがよい。The sheet material that has been subjected to intermediate annealing as described above is cold-rolled to a desired thickness, and then subjected to partial annealing. The rolling reduction of the final cold rolling is 50% or more, preferably 8%, in order to stabilize the sheet material quality after the partial annealing.
It is better to be 0% or more.
【0018】前記のように冷間圧延されて目的の板厚と
された硬質薄板は部分焼鈍によって製品とされるが、こ
の部分焼鈍も再結晶温度未満であって、一般的に250
〜360℃程度の温度範囲で1〜12時間、所望する半
硬質薄板の性質に即応させて実施する。このような部分
焼鈍によって伸びやエリクセン値が共に高く、しかも強
度(抗張力)において優れたものが得られ、再結晶温度
以下であることからエリクセン時の肌荒れも少いものと
なる。The hard thin plate which has been cold rolled to a desired thickness as described above is made into a product by partial annealing. This partial annealing is also performed at a temperature lower than the recrystallization temperature.
It is carried out in a temperature range of about 360 ° C. for 1 to 12 hours in accordance with the desired properties of the semi-rigid thin plate. By such partial annealing, both high elongation and Erichsen value and excellent strength (tensile strength) can be obtained, and since the recrystallization temperature is lower than the recrystallization temperature, the surface roughness during Erichsen is also small.
【0019】[0019]
【実施例】上記したような本発明によるものの具体的な
実施例について説明すると、先ず本発明者等が用いた本
発明によるAl−Mn合金、Al−Mn−Mg合金および比較例と
してのAl−Fe−Si合金(1100合金)の組成は次の表
1に示す如くである。DESCRIPTION OF THE PREFERRED EMBODIMENTS Specific examples of the present invention as described above will be described. First, an Al-Mn alloy, an Al-Mn-Mg alloy according to the present invention, and an Al-Mn alloy as a comparative example used by the present inventors. The composition of the Fe-Si alloy (1100 alloy) is as shown in Table 1 below.
【0020】[0020]
【表1】 [Table 1]
【0021】表1に示したA、B、Cの各合金は何れも
ハンター連続鋳造圧延機を用い、厚さ6.8mmのアルミニ
ウムコイルを製造し、これらの各コイルを次の表2に示
すような製板工程に従って0.115mm厚の薄板を作成
し、抗張力、伸び、エリクセン値を測定すると共にエリ
クセン時の肌荒れを検討した結果は表3に示す如くであ
った。即ち、本発明のものは、比較例に比し抗張力、伸
び、エリクセン値のバランスの優れた特性を有すること
が明かである。また、加工性にも優れ、品質的にも安定
していることが判る。Each of the alloys A, B, and C shown in Table 1 was manufactured using a Hunter continuous casting and rolling mill to produce aluminum coils having a thickness of 6.8 mm. These coils are shown in Table 2 below. A thin plate having a thickness of 0.115 mm was prepared according to the above plate making process, and the tensile strength, elongation and Erichsen value were measured, and the surface roughness during Erichsen was examined. The results are shown in Table 3. That is, it is clear that the product of the present invention has excellent properties in balance of tensile strength, elongation and Erichsen value as compared with the comparative example. Also, it is found that the workability is excellent and the quality is stable.
【0022】[0022]
【表2】 [Table 2]
【0023】[0023]
【表3】 [Table 3]
【0024】添附図面には前記した表3の本発明例B
1、2と従来の製造法によるB6、即ち中間焼鈍として
530℃×2hrを実施した比較例について最終焼鈍温度
の変化に対する抗張力と伸びの変化を併せて示す。本発
明によるものは250〜350℃程度での間に抗張力に
関し変化の小さいところがあり温度感受性が鈍く、従っ
て熱処理作業が容易で品質の安定したものが得られるこ
とが判る。The accompanying drawings show Example B of the present invention in Table 3 described above.
Changes in tensile strength and elongation with respect to changes in final annealing temperature are also shown for Comparative Examples 1 and 2 and B6 by a conventional production method, that is, Comparative Examples in which 530 ° C. × 2 hours were performed as intermediate annealing. It can be seen that the sample according to the present invention has a small change in tensile strength between about 250 ° C. and 350 ° C. and has low temperature sensitivity, so that a heat treatment operation is easy and a product of stable quality can be obtained.
【0025】[0025]
【発明の効果】以上説明したような本発明によるときは
部分焼鈍処理の温度範囲が広くて作業性に優れ、しかも
成形性と強度において共に卓越していてプレートフイン
型熱交換器用フインやキャップ、アルミ缶ないしアルミ
箔などとして好ましい製品を得しめることができるもの
であって、工業的にその効果の大きい発明である。According to the present invention as described above, the temperature range of the partial annealing treatment is wide, the workability is excellent, and the formability and strength are both excellent, and the fins and caps for plate-fin type heat exchangers are used. It is an invention which can obtain a product which is preferable as an aluminum can or an aluminum foil, and has a large industrial effect.
【図1】本発明による実施例B1、2と従来法による比
較例B6のものについて最終焼鈍温度の変化に対する抗
張力と伸びの変化を要約して示した図表である。FIG. 1 is a table summarizing changes in tensile strength and elongation with respect to changes in final annealing temperature for Examples B1 and 2 according to the present invention and Comparative Example B6 according to a conventional method.
フロントページの続き (51)Int.Cl.7 識別記号 FI C22F 1/04 C22F 1/04 C (58)調査した分野(Int.Cl.7,DB名) C22F 1/00 - 1/18 C22C 21/00 - 21/18 Continuation of the front page (51) Int.Cl. 7 identification code FI C22F 1/04 C22F 1/04 C (58) Field surveyed (Int.Cl. 7 , DB name) C22F 1/00-1/18 C22C 21 / 00-21/18
Claims (1)
1wt%およびMg:0.05〜0.5wt%を含有し、更にTi:
0.001〜0.1wt%、B:0.0001〜0.02wt%およ
びZr:0.001〜0.1wt%の何れか1種または2種以上
を含有させ、残部がAlと不純物とからなる板厚20mm以
下の厚さに連続鋳造圧延して得られたアルミニウム合金
コイルに対し冷間圧延の途中で中間焼鈍処理を再結晶温
度未満で行い、しかる後最終冷間圧延後の部分焼鈍も再
結晶温度未満で行うことを特徴とするアルミニウム合金
薄板の製造方法。1. Mn: 0.05 to 1 wt% or Mn: 0.05 to 1 wt%
1 wt% and Mg: 0.05-0.5 wt%, and further Ti:
0.001 to 0.1% by weight, B: 0.0001 to 0.02% by weight, and Zr: 0.001 to 0.1% by weight, and the balance consists of Al and impurities. In the course of cold rolling, an intermediate annealing treatment is performed at a temperature lower than the recrystallization temperature on the aluminum alloy coil obtained by continuous casting and rolling to a thickness of 20 mm or less, and then the partial annealing after the final cold rolling is also performed. A method for producing an aluminum alloy sheet, which is performed at a temperature lower than a recrystallization temperature.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP06477593A JP3161141B2 (en) | 1993-03-02 | 1993-03-02 | Manufacturing method of aluminum alloy sheet |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP06477593A JP3161141B2 (en) | 1993-03-02 | 1993-03-02 | Manufacturing method of aluminum alloy sheet |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH06256916A JPH06256916A (en) | 1994-09-13 |
JP3161141B2 true JP3161141B2 (en) | 2001-04-25 |
Family
ID=13267927
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP06477593A Expired - Fee Related JP3161141B2 (en) | 1993-03-02 | 1993-03-02 | Manufacturing method of aluminum alloy sheet |
Country Status (1)
Country | Link |
---|---|
JP (1) | JP3161141B2 (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN102642001A (en) * | 2012-04-28 | 2012-08-22 | 江苏鑫皇铝业发展有限公司 | Electromagnetic casting process for 5754 aluminum alloy |
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JP5090777B2 (en) * | 2007-04-24 | 2012-12-05 | 東洋アルミニウム株式会社 | Aluminum foil |
JP5233568B2 (en) * | 2008-10-14 | 2013-07-10 | 日本軽金属株式会社 | Aluminum alloy plate excellent in heat resistance and formability and manufacturing method thereof |
ES2568280T3 (en) * | 2009-04-24 | 2016-04-28 | Hydro Aluminium Rolled Products Gmbh | Aluminum band rich in manganese and magnesium |
CN105369074B (en) * | 2015-11-18 | 2018-02-09 | 安徽枫慧金属股份有限公司 | A kind of air-conditioner foil aluminum alloy plate materials |
WO2020189674A1 (en) | 2019-03-18 | 2020-09-24 | 東洋アルミニウム株式会社 | Aluminum alloy foil, laminate, method for manufacturing aluminum alloy foil, and method for manufacturing laminate |
CN113073236A (en) * | 2021-03-17 | 2021-07-06 | 内蒙古联晟新能源材料有限公司 | Preparation method of wide-width double-zero-foil blank manufactured by continuous casting and rolling method |
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CN102642001A (en) * | 2012-04-28 | 2012-08-22 | 江苏鑫皇铝业发展有限公司 | Electromagnetic casting process for 5754 aluminum alloy |
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