JP2003268476A - Aluminum alloy for quench welding, and welding method therefor - Google Patents
Aluminum alloy for quench welding, and welding method thereforInfo
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- JP2003268476A JP2003268476A JP2002259797A JP2002259797A JP2003268476A JP 2003268476 A JP2003268476 A JP 2003268476A JP 2002259797 A JP2002259797 A JP 2002259797A JP 2002259797 A JP2002259797 A JP 2002259797A JP 2003268476 A JP2003268476 A JP 2003268476A
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- strength
- quench
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、圧延材、押出し材
など溶接構造材、自動車用アルミ薄板材など、レーザ溶
接等の急冷溶接をして用いられる用途のアルミニウム合
金に関する。具体的には、溶接部で軟化することなく、
高い溶接継手強度を確保できる急冷溶接用アルミニウム
合金およびその溶接方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an aluminum alloy for use as a welded structural material such as a rolled material, an extruded material, an aluminum thin plate material for automobiles, etc., which is used by quenching welding such as laser welding. Specifically, without softening at the weld,
TECHNICAL FIELD The present invention relates to an aluminum alloy for quenching welding capable of ensuring high weld joint strength and a welding method thereof.
【０００２】[0002]
【従来の技術】アルミニウム合金は鉄鋼材料に比べて軽
量であり、構造体の軽量化に有効であることから自動
車、鉄道車両、船舶などに広く使用されるようになって
きた。構造部材は溶接によって組み立てられるため溶接
継ぎ手効率、すなわち溶接継ぎ手強度／母材強度は100%
以上であることが望ましい。アルミニウム合金の中では
ＪＩＳ６０００系に代表される熱処理型合金は高強度で
あるが、溶接した場合は溶接入熱によって析出物が溶体
化してしまうため溶接部が軟化し、後熱処理が必要にな
ってくる。一方、Mgにより強化を図った非熱処理型のＪ
ＩＳ Ａ５０００系合金はＡ６０００系アルミニウム合
金に比べて強度低下は少ないものの、溶接入熱によって
焼鈍され、結晶粒の粗大化に伴う強度低下によって溶接
継ぎ手効率は100%を切る場合が多い。このため、Mg含有
量を増加させる手法や、特開平10-237577号公報に見ら
れるように、Scを加えて強度の上昇を図る技術などが検
討されてきた。しかしながらScによる強度上昇は、Scの
材料自体が高価であるためコスト面での問題があり、ま
たMg含有量の増加は溶接部の高強度化に有効であるもの
の、所定の含有量以上を加えた場合、熱間加工性の低下
を招くためおのずと限界があった。2. Description of the Related Art Aluminum alloys are lighter in weight than steel materials and are effective in reducing the weight of structures. Therefore, aluminum alloys have come to be widely used in automobiles, railway vehicles, ships and the like. Since structural members are assembled by welding, weld joint efficiency, that is, weld joint strength / base metal strength is 100%
The above is desirable. Among the aluminum alloys, the heat treatment type alloys represented by JIS6000 series have high strength, but when welding, the welded portion becomes a solution due to welding heat input, so the welded portion softens and post heat treatment becomes necessary. come. On the other hand, a non-heat treated J reinforced with Mg
Although the IS A5000 series alloy has less strength reduction than the A6000 series aluminum alloy, it is often annealed by welding heat input, and the strength of the weld joint is often less than 100% due to the strength decrease due to coarsening of crystal grains. For this reason, techniques for increasing the Mg content, techniques for increasing the strength by adding Sc, as seen in JP-A-10-237577, have been studied. However, the increase in strength due to Sc has a problem in terms of cost because the material itself of Sc is expensive, and although the increase in the Mg content is effective for increasing the strength of the welded portion, the addition of a predetermined content or more is required. However, in that case, there is a limit because the hot workability is deteriorated.
【０００３】[0003]
【特許文献１】特開平１０−２３７５５７号公報（第１
頁[Patent Document 1] Japanese Unexamined Patent Publication No. 10-237557 (first
page
【０００４】[0004]
【発明が解決しようとする課題】本発明は、以上の事情
を背景にしてなされたものであり、レーザ溶接などのよ
うな急速な冷却がなされる溶接方法において、その溶接
部強度、すなわち溶接金属と溶接熱影響部の強度をMg含
有量の増加に頼らずに増加させ、継ぎ手効率を100%以上
に確保できる急冷溶接用アルミニウム合金およびその溶
接方法を提供することを課題とする。The present invention has been made in view of the above circumstances, and in a welding method such as laser welding in which rapid cooling is performed, the strength of the welded portion, that is, the weld metal. Another object of the present invention is to provide an aluminum alloy for quenching welding, which can increase the strength of the heat-affected zone of the welding without depending on the increase of the Mg content, and can secure the joint efficiency at 100% or more, and a welding method thereof.
【０００５】[0005]
【課題を解決するための手段】本発明は、溶接時の冷却
速度と溶接金属の硬さ変化について各種アルミニウム合
金について調査した結果、レーザ溶接のような冷却速度
の速い溶接方法においてはMn、Cr、Fe、V、Zr、Niの含
有量を所定の値以上にすることによって溶接部の硬さを
上昇させることができ、その結果溶接部強度を母材以上
の値にすることができることを見出し、本発明をなすに
至ったものである。すなわち、本発明の要旨は下記のと
おりである。According to the present invention, as a result of investigating various aluminum alloys with respect to a cooling rate at the time of welding and a change in hardness of weld metal, Mn and Cr are used in a welding method having a high cooling rate such as laser welding. It was found that the hardness of the weld can be increased by increasing the content of Fe, V, Zr, and Ni to a predetermined value or higher, and as a result, the weld strength can be made higher than the base metal. The present invention has been completed. That is, the gist of the present invention is as follows.
【０００６】（１）質量％で、Mg：０．４〜７．０％、
Cu：０．０５〜１％を含有し、さらに、Mn：０．８〜
２．５％、Cr：０．３５〜２．０％、Fe：０．７〜１．
５％のうち１種または２種以上を含有し、残部Alおよび
不可避的不純物からなることを特徴とする急冷溶接用ア
ルミニウム合金。
（２）質量％で、V ：０．５〜１．０％、Zr：２．０〜
２．５％、Ni：３．０〜３．５％のうち１種または２種
以上を含有することを特徴とする（１）記載の急冷溶接
用アルミニウム合金。
（３）（１）または（２）に記載のアルミニウム合金の
溶接方法において、溶接後、溶接部を融点から200℃ま
で平均冷却速度500〜10000℃／秒で冷却することを特徴
とする急冷溶接用アルミニウム合金の溶接方法。(1) In mass%, Mg: 0.4 to 7.0%,
Cu: 0.05 to 1%, and Mn: 0.8 to
2.5%, Cr: 0.35 to 2.0%, Fe: 0.7 to 1.
An aluminum alloy for quenching welding, characterized by containing one or more of 5% and the balance Al and unavoidable impurities. (2) In mass%, V: 0.5 to 1.0%, Zr: 2.0 to
2.5%, Ni: 3.0-3.5%, 1 type (s) or 2 or more types are contained, The aluminum alloy for rapid-quenching welding of (1) characterized by the above-mentioned. (3) In the method for welding an aluminum alloy according to (1) or (2), after the welding, the welded part is cooled from the melting point to 200 ° C at an average cooling rate of 500 to 10000 ° C / sec. Welding method for aluminum alloys.
【０００７】[0007]
【発明の実施の形態】以下に本発明を詳細に説明する。
本発明は、溶接用アルミニウム合金およびその溶接方法
であるが、溶接金属の強度を増加させるために所定量の
Mn、Cr、Feの１種または２種以上を含有することを特徴
とする。以下に各合金元素の役割とその限定理由につい
て説明する。BEST MODE FOR CARRYING OUT THE INVENTION The present invention is described in detail below.
The present invention is an aluminum alloy for welding and a welding method thereof, but in order to increase the strength of the weld metal,
It is characterized by containing one or more of Mn, Cr and Fe. The role of each alloying element and the reason for the limitation will be described below.
【０００８】Mgは、本発明の合金の基本成分であり、母
材および溶接金属の強度を確保および耐溶接割れ性のた
めに必要である。含有量を０．４〜７．０％にする理由
は、０．４％未満では十分な強度が得られず、一方、
７．０％を超えると高温変形抵抗が増大し始める結果、
熱間加工性が低下するためである。Cuは、合金板の強度
を高め、耐応力腐食割れ性に有効な元素であるが、０．
０５％未満では効果が無く、１％を超えると一般的な耐
食性が劣化する。よって０．０５〜１．０％とした。Mn
は、本発明で対象としている系の合金で基本となる元素
である。本元素は母材の強度確保にも有効である。母材
中に固溶状態および晶出物（MnAl6）として存在する
が、溶接を行った際にこの晶出物は全て溶解し、冷却過
程で凝固する。この際に、レーザ溶接の様な冷却速度の
速い溶接方法の場合は、一旦溶接金属中に溶解したMnは
凝固・冷却後に晶出することなく過飽和固溶の状態で残
存する。すなわち、冷却速度の増大によって固溶限の拡
大を図ることができ、著しい硬さの上昇が起こるのであ
る。この理由から、レーザ溶接のような冷却速度の速い
溶接継手に対しては強度の上昇に有効となるのである。
含有量を０．８〜２．５％にする理由は、０．８％未満
では急冷による過飽和固溶強化が十分に得られず、硬さ
の上昇は生じない。また２．５％を超えると粗大な晶出
物となって析出し、加工性を劣化させるためである。Mg is a basic component of the alloy of the present invention, and is necessary for ensuring the strength of the base metal and the weld metal and for the resistance to weld cracking. The reason for setting the content to 0.4 to 7.0% is that if the content is less than 0.4%, sufficient strength cannot be obtained.
When it exceeds 7.0%, high temperature deformation resistance starts to increase,
This is because the hot workability is reduced. Cu is an element that enhances the strength of the alloy plate and is effective for the resistance to stress corrosion cracking.
If it is less than 05%, there is no effect, and if it exceeds 1%, general corrosion resistance deteriorates. Therefore, it is set to 0.05 to 1.0%. Mn
Is a basic element in the alloy of the system targeted by the present invention. This element is also effective in securing the strength of the base material. It exists as a solid solution and crystallized substances (MnAl 6 ) in the base metal, but all these crystallized substances melt during welding and solidify during the cooling process. At this time, in the case of a welding method having a high cooling rate such as laser welding, Mn once melted in the weld metal remains in a supersaturated solid solution state without crystallizing after solidification and cooling. That is, the solid solubility limit can be increased by increasing the cooling rate, and the hardness is remarkably increased. For this reason, it is effective for increasing the strength of a welded joint having a high cooling rate such as laser welding.
The reason for setting the content to 0.8 to 2.5% is that if it is less than 0.8%, supersaturated solid solution strengthening by quenching cannot be sufficiently obtained, and hardness does not increase. Further, if it exceeds 2.5%, coarse crystallized substances are deposited and the workability is deteriorated.
【０００９】Crは、Mnと同様に本発明におけるアルミニ
ウム合金の基本元素である。Mnの場合と同様に、母材中
に固溶状態および化合物（CrAl7）の状態で存在する
が、レーザ溶接の様な冷却速度の速い溶接の場合、溶接
金属中に溶解したCrが凝固・冷却課程でも晶出せずに過
飽和のまま室温に至る。その結果、固溶強化に基づく強
化が起こり、硬さは著しく上昇する。含有量を０．３５
〜２．０％にする理由は、０．３５％未満では急冷によ
る過飽和固溶強化の効果が得られず、２．０％を超える
とMn場合と同様に粗大な晶出物となって析出して加工性
を劣化させるためである。Feは、Cr、Mnとともに本発明
におけるアルミニウム合金の基本元素である。Feは母材
中にはほとんど固溶しないが、溶接金属中に溶解し、過
飽和に固溶する結果、固さの上昇に寄与する。Feの範囲
としては、０．７％未満ではその効果が現れず、１．５
％を超えると成型性を阻害する。従って、０．７％以
上、１．５％以下とする。Cr, like Mn, is a basic element of the aluminum alloy of the present invention. As in the case of Mn, it exists in a solid solution state and compound (CrAl 7 ) state in the base metal, but in the case of welding with a high cooling rate such as laser welding, Cr dissolved in the weld metal solidifies and It does not crystallize even in the cooling process and reaches room temperature with supersaturation. As a result, strengthening based on solid solution strengthening occurs, and the hardness significantly increases. Content of 0.35
The reason for setting the content to ~ 2.0% is that if it is less than 0.35%, the effect of supersaturated solid solution strengthening by rapid cooling cannot be obtained, and if it exceeds 2.0%, coarse crystallized substances are precipitated as in the case of Mn. This is because the workability is deteriorated. Fe is a basic element of the aluminum alloy in the present invention together with Cr and Mn. Fe hardly dissolves in the base metal, but dissolves in the weld metal and becomes a supersaturated solution, which contributes to an increase in hardness. If the Fe content is less than 0.7%, the effect does not appear, and
If it exceeds%, the moldability is impaired. Therefore, it is set to 0.7% or more and 1.5% or less.
【００１０】さらに必要に応じて、V、Zr、Niを所定量
添加しても良い。V、Zr、Niも溶接後の溶接部の強度上
昇に寄与する元素であり、また母材の強度確保や結晶粒
径の粗大化抑制にも有効である。V、Zr、Niは母材への
固溶限が小さく、金属間化合物を形成しているが、Mn、
CrおよびFeと同様に、レーザ溶接の様な冷却速度の速い
溶接の場合、溶接金属中に溶解して凝固・冷却課程でも
晶出せずに過飽和のまま室温に至り、固溶強化によって
硬さが著しく上昇する。成分範囲をそれぞれ、V：０．
５〜１．０％、Zr：２．０〜２．５％、Ni：３．０〜
３．５％としたのは、V：０．５％未満、Zr：２．０％
未満、Ni：３．０％未満では、強度上昇効果が不十分で
あり、V：１．０％超、Zr：２．５％超、Ni：３．５％
超では母材中に粗大な晶出物が形成され、母材の加工性
を著しく損なってしまうためである。Further, if necessary, V, Zr and Ni may be added in predetermined amounts. V, Zr, and Ni are also elements that contribute to increasing the strength of the welded part after welding, and are also effective in securing the strength of the base metal and suppressing the coarsening of the crystal grain size. V, Zr, and Ni have small solid solubility in the base material and form intermetallic compounds, but Mn,
Similar to Cr and Fe, in the case of welding with a high cooling rate such as laser welding, it melts in the weld metal and does not crystallize even in the solidification / cooling process and reaches room temperature at supersaturation. It rises significantly. The component ranges are V: 0.
5 to 1.0%, Zr: 2.0 to 2.5%, Ni: 3.0 to
3.5% is V: less than 0.5%, Zr: 2.0%
%, Ni: less than 3.0%, the strength increasing effect is insufficient, V: more than 1.0%, Zr: more than 2.5%, Ni: 3.5%
This is because if it exceeds the above range, coarse crystallized substances are formed in the base material and the workability of the base material is significantly impaired.
【００１１】溶接後、溶接部を融点から200℃まで平均
冷却速度500℃／秒未満で冷却すると、母材中に、強化
に対する寄与が小さい粗大な析出物を生じて、固溶強化
が不十分になり、継手効率が低下するためである。ま
た、レーザ溶接などの急冷溶接によっても10000℃／秒
を超える冷却速度を得ることは極めて困難である。した
がって、溶接後、融点から200℃までの平均の冷却速度
を500〜10000℃／秒の範囲とした。さらに優れた特性を
有する溶接金属とするためには、融点から200℃まで100
0〜8000℃／秒の範囲で冷却することが好ましい。After the welding, when the welded portion is cooled from the melting point to 200 ° C. at an average cooling rate of less than 500 ° C./sec, coarse precipitates having a small contribution to strengthening are formed in the base metal, and solid solution strengthening is insufficient. This is because the joint efficiency decreases. Further, it is extremely difficult to obtain a cooling rate exceeding 10,000 ° C./second even by quenching welding such as laser welding. Therefore, after welding, the average cooling rate from the melting point to 200 ° C. was set in the range of 500 to 10000 ° C./sec. In order to obtain a weld metal with even more excellent properties, 100 from the melting point to 200 ° C
It is preferable to cool in the range of 0 to 8000 ° C./second.
【００１２】[0012]
【実施例】＜実施例１＞本発明の実施例について詳細に
説明する。表１に示す組成の本発明例合金（No．１〜
５）と比較例合金（No．６〜８）とをそれぞれ作製して
調査した。ここで、No．１〜４でMn、Crの影響、No．５
でFeの影響を調べる目的で作製している。これらの合金
は、溶解後に、鋳造・面削し、その後550℃１０時間の
均質化処理を行って熱間圧延し、さらに冷間圧延−中間
焼鈍−冷間圧延を行い、最後に最終焼鈍を行って板厚
２．０mmの合金板を作製した。得られた合金板について
表２に示す条件でレーザ溶接を行い、溶接部の特性を調
べた。硬さ分布は、荷重１００ｇｆの条件でビッカース
硬さ計にて測定した。溶接後の継手温度が融点から200
℃までの平均の冷却速度は、レーザ溶接などの急冷溶接
における好ましい範囲である500〜10000℃／秒とした。EXAMPLES Example 1 An example of the present invention will be described in detail. Inventive example alloys having compositions shown in Table 1 (No. 1 to No. 1)
5) and comparative alloys (Nos. 6 to 8) were prepared and investigated. Here, No. No. 1 to 4 influence of Mn and Cr 5
It is made for the purpose of investigating the influence of Fe. After melting, these alloys are cast and faced, homogenized at 550 ° C. for 10 hours, hot-rolled, further cold-rolled-intermediate-annealed-cold-rolled and finally subjected to final annealing. Then, an alloy plate having a plate thickness of 2.0 mm was prepared. The obtained alloy plate was laser-welded under the conditions shown in Table 2 and the characteristics of the welded portion were examined. The hardness distribution was measured with a Vickers hardness meter under the condition of a load of 100 gf. The joint temperature after welding is 200 from the melting point
The average cooling rate up to ° C was set to 500 to 10000 ° C / sec, which is a preferable range in quenching welding such as laser welding.
【００１３】引張特性は溶接部を含んだJIS５号の引張
り試験片を作成し、インストロンタイプの引張試験機に
よって引張強さおよび破断位置を求めた。その結果を表
３に示すが、本発明例の１〜５の合金はいずれも母材に
比べて硬さの上昇が見られており、引張試験において
も、破断位置すべて母材となっており、優れた継手強度
を示していることが分かる。本発明においてはレーザ溶
接における効果の例を示したが、スポット溶接や半導体
レーザ溶接においても、レーザ溶接と同様に溶接後の冷
却速度は速いことから同様の効果が得られる。For tensile properties, a JIS No. 5 tensile test piece including a welded portion was prepared, and the tensile strength and fracture position were determined by an Instron type tensile tester. The results are shown in Table 3, and all of the alloys 1 to 5 of the present invention show an increase in hardness as compared with the base metal, and even in the tensile test, all the fracture positions are the base metal. It can be seen that it shows excellent joint strength. Although the example of the effect in the laser welding is shown in the present invention, the same effect can be obtained in the spot welding and the semiconductor laser welding because the cooling rate after the welding is high similarly to the laser welding.
【００１４】＜実施例２＞表４に示す組成の本発明合金
（No．９〜１６）をそれぞれ作製して調査した。これら
の合金を実施例１と同様な製造条件で厚さ２．０ｍｍの
合金板とした。得られた合金板について表２に示す条件
でレーザー溶接を行い、引張強さおよび破断位置を実施
例１と同様な方法で調べた。その結果を表５に示す。合
金９〜１６はいずれも母材で破断しており、V、Zr、Ni
の添加によりさらに優れた継手強度を示していることが
わかる。Example 2 Alloys of the present invention (Nos. 9 to 16) having the compositions shown in Table 4 were prepared and investigated. These alloys were made into alloy plates with a thickness of 2.0 mm under the same manufacturing conditions as in Example 1. The obtained alloy sheet was laser-welded under the conditions shown in Table 2 and the tensile strength and the fracture position were examined by the same method as in Example 1. The results are shown in Table 5. Alloys 9 to 16 are fractured in the base material, and V, Zr, Ni
It can be seen that the addition of Al shows even better joint strength.
【００１５】[0015]
【発明の効果】本発明によれば、レーザ溶接などのよう
な急速な冷却がなされる溶接方法において、その溶接部
強度、すなわち溶接金属と溶接熱影響部の強度をMg含有
量の増加に頼らずに増加させ、継ぎ手効率を100%以上に
確保できる急冷溶接用アルミニウム合金およびその溶接
方法を提供することができる。具体的には、本発明のア
ルミニウム合金はレーザ溶接部の継手強度が高く、軟化
部を含まないため、従来問題となっていた溶接部におけ
る軟化部に伴う溶接部での破断が解消でき、溶接構造
体、あるいは溶接部を含む成型加工用途向けの素材とし
て有効であり、産業上有用な著しい効果を奏する。According to the present invention, in a welding method such as laser welding in which rapid cooling is performed, the strength of the weld, that is, the strength of the weld metal and the heat-affected zone of the weld depends on the increase of the Mg content. It is possible to provide an aluminum alloy for quenching welding and a welding method thereof which can be increased without increasing the efficiency of the joint to 100% or more. Specifically, the aluminum alloy of the present invention has a high joint strength of the laser welded portion and does not include a softened portion, so that the fracture at the welded portion associated with the softened portion in the conventional welded portion can be eliminated, It is effective as a structural body or a material for molding processing including welded parts, and has a remarkable industrially useful effect.
【表１】 [Table 1]
【表２】 [Table 2]
【表３】 [Table 3]
【表４】 [Table 4]
【表５】 [Table 5]
───────────────────────────────────────────────────── フロントページの続き (72)発明者 佐賀 誠 千葉県富津市新富20−１ 新日本製鐵株式 会社技術開発本部内 (72)発明者 一山 靖友 千葉県富津市新富20−１ 新日本製鐵株式 会社技術開発本部内 (72)発明者 浮穴 俊康 東京都千代田区大手町２−６−３ 新日本 製鐵株式会社内 (72)発明者 園田 弘文 千葉県習志野市東習志野７丁目６番１号 日鐵溶接工業株式会社機器・オプト事業部 内 (72)発明者 衣袋 順一 千葉県習志野市東習志野７丁目６番１号 日鐵溶接工業株式会社機器・オプト事業部 内 (72)発明者 矢羽々 隆憲 埼玉県和光市中央１丁目４番１号 株式会 社本田技術研究所内 (72)発明者 瀧川 正人 埼玉県和光市中央１丁目４番１号 株式会 社本田技術研究所内 Ｆターム(参考） 4E068 BA00 CA13 DB04 ─────────────────────────────────────────────────── ─── Continued front page (72) Inventor Makoto Saga 20-1 Shintomi, Futtsu-shi, Chiba Nippon Steel shares Company Technology Development Division (72) Inventor Yasutomo Ichiyama 20-1 Shintomi, Futtsu-shi, Chiba Nippon Steel shares Company Technology Development Division (72) Inventor Toshiyasu Ukiana 2-6-3 Otemachi, Chiyoda-ku, Tokyo New Japan Steelmaking Co., Ltd. (72) Inventor Hirofumi Sonoda 7-6-1, Higashi Narashino, Narashino, Chiba Prefecture Nittetsu Welding Industry Co., Ltd. Within (72) Inventor, Junichi 7-6-1, Higashi Narashino, Narashino, Chiba Prefecture Nittetsu Welding Industry Co., Ltd. Within (72) Inventor Takanori Yaba 1-4-1 Chuo Stock Market, Wako City, Saitama Prefecture Inside Honda Research Laboratory (72) Inventor Masato Takigawa 1-4-1 Chuo Stock Market, Wako City, Saitama Prefecture Inside Honda Research Laboratory F-term (reference) 4E068 BA00 CA13 DB04
Claims (3)
避的不純物からなることを特徴とする急冷溶接用アルミ
ニウム合金。1. In mass%, Mg: 0.4-7.0%, Cu: 0.05-1% are contained, Mn: 0.8-2.5%, Cr: 0.35 ˜2.0%, Fe: 0.7 to 1.5%, one or more kinds, and the balance Al and unavoidable impurities, an aluminum alloy for rapid cooling welding.
請求項１記載の急冷溶接用アルミニウム合金。2. In mass%, one or more of V: 0.5 to 1.0%, Zr: 2.0 to 2.5%, and Ni: 3.0 to 3.5% are used. The aluminum alloy for quench welding according to claim 1, wherein the aluminum alloy is contained.
合金の溶接方法において、溶接後、溶接部を融点から20
0℃まで平均冷却速度500〜10000℃／秒で冷却すること
を特徴とする急冷溶接用アルミニウム合金の溶接方法。3. The method of welding an aluminum alloy according to claim 1, wherein the welded portion is melted at a temperature of 20 to 20 ° C. after welding.
A method for welding an aluminum alloy for quenching welding, which comprises cooling to 0 ° C at an average cooling rate of 500 to 10000 ° C / sec.
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| JP2017110272A (en) * | 2015-12-17 | 2017-06-22 | 株式会社Uacj | Al ALLOY MATERIAL FOR HIGH ENERGY BEAM WELDMENT AND MANUFACTURING METHOD THEREFOR |
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