JP3754946B2 - Aluminum alloy for welding and welding method thereof - Google Patents
Aluminum alloy for welding and welding method thereof Download PDFInfo
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Description
【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溶接用アルミニウム合金およびその溶接方法に関する。
【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ＪＩＳ 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。
【０００３】
【特許文献１】
特開平１０−２３７５５７号公報（第１頁
【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。
【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。
【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、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溶接用アルミニウム合金。
（２）（１）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５００〜１０００℃／秒で冷却することを特徴とする溶接用アルミニウム合金の溶接方法。
【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。
【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。
【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。
【００１０】
さらに、Ｖ、Ｚｒ、Ｎｉを所定量添加する。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効果がある。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・冷却過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。
【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1000〜8000℃／秒の範囲で冷却することが好ましい。
【００１２】
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.１〜８）と比較合金（Ｎ o. ９〜１１）とをそれぞれ作製して調査した。これらの合金は、溶解後に、鍛造・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。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。
【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Ｎ o. １〜８の合金はいずれも母材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ようせつにおいても、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。
【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。
【表１】
BACKGROUND OF THE INVENTION
The present invention relates to an aluminum alloy that is used by performing rapid welding such as laser welding, such as a welded structural material such as a rolled material and an extruded material, and an aluminum thin plate material for automobiles. Specifically, the present invention relates to an aluminum alloy for welding that can secure high weld joint strength without softening at a welded portion, and a welding method thereof.
[0002]
[Prior art]
Aluminum alloys are lighter than steel materials and are effective in reducing the weight of structures, so they have been widely used in automobiles, railway vehicles, ships, and the like. Since the structural members are assembled by welding, it is desirable that the weld joint efficiency, that is, the weld joint strength / base material strength is 100% or more. Among aluminum alloys, heat treatment type alloys represented by JIS 6000 series have high strength, but when welded, precipitates are melted by welding heat input, so that the welded portion is softened and post heat treatment is required. come. On the other hand, the non-heat-treatable JIS A5000 series alloy strengthened with Mg is less deteriorated in strength than the A6000 series aluminum alloy, but is annealed by welding heat input, and the weld joint efficiency is improved by the decrease in strength accompanying the coarsening of crystal grains. Is often less than 100%. For this reason, a technique for increasing the Mg content and a technique for increasing the strength by adding Sc have been studied as seen in JP-A-10-237577.
However, the increase in strength due to Sc is problematic in terms of cost because the Sc material itself is expensive, and the increase in Mg content is effective in increasing the strength of the weld, but it exceeds the specified content. In such a case, there is a natural limit to the decrease in hot workability.
[0003]
[Patent Document 1]
JP-A-10-237557 (first page [0004]
[Problems to be solved by the invention]
The present invention has been made in the background of the above circumstances. In a welding method in which rapid cooling such as laser welding is performed, the strength of the welded portion, that is, the strength of the weld metal and the weld heat affected zone is set to Mg. It is an object of the present invention to provide an aluminum alloy for welding that can be increased without relying on an increase in content, and to ensure a joint efficiency of 100% or more, and a welding method thereof.
[0005]
[Means for Solving the Problems]
In the present invention, as a result of investigating various aluminum alloys with respect to the cooling rate during welding and the hardness change of the weld metal, in a welding method with a high cooling rate such as laser welding, Mn, Cr, Fe, V, Zr, Ni It was found that the hardness of the welded portion can be increased by setting the content to a predetermined value or higher, and as a result, the strength of the welded portion can be increased to a value higher than that of the base material, and the present invention has been made. It is.
That is, the gist of the present invention is as follows.
[0006]
(1) By mass%, Mg: 0.4-7.0%, Cu: 0.05-1%, Mn: 0.8-2.5%, Cr: 0.35-2 0.0%, Fe: 0.7 to 1.5%, one or more, V: 0.5 to 1.0%, Zr: 2.0 to 2.5%, Ni: 3.0 Aluminum alloy for welding characterized by containing 1 type (s) or 2 types or more out of -3.5%, and remaining balance and unavoidable impurities.
(2) The aluminum alloy welding method according to (1), wherein after welding, the welded portion is cooled from the melting point to 200 ° C. at an average cooling rate of 500 to 1000 ° C./second. Method.
[0007]
DETAILED DESCRIPTION OF THE INVENTION
The present invention is described in detail below. The present invention is an aluminum alloy for welding and a welding method thereof, and is characterized by containing a predetermined amount of one or more of Mn, Cr, and Fe in order to increase the strength of the weld metal.
The role of each alloy element and the reason for limitation will be described below.
[0008]
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 resistance to weld cracking. The reason why the content is set to 0.4 to 7.0% is that sufficient strength cannot be obtained if the content is less than 0.4%. On the other hand, if the content exceeds 7.0%, the high temperature deformation resistance starts to increase. This is because workability is lowered.
Cu is an element that increases the strength of the alloy plate and is effective for stress corrosion cracking resistance. However, Cu is less effective if it is less than 0.05%, and general corrosion resistance deteriorates if it exceeds 1%. Therefore, it was made 0.05 to 1.0%.
Mn is an element that is fundamental in the alloy of the system targeted in the present invention. This element is also effective in securing the strength of the base material. Although it exists as a solid solution state and a crystallized substance (MnAl 6 ) in the base metal, all the crystallized substance is dissolved and solidified 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 dissolved in the weld metal remains in a supersaturated solid solution state without crystallization after solidification and cooling. That is, the solid solution limit can be expanded by increasing the cooling rate, and the hardness increases significantly. 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%, the supersaturated solid solution strengthening due to rapid cooling cannot be sufficiently obtained, and the hardness does not increase. Moreover, when it exceeds 2.5%, it becomes a coarse crystallized substance and precipitates, and workability is deteriorated.
[0009]
Cr, like Mn, is a basic element of the aluminum alloy in the present invention. As in the case of Mn, it exists in the matrix as a solid solution and a compound (CrAl 7 ), but in the case of welding with a high cooling rate such as laser welding, Cr dissolved in the weld metal is solidified and solidified. Even in the cooling process, it reaches room temperature without crystallization and remaining supersaturated. As a result, strengthening based on solid solution strengthening occurs, and the hardness significantly increases. The reason for setting the content to 0.35 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 crystals are obtained as in the case of Mn. This is because it becomes a product and precipitates to deteriorate workability.
Fe, together with Cr and Mn, is a basic element of the aluminum alloy in the present invention. Fe hardly dissolves in the base metal, but dissolves in the weld metal and dissolves in supersaturation, thereby contributing to an increase in hardness. If the Fe content is less than 0.7%, the effect does not appear, and if it exceeds 1.5%, the moldability is impaired. Therefore, it is set to 0.7% or more and 1.5% or less.
[0010]
Further, a predetermined amount of V, Zr, and Ni is added. V, Zr, and Ni are also elements that contribute to increasing the strength of the welded portion after welding, and are effective in securing the strength of the base material and suppressing the coarsening of the crystal grain size. V, Zr, and Ni have a small solid solubility limit in the base material and form an intermetallic compound. Like Mn, Cr, and Fe, in the case of welding with a high cooling rate such as laser welding, weld metal It dissolves in the solution and does not crystallize even in the solidification / cooling process and reaches room temperature while remaining supersaturated.
The component ranges were V: 0.5 to 1.0%, Zr: 2.0 to 2.5%, Ni: 3.0 to 3.5%, V: less than 0.5%, If Zr: less than 2.0%, Ni: less than 3.0%, the effect of increasing the strength is insufficient, V: more than 1.0%, Zr: more than 2.5%, Ni: more than 3.5% This is because coarse crystallized substances are formed in the base material, and the workability of the base material is significantly impaired.
[0011]
After welding, when the welded part is cooled from the melting point to 200 ° C. at an average cooling rate of less than 500 ° C./second, coarse precipitates are formed in the base material with a small contribution to strengthening, resulting in insufficient solid solution strengthening, This is because the joint efficiency decreases. In addition, it is extremely difficult to obtain a cooling rate exceeding 10,000 ° C./second even by rapid welding such as laser welding. Therefore, after welding, the average cooling rate from the melting point to 200 ° C. was set to a range of 500 to 10,000 ° C./second. In order to obtain a weld metal having further excellent characteristics, it is preferable to cool in the range of 1000 to 8000 ° C./second from the melting point to 200 ° C.
[0012]
Examples of the present invention will be described in detail. Table 1 shows the present invention example alloy compositions (No.1~ 8) and comparative alloys (N o. 9 to 11) and were prepared to investigate respectively. After melting, these alloys are forged and chamfered, then homogenized at 550 ° C. for 10 hours, hot-rolled, cold-rolled, intermediate-annealed-cold-rolled, and finally subjected to final annealing. Then, an alloy plate having a thickness of 2.0 mm was produced. The obtained alloy plate was subjected to laser welding under the conditions shown in Table 2, and the characteristics of the welded portion were examined. The average cooling rate from the melting point to 200 ° C. of the joint temperature after welding was set to 500 to 10000 ° C./second, which is a preferable range in rapid cooling welding such as laser welding.
[0013]
As for the tensile properties, a tensile test piece of JIS No. 5 including a welded portion was prepared, and the tensile strength and the breaking position were obtained with an Instron type tensile tester. The results are shown in Table 3, both N o. 1 to 8 of the alloy of the present invention embodiment is seen rise in hardness than the base material, even in the tensile test, all breaking position becomes the base material It can be seen that the joint strength is excellent.
Although the example of the effect in laser welding was shown in this invention, also in spot welding and a semiconductor laser lamp, since the cooling rate after welding is high similarly to laser welding, the same effect is acquired.
[0015]
【The invention's effect】
According to the present invention, in a welding method in which rapid cooling such as laser welding is performed, the strength of the welded portion, that is, the strength of the weld metal and the weld heat affected zone is increased without depending on the increase in the Mg content, It is possible to provide an aluminum alloy for rapid welding capable of ensuring a joint efficiency of 100% or more and a welding method thereof. Specifically, since the aluminum alloy of the present invention has high joint strength in the laser welded portion and does not include the softened portion, the fracture at the welded portion accompanying the softened portion in the welded portion, which has been a problem in the past, can be eliminated, It is effective as a material for a molding process including a structure or a welded portion, and has a remarkable industrially useful effect.
[Table 1]
Claims (2)
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、
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溶接用アルミニウム合金。% By mass
Mg: 0.4-7.0%
Cu: 0.05 to 1%
In addition,
Mn: 0.8 to 2.5%
Cr: 0.35-2.0%,
Fe: 0.7 to 1.5%
One or more of them,
V: 0.5 to 1.0%
Zr: 2.0-2.5%,
Ni: 3.0-3.5%
An aluminum alloy for welding , comprising one or more of them, the balance being Al and inevitable impurities.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2002259797A JP3754946B2 (en) | 2002-01-08 | 2002-09-05 | Aluminum alloy for welding and welding method thereof |
| US10/655,592 US6955785B2 (en) | 2002-09-05 | 2003-09-05 | Aluminum alloy for rapidly cooled welding and welding method therefor |
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| JP2002-1155 | 2002-01-08 | ||
| JP2002001155 | 2002-01-08 | ||
| JP2002259797A JP3754946B2 (en) | 2002-01-08 | 2002-09-05 | Aluminum alloy for welding and welding method thereof |
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| JP2003268476A JP2003268476A (en) | 2003-09-25 |
| JP3754946B2 true JP3754946B2 (en) | 2006-03-15 |
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| JP6679269B2 (en) * | 2015-10-22 | 2020-04-15 | 株式会社Uacj | Al alloy material for high energy beam welding |
| JP6679296B2 (en) * | 2015-12-17 | 2020-04-15 | 株式会社Uacj | Al alloy material for high energy beam welding and method for producing the same |
| US12378643B2 (en) | 2019-01-18 | 2025-08-05 | Divergent Technologies, Inc. | Aluminum alloys |
| WO2023278878A1 (en) | 2021-07-01 | 2023-01-05 | Divergent Technologies, Inc. | Al-mg-si based near-eutectic alloy composition for high strength and stiffness applications |
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