JP2017082254A - Al alloy material for high energy beam welding - Google Patents
Al alloy material for high energy beam welding Download PDFInfo
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- 238000003466 welding Methods 0.000 title claims abstract description 69
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 62
- 239000000956 alloy Substances 0.000 title claims abstract description 44
- 229910052802 copper Inorganic materials 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 229910052742 iron Inorganic materials 0.000 claims abstract description 6
- 229910052725 zinc Inorganic materials 0.000 claims abstract description 4
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 3
- 238000005496 tempering Methods 0.000 claims description 4
- 229910052759 nickel Inorganic materials 0.000 claims description 3
- 229910052710 silicon Inorganic materials 0.000 claims description 3
- 229910052720 vanadium Inorganic materials 0.000 claims description 3
- 229910052804 chromium Inorganic materials 0.000 claims description 2
- 238000007670 refining Methods 0.000 abstract description 4
- 239000011324 bead Substances 0.000 description 27
- 239000000463 material Substances 0.000 description 25
- 230000000694 effects Effects 0.000 description 24
- 238000000034 method Methods 0.000 description 23
- 230000001788 irregular Effects 0.000 description 18
- 238000005336 cracking Methods 0.000 description 17
- 229910045601 alloy Inorganic materials 0.000 description 15
- 230000000052 comparative effect Effects 0.000 description 14
- 238000005266 casting Methods 0.000 description 13
- 230000008018 melting Effects 0.000 description 13
- 239000000203 mixture Substances 0.000 description 13
- 239000010949 copper Substances 0.000 description 12
- 238000002844 melting Methods 0.000 description 12
- 238000005482 strain hardening Methods 0.000 description 12
- 238000004519 manufacturing process Methods 0.000 description 11
- 238000000137 annealing Methods 0.000 description 10
- 238000000265 homogenisation Methods 0.000 description 10
- 238000012545 processing Methods 0.000 description 10
- 229910000765 intermetallic Inorganic materials 0.000 description 9
- 239000013078 crystal Substances 0.000 description 8
- 238000011156 evaluation Methods 0.000 description 7
- 239000000654 additive Substances 0.000 description 6
- 230000000996 additive effect Effects 0.000 description 6
- 229910018084 Al-Fe Inorganic materials 0.000 description 4
- 229910018134 Al-Mg Inorganic materials 0.000 description 4
- 229910018192 Al—Fe Inorganic materials 0.000 description 4
- 229910018467 Al—Mg Inorganic materials 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 230000001105 regulatory effect Effects 0.000 description 4
- 238000005096 rolling process Methods 0.000 description 4
- 230000001629 suppression Effects 0.000 description 4
- 238000005097 cold rolling Methods 0.000 description 3
- 238000009749 continuous casting Methods 0.000 description 3
- 238000005242 forging Methods 0.000 description 3
- 238000005098 hot rolling Methods 0.000 description 3
- 238000007711 solidification Methods 0.000 description 3
- 230000008023 solidification Effects 0.000 description 3
- 229910018507 Al—Ni Inorganic materials 0.000 description 2
- 229910001030 Iron–nickel alloy Inorganic materials 0.000 description 2
- QQHSIRTYSFLSRM-UHFFFAOYSA-N alumanylidynechromium Chemical compound [Al].[Cr] QQHSIRTYSFLSRM-UHFFFAOYSA-N 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
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- 238000010894 electron beam technology Methods 0.000 description 2
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- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
- 229910002551 Fe-Mn Inorganic materials 0.000 description 1
- 229910000861 Mg alloy Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 238000010622 cold drawing Methods 0.000 description 1
- 238000010273 cold forging Methods 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
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Abstract
Description
本発明は、高エネルギービーム溶接用Ａｌ合金材であって、特に耐溶接割れ性に優れるＡｌ合金材に関するものである。 The present invention relates to an Al alloy material for high energy beam welding, and particularly to an Al alloy material having excellent weld crack resistance.
近年、輸送材や構造材等の分野において、従来使用されてきたＦｅやＣｕをＡｌ合金材に置き換えることによる軽量化の要求が増えてきている。このような材料の置き換えにおいては、各部材に必要とされる強度や耐食性、成形性、接合性などを満たすことが必要で有り、Ａｌ合金材に関する種々の検討が成されている。特に、Ａｌ合金はＦｅやＣｕに比べて熱膨張率が大きく、表面に強固な酸化皮膜を形成するために接合性の向上が重要である。 In recent years, in the fields of transport materials and structural materials, there has been an increasing demand for weight reduction by replacing Fe and Cu that have been conventionally used with Al alloy materials. In such replacement of materials, it is necessary to satisfy the strength, corrosion resistance, formability, bondability, and the like required for each member, and various studies on Al alloy materials have been made. In particular, Al alloys have a higher coefficient of thermal expansion than Fe and Cu, and it is important to improve bondability in order to form a strong oxide film on the surface.
中、高強度材として一般的に用いられるＡｌ合金として、Ａｌ−Ｍｇ系合金が知られている。Ａｌ−Ｍｇ系合金は、Ｍｇの添加量により強度の調整が可能な非熱処理型合金であり、代表的な合金としては、５０５２、５１５４、５０８３などが挙げられる。前記Ａｌ合金は、強度や成形性、溶接性などを考慮してＭｇの添加量が調整され、輸送材や構造材等に用いられている。 Among these, Al—Mg alloys are known as Al alloys that are generally used as high-strength materials. The Al—Mg-based alloy is a non-heat-treatable alloy whose strength can be adjusted by adding Mg, and typical alloys include 5052, 5154, 5083, and the like. The Al alloy is used for a transport material, a structural material, and the like, in which the addition amount of Mg is adjusted in consideration of strength, formability, weldability, and the like.
また、近年、ＴＩＧ溶接やＭＩＧ溶接に代表される従来の溶接方法に対して、高エネルギービームを使用したレーザ溶接法や電子ビーム溶接法などの接合技術が開発されている。これらの高エネルギービーム溶接は、低歪みで高速度の溶接が可能であることが特徴である。しかしながら、生産性の向上のために高エネルギービームを使用して高速度で溶接を行う場合には、溶融部の急激な凝固を伴うために溶接割れが発生しやすい。特に、１〜３ｍａｓｓ％程度のＭｇを含有するＡｌ−Ｍｇ系合金は溶接割れが特に発生し易いことが知られており、充分な注意が必要である。 In recent years, joining techniques such as a laser welding method using a high energy beam and an electron beam welding method have been developed with respect to conventional welding methods represented by TIG welding and MIG welding. These high energy beam weldings are characterized by low strain and high speed welding. However, when welding is performed at a high speed using a high energy beam in order to improve productivity, weld cracking is likely to occur due to rapid solidification of the molten part. In particular, it is known that Al—Mg-based alloys containing about 1 to 3 mass% of Mg are particularly susceptible to weld cracking, and sufficient care is required.
特許文献１には、所定の組成を有するＡｌ−Ｍｎ−Ｍｇ合金をパルスレーザ溶接する際において、パルス波形を調整することにより溶接割れを抑制する技術が提案されている。また、特許文献２には、バスバー用途に使用するＡｌ−Ｆｅ系合金に関する技術が提案されている。この特許文献２においては、Ｆｅの添加により溶接割れを抑制することが示されている。 Patent Document 1 proposes a technique for suppressing weld cracking by adjusting a pulse waveform when pulse laser welding an Al—Mn—Mg alloy having a predetermined composition. Patent Document 2 proposes a technique related to an Al—Fe alloy used for bus bar applications. In this patent document 2, it is shown that weld cracking is suppressed by addition of Fe.
しかしながら、特許文献１に開示されている方法では、使用するＡｌ合金材の組成としてＭｇが１．２ｍａｓｓ％を超える範囲で添加された材料では割れが発生するため、中、高強度なＡｌ合金材に対して、割れの発生を抑制できる材料とは言えないのが現状であった。 However, in the method disclosed in Patent Document 1, cracking occurs in a material in which Mg is added in a range exceeding 1.2 mass% as the composition of the Al alloy material to be used. On the other hand, the present situation is that it cannot be said that the material can suppress the occurrence of cracks.
また、特許文献２に示すＡｌ−Ｆｅ系合金では、Ｍｇの添加により高強度化した材料では効果が確認されていない。また、Ｏ材強度が低い材料であるため、溶接継手を作製した際の継手強度が低く、構造材として十分な強度を有していない等の問題がある。 In addition, in the Al—Fe-based alloy shown in Patent Document 2, the effect has not been confirmed with a material whose strength is increased by adding Mg. Further, since the strength of the O material is low, there is a problem that the strength of the joint when the welded joint is produced is low and the structure material does not have sufficient strength.
本発明は、上記事情に鑑みてなされたものであり、高エネルギービーム溶接に用いられるＡｌ合金材であって、特に耐溶接割れ性に優れるＡｌ合金材を提供することを目的とする。 The present invention has been made in view of the above circumstances, and an object of the present invention is to provide an Al alloy material that is used for high energy beam welding and that is particularly excellent in weld crack resistance.
本発明者等は鋭意研究を重ねた結果、高エネルギービーム溶接用のＡｌ−Ｍｇ系合金の組成を調整することにより、高エネルギービーム溶接における割れの抑制が可能であることを見出して本発明を完成するに至った。 As a result of intensive studies, the present inventors have found that cracks in high energy beam welding can be suppressed by adjusting the composition of the Al-Mg alloy for high energy beam welding, and the present invention has been developed. It came to be completed.
すなわち、本発明は請求項１において、Ｍｇ：１．２０〜３．３０ｍａｓｓ％及びＦｅ：０．７５〜２．４０ｍａｓｓ％を含有し、Ｓｉ：０．２５ｍａｓｓ％未満、Ｃｕ：０．１０ｍａｓｓ％未満、Ｍｎ：０．１０ｍａｓｓ％未満及びＺｎ：０．１０ｍａｓｓ％未満にそれぞれ規制し、残部Ａｌ及び不可避的不純物からなるＡｌ合金からなり、調質Ｏにおける引張強度が１２５ＭＰａ以上であることを特徴とする高エネルギービーム溶接用Ａｌ合金材とした。 That is, the present invention according to claim 1 includes Mg: 1.20 to 3.30 mass% and Fe: 0.75 to 2.40 mass%, Si: less than 0.25 mass%, and Cu: less than 0.10 mass%. , Mn: less than 0.10 mass% and Zn: less than 0.10 mass%, respectively, the balance is made of an Al alloy composed of Al and inevitable impurities, and the tensile strength in the tempered O is 125 MPa or more. Al alloy material for high energy beam welding was used.
本発明は請求項２では請求項１において、前記Ａｌ合金が、Ｃｒ：０．０５０〜０．３５０ｍａｓｓ％、Ｖ：０．０５０〜０．１００ｍａｓｓ％及びＮｉ：０．０５０〜２．０００ｍａｓｓ％からなる群から選択される１種又は２種以上を更に含有するものとした。 According to a second aspect of the present invention, in the first aspect, the Al alloy includes Cr: 0.050 to 0.350 mass%, V: 0.050 to 0.100 mass%, and Ni: 0.050 to 2.000 mass%. One or two or more selected from the group consisting of
本発明は請求項３では請求項１又は２において、前記Ａｌ合金が、Ｔｉ：０．００５０〜０．３０００ｍａｓｓ％、ならびに、Ｂ：０．０００１０〜０．０５０００ｍａｓｓ％及びＣ：０．０００１０〜０．００２００ｍａｓｓ％の少なくとも一方を更に含有するものとした。 According to a third aspect of the present invention, in the first or second aspect, the Al alloy includes Ti: 0.0050 to 0.3000 mass%, B: 0.00010 to 0.05000 mass%, and C: 0.00010 to 0. Further, at least one of 00100 mass% was further contained.
本発明に係る高エネルギービーム溶接用Ａｌ合金材は、耐溶接割れ性に優れるという格別の効果を奏するものである。 The Al alloy material for high energy beam welding according to the present invention has a special effect of being excellent in weld crack resistance.
以下、本発明に係る高エネルギービーム溶接用Ａｌ合金材について詳細に説明する。 Hereinafter, the Al alloy material for high energy beam welding according to the present invention will be described in detail.
１．Ａｌ合金組成
まず、本発明に係る高エネルギービーム溶接用Ａｌ合金材を構成するアルミニウム合金成分組成について説明する。この合金組成を大きく分類すると、必須元素としてＭｇ及びＦｅ、制限元素としてＳｉ、Ｃｕ、Ｍｎ及びＺｎ、第一の選択的添加元素としてＣｒ、Ｖ及びＮｉ、第二の選択的添加元素としてＴｉ、Ｂ及びＣ、とに分けられる。本発明に係る高エネルギービーム溶接用アルミニウム合金材は、これらの合金成分組成を調整することにより、高エネルギービーム溶接における割れの抑制が可能とする。
1. Al alloy composition First, the aluminum alloy component composition which comprises the Al alloy material for high energy beam welding which concerns on this invention is demonstrated. This alloy composition is roughly classified as Mg and Fe as essential elements, Si, Cu, Mn and Zn as limiting elements, Cr, V and Ni as first selective additive elements, Ti as second selective additive elements, B and C. The aluminum alloy material for high energy beam welding according to the present invention can suppress cracking in high energy beam welding by adjusting the composition of these alloy components.
１−１．必須元素
Ｍｇ：１．２０〜３．３０ｍａｓｓ％
Ｍｇは、材料の高強度化に寄与する必須の添加元素である。Ｍｇの含有量は１．２０〜３．３０ｍａｓｓ％（以下、単に「％」と記す）とする。Ｍｇの含有量が１．２０％未満では高強度化に寄与する添加効果を得ることができない。一方、Ｍｇの含有量が３．３０％を超えると溶接部内部に残存するブローホールが増加する。その結果、継手強度の低下が生じる。好ましいＭｇの含有量は、２．００〜３．００％である。
1-1. Essential element Mg: 1.20 to 3.30 mass%
Mg is an essential additive element that contributes to increasing the strength of the material. The Mg content is 1.20 to 3.30 mass% (hereinafter simply referred to as “%”). If the Mg content is less than 1.20%, it is impossible to obtain the addition effect that contributes to high strength. On the other hand, if the Mg content exceeds 3.30%, blowholes remaining inside the welded portion increase. As a result, the joint strength is reduced. A preferable Mg content is 2.00 to 3.00%.
Ｆｅ：０．７５〜２．４０％
Ｆｅは、高エネルギービーム溶接において割れの抑制に寄与する成分である。Ｆｅの含有量は０．７５〜２．４０％とする。Ｆｅの含有量が０．７５％未満では上記効果が十分に得られない。一方、Ｆｅ含有量が２．４０％を超えると粗大なＡｌ−Ｆｅ系金属間化合物が形成されるため加工性が低下すると共に，溶接時の溶融挙動が不安定化する。好ましいＦｅの含有量は、０．９０〜１．８０％である。
Fe: 0.75 to 2.40%
Fe is a component that contributes to suppression of cracking in high energy beam welding. The Fe content is 0.75 to 2.40%. If the Fe content is less than 0.75%, the above effect cannot be obtained sufficiently. On the other hand, if the Fe content exceeds 2.40%, a coarse Al—Fe-based intermetallic compound is formed, so that workability is lowered and the melting behavior during welding becomes unstable. The preferable Fe content is 0.90 to 1.80%.
１−２．制限元素
Ｓｉ：０．２５％未満
Ｓｉは、高エネルギービーム溶接において、割れの発生を引き起こす成分であるためＡｌ合金中にＳｉが含有されることは好ましくない。Ｓｉの含有量が０．２５％以上であると、溶接時に割れが発生し易くなる。従って、Ｓｉの含有量を０．２５％未満に規制する。Ｓｉの含有量は、０．１０％未満に規制するのが好ましいが、Ｓｉの含有量を極めて低い値で管理することは製造上困難であることから、その下限値は製造上可能な範囲で自ずと決められる。
1-2. Limiting element Si: less than 0.25% It is not preferable that Si is contained in the Al alloy because Si is a component that causes cracking in high energy beam welding. If the Si content is 0.25% or more, cracks are likely to occur during welding. Therefore, the Si content is restricted to less than 0.25%. The Si content is preferably regulated to less than 0.10%. However, since it is difficult to manufacture the Si content at an extremely low value, the lower limit is within a range that can be manufactured. It is decided by itself.
Ｃｕ：０．１０％未満
Ｃｕは、高エネルギービーム溶接において、割れの発生を引き起こす成分であるためＡｌ合金中にＣｕが含有されることは好ましくない。Ｃｕの含有量が０．１０％以上であると、溶接時に割れが発生し易くなる。従って、Ｃｕの含有量を０．１０％未満に規制する。Ｃｕの含有量は、０．０５％未満に規制するのが好ましく、０％が最も好ましい。
Cu: Less than 0.10% It is not preferable that Cu is contained in the Al alloy because Cu is a component that causes cracking in high-energy beam welding. If the Cu content is 0.10% or more, cracking is likely to occur during welding. Therefore, the Cu content is restricted to less than 0.10%. The Cu content is preferably regulated to less than 0.05%, and most preferably 0%.
Ｍｎ：０．１０％未満
Ｍｎは、高エネルギービーム溶接の際に、イレギュラービードの形成を引き起こす成分であるためＡｌ合金中にＭｎが含有されることは好ましくない。Ｍｎの含有量が０．１０％以上であると、溶接ビードの不整を生じ易くなる。従って、Ｍｎの含有量を０．１０％未満に規制する。Ｍｎの含有量は、０．０５％未満に規制するのが好ましく、０％が最も好ましい。
Mn: Less than 0.10% It is not preferable that Mn is contained in the Al alloy because Mn is a component that causes the formation of irregular beads during high energy beam welding. If the Mn content is 0.10% or more, irregularities in the weld bead are likely to occur. Therefore, the Mn content is restricted to less than 0.10%. The Mn content is preferably regulated to less than 0.05%, and most preferably 0%.
Ｚｎ：０．１０％未満
Ｚｎは、高エネルギービーム溶接の際に、割れの発生とイレギュラービードの形成を引き起こす成分であるためＡｌ合金中にＺｎが含有されることは好ましくない。Ｚｎの含有量が０．１０％以上になると、溶接割れや溶接ビードの不整を生じ易くなる。従って、Ｚｎの含有量を０．１０％未満に規制する。Ｚｎの含有量は、０．０５％未満に規制するのが好ましく、０％が最も好ましい。
Zn: Less than 0.10% Since Zn is a component that causes cracking and formation of irregular beads during high energy beam welding, it is not preferable that Zn be contained in the Al alloy. If the Zn content is 0.10% or more, weld cracks and weld bead irregularities are likely to occur. Therefore, the Zn content is restricted to less than 0.10%. The Zn content is preferably regulated to less than 0.05%, and most preferably 0%.
１−３．第一の選択的添加元素
Ｃｒ：０．０５０〜０．３５０％
Ｃｒは、結晶粒の微細化、高エネルギービーム溶接における割れの抑制に寄与する成分である。Ｃｒの含有量は、０．０５０〜０．３５０％とする。Ｃｒの含有量が０．０５０％未満では上記効果が十分に得られない。一方、Ｃｒの含有量が０．３５０％を超えると粗大なＡｌ−Ｃｒ系金属間化合物が形成されるため、溶接ビードの不整を生じ易くなる。好ましいＣｒの含有量は、０．１５〜０．３０％である。
1-3. First selective additive element Cr: 0.050 to 0.350%
Cr is a component that contributes to the refinement of crystal grains and the suppression of cracks in high energy beam welding. The Cr content is 0.050 to 0.350%. If the content of Cr is less than 0.050%, the above effect cannot be obtained sufficiently. On the other hand, when the content of Cr exceeds 0.350%, a coarse Al—Cr intermetallic compound is formed, so that the weld bead is likely to be irregular. The preferable Cr content is 0.15 to 0.30%.
Ｖ：０．０５０〜０．１００％
Ｖは、高エネルギービーム溶接における割れの抑制に寄与する成分である。Ｖの含有量は、０．０５０〜０．１００％とする。Ｖの含有量が０．０５０％未満では上記効果が十分に得られない。一方、Ｖの含有量が０．１００％を超えると粗大なＡｌ−Ｖ系金属間化合物が形成されるため、溶接ビードの不整を生じ易くなる。
V: 0.050-0.100%
V is a component that contributes to suppression of cracking in high energy beam welding. The V content is 0.050 to 0.100%. If the V content is less than 0.050%, the above effects cannot be obtained sufficiently. On the other hand, when the content of V exceeds 0.100%, a coarse Al—V intermetallic compound is formed, and irregularities in the weld bead are likely to occur.
Ｎｉ：０．０５０〜２．０００％
Ｎｉは、高エネルギービーム溶接における割れの抑制に寄与する成分である。Ｎｉの含有量は、０．０５０〜２．０００％とする。Ｎｉの含有量が０．０５０％未満では上記効果が十分に得られない。一方、Ｎｉの含有量が２．０００％を超えると粗大なＡｌ−Ｎｉ系、Ａｌ−Ｆｅ−Ｎｉ系金属間化合物が形成されるため、溶接ビードの不整を生じ易くなる。好ましいＮｉの含有量は、０．５００〜１．５００％である。
Ni: 0.050 to 2.000%
Ni is a component that contributes to suppression of cracking in high energy beam welding. The Ni content is 0.050 to 2.000%. If the Ni content is less than 0.050%, the above effects cannot be obtained sufficiently. On the other hand, when the Ni content exceeds 2.000%, coarse Al—Ni-based and Al—Fe—Ni-based intermetallic compounds are formed, and it becomes easy to cause irregularities in the weld bead. A preferable Ni content is 0.500 to 1.500%.
１−４．第二の選択的添加元素
Ｔｉ：０．００５０〜０．３０００％、Ｂ：０．０００１０〜０．０５０００％、Ｃ：０．０００１０〜０．００２００％
Ｔｉはマトリクス中に固溶して強度向上させる他に、層状に分布して板厚方向の腐食の進展を防ぐ効果を発揮する。また、ＴｉとＢから形成されるＴｉＢ２及びＴｉとＣから形成されるＴｉＣは、鋳塊組織の微細化材として作用する。さらに、溶接部の結晶粒の微細化に寄与し、継手強度の向上効果を有する。溶接継手においては、溶接部における溶融凝固の結果加工歪みは消失し、継手強度は調質Ｏにおける強度に近い値となる。このように、溶接部の結晶粒を微細化することにより、継手強度の向上効果を保障することができる。
1-4. Second selective additive element Ti: 0.0050 to 0.3000%, B: 0.00010 to 0.05000%, C: 0.00010 to 0.00200%
Ti is dissolved in the matrix to improve the strength, and is distributed in a layered manner to exhibit the effect of preventing the progress of corrosion in the thickness direction. Further, TiB 2 formed from Ti and B and TiC formed from Ti and C act as a material for refining the ingot structure. Furthermore, it contributes to the refinement of the crystal grains of the welded portion and has an effect of improving the joint strength. In the welded joint, the processing strain disappears as a result of melt solidification in the welded portion, and the joint strength becomes a value close to the strength in the tempered O. Thus, the refinement | purification of the crystal grain of a welding part can ensure the improvement effect of joint strength.
本発明では、選択的添加元素として、Ｔｉ：０．００５０〜０．３０００％をＢ：０．０００１０〜０．０５０００％及びＣ：０．０００１０〜０．００２００％の少なくとも一方と共存させて含有させる。Ｔｉの含有量が０．００５０％未満では、上記効果が十分に得られない。一方、０．３０００％を超えると粗大凝集物によって溶融挙動が不安定化し、ビードの不整を生じ易くなる。Ｂの含有量が０．０００１０％未満では、微細化材の効果が十分に得られない場合がある。一方、０．０５０００％を超えるとＴｉ−Ｂ系化合物（例えば、ＴｉＢ２）の粗大凝集物によって溶融挙動が不安定化し、ビードの不整を生じ易くなる。また、Ｃの含有量が０．０００１０％未満では、十分な微細化効果が得られない場合がある。一方、０．００２００％を超えるとＴｉ−Ｃ系化合物（例えば、ＴｉＣ）の粗大凝集物により、溶融挙動が不安定化し、ビードの不整を生じ易くなる。 In the present invention, Ti: 0.0050 to 0.3000% is contained as a selective additive element in combination with at least one of B: 0.00010 to 0.05000% and C: 0.00010 to 0.00200%. Let If the Ti content is less than 0.0050%, the above effect cannot be obtained sufficiently. On the other hand, if it exceeds 0.3000%, the melting behavior becomes unstable due to coarse agglomerates and bead irregularities are likely to occur. If the content of B is less than 0.00010%, the effect of the fine material may not be sufficiently obtained. On the other hand, if it exceeds 0.05000%, the melting behavior becomes unstable due to coarse aggregates of Ti-B compounds (for example, TiB 2 ), and irregular beads are likely to occur. Further, if the C content is less than 0.00010%, a sufficient fine effect may not be obtained. On the other hand, if it exceeds 0.00200%, the coarse behavior of Ti—C compounds (for example, TiC) makes the melting behavior unstable and tends to cause irregular beads.
その他の元素：
また、また、本発明に係るＡｌ合金の残部は、Ａｌと不可避的不純物とからなる。ここで、不可避的不純物は、各々が０．０５０％以下で、かつ、合計で０．１５０％以下であれば、本発明で得られるＡｌ合金材としての特性を損なうことはない。
Other elements:
Moreover, the balance of the Al alloy according to the present invention is composed of Al and inevitable impurities. Here, if the inevitable impurities are each 0.050% or less and 0.150% or less in total, the characteristics as the Al alloy material obtained in the present invention are not impaired.
２．高エネルギービーム溶接用Ａｌ合金材の調質Ｏにおける引張強度
次に、本発明に係る高エネルギービーム溶接用Ａｌ合金材の調質Ｏにおける強度について説明する。
2. Next, the tensile strength in the tempering O of the Al alloy material for high energy beam welding according to the present invention will be described.
高エネルギービーム溶接用Ａｌ合金材は、Ｏ材に調質を行った場合において１２５ＭＰａ以上の引張強度を有するものとする。溶接継手においては、溶接部及び熱影響部における加工歪みが消失するため、継手強度は調質Ｏにおける強度に近い値となる。したがって、調質Ｏにおける引張強度を１２５ＭＰａ以上とすることにより、構造材としての最低限の強度を保障することが出来る。この調質Ｏにおける引張強度は１７０ＭＰａ以上であることが好ましい。なお、調質Ｏにおける引張強度の上限値は、Ａｌ合金組成や製造工程に拠って決まるが、本発明では、３００ＭＰａである。 The Al alloy material for high energy beam welding has a tensile strength of 125 MPa or more when the O material is tempered. In the welded joint, since the processing distortion in the welded part and the heat affected zone disappears, the joint strength becomes a value close to the strength in the tempered O. Therefore, by setting the tensile strength in the tempering O to 125 MPa or more, the minimum strength as a structural material can be ensured. It is preferable that the tensile strength in this tempering O is 170 MPa or more. In addition, although the upper limit of the tensile strength in the refining O is decided by Al alloy composition and a manufacturing process, in this invention, it is 300 MPa.
４．高エネルギービーム溶接用Ａｌ合金材の製造方法 4). Method for producing Al alloy material for high energy beam welding
次に、本発明に係る高エネルギービーム溶接用Ａｌ合金材の製造工程について詳述する。本発明に係る高エネルギービーム溶接用Ａｌ合金材の製造方法は、基本的には、圧延、押出及び鍛造といったＡｌ合金展伸材の常法に従って製造することができるが、その製造工程のうちの溶解・鋳造工程において所定の合金組成に調整することによって、優れた耐溶接割れ性を付与することが可能となる。 Next, the manufacturing process of the Al alloy material for high energy beam welding according to the present invention will be described in detail. The method for producing an Al alloy material for high energy beam welding according to the present invention can be basically produced in accordance with a conventional method for extending an Al alloy material such as rolling, extrusion and forging. By adjusting to a predetermined alloy composition in the melting / casting process, it is possible to impart excellent weld crack resistance.
圧延・押出・鍛造といったＡｌ合金展伸材に共通して行われる製造方法について説明する。高エネルギービーム溶接用Ａｌ合金材の製造方法は、Ａｌ合金溶湯を本発明に係るＡｌ合金の成分範囲内に溶解調整する溶解工程と；溶解調整された溶湯を鋳造して鋳塊を得る鋳造工程と；鋳塊を特定条件で保持する均質化処理工程と；均質化処理した鋳塊を特定の条件で熱間加工する熱間加工工程と；必要に応じて熱間加工材を特定の条件で冷間加工する冷間加工工程と；必要に応じて焼鈍処理工程と；を備える。 A manufacturing method commonly performed for Al alloy wrought materials such as rolling, extrusion, and forging will be described. The method for producing an Al alloy material for high energy beam welding includes: a melting step for adjusting the melting of the Al alloy melt within the component range of the Al alloy according to the present invention; a casting step for casting the molten metal adjusted for melting to obtain an ingot A homogenization process for holding the ingot under specific conditions; a hot working process for hot working the homogenized ingot under specific conditions; and a hot work material under specific conditions as necessary. A cold working step for cold working; and an annealing treatment step as necessary.
４−１．溶解工程
溶解工程としては、Ａｌ合金溶湯を本発明に係るＡｌ合金の成分範囲内に溶解調整を行い、当該Ａｌ合金溶湯に対して、脱ガス処理や不純物を除去するための濾過処理などを行う。
4-1. Melting step As the melting step, the Al alloy molten metal is adjusted to be dissolved within the component range of the Al alloy according to the present invention, and the Al alloy molten metal is subjected to a degassing process or a filtering process for removing impurities. .
４−２．鋳造工程
鋳造工程としては、半連続鋳造法（ＤＣ鋳造法またはホットトップ鋳造法）又は連続鋳造法（ＣＣ鋳造法）によって鋳塊（スラブ）に製造する。Ａｌ−Ｆｅ−Ｍｎ系金属間化合物の粗大化を防ぐため、鋳造時の冷却速度を１００〜１０２℃／ｓｅｃの範囲とするのが好ましい。また、鋳造に使用する原料として、溶接用構造材として一般的に使用されている５０５２や５１５４などのスクラップを多く使用してもよい。鋳造後には、引き続き行われる熱間加工に備えて、必要に応じて鋳塊表面の鋳肌を削り取る面削を行ってもよく、面削は後述する均質化処理後に行ってもよい。
4-2. Casting process As a casting process, the ingot (slab) is manufactured by a semi-continuous casting method (DC casting method or hot top casting method) or a continuous casting method (CC casting method). In order to prevent coarsening of the Al—Fe—Mn intermetallic compound, the cooling rate during casting is preferably in the range of 10 0 to 10 2 ° C./sec. Further, as a raw material used for casting, a lot of scraps such as 5052 and 5154 that are generally used as welding structural materials may be used. After casting, in preparation for the subsequent hot working, chamfering may be performed by scraping the cast surface of the ingot surface as necessary, and the chamfering may be performed after a homogenization treatment described later.
４−３．均質化処理工程
均質化処理工程としては、通常、Ａｌ合金の鋳造の凝固時に形成される凝固組織に特徴的な濃度偏析を解消して均一化させるために均質化処理が施される。均質化処理温度は４００〜５５０℃である。均質化処理温度が４００℃未満であると充分な均質化効果が得られない。一方、均質化処理温度が５５０℃を超えると鋳塊が溶融する恐れがあるため好ましくない。また、処理時間は４〜１０時間である。処理時間が４時間未満であると充分な均質化効果が得られ。ない。一方、処理時間が１０時間を超えると生産性が低下する。
4-3. Homogenization treatment step As the homogenization treatment step, a homogenization treatment is usually performed in order to eliminate the concentration segregation characteristic of the solidified structure formed during solidification of the casting of the Al alloy and to make it uniform. The homogenization treatment temperature is 400 to 550 ° C. If the homogenization temperature is less than 400 ° C., a sufficient homogenization effect cannot be obtained. On the other hand, if the homogenization temperature exceeds 550 ° C., the ingot may be melted, which is not preferable. The processing time is 4 to 10 hours. If the treatment time is less than 4 hours, a sufficient homogenizing effect can be obtained. Absent. On the other hand, when the processing time exceeds 10 hours, productivity decreases.
４−４熱間加工工程
熱間加工としては、板を製造する場合は熱間圧延により行い、管や棒などを製造する場合は熱間押出により行い、その他の形状に加工する場合は熱間鍛造により行うことができる。本発明の実施形態に係るＡｌ合金はいずれの熱間加工も行うことができ、またその加工条件は、最終製品の特性に影響しないため、熱間加工条件は素材の熱間加工性を考慮して、本発明の効果を奏する範囲で適宜選択される。本発明の効果を奏する範囲においては、熱間加工開始温度は３００〜５２０℃である。熱間加工開始温度が３００℃未満であると加工が困難となる。一方、熱間加工開始温度が５２０℃を超えると溶融する虞がある。
4-4 Hot working process Hot working is performed by hot rolling when manufacturing a plate, by hot extrusion when manufacturing a tube or a rod, and hot when processing into other shapes. It can be performed by forging. Since the Al alloy according to the embodiment of the present invention can perform any hot working, and the working conditions do not affect the properties of the final product, the hot working conditions consider the hot workability of the material. Thus, it is appropriately selected within the range where the effects of the present invention are exhibited. In the range where the effect of the present invention is exhibited, the hot working start temperature is 300 to 520 ° C. If the hot working start temperature is less than 300 ° C., the working becomes difficult. On the other hand, if the hot working start temperature exceeds 520 ° C., there is a risk of melting.
４−５．冷間加工工程
最終製品の形状及び強度に精度良く仕上げるため、熱間加工の後、冷間加工を行ってもよい。冷間加工は、板を製造する場合は冷間圧延、管や棒などを製造する場合は冷間引抜き、その他の形状に加工する場合は冷間鍛造によって行う。冷間加工工程を実施する場合には、最終的な特性に影響しないため、本発明の効果を奏する範囲で適宜選択される。本発明の効果を奏する範囲においては、冷間加工工程における加工率は、２０〜７０％である。冷間加工率が２０％未満であると充分な加工硬化が起こらないため冷間加工の必要性が無くなる。一方、７０％を超えると加工硬化により冷間加工性が低下し、割れが生じる虞がある。
4-5. Cold working process In order to accurately finish the shape and strength of the final product, cold working may be performed after hot working. The cold working is performed by cold rolling when manufacturing a plate, cold drawing when manufacturing a tube or a rod, and cold forging when processing into other shapes. When the cold working process is performed, the final characteristics are not affected, and therefore, the cold working process is appropriately selected within the range where the effects of the present invention are exhibited. In the range where the effect of the present invention is exhibited, the processing rate in the cold processing step is 20 to 70%. If the cold working rate is less than 20%, sufficient work hardening does not occur, and the need for cold working is eliminated. On the other hand, when it exceeds 70%, cold workability is lowered due to work hardening, and there is a possibility that cracking occurs.
３−６．焼鈍工程
良好な冷間加工性を保持するために、冷間加工の前、途中及び後の少なくともいずれかにおいて、焼鈍を施してもよい。焼鈍を実施する場合には、最終的な特性に影響しないため、本発明の効果を奏する範囲で適宜選択される。本発明の効果を奏する範囲においては、焼鈍の温度を３００〜５００℃とするのが好ましい。焼鈍温度が３００℃未満であると鈍効果が充分ではない。一方、焼鈍温度が５００℃を超えると結晶粒成長が促進され、粗大な結晶粒を形成する恐れがある。また、処理時間は０．５〜８時間である。処理時間が０．５時間未満であると充分な焼鈍効果が得られなくなる、一方、処理時間が８時間を超えると生産性が低下する。
3-6. Annealing Step In order to maintain good cold workability, annealing may be performed at least before, during and after cold working. When annealing is performed, the final characteristics are not affected, and therefore, the annealing is appropriately selected within the range where the effects of the present invention are exhibited. In the range where the effects of the present invention are exhibited, the annealing temperature is preferably 300 to 500 ° C. If the annealing temperature is less than 300 ° C., the dull effect is not sufficient. On the other hand, when the annealing temperature exceeds 500 ° C., crystal grain growth is promoted, and coarse crystal grains may be formed. The processing time is 0.5 to 8 hours. When the treatment time is less than 0.5 hours, a sufficient annealing effect cannot be obtained. On the other hand, when the treatment time exceeds 8 hours, the productivity is lowered.
４．高エネルギービームによる溶接
従来の溶接手法であるアーク溶接においては、溶接割れを抑制するために、溶加材を用いて溶接部の成分を調整する。一方で、高エネルギービーム溶接は高速度で溶接が可能であり生産性が高いという利点があるため、生産性の低下を招く溶加材の使用を行わない場合が多い。また、高エネルギービーム溶接では、溶融部が凝固する際の冷却速度が大きいため、溶接部における歪み速度は大きくなる。したがって、生産性の向上を図って高エネルギービーム溶接を適用した場合には、従来の溶接手法を用いるよりも溶接割れが発生し易くなる。本発明に係る高エネルギービーム溶接用Ａｌ合金材は、合金成分組成を調整することにより、前記高エネルギービームによる溶接において優れた耐溶接割れ性を示す。
4). Welding with a high energy beam In arc welding, which is a conventional welding technique, the components of the weld are adjusted using a filler metal in order to suppress weld cracking. On the other hand, high energy beam welding has the advantage that it can be welded at a high speed and has high productivity, and therefore there is often no use of a filler material that causes a decrease in productivity. Moreover, in high energy beam welding, since the cooling rate at the time of solidification of a fusion | melting part is large, the distortion rate in a welding part becomes large. Therefore, when high energy beam welding is applied in order to improve productivity, weld cracks are more likely to occur than when using a conventional welding technique. The Al alloy material for high energy beam welding according to the present invention exhibits excellent weld crack resistance in welding with the high energy beam by adjusting the alloy composition.
溶接に使用する高エネルギービームとしては、電子ビームやレーザビームなどが選択可能である。また、前記ビームの波形は、連続波やパルス波などが用いられる。溶接に用いられる出力は６０ｋＷ以下である場合が多く、溶接速度は１ｍｍ／ｓ〜１０００ｍｍ／ｓの間で適宜選択される。本発明に係る高エネルギービーム溶接用Ａｌ合金材を接合する相手部材の合金としては、同一の合金組成を有するＡｌ合金展伸材を使用することが好ましいが、他の合金組成を有するＡｌ合金展伸材、銅及び銅合金、鋼材なども適用できる。 An electron beam, a laser beam, or the like can be selected as the high energy beam used for welding. The beam waveform may be a continuous wave or a pulse wave. The output used for welding is often 60 kW or less, and the welding speed is appropriately selected between 1 mm / s and 1000 mm / s. As the alloy of the mating member for joining the Al alloy material for high energy beam welding according to the present invention, it is preferable to use an Al alloy stretched material having the same alloy composition, but an Al alloy exhibiting another alloy composition. Stretched materials, copper and copper alloys, steel materials, etc. are also applicable.
以下に、本発明の実施例に基づいて更に詳細に説明するが、本発明はこれらに限定されるものではない。 Hereinafter, the present invention will be described in more detail based on examples, but the present invention is not limited thereto.
まず、表１及び表２に示す成分組成のＡｌ合金を常法の半連続鋳造法（ＤＣ鋳造）により溶解鋳造して、鋳塊を製造した。 First, an Al alloy having the composition shown in Tables 1 and 2 was melt cast by a conventional semi-continuous casting method (DC casting) to produce an ingot.
次に、この鋳塊を５００℃で５時間の均質化処理工程にかけ、５ｍｍ面削し額縁組織を除去した。次に、鋳塊を熱間圧延工程にかけた。熱間圧延工程の条件は、圧延開始温度が４８０℃とし、板厚３ｍｍの熱間圧延板を得た。次に、この熱間圧延板を冷間圧延工程にかけ、板厚１ｍｍの冷間圧延板を得た。冷間圧延工程では、加工率（圧下率）を３３％とした。更にこの冷間圧延板を３９０℃で４時間の条件で最終焼鈍を行い、高エネルギービーム溶接用Ａｌ合金材試料とした。なお、上記で作製した試料は全てＯ材である。 Next, this ingot was subjected to a homogenization treatment process at 500 ° C. for 5 hours, and the frame structure was removed by 5 mm chamfering. Next, the ingot was subjected to a hot rolling process. The conditions for the hot rolling process were a rolling start temperature of 480 ° C. and a hot rolled plate having a thickness of 3 mm. Next, this hot-rolled sheet was subjected to a cold rolling step to obtain a cold-rolled sheet having a thickness of 1 mm. In the cold rolling step, the processing rate (rolling rate) was 33%. Further, this cold-rolled sheet was subjected to final annealing at 390 ° C. for 4 hours to obtain an Al alloy material sample for high energy beam welding. In addition, all the samples produced above are O materials.
上記試料について以下の評価を行った。 The following evaluation was performed on the sample.
〔引張強度〕
上記で作製したＡｌ合金板の引張強度を測定した。引張強度はＪＩＳ Ｚ ２２０１で規定されるＪＩＳ５号試験片を試料から切り出し、ＪＩＳ Ｚ ２２４１準拠による引張試験により測定した。結果を表３に示す。
[Tensile strength]
The tensile strength of the Al alloy plate produced above was measured. Tensile strength was measured by cutting a JIS No. 5 test piece defined in JIS Z 2201 from a sample and performing a tensile test according to JIS Z 2241. The results are shown in Table 3.
〔溶接割れ〕
板厚１．０ｍｍを有する上記試料であるＡｌ合金板を２枚用いて、レーザによる突合せ溶接を実施し、溶接割れの評価を行った。レーザ照射条件は、出力が２０００Ｗ、速度が２０ｍ／ｍｉｎの連続波とし、溶接長は１００ｍｍとした。評価基準としては、溶接後の断面を観察し、溶接部表面及び断面に割れが無いものを「◎」、溶接部断面のみに割れが存在するものを「○」、断面及び表面に割れが存在するものを「×」として評価を行った。結果を表３に示す。
(Weld crack)
Butt welding by laser was performed using two Al alloy plates, which are the above samples having a plate thickness of 1.0 mm, to evaluate weld cracks. The laser irradiation conditions were a continuous wave with an output of 2000 W and a speed of 20 m / min, and a welding length of 100 mm. As the evaluation criteria, observe the cross-section after welding, "◎" if there is no crack on the weld surface and cross-section, "○" if there is a crack only on the weld cross-section, and cracks on the cross-section and surface The evaluation was performed with “×” as the item to be performed. The results are shown in Table 3.
〔イレギュラービード〕
板厚１．５ｍｍを有する上記試料であるＡｌ合金板を２枚用いて、レーザ出力を２０００Ｗとして、溶接速度を１５ｍ／ｍｉｎの連続波条件でビードオンプレート（ＢＯＰ）溶接を１０００ｍｍ施し、形成された溶接ビードの形状を測定し、イレギュラービードについて評価を行った。評価基準としては、ビード幅の最大値と最小値の差がビード算術平均幅に対して１０％未満の場合を「◎」、１０〜１５％の場合を「○」、１５％以上の場合を「×」として評価した。結果を表３に示す。
[Irregular beads]
Using two Al alloy plates, which are the above samples having a plate thickness of 1.5 mm, with a laser output of 2000 W and a bead-on-plate (BOP) welding of 1000 mm under a continuous wave condition of a welding speed of 15 m / min. The shape of the weld bead was measured and the irregular bead was evaluated. As an evaluation standard, the difference between the maximum value and the minimum value of the bead width is less than 10% with respect to the bead arithmetic average width, “◎”, 10 to 15% is “◯”, and 15% or more. Evaluated as “x”. The results are shown in Table 3.
〔ブローホール〕
前記イレギュラービードの評価を行った試料に対しＸ線透過像観察を行い、ブローホールの評価を行った。評価基準としては、溶接ビード１０００ｍｍを観察し、ブローホールが０．３個／ｍｍ未満の場合を「◎」、０．３〜０．６個／ｍｍの場合を「○」、０．６個／ｍｍを超える場合を「×」として評価した。結果を表３に示す。
〔blow hole〕
X-ray transmission image observation was performed on the sample on which the irregular beads were evaluated, and blowholes were evaluated. As an evaluation standard, a weld bead of 1000 mm was observed, “◎” when the blowhole was less than 0.3 pieces / mm, “◯” when 0.6 to 0.6 pieces / mm, and 0.6 pieces. When exceeding / mm, it evaluated as "x". The results are shown in Table 3.
〔溶接部の結晶粒径〕
前記イレギュラービード評価試験と同条件にてレーザ溶接を行った上記試料に対して、任意断面を光学顕微鏡にて観察し、これを画像解析ソフトによって解析することにより溶接部における平均結晶粒サイズを求めた。評価基準としては、平均結晶粒サイズが円相当直径で５０μｍ未満のものを「◎」、５０μｍ〜１５０μｍのものを「○」、１５０μｍを超えるものを「×」とした。結果を表３に示す。
[Grain size of weld zone]
With respect to the above sample subjected to laser welding under the same conditions as the irregular bead evaluation test, an arbitrary cross section is observed with an optical microscope, and this is analyzed by image analysis software to determine the average crystal grain size in the weld. Asked. As evaluation criteria, those having an average crystal grain size with an equivalent circle diameter of less than 50 μm were designated as “、”, those having a diameter of 50 μm to 150 μm as “◯”, and those having a mean crystal grain size exceeding 150 μm as “X”. The results are shown in Table 3.
表２に示すように、発明例１〜１７では、溶接割れ、イレギュラービード、ブローホール及び溶接部結晶粒径が優良であり、引張強度に優れる高エネルギービーム溶接用Ａｌ合金材が得られた。これに対して比較例２０〜３２では何れも、本発明の規定外の構成要件を含んでいた。 As shown in Table 2, in Invention Examples 1 to 17, an Al alloy material for high energy beam welding having excellent weld cracking, irregular beads, blowholes and weld grain size and excellent tensile strength was obtained. . On the other hand, in Comparative Examples 20 to 32, all of the constituent requirements outside the specification of the present invention were included.
比較例２０では、Ｍｇの含有量が多過ぎたために、溶接部に多数のブローホールが発生した。 In Comparative Example 20, since the content of Mg was too large, a large number of blow holes were generated in the welded portion.
比較例２１では、Ｍｇの含有量が少な過ぎたために、調質Ｏにおける引張強度が不足した。 In Comparative Example 21, the tensile strength in the refining O was insufficient because the Mg content was too small.
比較例２２では、Ｆｅの含有量が多過ぎたために、粗大なＡｌ−Ｆｅ系金属間化合物が形成されるため、加工性が低下すると共に溶接時の溶融挙動が不安定となった。その結果、溶接時にイレギュラービードが発生した。 In Comparative Example 22, since the Fe content was too large, a coarse Al—Fe intermetallic compound was formed, so that the workability was lowered and the melting behavior during welding became unstable. As a result, irregular beads were generated during welding.
比較例２３では、Ｆｅの含有量が少な過ぎたために、割れの抑制効果が不足となった。その結果、溶接部断面及び表面に割れが発生した。 In Comparative Example 23, since the Fe content was too small, the effect of suppressing cracking was insufficient. As a result, cracks occurred in the weld cross section and the surface.
比較例２４では、Ｓｉの含有量が多過ぎたために、溶接部断面及び表面に割れが発生した。 In Comparative Example 24, since the Si content was too large, cracks occurred on the weld cross section and the surface.
比較例２５では、Ｃｕの含有量が多過ぎたために、溶接部断面及び表面に割れが発生した。 In Comparative Example 25, since the Cu content was excessive, cracks occurred on the weld cross section and the surface.
比較例２６では、Ｍｎの含有量が多過ぎたために、溶接時にイレギュラービードが発生した。 In Comparative Example 26, since the Mn content was too large, irregular beads were generated during welding.
比較例２７では、Ｚｎの含有量が多過ぎたために、溶接部断面及び表面に割れが発生した。また溶接時にイレギュラービードが発生した。 In Comparative Example 27, since the Zn content was too large, cracks occurred on the weld cross section and the surface. Irregular beads were generated during welding.
比較例２８では、Ｃｒの含有量が多過ぎたために、粗大なＡｌ−Ｃｒ系金属間化合物が形成されるため、溶接ビードの不整が生じた。 In Comparative Example 28, since the content of Cr was too large, a coarse Al—Cr intermetallic compound was formed, resulting in irregular weld beads.
比較例２９では、Ｖの含有量が多過ぎたために、粗大なＡｌ−Ｖ系金属間化合物が形成されるため、溶接ビードの不整が生じた。 In Comparative Example 29, since the content of V was too large, a coarse Al—V intermetallic compound was formed, resulting in irregular weld beads.
比較例３０では、Ｎｉの含有量が多過ぎたために、粗大なＡｌ−Ｎｉ系、Ａｌ−Ｆｅ−Ｎｉ系金属間化合物が形成されるため、溶接ビードの不整が生じた。 In Comparative Example 30, since the Ni content was too large, coarse Al—Ni-based and Al—Fe—Ni-based intermetallic compounds were formed, resulting in irregular weld beads.
比較例３１では、Ｔｉ及びＢの含有量が多過ぎたために、粗大なＴｉ−Ｂ系の凝集物が形成されるため、溶接ビードの不整が生じた。 In Comparative Example 31, since the contents of Ti and B were too large, coarse Ti-B aggregates were formed, resulting in irregular weld beads.
比較例３２では、Ｔｉ及びＣの含有量が多過ぎたために、粗大なＴｉ−Ｃ系の凝集物が形成されるため、溶接ビードの不整が生じた。 In Comparative Example 32, since the contents of Ti and C were too large, coarse Ti—C agglomerates were formed, resulting in irregular weld beads.
本発明は、高エネルギービーム溶接において耐溶接割れ性に優れるＡｌ合金を提供することができ、その産業上の利用可能性に優れる。 INDUSTRIAL APPLICABILITY The present invention can provide an Al alloy having excellent weld crack resistance in high energy beam welding, and is excellent in industrial applicability.
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