JPH05169290A - Aluminum alloy filler material and its production - Google Patents
Aluminum alloy filler material and its productionInfo
- Publication number
- JPH05169290A JPH05169290A JP35368791A JP35368791A JPH05169290A JP H05169290 A JPH05169290 A JP H05169290A JP 35368791 A JP35368791 A JP 35368791A JP 35368791 A JP35368791 A JP 35368791A JP H05169290 A JPH05169290 A JP H05169290A
- Authority
- JP
- Japan
- Prior art keywords
- filler material
- aluminum alloy
- strength
- alloy filler
- melting
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Landscapes
- Laser Beam Processing (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は溶接に用いられるアルミ
ニウム合金溶加材、特にＡl−Ｚn−Ｍg系合金材料の溶
接に用いられる溶加材とその製造方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an aluminum alloy filler material used for welding, and more particularly to a filler material used for welding Al-Zn-Mg type alloy materials and a method for producing the same.
【０００２】[0002]
【従来の技術】溶融溶接が可能なＡl−Ｚn−Ｍg系合金
は車両、橋梁や他の構造物に広く用いられている。本系
合金は、共材の溶加材で溶接した場合、継手強度は高く
なるものの、割れ感受性が高く、溶接割れや応力腐食割
れが発生し易い。このため、実施施工では母材と成分の
異なるＡl−Ｍg系の５３５６、５１８３や５０５６が溶
加材として用いられる。一方、パルス溶接などにより溶
湯を撹拌して結晶粒を微細化する方法も用いられている
が、実施施工では溶接割れの発生を完全に防止すること
はできない。また、溶接部と母材の組成が異なるため、
母材の強さに比べ溶接継手部の強さが低く、高性能、大
型化が阻害されている。2. Description of the Related Art Al-Zn-Mg type alloys which can be melt-welded are widely used for vehicles, bridges and other structures. When the present alloy is welded with a filler metal as a co-material, the joint strength is high, but the crack susceptibility is high, and weld cracking and stress corrosion cracking are likely to occur. For this reason, Al-Mg-based 5356, 5183, and 5056, which have different components from the base metal, are used as the filler in the actual construction. On the other hand, there is also used a method of refining crystal grains by stirring the molten metal by pulse welding or the like, but it is not possible to completely prevent the occurrence of welding cracks in the actual construction. Also, because the composition of the weld and the base metal is different,
The strength of the welded joint is lower than the strength of the base metal, which hinders high performance and large size.
【０００３】[0003]
【発明が解決しようとする課題】上述のように、本系合
金は強度を高めるためにＺn、Ｍgが含有されているが、
高強度化により割れ感受性が高くなり溶接割れや応力腐
食割れが発生し易くなるため、従来より、割れ感受性の
低いＡl−Ｍg系の５３５６や５１８３等が溶加材として
用いられているが、その溶接金属部は、時効硬化性が劣
ったりするため、溶接後の時効処理での強度の向上は期
待できない。そのため、高強度である母材に比べ溶接部
の強さが著しく劣るという問題があった。As described above, the present alloy contains Zn and Mg in order to enhance the strength.
Since cracking susceptibility increases due to higher strength and weld cracking and stress corrosion cracking are more likely to occur, Al-Mg-based 5356 and 5183, which have low cracking susceptibility, have been conventionally used as filler metals. Since the age-hardening property of the welded metal part is poor, improvement in strength cannot be expected in the aging treatment after welding. Therefore, there is a problem that the strength of the welded portion is significantly inferior to that of the base material having high strength.
【０００４】一方、割れ感受性を改善する方法として
は、例えば、「軽金属」Ｖol.１９、Ｎo.１１(１９６
９)、ｐ.４７０〜４８０に示すように、Ｚr、ＴiやＢの
微量添加が有効であり、特にＺrの添加が最も効果的
で、添加量が多い程、効果は顕著であることが知られて
いる。On the other hand, as a method for improving the susceptibility to cracking, for example, “Light Metal”, Vol. 19, No. 11 (196).
9), p.470-480, it is effective to add a small amount of Zr, Ti or B. Especially, it is known that the addition of Zr is the most effective, and the larger the addition amount, the more remarkable the effect. Has been.
【０００５】ところで、平衡状態におけるＺrの固溶量
は最大で０.３％であり、本系合金の割れ感受性を実用
上問題のないレベルまで改善するためには固溶量以上の
Ｚr添加が必要である。しかし、通常の金型を用いる鋳
造法では凝固速度が１０2℃／sec以下と遅く、固溶量以
上のＺrを添加すると、過剰なＺrは巨大な晶出物を形成
する。その結果、圧延や線引き等の加工性悪化を引き起
こすため、実用上、Ｚrの添加は固溶量範囲内に限定さ
れ、本系合金の溶接割れ感受性の改善には限界があっ
た。In the meantime, the solid solution amount of Zr in the equilibrium state is 0.3% at maximum, and in order to improve the crack susceptibility of this system alloy to a level where there is no practical problem, addition of Zr in excess of the solid solution amount is required. is necessary. However, in the casting method using a normal die, the solidification rate is as slow as 10 2 ° C / sec or less, and when Zr in a solid solution amount or more is added, excess Zr forms a huge crystallized substance. As a result, since workability such as rolling and wire drawing is deteriorated, the addition of Zr is practically limited within the range of the amount of solid solution, and there is a limit in improving the weld crack susceptibility of the present alloy.
【０００６】一方、前述のパルス溶接法などにより溶湯
を撹拌して結晶粒を微細化する方法は、市販の溶接機で
は溶接条件的に微細化効果が少なかったり、装置的に付
与設備を必要として大掛かりとなり、実用的ではない。On the other hand, the method of agitating the molten metal by the above-mentioned pulse welding method or the like to refine the crystal grains does not have a sufficient refining effect in terms of welding conditions in a commercially available welding machine, or requires equipment for providing equipment. It is a large scale and not practical.
【０００７】以上のとおり、本系合金の溶加材には、従
来より、割れ感受性の低いＡl−Ｍg系の溶加材(例え
ば、５３５６や５１８３等)が使用されているが、強
度、耐割れ性の観点で問題が多く、高性能、軽量化の障
害となっていることから、高い継手強度を有し、耐割れ
性に優れた溶加材に対する強いニーズがある。As described above, Al-Mg type fillers (for example, 5356 and 5183) having low cracking susceptibility have been conventionally used as filler metals for the alloys of the present invention. Since there are many problems from the viewpoint of crackability and they hinder high performance and weight reduction, there is a strong need for a filler material having high joint strength and excellent crack resistance.
【０００８】本発明は、かゝるニーズに応えるべくなさ
れたものであって、Ａl−Ｚn−Ｍg系アルミニウム合金
材料に対して、その耐割れ性を改善しつつ、溶接継手部
の強度向上を兼ね備えたアルミニウム合金溶加材を提供
することを目的とするものである。The present invention has been made in order to meet such needs, and it is possible to improve the strength of the welded joint portion while improving the crack resistance of the Al-Zn-Mg type aluminum alloy material. The object is to provide an aluminum alloy filler material having the dual function.
【０００９】[0009]
【課題を解決するための手段】前記課題を解決するた
め、本発明者は、従来のＡl−Ｚn−Ｍg系アルミニウム
合金溶加材の欠点を改善し得る方策について鋭意研究を
重ねた。その結果、Ａl−Ｍg−Ｚn系組成に高含有量の
Ｚrを添加し、溶接割れ性を改善しつつ溶接継手部の強
度向上を図ること、また、Ａgを添加することにより耐
応力腐食割れ性を改善させること、更には、高含有量の
Ｚrを添加させる方法として、通常法で造塊した鋳塊を
高エネルギー密度を有するエネルギービームにより再溶
融し、急速凝固させることにより、固溶量より多いＺr
を含有させることができることを見い出し、これらの知
見に基づいて本発明をなしたものである。In order to solve the above-mentioned problems, the inventor of the present invention has earnestly studied a method for improving the drawbacks of the conventional Al-Zn-Mg type aluminum alloy filler metal. As a result, a high content of Zr is added to the Al-Mg-Zn composition to improve the strength of the weld joint while improving the weld crackability, and the stress corrosion cracking resistance is improved by adding Ag. In addition, as a method of adding a high content of Zr, the ingot produced by the usual method is remelted by an energy beam having a high energy density and rapidly solidified Many Zr
The present invention has been made on the basis of these findings, by discovering that it is possible to incorporate
【００１０】すなわち、本発明は、Ｚn:１〜６％、Ｍg:
３〜６％(但し、Ｚn≦Ｍg)、Ｍn:０.２〜０.９％、Ｃr:
０.０５〜０.５％、Ｔi:０.０５〜０.２％、Ｂ:０.０１
〜０.２％及びＺr:０.０５〜２％を含有し、必要に応じ
て更にＡg:０.０２〜１％を含有し、残部がＡlと不可避
的不純物からなることを特徴とするＡl−Ｍg−Ｚn系ア
ルミニウム合金溶加材を要旨とするものである。That is, in the present invention, Zn: 1 to 6%, Mg:
3 to 6% (however Zn ≦ Mg), Mn: 0.2 to 0.9%, Cr:
0.05-0.5%, Ti: 0.05-0.2%, B: 0.01
.About.0.2% and Zr: 0.05 to 2%, and optionally Ag: 0.02 to 1%, and the balance Al and unavoidable impurities. -Mg-Zn type aluminum alloy filler material is the main point.
【００１１】また、その製造方法は、通常の方法により
鋳造した上記化学成分を有するアルミニウム合金鋳塊
を、１０4〜１０9w／mm2と高いパワー密度を有するエネ
ルギービームを用い、かつ１回の溶融幅を３０mm以下と
するゾーンメルティング法で再溶融し、１〜３×１０2
℃／sec以上の凝固速度で急速凝固させることを特徴と
するものである。The manufacturing method is such that an aluminum alloy ingot having the above chemical composition cast by a usual method is used once with an energy beam having a high power density of 10 4 to 10 9 w / mm 2. 1 to 3 × 10 2 by remelting by the zone melting method with the melting width of 30 mm or less.
It is characterized by rapid solidification at a solidification rate of ° C / sec or more.
【００１２】以下に本発明を更に詳述する。The present invention will be described in more detail below.
【００１３】[0013]
【００１４】まず、本発明のアルミニウム合金溶加材に
おける化学成分の限定理由について説明する。First, the reasons for limiting the chemical components in the aluminum alloy filler material of the present invention will be described.
【００１５】Ｚn、Ｍg：ＺnとＭgは、アルミニウム合金
中においてＭgＺn2、Ａl2Ｍg3Ｚn3などの化合物を生成
し、強化元素として作用するが、Ｚnが１％未満、Ｍgが
３％未満ではこの効果がなく、また、Ｚn、Ｍgがそれぞ
れ６％を超えると加工性や応力腐食割れに対する抵抗が
劣化するので不適当である。よって、Ｚn量は１〜６
％、Ｍgは３〜６％の範囲とする。Zn, Mg: Zn and Mg form compounds such as MgZn 2 , Al 2 Mg 3 Zn 3 in an aluminum alloy and act as a strengthening element, but Zn is less than 1% and Mg is less than 3%. However, this effect is not obtained, and if Zn and Mg exceed 6% each, workability and resistance to stress corrosion cracking deteriorate, which is not suitable. Therefore, the amount of Zn is 1-6
% And Mg are in the range of 3 to 6%.
【００１６】但し、上記範囲において、Ｚn量は、Ｍg量
と等しいか、又は少ない量とする必要がある。すなわ
ち、ＺnはＭgと共に強化元素として作用するが、Ａl−
Ｚn−Ｍg系の三元合金を共金系の溶加材で溶接すると溶
接割れや感受性が高くなるために、Ｚn量はＭg量より多
く添加できず、両者の関係はＺn≦Ｍgとする。However, in the above range, the Zn content must be equal to or less than the Mg content. That is, Zn acts as a strengthening element together with Mg, but Al-
When a Zn-Mg ternary alloy is welded with a common-metal filler metal, weld cracking and susceptibility increase, so the Zn content cannot be added in excess of the Mg content, and the relationship between them is Zn≤Mg.
【００１７】Ｍn：Ｍnは、０.２％以上であれば強度及
び耐応力腐食割れ性を改善するが、０.９％を越えて含
有すると巨大化合物を生成するので好ましくない。よっ
て、Ｍn量は０.２〜０.９％の範囲とする。Mn: If Mn is 0.2% or more, the strength and stress corrosion cracking resistance are improved, but if it exceeds 0.9%, a huge compound is formed, which is not preferable. Therefore, the amount of Mn is made into the range of 0.2-0.9%.
【００１８】Ｃr：Ｃrは、結晶粒を微細化し、強度及び
耐応力腐食割れ性を改善するが、そのためには０.０５
％以上が必要である。しかし、０.５％を超えると機械
的性質を劣化させるので不適当である。よって、Ｃr量
は０.０５〜０.５％の範囲とする。Cr: Cr refines the crystal grains to improve the strength and the resistance to stress corrosion cracking.
% Or more is required. However, if it exceeds 0.5%, mechanical properties are deteriorated, so that it is unsuitable. Therefore, the Cr content is set to be in the range of 0.05 to 0.5%.
【００１９】Ｔi、Ｂ：Ｔi及びＢは、結晶粒微細化によ
り溶接割れ性を改善するが、Ｔiが０.０５％未満、Ｂが
０.０１％未満ではその効果がなく、またＴi、Ｂがそれ
ぞれ０.２％を超えるとＡlとの化合物を形成し、靭性を
劣化させるという点で不適当である。よって、Ｔi量は
０.０５〜０.２％、Ｂ量は０.０１〜０.２％の範囲とす
る。Ti, B: Ti and B improve the weld cracking property by refining the crystal grains, but when Ti is less than 0.05% and B is less than 0.01%, there is no effect. If each exceeds 0.2%, it is unsuitable in that it forms a compound with Al and deteriorates the toughness. Therefore, the Ti content is set to 0.05 to 0.2%, and the B content is set to 0.01 to 0.2%.
【００２０】Ｚr：Ｚrは、Ｔi及びＢと同様に、結晶粒
微細化により溶接割れ性を改善するが、０.０５％未満
では溶接割れ防止効果に乏しい。逆に、２％を超えると
加工性、靭性を悪化させるので好ましくない。よって、
Ｚr量は０.０５〜２％の範囲とする。なお、Ｚrを固溶
量以上に含有させるには、後述の製造方法によると、巨
大晶出物の形成並びに加工性悪化を伴うことがない。Zr: Zr, like Ti and B, improves the weld cracking property by refining the crystal grains, but if it is less than 0.05%, the effect of preventing weld cracking is poor. On the contrary, if it exceeds 2%, workability and toughness are deteriorated, which is not preferable. Therefore,
The amount of Zr is set in the range of 0.05 to 2%. Incidentally, in order to contain Zr in a solid solution amount or more, according to the manufacturing method described later, formation of giant crystallized substances and deterioration of workability are not accompanied.
【００２１】Ａg：Ａgは、応力腐食割れ性を改善し強度
を増大させる効果があるので、必要に応じて添加する。
しかし、０.０２％未満ではその効果が少なく、また１
％を超えると溶接性が劣ったり、また不経済でもあるの
で好ましくない。よって、Ａg量は０.０２〜１％の範囲
とする。Ag: Ag has the effect of improving the stress corrosion cracking property and increasing the strength, so it is added if necessary.
However, if less than 0.02%, the effect is small, and
% Is not preferable because weldability is poor and it is uneconomical. Therefore, the amount of Ag is set in the range of 0.02 to 1%.
【００２２】次に、上述のＡl−Ｍg−Ｚn系アルミニウ
ム合金溶加材の製造方法について説明する。Next, a method of manufacturing the above Al-Mg-Zn type aluminum alloy filler material will be described.
【００２３】Ｚrは、消失元素であるため、溶加材に添
加する場合は、母材に添加する場合に比べて割れ防止に
対する効果は減少する。そのため、割れ性を改善するた
めには母材に添加するより多くのＺr量の添加が必要と
なるが、平衡状態におけるＺrの固溶量は０.３％以下で
あり、通常の金型を用いる鋳造法では、凝固時の冷却速
度が１０2℃／sec以下と遅いために、固溶量以上のＺr
添加では巨大な晶出物を形成し、加工性の悪化を引き起
こすため好ましくない。Since Zr is a vanishing element, when it is added to the filler material, the effect of preventing cracking is reduced compared to when it is added to the base material. Therefore, in order to improve the crackability, it is necessary to add a larger amount of Zr than that added to the base material, but the solid solution amount of Zr in the equilibrium state is 0.3% or less, and it is In the casting method used, since the cooling rate during solidification is as slow as 10 2 ° C / sec or less, Zr above the solid solution amount is used.
If added, a huge crystallized product is formed and the workability is deteriorated, which is not preferable.
【００２４】そこで、本発明者等はこの改善策について
鋭意研究を重ねた。まず、パワー密度が１０4〜１０9w
／mm2と非常に高いエネルギー密度を有するエネルギー
ビームを溶接に応用した場合、ビード幅が非常に狭く、
溶込みの深いビードが形成されると共に、凝固時の冷却
速度が非常に大きいことに着目した。例えば、パワー密
度が１０3w／mm2以下の場合は凝固時の冷却速度が１〜
３×１０2℃／sec以下となるが、パワー密度が１０4w／
mm2以上の場合は、３×１０2℃／sec以上の冷却速度が
得られる。Therefore, the inventors of the present invention have conducted intensive studies on this improvement measure. First, the power density is 10 4 to 10 9 w
When applying an energy beam with a very high energy density of / mm 2 to welding, the bead width is very narrow,
We focused on the fact that a bead with deep penetration was formed and the cooling rate during solidification was very high. For example, when the power density is 10 3 w / mm 2 or less, the cooling rate during solidification is 1 to
3 × 10 2 ° C / sec or less, but power density is 10 4 w /
In the case of mm 2 or more, a cooling rate of 3 × 10 2 ° C / sec or more can be obtained.
【００２５】この原理を、固溶量以上のＺrを含有させ
たアルミニウム合金を通常の金型(冷却速度は１０2℃／
sec以下)を用いて鋳造した鋳塊の再溶解に適用したとこ
ろ、巨大な晶出物を形成することなく、また加工性の悪
化を引き起こすことなく、固溶量以上の高Ｚrを含有さ
せられることが判明した。According to this principle, an aluminum alloy containing a solid solution amount of Zr or more is used in an ordinary die (cooling rate is 10 2 ° C /
When applied to the remelting of ingots cast using (sec or less), it can contain a high amount of solid solution Zr or more without forming huge crystallized substances and causing deterioration of workability. It has been found.
【００２６】その際、肉厚方向に完全に再溶融させるた
めに、例えば、後述の表２に示す条件を用い、適当なリ
メルトピッチで、１回の溶融幅が３０mm以下でゾーンメ
ルティングすることにより、鋳塊の冷却速度は３×１０
2℃／sec以上となり、急速凝固が可能となる。At this time, in order to completely remelt in the thickness direction, for example, by using the conditions shown in Table 2 described later, zone melting is performed with an appropriate remelt pitch and a single melting width of 30 mm or less. , Cooling rate of ingot is 3 × 10
2 ° C / sec or more, enabling rapid solidification.
【００２７】このような高いエネルギー密度を有するエ
ネルギービームとしては、電子ビームやレーザが挙げら
れる。熱源を連続的でなくパワー密度を集約(高く)し周
期的に照射する方法では１０9w／mm2以上のパワー密度
を得ることは可能であるが、本方法のように連続的に熱
源を照射する方法では、現在の設備では能力的に不可能
である。よって、パワー密度の上限は１０9w／mm2とす
る。Examples of the energy beam having such a high energy density include an electron beam and a laser. Although it is possible to obtain a power density of 10 9 w / mm 2 or more by the method of irradiating the heat source not continuously but by consolidating (increasing) the power density (higher), it is possible to continuously obtain the heat source like this method. Irradiation methods are not possible with current equipment. Therefore, the upper limit of the power density is 10 9 w / mm 2 .
【００２８】なお、現状では、設備の能力的にゾーンメ
ルティング法以外の方法では凝固時の冷却速度が遅く不
可能である。また、本法以外に急速凝固させる方法には
連続鋳造法があるが、現状の技術ではゾーンメルティン
グ法に相当する冷却速度が得られない。At present, the cooling rate at the time of solidification cannot be slowed by a method other than the zone melting method due to the capacity of the equipment. In addition to the present method, there is a continuous casting method as a method for rapid solidification, but the cooling rate equivalent to the zone melting method cannot be obtained with the current technology.
【００２９】本溶加材を用いる母材としては、Ａl−Ｚn
−Ｍg系３元アルミニウム合金が最も好ましく、その成
分組成、並びに溶接法は特に制限はない。The base material using the present filler metal is Al--Zn.
-Mg-based ternary aluminum alloy is most preferable, and its component composition and welding method are not particularly limited.
【００３０】次に本発明の実施例を示す。Next, examples of the present invention will be shown.
【００３１】[0031]
【表１】 に示す化学成分を有するアルミニウム合金のうち、Ｎo.
１〜Ｎo.１９のアルミニウム合金を通常法で鋳造し、得
られた鋳塊(板厚５０mm)を、電子ビームを用い、[Table 1] Among the aluminum alloys having the chemical composition shown in No.
Aluminum alloy of No. 1 to No. 19 was cast by a usual method, and the obtained ingot (plate thickness 50 mm) was used with an electron beam,
【表２】 に示す条件で、リメルトピッチ１５mmで、１回の溶融幅
が１５〜３０mmとなる条件で、両面から板厚方向に完全
に溶融するように鋳塊の幅、及び長さ方向に再溶融凝固
させた後、圧延、線引きにより、線径３.２mmの溶接棒
を製作し、ＴＩＧ溶接に供した。[Table 2] Under the conditions shown in (1), the ingot was remelted and solidified in the width direction and the length direction so as to be completely melted from both sides in the plate thickness direction under the condition that the remelt pitch was 15 mm and the one-time melting width was 15 to 30 mm. After that, by rolling and drawing, a welding rod having a wire diameter of 3.2 mm was manufactured and subjected to TIG welding.
【００３２】表１のＮo.１〜Ｎo.７が本発明例である。
比較のため、従来合金の５３５６(表１中のＮo.２０)も
用いた。母材には代表的なＡl−Ｚn−Ｍg系合金である
Ａ７Ｎ０１-Ｔ６を用いた。No. 1 to No. 7 in Table 1 are examples of the present invention.
For comparison, a conventional alloy 5356 (No. 20 in Table 1) was also used. A7N01-T6, which is a typical Al-Zn-Mg type alloy, was used as the base material.
【表３】 に溶接試験結果を示す。[Table 3] The welding test results are shown in.
【００３３】なお、溶接割れ感受性は、板厚２mmのフィ
ッシュボーン型試験法を用い、ＡＣ・ＴＩＧ法で試験を
行い、割れ率(％)＝(割れ長さ／溶接全長)×１００を求
めて評価した。継手強度については、板厚６mmのＶ開先
(開先角度は９０°)を片面２パスで仕上げ、室温で１ヶ
月の常温時効処理を実施した後、余盛を削除して強度試
験を行った。応力腐食割れ性は、３点支持法により１５
kg／mm2の応力を加え、１００℃で３g／１のＮaＣlと３
６g／１のＣrＯ3と３０g／１のＫ2Ｃr2Ｏ7との混合水溶
液に浸漬し、割れを観察して評価した。また、加工性
は、溶接棒製作工程における圧延加工時の耳割れの有無
により判定した。評価は、従来合金の５３５６との対比
で行い、◎(特に優れている)、○(優れている)、△(同
等)、×(劣る)の４段階で評価した。The weld crack susceptibility was tested by the AC / TIG method using a fishbone type test method with a plate thickness of 2 mm, and the crack rate (%) = (crack length / weld total length) × 100 was obtained. evaluated. Regarding joint strength, V groove with a plate thickness of 6 mm
(Groove angle of 90 °) was finished on two passes on one side, and after normal temperature aging treatment for one month at room temperature, the extra reinforcement was removed and a strength test was conducted. The stress corrosion cracking property is 15 by the three-point support method.
Apply 3 kg / mm 2 of stress and 100 g of 3g / 1 NaCl.
It was immersed in a mixed aqueous solution of 6 g / 1 of CrO 3 and 30 g / 1 of K 2 Cr 2 O 7, and cracks were observed and evaluated. The workability was determined by the presence or absence of edge cracks during rolling in the welding rod manufacturing process. The evaluation was performed in comparison with the conventional alloy 5356, and was evaluated in four grades of ⊚ (especially excellent), ◯ (excellent), Δ (equivalent), and × (inferior).
【００３４】また、In addition,
【表４】 に圧延加工におけるインゴットの種類についての試験結
果を示す。判定は、圧延加工における割れの有無により
判定し、１個の割れの長さが１０mm以下を○、１０mm以
上を×とした。[Table 4] The test results for the types of ingots used in the rolling process are shown in. The judgment was made based on the presence or absence of cracks in the rolling process, and the crack length of one crack was 10 mm or less, and ◯ was 10 mm or more.
【００３５】表３より、以下のように考察される。From Table 3, the following is considered.
【００３６】本発明例のＮo.１〜Ｎo.７は、いずれも、
継手強度が高く、耐割れ性、加工性が優れている。No. 1 to No. 7 of the present invention are all
High joint strength, excellent crack resistance and workability.
【００３７】一方、比較例Ｎo.８はＺn量が少なく、継
手強度が現状と同等で改善効果が認められない。また、
Ｎo.９はＺn量が多く、継手強度は改善されるが、加工
性が悪化している。On the other hand, Comparative Example No. 8 has a small amount of Zn, the joint strength is the same as the present condition, and no improvement effect is observed. Also,
No. 9 has a large amount of Zn and the joint strength is improved, but the workability is deteriorated.
【００３８】Ｎo.１０はＭg量が少なく、継手強度の改
善が認められない。Ｎo.１１はＭg量が多く、割れ感受
性及び継手強度の改善は認められるものの、加工性が悪
化している。No. 10 has a small amount of Mg and no improvement in joint strength is observed. No. 11 has a large amount of Mg, and although crack susceptibility and joint strength are improved, the workability is deteriorated.
【００３９】Ｎo.１２は、継手強度の改善効果は認めら
れるものの、Ｚr量が少ないために割れ感受性の改善が
認められない。Ｎo.１３は、逆にＺr量が多いために割
れ感受性及び継手強度の改善効果は認められるものの、
加工性の悪化を引き起こすので好ましくない。In No. 12, although the effect of improving the joint strength is recognized, the improvement in crack susceptibility is not recognized because the amount of Zr is small. On the other hand, No. 13 has a large amount of Zr, so that crack susceptibility and joint strength improving effects are recognized, but
It is not preferable because it causes deterioration of workability.
【００４０】Ｎo.１４は、Ｔi、Ｂ量が少なく割れ感受
性の改善効果が少ない。Ｎo.１５は逆にＴi、Ｂ量が多
く、継手強度の改善効果が認められない。No. 14 has a small amount of Ti and B and has a small effect of improving crack susceptibility. On the contrary, No. 15 has a large amount of Ti and B, and the effect of improving the joint strength is not recognized.
【００４１】Ｎo.１６はＭn量が少なく継手強度の改善
効果が少ない。Ｎo.１７は逆にＭn量が多く加工性の悪
化を引き起こすので好ましくない。No. 16 has a small amount of Mn and little improvement effect on joint strength. On the contrary, No. 17 is not preferable because it has a large amount of Mn, which causes deterioration of workability.
【００４２】Ｎo.１８はＣr量が少なく耐割れ性の改善
が認められず、効果が少ない。また、従来合金のＮo.１
９は、Ｃr量が多く加工性が悪化している。No. 18 has a small amount of Cr and no improvement in cracking resistance is observed, and the effect is small. In addition, the conventional alloy No. 1
In No. 9, the amount of Cr is large and the workability is deteriorated.
【００４３】また、加工におけるインゴットの影響につ
いては、表４に示すように、通常法に比べ、本発明法
(再溶融法)が圧延加工時における耳割れの発生も少な
く、優れていることがわかる。As to the influence of the ingot on the processing, as shown in Table 4, the method according to the present invention was compared with the conventional method.
It can be seen that the (remelting method) is excellent in that the occurrence of edge cracks during rolling is small.
【００４４】[0044]
【発明の効果】以上詳述したように、本発明の溶加材に
よれば、Ａl−Ｚn−Ｍg系アルミニウム合金の溶接に適
し、耐割れ性を改善し、更に高い継手強度が得られる。
また加工性も優れているので、その工業上の効果は顕著
である。As described in detail above, the filler metal of the present invention is suitable for welding Al-Zn-Mg type aluminum alloys, has improved crack resistance, and has higher joint strength.
Further, since it has excellent workability, its industrial effect is remarkable.
Claims (3)
Ｍg:３〜６％(但し、Ｚn≦Ｍg)、Ｍn:０.２〜０.９％、
Ｃr:０.０５〜０.５％、Ｔi:０.０５〜０.２％、Ｂ:０.
０１〜０.２％及びＺr:０.０５〜２％を含有し、残部が
Ａlと不可避的不純物からなることを特徴とするＡl−Ｍ
g−Ｚn系アルミニウム合金溶加材。1. By weight% (hereinafter, the same), Zn: 1 to 6%,
Mg: 3 to 6% (however Zn ≦ Mg), Mn: 0.2 to 0.9%,
Cr: 0.05-0.5%, Ti: 0.05-0.2%, B: 0.0.
Al-M containing 01 to 0.2% and Zr: 0.05 to 2%, the balance being Al and inevitable impurities.
g-Zn aluminum alloy filler material.
≦Ｍg)、Ｍn:０.２〜０.９%、Ｃr:０.０５〜０.５％、
Ｔi:０.０５〜０.２％、Ｂ:０.０１〜０.２％及びＺr:
０.０５〜２％を含有し、更にＡg:０.０２〜１％を含有
し、残部がＡlと不可避的不純物からなることを特徴と
するＡl−Ｍg−Ｚn系アルミニウム合金溶加材。2. Zn: 1 to 6%, Mg: 3 to 6% (however, Zn:
≤ Mg), Mn: 0.2-0.9%, Cr: 0.05-0.5%,
Ti: 0.05-0.2%, B: 0.01-0.2% and Zr:
An Al-Mg-Zn-based aluminum alloy filler material containing 0.05 to 2%, further containing Ag: 0.02 to 1%, and the balance being Al and inevitable impurities.
２に記載の化学成分を有するアルミニウム合金鋳塊を、
１０4〜１０9w／mm2と高いパワー密度を有するエネルギ
ービームを用い、かつ１回の溶融幅を３０mm以下とする
ゾーンメルティング法で再溶融し、１〜３×１０2℃／s
ec以上の凝固速度で急速凝固させることを特徴とするＡ
l−Ｍg−Ｚn系アルミニウム合金溶加材の製造方法。3. An aluminum alloy ingot having the chemical composition according to claim 1, which is cast by a normal method,
1 to 3 × 10 2 ° C / s by using an energy beam having a high power density of 10 4 to 10 9 w / mm 2 and remelting by a zone melting method with a melting width of 30 mm or less once.
A characterized by rapid solidification at a solidification rate of ec or higher
A method for producing an l-Mg-Zn-based aluminum alloy filler material.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP35368791A JP3219293B2 (en) | 1991-12-18 | 1991-12-18 | Aluminum alloy filler metal and its manufacturing method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP35368791A JP3219293B2 (en) | 1991-12-18 | 1991-12-18 | Aluminum alloy filler metal and its manufacturing method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH05169290A true JPH05169290A (en) | 1993-07-09 |
| JP3219293B2 JP3219293B2 (en) | 2001-10-15 |
Family
ID=18432539
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP35368791A Expired - Fee Related JP3219293B2 (en) | 1991-12-18 | 1991-12-18 | Aluminum alloy filler metal and its manufacturing method |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3219293B2 (en) |
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1999017903A1 (en) * | 1997-10-03 | 1999-04-15 | Hoogovens Aluminium Walzprodukte Gmbh | Aluminium-magnesium weld filler alloy |
| US6238495B1 (en) | 1996-04-04 | 2001-05-29 | Corus Aluminium Walzprodukte Gmbh | Aluminium-magnesium alloy plate or extrusion |
| EP1249303A1 (en) * | 2001-03-15 | 2002-10-16 | McCook Metals L.L.C. | High titanium/zirconium filler wire for aluminum alloys and method of welding |
| WO2006040034A1 (en) * | 2004-10-15 | 2006-04-20 | Aleris Aluminum Koblenz Gmbh | Al-mg-mn weld filler alloy |
| US7494043B2 (en) | 2004-10-15 | 2009-02-24 | Aleris Aluminum Koblenz Gmbh | Method for constructing a welded construction utilizing an Al-Mg-Mn weld filler alloy |
| WO2010060021A1 (en) * | 2008-11-24 | 2010-05-27 | Alcoa Inc. | Fusion weldable filler alloys |
| WO2010126748A1 (en) * | 2009-04-29 | 2010-11-04 | Alcoa Inc. | 7xxx weld filler alloys and methods of using the same |
| CN101972902A (en) * | 2010-11-22 | 2011-02-16 | 山东电力研究院 | Aluminum alloy welding flux for copper and aluminum welding |
| CN105401022A (en) * | 2015-11-14 | 2016-03-16 | 合肥标兵凯基新型材料有限公司 | High-toughness corrosion-resistant aluminum alloy and preparation method thereof |
| CN108396206A (en) * | 2018-03-06 | 2018-08-14 | 东北大学 | A kind of Al-Mg-Zn aluminium alloy welding wires and preparation method thereof |
| CN114341377A (en) * | 2019-09-03 | 2022-04-12 | 日本轻金属株式会社 | Bright aluminum alloy and bright aluminum alloy die casting material |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104646850A (en) * | 2015-01-09 | 2015-05-27 | 西安交通大学 | Al-Cu-Mg-Ti quaternary active solder for high-volume-fraction cast aluminum-based composite material, and preparation method for Al-Cu-Mg-Ti quaternary active solder |
-
1991
- 1991-12-18 JP JP35368791A patent/JP3219293B2/en not_active Expired - Fee Related
Cited By (17)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6238495B1 (en) | 1996-04-04 | 2001-05-29 | Corus Aluminium Walzprodukte Gmbh | Aluminium-magnesium alloy plate or extrusion |
| US6342113B2 (en) | 1996-04-04 | 2002-01-29 | Corus Aluminium Walzprodukte Gmbh | Aluminum-magnesium alloy plate or extrusion |
| WO1999017903A1 (en) * | 1997-10-03 | 1999-04-15 | Hoogovens Aluminium Walzprodukte Gmbh | Aluminium-magnesium weld filler alloy |
| AU732493B2 (en) * | 1997-10-03 | 2001-04-26 | Corus Aluminium Walzprodukte Gmbh | Aluminium-magnesium weld filler alloy |
| US6416884B1 (en) | 1997-10-03 | 2002-07-09 | Corus Aluminium Walzprodukte Gmbh | Aluminium-magnesium weld filler alloy |
| CN1098743C (en) * | 1997-10-03 | 2003-01-15 | 荷高文斯铝轧制品有限公司 | Aluminium-Magnesium weld filler alloy |
| KR100495261B1 (en) * | 1997-10-03 | 2005-06-14 | 후고벤스 알루미늄 발츠프로두크테 게엠베하 | Aluminium-magnesium weld filler alloy |
| EP1249303A1 (en) * | 2001-03-15 | 2002-10-16 | McCook Metals L.L.C. | High titanium/zirconium filler wire for aluminum alloys and method of welding |
| WO2006040034A1 (en) * | 2004-10-15 | 2006-04-20 | Aleris Aluminum Koblenz Gmbh | Al-mg-mn weld filler alloy |
| US7494043B2 (en) | 2004-10-15 | 2009-02-24 | Aleris Aluminum Koblenz Gmbh | Method for constructing a welded construction utilizing an Al-Mg-Mn weld filler alloy |
| WO2010060021A1 (en) * | 2008-11-24 | 2010-05-27 | Alcoa Inc. | Fusion weldable filler alloys |
| WO2010126748A1 (en) * | 2009-04-29 | 2010-11-04 | Alcoa Inc. | 7xxx weld filler alloys and methods of using the same |
| CN101890599A (en) * | 2009-04-29 | 2010-11-24 | 美铝公司 | 7xxx weld filler alloys and using method thereof |
| CN101972902A (en) * | 2010-11-22 | 2011-02-16 | 山东电力研究院 | Aluminum alloy welding flux for copper and aluminum welding |
| CN105401022A (en) * | 2015-11-14 | 2016-03-16 | 合肥标兵凯基新型材料有限公司 | High-toughness corrosion-resistant aluminum alloy and preparation method thereof |
| CN108396206A (en) * | 2018-03-06 | 2018-08-14 | 东北大学 | A kind of Al-Mg-Zn aluminium alloy welding wires and preparation method thereof |
| CN114341377A (en) * | 2019-09-03 | 2022-04-12 | 日本轻金属株式会社 | Bright aluminum alloy and bright aluminum alloy die casting material |
Also Published As
| Publication number | Publication date |
|---|---|
| JP3219293B2 (en) | 2001-10-15 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US11267081B2 (en) | Aluminum welding filler composition suitable for formation into wire used for fusion welding | |
| JP4101749B2 (en) | Weldable high strength Al-Mg-Si alloy | |
| JP5652574B1 (en) | Solid wire for gas shielded arc welding, gas shielded arc welding metal, welded joint, welded member, welding method, and method of manufacturing welded joint | |
| JPH0686027B2 (en) | Electric arc welding method | |
| EP3265264B1 (en) | Process for manufacturing welded parts comprising arc-welded wrought components made of 6xxx series aluminium alloy using a 5xxx series aluminium filler wire | |
| JP3219293B2 (en) | Aluminum alloy filler metal and its manufacturing method | |
| JP2000317676A (en) | Filler metal for welding of al-zn-mg-cu base alloy and heat treatment of welding material using the filler metal | |
| US3852122A (en) | Method of producing a weldable and ageable aluminium alloy of great strength and product | |
| JP2859019B2 (en) | Aluminum alloy filler metal for molding dies and method of manufacturing the same | |
| AU2017204285A1 (en) | Aluminum welding filler metal, casting and wrought metal alloy | |
| US4108688A (en) | Cast aluminum plate and method therefor | |
| JPH07150312A (en) | Manufacture of aluminum alloy forged base stock | |
| JP2746520B2 (en) | Method for producing Al-Zn-Mg based alloy | |
| JP6679269B2 (en) | Al alloy material for high energy beam welding | |
| JPH11140610A (en) | Production of aluminum alloy structural material excellent in toughness and weldability | |
| JP7534563B1 (en) | Manufacturing method of aluminum alloy material and manufacturing method of clad material | |
| JP2578453B2 (en) | Manufacturing method of aluminum alloy filler metal | |
| JP2008207249A (en) | Method for welding aluminum alloy material having excellent weld crack resistance, and method for evaluating weld crack resistance of aluminum alloy material | |
| JPH08165539A (en) | Heat treated type thin aluminum extruded shape and its production | |
| JP3378621B2 (en) | Electrode for resistance welding and method of manufacturing the same | |
| JPH01143791A (en) | Aluminum alloy filler metal | |
| JP3529664B2 (en) | Aluminum alloy filler metal | |
| JPS6111155B2 (en) | ||
| JP2017110272A (en) | Al ALLOY MATERIAL FOR HIGH ENERGY BEAM WELDMENT AND MANUFACTURING METHOD THEREFOR | |
| JP2860075B2 (en) | Aluminum alloy filler metal |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| FPAY | Renewal fee payment (prs date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20070810 Year of fee payment: 6 |
|
| FPAY | Renewal fee payment (prs date is renewal date of database) |
Year of fee payment: 7 Free format text: PAYMENT UNTIL: 20080810 |
|
| FPAY | Renewal fee payment (prs date is renewal date of database) |
Year of fee payment: 7 Free format text: PAYMENT UNTIL: 20080810 |
|
| FPAY | Renewal fee payment (prs date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20090810 Year of fee payment: 8 |
|
| FPAY | Renewal fee payment (prs date is renewal date of database) |
Year of fee payment: 8 Free format text: PAYMENT UNTIL: 20090810 |
|
| FPAY | Renewal fee payment (prs date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20100810 Year of fee payment: 9 |
|
| LAPS | Cancellation because of no payment of annual fees |