JPH0938783A - Welded structure of aluminum alloy - Google Patents
Welded structure of aluminum alloyInfo
- Publication number
- JPH0938783A JPH0938783A JP7212548A JP21254895A JPH0938783A JP H0938783 A JPH0938783 A JP H0938783A JP 7212548 A JP7212548 A JP 7212548A JP 21254895 A JP21254895 A JP 21254895A JP H0938783 A JPH0938783 A JP H0938783A
- Authority
- JP
- Japan
- Prior art keywords
- nugget
- aluminum alloy
- magnesium
- strength
- welded structure
- 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.)
- Pending
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- Resistance Welding (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明はアルミニウム合金構
造物におけるナゲット部の強度向上技術に関する。TECHNICAL FIELD The present invention relates to a technique for improving the strength of a nugget portion in an aluminum alloy structure.
【０００２】[0002]
【従来の技術】アルミニウム合金の溶融接合部（以下
「ナゲット部」と言う）の強度は母材の強度より低くな
る傾向にあり、特にスポット溶接ではナゲット部の強度
が母材の強度の６０％以下に低下することは珍しくな
い。それゆえにスポット溶接では、電流値を上げて接合
面積を増加させる、又は、スポット点の数を増加させる
等の対策を講じている。2. Description of the Related Art The strength of a fusion-bonded portion of an aluminum alloy (hereinafter referred to as "nugget portion") tends to be lower than that of a base metal, and particularly in spot welding, the strength of the nugget portion is 60% of the strength of the base metal. It is not uncommon to drop below. Therefore, in spot welding, measures such as increasing the current value to increase the joining area or increasing the number of spot points are taken.
【０００３】しかし、電流値を上げるには設備を大型
化、高性能化する必要があってイニシャルコストを増す
という不都合があり、またスポット点の数を増すことは
工数の増加となってコストアップの要因となる。However, in order to increase the current value, it is necessary to increase the size and performance of the equipment, which increases the initial cost, and increasing the number of spot points increases the man-hours and increases the cost. It becomes a factor of.
【０００４】そこで、アルミニウム合金同士の間に、亜
鉛薄膜を介在させる改良技術が特公昭５４−４１５５０
号で提案されている。即ち、アルミニウム板とアルミニ
ウム板の抵抗溶接部に予め亜鉛薄膜を介在させて抵抗溶
接時に亜鉛を瞬間的に溶融せしめて局部的な高抵抗部を
形成して電力を集中させ、ナゲット部をＡｌ−Ｚｎの固
溶化、析出を図り、接合部の強度向上を図るというもの
である。上記亜鉛薄膜をＴｉ薄層に変更したのものが特
公昭５９−２６３９２号、又亜鉛薄膜をステンレス鋼薄
板に変更したのものが特公昭５９−２６３９３号で提案
されている。Therefore, an improved technique of interposing a zinc thin film between aluminum alloys is disclosed in Japanese Examined Patent Publication No. 54-41550.
No. has been proposed. That is, by interposing a zinc thin film in advance between the aluminum plate and the resistance welding part of the aluminum plate, zinc is instantaneously melted during resistance welding to form a local high resistance part to concentrate electric power, and the nugget part is Al- It aims to improve the strength of the joint by solidifying and precipitating Zn. JP-B-59-26392 proposes a zinc thin film changed to a Ti thin layer, and JP-B-59-26393 proposes a zinc thin film changed to a stainless steel thin plate.
【０００５】[0005]
【発明が解決しようとする課題】しかし、上記亜鉛薄
板、Ｔｉ薄層、ステンレス鋼薄板はいずれも局部的に抵
抗を高める作用は発揮されるものの、ナゲット部の強度
を母材まで引き上げるに至ってない。これは、アルミニ
ウムに対して亜鉛は固溶するが格子定数差が小さいため
に固溶強化は小さい。また、アルミニウムに対してＴｉ
の固溶限が０．１５ｗｔ％、そしてＦｅ（鉄）の固溶限
が０．０５ｗｔ％と極めて小さいためにこれらによる固
溶化効果が小さいためである。そこで、亜鉛薄板、Ｔｉ
薄層、ステンレス鋼薄板に代る技術が求められている。However, although the zinc thin plate, the Ti thin layer, and the stainless steel thin plate all have the effect of locally increasing the resistance, the strength of the nugget portion has not been increased to the base material. . This is because although zinc is solid-dissolved in aluminum, the solid-solution strengthening is small because the difference in lattice constant is small. Also, for aluminum, Ti
This is because the solid solution limit of 0.15 wt% and the solid solution limit of Fe (iron) are extremely small at 0.05 wt%, so that the solid solution effect by these is small. Therefore, zinc thin plate, Ti
There is a need for an alternative technology to thin layers, stainless steel sheets.
【０００６】また、通常の抵抗溶接法によるアルミニウ
ム合金溶接構造物には次のような欠陥が認められること
がある。図３は従来の抵抗溶接法によるアルミニウム合
金溶接構造物の溶接部の顕微鏡写真（倍率＝４００）で
あり、詳細な溶接条件は比較例１として実施例の項で述
べる。写真は、アルミニウム合金製の母材間に形成され
たナゲット部を示し、このナゲット部に横筋状のクラッ
クが入り、しかも母材にもクラック入っていることをも
示す。Further, the following defects may be observed in the aluminum alloy welded structure formed by the usual resistance welding method. FIG. 3 is a micrograph (magnification = 400) of a welded portion of an aluminum alloy welded structure by a conventional resistance welding method, and detailed welding conditions will be described in Comparative Example 1 in the section of Examples. The photograph shows a nugget part formed between base materials made of aluminum alloy, and also shows that the nugget part has horizontal streak-like cracks and that the base material also has cracks.
【０００７】[0007]
【課題を解決するための手段】上記図３のクラックは有
害であるため、本発明者等はクラックの発生プロセスを
解明すべく鋭意研究を進めた。その結果、上記抵抗溶接
ではナゲット部の端部にクラックの発生起点となる窪み
（ノッチ）が形成されことを見出し、更にこの窪みはア
ルミニウム材に付き物の酸化物が原因していることを突
き止めた。即ち、アルミニウム材の表面に強固な酸化物
が形成され、この酸化物が抵抗溶接の際に溶融せずに残
って、ナゲット部の周囲に不都合な窪みを形成するとい
うものである。Since the cracks shown in FIG. 3 are harmful, the inventors of the present invention have conducted extensive studies to clarify the crack generation process. As a result, it was found that a dent (notch), which is a starting point of crack generation, was formed at the end of the nugget portion in the resistance welding, and it was further found that the dent was caused by an oxide attached to the aluminum material. . That is, a strong oxide is formed on the surface of the aluminum material, and this oxide remains without melting during resistance welding, forming an inconvenient depression around the nugget portion.
【０００８】そこで、本発明者等は前記窪みの発生を抑
える研究をし、この酸化物を除去することで強度の高い
アルミニウム合金溶接構造物を得ることに成功した。具
体的には、請求項１の溶接部は、ナゲット部と、このナ
ゲット部の周囲に形成された合金化層とからなり、この
合金化層に母材より多くのマグネシウムを含ませたこと
を特徴とする。[0008] Therefore, the inventors of the present invention conducted a study to suppress the generation of the depressions, and succeeded in obtaining an aluminum alloy welded structure having high strength by removing this oxide. Specifically, the welded portion of claim 1 comprises a nugget portion and an alloyed layer formed around the nugget portion, and the alloyed layer contains more magnesium than the base metal. Characterize.
【０００９】即ち、抵抗溶接の際にマグネシウム成分で
自己発熱反応を起こさせ、その熱で酸化膜を破壊する。
そして、ナゲット部の周囲に合金層を形成したことによ
り、従来発生していたナゲット部端部の酸化膜の発生を
抑えることができる。酸化膜がクラックの起点となりや
すいので、酸化膜の発生を抑えることで、高強度が得ら
れる。That is, during resistance welding, the magnesium component causes a self-heating reaction, and the heat destroys the oxide film.
By forming the alloy layer around the nugget portion, it is possible to suppress the generation of the oxide film at the end portion of the nugget portion, which has been conventionally generated. Since the oxide film easily becomes a starting point of cracks, high strength can be obtained by suppressing the generation of the oxide film.
【００１０】請求項２は、合金化層に、ナゲット部より
多くのマグネシウムを含ませたことを特徴とする。A second aspect of the present invention is characterized in that the alloyed layer contains more magnesium than the nugget portion.
【００１１】マグネシウムリッチの合金化層は、ナゲッ
ト部より強度が大きくなり、溶接部の強度向上に寄与す
る。The magnesium-rich alloyed layer has a strength higher than that of the nugget portion and contributes to the improvement of the strength of the welded portion.
【００１２】[0012]
【発明の実施の形態】本発明の実施の形態を添付図に基
づいて以下に説明する。なお、図面は符号の向きに見る
ものとする。図１（ａ）〜（ｄ）は本発明に係る抵抗溶
接の工程図である。（ａ）において、母材１に、アルミ
ニウム粉末、マグネシウム粉末及び金属酸化物を混合し
てなる混合粉末２を適量載せて、その上から母材３を被
せる。母材１，３はアルミニウム合金板である。（ｂ）
において、母材１，３を電極４，５にて所定の押圧力で
挟持し、所定の電流を流して、抵抗溶接を実施する。BEST MODE FOR CARRYING OUT THE INVENTION Embodiments of the present invention will be described below with reference to the accompanying drawings. The drawings should be viewed in the direction of reference numerals. 1A to 1D are process diagrams of resistance welding according to the present invention. In (a), an appropriate amount of mixed powder 2 obtained by mixing aluminum powder, magnesium powder and metal oxide is placed on the base material 1, and the base material 3 is covered thereon. The base materials 1 and 3 are aluminum alloy plates. (B)
In, the base materials 1 and 3 are sandwiched between the electrodes 4 and 5 with a predetermined pressing force, and a predetermined current is passed to perform resistance welding.
【００１３】（ｃ）は母材１，３間に生成した溶融部６
を示し、この溶融部６はジュール熱と混合粉末内におけ
るテルミット発熱反応、すなわちマグネシウムと金属酸
化物との酸化反応による自己発熱反応とにより、溶融が
促進され溶融部６は拡大される。（ｄ）は通電終了後の
状態を示し、前記溶融部は凝固してナゲット部７とな
り、このナゲット部７の上部及び下部は電極４，５を通
じて冷却が進むが、ナゲット部７の端部７ａ，７ａは冷
却の度合が小さく、母材１，３の接合面に沿って混合粉
末の酸化反応が進行し、接合面にＭｇ−Ａｌ合金を主成
分とした合金化層８，８が形成される。上記テルミット
反応が期待できない従来技術では前記端部７ａ，７ａの
凝固がかなり遅れて、酸化膜による窪みが残ることにな
るが、本発明ではその心配はない。(C) is a fusion zone 6 formed between the base materials 1 and 3.
The melting portion 6 is expanded by the Joule heat and thermite exothermic reaction in the mixed powder, that is, a self-exothermic reaction due to an oxidation reaction of magnesium and a metal oxide. (D) shows the state after the end of energization, the molten portion is solidified to become the nugget portion 7, and the upper and lower portions of the nugget portion 7 are cooled through the electrodes 4 and 5, but the end portion 7a of the nugget portion 7 is , 7a has a low degree of cooling, the oxidation reaction of the mixed powder progresses along the joint surfaces of the base materials 1 and 3, and alloying layers 8 and 8 containing Mg-Al alloy as a main component are formed on the joint surfaces. It In the prior art in which the thermite reaction cannot be expected, the solidification of the end portions 7a, 7a is considerably delayed, and a dent due to an oxide film remains, but in the present invention, there is no concern.
【００１４】[0014]
【実施例】本発明に係る実施例を次に説明する。以下、
本発明の実施例を示すが、本発明はこれに限定されるも
のではない。 実施例１〜３及び比較例１，２： 被溶接材（母材）； 材質；Ａｌ−Ｍｇ系アルミニウム合金（Ａ５１８２材）
圧延材 形状；００ｍｍ×３０ｍｍ×１．２ｍｍ 溶接条件； 電源；インバータ式 電流；１２又は１８ｋＡ 加圧力；４００ｋｇｆ 電極； 材質；無酸素銅 直径；１６ｍｍ 先端の曲率半径；６０，８０又は００ｍｍ インサート材； 塗布量；０．２５ｇ／ｃｍ2 塗布面積；９００ｍｍ2 組成；マグネシウム粉末（３００μｍ以下）とアルミニ
ウム粉末（１５０μｍ以下）との混合物又は、金属酸化
物粉末とマグネシウム粉末とアルミニウム粉末との混合
物。Embodiments of the present invention will be described below. Less than,
Examples of the present invention will be shown, but the present invention is not limited thereto. Examples 1 to 3 and Comparative Examples 1 and 2: Material to be welded (base material); Material; Al-Mg based aluminum alloy (A5182 material)
Rolled material shape; 00 mm x 30 mm x 1.2 mm Welding conditions; Power source; Inverter type current; 12 or 18 kA Pressurizing force; 400 kgf electrode; Material; Oxygen-free copper diameter; 16 mm Tip curvature radius; 60, 80 or 00 mm Insert material; Application amount: 0.25 g / cm 2 Application area: 900 mm 2 Composition: A mixture of magnesium powder (300 μm or less) and aluminum powder (150 μm or less) or a mixture of metal oxide powder, magnesium powder and aluminum powder.
【００１５】インサート材としての混合粉末の組成を次
の表１に示す通りに実施例１〜３，比較例２，３でそれ
ぞれ変更し、比較例１はインサート材を介在させないこ
とを条件にスポット溶接し、生成したナゲット部のマグ
ネシウムの含有量、合金化層が生成されたか否か、及び
引張剪断強度を調べた。なお、引張剪断荷重は引張荷重
によって接着面に剪断応力を加え、接着接合面が破断し
た時の荷重をいう。The composition of the mixed powder as the insert material was changed in each of Examples 1 to 3 and Comparative Examples 2 and 3 as shown in Table 1 below, and Comparative Example 1 was spotted under the condition that no insert material was interposed. The content of magnesium in the nugget portion produced by welding, whether an alloyed layer was produced, and the tensile shear strength were examined. The tensile shear load means a load when the adhesive bonding surface is broken by applying shear stress to the adhesive surface by the tensile load.
【００１６】[0016]
【表１】 [Table 1]
【００１７】比較例１は、溶接電流を１８ｋＡとし、イ
ンサート材なしの従来の抵抗溶接法によったものであ
る。比較例１の溶接部の顕微鏡写真は、前記図３に示す
通りであり、ナゲット部の周囲にクラックが発生してい
るので、強度は低下する。具体的には、ナゲット部のＭ
ｇ含有量は５．０ｗｔ％であり、合金化層は形成され
ず、その結果、引張剪断強度は６．８ｋｇ／ｍｍ2であ
り、引張剪断強度が１０．０ｋｇ／ｍｍ2以上で評価を
「○」、１０．０ｋｇ／ｍｍ2未満で「×」とすれば、
比較例１の評価は「×」である。なお、インサート材な
しなのでナゲット部の含有Ｍｇは、母材中のＭｇ成分が
源となる。In Comparative Example 1, the welding current was 18 kA and the conventional resistance welding method without insert material was used. The micrograph of the welded portion of Comparative Example 1 is as shown in FIG. 3 above. Since cracks are generated around the nugget portion, the strength is reduced. Specifically, M of the nugget part
The g content was 5.0 wt% and no alloyed layer was formed. As a result, the tensile shear strength was 6.8 kg / mm 2 , and the evaluation was made when the tensile shear strength was 10.0 kg / mm 2 or more. ◯ ”, if less than 10.0 kg / mm 2 and“ x ”,
The evaluation of Comparative Example 1 is “x”. Since there is no insert material, the Mg content in the nugget portion comes from the Mg component in the base material.
【００１８】比較例２は、６０ｗｔ％Ｍｇ−Ａｌを成分
としたインサート材を介在させて、図１の要領で抵抗溶
接したもので、ナゲット部のＭｇ含有量は８．９ｗｔ％
と増加したが、合金化層は形成されず、その結果、引張
剪断強度は９．１ｋｇ／ｍｍ2であり、評価は「×」で
ある。即ち、インサート材に金属酸化物が含まれていな
いので、期待したテルミット反応が得られず、合金化層
が得られなかったので、ナゲット部の周囲に微細な窪み
（ノッチ）が発生し、強度が低くなったと考える。In Comparative Example 2, resistance welding was carried out as in FIG. 1 with an insert material containing 60 wt% Mg-Al as a component, and the Mg content in the nugget portion was 8.9 wt%.
However, the alloyed layer was not formed, and as a result, the tensile shear strength was 9.1 kg / mm 2 , and the evaluation was “x”. That is, since the insert material does not contain a metal oxide, the expected thermite reaction was not obtained, and the alloyed layer was not obtained, so a minute recess (notch) occurred around the nugget portion, and the strength was increased. I think that has become low.
【００１９】実施例１は、金属酸化物を含むところの１
０ｗｔ％ＭｎＯ2−６５ｗｔ％Ｍｇ−Ａｌのインサート
材を介在させて、比較例１より低い１２ｋＡで抵抗溶接
を実施した。すると、ナゲット部のＭｇ含有量は７．６
ｗｔ％で、合金化層は形成され、その結果、引張剪断強
度は１１．７ｋｇ／ｍｍ2と高まり、評価は「○」であ
る。Example 1 is one containing a metal oxide.
Resistance welding was performed at 12 kA, which is lower than in Comparative Example 1, with an insert material of 0 wt% MnO 2 -65 wt% Mg-Al interposed. Then, the Mg content of the nugget portion is 7.6.
At wt%, the alloyed layer was formed, and as a result, the tensile shear strength was increased to 11.7 kg / mm 2, and the evaluation was “◯”.
【００２０】図２は本発明の実施例１のアルミニウム合
金溶接構造物の溶接部の顕微鏡写真（倍率＝４００）で
あり、ナゲット部の周囲（図では左端）で且つ上下母材
の接合面に合金化層（図１（ｄ）の符号８に相当）が認
められる。ナゲット部のＭｇ含有量は比較例２に比べて
減少したにもかかわらず、金属酸化物（ＭｎＯ2）とＭ
ｇとのテルミット反応により、酸化膜が破壊され、合金
化層が形成されたので強度が上がったと考えられる。テ
ルミット反応が期待できるので、溶接電流を１２ｋＡに
下げたにもかかわらず良好な溶接部が得られた。従っ
て、本発明によれば溶接電流を下げることができる。FIG. 2 is a photomicrograph (magnification = 400) of the welded portion of the aluminum alloy welded structure of Example 1 of the present invention, which is around the nugget portion (left end in the figure) and on the joint surfaces of the upper and lower base materials. An alloyed layer (corresponding to reference numeral 8 in FIG. 1 (d)) is recognized. Although the Mg content of the nugget part was reduced as compared with Comparative Example 2, the metal oxide (MnO 2 ) and M
It is believed that the thermite reaction with g destroyed the oxide film and formed an alloyed layer, resulting in increased strength. Since a thermite reaction can be expected, a good weld was obtained even though the welding current was reduced to 12 kA. Therefore, according to the present invention, the welding current can be reduced.
【００２１】比較例３は、電極の先端の曲率半径を８０
ｍｍから６０ｍｍに変更し、他の条件は前記実施例１と
同じにしたものである。ナゲット部のＭｇ含有量は７．
３ｗｔ％であったが、合金化層は形成されず、その結
果、引張剪断強度は９．４ｋｇ／ｍｍ2と減少し、評価
は「×」である。電極の先端の曲率半径が小さくなった
ために、ナゲット部の周囲における母材同士の圧着が弱
まり、この部分では十分なジュール熱の発生がなかった
ためと考えられる。In Comparative Example 3, the radius of curvature of the tip of the electrode is set to 80.
mm was changed to 60 mm, and the other conditions were the same as in Example 1 above. The Mg content of the nugget part is 7.
Although it was 3 wt%, an alloyed layer was not formed, and as a result, the tensile shear strength was reduced to 9.4 kg / mm 2, and the evaluation was “x”. It is considered that because the radius of curvature of the tip of the electrode was reduced, the pressure bonding between the base materials around the nugget portion was weakened, and sufficient Joule heat was not generated in this portion.
【００２２】実施例２は、逆に電極の先端の曲率半径を
００ｍｍに増加し、他の条件は前記実施例１と同じにし
たものである。ナゲット部のＭｇ含有量は７．３ｗｔ％
であったが、合金化層は形成され、その結果、引張剪断
強度は１１．５ｋｇ／ｍｍ2で、評価は「○」である。
比較例３，実施例１及び実施例２から、電極の先端の曲
率半径は８０ｍｍ以上であることが望ましい。In the second embodiment, on the contrary, the radius of curvature of the tip of the electrode is increased to 00 mm, and the other conditions are the same as those in the first embodiment. Mg content of the nugget part is 7.3 wt%
However, the alloyed layer was formed, and as a result, the tensile shear strength was 11.5 kg / mm 2 , and the evaluation was “◯”.
From Comparative Example 3, Example 1 and Example 2, it is desirable that the radius of curvature of the tip of the electrode be 80 mm or more.
【００２３】実施例３は、インサート材を２０ｗｔ％Ｃ
ｒ2Ｏ3−５５ｗｔ％Ｍｇ−Ａｌとし、他の条件は前記実
施例１と同じにしたものである。ナゲット部のＭｇ含有
量は６．９ｗｔ％であったが、合金化層は形成され、そ
の結果、引張剪断強度は１１．１ｋｇ／ｍｍ2で、評価
は「○」である。従って、金属酸化物を含むインサート
材、テルミット反応、合金化層形成の要素から溶接部の
強度を高め得ることが確認できた。In Example 3, the insert material is 20 wt% C
r 2 O 3 -55 wt% Mg-Al, and the other conditions are the same as those in the first embodiment. Although the Mg content in the nugget portion was 6.9 wt%, the alloyed layer was formed, and as a result, the tensile shear strength was 11.1 kg / mm 2 , and the evaluation was “◯”. Therefore, it has been confirmed that the strength of the welded portion can be increased from the factors of the insert material containing the metal oxide, the thermite reaction, and the alloying layer formation.
【００２４】尚、前記金属酸化物は、ＭｎＯ2、Ｃｒ2Ｏ
3の他、ＴｉＯ2、ＳｉＯ2、Ｆｅ2Ｏ3、ＣｕＯ、Ｔｉ2Ｏ
3が適当である。The metal oxides are MnO 2 and Cr 2 O.
3 , TiO 2 , SiO 2 , Fe 2 O 3 , CuO, Ti 2 O
3 is appropriate.
【００２５】[0025]
【発明の効果】本発明は上記構成により次の効果を発揮
する。請求項１の溶接構造物は、その溶接部が、ナゲッ
ト部と、このナゲット部の周囲に形成された合金化層と
からなり、この合金化層に母材より多くのマグネシウム
を含ませたことを特徴とする。抵抗溶接の際にマグネシ
ウム成分で自己発熱反応を起こさせ、その熱で酸化膜を
破壊する。そして、ナゲット部の周囲に合金層を形成し
たことにより、従来発生していたナゲット部端部の酸化
膜の発生を抑えることができる。酸化膜がクラックの起
点となりやすいので、酸化膜の発生を抑えることで、高
強度が得られる。テルミット反応が期待できるので、溶
接電流を大幅に下げることができ、ランニングコストを
削減できる。The present invention has the following effects due to the above configuration. The welded structure according to claim 1, wherein the welded portion includes a nugget portion and an alloyed layer formed around the nugget portion, and the alloyed layer contains more magnesium than the base material. Is characterized by. During resistance welding, the magnesium component causes a self-heating reaction, and the heat destroys the oxide film. By forming the alloy layer around the nugget portion, it is possible to suppress the generation of the oxide film at the end portion of the nugget portion, which has been conventionally generated. Since the oxide film easily becomes a starting point of cracks, high strength can be obtained by suppressing the generation of the oxide film. Since the thermite reaction can be expected, the welding current can be significantly reduced and the running cost can be reduced.
【００２６】請求項２の溶接構造物は、合金化層に、ナ
ゲット部より多くのマグネシウムを含ませたことを特徴
とする。マグネシウムリッチの合金化層は、ナゲット部
より強度が大きくなり、溶接部の強度向上に寄与する。A welded structure according to a second aspect is characterized in that the alloyed layer contains more magnesium than the nugget portion. The magnesium-rich alloyed layer has a higher strength than the nugget portion and contributes to improving the strength of the welded portion.
【図１】本発明に係る抵抗溶接の工程図FIG. 1 is a process diagram of resistance welding according to the present invention.
【図２】本発明の実施例１のアルミニウム合金溶接構造
物の溶接部の顕微鏡写真（倍率＝４００）FIG. 2 is a micrograph (magnification = 400) of a welded portion of the aluminum alloy welded structure of Example 1 of the present invention.
【図３】従来の抵抗溶接法によるアルミニウム合金溶接
構造物の溶接部の顕微鏡写真（倍率＝４００）FIG. 3 is a micrograph (magnification = 400) of a welded portion of an aluminum alloy welded structure by a conventional resistance welding method.
１，３…母材、２…混合粉末（インサート材）、４，５
…電極、６…溶融部、７…ナゲット部、７ａ…ナゲット
の端部、８…合金化層。1, 3 ... Base material, 2 ... Mixed powder (insert material), 4, 5
... electrode, 6 ... fusion part, 7 ... nugget part, 7a ... end of nugget, 8 ... alloying layer.
Claims (2)
材同士を抵抗溶接による溶接部を介して接合したアルミ
ニウム合金溶接構造物において、前記溶接部は、ナゲッ
ト部と、このナゲット部の周囲に形成された合金化層と
からなり、この合金化層に前記母材より多くのマグネシ
ウムを含ませたことを特徴とするアルミニウム合金溶接
構造物。1. An aluminum alloy welded structure in which an aluminum alloy is used as a base material and the base materials are joined together via a welded portion by resistance welding, the welded portion being formed around a nugget portion and the periphery of the nugget portion. And an alloyed layer formed from the base material, the alloyed layer containing more magnesium than the base metal.
くのマグネシウムを含ませたことを特徴とする請求項１
記載のアルミニウム合金溶接構造物。2. The alloyed layer contains more magnesium than the nugget portion.
The aluminum alloy welded structure described.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP7212548A JPH0938783A (en) | 1995-07-28 | 1995-07-28 | Welded structure of aluminum alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP7212548A JPH0938783A (en) | 1995-07-28 | 1995-07-28 | Welded structure of aluminum alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0938783A true JPH0938783A (en) | 1997-02-10 |
Family
ID=16624515
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP7212548A Pending JPH0938783A (en) | 1995-07-28 | 1995-07-28 | Welded structure of aluminum alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0938783A (en) |
-
1995
- 1995-07-28 JP JP7212548A patent/JPH0938783A/en active Pending
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