JPH0825080A - Solid wire for welding and welding method - Google Patents
Solid wire for welding and welding methodInfo
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- JPH0825080A JPH0825080A JP15726994A JP15726994A JPH0825080A JP H0825080 A JPH0825080 A JP H0825080A JP 15726994 A JP15726994 A JP 15726994A JP 15726994 A JP15726994 A JP 15726994A JP H0825080 A JPH0825080 A JP H0825080A
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は薄板高張力鋼板の溶接に
好適の溶接用ソリッドワイヤ及び溶接方法に関し、特に
継手疲労特性が優れた隅肉溶接部が得られる溶接用ソリ
ッドワイヤ及び溶接方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a welding solid wire and welding method suitable for welding thin high-strength steel sheets, and more particularly to a welding solid wire and welding method capable of obtaining a fillet weld having excellent joint fatigue characteristics. .
【０００２】[0002]
【従来の技術】従来、薄板高張力鋼板を隅肉溶接する場
合には、ソリッドワイヤが多く使用されている。しか
し、溶接に使用するワイヤ組成及び溶接条件が溶接継手
の疲労強度に与える影響については未だ研究がなされて
いない。2. Description of the Related Art Conventionally, solid wires are often used for fillet welding thin thin high strength steel sheets. However, no study has been made on the effect of the wire composition and welding conditions used for welding on the fatigue strength of welded joints.
【０００３】[0003]
【発明が解決しようとする課題】上述したように、従来
の高張力鋼板の溶接においては、溶接ワイヤの組成及び
溶接条件が溶接継手の疲労強度に与える影響については
考慮されていないため、溶接継手の疲労強度が十分でな
い場合があるという問題点がある。この場合、高張力鋼
板本来の疲労強度を発揮することができない。As described above, in the welding of the conventional high-strength steel sheet, the influence of the composition of the welding wire and the welding conditions on the fatigue strength of the welded joint is not taken into consideration. However, there is a problem in that the fatigue strength may not be sufficient. In this case, the original fatigue strength of the high-tensile steel plate cannot be exhibited.
【０００４】本発明はかかる問題点に鑑みてなされたも
のであって、疲労強度が優れた溶接継手を得ることがで
き、高張力鋼板本来の疲労強度を十分に生かすことがで
きる溶接用ソリッドワイヤ及び溶接方法を提供すること
を目的とする。The present invention has been made in view of the above problems, and it is possible to obtain a welded joint having excellent fatigue strength and to sufficiently utilize the original fatigue strength of a high-strength steel sheet. And a welding method.
【０００５】[0005]
【課題を解決するための手段】本発明に係る溶接用ソリ
ッドワイヤは、Ｃ；０．０１乃至０．４０重量％、Ｓ
ｉ；０．０５乃至２．００重量％及びＭｎ；０．２０乃
至３．００重量％を含有すると共に、Ｎｉ；０．５乃至
５．０重量％、Ｃｒ；０．００５乃至３．００重量％、
Ｍｏ；０．１０乃至２．００重量％、Ｖ；０．０１乃至
１．００重量％、Ｎｂ；０．０１乃至１．００重量％、
Ｔｉ；０．０１乃至１．００重量％、Ａｌ；０．０１乃
至１．００重量％、Ｚｒ；０．０１乃至１．００重量
％、Ｃｕ；０．０５乃至１．５０重量％、Ｂ；０．００
０５乃至０．０５００重量％、Ｃａ；０．００１乃至
０．０５０重量％及び希土類元素；０．００１乃至０．
０５０重量％からなる群から選択された少なくとも１種
の元素を含有し、Ｐ含有量を０．０５重量％以下、Ｓ含
有量を０．０５重量％以下に規制し、残部が鉄及び不可
避的不純物からなり、且つ、下記数式１で示す炭素当量
Ｗeqが０．１５乃至０．７０であることを特徴とする。The solid wire for welding according to the present invention comprises C: 0.01 to 0.40% by weight and S
i: 0.05 to 2.00% by weight and Mn: 0.20 to 3.00% by weight, Ni: 0.5 to 5.0% by weight, Cr: 0.005 to 3.00% by weight %,
Mo; 0.10 to 2.00% by weight, V; 0.01 to 1.00% by weight, Nb; 0.01 to 1.00% by weight,
Ti; 0.01 to 1.00% by weight, Al; 0.01 to 1.00% by weight, Zr; 0.01 to 1.00% by weight, Cu; 0.05 to 1.50% by weight, B; 0.00
05 to 0.0500% by weight, Ca; 0.001 to 0.050% by weight and rare earth element; 0.001 to 0.
It contains at least one element selected from the group consisting of 050% by weight, regulates the P content to 0.05% by weight or less and the S content to 0.05% by weight or less, and balances iron and unavoidable. It is characterized by being made of impurities and having a carbon equivalent Weq represented by the following formula 1 of 0.15 to 0.70.
【０００６】[0006]
【数１】Ｗeq＝［Ｃ］＋［Ｓｉ］／２４＋［Ｍｎ］／６
＋［Ｎｉ］／６０＋［Ｃｒ］／５＋［Ｍｏ］／４＋
［Ｖ］／１４＋［Ｎｂ］＋［Ｔｉ］／１４ 但し、［Ｍ］はワイヤ中の成分Ｍの含有量（重量％） 本発明に係る溶接方法は、上記溶接用ソリッドワイヤを
使用し、溶接電圧Ｖａを下記数式２で示す範囲内に設定
し、溶接電流が５０乃至５００Ａ、溶接速度が５乃至２
５０ｃｍ／分の条件で、１パスで溶接することを特徴と
する。## EQU1 ## Weq = [C] + [Si] / 24 + [Mn] / 6
+ [Ni] / 60 + [Cr] / 5 + [Mo] / 4 +
[V] / 14 + [Nb] + [Ti] / 14 where [M] is the content (% by weight) of the component M in the wire. The welding method according to the present invention uses the above solid wire for welding, The voltage Va is set within the range shown by the following mathematical formula 2, the welding current is 50 to 500 A, and the welding speed is 5 to 2
It is characterized by welding in one pass under the condition of 50 cm / min.
【０００７】[0007]
【数２】ＶL≦Ｖａ≦ＶH 但し、ＶL及びＶHは夫々下記数式３及び４にて表され
る。## EQU2 ## VL≤Va≤VH However, VL and VH are expressed by the following equations 3 and 4, respectively.
【０００８】[0008]
【数３】ＶL＝7.96×10-8×Ａ3−1.12×10-4×Ａ2＋0.1
1×Ａ＋9.43＋Ｐ1＋Ｐ2−Ｗeq×5−4[Formula 3] VL = 7.96 × 10 -8 × A 3 −1.12 × 10 -4 × A 2 +0.1
1 x A + 9.43 + P1 + P2-Weq x 5-4
【０００９】[0009]
【数４】ＶH＝7.96×10-8×Ａ3−1.12×10-4×Ａ2＋0.1
1×Ａ＋9.43＋Ｐ1＋Ｐ2 また、Ａ、Ｐ1及びＰ2は下記表１に示す値をとる。[Equation 4] VH = 7.96 × 10 -8 × A 3 −1.12 × 10 -4 × A 2 +0.1
1 × A + 9.43 + P1 + P2 Further, A, P1 and P2 take the values shown in Table 1 below.
【００１０】[0010]
【表１】 [Table 1]
【００１１】[0011]
【作用】本願発明者等は、溶接ビード形状と疲労強度と
の関係について調査し、母材に対するビード止端部形状
が継手の疲労強度と密接な関係があることを見い出し
た。その結果、ビード止端部の曲率半径ρが大きいほど
疲労強度が高く、疲労特性が優れた継手になるという知
見を得た。The present inventors investigated the relationship between the weld bead shape and the fatigue strength, and found that the bead toe shape with respect to the base material had a close relationship with the fatigue strength of the joint. As a result, it was found that the larger the radius of curvature ρ of the bead toe, the higher the fatigue strength and the better the fatigue properties of the joint.
【００１２】図１（ａ）に示すように、溶接母材１上に
母材２を重ね、母材１、２を水平隅肉溶接してビード３
を形成した場合、そのビード止端部４は、図１（ｂ）に
拡大して示すように、下に凸の形状で曲率半径ρで湾曲
している。このビード止端部４の曲率半径ρが大きいほ
ど、ビード３の裾野は滑らかに母材１と接触する。As shown in FIG. 1A, a base material 2 is superposed on a weld base material 1 and the base materials 1 and 2 are welded by horizontal fillet welding to a bead 3.
When the bead is formed, the bead toe portion 4 has a downwardly convex shape and is curved with a radius of curvature ρ, as shown in an enlarged view in FIG. The larger the radius of curvature ρ of the bead toe 4, the smoother the skirt of the bead 3 contacts the base material 1.
【００１３】図２は横軸に止端部曲率半径ρをとり、縦
軸に時間強さ（母材１、２で構成される継手に１０6回
の曲げを加えても破壊しない場合の母材１、２間の応力
の上限値）をとって、疲労試験結果を示すグラフ図であ
る。この疲労試験方法は、平面曲げ疲労試験機を使用
し、応力負荷として両振りの正弦波応力を印加して行っ
たものである。鋼板（母材）は薄板高張力鋼板（５０ｋ
ｇｆ級高張力鋼ＨＴ５０及び８０ｋｇｆ級高張力鋼ＨＴ
８０）である。この図２から明らかなように、止端部曲
率半径ρが大きくなるほど、時間強さσが大きくなり、
疲労強度が高くなることがわかる。In FIG. 2, the abscissa represents the radius of curvature ρ of the toe, and the ordinate represents the time strength (in the case where the joint composed of the base materials 1 and 2 is not broken even if it is bent 10 6 times). It is a graph which shows the fatigue test result by taking the upper limit of the stress between the materials 1 and 2. This fatigue test method is carried out by using a plane bending fatigue tester and applying both sine wave stress as a stress load. The steel plate (base material) is a thin high-strength steel plate (50k
gf class high strength steel HT50 and 80 kgf class high strength steel HT
80). As is clear from FIG. 2, as the radius of curvature ρ of the toe portion increases, the time strength σ increases,
It can be seen that the fatigue strength increases.
【００１４】本発明はこのような知見に基づき、薄板高
張力鋼の溶接において、ビード止端部の曲率半径ρが大
きくなるような溶接ソリッドワイヤを開発することによ
り、疲労強度が極めて高く、良好な継手を得ようとした
ものである。Based on the above findings, the present invention has developed a welded solid wire having a large bead toe radius of curvature ρ in the welding of thin plate high-strength steel, whereby fatigue strength is extremely high and good. I tried to obtain a large joint.
【００１５】本願発明者等は、前記課題を解決するため
に鋭意研究を重ねた結果、ワイヤ組成から導き出される
炭素当量Ｗeqと、適正な止端部曲率半径が得られる適正
溶接電圧Ｖａの範囲との間に相関があることを見い出
し、本発明を完成したものである。また、本発明におい
ては、適正溶接電圧範囲の他の溶接施工条件、前進後退
角及びトーチ角度についてもより好ましいビード止端部
曲率半径が得られる範囲を規定した。図３は母材１、２
を重ね、その端部を水平隅肉溶接する場合に、溶接トー
チ５を図中矢印にて示す方向に移動させて溶接する状態
を示す。この図３において、溶接トーチの水平方向に対
する傾斜角度をθ2とし、溶接線に垂直の方向に対して
傾斜する角度を前進角θ1とする。The inventors of the present invention have conducted extensive studies in order to solve the above problems, and as a result, have found a carbon equivalent Weq derived from the wire composition and a range of an appropriate welding voltage Va at which an appropriate curvature radius at the toe portion can be obtained. The present invention has been completed by finding that there is a correlation between the two. Further, in the present invention, the range in which a more favorable bead toe radius of curvature is obtained is defined for other welding execution conditions within the proper welding voltage range, advancing and receding angles, and torch angles. Figure 3 shows base materials 1 and 2
FIG. 3 shows a state in which the welding torch 5 is moved in the direction shown by the arrow in the drawing and welded when the edges are overlapped and horizontal fillet welding is performed. In FIG. 3, the inclination angle of the welding torch with respect to the horizontal direction is θ2, and the angle of inclination with respect to the direction perpendicular to the welding line is the advance angle θ1.
【００１６】次に、本発明にて規定したソリッドワイヤ
の組成の成分添加理由及び組成限定理由について説明す
る。Next, the reason for adding the components of the composition of the solid wire defined in the present invention and the reason for limiting the composition will be explained.
【００１７】Ｃ（炭素） Ｃは、鋼の強度を向上させる。しかし、ワイヤ成分の溶
接金属中への歩留まりを考慮すると、０．０１重量％未
満では溶接金属の所望の強度を確保することができな
い。一方、Ｃ含有量が０．４０重量％を超えると、溶接
性の劣化を招来すると共に、高炭素マルテンサイトを生
成し、靱性が劣化する。従って、Ｃ含有量は０．０１乃
至０．４０重量％とする。 C (Carbon) C improves the strength of steel. However, considering the yield of the wire component in the weld metal, if the content is less than 0.01% by weight, the desired strength of the weld metal cannot be secured. On the other hand, when the C content exceeds 0.40% by weight, the weldability is deteriorated, high carbon martensite is generated, and the toughness is deteriorated. Therefore, the C content is 0.01 to 0.40% by weight.
【００１８】Ｓｉ（シリコン） Ｓｉは、鋼の強度上昇に有効であると共に、強力な脱酸
効果を有する元素である。ワイヤ中にＳｉを含有するこ
とにより、気泡の発生及び溶接金属の酸化を防止するこ
とができる。しかし、Ｓｉ含有量が０．０５重量％未満
の場合は、上述の効果を得ることができない。一方、Ｓ
ｉ含有量が２．００重量％を超えると、溶接金属の靱性
が著しく劣化する。従って、Ｓｉ含有量は０．０５乃至
２．００重量％とする。 Si (Si) Si is an element that is effective in increasing the strength of steel and has a strong deoxidizing effect. By containing Si in the wire, generation of bubbles and oxidation of the weld metal can be prevented. However, if the Si content is less than 0.05% by weight, the above effect cannot be obtained. On the other hand, S
If the i content exceeds 2.00% by weight, the toughness of the weld metal deteriorates significantly. Therefore, the Si content is set to 0.05 to 2.00% by weight.
【００１９】Ｍｎ（マンガン） Ｍｎは、固溶強化、変態強化及び結晶粒微細化強化等の
作用により、鋼の強度と靱性の双方を向上させる効果が
ある。しかし、Ｍｎ含有量が０．２０重量％未満の場合
は上述の効果を得ることができない。一方、Ｍｎ含有量
が３．００重量％を超えると、一次晶粒界が発達して粒
界破壊が生じるようになり、耐割れ性及び靱性が著しく
劣化する。このため、Ｍｎ含有量は０．２０乃至３．０
０重量％とする。 Mn (Manganese) Mn has an effect of improving both strength and toughness of steel by actions such as solid solution strengthening, transformation strengthening and grain refinement strengthening. However, if the Mn content is less than 0.20% by weight, the above effect cannot be obtained. On the other hand, when the Mn content exceeds 3.00% by weight, primary crystal grain boundaries develop to cause grain boundary fracture, resulting in significant deterioration in crack resistance and toughness. Therefore, the Mn content is 0.20 to 3.0
0% by weight.
【００２０】Ｐ（リン） Ｐ含有量が０．０５０重量％を超える場合は、フェライ
ト中に固溶したＰにより、マトリックスの靱性が損なわ
れるだけでなく、溶接割れの原因にもなる。このため、
Ｐ含有量は０．０５０重量％以下に規制する必要があ
る。If the P (phosphorus) P content exceeds 0.050% by weight, the solid solution of P in ferrite not only impairs the toughness of the matrix but also causes weld cracking. For this reason,
It is necessary to regulate the P content to be 0.050% by weight or less.
【００２１】Ｓ（硫黄） Ｓ含有量が０．０５０重量％を超えると、Ｐの場合と同
様に、溶接金属部の延性の低下及び溶接金属部の耐割れ
性の劣化を招来する。このため、Ｓ含有量は０．０５０
重量％以下とすることが必要である。 S (Sulfur) When the S content exceeds 0.050% by weight, the ductility of the weld metal part and the crack resistance of the weld metal part are deteriorated as in the case of P. Therefore, the S content is 0.050
It is necessary to make it less than or equal to the weight%.
【００２２】更に、上記必須元素に加えて、下記元素を
選択して１種類以上添加することにより、溶接金属の機
械的性質の改善、特に強度及び延性の向上、靱性の強化
を図ることができる。Furthermore, in addition to the above essential elements, the following elements can be selected and added in one or more kinds to improve the mechanical properties of the weld metal, in particular, improve the strength and ductility, and strengthen the toughness. .
【００２３】Ａｌ（アルミニウム） Ａｌは、鋼の脱酸効果を有する元素である。しかし、Ａ
ｌ含有量が０．０１重量％未満の場合は、脱酸効果が十
分でない。一方、Ａｌ含有量が１．００重量％を超える
と、脱酸生成物であるＡｌ2Ｏ3が溶接金属中に多く残存
するようになるため、脱酸効果が消失すると共に、靱性
が大幅に劣化する。このため、Ａｌを含有する場合は、
その含有量を０．０１乃至１．００重量％とする。ま
た、不可避的不純物量は０．０１重量％未満とする。 Al (Aluminum) Al is an element having a deoxidizing effect on steel. However, A
If the 1 content is less than 0.01% by weight, the deoxidizing effect is not sufficient. On the other hand, when the Al content exceeds 1.00% by weight, a large amount of Al 2 O 3, which is a deoxidation product, remains in the weld metal, so that the deoxidization effect disappears and the toughness significantly increases. to degrade. Therefore, when containing Al,
Its content is 0.01 to 1.00% by weight. The amount of unavoidable impurities is less than 0.01% by weight.
【００２４】Ｎｉ（ニッケル） Ｎｉは、溶接金属の靱性改善及び強度向上に有効な元素
である。しかし、Ｎｉ含有量が０．５重量％未満の場合
は、上述の効果を得ることができない。また、Ｎｉ含有
量が５．０重量％を超えると、一次晶粒界が発達し、逆
に脆化してしまう。このため、Ｎｉを含有する場合は、
その含有量を０．５乃至５．０重量％とする。また、不
可避的不純物量は０．５重量％未満とする。 Ni (Nickel) Ni is an element effective for improving the toughness and strength of the weld metal. However, if the Ni content is less than 0.5% by weight, the above effect cannot be obtained. On the other hand, if the Ni content exceeds 5.0% by weight, primary grain boundaries develop and, conversely, embrittlement occurs. Therefore, when Ni is contained,
Its content is 0.5 to 5.0% by weight. The amount of unavoidable impurities is less than 0.5% by weight.
【００２５】Ｃｒ（クロム） Ｃｒは、溶接金属部を強靱化すると共に、酸化物皮膜に
よる耐蝕性向上及び高温強度向上等の効果がある。しか
し、Ｃｒ含有量が０．００５重量％未満の場合は、上述
の効果を得ることができない。また、Ｃｒ含有量が３．
００重量％を超えると、自硬性が高くなり、耐割れ性が
低下する。このため、Ｃｒを含有する場合は、その含有
量を０．００５乃至３．００重量％とする。また、不可
避的不純物量は０．００５重量％未満とする。 Cr (Chromium) Cr has the effects of strengthening the weld metal portion and improving the corrosion resistance and the high temperature strength by the oxide film. However, if the Cr content is less than 0.005% by weight, the above effect cannot be obtained. Further, the Cr content is 3.
If it exceeds 00% by weight, the self-hardening property is increased and the crack resistance is deteriorated. Therefore, when Cr is contained, its content is set to 0.005 to 3.00% by weight. The amount of unavoidable impurities is less than 0.005% by weight.
【００２６】Ｍｏ（モリブデン） Ｍｏは、溶接金属の焼入れ性を高めるという効果があ
り、その強度向上に寄与する。しかし、Ｍｏ含有量が
０．１０重量％未満の場合は、上述の効果を得ることが
できない。一方、Ｍｏ含有量が２．００重量％を超える
と、炭化物が生成され、靱性が著しく低下する。このた
め、Ｍｏを含有する場合は、その含有量を０．１０乃至
２．００重量％とする。また、不可避的不純物量は０．
１０重量％未満とする。 Mo (Molybdenum) Mo has the effect of enhancing the hardenability of the weld metal and contributes to the improvement of its strength. However, if the Mo content is less than 0.10% by weight, the above effect cannot be obtained. On the other hand, when the Mo content exceeds 2.00% by weight, carbides are formed and the toughness is significantly reduced. Therefore, when Mo is contained, its content is set to 0.10 to 2.00% by weight. In addition, the amount of unavoidable impurities is 0.
It is less than 10% by weight.
【００２７】Ｔｉ，Ｚｒ（チタン、ジルコニウム） Ｔｉ及びＺｒはいずれも強脱酸剤であり、溶着金属の酸
化を防止する。また、Ｔｉ及びＺｒは酸化物を生成する
ので、析出効果による強度上昇と、組織の微細化による
靱性の改善に効果がある。しかし、Ｔｉ含有量が０．０
１重量％未満の場合は、上述の効果を得ることができ
ず、Ｔｉ含有量が１．００重量％を超えると、溶接性が
劣化すると共に、炭化物の形成及び析出により靱性が大
幅に低下する。また、これと同様に、Ｚｒ含有量が０．
０１重量％未満の場合も、上述の効果を得ることができ
ず、Ｚｒ含有量が１．００重量％を超えると、溶接性が
劣化すると共に、炭化物の形成及び析出により靱性が大
幅に低下する。このため、Ｔｉを含有する場合は、その
含有量を０．０１乃至１．００重量％とし、Ｚｒを含有
する場合は、その含有量を０．０１乃至１．００重量％
とする。また、Ｔｉ及びＺｒの不可避的不純物量は夫々
０．０１重量％未満とする。 Ti, Zr (Titanium, Zirconium) Ti and Zr are both strong deoxidizing agents and prevent oxidation of the deposited metal. Further, since Ti and Zr form an oxide, they are effective in increasing the strength due to the precipitation effect and improving the toughness due to the refinement of the structure. However, the Ti content is 0.0
If it is less than 1% by weight, the above-mentioned effect cannot be obtained, and if the Ti content exceeds 1.00% by weight, the weldability is deteriorated and the toughness is significantly lowered due to the formation and precipitation of carbides. . Further, similarly to this, the Zr content is 0.
Even when the amount is less than 01% by weight, the above effect cannot be obtained, and when the Zr content exceeds 1.00% by weight, the weldability is deteriorated and the toughness is significantly reduced due to the formation and precipitation of carbides. . Therefore, when Ti is contained, the content is 0.01 to 1.00% by weight, and when Zr is contained, the content is 0.01 to 1.00% by weight.
And The inevitable impurities of Ti and Zr are less than 0.01% by weight, respectively.
【００２８】Ｎｂ、Ｖ（ニオブ、バナジウム） Ｎｂ及びＶは強度上昇、高温強度向上及び靱性改善のた
めに添加される。しかし、Ｎｂ及びＶは夫々０．０１重
量％未満ではこの効果を期待できず、また、夫々１．０
０重量％を超えると、炭化物の生成により、靱性及び耐
割れ性の低下が生じる。従って、ワイヤ中のＮｂ及びＶ
の含有量は夫々０．０１〜１．００重量％とする。 Nb, V (Niobium, Vanadium) Nb and V are added for increasing strength, improving high temperature strength and improving toughness. However, if Nb and V are less than 0.01% by weight, respectively, this effect cannot be expected.
If it exceeds 0% by weight, toughness and crack resistance are deteriorated due to the formation of carbide. Therefore, Nb and V in the wire
The content of each is 0.01 to 1.00% by weight.
【００２９】なお、Ｎｂ及びＶはそれを添加せず、不可
避的不純物としてのみ許容する場合には、この不可避的
不純物量は夫々０．０１重量％未満とする。When Nb and V are not added and are allowed only as unavoidable impurities, the amount of these unavoidable impurities is less than 0.01% by weight.
【００３０】Ｃｕ（銅） Ｃｕは防食効果のある非晶質の皮膜を形成する働きがあ
る。この効果はＣｕ含有量が０．０５重量％未満では認
められず、１．５０重量％を超えるとその効果は飽和
し、逆に溶接割れなどの弊害が生じる。従って、ワイヤ
のＣｕ含有量は０．０５〜１．５０重量％とする。 Cu (Copper) Cu has a function of forming an amorphous film having an anticorrosion effect. This effect is not recognized when the Cu content is less than 0.05% by weight, and the effect is saturated when the Cu content exceeds 1.50% by weight, and adverse effects such as weld cracking occur. Therefore, the Cu content of the wire is 0.05 to 1.50% by weight.
【００３１】なお、Ｃｕが不可避的不純物として含まれ
る場合には、その不可避的不純物量は、０．０５重量％
未満とする。When Cu is contained as an unavoidable impurity, the amount of the unavoidable impurity is 0.05% by weight.
Less than
【００３２】また、ワイヤにＣｕメッキが施されている
場合は、メッキＣｕ量も含めたＣｕ含有量をワイヤのＣ
ｕ含有量とする。When the wire is plated with Cu, the Cu content including the amount of plated Cu is calculated as C of the wire.
u content.
【００３３】Ｃａ（カルシウム）及び希土類元素（ＲＥ
Ｍ） Ｃａ及びＲＥＭは主に溶接金属の強度上昇、延性の向
上、アークの安定化に有効な元素であり、そのためには
夫々０．００１重量％以上含有する必要がある。しか
し、これらの元素を夫々０．０５０重量％を超えて添加
すると鋼中の非金属介在物が多くなり、延性を劣化させ
る。従って、ワイヤのＣａ及びＲＥＭの含有量は夫々
０．００１〜０．０５０重量％とする。なお、ＲＥＭ
（希土類元素）は原子番号５７〜７１の全ての元素をさ
す。 Ca (calcium) and rare earth elements (RE
M) Ca and REM are elements that are mainly effective in increasing the strength of weld metal, improving ductility, and stabilizing the arc, and for that purpose, each must be contained in an amount of 0.001% by weight or more. However, if each of these elements is added in an amount of more than 0.050% by weight, the amount of non-metallic inclusions in the steel increases and the ductility deteriorates. Therefore, the Ca and REM contents of the wire are 0.001 to 0.050% by weight, respectively. In addition, REM
(Rare earth element) refers to all elements having atomic numbers 57 to 71.
【００３４】また、Ｃａ、ＲＥＭの不可避的不純物量は
夫々０．００１重量％未満とする。The inevitable impurities of Ca and REM are less than 0.001% by weight, respectively.
【００３５】Ｂ（ボロン） Ｂは微量添加することで、組織を微細にし、優れた低温
靱性を付与する元素である。しかし、０．０００５重量
％未満の含有量ではこのような効果は期待できない。一
方、０．０５００重量％を超えてＢを含有すると、著し
く耐溶接割れ性が悪化する。従って、Ｂの含有量は０．
０００５〜０．０５００重量％とする。なお、Ｂの不可
避的不純物は０．０００５重量％未満とする。 B (Boron) B is an element which, when added in a trace amount, makes the structure fine and imparts excellent low temperature toughness. However, if the content is less than 0.0005% by weight, such an effect cannot be expected. On the other hand, if B is contained in an amount of more than 0.0500% by weight, the weld crack resistance is significantly deteriorated. Therefore, the content of B is 0.
It is 0005 to 0.0500% by weight. The unavoidable impurities of B are less than 0.0005% by weight.
【００３６】炭素当量Ｗeq：０．１５≦Ｗeq≦０．７０ 炭素当量Ｗeqが０．１５未満では、どのような溶接条件
で溶接しても、止端部の溶接金属と母材とのなじみが悪
く、止端部形状が悪い。このため、良好な疲労特性は期
待できない。炭素当量Ｗeqが大きくなるにつれ、止端部
形状は滑らかとなるが、炭素当量が０．７０を超える
と、溶接作業性が悪く、正常な溶接部が得られない。こ
のような理由で、Ｗeqは０．１５〜０．７０とする。 Carbon equivalent Weq: 0.15≤Weq≤0.70 When the carbon equivalent Weq is less than 0.15, the weld metal at the toe and the base metal are compatible with each other under any welding condition. Poor, bad toe shape. Therefore, good fatigue characteristics cannot be expected. As the carbon equivalent Weq increases, the toe shape becomes smoother, but if the carbon equivalent exceeds 0.70, the welding workability is poor and a normal weld cannot be obtained. For this reason, Weq is set to 0.15 to 0.70.
【００３７】好ましくは、炭素当量Ｗeqは０．２５乃至
０．７０、更に好ましくは、炭素当量Ｗeqは０．３５乃
至０．７０である。The carbon equivalent Weq is preferably 0.25 to 0.70, more preferably the carbon equivalent Weq is 0.35 to 0.70.
【００３８】なお、炭素当量は前記１式に基づいて算出
するが、このＷeqの定義式中の各成分項については、そ
の成分が不可避的不純物の場合でも、その含有量を代入
することとする。各成分について検出限界以下の含有量
では夫々０として代入することとする。The carbon equivalent is calculated on the basis of the above formula 1. For each component term in this definition formula of Weq, the content is substituted even if the component is an unavoidable impurity. . For each component, if the content is below the detection limit, 0 is substituted.
【００３９】次に、本発明の溶接方法の溶接条件につい
て説明する。Next, the welding conditions of the welding method of the present invention will be described.
【００４０】溶接電流Ａ：５０〜５００Ａ 一般のアーク溶接では溶接電流が５０Ａ未満ではアーク
が不安定であり、溶接は不能である。よって、溶接電流
の下限を５０Ａとする。溶接電流が５００Ａを超える
と、シールド不良及びビード形状不良等の問題が発生し
易い。このため、溶接電流は５００Ａを上限とする。 Welding current A: 50 to 500 A In general arc welding, when the welding current is less than 50 A, the arc is unstable and welding is impossible. Therefore, the lower limit of the welding current is set to 50A. If the welding current exceeds 500 A, problems such as defective shield and defective bead shape are likely to occur. Therefore, the upper limit of the welding current is 500A.
【００４１】溶接速度γ：５ｃｍ／分〜２５０ｃｍ／分 溶接速度が５ｃｍ／分未満では、どのような溶接条件で
も、アークが溶融した溶接金属上に埋もれた状態とな
り、アークが不安定になると共にビード形状が悪化す
る。よって、５ｃｍ／分を溶接速度の下限とする。ま
た、溶接速度が２５０ｃｍ／分を超えると、溶接速度が
速すぎてアークが持続しなくなり、ハンピングビードに
なってしまう。よって、２５０ｃｍ／分を溶接速度の上
限とする。 Welding speed γ: 5 cm / min to 250 cm / min If the welding speed is less than 5 cm / min, the arc becomes buried in the molten weld metal under any welding condition, and the arc becomes unstable. The bead shape deteriorates. Therefore, the lower limit of the welding speed is 5 cm / min. If the welding speed exceeds 250 cm / min, the welding speed is too high and the arc does not continue, resulting in a humping bead. Therefore, 250 cm / min is set as the upper limit of the welding speed.
【００４２】溶接電圧：ＶL≦Ｖa≦ＶH 但し、これらのＶL，Ｖa，ＶHは前記数式２、３、４に
より表される。即ち、 Ｖa＝適正溶接電圧（Ｖ） ＶH＝7.96×10-8×Ａ3−1.12×10-4×Ａ2＋0.11×Ａ＋
9.43＋Ｐ1＋Ｐ2−Ｗeq×5−4 ＶL＝7.96×10-8×Ａ3−1.12×10-4×Ａ2＋0.11×Ａ＋
9.43＋Ｐ1＋Ｐ2 また、Ａ、Ｐ1、Ｐ2は表１に示す値をとり、炭素当量Ｗ
eqは前記数式１により表される。 Welding voltage: VL≤Va≤VH However, these VL, Va, and VH are represented by the above-mentioned equations 2, 3, and 4. That is, Va = adequate welding voltage (V) VH = 7.96 × 10 −8 × A 3 −1.12 × 10 −4 × A 2 + 0.11 × A +
9.43 + P 1 + P 2 -Weq × 5−4 VL = 7.96 × 10 −8 × A 3 −1.12 × 10 −4 × A 2 + 0.11 × A +
9.43 + P1 + P2 Moreover, A, P1 and P2 take the values shown in Table 1, and carbon equivalent W
eq is represented by Equation 1 above.
【００４３】図４は横軸に溶接電圧をとり、縦軸に曲率
半径ρをとって、溶接電圧、炭素当量Ｗeq及び曲率半径
ρの関係を示すグラフ図である。この図４にみるよう
に、溶接電圧が高くなるにつれて、ビード止端部の曲率
半径ρは大きくなり、溶接継手の疲労強度が向上する。FIG. 4 is a graph showing the relationship between the welding voltage, the carbon equivalent Weq, and the radius of curvature ρ, with the horizontal axis representing the welding voltage and the vertical axis representing the radius of curvature ρ. As shown in FIG. 4, as the welding voltage increases, the radius of curvature ρ of the bead toe increases, and the fatigue strength of the welded joint improves.
【００４４】しかしながら、溶接電流、シールドガス組
成、溶接速度によって決まる電圧ＶHより高い電圧にな
ると、アンダーカットが発生し、継手として不良になっ
てしまう。よって、適正溶接電圧Ｖaの上限はＶHで定義
される値とする。However, when the voltage becomes higher than the voltage VH determined by the welding current, the shield gas composition, and the welding speed, undercutting occurs and the joint becomes defective. Therefore, the upper limit of the proper welding voltage Va is a value defined by VH.
【００４５】逆に、溶接電圧が低くなるにつれて、止端
部の曲率半径ρは小さくなる。しかし、その傾向はワイ
ヤ組成によって異なる。発明者等はＷeqで定義する炭素
当量が大きいワイヤほど同一電圧ではビード止端部の曲
率半径ρが大きいという事実を見い出した。図２から、
止端部曲率半径ρが０．０５ｍｍ未満では急激に疲労強
度が悪化することが分かる。このことから、良好な疲労
強度を得るのに必要とされる止端部曲率半径ρ＝０．０
５ｍｍが得られる最低溶接電圧をＶLと定義し、これを
適正溶接電圧の下限値とする。ＶLは溶接電流、シール
ドガス組成及び溶接速度の他、炭素当量Ｗeqの関数にな
っている。このＶL未満の溶接電圧では、止端部曲率半
径が小さく、その結果、継手の疲労強度が小さくなる。
以上のことから、適正溶接電圧はＶL以上ＶH以下であ
る。On the contrary, the radius of curvature ρ of the toe portion becomes smaller as the welding voltage becomes lower. However, the tendency depends on the wire composition. The inventors have found that a wire having a larger carbon equivalent defined by Weq has a larger radius of curvature ρ at the toe of the bead at the same voltage. From FIG.
It can be seen that the fatigue strength rapidly deteriorates when the curvature radius ρ of the toe portion is less than 0.05 mm. From this, the toe radius of curvature ρ = 0.0 required to obtain good fatigue strength
The minimum welding voltage at which 5 mm is obtained is defined as VL, and this is the lower limit of the proper welding voltage. VL is a function of the carbon equivalent Weq in addition to the welding current, the shield gas composition and the welding speed. At a welding voltage below VL, the radius of curvature of the toe is small, and as a result, the fatigue strength of the joint is small.
From the above, the proper welding voltage is VL or more and VH or less.
【００４６】薄板高張力鋼板の板厚 ０．５〜７．０ｍ
ｍ 板厚が７．０ｍｍ超えると１パスで溶接することが難し
くなり、また、大電流を必要とすることにより、シール
ド性の悪化及びビード形状不良が起こりやすくなる。逆
に、板厚が０．５ｍｍ未満では、ソリッドワイヤによる
溶接では溶接不能である。このため、薄板高張力鋼板の
板厚は、０．５乃至７．０ｍｍとする。 Thickness of thin high-strength steel plate 0.5 to 7.0 m
When the m plate thickness exceeds 7.0 mm, it becomes difficult to perform welding in one pass, and a large current is required, so that the shield property is deteriorated and the bead shape is apt to occur. On the contrary, if the plate thickness is less than 0.5 mm, it cannot be welded by solid wire welding. Therefore, the thickness of the thin high-tensile steel plate is set to 0.5 to 7.0 mm.
【００４７】溶接トーチの前進角θ1：０°〜３０° 溶接トーチの溶接方向の角度（前進後退角）θ1（図３
参照）を後退角（０°未満）にすると、ビードが凸にな
り、幅も不足しやすくなると共に、止端部曲率半径も小
さくなり、疲労強度の低下につながる。前進角θ1を大
きくするにつれ、止端部曲率半径は大きくなるが、前進
角θ1が３０°を超えると、アークが不安定になり、ア
ンダーカットの発生が生じる。よって、トーチの前進角
θ1は０°以上３０°以下とする。 Advance angle θ1 of welding torch: 0 ° to 30 ° Angle of welding direction of welding torch (advance receding angle) θ1 (Fig. 3)
When the angle of refraction is smaller than 0 °, the bead becomes convex and the width tends to be insufficient, and the radius of curvature of the toe portion also becomes small, leading to a reduction in fatigue strength. As the advancing angle θ1 increases, the radius of curvature of the toe increases, but when the advancing angle θ1 exceeds 30 °, the arc becomes unstable and undercut occurs. Therefore, the advancing angle θ1 of the torch is set to 0 ° or more and 30 ° or less.
【００４８】溶接トーチ傾斜角度θ2：３０°〜６０° トーチと下板との間の角度（傾斜角度）θ2（図３参
照）が６０°を超えると、止端部曲率半径ρが小さくな
り、また下板に重点的にアークが当たり、所謂抜けやす
くなる。傾斜角度を小さくするにつれて、止端部曲率半
径ρが大きくなるが、３０°未満ではビードが凸になり
やすく、形状不良となる。従って、トーチの傾斜角度θ
2は３０乃至６０°とする。 Welding torch tilt angle θ2: 30 ° to 60 ° If the angle (tilt angle) θ2 (see FIG. 3) between the torch and the lower plate exceeds 60 °, the toe curvature radius ρ becomes small, Further, the arc is focused on the lower plate, so that the so-called easily comes off. The radius of curvature ρ of the toe portion increases as the inclination angle decreases, but if the angle of inclination is less than 30 °, the bead is likely to be convex, resulting in poor shape. Therefore, the torch tilt angle θ
2 is 30 to 60 °.
【００４９】[0049]
【実施例】次に、本発明の実施例について、その比較例
と比較して説明する。下記表２に示す化学成分のソリッ
ドワイヤを使用して、下記表３に示す試験条件及び下記
表４に示す溶接条件で重ね隅肉溶接を行い、継手の疲労
試験片を採取した。但し、Ａ乃至Ｈはソリッドワイヤの
番号である。EXAMPLES Next, examples of the present invention will be described in comparison with comparative examples. Using a solid wire having the chemical composition shown in Table 2 below, lap fillet welding was performed under the test conditions shown in Table 3 below and the welding conditions shown in Table 4 below, and fatigue test pieces of the joint were collected. However, A to H are solid wire numbers.
【００５０】[0050]
【表２】 [Table 2]
【００５１】[0051]
【表３】 [Table 3]
【００５２】[0052]
【表４】 [Table 4]
【００５３】この疲労試験片のビードを一条件につき２
０カ所採取し、倍率５０倍で止端部の曲率半径ρを測定
した。各条件での半径は累積確率５０％以上の代表径と
した。これらの試験結果を表４に合わせて示した。The bead of this fatigue test piece was 2 per condition.
It was sampled at 0 places and the curvature radius ρ of the toe portion was measured at a magnification of 50 times. The radius under each condition was a representative diameter with a cumulative probability of 50% or more. The results of these tests are also shown in Table 4.
【００５４】この表４にみるように、 （１）実施例１〜３、４〜６、７〜９、１０〜１２、１
３〜１５、１６〜２３はソリッドワイヤの化学成分及び
Ｗeqが全て本発明の限定範囲を満足しており、その結
果、ビード止端部曲率半径ρが０．０５ｍｍ以上とな
り、良好な疲労特性を持つ継手となった。As shown in Table 4, (1) Examples 1 to 3, 4 to 6, 7 to 9, 10 to 12 and 1
Nos. 3 to 15 and 16 to 23 all have the chemical composition and Weq of the solid wire satisfying the limited range of the present invention, and as a result, the bead toe curvature radius ρ becomes 0.05 mm or more, and good fatigue properties are obtained. It became a joint to have.
【００５５】（２）比較例２４、２６、２８、３０、３
２は溶接電圧がＶLより低いために、止端部曲率半径が
０．０５ｍｍより小さくなり、その結果疲労特性の劣る
継ぎ手となり不良である。(2) Comparative Examples 24, 26, 28, 30, 3
In No. 2, since the welding voltage is lower than VL, the radius of curvature of the toe portion becomes smaller than 0.05 mm, and as a result, the joint becomes inferior in fatigue characteristics and is defective.
【００５６】（３）比較例２５、２７、２９、３１、３
３は溶接電圧がＶHより高いために、止端部曲率半径は
大きいのであるが、アンダーカットが発生してしまい、
溶接継手として不良である。(3) Comparative Examples 25, 27, 29, 31, 3
In No. 3, since the welding voltage is higher than VH, the curvature radius of the toe is large, but undercut occurs,
It is defective as a welded joint.
【００５７】（４）比較例３４は止端部曲率半径ρは良
好な値を示していたものの、Ｗeqが限定範囲０．１５以
上０．７０以下を上回っている。そのため、強度過剰と
なり、低温割れが発生した。溶接部として割れが発生し
ては継手として不良である。(4) In Comparative Example 34, the curvature radius ρ of the toe portion showed a good value, but the Weq exceeded the limited range of 0.15 to 0.70. Therefore, the strength became excessive and low temperature cracking occurred. If cracks occur in the welded part, the joint is defective.
【００５８】（５）比較例３５はＷeqが限定範囲０．１
５乃至０．７０を下回っている。そのため、溶接電圧が
限定範囲を満足しているものの、ビード形状が悪く、止
端部曲率半径がρが０．０５ｍｍを下回り、疲労特性が
劣る。(5) In Comparative Example 35, Weq is in a limited range of 0.1.
It is below 5 to 0.70. Therefore, although the welding voltage satisfies the limited range, the bead shape is poor, the radius of curvature of the toe portion is less than 0.05 mm, and the fatigue property is poor.
【００５９】（６）比較例３６は止端部曲率半径ρは良
好な値を示したものの、ソリッドワイヤの成分のうち、
ＳｉとＭｎが本発明の限定範囲より低いために、溶接作
業性が著しく悪く、また、脱酸不足となり、酸化された
不良なビードとなった。(6) In Comparative Example 36, the radius of curvature ρ of the toe portion showed a good value, but among the components of the solid wire,
Since Si and Mn were lower than the limits of the present invention, the welding workability was remarkably poor, and deoxidation became insufficient, resulting in oxidized poor beads.
【００６０】図４はこれらの試験結果のうち、溶接電
流、板厚、トーチ前進後退角、トーチ傾斜角の条件が同
一である試験（実施例１乃至１５、比較例２４乃至３
３）について、溶接電圧、Ｗeq、ビード止端部曲率半径
ρの関係を示したものである。FIG. 4 shows a test in which the welding current, the plate thickness, the torch advance / retreat angle and the torch tilt angle are the same among these test results (Examples 1 to 15 and Comparative Examples 24 to 3).
3) shows the relationship among welding voltage, Weq, and bead toe curvature radius ρ.
【００６１】また、図５は同じく炭素当量Ｗeqと適正溶
接電圧範囲Ｖaとの関係を示したものである。この図５
には、適正溶接電圧Ｖaがその上限値ＶHと、下限値ＶL
との間の領域として示されている。FIG. 5 also shows the relationship between the carbon equivalent Weq and the proper welding voltage range Va. This Figure 5
The proper welding voltage Va is the upper limit value VH and the lower limit value VL.
It is shown as the area between and.
【００６２】また、本試験で得られた溶接金属部の化学
成分は、夫々下記表５に示される成分範囲内であった。
但し、表５において、は実施例１〜３及び比較例２
４、２５の場合、は実施例４〜６、比較例２６、２７
の場合、は実施例７〜９、比較例２８、２９の場合、
は実施例１０〜１２、比較例３０、３１の場合、は
実施例１３〜１５、実施例１６〜２３、比較例３２、３
３の場合、は比較例３４の場合、は比較例３５の場
合、は比較例３６の場合である。The chemical compositions of the weld metal parts obtained in this test were within the ranges shown in Table 5 below.
However, in Table 5, Examples 1 to 3 and Comparative Example 2
In the case of 4 and 25, Examples 4 to 6 and Comparative Examples 26 and 27
In the case of Examples 7 to 9 and Comparative Examples 28 and 29,
In the case of Examples 10 to 12 and Comparative Examples 30 and 31, are Examples 13 to 15, Examples 16 to 23, Comparative Examples 32 and 3.
In the case of 3, is the case of Comparative Example 34, is the case of Comparative Example 35, and is the case of Comparative Example 36.
【００６３】[0063]
【表５】 [Table 5]
【００６４】[0064]
【発明の効果】以上説明したように、本発明はソリッド
ワイヤの組成及び炭素当量Ｗeqを所定範囲に規定し、更
に、溶接電圧、溶接電流及び溶接速度を適切な範囲に規
定して溶接するので、ビード止端部の曲率半径を大きく
することができ、薄板高張力鋼の溶接ワイヤとして極め
て有効であり、本発明の溶接ワイヤ及び溶接方法を使用
することにより、溶接継手の疲労特性を著しく向上させ
ることができる。As described above, according to the present invention, the solid wire composition and the carbon equivalent Weq are defined within a predetermined range, and further, the welding voltage, the welding current and the welding speed are defined within the appropriate ranges, and thus welding is performed. , The radius of curvature of the toe of the bead can be increased, and it is extremely effective as a welding wire for thin plate high-strength steel. By using the welding wire and welding method of the present invention, the fatigue characteristics of welded joints are significantly improved. Can be made.
【図１】ビード止端部の曲率半径ρを示す模式図であ
る。FIG. 1 is a schematic view showing a radius of curvature ρ of a bead toe portion.
【図２】止端部曲率半径ρと、時間強さとの関係を示す
グラフ図である。FIG. 2 is a graph showing a relationship between a toe radius of curvature ρ and temporal strength.
【図３】溶接方法を説明する模式図である。FIG. 3 is a schematic diagram illustrating a welding method.
【図４】溶接電圧、炭素当量Ｗeq、曲率半径ρの相互関
係を示すグラフ図である。FIG. 4 is a graph showing a mutual relationship between welding voltage, carbon equivalent Weq, and radius of curvature ρ.
【図５】炭素当量Ｗeqと、適正溶接電圧Ｖaとの関係を
示すグラフ図である。FIG. 5 is a graph showing the relationship between carbon equivalent Weq and appropriate welding voltage Va.
１，２：母材 ３；ビード ４；止端部 ５；トーチ 1, 2: base material 3; bead 4; toe portion 5; torch
Claims (5)
ｉ；０．０５乃至２．００重量％及びＭｎ；０．２０乃
至３．００重量％を含有すると共に、Ｎｉ；０．５乃至
５．０重量％、Ｃｒ；０．００５乃至３．００重量％、
Ｍｏ；０．１０乃至２．００重量％、Ｖ；０．０１乃至
１．００重量％、Ｎｂ；０．０１乃至１．００重量％、
Ｔｉ；０．０１乃至１．００重量％、Ａｌ；０．０１乃
至１．００重量％、Ｚｒ；０．０１乃至１．００重量
％、Ｃｕ；０．０５乃至１．５０重量％、Ｂ；０．００
０５乃至０．０５００重量％、Ｃａ；０．００１乃至
０．０５０重量％及び希土類元素；０．００１乃至０．
０５０重量％からなる群から選択された少なくとも１種
の元素を含有し、Ｐ含有量を０．０５重量％以下、Ｓ含
有量を０．０５重量％以下に規制し、残部が鉄及び不可
避的不純物からなり、且つ、下記数式で示す炭素当量Ｗ
eqが０．１５乃至０．７０であることを特徴とする溶接
用ソリッドワイヤ。 Ｗeq＝［Ｃ］＋［Ｓｉ］／２４＋［Ｍｎ］／６＋［Ｎ
ｉ］／６０＋［Ｃｒ］／５＋［Ｍｏ］／４＋［Ｖ］／１
４＋［Ｎｂ］＋［Ｔｉ］／１４ 但し、［Ｍ］はワイヤ中の成分Ｍの含有量（重量％）1. C: 0.01 to 0.40% by weight, S
i: 0.05 to 2.00% by weight and Mn: 0.20 to 3.00% by weight, Ni: 0.5 to 5.0% by weight, Cr: 0.005 to 3.00% by weight %,
Mo; 0.10 to 2.00% by weight, V; 0.01 to 1.00% by weight, Nb; 0.01 to 1.00% by weight,
Ti; 0.01 to 1.00% by weight, Al; 0.01 to 1.00% by weight, Zr; 0.01 to 1.00% by weight, Cu; 0.05 to 1.50% by weight, B; 0.00
05 to 0.0500% by weight, Ca; 0.001 to 0.050% by weight and rare earth element; 0.001 to 0.
It contains at least one element selected from the group consisting of 050% by weight, regulates the P content to 0.05% by weight or less and the S content to 0.05% by weight or less, and balances iron and unavoidable. Carbon equivalent W consisting of impurities and represented by the following formula
A solid wire for welding, wherein eq is 0.15 to 0.70. Weq = [C] + [Si] / 24 + [Mn] / 6 + [N
i] / 60 + [Cr] / 5 + [Mo] / 4 + [V] / 1
4+ [Nb] + [Ti] / 14 where [M] is the content of the component M in the wire (% by weight)
を使用し、溶接電圧Ｖaを下記数式で示す範囲内に設定
し、溶接電流が５０乃至５００Ａ、溶接速度が５乃至２
５０ｃｍ／分の条件で、１パスで溶接することを特徴と
する溶接方法。 ＶL≦Ｖa≦ＶH、但し、 ＶL＝7.96×10-8×Ａ3−1.12×10-4×Ａ2＋0.11×Ａ＋
9.43＋Ｐ1＋Ｐ2−Ｗeq×5−4 ＶH＝7.96×10-8×Ａ3−1.12×10-4×Ａ2＋0.11×Ａ＋
9.43＋Ｐ1＋Ｐ2 Ａ；溶接電流 Ｐ1；シールドガス組成が、ＣＯ2及び不可避的不純物か
らなる場合はＰ1＝０、シールドガス組成が、Ａｒ；５
０体積％以上を含有すると共に、残部がＣＯ2、Ｏ2及び
Ｈｅからなる群から選択された少なくとも１種のガス及
び不可避的不純物からなる混合ガスの場合は、Ｐ1＝−
２、それ以外のシールドガス組成の場合は、Ｐ1＝−１ Ｐ2；溶接速度ｒが５０ｃｍ／分以下の場合はＰ2＝０、
溶接速度ｒが５０ｃｍ／分を超える場合はＰ2＝−ｒ／
２５＋２2. The solid wire for welding according to claim 1 is used, the welding voltage Va is set within the range shown by the following mathematical formula, the welding current is 50 to 500 A, and the welding speed is 5 to 2.
A welding method characterized by welding in one pass under the condition of 50 cm / min. VL ≦ Va ≦ VH, where VL = 7.96 × 10 −8 × A 3 −1.12 × 10 −4 × A 2 + 0.11 × A +
9.43 + P1 + P2-Weq x 5-4 VH = 7.96 x 10 -8 x A 3 -1.12 x 10 -4 x A 2 + 0.11 x A +
9.43 + P1 + P2 A; Welding current P1; P1 = 0 when shield gas composition consists of CO 2 and inevitable impurities, shield gas composition is Ar; 5
In the case of a mixed gas containing 0 volume% or more and the balance being at least one gas selected from the group consisting of CO 2 , O 2 and He and an unavoidable impurity, P 1 = −
2, P1 = -1 P2 for other shield gas compositions; P2 = 0 for welding speed r of 50 cm / min or less,
When the welding speed r exceeds 50 cm / min, P2 = -r /
25 + 2
ｍの高張力鋼板であることを特徴とする請求項２に記載
の溶接方法。3. The material to be welded has a thickness of 0.5 to 7.0 m.
The high-strength steel sheet of m is a welding method according to claim 2.
であることを特徴とする請求項２又は３に記載の溶接方
法。4. The advancing angle θ1 of the welding torch is 0 to 30 °.
The welding method according to claim 2 or 3, wherein
０°であることを特徴とする請求項２乃至４のいずれか
１項に記載の溶接方法。5. The inclination angle θ2 of the welding torch is 30 to 6
It is 0 degree, The welding method of any one of Claims 2 thru | or 4 characterized by the above-mentioned.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6157269A JP2801147B2 (en) | 1994-07-08 | 1994-07-08 | Welding method |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6157269A JP2801147B2 (en) | 1994-07-08 | 1994-07-08 | Welding method |
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| Publication Number | Publication Date |
|---|---|
| JPH0825080A true JPH0825080A (en) | 1996-01-30 |
| JP2801147B2 JP2801147B2 (en) | 1998-09-21 |
Family
ID=15645968
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP6157269A Expired - Fee Related JP2801147B2 (en) | 1994-07-08 | 1994-07-08 | Welding method |
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| Country | Link |
|---|---|
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| JP2010228001A (en) * | 2009-03-03 | 2010-10-14 | Kobe Steel Ltd | Solid wire for welding |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0796391A (en) * | 1993-09-29 | 1995-04-11 | Daido Steel Co Ltd | Wire for gas shielded arc welding |
-
1994
- 1994-07-08 JP JP6157269A patent/JP2801147B2/en not_active Expired - Fee Related
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0796391A (en) * | 1993-09-29 | 1995-04-11 | Daido Steel Co Ltd | Wire for gas shielded arc welding |
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| JP2005046879A (en) * | 2003-07-29 | 2005-02-24 | Jfe Steel Kk | Steel strand to form steel wire for carbon dioxide gas-shielded arc welding |
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