JP2005028409A - Submerged-arc welding method - Google Patents
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本発明は、優れた低温靭性を有し、両面一層の高速溶接性が優れたサブマージアーク溶接方法に関する。 The present invention relates to a submerged arc welding method having excellent low-temperature toughness and excellent high-speed weldability on both sides.
天然ガス又は石油を輸送するパイプラインに使用されるＵＯＥ鋼管は、操業圧力を増加させ、輸送効率の向上を図るため、高強度化と共に、高靭性化が求められている。このため、母材は熱影響部の靭性確保及び溶接性向上を目的として、低炭素当量化が進められている。また、母材と同様に溶接金属も従来より良好な靭性が必要になっている。一般に、ＵＯＥ鋼管のシーム溶接には多電極サブマージアーク溶接法による両面一層溶接が使用されているが、母材希釈が大きいため、溶接金属の靭性は母材成分の影響を受けやすい。特に、母材の炭素当量が低くなると、溶接金属の炭素当量も低くなるために、ミクロ組織が劣化し、靭性の向上がより困難になる。 UOE steel pipes used in pipelines for transporting natural gas or oil are required to have high strength and high toughness in order to increase operating pressure and improve transport efficiency. For this reason, the base material is being reduced in carbon equivalent for the purpose of ensuring the toughness of the heat-affected zone and improving the weldability. In addition, as with the base material, the weld metal is required to have better toughness than before. In general, double-sided single-layer welding by a multi-electrode submerged arc welding method is used for seam welding of UOE steel pipes. However, since the base metal dilution is large, the toughness of the weld metal is easily affected by the base material components. In particular, when the carbon equivalent of the base metal is lowered, the carbon equivalent of the weld metal is also lowered, so that the microstructure is deteriorated and it becomes more difficult to improve toughness.
低温靭性が優れた溶接材料としては、例えば、特開平１０−１１３７９１号公報に開示されているが、この公報に記載の技術は両面一層高速溶接ではない。また、特開昭６１−１４７９９０号公報には、ワイヤの構成元素及び含有率を厳密に規定することによって、強度、低温靭性及び耐割れ性が優れた溶接金属部を得ることができると記載されている。しかし、この公報に記載の技術は、単電極溶接であり、溶接速度も比較的低速である。 As a welding material excellent in low-temperature toughness, for example, it is disclosed in Japanese Patent Laid-Open No. 10-113791, but the technique described in this publication is not double-sided and high-speed welding. Japanese Patent Application Laid-Open No. 61-147990 describes that a weld metal part having excellent strength, low temperature toughness and crack resistance can be obtained by strictly defining the constituent elements and content of the wire. ing. However, the technique described in this publication is single electrode welding, and the welding speed is also relatively low.
一方、多電極サブマージアーク溶接法による両面一層溶接は高速度であるため、スラグ巻き込み及びオーバーラップ等の溶接欠陥が発生しやすい。そこで、これまでにもＵＯＥ鋼管の高速溶接に関しては溶接欠陥の軽減法がいくつか提案されている。例えば、特開平９−８５４４０号公報、特開平９−２７７０４３号公報、特開平９−２３９５３６号公報、特開平１０−４３８５９号公報、特開平１０−２５８３６３号公報及び特開平１０−２５８３６４号公報には、多電極を使用し、溶接金属に磁気撹拌を与えることにより、溶接欠陥の軽減を図ることができるとしている。しかし、この方法は磁場を形成するような設備が必要となり、コストがかかるうえ、溶接金属の低温靭性までも改善できるものではない。また、特開平４−１４７７７０号公報には、６本以上の電極を使用した高速サブマージアーク溶接法が提案されている。しかし、この方法は、電極数を増やすことで高速化は図られるものの、それに伴い、溶接欠陥発生の危険率が増大し、設備費が増大したり、オペレーションが複雑化するために、高速化のメリットが十分に生かされたものとは必ずしも言えないものであった。更に、この公報に記載された技術は、溶接金属の低温靭性を改善できるものではない。 On the other hand, double-sided single-layer welding by the multi-electrode submerged arc welding method has a high speed, so that welding defects such as slag entrainment and overlap are likely to occur. So far, several methods for reducing welding defects have been proposed for high-speed welding of UOE steel pipes. For example, in JP-A-9-85440, JP-A-9-277043, JP-A-9-239536, JP-A-10-43859, JP-A-10-258363, and JP-A-10-258364. Uses multi-electrodes and gives magnetic agitation to the weld metal to reduce welding defects. However, this method requires equipment for forming a magnetic field, which is costly and cannot improve even the low temperature toughness of the weld metal. Japanese Laid-Open Patent Publication No. 4-147770 proposes a high-speed submerged arc welding method using six or more electrodes. However, although this method can increase the speed by increasing the number of electrodes, the risk of welding defects increases, the equipment cost increases, and the operation becomes complicated. It could not be said that the merit was fully utilized. Furthermore, the technique described in this publication cannot improve the low temperature toughness of the weld metal.
上述の如く、低炭素当量の高張力鋼又は鋼管のシーム溶接で適用する母材希釈が大きい両面一層溶接の場合でも、優れた低温靭性と高速溶接における優れた品質が得られる最適な溶接方法については、従来存在しなかった。 As described above, the optimum welding method that provides excellent low-temperature toughness and excellent quality in high-speed welding even in the case of double-sided single-layer welding with large base metal dilution applied in seam welding of high-tensile steel or steel pipe with low carbon equivalent Did not exist in the past.
本発明はかかる問題点に鑑みてなされたものであって、母材成分系の低炭素当量化においても、優れた低温靭性の溶接金属が得られると共に、両面一層の高速溶接性が優れたサブマージアーク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 such problems, and even in the low carbon equivalent of the base material component system, it is possible to obtain a weld metal having excellent low temperature toughness, and a submerged excellent in high-speed weldability on both sides. An object is to provide an arc welding method.
本発明に係るサブマージアーク溶接方法は、２電極乃至４電極の多電極サブマージアーク溶接方法において、下記数式１で示される［Ｍ］の値が下記各元素の範囲を満足する溶接ワイヤを使用し、下記範囲の溶接電流比にてサブマージアーク溶接することを特徴とする。
The submerged arc welding method according to the present invention uses a welding wire in which the value of [M] represented by the following
但し、［Ｍ］は第１電極乃至第４電極ワイヤに含まれる元素Ｍにより下記数式１で計算される値を表す。但し、３電極及び２電極サブマージアーク溶接の場合は、夫々第４電極ワイヤの［Ｍ］ＡＴ３と、第４電極ワイヤの［Ｍ］ＡＴ３及び第３電極ワイヤの［Ｍ］ＡＴ２とは０である。なお、［Ｍ］の適正範囲は、電極の数によらず、同一である。
However, [M] represents a value calculated by the following
［Ｍ］ＡＬ：第１電極ワイヤ中のＭ元素の質量（％）
［Ｍ］ＡＴ１：第２電極ワイヤ中のＭ元素の質量（％）
［Ｍ］ＡＴ２：第３電極ワイヤ中のＭ元素の質量（％）
［Ｍ］ＡＴ３：第４電極ワイヤ中のＭ元素の質量（％）
ＩＬ：第１電極ワイヤの溶接電流（Ａ）
ＩＴ１：第２電極ワイヤの溶接電流（Ａ）
ＩＴ２：第３電極ワイヤの溶接電流（Ａ）
ＩＴ３：第４電極ワイヤの溶接電流（Ａ）
[M] AL : Mass of element M in the first electrode wire (%)
[M] AT1 : Mass of element M in the second electrode wire (%)
[M] AT2 : Mass of element M in the third electrode wire (%)
[M] AT3 : Mass of element M in the fourth electrode wire (%)
I L : welding current of the first electrode wire (A)
IT1 : Welding current of the second electrode wire (A)
IT2 : welding current of the third electrode wire (A)
IT3 : welding current of the fourth electrode wire (A)
Ｍ元素の［Ｍ］の値は、下記範囲を満たす。
［Ｃ］：０．０７乃至０．２０質量％
［Ｍｎ］：１．４５乃至２．７０質量％
［Ｓｉ］：０．１０乃至０．７０質量％
［Ｔｉ］：０．１０乃至０．３０質量％
［Ａｌ］：０．００３乃至０．０３０質量％
［Ｐ］：≦０．０２０質量％
［Ｓ］：≦０．０２０質量％
［Ｖ］：≦０．０２０質量％
［Ｃｕ］：≦０．７０質量％
［Ｂ］：≦０．０２０質量％
［Ｏ］：≦０．０１０質量％
［Ｎ］：≦０．００８質量％
［Ｍｏ］：≦１．０質量％
［Ｎｉ］、［Ｃｒ］、［Ｍｏ］（合計量で）；２．０質量％以下
残部はＦｅ及び不可避不純物である。
The value of [M] of the M element satisfies the following range.
[C]: 0.07 to 0.20 mass%
[Mn]: 1.45 to 2.70 mass%
[Si]: 0.10 to 0.70 mass%
[Ti]: 0.10 to 0.30 mass%
[Al]: 0.003 to 0.030 mass%
[P]: ≦ 0.020 mass%
[S]: ≦ 0.020 mass%
[V]: ≦ 0.020 mass%
[Cu]: ≦ 0.70 mass%
[B]: ≦ 0.020 mass%
[O]: ≦ 0.010 mass%
[N]: ≦ 0.008 mass%
[Mo]: ≦ 1.0% by mass
[Ni], [Cr], [Mo] (in total amount); 2.0 mass% or less The balance is Fe and inevitable impurities.
溶接電流比は下記範囲を満たす。但し、３電極の場合はＩＴ３／ＩＬは０である。また、４電極の場合はＩＴ２／ＩＬ及びＩＴ３／ＩＬが０である。
ＩＴ１／ＩＬ：０．６０乃至０．９０
ＩＴ２／ＩＬ：０．５０乃至０．８０
ＩＴ３／ＩＬ：０．５０乃至０．８０
The welding current ratio satisfies the following range. However, in the case of 3 electrodes, IT3 / IL is 0. In the case of four electrodes, IT2 / IL and IT3 / IL are zero.
I T1 / I L : 0.60 to 0.90
I T2 / I L : 0.50 to 0.80
I T3 / I L : 0.50 to 0.80
以上詳述したように、本発明によれば、優れた低温靭性を有する溶接金属を得ることができ、母材成分系の低炭素等量化に際し両面一層の高速溶接性が優れたサブマージアーク溶接が可能になる。 As described above in detail, according to the present invention, it is possible to obtain a weld metal having excellent low temperature toughness, and submerged arc welding having excellent high-speed weldability on both sides in reducing the carbon equivalent of the base material component system. It becomes possible.
以下、本発明について、詳細に説明する。前述のとおり、母材の成分系は高品質化及び溶接性を考慮して、低炭素当量化が進められている。これは、溶接による熱影響部の靭性確保のために低Ｃ、低Ｓｉとし、低炭素当量化にともなう母材強度の低下をＮｂ、Ｔｉ、Ｖ等の微量添加及び制御圧延による組織の微細化により補い、高強度と高靭性を得るものである。しかし、両面一層溶接の場合、母材希釈が大きいために、溶接金属の化学成分は母材化学成分の影響を受けやすく、母材の低炭素当量化にともない、溶接金属の炭素当量も低くなる。そのため、溶接金属では、初析フェライト析出及び組織の粗大化が起こり、更に母材の低Ｃ及び低Ｓｉ化によって、脱酸成分が不足するために、溶接金属の酸素量が増加する等、複合的な原因によって靭性が劣化してしまうという問題点がある。組織の劣化に対しては、ワイヤ及びフラックス成分の調整により、Ｃ、Ｍｎ、Ｎｉ、Ｃｒ、Ｍｏ、Ｖ、Ｔｉ及びＢ等の合金成分を補填する方法が考えられる。特に、組織改善に有効なＣ、Ｍｏ、Ｖ、Ｔｉ及びＢ等の添加は、２番目に溶接する側（裏面側）の溶接金属の熱影響による最初に溶接する側（表面側）の溶接金属の硬化を引き起こすことがあるため、適量に制限しなければならず、従って上記方法は溶接金属の高靭性化を達成できる有効な手段とは言えない。また、脱酸成分の不足を補うために、溶接材料に単純にＣ及びＳｉを添加しても靭性向上の効果は少ない。これは、母材の低炭素当量化にともなって添加したＴｉ及びＶがＣと炭化物を形成したり、Ｓｉの酸化物が溶接金属に過剰に残留し、靭性に悪影響を及ぼすためと考えられる。また、脱酸作用のあるＭｎのみを更に添加しても、脱酸効果が少なく靭性の向上効果は認められなかった。 Hereinafter, the present invention will be described in detail. As described above, the component system of the base material is being reduced in carbon equivalent in consideration of high quality and weldability. In order to ensure the toughness of the heat-affected zone by welding, low C and low Si are used. The reduction in the base metal strength due to the low carbon equivalent is reduced by the addition of a small amount of Nb, Ti, V, etc., and the microstructure is refined by controlled rolling. Thus, high strength and high toughness are obtained. However, in the case of double-sided single-layer welding, since the base metal dilution is large, the chemical component of the weld metal is easily affected by the base metal chemical component, and the carbon equivalent of the weld metal also decreases as the base material has a low carbon equivalent. . Therefore, in the weld metal, precipitation of proeutectoid ferrite and coarsening of the structure occur, and further, the amount of oxygen in the weld metal increases due to insufficient deoxidation component due to low C and low Si of the base metal. There is a problem that toughness deteriorates due to various causes. For the deterioration of the structure, a method of compensating for alloy components such as C, Mn, Ni, Cr, Mo, V, Ti, and B by adjusting the wire and flux components can be considered. In particular, the addition of C, Mo, V, Ti, and B, which is effective for improving the structure, is the weld metal on the first weld side (front side) due to the thermal effect of the weld metal on the second weld side (back side). Therefore, the above method is not an effective means for achieving high toughness of the weld metal. Moreover, even if C and Si are simply added to the welding material in order to compensate for the shortage of the deoxidizing component, the effect of improving toughness is small. This is thought to be because Ti and V added as the base material has a low carbon equivalent form carbides with C, and excessively oxides of Si remain in the weld metal, adversely affecting toughness. Further, even when only Mn having a deoxidizing action was further added, the deoxidizing effect was small and the toughness improving effect was not recognized.
そこで、本発明者等が鋭意実験研究した結果、Ｃ、Ｓｉ及びＭｎの適正添加に加えて、Ｔｉ及びＡｌの複合添加が最も有効であることを見出した。これは、Ｔｉ酸化物の微細分散による組織の微細化により高靭性を得るものである。この効果を得るためには溶接金属のＴｉ及び酸素量の適正化が重要であるが、低炭素当量の母材では酸素量が過大となりやすい。そこで、Ｓｉ及びＡｌの複合添加により溶接金属の酸素量を適正化し、前述の効果を得ている。 Therefore, as a result of intensive experiment research conducted by the present inventors, it was found that the combined addition of Ti and Al is the most effective in addition to the appropriate addition of C, Si and Mn. This is to obtain high toughness by refining the structure by fine dispersion of Ti oxide. In order to obtain this effect, it is important to optimize the amount of Ti and oxygen in the weld metal, but the amount of oxygen tends to be excessive in a base material having a low carbon equivalent. Therefore, the amount of oxygen in the weld metal is optimized by the combined addition of Si and Al, and the above-described effect is obtained.
一方、母材の低炭素当量化に伴い従来の溶接材料では溶接金属中の脱酸成分が不足することは既に述べた。ＵＯＥ鋼管のシーム溶接のような多電極高速溶接の場合、アーク雰囲気の領域が大きいため大気が混入しやすく、凝固速度が速いためにガス成分の浮上時間が短く、さらには、脱酸成分が不足している溶接金属では過剰にガスが発生し、ポックマークが発生しやすくなる。このポックマークの発生を抑制するためにも、強脱酸成分であるＳｉ及びＡｌの添加は有効であり、高速溶接においても優れた内部品質が得られる。 On the other hand, it has already been described that the deoxidation component in the weld metal is insufficient in the conventional welding material as the carbon equivalent of the base metal is lowered. In the case of multi-electrode high-speed welding such as seam welding of UOE steel pipe, the atmosphere of the arc is large, so air is easily mixed in, the solidification rate is fast, and the rising time of the gas component is short. In the weld metal that is being used, excessive gas is generated, and a pock mark is likely to be generated. In order to suppress the generation of the pock mark, addition of Si and Al, which are strong deoxidizing components, is effective, and excellent internal quality can be obtained even in high-speed welding.
また、多電極高速溶接性に及ぼす電流比の影響は極めて大きい。電流比のバランスが悪いと、ビード形状及び内部品質にも大きく影響を及ぼす。また、電極によってワイヤが異なる場合、ワイヤの組合せが同じであっても、電流比が大きく異なれば、［Ｍ］の値も変化し、低温靭性及び高速溶接性に影響を及ぼす。そこで、本発明者等は、鋭意実験研究を行ない、優れた低温靭性と高速溶接性が得られる電流比範囲を見出した。 In addition, the influence of the current ratio on the multi-electrode high-speed weldability is extremely large. If the current ratio is poorly balanced, the bead shape and internal quality will be greatly affected. In addition, when the wire is different depending on the electrode, even if the combination of the wires is the same, if the current ratio is greatly different, the value of [M] also changes, which affects low-temperature toughness and high-speed weldability. Accordingly, the present inventors conducted extensive experimental research and found a current ratio range in which excellent low temperature toughness and high speed weldability can be obtained.
ＵＯＥ鋼管のストレートシーム溶接の場合、生産性向上の観点から一般的に多電極溶接を使用している。造管される鋼管は多種多様であり、１種類の溶接材料で全てをカバーすることは困難であるため、種々のワイヤの組合せで溶接されることが多い。本発明においては、組合せるワイヤの種類及び数には何ら制約がなく、いかなる組合せでも［Ｍ］の値が本発明の範囲内であれば同じ効果を得ることができる。また、実生産ではワイヤ交換に要する時間が生産性に大きく影響することから、１極のみワイヤ交換を行なうことであらゆる鋼管に対応できるシステムが望ましい。本発明を適用すれば、例えばＴ１乃至Ｔ３極を固定し、Ｌ極のみ交換することで所定のワイヤ成分系を得ることが可能であり、ワイヤ交換時間の短縮による生産性向上と、ワイヤ種類の削減によるコストダウンが可能となる。 In the case of straight seam welding of UOE steel pipe, multi-electrode welding is generally used from the viewpoint of improving productivity. There are many types of steel pipes to be formed, and it is difficult to cover all with one kind of welding material. In the present invention, there are no restrictions on the type and number of wires to be combined, and any combination can achieve the same effect as long as the value of [M] is within the scope of the present invention. Moreover, since the time required for wire replacement greatly affects productivity in actual production, it is desirable to have a system that can handle all types of steel pipes by performing wire replacement for only one pole. By applying the present invention, for example, it is possible to obtain a predetermined wire component system by fixing the T1 to T3 poles and exchanging only the L poles, improving productivity by shortening the wire exchange time, Cost reduction by reduction is possible.
次に、本発明における組成の数値限定理由について説明する。前述のとおり、ＵＯＥ鋼管のストレートシーム溶接の場合、生産性向上の観点から一般的に多電極溶接を使用している。本発明においては、１電極溶接の場合は高速溶接性が劣るため、２電極以上とした。一方、高速溶接化を図るためには、電極数の増加は有効であるが、電極数の増加に伴う設備費のアップに対して得られる高速化の効果を考慮し、４電極以下とした。 Next, the reason for limiting the numerical values of the composition in the present invention will be described. As described above, in the case of straight seam welding of UOE steel pipe, multi-electrode welding is generally used from the viewpoint of improving productivity. In the present invention, since the high-speed weldability is inferior in the case of one-electrode welding, two or more electrodes are used. On the other hand, an increase in the number of electrodes is effective for achieving high-speed welding, but the number of electrodes is set to 4 or less in consideration of the effect of high speed obtained for an increase in equipment cost accompanying an increase in the number of electrodes.
［Ｃ］：０．０７乃至０．２０質量％
Ｃは炭素当量式の基本成分であり、溶接金属部の強度及び靭性に大きく影響を与える。［Ｃ］が０．０７質量％未満であると、溶接金属部のミクロ組織が粗大となり、靭性が劣化する。一方、［Ｃ］が多すぎると、強度が高くなり過ぎ、靭性が劣化するうえ、高温割れが発生する虞があるため、０．２０質量％以下とする。
[C]: 0.07 to 0.20 mass%
C is a basic component of the carbon equivalent formula and greatly affects the strength and toughness of the weld metal part. When [C] is less than 0.07% by mass, the microstructure of the weld metal part becomes coarse and the toughness deteriorates. On the other hand, if the amount of [C] is too large, the strength becomes too high, the toughness deteriorates, and hot cracking may occur.
［Ｍｎ］：１．４５乃至２．７０質量％
Ｍｎは溶融金属中の酸素と結合して、これを除去する作用を有し、優れた靭性及び強度を得るのに必要な成分である。［Ｍｎ］が１．４５質量％未満であると、靭性は劣化する。一方、［Ｍｎ］が２．７０質量％を超えると、過度な焼入れ組織となり、靭性が劣化する。
[Mn]: 1.45 to 2.70 mass%
Mn combines with oxygen in the molten metal to remove it, and is a component necessary for obtaining excellent toughness and strength. If [Mn] is less than 1.45% by mass, the toughness deteriorates. On the other hand, when [Mn] exceeds 2.70% by mass, an excessively quenched structure is formed and the toughness is deteriorated.
［Ｓｉ］：０．１０乃至０．７０質量％
Ｓｉは脱酸成分として効果があり、その作用力も高い。母材の低炭素当量化に伴い、脱酸成分が不足し、溶接金属部の酸素量は高くなる傾向にあり、衝撃値も低値を示す。Ｓｉを添加することにより、低炭素当量の母材においても、脱酸成分が不足することなく、溶接金属部の酸素量が抑制されて、靭性が確保される。［Ｓｉ］が０．１０質量％未満であると、脱酸不足となり、靭性が劣化するうえ、ポックマークが発生する。一方、［Ｓｉ］が０．７０質量％を超えると、溶接金属中にＳｉの酸化物が過剰に残留し、靭性が劣化する。
[Si]: 0.10 to 0.70 mass%
Si is effective as a deoxidizing component, and its working force is also high. Along with the lower carbon equivalent of the base material, the deoxidizing component is insufficient, the oxygen content of the weld metal part tends to be high, and the impact value is also low. By adding Si, even in a base material having a low carbon equivalent, the amount of oxygen in the weld metal part is suppressed and toughness is ensured without the deoxidation component being insufficient. When [Si] is less than 0.10% by mass, deoxidation is insufficient, toughness is deteriorated, and a pock mark is generated. On the other hand, if [Si] exceeds 0.70% by mass, an excessive amount of Si oxide remains in the weld metal and the toughness deteriorates.
［Ｔｉ］：０．１０乃至０．３０質量％
Ｔｉも非常に強い脱酸作用を示す。その酸化物は溶接金属中に微細分散し、ミクロ組織を微細化するため靭性を向上させる。［Ｔｉ］が０．１０質量％未満であると、その効果が得られず、靭性が劣化する。また、両面一層溶接のように、２番目に溶接する側の溶接熱により、最初に溶接する側の溶接金属が熱影響を受ける場合、熱影響部は析出硬化し、衝撃性能が劣化する虞がある。［Ｔｉ］が０．３０質量％を超えると、前述のとおり、最初に溶接する側の熱影響部が析出硬化し、靭性が劣化する。
[Ti]: 0.10 to 0.30 mass%
Ti also exhibits a very strong deoxidizing action. The oxide is finely dispersed in the weld metal and refines the microstructure to improve toughness. If [Ti] is less than 0.10% by mass, the effect cannot be obtained and the toughness deteriorates. In addition, as in the case of double-sided single-layer welding, when the weld metal on the first welding side is thermally affected by the welding heat on the second welding side, the heat-affected zone may precipitate and harden and impact performance may deteriorate. is there. When [Ti] exceeds 0.30% by mass, as described above, the heat-affected zone on the side to be welded first is precipitated and hardened, and the toughness deteriorates.
［Ａｌ］：０．００３乃至０．０３０質量％
Ａｌも極めて強い脱酸作用を示し、溶接金属酸素量の低減により、靭性を向上させる。しかし、酸素との親和力はＴｉよりも大きく、適正量を超えると、Ｔｉ酸化物の生成が抑制されて靭性が劣化する。即ち、靭性確保のためには、Ｔｉ酸化物の微細分散による組織の微細化を妨げないようなＡｌの微量添加が最も有効である。［Ａｌ］が０．００３質量％未満であると、脱酸不足になり、靭性が劣化するうえ、ポックマークが発生する。［Ａｌ］が０．０３０質量％を超えると、Ｔｉ酸化物の生成が抑制され、組織が粗大化して靭性が劣化する。
[Al]: 0.003 to 0.030 mass%
Al also exhibits a very strong deoxidation action and improves toughness by reducing the amount of weld metal oxygen. However, the affinity with oxygen is greater than that of Ti, and if it exceeds an appropriate amount, the formation of Ti oxide is suppressed and the toughness deteriorates. That is, in order to ensure toughness, it is most effective to add a small amount of Al that does not hinder the refinement of the structure due to the fine dispersion of Ti oxide. When [Al] is less than 0.003 mass%, deoxidation is insufficient, toughness is deteriorated, and a pock mark is generated. When [Al] exceeds 0.030% by mass, the generation of Ti oxide is suppressed, the structure becomes coarse and the toughness deteriorates.
［Ｐ］：≦０．０２０質量％、［Ｓ］：≦０．０２０質量％
Ｐ及びＳは、高温割れ、靭性又は曲げ性能等、溶接金属部の品質に悪影響を及ぼすので、［Ｐ］及び［Ｓ］は０．０２０質量％以下に規制する。
[P]: ≦ 0.020 mass%, [S]: ≦ 0.020 mass%
Since P and S adversely affect the quality of the weld metal part such as hot cracking, toughness or bending performance, [P] and [S] are regulated to 0.020% by mass or less.
［Ｖ］：≦０．０２０質量％
Ｖは２番目に溶接する側の溶接により、最初に溶接する側の熱影響部が硬化し、靭性を劣化させる傾向がある。従って、［Ｖ］は０．０２０質量％以下に規制する。
[V]: ≦ 0.020 mass%
V tends to harden the heat-affected zone on the side to be welded first and deteriorate toughness by welding on the side to be welded second. Therefore, [V] is regulated to 0.020 mass% or less.
［Ｃｕ］：≦０．７０質量％
［Ｃｕ］が０．７０質量％以下であれば、靭性に影響を及ぼさない。また、Ｃｕは高温割れに悪影響を及ぼす成分であり、低く抑えるのが望ましい。［Ｃｕ］が０．７０質量％を超えると、高温割れが発生しやすくなる。
[Cu]: ≦ 0.70 mass%
If [Cu] is 0.70 mass% or less, the toughness is not affected. Further, Cu is a component that adversely affects hot cracking, and is desirably kept low. When [Cu] exceeds 0.70% by mass, hot cracking tends to occur.
［Ｂ］：≦０．０２０質量％
Ｂは２番目に溶接する側の溶接熱により、最初に溶接する側の熱影響部が硬化し、靭性を著しく劣化させる。従って、［Ｂ］は０．０２０質量％以下に規制する。
[B]: ≦ 0.020 mass%
In B, the heat-affected zone on the first welding side is hardened by the welding heat on the second welding side, and the toughness is remarkably deteriorated. Therefore, [B] is regulated to 0.020 mass% or less.
［Ｏ］：≦０．０１０質量％
Ｏは溶接金属の靭性に悪影響を及ぼす成分であり、このため、［Ｏ］は０．０１０質量％以下に規制する。
[O]: ≦ 0.010 mass%
O is a component that adversely affects the toughness of the weld metal. For this reason, [O] is regulated to 0.010% by mass or less.
［Ｎ］：≦０．００８質量％
Ｎは溶接金属の靭性に悪影響を及ぼす成分であり、このため、［Ｎ］は０．００８質量％以下に規制する。
[N]: ≦ 0.008 mass%
N is a component that adversely affects the toughness of the weld metal. For this reason, [N] is regulated to 0.008% by mass or less.
［Ｍｏ］：≦１．０質量％
Ｍｏは強度を高める効果が大きいうえ、２番目に溶接する側の溶接熱により最初に溶接する側の熱影響部が硬化し、靭性を劣化させる虞があるため、［Ｍｏ］は必要最低限にとどめる必要がある。従って［Ｍｏ］は１．０質量％以下に規制する。
[Mo]: ≦ 1.0% by mass
Mo has a great effect of increasing strength, and the heat-affected zone on the first welding side is hardened by the welding heat on the second welding side, which may deteriorate toughness. It is necessary to stay. Therefore, [Mo] is regulated to 1.0% by mass or less.
［Ｎｉ］、［Ｃｒ］、［Ｍｏ］の合計量：≦２．０質量％
Ｍｏ同様、Ｎｉ及びＣｒは強度を高める効果が大きく、これらを過度に添加すると、強度が高くなり過ぎ、靭性を劣化させる虞がある。従って、［Ｎｉ］、［Ｃｒ］及び［Ｍｏ］の合計量は２．０質量％以下に規制する必要がある。
Total amount of [Ni], [Cr] and [Mo]: ≦ 2.0% by mass
Like Mo, Ni and Cr have a large effect of increasing the strength. If these are added excessively, the strength becomes too high and the toughness may be deteriorated. Therefore, the total amount of [Ni], [Cr] and [Mo] needs to be regulated to 2.0% by mass or less.
次に、溶接電流比の規制理由について説明する。多電極サブマージアーク溶接において、ビード形状及び溶接金属部の内部品質を考慮した場合に、溶接電流比が本発明の電流比範囲外で溶接を行うと、溶込み不良、余盛過大、スラグ巻込み又はオーバーラップが発生する虞がある。 Next, the reason for regulating the welding current ratio will be described. In multi-electrode submerged arc welding, when considering the bead shape and the internal quality of the weld metal part, if welding is performed with a welding current ratio outside the current ratio range of the present invention, poor penetration, excessive surplus, slag entrainment Or there is a possibility that overlap occurs.
ＩＴ１／ＩＬ：０．６０乃至０．９０
第１及び第２電極の電流は溶込みに大きく影響を及ぼす。ＩＴ１／ＩＬの電流比が０．６０未満であると、溶込みが不足する。ＩＴ１／ＩＬの電流比が０．９０を超えると、溶け込みは深くなるものの、ビード幅が狭くなりやすく、余盛過大となる。
I T1 / I L : 0.60 to 0.90
The currents of the first and second electrodes greatly affect the penetration. When the current ratio of I T1 / I L is less than 0.60, insufficient penetration. When the current ratio of I T1 / I L exceeds 0.90, penetration although deeper, bead width tends narrowed, the excess metal excessively.
ＩＴ２／ＩＬ：０．５０乃至０．８０又はＩＴ３／ＩＬ：０．５０乃至０．８０
第３及び第４電極の電流は、溶込みよりも、ビード幅に大きく影響を及ぼす。ＩＴ２／ＩＬ又はＩＴ３／ＩＬの電流比が０．５０未満であると、溶融池が十分に撹拌されず、スラグ巻き込みが発生する。ＩＴ２／ＩＬ又はＩＴ３／ＩＬの電流比が０．８０を超えると、溶融金属量が過大となり、ビードが広がりすぎてオーバーラップとなる。
I T2 / I L : 0.50 to 0.80 or I T3 / I L : 0.50 to 0.80
The currents of the third and fourth electrodes have a greater influence on the bead width than the penetration. When the current ratio of I T2 / I L or I T3 / I L is less than 0.50, the melt pool is not stirred sufficiently, slag inclusion occurs. When the current ratio of I T2 / I L or I T3 / I L exceeds 0.80, the amount of the molten metal becomes excessive, the overlap with the bead too wide.
以下、本発明の範囲に入る実施例の効果について、本発明の範囲から外れる比較例と比較して説明する。供試鋼板の化学成分組成を下記表１に示す。この供試鋼板を、下記表２に示す組成のフラックスと、表６及び表７に示す種々のワイヤを使用して両面一層溶接を行った。表３及び図１は、４電極の場合の溶接条件、電極配置及び開先形状を示し、表４及び図２は、３電極の場合の溶接条件及び電極配置を示し、表５及び図３は、２電極の場合の溶接条件及び電極配置を示す。 Hereinafter, the effects of the examples that fall within the scope of the present invention will be described in comparison with comparative examples that deviate from the scope of the present invention. The chemical composition of the test steel sheet is shown in Table 1 below. This test steel plate was subjected to double-sided single layer welding using a flux having the composition shown in Table 2 below and various wires shown in Tables 6 and 7. Table 3 and FIG. 1 show the welding conditions, electrode arrangement, and groove shape in the case of four electrodes, Tables 4 and 2 show the welding conditions and electrode arrangement in the case of three electrodes, and Tables 5 and 3 The welding conditions and electrode arrangement in the case of two electrodes are shown.
表８乃至表１３は、本発明の実施例及び比較例の［Ｍ］の値を示す。図４は得られた溶接継手の形状を模式的に示す。この図４に示す位置より試験片を採取し、衝撃試験を実施した。この衝撃値を表９、表１１及び表１３に併せて示す。なお、衝撃値の判断基準として、−２０℃で評価し、３本の平均値が８０Ｊ以上を良好とした。 Table 8 thru | or Table 13 shows the value of [M] of the Example and comparative example of this invention. FIG. 4 schematically shows the shape of the obtained welded joint. A test piece was taken from the position shown in FIG. 4 and subjected to an impact test. The impact values are also shown in Table 9, Table 11, and Table 13. In addition, it evaluated at -20 degreeC as a judgment standard of an impact value, and the average value of three was set to 80J or more as favorable.
塩基度＝（ＣａＦ２＋ＣａＯ＋ＭｇＯ＋Ｎａ２Ｏ＋Ｋ２Ｏ＋ＭｎＯ／２＋ＦｅＯ／２）／（ＳｉＯ２＋Ａｌ２Ｏ３／２＋ＺｒＯ２／２＋ＴｉＯ２／２） Basicity = (CaF 2 + CaO + MgO + Na 2 O + K 2 O + MnO / 2 + FeO / 2) / (SiO 2 + Al 2 O 3/2 + ZrO 2/2 + TiO 2/2)
これらの表３乃至表５において、最初に溶接する側（１ｓｔ側）の溶接ワイヤ径は４．０ｍｍである。また、２番目に溶接する側の仮付け溶接のワイヤ径は１．２ｍｍであり、ワイヤ種類はＪＩＳ Ｚ３３１２ ＹＧＷ１１である。この２番目に溶接する側の仮付け溶接の溶接条件は２６０Ａ−３２Ｖ−５０ｃｍ／分、シールドガスはＣＯ２である。 In Tables 3 to 5, the welding wire diameter on the first welding side (1st side) is 4.0 mm. The wire diameter of the tack welding on the second welding side is 1.2 mm, and the wire type is JIS Z3312 YGW11. Welding conditions for tack welding the side to be welded to the second is 260A-32V-50cm / min, shield gas is CO 2.
表８乃至表１１中の実施例１乃至４０では衝撃値は８０Ｊ以上であった。一方、比較例４１及び５９では、［Ｃ］が０．０７質量％未満であり、靭性が劣化した。比較例Ｎｏ．４２では［Ｃ］が０．２０質量％を超えており靭性が劣化するうえ、高温割れが発生した。比較例４３及び６１では、［Ｓｉ］が０．１０質量％未満であり、靭性が劣化するうえ、ポックマークが発生した。比較例４４では、［Ｓｉ］が０．７０質量％を超えており、靭性が劣化した。比較例４５及び６３では、［Ｍｎ］が１．４５質量％未満であり、靭性が劣化した。比較例４６では、［Ｍｎ］が２．７０質量％を超えており、靭性が劣化した。比較例４７では、［Ｃｕ］が０．７０質量％を超えており、高温割れが発生した。比較例４８及び６２では、［Ｔｉ］が０．１０質量％未満であり靭性が劣化した。比較例４９では、［Ｔｉ］が０．３０質量％を超えており、靭性が劣化した。比較例５０では、［Ｖ］が０．０２０質量％を超えており、靭性が劣化した。比較例５１では、［Ａｌ］が０．００３質量％未満であり、靭性が劣化するうえ、ポックマークが発生した。比較例５２では、［Ａｌ］が０．０３０質量％を超えており、靭性が劣化した。比較例５３では、［Ｂ］が０．０２０質量％を超えており、靭性が劣化した。比較例５４では、［Ｏ］が０．０１０質量％を超えており、靭性が劣化した。比較例５５では、［Ｎ］が０．００８質量％を超えており、靭性が劣化した。比較例５６、５７及び６０では、［Ｎｉ］、［Ｃｒ］及び［Ｍｏ］の合計量が２．０質量％を超えており、靭性が劣化した。比較例５８では、［Ｍｏ］が１．０質量％を超えており、靭性が劣化した。なお、実施例１９乃至３８に示すとおり、複数種類のワイヤを用いても［Ｍ］が本発明の範囲内であれば、衝撃値は良好な値を示す。 In Examples 1 to 40 in Tables 8 to 11, the impact value was 80 J or more. On the other hand, in Comparative Examples 41 and 59, [C] was less than 0.07% by mass, and toughness deteriorated. Comparative Example No. In No. 42, [C] exceeded 0.20% by mass, and the toughness deteriorated and hot cracking occurred. In Comparative Examples 43 and 61, [Si] was less than 0.10% by mass, toughness was deteriorated, and a pock mark was generated. In Comparative Example 44, [Si] exceeded 0.70 mass%, and the toughness was deteriorated. In Comparative Examples 45 and 63, [Mn] was less than 1.45% by mass, and toughness deteriorated. In Comparative Example 46, [Mn] exceeded 2.70 mass%, and toughness deteriorated. In Comparative Example 47, [Cu] exceeded 0.70% by mass, and hot cracking occurred. In Comparative Examples 48 and 62, [Ti] was less than 0.10% by mass and the toughness deteriorated. In Comparative Example 49, [Ti] exceeded 0.30 mass%, and the toughness was deteriorated. In Comparative Example 50, [V] exceeded 0.020 mass%, and the toughness deteriorated. In Comparative Example 51, [Al] was less than 0.003% by mass, toughness was deteriorated, and pock marks were generated. In Comparative Example 52, [Al] exceeded 0.030 mass%, and the toughness deteriorated. In comparative example 53, [B] exceeded 0.020 mass%, and toughness deteriorated. In Comparative Example 54, [O] exceeded 0.010 mass%, and the toughness deteriorated. In comparative example 55, [N] exceeded 0.008 mass% and toughness deteriorated. In Comparative Examples 56, 57, and 60, the total amount of [Ni], [Cr], and [Mo] exceeded 2.0 mass%, and the toughness deteriorated. In comparative example 58, [Mo] exceeded 1.0 mass% and toughness deteriorated. As shown in Examples 19 to 38, even if a plurality of types of wires are used, the impact value is a good value as long as [M] is within the range of the present invention.
次に、溶接作業性を評価した。ワイヤはＷ１を用い、表３乃至表５に示す溶接条件において、２ｎｄ側（２番目に溶接される側）の溶接を下記表１４及び表１５に示すように変化させて溶接作業性を確認した。１ｓｔ側（最初に溶接する側）の溶接は、表３乃至表５に示すとおりである。なお、溶接作業性の評価は試験片長さ１５００ｍｍを溶接し、中央部７５０ｍｍ長さで評価した。溶接作業性は、余盛高さが３ｍｍ以下の場合を○、３ｍｍを超える場合を×とした。オーバーラップは２ｍｍ以下の場合を○、２ｍｍを超える場合を×とした。溶け込み不良は１ｓｔ側と２ｎｄ側の溶接金属が重なっているものを○、ルート部が溶け残っているものを×とした。これらの全ての評価項目が○の場合を溶接作業性が○、いずれかが×の場合を溶接作業性が×であるとした。図５は、余盛高さ、オーバーラップ及び溶け込み不良を示す。表１４中のテストＮｏ．Ｙ１乃至Ｎｏ．Ｙ４が本発明実施例で、表１５中のテストＮｏ．Ｙ５乃至Ｎｏ．Ｙ１０が比較例である。本発明実施例テストＮｏ．Ｙ１乃至Ｎｏ．Ｙ４では溶接作業性は良好で、衝撃値も８０Ｊ以上であった。テストＮｏ．Ｙ５では第２電極の電流比が０．６０未満であり、溶込み不良が発生した。テストＮｏ．Ｙ６では第２電極の電流比が０．９０を超えており、余盛過大となった。テストＮｏ．Ｙ７では第３電極の電流比が０．５０未満でありスラグ巻き込みが発生した。テストＮｏ．Ｙ８では第３電極の電流比が０．８０を超えており、オーバーラップとなった。テストＮｏ．Ｙ９では第４電極の電流比が０．５０未満であり、スラグ巻き込みが発生した。テストＮｏ．Ｙ１０では第４電極の電流比が０．８０を超えており、オーバーラップとなった。 Next, welding workability was evaluated. The wire was W1, and welding workability was confirmed by changing the welding on the 2nd side (the second welded side) as shown in Table 14 and Table 15 below under the welding conditions shown in Tables 3 to 5. . The welding on the first side (the side to be welded first) is as shown in Tables 3 to 5. The weld workability was evaluated by welding a test piece length of 1500 mm and a length of 750 mm at the center. As for the welding workability, the case where the extra height was 3 mm or less was evaluated as ◯, and the case where the height exceeded 3 mm was evaluated as x. The overlap was evaluated as ◯ when the length was 2 mm or less, and x when the length exceeded 2 mm. For the poor penetration, the case where the weld metal on the 1st side and the 2nd side overlapped was marked with ○, and the case where the root portion remained undissolved was marked with ×. When all these evaluation items were ○, the welding workability was ○, and when either one was ×, the welding workability was ×. FIG. 5 shows extra height, overlap and poor penetration. Test No. in Table 14 Y1-No. Y4 is an example of the present invention. Y5 to No. Y10 is a comparative example. Inventive Example Test No. Y1-No. In Y4, the welding workability was good, and the impact value was 80 J or more. Test No. In Y5, the current ratio of the second electrode was less than 0.60, and poor penetration occurred. Test No. In Y6, the current ratio of the second electrode exceeded 0.90, which was excessive. Test No. In Y7, the current ratio of the third electrode was less than 0.50, and slag entrainment occurred. Test No. In Y8, the current ratio of the third electrode exceeded 0.80 and overlapped. Test No. In Y9, the current ratio of the fourth electrode was less than 0.50, and slag entrainment occurred. Test No. In Y10, the current ratio of the fourth electrode exceeded 0.80 and overlapped.
Claims (3)
［Ｃ］：０．０７乃至０．２０質量％
［Ｍｎ］：１．４５乃至２．７０質量％
［Ｓｉ］：０．１０乃至０．７０質量％
［Ｔｉ］：０．１０乃至０．３０質量％
［Ａｌ］：０．００３乃至０．０３０質量％
［Ｐ］：≦０．０２０質量％
［Ｓ］：≦０．０２０質量％
［Ｖ］：≦０．０２０質量％
［Ｃｕ］：≦０．７０質量％
［Ｂ］：≦０．０２０質量％
［Ｏ］：≦０．０１０質量％
［Ｎ］：≦０．００８質量％
［Ｍｏ］：≦１．０質量％
［Ｎｉ］、［Ｃｒ］、［Ｍｏ］の合計量：２．０質量％以下
であり、
上記各元素の他は、Ｆｅ及び不可避不純物である組成の溶接ワイヤを使用し、
ＩＬを第１電極ワイヤの溶接電流（Ａ）、ＩＴ１を第２電極ワイヤの溶接電流（Ａ）、ＩＴ２を第３電極ワイヤの溶接電流（Ａ）、ＩＴ３を第４電極ワイヤの溶接電流（Ａ）とした場合に、溶接電流比を、ＩＴ１／ＩＬ：０．６０乃至０．９０、ＩＴ２／ＩＬ：０．５０乃至０．８０、ＩＴ３／ＩＬ：０．５０乃至０．８０としてサブマージアーク溶接することを特徴とするサブマージアーク溶接方法。
［Ｍ］＝（［Ｍ］ＡＬ＋（ＩＴ１／ＩＬ）×［Ｍ］ＡＴ１＋（ＩＴ２／ＩＬ）×［Ｍ］ＡＴ２＋（ＩＴ３／ＩＬ）×［Ｍ］ＡＴ３）／（１＋（ＩＴ１／ＩＬ）＋（ＩＴ２／ＩＬ）＋（ＩＴ３／ＩＬ））
［Ｍ］ＡＬ：第１電極ワイヤ中のＭ元素の質量（％）
［Ｍ］ＡＴ１：第２電極ワイヤ中のＭ元素の質量（％）
［Ｍ］ＡＴ２：第３電極ワイヤ中のＭ元素の質量（％）
［Ｍ］ＡＴ３：第４電極ワイヤ中のＭ元素の質量（％） In the four-electrode submerged arc welding method, the element type is M, and [M] is a value calculated by the following formula using the element M included in the welding wires of the first electrode to the fourth electrode.
[C]: 0.07 to 0.20 mass%
[Mn]: 1.45 to 2.70 mass%
[Si]: 0.10 to 0.70 mass%
[Ti]: 0.10 to 0.30 mass%
[Al]: 0.003 to 0.030 mass%
[P]: ≦ 0.020 mass%
[S]: ≦ 0.020 mass%
[V]: ≦ 0.020 mass%
[Cu]: ≦ 0.70 mass%
[B]: ≦ 0.020 mass%
[O]: ≦ 0.010 mass%
[N]: ≦ 0.008 mass%
[Mo]: ≦ 1.0% by mass
[Ni], [Cr], [Mo] total amount: 2.0 mass% or less,
In addition to the above elements, use a welding wire having a composition that is Fe and inevitable impurities,
Welding current of the first electrode wire and I L (A), the welding current of the second electrode wires I T1 (A), the welding current of the third electrode wires I T2 (A), the I T3 of the fourth electrode wire when the welding current (a), the welding current ratio, I T1 / I L: 0.60 to 0.90, I T2 / I L: 0.50 to 0.80, I T3 / I L: 0 Submerged arc welding method, characterized in that submerged arc welding is performed at 50 to 0.80.
[M] = ([M] AL + (I T1 / I L) × [M] AT1 + (I T2 / I L) × [M] AT2 + (I T3 / I L) × [M] AT3) / (1+ (I T1 / I L ) + (I T2 / I L ) + (I T3 / I L ))
[M] AL : Mass of element M in the first electrode wire (%)
[M] AT1 : Mass of element M in the second electrode wire (%)
[M] AT2 : Mass of element M in the third electrode wire (%)
[M] AT3 : Mass of element M in the fourth electrode wire (%)
［Ｃ］：０．０７乃至０．２０質量％
［Ｍｎ］：１．４５乃至２．７０質量％
［Ｓｉ］：０．１０乃至０．７０質量％
［Ｔｉ］：０．１０乃至０．３０質量％
［Ａｌ］：０．００３乃至０．０３０質量％
［Ｐ］：≦０．０２０質量％
［Ｓ］：≦０．０２０質量％
［Ｖ］：≦０．０２０質量％
［Ｃｕ］：≦０．７０質量％
［Ｂ］：≦０．０２０質量％
［Ｏ］：≦０．０１０質量％
［Ｎ］：≦０．００８質量％
［Ｍｏ］：≦１．０質量％
［Ｎｉ］、［Ｃｒ］、［Ｍｏ］の合計量：２．０質量％以下
であり、
上記各元素の他は、Ｆｅ及び不可避不純物である組成の溶接ワイヤを使用し、
ＩＬを第１電極ワイヤの溶接電流（Ａ）、ＩＴ１を第２電極ワイヤの溶接電流（Ａ）、ＩＴ２を第３電極ワイヤの溶接電流（Ａ）とした場合に、溶接電流比を、ＩＴ１／ＩＬ：０．６０乃至０．９０、ＩＴ２／ＩＬ：０．５０乃至０．８０としてサブマージアーク溶接することを特徴とするサブマージアーク溶接方法。
［Ｍ］＝（［Ｍ］ＡＬ＋（ＩＴ１／ＩＬ）×［Ｍ］ＡＴ１＋（ＩＴ２／ＩＬ）×［Ｍ］ＡＴ２）／（１＋（ＩＴ１／ＩＬ）＋（ＩＴ２／ＩＬ））
［Ｍ］ＡＬ：第１電極ワイヤ中のＭ元素の質量（％）
［Ｍ］ＡＴ１：第２電極ワイヤ中のＭ元素の質量（％）
［Ｍ］ＡＴ２：第３電極ワイヤ中のＭ元素の質量（％） In the three-electrode submerged arc welding method, the element type is M, and [M] is a value calculated by the following formula using the element M included in the welding wires of the first electrode to the third electrode,
[C]: 0.07 to 0.20 mass%
[Mn]: 1.45 to 2.70 mass%
[Si]: 0.10 to 0.70 mass%
[Ti]: 0.10 to 0.30 mass%
[Al]: 0.003 to 0.030 mass%
[P]: ≦ 0.020 mass%
[S]: ≦ 0.020 mass%
[V]: ≦ 0.020 mass%
[Cu]: ≦ 0.70 mass%
[B]: ≦ 0.020 mass%
[O]: ≦ 0.010 mass%
[N]: ≦ 0.008 mass%
[Mo]: ≦ 1.0% by mass
[Ni], [Cr], [Mo] total amount: 2.0 mass% or less,
In addition to the above elements, use a welding wire having a composition that is Fe and inevitable impurities,
Welding current of the first electrode wire and I L (A), the welding current of the second electrode wires I T1 (A), when the welding current of the third electrode wires I T2 (A), the welding current ratio , I T1 / I L : 0.60 to 0.90, I T2 / I L : 0.50 to 0.80, submerged arc welding,
[M] = ([M] AL + (I T1 / I L) × [M] AT1 + (I T2 / I L) × [M] AT2) / (1+ (I T1 / I L) + (I T2 / I L ))
[M] AL : Mass of element M in the first electrode wire (%)
[M] AT1 : Mass of element M in the second electrode wire (%)
[M] AT2 : Mass of element M in third electrode wire (%)
［Ｃ］：０．０７乃至０．２０質量％
［Ｍｎ］：１．４５乃至２．７０質量％
［Ｓｉ］：０．１０乃至０．７０質量％
［Ｔｉ］：０．１０乃至０．３０質量％
［Ａｌ］：０．００３乃至０．０３０質量％
［Ｐ］：≦０．０２０質量％
［Ｓ］：≦０．０２０質量％
［Ｖ］：≦０．０２０質量％
［Ｃｕ］：≦０．７０質量％
［Ｂ］：≦０．０２０質量％
［Ｏ］：≦０．０１０質量％
［Ｎ］：≦０．００８質量％
［Ｍｏ］：≦１．０質量％
［Ｎｉ］、［Ｃｒ］、［Ｍｏ］の合計量：２．０質量％以下
であり、
上記各元素の他は、Ｆｅ及び不可避不純物である組成の溶接ワイヤを使用し、
ＩＬを第１電極ワイヤの溶接電流（Ａ）、ＩＴ１を第２電極ワイヤの溶接電流（Ａ）とした場合に、溶接電流比を、ＩＴ１／ＩＬ：０．６０乃至０．９０としてサブマージアーク溶接することを特徴とするサブマージアーク溶接方法。
［Ｍ］＝（［Ｍ］ＡＬ＋（ＩＴ１／ＩＬ）×［Ｍ］ＡＴ１）／（１＋（ＩＴ１／ＩＬ））
［Ｍ］ＡＬ：第１電極ワイヤ中のＭ元素の質量（％）
［Ｍ］ＡＴ１：第２電極ワイヤ中のＭ元素の質量（％）
In the two-electrode submerged arc welding method, the element type is M, and [M] is a value calculated by the following formula using the element M included in the welding wires of the first electrode and the second electrode,
[C]: 0.07 to 0.20 mass%
[Mn]: 1.45 to 2.70 mass%
[Si]: 0.10 to 0.70 mass%
[Ti]: 0.10 to 0.30 mass%
[Al]: 0.003 to 0.030 mass%
[P]: ≦ 0.020 mass%
[S]: ≦ 0.020 mass%
[V]: ≦ 0.020 mass%
[Cu]: ≦ 0.70 mass%
[B]: ≦ 0.020 mass%
[O]: ≦ 0.010 mass%
[N]: ≦ 0.008 mass%
[Mo]: ≦ 1.0% by mass
[Ni], [Cr], [Mo] total amount: 2.0 mass% or less,
In addition to the above elements, use a welding wire having a composition that is Fe and inevitable impurities,
When I L is the welding current (A) of the first electrode wire and I T1 is the welding current (A) of the second electrode wire, the welding current ratio is I T1 / I L : 0.60 to 0.90 A submerged arc welding method characterized by submerged arc welding.
[M] = ([M] AL + (I T1 / I L) × [M] AT1) / (1+ (I T1 / I L))
[M] AL : Mass of element M in the first electrode wire (%)
[M] AT1 : Mass of element M in the second electrode wire (%)
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| JPH09225682A (en) * | 1996-02-22 | 1997-09-02 | Nippon Steel Corp | Submerged arc welding for fire resistant steel |
| JPH09308987A (en) * | 1996-05-17 | 1997-12-02 | Nippon Steel Corp | Submerged arc welding wire excellent in low temperature toughness |
| JP2003138340A (en) * | 2001-10-31 | 2003-05-14 | Nippon Steel Corp | Ultrahigh strength steel pipe with excellent toughness of weld zone, and its manufacturing method |
| JP2004337863A (en) * | 2003-05-13 | 2004-12-02 | Jfe Steel Kk | Wire for submerged arc welding of high-tensile steel |
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| JPH09225682A (en) * | 1996-02-22 | 1997-09-02 | Nippon Steel Corp | Submerged arc welding for fire resistant steel |
| JPH09308987A (en) * | 1996-05-17 | 1997-12-02 | Nippon Steel Corp | Submerged arc welding wire excellent in low temperature toughness |
| JP2003138340A (en) * | 2001-10-31 | 2003-05-14 | Nippon Steel Corp | Ultrahigh strength steel pipe with excellent toughness of weld zone, and its manufacturing method |
| JP2004337863A (en) * | 2003-05-13 | 2004-12-02 | Jfe Steel Kk | Wire for submerged arc welding of high-tensile steel |
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