JPH0890239A - Seam welding method of clad steel tube - Google Patents
Seam welding method of clad steel tubeInfo
- Publication number
- JPH0890239A JPH0890239A JP23291094A JP23291094A JPH0890239A JP H0890239 A JPH0890239 A JP H0890239A JP 23291094 A JP23291094 A JP 23291094A JP 23291094 A JP23291094 A JP 23291094A JP H0890239 A JPH0890239 A JP H0890239A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- welding
- clad
- surface side
- alloy
- 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.)
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- Arc Welding In General (AREA)
- Butt Welding And Welding Of Specific Article (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明はステンレス鋼またはニッ
ケル基合金などの高耐食材料の合わせ材と低合金鋼の母
材からなるクラッド鋼管（ＵＯＥ鋼管、ベンディングロ
ール鋼管など）の高品質・高能率なシーム溶接方法に関
するものである。BACKGROUND OF THE INVENTION The present invention relates to a clad steel pipe (UOE steel pipe, bending roll steel pipe, etc.) made of a base material of a low-alloy steel and a high corrosion-resistant material such as stainless steel or a nickel-based alloy. The present invention relates to a simple seam welding method.
【０００２】[0002]
【従来の技術】安全性、経済性の観点から腐食性物質
（Ｈ2 Ｓ，ＣＯ2 ，Ｃ１- ）を多く含有する原油・天然
ガス輸送ラインパイプに、ステンレス鋼、ニッケル基合
金を合わせ材とする高合金クラッド鋼管の需要がますま
す増加する傾向にある。従来、このような鋼管は圧延で
製造したクラッド鋼板を成形、シーム溶接後、鋼管全体
を再加熱・水冷（溶体化処理）することにより製造され
ていたが、この方法は極めて生産性が低かった。BACKGROUND ART Safety, economical point of view from corrosive substances (H 2 S, CO 2, C1 -) crude oil and natural gas transport line pipe containing a large amount of a stainless steel, material combined nickel-based alloy The demand for high alloy clad steel pipes is increasing more and more. Conventionally, such a steel pipe was manufactured by forming a clad steel plate manufactured by rolling, seam welding, and then reheating and water cooling (solution treatment) the entire steel pipe, but this method had extremely low productivity. .
【０００３】そこで最近、溶体化処理を省略し圧延まま
で良好な諸特性を達成できる技術（たとえば特開昭６０
−２１６９８４、６２−１６８９２、６３−１３０２８
３号公報）が発明され、クラッド鋼板の製造技術は飛躍
的に進歩した。しかし、これらの技術で達成できる合わ
せ材の耐食性、母材の低温靭性は必ずしも満足できるも
のではなかった。Therefore, recently, a technique capable of achieving various properties without rolling by solution heat treatment (for example, JP-A-60).
-216984, 62-16892, 63-13028
No. 3 gazette) was invented, and the manufacturing technique of clad steel plate has made a great progress. However, the corrosion resistance of the laminated material and the low temperature toughness of the base material which can be achieved by these techniques are not always satisfactory.
【０００４】一方、そのシーム溶接においては鋼管内側
の合わせ材の溶接法としてタングステン・イナートガス
（ＴＩＧ）溶接法（たとえば特開昭６０−１５４８７５
号公報）が多く適用されていたが、この溶接法は溶接速
度が極めて遅く、クラッド鋼管の安定大量生産の大きな
障害となっていた。本発明者らは、これらの問題を解決
するため、新しいクラッド鋼管の製造方法を発明した
（特開平３−８５５８５号公報）。しかし、これらの方
法も溶接金属の耐食性、健全性（耐高温割れ性）に問題
を有していた。On the other hand, in the seam welding, a tungsten-inert gas (TIG) welding method (for example, Japanese Patent Laid-Open No. 60-154875) is used as a welding method for a laminated material inside a steel pipe.
However, this welding method has a very slow welding speed, which has been a major obstacle to stable mass production of clad steel pipes. In order to solve these problems, the present inventors have invented a new method for producing a clad steel pipe (JP-A-3-85585). However, these methods also have problems in the corrosion resistance and the soundness (hot crack resistance) of the weld metal.
【０００５】[0005]
【発明が解決しようとする課題】本発明は鋼管の溶体化
処理なしで優れた合わせ材（溶接金属を含む）の耐食性
と母材の強度、低温靭性、を同時に達成できる大径クラ
ッド鋼管のシーム溶接技術を提供するものである。とく
に本発明では高能率のサブマージアーク溶接法がシーム
溶接に適用され、高品質（優れた諸特性と健全性）に加
えて高生産性であるという特徴を有する。SUMMARY OF THE INVENTION The present invention is a seam of a large-diameter clad steel pipe capable of simultaneously achieving excellent corrosion resistance of a laminated material (including weld metal), strength of a base metal, and low temperature toughness without solution treatment of a steel pipe. Welding technology is provided. In particular, in the present invention, the highly efficient submerged arc welding method is applied to seam welding, and is characterized by high productivity in addition to high quality (excellent characteristics and soundness).
【０００６】[0006]
【課題を解決するための手段】本発明の要旨は、ステン
レス鋼またはニッケル基合金の合わせ材とＣ含有量が
０．０６wt％以下の低合金鋼からなるクラッド鋼板を合
わせ材が鋼管内側になるように冷間成形後、内面側より
合わせ材部を高合金溶接材料を用いてサブマージアーク
溶接を行い、続いて外面側より低合金溶接材料を用いて
溶接金属成分がＣ：０．００５〜０．０３５wt％、Ｔ
ｉ：０．００５〜０．０２wt％、Ｂ：０．００１０wt％
以下、Ｏ：０．０１〜０．０８wt％を含有し、かつＰCM
＝Ｃ＋Ｓｉ／３０＋（Ｍｎ＋Ｃｕ＋Ｃｒ）／２０＋Ｖ／
１０＋Ｍｏ／１５＋Ｎｉ／６０＋５Ｂが０．１２〜０．
１８wt％となるようにサブマージアーク溶接することで
ある。SUMMARY OF THE INVENTION The gist of the present invention is to provide a clad steel plate made of a stainless steel or nickel-base alloy composite material and a low alloy steel having a C content of 0.06 wt% or less. As described above, after cold forming, the joining material portion is subjected to submerged arc welding from the inner surface side using the high alloy welding material, and subsequently, the weld metal component is C: 0.005 to 0 using the low alloy welding material from the outer surface side. 0.035 wt%, T
i: 0.005-0.02 wt%, B: 0.0010 wt%
Below, O: 0.01 to 0.08 wt% is contained, and P CM
= C + Si / 30 + (Mn + Cu + Cr) / 20 + V /
10 + Mo / 15 + Ni / 60 + 5B is 0.12 to 0.
It is to perform submerged arc welding so that it becomes 18 wt%.
【０００７】本発明のステンレス鋼とは、オーステナイ
ト系およびオーステナイト・フェライト２相系を意味
し、ニッケル基合金とはインコロイ８２５、インコネル
６２５などの耐食材料である。また母材は圧延方向と直
角方向において、強度がＸ５２以上（ＡＰＩ規格）、低
温靭性がシャルピー試験における−３０℃の吸収エネル
ギー≧１００Ｊ、破面遷移温度≦−４０℃となるような
高強度、高靭性の低合金鋼である。The stainless steel of the present invention means austenite and austenite-ferrite two-phase system, and nickel-based alloy is a corrosion resistant material such as Incoloy 825 and Inconel 625. Further, the base material has a strength of X52 or more (API standard) in the direction perpendicular to the rolling direction, a low temperature toughness, a high strength such that absorbed energy at -30 ° C in a Charpy test ≧ 100 J, fracture surface transition temperature ≦ -40 ° C, It is a high toughness low alloy steel.
【０００８】以下、本発明のクラッド鋼管のシーム溶接
方法について詳細に説明する。本発明では、クラッド鋼
板の合わせ材を内側にして鋼管成形を行い、内面側より
合わせ材部を高合金材料を用いてサブマージアーク溶接
を行い、続いて外面側より低合金溶接材料を用いてサブ
マージアーク溶接を実施する。クラッド鋼板は、たとえ
ば特願平６−０４０１５３号などで開示されたサンドイ
ッチスラブを組み立てて、熱間圧延により製造された鋼
板、あるいは爆着法で製造された鋼板、いずれのクラッ
ド鋼板も使用できる。The clad steel pipe seam welding method of the present invention will be described in detail below. In the present invention, steel pipe forming is performed with the cladding material of the clad steel plate inside, and the cladding material portion is subjected to submerged arc welding using the high alloy material from the inner surface side, and subsequently the submerged material is used from the outer surface side using the low alloy welding material Carry out arc welding. As the clad steel plate, for example, a clad steel plate manufactured by assembling a sandwich slab disclosed in Japanese Patent Application No. 6-040153, and manufactured by hot rolling, or a steel plate manufactured by an explosion bonding method can be used.
【０００９】本発明では、母材の強度・低温靭性の確保
および合わせ材の耐食性確保のため、母材のＣ量を０．
０６％以下に限定する。この上限の値は、母材の優れた
低温靭性、現地溶接性を得るための限界値である。母材
のＣ量が高過ぎるとスラブ再加熱時Ｃが極低Ｃの合わせ
材へ拡散し、耐食性を劣化させるので、合わせ材の耐食
性の観点からもＣ量の上限の値を０．０６％以下に制限
する必要がある。In the present invention, in order to secure the strength and low temperature toughness of the base material and the corrosion resistance of the laminated material, the C content of the base material is set to 0.
It is limited to 06% or less. This upper limit value is a limit value for obtaining excellent low temperature toughness and field weldability of the base material. If the C content of the base material is too high, C will diffuse into the extremely low C composite material when the slab is reheated, and the corrosion resistance will deteriorate. Therefore, from the viewpoint of the corrosion resistance of the composite material, the upper limit of the C content is 0.06%. Must be limited to:
【００１０】図１は本発明におけるシーム溶接法の例を
示したものである。ここで１は鋼管外側の低合金鋼母
材、２は鋼管内側の合わせ材（ステンレス鋼または高合
金）、３は鋼管内側の開先、４は鋼管外側の開先、５は
鋼管外側から溶接した仮付け溶接ビード、６は鋼管内側
のサブマージアーク溶接ビード（内面溶接金属）、７は
鋼管外側のサブマージアーク溶接ビード（外面溶接金
属）である。FIG. 1 shows an example of the seam welding method according to the present invention. Here, 1 is a low alloy steel base material outside the steel pipe, 2 is a laminated material (stainless steel or high alloy) inside the steel pipe, 3 is a groove inside the steel pipe, 4 is a groove outside the steel pipe, and 5 is welded from outside the steel pipe 6 is a submerged arc welding bead inside the steel pipe (inner surface weld metal), and 7 is a submerged arc welding bead outside the steel pipe (outer surface weld metal).
【００１１】図１において、まず低合金鋼母材の開先４
内に低合金鋼溶接ワイヤを使用して仮付け溶接を行う
（５）。この溶接法に関してはとくに限定しないが、通
常ＵＯＥ工場では炭酸ガスアーク溶接法が適用される。
仮付け溶接後、合わせ材側の開先３にサブマージアーク
溶接６を行い、内面溶接金属を形成する。ついで母材側
の開先４にサブマージアーク溶接を行い、外面溶接金属
７を形成する。鋼管内外面のサブマージアーク溶接にお
ける電極数については、とくに限定しないが、１〜３電
極が望ましい。In FIG. 1, first, a groove 4 of a low alloy steel base material
Temporary welding is performed using a low alloy steel welding wire inside (5). The welding method is not particularly limited, but the carbon dioxide arc welding method is usually applied in the UOE factory.
After the tack welding, submerged arc welding 6 is performed on the groove 3 on the side of the laminated material to form an inner surface weld metal. Then, submerged arc welding is performed on the groove 4 on the base metal side to form the outer surface weld metal 7. The number of electrodes in the submerged arc welding on the inner and outer surfaces of the steel pipe is not particularly limited, but 1 to 3 electrodes is preferable.
【００１２】上記の溶接において内面のサブマージアー
ク溶接は、溶接時の希釈を考慮し高合金材料を使用して
実施することにより、内面溶接金属において、優れた耐
食性が得られる。In the above welding, the submerged arc welding on the inner surface is performed by using a high alloy material in consideration of dilution during welding, whereby excellent corrosion resistance can be obtained in the inner surface weld metal.
【００１３】つぎに外面溶接金属においては低合金材料
を用いてサブマージアーク溶接し、溶接金属成分がＣ：
０．００５〜０．０３５wt％、Ｔｉ：０．００５〜０．
０２wt％、Ｂ：０．００１０wt％以下、Ｏ：０．０１〜
０．０８wt％を含有し、かつＰCM＝Ｃ＋Ｓｉ／３０＋
（Ｍｎ＋Ｃｕ＋Ｃｒ）／２０＋Ｖ／１０＋Ｍｏ／１５＋
Ｎｉ／６０＋５Ｂが０．１２〜０．１８wt％とする必要
がある。Next, for the outer surface weld metal, submerged arc welding is performed using a low alloy material, and the weld metal component is C:
0.005-0.035 wt%, Ti: 0.005-0.
02 wt%, B: 0.0010 wt% or less, O: 0.01 to
Contains 0.08 wt% and P CM = C + Si / 30 +
(Mn + Cu + Cr) / 20 + V / 10 + Mo / 15 +
Ni / 60 + 5B needs to be 0.12 to 0.18 wt%.
【００１４】溶接金属の低温靭性を確保するためには、
低Ｃ化と溶接金属組織の微細化が必要である。組織の微
細化を図るためには、（１）溶接金属のオーステナイト
（γ）粒界に生成する粒界フェライト（α）を抑制し、
（２）粒内変態フェライトを活用する必要がある。ま
ず、硬さの上昇を抑制して低温靭性を確保するためには
低Ｃ化が必須である。このためＣ量の上限を０．０３５
％とした。ただし、Ｃ量が低過ぎると強度不足となるた
め、その下限を０．００５％とした。In order to secure the low temperature toughness of the weld metal,
It is necessary to reduce the carbon content and refine the weld metal structure. In order to refine the structure, (1) suppressing grain boundary ferrite (α) generated at the austenite (γ) grain boundary of the weld metal,
(2) It is necessary to utilize the intragranular transformation ferrite. First, in order to suppress the increase in hardness and ensure the low temperature toughness, it is essential to reduce the carbon content. Therefore, the upper limit of the amount of C is 0.035.
%. However, if the C content is too low, the strength becomes insufficient, so the lower limit was made 0.005%.
【００１５】Ｂはγ−α変態時にγ粒界から生成する初
析フェライトの抑制に有効であるが、Ｂ量が多過ぎると
Ｆｅ23（ＣＢ）6 などの析出物が生成し、低温靭性が劣
化する。このためＢ量の上限を０．００１０％とした。
この時たとえＢ量が適正であっても、ＰCMを適正な範囲
に制御しないと良好な低温靭性は得られない。ＰCMが小
さ過ぎる場合には、鋼の焼入性が不足し、γ粒界から初
析フェライトが生成し、低温靭性が劣化する。このため
ＰCMの下限を０．１２％とした。また、ＰCMが高過ぎる
と鋼の焼入性が高くなり、硬さが上昇し低温靭性が劣化
する。このためＰCMの上限を０．１８％とした。B is effective in suppressing the pro-eutectoid ferrite generated from the γ grain boundary during the γ-α transformation, but if the B content is too large, precipitates such as Fe 23 (CB) 6 are generated, and the low temperature toughness is improved. to degrade. Therefore, the upper limit of the amount of B is set to 0.0010%.
At this time, even if the B content is appropriate, good low temperature toughness cannot be obtained unless P CM is controlled within an appropriate range. If P CM is too small, the hardenability of the steel becomes insufficient, pro-eutectoid ferrite is generated from the γ grain boundaries, and the low temperature toughness deteriorates. Therefore, the lower limit of P CM is set to 0.12%. On the other hand, if P CM is too high, the hardenability of steel becomes high, the hardness increases, and the low temperature toughness deteriorates. Therefore, the upper limit of P CM is set to 0.18%.
【００１６】Ｔｉ，Ｏはγ−α変態時にγ粒内から粒内
変態フェライトが生成する際の変態核（Ｔｉ2 Ｏ3 な
ど）を形成する。このような変態核（Ｔｉ2 Ｏ3 など）
を形成するためのＴｉおよびＯ量の必要最小量はそれぞ
れ、０．００５％、０．０１％である。しかしながらＴ
ｉ量が多過ぎると、ＴｉＣの析出などにより低温靭性が
劣化するため、その上限を０．０２％とした。またＯ量
が多過ぎると清浄度が劣化して低温靭性が劣化するため
に、その上限を０．０８％とした。Ti and O form transformation nuclei (such as Ti 2 O 3 ) when the intragranular transformation ferrite is formed from within the γ grains during the γ-α transformation. Such transformation nuclei (such as Ti 2 O 3 )
The required minimum amounts of Ti and O for forming a are 0.005% and 0.01%, respectively. However, T
If the amount of i is too large, the low temperature toughness deteriorates due to precipitation of TiC, etc., so the upper limit was made 0.02%. If the amount of O is too large, the cleanliness deteriorates and the low temperature toughness deteriorates, so the upper limit was made 0.08%.
【００１７】[0017]
【実施例】つぎに実施例について述べる。転炉−連続鋳
造法で種々の鋼成分の母材スラブ（厚み２４０mm）を製
造した。このスラブを所定の厚みに圧延した後、片表面
を機械加工、所定の厚みのＳＵＳ３１６Ｌまたはインコ
ロイ８２５合わせ材（圧延後のクラッド鋼板の合わせ材
厚みが３mmになるように調整）と重ね合わせて、四周を
真空引きを行いながらシール溶接した。さらに、このよ
うにして製造したスラブを分離材を介して２枚重ね合わ
せ、四周を溶接してサンドイッチスラブを組み立てた。
なお、低合金鋼と合わせ材の接着面はすべて機械加工で
平滑にし、洗浄・脱脂を行った。EXAMPLES Next, examples will be described. Base metal slabs (thickness: 240 mm) of various steel components were manufactured by a converter-continuous casting method. After rolling this slab to a predetermined thickness, one surface is machined and laminated with a predetermined thickness of SUS316L or Incoloy 825 laminated material (adjusted so that the laminated material thickness of the clad steel plate after rolling is 3 mm), Seal welding was performed while vacuuming the four laps. Further, two slabs manufactured in this way were overlapped with a separating material interposed therebetween, and four laps were welded to assemble a sandwich slab.
The low-alloy steel and the bonded material were all machined on a smooth surface and then washed and degreased.
【００１８】サンドイッチスラブを圧延してクラッド鋼
板を製造し、溶接材料を変えて外径５０８mmのＵＯＥ鋼
管およびベンディングロール鋼管を製造して、諸性質を
調査した。母材の機械的性質は圧延と直角な方向で、合
わせ材の耐食性は孔食試験（試験条件：１０％ＦｅＣｌ
3 ・６Ｈ2 Ｏ溶液に、ＳＵＳ３１６Ｌは１５℃で４８時
間、インコロイ８２５は３０℃で４８時間浸漬）で評価
した。The sandwich slab was rolled to produce a clad steel plate, the welding material was changed to produce a UOE steel pipe and a bending roll steel pipe having an outer diameter of 508 mm, and various properties were investigated. The mechanical properties of the base material are in the direction perpendicular to the rolling, and the corrosion resistance of the laminated material is the pitting corrosion test (test condition: 10% FeCl
To 3 · 6H 2 O solution, SUS316L 48 hours at 15 ° C., Incoloy 825 were evaluated at at 30 ° C. for 48 hours immersion).
【００１９】実施例を表１に示す。本発明にしたがって
製造したクラッド鋼管は低合金母材において優れた強度
・低温靭性を有し、かつ合わせ材において優れた耐食性
を有する。これに対して比較鋼は母材の化学成分または
外面溶接金属の化学成分が適切でなく、いずれかの特性
が劣る。Examples are shown in Table 1. The clad steel pipe manufactured according to the present invention has excellent strength and low temperature toughness in the low alloy base material and excellent corrosion resistance in the laminated material. On the other hand, the comparative steel is not suitable in the chemical composition of the base metal or the chemical composition of the outer surface weld metal, and either characteristic is inferior.
【００２０】鋼５は低合金鋼母材のＣ量が多過ぎるため
に、母材の低温靭性および合わせ材の耐食性が悪い。鋼
６は外面側溶接金属のＣ量が多過ぎるために、低温靭性
が劣る。鋼７は外面側溶接金属のＣ量が少な過ぎるため
に、強度が低下している。鋼８は外面側溶接金属のＴｉ
量が多過ぎるために、低温靭性が劣化する。鋼９は外面
側溶接金属のＴｉ量が少な過ぎるために、粒内フェライ
トの変態核となるＴｉ酸化物の生成量が少なく、低温靭
性が劣化する。鋼１０は外面側溶接金属のＢ量が多過ぎ
るために、Ｆｅ23（ＣＢ）6 析出物が生成し、低温靭性
が変化する。鋼１１は外面側溶接金属のＢ量が少な過ぎ
るために、粒界フェライトの生成が抑制されず、低温靭
性が劣化する。鋼１２は外面側溶接金属のＯ量が多過ぎ
るために、清浄度が悪く、低温靭性が劣化する。鋼１３
は外面側溶接金属のＯ量が少な過ぎるために、粒内フェ
ライトの変態核となるＴｉ酸化物の生成量が少なく、低
温靭性が劣化する。鋼１４は外面側溶接金属のＰCMが多
過ぎるために、硬さが上昇し、低温靭性が劣化する。鋼
１５は外面側溶接金属のＰCMが少な過ぎるために、粒界
フェライトの生成が抑制されず、低温靭性が劣化する。In Steel 5, the low alloy steel base material has too much C content, so that the low temperature toughness of the base material and the corrosion resistance of the laminated material are poor. Steel 6 is inferior in low temperature toughness because the C content of the weld metal on the outer surface side is too large. Steel 7 has reduced strength because the C content of the weld metal on the outer surface side is too small. Steel 8 is Ti of the outer side weld metal
Since the amount is too large, the low temperature toughness deteriorates. Since the amount of Ti in the weld metal on the outer surface side of steel 9 is too small, the amount of Ti oxide, which becomes the transformation nucleus of intragranular ferrite, is small, and the low temperature toughness deteriorates. Since the amount of B in the weld metal on the outer surface side of steel 10 is too large, Fe 23 (CB) 6 precipitates are formed and the low temperature toughness changes. Since the amount of B in the weld metal on the outer surface side of steel 11 is too small, the generation of grain boundary ferrite is not suppressed and the low temperature toughness deteriorates. Steel 12 has poor cleanliness and low-temperature toughness because the O content of the weld metal on the outer surface is too large. Steel 13
Since the amount of O in the weld metal on the outer surface side is too small, the amount of Ti oxide, which is a transformation nucleus of intragranular ferrite, is small and the low temperature toughness deteriorates. Since steel 14 has too much P CM of the weld metal on the outer surface side, hardness increases and low temperature toughness deteriorates. Steel 15 has too little P CM of the weld metal on the outer surface, so that the generation of grain boundary ferrite is not suppressed and the low temperature toughness deteriorates.
【００２１】[0021]
【表１】 [Table 1]
【００２２】[0022]
【表２】 [Table 2]
【００２３】[0023]
【表３】 [Table 3]
【００２４】[0024]
【発明の効果】本発明により高品質の大径クラッド鋼管
が製造できるようになった。その結果、省エネルギー・
省工程が可能になるとともに、諸特性の向上によりパイ
プラインの安全性が著しく向上した。According to the present invention, a high quality large diameter clad steel pipe can be manufactured. As a result, energy conservation
The process can be saved, and the safety of the pipeline has been significantly improved by improving various characteristics.
【図１】本発明にかかわるクラッド鋼管のシーム溶接部
の断面を示す図である。FIG. 1 is a view showing a cross section of a seam welded portion of a clad steel pipe according to the present invention.
【符号の説明】 １ 鋼管外側の低合金鋼母材 ２ 鋼管内側の合わせ材 ３ 合わせ材側の開先 ４ 低合金鋼母材側の開先 ５ 低合金鋼母材側の開先内の仮付け溶接ビード ６ 合わせ材側のサブマージアーク溶接ビード（内面溶
接金属） ７ 低合金母材側のサブマージアーク溶接ビード（外面
溶接金属）[Explanation of symbols] 1 Low alloy steel base metal outside the steel pipe 2 Laminated material inside the steel pipe 3 Groove on the side of the laminated material 4 Groove on the side of the low alloy steel base 5 Temporary inside the groove on the side of the low alloy steel base Attached welding bead 6 Submerged arc welding bead on the mating material side (inner surface weld metal) 7 Submerged arc welding bead on the low alloy base material side (outer surface weld metal)
Claims (1)
わせ材とＣ含有量が０．０６wt％以下の低合金鋼からな
るクラッド鋼板を合わせ材が鋼管内側になるように冷間
成形後、内面側より合わせ材部を高合金溶接材料を用い
てサブマージアーク溶接を行い、続いて外面側より低合
金溶接材料を用いて溶接金属成分がＣ：０．００５〜
０．０３５wt％、Ｔｉ：０．００５〜０．０２wt％、
Ｂ：０．００１０wt％以下、Ｏ：０．０１〜０．０８wt
％を含有し、かつＰCM＝Ｃ＋Ｓｉ／３０＋（Ｍｎ＋Ｃｕ
＋Ｃｒ）／２０＋Ｖ／１０＋Ｍｏ／１５＋Ｎｉ／６０＋
５Ｂが０．１２〜０．１８wt％となるようにサブマージ
アーク溶接することを特徴とするクラッド鋼管のシーム
溶接方法。1. A clad steel plate made of a stainless steel or nickel-base alloy composite material and a low alloy steel having a C content of 0.06 wt% or less is cold-formed so that the composite material is inside the steel pipe, and then from the inner surface side. Submerged arc welding is performed on the laminated material portion using a high alloy welding material, and subsequently, a weld metal component is C: 0.005 to 0.005 using a low alloy welding material from the outer surface side.
0.035 wt%, Ti: 0.005-0.02 wt%,
B: 0.0010 wt% or less, O: 0.01 to 0.08 wt
%, And P CM = C + Si / 30 + (Mn + Cu
+ Cr) / 20 + V / 10 + Mo / 15 + Ni / 60 +
A seam welding method for a clad steel pipe, which comprises performing submerged arc welding so that 5B is 0.12 to 0.18 wt%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP23291094A JPH0890239A (en) | 1994-09-28 | 1994-09-28 | Seam welding method of clad steel tube |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP23291094A JPH0890239A (en) | 1994-09-28 | 1994-09-28 | Seam welding method of clad steel tube |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0890239A true JPH0890239A (en) | 1996-04-09 |
Family
ID=16946761
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP23291094A Withdrawn JPH0890239A (en) | 1994-09-28 | 1994-09-28 | Seam welding method of clad steel tube |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0890239A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB2283827A (en) * | 1992-08-05 | 1995-05-17 | Hodogaya Chemical Co Ltd | Charge-control agent composition and toner containing this composition |
| WO2009003326A1 (en) * | 2007-06-29 | 2009-01-08 | Mengjie Yan | A process for continuous welding a composite pipe with outer stainless cladding layer |
| WO2009003325A1 (en) * | 2007-06-29 | 2009-01-08 | Mengjie Yan | A producing process for a spiral composite steel pipe |
| CN101817124A (en) * | 2009-02-27 | 2010-09-01 | 鞍钢股份有限公司 | High-toughness meal cored submerged arc welding wire and production method thereof |
-
1994
- 1994-09-28 JP JP23291094A patent/JPH0890239A/en not_active Withdrawn
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB2283827A (en) * | 1992-08-05 | 1995-05-17 | Hodogaya Chemical Co Ltd | Charge-control agent composition and toner containing this composition |
| GB2283827B (en) * | 1992-08-05 | 1996-07-17 | Hodogaya Chemical Co Ltd | Charge-control agent composition and toner containing this composition |
| WO2009003326A1 (en) * | 2007-06-29 | 2009-01-08 | Mengjie Yan | A process for continuous welding a composite pipe with outer stainless cladding layer |
| WO2009003325A1 (en) * | 2007-06-29 | 2009-01-08 | Mengjie Yan | A producing process for a spiral composite steel pipe |
| CN101817124A (en) * | 2009-02-27 | 2010-09-01 | 鞍钢股份有限公司 | High-toughness meal cored submerged arc welding wire and production method thereof |
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