JPS6310095A - Manufacture of high alloy clad steel pipe - Google Patents
Manufacture of high alloy clad steel pipeInfo
- Publication number
- JPS6310095A JPS6310095A JP15456686A JP15456686A JPS6310095A JP S6310095 A JPS6310095 A JP S6310095A JP 15456686 A JP15456686 A JP 15456686A JP 15456686 A JP15456686 A JP 15456686A JP S6310095 A JPS6310095 A JP S6310095A
- Authority
- JP
- Japan
- Prior art keywords
- welding
- carbon steel
- alloy
- wire
- high 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.)
- Pending
Links
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 91
- 239000000956 alloy Substances 0.000 title claims abstract description 91
- 229910000831 Steel Inorganic materials 0.000 title claims description 36
- 239000010959 steel Substances 0.000 title claims description 36
- 238000004519 manufacturing process Methods 0.000 title claims description 18
- 238000003466 welding Methods 0.000 claims abstract description 159
- 229910000975 Carbon steel Inorganic materials 0.000 claims abstract description 83
- 239000010962 carbon steel Substances 0.000 claims abstract description 83
- 238000000034 method Methods 0.000 claims description 55
- 230000004907 flux Effects 0.000 claims description 11
- 238000005253 cladding Methods 0.000 claims description 7
- 230000008569 process Effects 0.000 claims description 5
- 239000007787 solid Substances 0.000 claims description 3
- 239000000203 mixture Substances 0.000 abstract description 10
- 229910000851 Alloy steel Inorganic materials 0.000 abstract description 5
- 238000002844 melting Methods 0.000 abstract description 4
- 230000008018 melting Effects 0.000 abstract description 4
- 239000011324 bead Substances 0.000 description 11
- 229910052751 metal Inorganic materials 0.000 description 11
- 239000002184 metal Substances 0.000 description 11
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 10
- 229910052799 carbon Inorganic materials 0.000 description 10
- 230000035515 penetration Effects 0.000 description 9
- 238000010790 dilution Methods 0.000 description 6
- 239000012895 dilution Substances 0.000 description 6
- 230000000694 effects Effects 0.000 description 6
- 238000010586 diagram Methods 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 4
- 238000005275 alloying Methods 0.000 description 4
- 239000007789 gas Substances 0.000 description 4
- 239000002893 slag Substances 0.000 description 4
- 238000012733 comparative method Methods 0.000 description 3
- 239000010410 layer Substances 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 229910002065 alloy metal Inorganic materials 0.000 description 2
- 229910002092 carbon dioxide Inorganic materials 0.000 description 2
- 239000001569 carbon dioxide Substances 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000007865 diluting Methods 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- 238000002156 mixing Methods 0.000 description 2
- 239000002356 single layer Substances 0.000 description 2
- 239000010935 stainless steel Substances 0.000 description 2
- 102100028253 Breast cancer anti-estrogen resistance protein 3 Human genes 0.000 description 1
- 101000935648 Homo sapiens Breast cancer anti-estrogen resistance protein 3 Proteins 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 239000012141 concentrate Substances 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000002950 deficient Effects 0.000 description 1
- 238000012217 deletion Methods 0.000 description 1
- 230000037430 deletion Effects 0.000 description 1
- 230000003467 diminishing effect Effects 0.000 description 1
- 229910001039 duplex stainless steel Inorganic materials 0.000 description 1
- 239000002360 explosive Substances 0.000 description 1
- 210000004907 gland Anatomy 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
Landscapes
- Arc Welding In General (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明はＵＯＥ法によって高合金クラッド鋼管を製造す
る方法に関するものである。ここに、ＵＯＥ法とは、所
定の寸法に切断した鋼板を縁切断加工し、ＵプレスでＵ
型に、０プレスで０型に成形する成型工程と、Ｏ型に成
型された鋼板の突合せ部の内側ならびに外側にそれぞれ
自動サブマージアーク溶接を施す溶接工程と、溶接され
た管体を水圧エキスパンダまたはメカニカルエキスパン
ダで拡管する拡管工程とからなる製管法であって、本発
明は特に、このＵＯＥ法の諸工程のうちの溶接工程の改
良に係る。DETAILED DESCRIPTION OF THE INVENTION [Industrial Field of Application] The present invention relates to a method for manufacturing high-alloy clad steel pipes by the UOE method. Here, the UOE method involves cutting a steel plate to a predetermined size, cutting the edges, and pressing the UOE method with a U press.
There is a forming process in which the O-shaped steel plates are formed into a 0-shaped mold, a welding process in which automatic submerged arc welding is performed on the inside and outside of the butt parts of the O-shaped steel plates, and the welded pipe is transferred to a hydraulic expander. Alternatively, the present invention relates to an improvement in the welding process among the various processes of this UOE method.
炭素鋼管の内側にステンレス鋼等の高合金をクラッドし
た鋼管（高合金クラッド鋼管）は、炭素鋼と高合金の長
所を兼ね備えた新しい耐食性鋼管として注目を集めてい
る。Steel pipes in which the inside of a carbon steel pipe is clad with a high alloy such as stainless steel (high alloy clad steel pipe) are attracting attention as a new corrosion-resistant steel pipe that combines the advantages of carbon steel and high alloy.
従来から、炭素鋼に高合金をクラフトした鋼材の溶接に
ついて言われているのは、高合金側の溶接を行う場合に
溶接部の高合金が炭素鋼と溶融混合して、Ｎｉ、 Ｃｒ
等の合金元素が希釈されて高合金の組成を維持できなく
なるのを防止することである。このような点を考慮して
、高合金クラッド鋼の板材においては特別の溶接方法が
用いられる。Conventionally, it has been said that when welding carbon steel with a high alloy, when welding is performed on the high alloy side, the high alloy in the weld zone melts and mixes with the carbon steel, causing Ni and Cr to form.
This is to prevent alloying elements such as those from being diluted and unable to maintain a high alloy composition. With this in mind, special welding methods are used for high-alloy clad steel plates.
第３図（イ）〜（ニ）はこのような方法の一例を示す模
式図である。先ず、同図（イ）に示すように外側の炭素
！ｌ１ｉｌ （１）に開先を設けた後、同図（ロ）に示
すように高合金を溶融させない程度の小人熱をもって、
上記開先を炭素鋼の溶接棒で多層溶接する０次に、同図
（ハ）に示すように内側の高合金（２）の突合せ部分に
いわゆる裏はつりを施した後、同図（ニ）に示すように
小人熱をもって高合金（２）を高合金の溶接棒により溶
接する。FIGS. 3(a) to 3(d) are schematic diagrams showing an example of such a method. First, as shown in the same figure (a), the outer carbon! After making a groove in l1il (1), as shown in the same figure (b), heat it with a small amount of heat that does not melt the high alloy.
The above groove is multi-layer welded with a carbon steel welding rod. Next, as shown in Figure (C), the butt part of the inner high alloy (2) is subjected to so-called back chiseling, and then as shown in Figure (D). As shown in Figure 2, high alloy (2) is welded using a high alloy welding rod with dwarf heat.
しかしこのような方法は低能率であるので、高能率を要
求するＵＯＥ法による鋼管製造には通用できない。However, since such a method has low efficiency, it cannot be used for manufacturing steel pipes by the UOE method, which requires high efficiency.
ＵＯＥ法では高能率を維持するため、従来から内外面共
各々一層の大人熱溶接方法が採用され、能率面から考え
るなら、高合金クラッド鋼に対して第４図（イ）〜（ニ
）に示すような溶接方法が採られることになる。In order to maintain high efficiency in the UOE method, a single-layer heat welding method has traditionally been adopted for both the inner and outer surfaces, and from the standpoint of efficiency, the results shown in Figures 4 (a) to (d) for high-alloy clad steel. The welding method shown will be adopted.
即ち、同図（イ）に示すように、外側の炭素鋼（１）な
らびに内側の高合金（２）にまず開先を設けた後、同図
（ロ）に示すように外側の開先の底部を炭素鋼の溶接ワ
イヤで小人熱をもって仮付溶接する。That is, as shown in Figure (A), a groove is first formed in the outer carbon steel (1) and the inner high alloy (2), and then the outer groove is formed as shown in Figure (B). Tack weld the bottom part with carbon steel welding wire using dwarf heat.
次に、同図（ハ）に示すように内側より高合金の溶接ワ
イヤをもって−Ｐ！ｉ溶接を施した後、同図（ニ）に示
すように外側より炭素鋼または高合金の溶接ワイヤをも
って一層溶接を施す。Next, as shown in the same figure (c), hold the high-alloy welding wire from the inside and -P! After welding, a further weld is performed from the outside using a carbon steel or high alloy welding wire, as shown in Figure (d).
しかしながら、この方法では、内面側の高合金クラッド
層を高合金ワイヤで溶接する場合に、高合金溶接金属に
開先底部の炭素鋼が溶は混むことが避けられず、そのた
めに高合金中の炭素鋼による希釈が５０％以上になり、
内面側の溶接金属の組成をクラッド層の組成と同等に維
持することが困難となる。また、外面側を炭素鋼ワイヤ
で溶接した場合には、内面側のＮｉｑ Ｃｒ等の合金元
素が溶接金属に入り、マルテンサイト組織が形成されて
、高温割れが発生し易くなる。なお、外面側からの溶接
に高合金ワイヤを使用した場合には、炭素謂母材と高合
金溶接金属との境界線で選択腐食が生じ易く、また、成
品どおしを接続する際の円周溶接が炭素鋼の溶接棒では
実施できない等の問題を生じる。However, with this method, when welding the inner high-alloy cladding layer with high-alloy wire, it is inevitable that the carbon steel at the bottom of the groove will mix with the high-alloy weld metal. The dilution by carbon steel is more than 50%,
It becomes difficult to maintain the composition of the weld metal on the inner surface side to be the same as the composition of the cladding layer. In addition, when the outer surface side is welded with carbon steel wire, alloy elements such as Niq Cr on the inner surface side enter the weld metal, forming a martensitic structure and making hot cracking more likely to occur. Note that when high-alloy wire is used for welding from the outside, selective corrosion tends to occur at the boundary between the so-called carbon base material and the high-alloy weld metal. This causes problems such as circumferential welding which cannot be performed with a carbon steel welding rod.
本発明の目的は、開先形状、溶接作業性等に実用上不利
な工夫を講じることなく、上記諸問題を解決することに
ある。An object of the present invention is to solve the above-mentioned problems without making any practical disadvantages to the groove shape, welding workability, etc.
ところで、本出願人は上記目的を達成するための新規な
高合金クラッド鋼管の製造方法を先に出願した（特願昭
６０−６７９１６号および特願昭６０−１８６４７４号
）。By the way, the present applicant has previously filed an application for a method for producing a novel high-alloy clad steel pipe to achieve the above object (Japanese Patent Application No. 60-67916 and Japanese Patent Application No. 60-186474).
この先願発明の方法は、炭素鋼に高合金鋼を重層してな
るクラッド鋼板を高合金を内側として管状に成形した後
、相対向する端同志を突合せ、その突合せ部を溶接して
高合金クラフト鋼管を製造する方法において、第５図（
イ）〜（ハ）に示す如く、炭素［４（１）に開先を設け
る際に高合金（２）の突合せ部近傍を炭素！１！４（１
）の内側開先と干渉しない幅で削除しておいて（（イ）
図）、炭素鋼開先を炭素鋼ワイヤにて内側と外側よりそ
れぞれ溶接しく（ロ）図）、その内側溶接部ａυの上か
ら更に高合金削除部分に高合金ワイヤでサブマージアー
ク溶接により溶接部側を形成するというものである（（
ハ）図）。The method of this prior invention involves forming a clad steel plate made by layering carbon steel and high-alloy steel into a tube shape with the high-alloy inside, and then abutting the opposing ends and welding the abutted parts to create a high-alloy craft. In the method of manufacturing steel pipes, Fig. 5 (
As shown in (a) to (c), when creating a groove in carbon [4 (1), the vicinity of the abutting part of high alloy (2) is cut into carbon! 1!4(1
) to a width that does not interfere with the inner groove ((a)
Figure), the carbon steel groove is welded from the inside and outside with carbon steel wire (Figure 2), and the weld is submerged arc welded with high alloy wire from above the inner welded part aυ to the high alloy removed part. This is to form a side ((
C) Figure).
この方法によれば、炭素鋼ｆｉｌを溶接する際にその影
響が高合金（２）に及ぶのを大幅に回避でき、その結果
として炭素鋼［１）の溶接を高能率かつ容易に行うこと
ができる。According to this method, when welding carbon steel fil, it is possible to largely avoid the effects of the welding on the high alloy (2), and as a result, it is possible to weld carbon steel [1] with high efficiency and ease. can.
ところが、この先願発明の方法は、内面側の溶接が炭素
鋼と高合金とに対して２工程必要であることから、ＵＯ
Ｅ法で通常採用されている内１ｆｉｌパスの溶接ライン
では、直接実施できない難点があり、望ましくは内面側
も１パスで溶接できることが求められる。However, the method of this prior invention requires two steps for welding the inner surface for carbon steel and high alloy, so UO
The one-fil pass welding line normally employed in the E method has the disadvantage that it cannot be directly performed, and it is desirable to be able to weld the inner surface in one pass.
また、最近ではコスト低減の観点から、高合金の厚さを
薄くした、いわゆる薄クラッドの必要性が高まっており
、この薄クラッドに対しても良好な溶接性を確保するこ
とが望まれる。Furthermore, recently, from the viewpoint of cost reduction, there has been an increasing need for so-called thin cladding in which the thickness of high alloy is reduced, and it is desired to ensure good weldability even for this thin cladding.
本発明は、先願発明の方法が本来的に合わせ持つ優位性
、すなわち高品質性、高能率性を減殺することなく、上
記要望に応えるもので、その要旨とするところは第１図
および第２図に示すように、ＵＯＥ法による高合金（２
）と炭素＠ ｉｌ＋のクラッド鋼管の製造において、あ
らかじめ外側に深さく８）が炭素鋼の厚さの４０〜７０
％で角度（Ａ）が６０〜９０’である開先を設け、内側
突合せ部の１０〜２０１）１幅（Ｃ）の部分の高合金を
削除して炭素鋼を露出させ、更に炭素鋼のこの内側露出
部分に深さ山）が炭素鋼の厚さの２０〜５０％で角度（
Ｂ）が６０〜９０°の角度の開先を設けた成形管に対し
、先ず外側の開先に炭素鋼ワイヤによる仮付溶接（６）
を施した後、内側突合せについてその炭素鋼開先を炭素
鋼ワイヤによるＭＩＧ溶接（７）を、また高合金削除部
分に高合金ワイヤによるサブマージアーク溶接（８）を
１ラン連Ｖｔ溶接で施し、その後、外側の開先に対し炭
素鋼ワイヤでサブマージアーク溶接θ１を行うことを特
徴とする高合金クラッド鋼管の製造方法にある。The present invention satisfies the above demands without diminishing the inherent advantages of the method of the prior invention, that is, high quality and high efficiency. As shown in Figure 2, high alloy (2
) and carbon@il+ clad steel pipes, the outer depth 8) is 40 to 70 mm thicker than the carbon steel.
A groove with an angle (A) of 60 to 90' is provided, and the high alloy in the 10 to 201) width (C) portion of the inner butt part is removed to expose the carbon steel, and the carbon steel is further removed. In this inner exposed part, the depth peak) is 20 to 50% of the thickness of the carbon steel and the angle (
B) For a formed pipe with a bevel at an angle of 60 to 90°, first tack weld the outer bevel with carbon steel wire (6)
After that, for the inner butt, the carbon steel groove was MIG welded with carbon steel wire (7), and the high alloy removed part was submerged arc welded with high alloy wire (8) by one run continuous Vt welding, Thereafter, the method for manufacturing a high alloy clad steel pipe is characterized in that submerged arc welding θ1 is performed on the outer groove using a carbon steel wire.
本発明の方法は、内側の炭素鋼に設けた開先と、高合金
を削除した炭素ｆｉｌ露出部分とを１パス連続溶接する
点に最大の特徴があり、この１パス連続溶接はＭＩＧ溶
接とサブマージアーク溶接との組合せでしか達成し得な
いものである。The most distinctive feature of the method of the present invention is that the groove provided in the inner carbon steel is continuously welded in one pass to the exposed carbon film portion from which the high alloy has been removed.This one-pass continuous welding is similar to MIG welding. This can only be achieved in combination with submerged arc welding.
すなわち、ＭＩＧ溶接はスラグがほとんど発生せず、そ
の上に引き続きサブマージアーク溶接を実施しても、何
ら問題を生じないばかりでなく、サブマージアーク溶接
は炭素Ｗ４露出部分の如き幅広部分に浅溶込みビードを
比較的高速で形成できるのである。In other words, MIG welding generates almost no slag, and even if submerged arc welding is subsequently performed on top of it, there is no problem. Submerged arc welding also allows shallow penetration into wide areas such as carbon W4 exposed areas. Beads can be formed relatively quickly.
ちなみに、この組合せを他の組合せと比較すると、次の
とおりである。Incidentally, a comparison of this combination with other combinations is as follows.
いま仮に、ＭＩＧ溶接とＭＩＧ７＄接とを組合せるなら
ば、あとのＭＩＧ溶接では浅溶は込みとなって幅広のビ
ードを得ることが難しく、またスパッターも発生しやす
く、そのために高合金削除部分の溶接が不良となる。If we were to combine MIG welding and MIG7$ welding, the subsequent MIG welding would involve shallow welding, making it difficult to obtain a wide bead, and spatter would also be likely to occur, which would result in the removal of high-alloy parts. Welding becomes defective.
また仮に、先行、後行ともサブマージアークｌ容接を採
用した場合には、内側の炭素鋼開先の溶着金属にスラグ
を生じ、あとのサブマージアーク溶接のときにアークが
不安定となって内側の溶着金属全体に欠陥を生じる。Furthermore, if submerged arc welding is used for both leading and trailing welding, slag will occur in the weld metal on the inner carbon steel groove, and the arc will become unstable during subsequent submerged arc welding, causing Defects occur throughout the deposited metal.
また、先行溶接においてＭＩＧ？８接の代わりにＴＩＧ
溶接が採用されない理由は、ＴＩＧ溶接ではスパッター
が発生するおそれはないものの、溶接速度が権端に遅く
なってサブマージアーク溶接に溶接速度を合わせること
ができなくなる点にある。Also, MIG in advance welding? TIG instead of 8 tangent
The reason why welding is not adopted is that although there is no risk of spatter occurring in TIG welding, the welding speed is extremely slow, making it impossible to match the welding speed to submerged arc welding.
また、本発明の方法はクラッド鋼の高合金が２゜０−−
以下の場合にも安定な溶接を行い得るが、その理由は次
のとおりである。In addition, the method of the present invention is such that the high alloy of the clad steel is 2゜0--
Stable welding can also be performed in the following cases, and the reason is as follows.
ＭＩＧ溶接とサブマージアーク溶接とでは溶接、速度を
合わせることが出来、溶着量を溶接電流や速度でコント
ロールすることによりクラッド鋼の高合金の厚さが薄い
場合にも対応可能である。With MIG welding and submerged arc welding, welding speeds can be matched, and by controlling the amount of welding by the welding current and speed, it is possible to handle cases where the thickness of the high-alloy clad steel is thin.
以下、本発明の実施の態様を第１図および第２図を参照
しながら項目別に詳しく説明する。Hereinafter, embodiments of the present invention will be explained in detail item by item with reference to FIGS. 1 and 2.
ａ、高合金鋼
本発明において高合金とはＣｒとＮｉの少なくとも一方
が重量％で２０％以上を含まれているものを言い、具体
的には２２Ｃｒ −６Ｎｉ系の２相ステンレス鋼や２０
Ｃｒ ４ＯＮｉ系のアロイ８２５等である。a. High alloy steel In the present invention, high alloy refers to a material containing at least 20% by weight of at least one of Cr and Ni, specifically 22Cr-6Ni duplex stainless steel and 20
Cr4ONi alloy 825 or the like.
炭素鋼に高合金をクラフトさせる方法としては圧延、爆
着等の常法を全て適用できる。All conventional methods such as rolling and explosive bonding can be used to craft high alloys from carbon steel.
ｂ、外側突合せ部の炭素鋼開先
深さくａｌについては、深さが炭素鋼の厚さの４０％未
満では、内側からの溶接の溶込み部と重ならずに未溶接
部が残ることになり、また逆に７０％を超える場合には
、外側の溶接時に、内側への溶は落ちが生じやす（なる
ので、炭素鋼の厚さ４０〜７０％とする。b. Regarding the depth al of the carbon steel groove at the outer butt part, if the depth is less than 40% of the thickness of the carbon steel, an unwelded part will remain without overlapping with the penetration part of welding from the inside. On the other hand, if it exceeds 70%, melting to the inside tends to drop when welding the outside (therefore, the thickness of carbon steel is set to 40 to 70%).
開先角度（Ａ）については、６０”未満では、溶接ビー
ドが凸形となって高温割れの危険性があり、９０’を超
えると溶着金属の量が多くなり能率的でないので、６０
〜９０°とする。Regarding the groove angle (A), if it is less than 60'', the weld bead will become convex and there is a risk of hot cracking, and if it exceeds 90', the amount of weld metal will increase and it is not efficient.
~90°.
Ｃ０内側突合せ部における高合金鋼削除目的は前述した
とおり、炭素鋼を溶接する際の影響が高合金に及ぶのを
防止することである。As mentioned above, the purpose of removing the high alloy steel at the C0 inner butt portion is to prevent the effect of welding the carbon steel from affecting the high alloy.
削除の輻（Ｃ）については１０１）未満では、内側の炭
素鋼の溶接ワイヤによる溶接ビードと高合金とが接触し
て溶融混合がおこり高合金が希釈される。When the radius of deletion (C) is less than 101), the weld bead of the inner carbon steel welding wire contacts the high alloy, causing melting and mixing and diluting the high alloy.
２５０を超えると、必要溶着量が増加し、一層溶接では
盛り上げが困難になるので、１０〜２０−１とする。When it exceeds 250, the required amount of welding increases and it becomes even more difficult to build up by welding, so it is set to 10 to 20-1.
言うまでもないが、この１０〜２０ｍ−は、突合せ線を
中心として両側にほぼ均等にふりわけられなけれ°ばな
らない。Needless to say, this 10 to 20 m must be distributed almost equally on both sides of the butt line.
また、たとえ高合金鋼の削除幅と炭素鋼の内側開先幅と
がその数的条件範囲であうでも、削除幅は開先幅より大
（同一は含まず）でなければならない、換言すれば、高
合金の端面（３）が炭素鋼の内側開先と干渉してはなら
ず、両者の間にクリアランスが必要である。In addition, even if the removal width of high alloy steel and the inner groove width of carbon steel are within the numerical condition range, the removal width must be larger (not including the same) than the groove width, in other words, The high alloy end face (3) must not interfere with the carbon steel inner groove, and a clearance is required between the two.
高合金の端面（３）には傾斜を付与するのがよく、その
角度θは２０〜４０°が好ましい、θが２０°未満では
、高合金削除部分のコーナ一部にスラグ巻込みが生じや
すく、４０“を超えると必要溶ＭＷが過大となり、一層
溶接では盛り土げが困難となる。The end face (3) of the high alloy is preferably sloped, and the angle θ is preferably 20 to 40°. If θ is less than 20°, slag is likely to be caught in a part of the corner of the high alloy removed part. , 40", the required melt MW becomes excessive, and it becomes even more difficult to build up the earth by welding.
ｄ、内側突合せ部の炭素鋼開先
開先深さくｂｌについては、深さが炭素鋼の厚さの２０
％未満では外側の炭素鋼からの溶は込み部と重ならず未
溶接部が残ることになり、また５０％を超えると、あら
かじめ高合金を削除すべき幅が広くなって能率的でない
ので、炭素鋼の厚さの２０〜５０％とする。d. Regarding the carbon steel groove groove depth bl of the inner butt part, the depth is 20 mm of the thickness of the carbon steel.
If it is less than 50%, the welding from the outer carbon steel will not overlap with the welded part and an unwelded part will remain, and if it exceeds 50%, there will be a wide range of high alloy to be removed in advance, which is not efficient. The thickness should be 20 to 50% of the thickness of carbon steel.
開先角度（Ｂ）については、外側突合せ部の炭素鋼開先
の場合と同じ理由から、６０〜９０°の範囲とする。The groove angle (B) is set in the range of 60 to 90 degrees for the same reason as in the case of the carbon steel groove of the outer abutting portion.
ｅ、外側炭素鋼の仮付）８接
第１図（イ）に示すように仮付溶接部（６）は、通常の
炭素鋼ワイヤを使った炭酸ガス溶接で能率よく形成する
ことができる。e. Tack welding of outer carbon steel) 8-junction As shown in FIG. 1(a), the tack weld (6) can be efficiently formed by carbon dioxide gas welding using ordinary carbon steel wire.
ｒ、内側突合せ部の溶接
この溶接については、炭素鋼開先をＭＩＧ溶接で、また
、高合金削除部分をサブマージアーク溶接で１ラン連続
溶接する。この連続溶接とは、第２図に示す通り、ＭＩ
Ｇ）−チ（４）を先行、サブマージアーク溶接トーチ（
５）を後行にタンデム配置し、両者に同時にアークを発
生させて、１ランで炭素鋼溶接部（７）と高合金溶接部
（８）（第２図（ロ））とを得る方法である。r. Welding of the inner butt part For this welding, the carbon steel groove is welded by MIG welding, and the high alloy removed part is welded continuously in one run by submerged arc welding. This continuous welding is, as shown in Figure 2, MI
G)-Chi (4) is preceded by a submerged arc welding torch (
5) are arranged in tandem in the rear row, and an arc is generated in both at the same time to obtain a carbon steel weld (7) and a high alloy weld (8) (Fig. 2 (b)) in one run. be.
炭素鋼開先の炭素鋼ワイヤによるＭＵＧ溶接は、開先を
炭素鋼で完全に埋めきることが重要であり、溶着量が少
なすぎても多すぎても後続の高合金ワイヤによるサブマ
ージアーク溶接に悪影響を及ぼすので、後述するように
主にこの観点から諸条件が設定される。When performing MUG welding with carbon steel wire on a carbon steel groove, it is important to completely fill the groove with carbon steel, and if the amount of welding is too small or too large, it will not be possible to perform submerged arc welding with subsequent high alloy wire. Since this has an adverse effect, various conditions are set mainly from this viewpoint, as will be described later.
なお本来、ＭＩＧ溶接とはシールドガスにアルゴンのみ
を使用するものを指すが本発明の方法ではアークの安定
化等、作業性を増すために２０％以下の炭酸ガスを含む
シールドガスを使用する溶接もＭＴＧ溶接の筒中として
いる。Originally, MIG welding refers to welding that uses only argon as a shielding gas, but the method of the present invention uses a shielding gas that contains less than 20% carbon dioxide gas to stabilize the arc and increase workability. It is also used in MTG welding.
ＭＩＧ溶接の炭素鋼ワイヤ径は１．６〜３．２■量が好
ましい、 １．６■−未満では溶接電流を十分に上げ
られず、溶込量、溶ｆＦ！ともに不足し、３．２ｍｍを
超えるとワイヤの送給速度が遅（なりすぎ、溶接速度を
十分に高めることが困難になる。The carbon steel wire diameter for MIG welding is preferably 1.6 to 3.2 mm. If it is less than 1.6 mm, the welding current cannot be raised sufficiently and the penetration amount and weld fF! If both are insufficient, and if it exceeds 3.2 mm, the wire feeding speed becomes too slow (too much), making it difficult to sufficiently increase the welding speed.
ＭＩＧ溶接の電流は２５０〜５００Ａが好ましい。The current for MIG welding is preferably 250 to 500A.
２５０Ａ未満ではＰａ着量が不足し、５００Ａを超える
と逆に溶着量が増加し、溶着金属が高合金属と接触する
危険を生じる。If it is less than 250A, the amount of Pa deposited will be insufficient, and if it exceeds 500A, the amount of welded will increase, creating the risk that the deposited metal will come into contact with the high alloy metal.
ＭＩＧ溶接の電圧の２０Ｖから３５Ｖが好ましい。The voltage for MIG welding is preferably 20V to 35V.
２０Ｖ未満では短絡が生じ易くなり、３５■を超えると
溶接ビードにハンピング現象が生じ易くなる。If it is less than 20 V, a short circuit tends to occur, and if it exceeds 35 V, a humping phenomenon tends to occur in the weld bead.
本発明の方法では炭素鋼のＭＩＧ溶接に引き続いて高合
金のサブマージアーク溶接を行うが、このサブマージア
ーク溶接における要点は炭素鋼をいかに希釈せずに高合
金の溶接を行うかという点にある０本発明の方法では高
合金溶接時の希釈率（高合金中に炭素鋼が溶解する割合
）を２０％以下に抑制し、かつ炭素鋼への熔込み深さを
２１■程度にすることを目標にした。In the method of the present invention, MIG welding of carbon steel is followed by submerged arc welding of high alloy.The key point in this submerged arc welding is how to weld high alloy without diluting the carbon steel. The goal of the method of the present invention is to suppress the dilution rate during high alloy welding (the rate at which carbon steel melts into the high alloy) to 20% or less, and to achieve a welding depth of approximately 21 cm into the carbon steel. I made it.
このサブマージアーク溶接においては、高合金属の厚さ
が２ｆｌ以下のクラッド鋼板の場合、溶着量、溶接速度
、希釈率の関係を考慮しても単電極一層溶接で十分であ
る。In this submerged arc welding, in the case of a clad steel plate in which the thickness of the high-alloy metal is 2 fl or less, single-electrode single-layer welding is sufficient even considering the relationship between the amount of welding, welding speed, and dilution rate.
サブマージアーク溶接の溶接ワイヤは直径３．２〜４．
ＯＨの高合金コアードワイヤ又はソリッドワイヤが好ま
しい、ワイヤ直径が３．２ｆｉ未満ではアークが集中し
易くなって溶込み量が増加し、４．０鴎を超えると後述
の通り低電流域でアークが不安定になり、スラグ巻込み
が発生し易くなる。The welding wire for submerged arc welding has a diameter of 3.2 to 4.
OH high-alloy cored wire or solid wire is preferred. If the wire diameter is less than 3.2 fi, the arc tends to concentrate and the amount of penetration increases, and if it exceeds 4.0 fi, the arc will fail in the low current range as described below. It becomes stable and slag entrainment becomes more likely to occur.
ワイヤの種類についてはコアードワイヤの方がアークが
軟らかく溶込み量に対して適応性があるが、ソリッドワ
イヤの使用でも低電流域の溶接において２０％以下の希
釈率を満足させることができる。Regarding the type of wire, cored wire has a softer arc and is more adaptable to the amount of penetration, but even when using solid wire, a dilution rate of 20% or less can be satisfied in welding in a low current range.
フラックスはボンドフラックスが好ましい、ボンドフラ
ックスを用いて溶接する場合は、溶融型フラックスを使
用する場合に比べて溶込みの浅い溶接ビードが得られる
とともに、合金元素の添加が可能であることがら溶着金
属の成分調整が容易であり、しかも高アーク電化でのア
ーク安定性が良好である。Bonded flux is preferred as the flux. When welding using bonded flux, a weld bead with shallower penetration can be obtained than when using molten type flux, and it is possible to add alloying elements. It is easy to adjust the components, and the arc stability is good at high arc electrification.
サブマージアーク溶接の電極は前進角０〜３０’が好ま
しい。０°未満ではいわゆる後退角となって溶込み深さ
が過大となり、３０°を超えるとアークが不安定になる
ことがある。The electrode for submerged arc welding preferably has an advancing angle of 0 to 30'. If it is less than 0°, the angle becomes so-called a recession angle, resulting in an excessive penetration depth, and if it exceeds 30°, the arc may become unstable.
サブマージアーク溶接の溶接電流は３００〜６００Ａが
好ましい、 ３００Ａ未満では溶接ビード輻、溶接ビ
ード輻、溶着量が不足し、６００ Ａを超えると溶込み
が過大となる。The welding current for submerged arc welding is preferably 300 to 600 A. If it is less than 300 A, weld bead radius, weld bead radius, and welding amount will be insufficient, and if it exceeds 600 A, penetration will be excessive.
ＭＩＧｉ接とサブマージアーク溶接における電極間距離
は３０ＩＩｍ以上が好ましい、３０１ｓ未満では両者の
アークに干渉が生してアーク不安定を生じる。The distance between the electrodes in MIGi welding and submerged arc welding is preferably 30 II m or more; if it is less than 301 seconds, interference will occur between the two arcs, causing arc instability.
上限については、溶接ヘッドをコンパクト化する意味か
ら、３００ｗ程度が好ましい。The upper limit is preferably about 300 W in order to make the welding head more compact.
両溶接の速度は、３０〜６０ｃ＋ａ／ｎ＋ｉｎが好まし
い。The speed of both welding is preferably 30 to 60 c+a/n+in.
３Ｑｃｍ／ｍｉｎ未満では溶接ビードの溶込みが深くな
ると同時に能率を悪くする。逆に６０ｃ＋ｍ／ｓｉｎを
超えると溶接ビードが不安定となる。If the welding speed is less than 3Qcm/min, the weld bead penetrates deeply and at the same time the efficiency deteriorates. On the other hand, if it exceeds 60c+m/sin, the weld bead becomes unstable.
ｇ、外側炭素鋼の溶接
外側の炭素鋼開先に炭素鋼ワイヤでサブマージアーク溶
接を行うものであり、第１図（ハ）に示すとおり、仮付
溶接部（６）を溶かし、内側炭素鋼溶接部（７）とビー
ドを重ねて外側炭素ｍ溶接部Ｑｌを形成する０手法的に
は通常のＵＯＥ法と同様でよい。g. Welding of outer carbon steel Submerged arc welding is performed with carbon steel wire on the outer carbon steel groove. As shown in Figure 1 (c), the tack welded part (6) is melted and the inner carbon steel is welded. The method of forming the outer carbon m welding part Ql by overlapping the welding part (7) and the bead may be the same as the normal UOE method.
実施例１゜
第１表に成分組成および肉厚を示す供試クラッド材を本
発明法、即ち第１図に模式的に示した方法と、ＵＯＥ法
で通常行われている方法、即ち第４図に模式的に示した
方法（以下、比較法という）とで溶接した。溶接にあた
っては第２表に示す開先を供試材に設け、第３表に示す
溶接条件を設定した。また、使用した溶接ワイヤは化学
組成が第４表のとおりであって、本発明法については内
側ＭＵＧ溶接と外側に同表の炭素鋼の溶接ワイヤを、内
側のサブマージアーク溶接には高合金の溶接ワイヤを用
い、比較法については内側、外側とも同表の高合金溶接
ワイヤを用いた。フラックスはボンドフラックスを用い
た。溶接後の内側溶接金属の化学組織と第５表に示す。Example 1 Test cladding materials whose component compositions and wall thicknesses are shown in Table 1 were prepared using the method of the present invention, that is, the method schematically shown in FIG. Welding was carried out using the method schematically shown in the figure (hereinafter referred to as the comparative method). For welding, the grooves shown in Table 2 were provided on the sample materials, and the welding conditions shown in Table 3 were set. The chemical composition of the welding wire used is as shown in Table 4. For the method of the present invention, carbon steel welding wire shown in the same table was used for the inner MUG welding and the outer side, and high alloy welding wire was used for the inner submerged arc welding. Welding wire was used, and for the comparative method, high alloy welding wire shown in the same table was used for both the inside and outside. Bond flux was used as the flux. Table 5 shows the chemical structure of the inner weld metal after welding.
供試クラッド鋼は高合金の厚みが２゜Ｏｆｉと薄いもの
であるが、本発明法においては溶接金属はクランド鋼の
高合金部分に近い成分が得られている。The sample clad steel has a high alloy thickness as thin as 2°Ofi, but in the method of the present invention, the weld metal has a composition close to that of the high alloy part of the clad steel.
これに対し、比較法の場合には著しく成分の異なった溶
接金属となり、希釈の大きいことが分かる。On the other hand, in the case of the comparative method, the weld metal has a significantly different composition, indicating that dilution is large.
また、本発明法の内側溶接ではＭＩＧ溶接とサブマージ
アーク溶接を同時に行っているが、と−ド不良等はなく
、良好な溶接部が得られた。In addition, in the inside welding method of the present invention, MIG welding and submerged arc welding were performed simultaneously, and a good welded part was obtained without any lead defects.
また、高合金の厚みが１．０鶴の場合にも内側の溶接速
度を７０〜８０（Ｊ／■ｉｎに設定することにより厚み
が２ 、０ 鶴と同様に良好な溶接部が得られることを
確認した。In addition, even when the thickness of the high alloy is 1.0 mm, by setting the inner welding speed to 70 to 80 (J/■in), a good welded part can be obtained like when the thickness is 2.0 mm. It was confirmed.
第 １ 表
第 ２ 表
実施例２゜
第６表に成分組成を示す供試クラッド材に対し、本発明
法の手順により種々の開先部形状について溶接を行った
。溶接条件は第３表の本発明法、溶接ワイヤは第４表に
それぞれ示すとおりである。Table 1 Table 2 Example 2 Welding of various groove shapes was performed on the test cladding materials whose compositions are shown in Table 6 according to the procedure of the present invention. The welding conditions are as shown in Table 3 for the method of the present invention, and the welding wires are as shown in Table 4.
第７表に開先部形状と、各形状について溶接を行ったと
きの作業性との関係を示すが、開先部形状が本発明範囲
内のものはいずれも溶接作業性が良好である。Table 7 shows the relationship between the groove shape and the workability when welding each shape, and all groove shapes within the range of the present invention have good welding workability.
実施例３゜
第６表に示す供試クラッド綱に対し、第８表に示す本発
明範囲内の形状の開先を形成し、本発明方法の手順によ
り種々の条件で内側部分の１パス連続溶接を行った。こ
の時の溶接条件と溶接作業性の関係を第９表に示す、な
お、ワイヤは第４表に示すものを使用し、ＭＩＧ溶接で
は炭素調ワイヤ、サブマージアーク溶接では高合金ワイ
ヤをそれぞれ用いた。Example 3 A groove having a shape within the scope of the present invention as shown in Table 8 was formed on the test clad steel shown in Table 6, and one continuous pass of the inner part was performed under various conditions according to the procedure of the method of the present invention. Performed welding. The relationship between the welding conditions and welding workability at this time is shown in Table 9.The wires shown in Table 4 were used, carbon tone wire was used for MIG welding, and high alloy wire was used for submerged arc welding. .
第 ８ 表
第９表における本発明例のうち、ケース目ま溶接諸条件
の少なくとも１つが最適条件から外れた場合、ケース■
は全条件が最適の場合をそれぞれ表している。Table 8 Among the invention examples in Table 9, if at least one of the case welding conditions deviates from the optimal condition, case ■
represents the case where all conditions are optimal.
また、第９表の本発明例（ケース■）のうち、２番目の
ものについてフラックスのみをボンドフラックスから溶
融型フラフクスに変更したところ溶込み深さが約４鰭と
深くなった。Furthermore, in the second example of the present invention in Table 9 (Case ■), when only the flux was changed from bonded flux to melted flux, the penetration depth became as deep as about 4 fins.
以上の如く本発明の高合金グランド鋼管の製造方法によ
れば、厚み２龍以下の高合金を重量してなるクラッド鋼
にあっても、高合金削除部分の溶接の際に高合金が炭素
鋼と溶融混合するのを抑止し、Ｎｉｓ Ｃｒ等の合金元
素が希釈されるのを抑えることができるので、成品管の
機械的性質および化学的性質を溶接部近傍で劣化させる
ことなく、すぐれた高合金クラッド鋼管を製造すること
ができる。As described above, according to the method for manufacturing a high alloy gland steel pipe of the present invention, even if the clad steel is made of a high alloy with a thickness of 2 or less, the high alloy is removed from the carbon steel when welding the high alloy removed portion. This prevents the melting and mixing of alloying elements such as Nis Cr and dilution of alloying elements such as Nis Cr, so the mechanical and chemical properties of the finished pipe are not deteriorated near the welded area and excellent high quality properties can be achieved. Alloy clad steel pipes can be manufactured.
また、内側突合せ部において高合金を削除しであること
により、炭素鋼を独立的に溶接し得、通常のＵＯＥ法に
おける溶接速度および作業性を確保できる。Furthermore, by eliminating the high alloy at the inner butt portion, the carbon steel can be welded independently, and the welding speed and workability of the normal UOE method can be ensured.
そして何よりも内側突合せ部において炭素鋼開先の溶接
と高合金削除部分の溶接とを１パスで連続溶接するので
、既設のＵＯＥ法製管ラインへの直接通用が可能になり
全体として製管能率が大幅に向上し、製管コストの低減
に大きな効果を発揮するものとなる。Best of all, since the welding of the carbon steel groove and the welding of the high-alloy removed portion are performed continuously in one pass at the inner butt part, it can be directly connected to the existing UOE pipe manufacturing line, improving overall pipe manufacturing efficiency. This is a significant improvement and will have a significant effect on reducing pipe manufacturing costs.
第１図（イ）〜（ハ）および第２図は本発明方法の実施
状態を示す模式図、第３図（イ）〜（ハ）はクラッド鋼
板溶接法の溶接手順を示す模式図、第４図（イ）〜（ニ
）はＵＯＥ鋼管製造法でクラッド鋼管を溶接する場合の
溶接手順を示す模式図、第５図（イ）〜（ハ）は先願発
明の方法における溶接手順を示す模式図である。
ｌ：炭素鋼、２：高合金、４：ＭＩＧ溶接トーチ、５：
サブマージアーク溶接トーチ、６：仮付溶接部、７：Ｍ
ＩＧ溶接部（内側炭素鋼溶接部）、８：サブマージアー
ク溶接部（高合金溶接部）、１０：サブマージアーク溶
接部（外側炭素ｆｉ４溶着部）。Figures 1 (a) to (c) and 2 are schematic diagrams showing the implementation state of the method of the present invention, and Figures 3 (a) to (c) are schematic diagrams showing the welding procedure of the clad steel plate welding method. Figures 4 (a) to (d) are schematic diagrams showing the welding procedure when clad steel pipes are welded by the UOE steel pipe manufacturing method, and Figures 5 (a) to (c) show the welding procedure in the method of the prior invention. It is a schematic diagram. l: carbon steel, 2: high alloy, 4: MIG welding torch, 5:
Submerged arc welding torch, 6: Tack welding part, 7: M
IG weld (inner carbon steel weld), 8: submerged arc weld (high alloy weld), 10: submerged arc weld (outer carbon fi4 weld).
Claims (5)
合金を内側として管状に成形した後、相対向する端同志
を突合せ、その突合せ部を溶接して高合金クラッド鋼管
を製造する方法において、あらかじめ外側に深さが炭素
鋼の厚さの４０〜７０％で角度が６０〜９０°である開
先を設け、内側突合せ部の１０〜２０ｍｍ幅の部分の高
合金を削除して炭素鋼を露出させ、更に炭素鋼のこの内
側露出部分に深さが炭素鋼の厚さ２０〜５０％で角度が
６０〜９０°の開先を設けた成形管に対し、先ず外側の
開先に炭素鋼ワイヤによる仮付溶接を施した後、内側突
合せ部についてその炭素鋼開先に炭素鋼ワイヤによるＭ
ＩＧ溶接を、また高合金削除部分に高合金ワイヤによる
サブマージアーク溶接を１ラン連続溶接で施し、その後
、外側の開先に対し炭素鋼ワイヤでサブマージアーク溶
接を行うことを特徴とする高合金クラッド鋼管の製造方
法。(1) A method of manufacturing a high-alloy clad steel pipe by forming a clad steel plate made by layering a high alloy on carbon steel into a tube shape with the high alloy on the inside, and then butting the opposing ends together and welding the butted parts. In this process, a bevel with a depth of 40 to 70% of the thickness of the carbon steel and an angle of 60 to 90° is prepared in advance on the outside, and the high alloy in the 10 to 20 mm wide part of the inner butt part is removed to form a carbon steel. For a formed tube in which the steel is exposed and a bevel with a depth of 20 to 50% of the thickness of the carbon steel and an angle of 60 to 90° is provided in this inner exposed part of the carbon steel, first, the outer groove is After tack welding with carbon steel wire, M is applied to the carbon steel groove of the inner butt part with carbon steel wire.
A high-alloy cladding characterized by IG welding, submerged arc welding using a high-alloy wire on the high-alloy removed portion in one continuous run, and then submerged arc welding using a carbon steel wire on the outer groove. Method of manufacturing steel pipes.
ことを特徴とする特許請求の範囲第１項に記載の高合金
クラッド鋼管の製造方法。(2) The method for manufacturing a high-alloy clad steel pipe according to claim 1, wherein the high-alloy thickness of the clad steel is 2.0 mm or less.
５Ｖとする。 の各条件で実施されることを特徴とする特許請求の範囲
第１項又は第２項に記載の高合金クラッド鋼管の製造方
法。(3) MIG welding of the inner butt portion: [1] Carbon steel wire with a diameter of 1.6 to 3.2 mm is used. [2] Welding current 250-500A, arc voltage 20-3
Set it to 5V. A method for manufacturing a high-alloy clad steel pipe according to claim 1 or 2, characterized in that the method is carried out under each of the following conditions.
３．２〜４．０ｍｍ径の高合金コアードワイヤ又はソリ
ッドワイヤを用いる。 ［２］溶接フラックスとしてボンドフラックスを用いる
。 ［３］電極の角度を前進角０〜３０°とする。 ［４］溶接電流３００〜６００Ａ、アーク電圧３０〜５
０Ｖとする。 の各条件で実施されることを特徴とする特許請求の範囲
第１項乃至第３項記載のいずれかに記載の高合金クラッ
ド鋼管の製造方法。(4) Submerged arc welding of the inner butt part [1]
A high alloy cored wire or solid wire with a diameter of 3.2 to 4.0 mm is used. [2] Bond flux is used as welding flux. [3] The angle of the electrode is set to an advancing angle of 0 to 30 degrees. [4] Welding current 300-600A, arc voltage 30-5
Set it to 0V. A method for manufacturing a high-alloy clad steel pipe according to any one of claims 1 to 3, characterized in that the method is carried out under each of the following conditions.
ジアーク溶接が、電極間距離３０ｍｍ以上、溶接速度３
０〜６０ｃｍ／ｍｉｎで実施されることを特徴とする特
許請求の範囲第１項乃至第４項のいずれかに記載の高合
金クラッド鋼管の製造方法。(5) MIG welding and submerged arc welding at the inner butt part are performed with an electrode distance of 30 mm or more and a welding speed of 3
5. The method for manufacturing a high-alloy clad steel pipe according to any one of claims 1 to 4, characterized in that the manufacturing method is carried out at a rate of 0 to 60 cm/min.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP15456686A JPS6310095A (en) | 1986-06-30 | 1986-06-30 | Manufacture of high alloy clad steel pipe |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP15456686A JPS6310095A (en) | 1986-06-30 | 1986-06-30 | Manufacture of high alloy clad steel pipe |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS6310095A true JPS6310095A (en) | 1988-01-16 |
Family
ID=15587039
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP15456686A Pending JPS6310095A (en) | 1986-06-30 | 1986-06-30 | Manufacture of high alloy clad steel pipe |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6310095A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101767260A (en) * | 2008-12-30 | 2010-07-07 | 湖北双环科技股份有限公司 | Welding method for overhaul of furnace chamber heat exchange tube |
-
1986
- 1986-06-30 JP JP15456686A patent/JPS6310095A/en active Pending
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101767260A (en) * | 2008-12-30 | 2010-07-07 | 湖北双环科技股份有限公司 | Welding method for overhaul of furnace chamber heat exchange tube |
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