JPS6114097A - Submerged arc welding method of two-phase stainless steel - Google Patents
Submerged arc welding method of two-phase stainless steelInfo
- Publication number
- JPS6114097A JPS6114097A JP13184084A JP13184084A JPS6114097A JP S6114097 A JPS6114097 A JP S6114097A JP 13184084 A JP13184084 A JP 13184084A JP 13184084 A JP13184084 A JP 13184084A JP S6114097 A JPS6114097 A JP S6114097A
- Authority
- JP
- Japan
- Prior art keywords
- welding
- weld metal
- content
- stainless steel
- submerged arc
- 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
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/36—Selection of non-metallic compositions, e.g. coatings, fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest
- B23K35/3601—Selection of non-metallic compositions, e.g. coatings, fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest with inorganic compounds as principal constituents
- B23K35/3603—Halide salts
- B23K35/3605—Fluorides
Landscapes
- Chemical & Material Sciences (AREA)
- Inorganic Chemistry (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Nonmetallic Welding Materials (AREA)
- Arc Welding In General (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
高クロム系の、オー−ステナイト・フェライト混合相を
呈する２相ステンレス鋼は、オーステナイト系ステンレ
ス鋼に比べ高い強度を有していると同時に塩素イオンを
含む環境において応力腐食割れや孔食に対して優れた特
性を有し、そのため腐食性の高いオイル・ガスの輸送用
パイプとして使用されつつある。Detailed Description of the Invention (Field of Industrial Application) High chromium duplex stainless steel exhibiting a mixed phase of austenite and ferrite has higher strength than austenitic stainless steel, and at the same time is free from chlorine. It has excellent properties against stress corrosion cracking and pitting corrosion in environments containing ions, and is therefore increasingly being used as pipes for transporting highly corrosive oil and gas.
前記の混合相を呈する２相ステンレス鋼のうち、とくに
２２Ｃｒ −５，５Ｎｉ −３ＭＣ１−Ｎ系２相ステン
レス鋼はその仮相を用いるＵＯＥパイプの如き製造工程
に６けるシーム溶接のためのサブマージアーク溶接方法
の改善に関してこの明細書で述べる技術内容は適切な組
成の電極と７ラツクスの最適組合わせについての開発成
果を提案するところにある。Among the duplex stainless steels exhibiting a mixed phase, 22Cr-5,5Ni-3MC1-N duplex stainless steels are particularly suitable for submerged arc welding for seam welding in manufacturing processes such as UOE pipes using the temporary phase. Regarding the improvement of welding methods, the technical content described in this specification is to propose the development results regarding the optimal combination of electrodes with appropriate compositions and 7 lux.
（従来の技術）
従来、この種の溶接に当っては共金糸の溶接金属を１ｑ
るサブマージアーク溶接については、鉄と鋼ＶＯぶ６３
． Ｎｏ ４．１９７７の５３９４ページに示されるよ
うに施されていたが、溶接作業性、溶接ままの溶接金属
のしん性において問題があった。(Prior art) Conventionally, in this type of welding, 1q of weld metal of the same metal thread was used.
Regarding submerged arc welding, see Tetsu-to-Hagane VO 63.
．． No. 4.1977, page 5394, but there were problems with welding workability and the toughness of the as-welded weld metal.
（発明が解決しようとする問題点）
溶接用電極と７ラツクスの最適組合わせに係る開発研究
の結果としＣ溶接作業性を良好にするとともに溶接金属
のしん性を向−卜するところにある。(Problems to be Solved by the Invention) As a result of research and development on the optimal combination of welding electrodes and 7lux, the present invention aims to improve C welding workability and improve the toughness of weld metal.
（問題点の解決手段）
この発明は２２Ｃｒ −！＋、５Ｎｉ −３Ｍｏ Ｌ−
Ｎ系２相ステンレス鋼のサブマージアーク溶接を行う際
に、
Ｃ≦ ０．０３０ｗｔ％
３ｉ≦１．０ ｗｔ％
ＭｎＳ２．０ ｗｔ％
Ｐ ６０．０３０ｗｔ％
Ｓ ６０．０２０ｗｔ％
Ｎｉ ： ８．０〜１１．５ｗｔ％Ｃｒ ： ２
１．０〜２４．０ｗｔ％Ｍｏ ： ２．５〜４．０
ｗｔ％
Ｎｉ ： ０．０８ 〜０．２５ ｗｔ％残部が
Ｆｅど不可避的不純物からなる溶接電極に、ＣａＦ２含
有量が４０〜７０ｗｔ％で、かつＳｉ ０２を５〜２５
Ｗ（％
ＣａＯ及び又はＭａＯをそれらの合計にて５へ一２５ｗ
ｔ％
ＡＪ２２０３は１０〜３０Ｗ［％
の組成になる溶接用フラックスを組み合わせて用いるこ
とを特徴と丈る２相ステンレス鋼のサブマージアーク溶
接方法である。(Means for solving the problem) This invention provides 22Cr −! +, 5Ni-3Mo L-
When performing submerged arc welding of N-based duplex stainless steel, C≦0.030wt% 3i≦1.0 wt% MnS2.0 wt% P 60.030wt% S 60.020wt% Ni: 8.0 to 11 .5wt%Cr: 2
1.0~24.0wt%Mo: 2.5~4.0
wt% Ni: 0.08 to 0.25 wt% A welding electrode with the balance consisting of unavoidable impurities such as Fe has a CaF2 content of 40 to 70 wt% and a SiO2 content of 5 to 25 wt%.
W (% CaO and/or MaO in their total to 5 - 25 w
t% AJ2203 is a submerged arc welding method for duplex stainless steel characterized by the use of a combination of welding fluxes having a composition of 10 to 30 W [%].
さて一般に、２２０ｒ ’ ５．５Ｎ ｉ −３Ｍ、０
−Ｎ系２相ステンレス鋼は、溶体化処理を施すことによ
つＣ１γ／αの相比はほぼ５０／ ５０を呈し、じん性
および耐食性とも良好な特性をもつ。−しかしながらこ
れと共金糸の溶接金属は通常、７、フイ１１．ッ’ｙｏ
ｍ□９゜、。、６〜６− ）素置が６００〜１ｏｏ
ｏｐｐｍ程度含有しているので、すでに触れたように溶
接金属のしん竹が、ｆｒＪ ＋Ｊに比べて著しく劣化し
Ｃいる。Now, in general, 220r' 5.5N i -3M, 0
-N-based duplex stainless steel exhibits a C1γ/α phase ratio of approximately 50/50 through solution treatment, and has good properties in both toughness and corrosion resistance. - However, the welding metal of this and the same metal thread is usually 7, 11. t'yo
m□9゜. , 6~6-) The arrangement is 600~1oo
As mentioned above, since the weld metal contains about oppm C, the weld metal shintake deteriorates significantly compared to frJ +J.
したがってこの発明ｅは、溶接金属についての相バラン
スの調整および酸素ｍの低減によつ（、溶接ままの溶接
金属のしん性向上を上に述べた溶接用の電極とフラック
スの組合わけ使用をもつで安定に実現する。Therefore, this invention (e) improves the toughness of as-welded weld metal by adjusting the phase balance of the weld metal and reducing oxygen m (by using a combination of the welding electrode and flux described above). This is achieved stably.
まず発明を導いた実験について説明を進める。First, I will explain the experiment that led to the invention.
さて第１図には、Ｃ：０．００７〜０．０１０ｗｔ％。Now, in FIG. 1, C: 0.007 to 0.010 wt%.
Ｓ ｉ ： ０．１９〜０．２２ ｗｔ％、 Ｍｎ
： Ｌ５〜１．５２ ’Ｗ（％、 Ｐ ： ０
．００／Ｉ〜０．００５ｗｔ％、 Ｓ： ０．００１
ｗｔ％。Si: 0.19-0.22 wt%, Mn
: L5~1.52'W(%, P: 0
．． 00/I~0.005wt%, S: 0.001
wt%.
Ｃｒ ： ２３．３〜２３．５ｗｔ ％ 、
Ｍｏ 二 ３．２−３．３ｗｔ ％ 。Cr: 23.3-23.5wt%,
Mo2 3.2-3.3wt%.
Ｎ：０．１１〜０．１２ ｗｔ％のベース成分において
、Ｎ１含有伝のみ異なる溶接用電極を使用し、８ｍｍ
、９０’ ｙ溝囲先内を２電極サブンージアーク溶接し
て得られた溶接金属にお（プるγ量の変化を示す。この
溶接実験に用いたフラックスは、溶接金属中の酸素間を
低減さゼる溶接用フラックス、６０％ＣａＦ２−１０％
Ｓ！’０ｚ−１０％ＣａＱ−’２０％ＡＪ２２０３ 、
および溶接金属中の酸素量をと（に低減させる効果を有
しない溶接用フラックス、２０％ＣａＦ２−２５％Ｓｉ
０２−２０％Ｃａｂ−３０％ＡＪ２２’０３の両者Ｃ
あり、各々の溶接金属中の酸素量は３４０〜３８０ｐｐ
ｍおよび７５０〜８００ｐｐＨｌである。With a base component of N: 0.11 to 0.12 wt%, a welding electrode that differs only in N1 content was used, and the welding electrode was 8 mm.
, shows the change in the amount of γ applied to the weld metal obtained by two-electrode subundial arc welding inside the 90' Y-groove. Zeru welding flux, 60%CaF2-10%
S! '0z-10%CaQ-'20%AJ2203,
and a welding flux that does not have the effect of reducing the amount of oxygen in the weld metal to (20%CaF2-25%Si)
02-20%Cab-30%AJ22'03 both C
Yes, the amount of oxygen in each weld metal is 340 to 380 pp
m and 750-800 ppHl.
電極中のＮ；がの増加につれて溶接金属の１ｍも増加す
る。As the amount of N in the electrode increases, the amount of weld metal increases by 1 m.
第２図（Ｊ溶接金属中のＮｉ鵠を変化させたことに由来
するγ苗とじん性との関係を示すが、いずれのフラック
スを用いた場合においても溶接金属中のγ量の増加とと
もに溶接金属のしん性も増加りることがわかる。Figure 2 (shows the relationship between γ seedlings and toughness derived from changing the Ni content in the weld metal). It can be seen that the toughness of the metal also increases.
しかるに、寒冷地においても十分なしん性値、寸なわら
一４０℃にて１０ｋｇ−ｍ以上のしん性値を有する溶接
金属を得るためには、溶接金属中の酸素間を低減しうる
溶接フラックスを用い、かつ溶接金属のγ量を４０％以
上にする必要があり、そのためには８．０％以上のＮｉ
を含有する溶接電極を使用する必要がある。一方、溶接
金属のγ量が６０％を越えると耐食性が劣化し、そのた
め溶接電極Ｎ１含有母はＩＴ、５ｗｔ％以下にすること
が必要である。However, in order to obtain a weld metal that has a sufficient tenacity value even in cold regions, that is, a tenacity value of 10 kg-m or more at -40°C, it is necessary to use a welding flux that can reduce the oxygen content in the weld metal. In addition, it is necessary to make the γ content of the weld metal 40% or more, and for this purpose, it is necessary to use 8.0% or more Ni.
It is necessary to use a welding electrode containing On the other hand, if the γ content of the weld metal exceeds 60%, the corrosion resistance will deteriorate, and therefore the welding electrode N1-containing matrix must be IT, 5 wt% or less.
次にＣｒは６１食性を向上さけるための重要ｔ「元素で
あり、厳しい腐食環境においてし優れた耐食性を確保す
るためには２１ｗｔ％以上必要ぐある。Next, Cr is an important element to avoid improving corrosion resistance, and 21 wt% or more is required to ensure excellent corrosion resistance in a severe corrosive environment.
しかしＣｒ量が２４ｗｔ％をこえて過剰になると電極製
造時の熱間加工性が著しく劣化すると同時に、溶接金属
フェライト量が増加するため上記のγ、／αバランスを
調整するにはさらにＮｉ量を増加づる必要がありコスト
高になるので、Ｃｒ含有量は２１．０〜２４．０ｗｔ％
とした。However, if the amount of Cr exceeds 24wt% and becomes excessive, hot workability during electrode manufacturing will be significantly degraded, and at the same time, the amount of weld metal ferrite will increase. Since it is necessary to increase the Cr content, which increases the cost, the Cr content is 21.0 to 24.0 wt%.
And so.
またＭｏは耐食性向上に最も有効な元素であり、その効
果を発揮させるためには２．５ｗｔ％以上の添加が必要
であるが、４ｗｔ％を越えて添加すると電極製造時の熱
間加工性が著しく劣化するためＭｏ含有量は２．５〜４
．０ｗｔ％とした。Furthermore, Mo is the most effective element for improving corrosion resistance, and it is necessary to add 2.5 wt% or more in order to achieve its effect, but if it is added in excess of 4 wt%, hot workability during electrode manufacturing will deteriorate. The Mo content is 2.5 to 4 because it deteriorates significantly.
．． It was set to 0 wt%.
ざらにＮもまた耐食性向上効果を有するが０．０８ Ｊ
％未満では効果が期待できず、反面０．２５ ｗｔ％を
こえて含有すると、溶接金属にブローホールが発生ずる
ためＮ含有量は０．０８〜０．２５ ｗｔ％とした。Zarani N also has the effect of improving corrosion resistance, but at 0.08 J
If the N content is less than 0.25 wt%, no effect can be expected, whereas if the N content exceeds 0.25 wt%, blowholes will occur in the weld metal.
次にＣは粒界にＯｒ炭化物を形成して局部的に耐食性向
上に有害なＣｒの欠乏層を形成し゛粒界腐食を起こづた
め、Ｃの含有量は０．０３０ｗｔ％以下とした。Next, C forms Or carbides at grain boundaries, locally forming a Cr-depleted layer that is harmful to improving corrosion resistance and causing intergranular corrosion, so the C content was set to 0.030 wt% or less.
そしＵ３ｉおよびＭｌｌは溶接金属の１１１２酸に有効
な元素であるが、それぞれ１，０ｗｔ％および２，０ｗ
ｔ％を越えで添加するど溶接金属の延性および靭性を劣
化さけるため、Ｓ１含有量は１．０ｗｔ％以下、Ｍｌｌ
含右量は２．０ｗｔ％以下に制限した。U3i and Mll are effective elements for the 1112 acid of weld metal, but they are 1,0 wt% and 2,0 wt%, respectively.
In order to avoid deterioration of the ductility and toughness of the weld metal if added in excess of t%, the S1 content should be 1.0wt% or less, Mll
The content was limited to 2.0 wt% or less.
ＰおよびＳは溶接時の高温割れ感受性を高める元素であ
り、まＩＣさらにＳは、電極製造時の熱間加工性を著し
く劣化させるため、ＰおよびＳ含有量はそれぞれ０．０
３０ｗｔ％以下および０．０２０ｗｔ％以下とした。P and S are elements that increase hot cracking susceptibility during welding, and S also significantly deteriorates hot workability during electrode manufacturing, so the P and S contents are each 0.0.
30 wt% or less and 0.020 wt% or less.
次に溶接金属中の酸素量を低減させるのに付与する溶接
用フラックスの組成に関し、Ｓｉ ０２−ｃａｏ、−Ａ
ｌ１２０３系溶融型フラツクスを使用して塩基度と溶接
金属中の酸素量との関係について検問した結果、塩基度
の上昇によって、酸素量を −低減することは可
能であるが、溶接作業性とくに溶接スラブの剥離性に問
題があり、実用１イ１に欠くことが判明した。Next, regarding the composition of the welding flux applied to reduce the amount of oxygen in the weld metal, Si 02-cao, -A
As a result of investigating the relationship between basicity and oxygen content in weld metal using l1203 series melting flux, it was found that it is possible to reduce the oxygen content by increasing basicity, but welding workability, especially welding It was found that there was a problem with the peelability of the slab and that it was not practical.
そこでＣａ Ｆ２−３ｉ ０２−Ｃａ Ｏ−Ｍ（Ｉ Ｏ
−Ａｌ２２０３系溶融型フラツクスを使用して、フラッ
クス中ＣａＯ含有量と溶接湾屈中の酸素量との関係を調
査した結果、とくにＣａＦ２を４０ｗｔ％以上含有する
ことによって溶接金属中の酸素量を著しく低減すること
が可能であり、反面、Ｃａ１−２含有量が７０ｗｔ％を
こえるとやはり溶接スラブの剥離性およびビード形状←
悪影響を及ぼすことが判゛明した。Therefore, Ca F2-3i 02-Ca OM(IO
- Using Al2203-based molten flux, we investigated the relationship between the CaO content in the flux and the amount of oxygen in the weld bend, and found that by containing 40 wt% or more of CaF2, the amount of oxygen in the weld metal was significantly reduced. On the other hand, if the Ca1-2 content exceeds 70wt%, the peelability of the welding slab and the bead shape may be affected.
It was found that this had a negative effect.
以上の解明に基いてＣａＦ２含有量を４０〜７０ｗｔ％
に限定した。Based on the above clarification, the CaF2 content was set at 40 to 70 wt%.
limited to.
また、ＳｉＯ２，ＣａＯおよびＭ（１０は、何れもビー
ド足止端部の足並みを整えるのに有効であるが、Ｓｉ
０２が５ｗｔ％未満そしＵＣａＯ及び又はＭ（１０はそ
れらの合計間にて５’ｗｔ％未渦のとき、何れも上記効
果は薄い。また２０ｗｔ％を越えるＳｉ ０２を含有す
ると、ＣａＦ２と反応して５ＩＦ４なる刺激臭ガスを発
生するためＳｉＯ２含有量は２０ｗｔ％以下に限定され
、そしＣ，（：ａ Ｑ及び又はＭｏｏｂ合占１伊が２０
ｗｔ％を越えると、スラブかすの焼付きが生じたためこ
れらの合計含有量は、２０ｗｔ％以下に限定される。In addition, SiO2, CaO, and M (10) are all effective for adjusting the alignment of the bead toe end, but Si
When 02 is less than 5wt% and UCaO and/or M (10 is 5'wt% unvortexed), the above effects are weak.Also, if Si02 is contained in excess of 20wt%, it reacts with CaF2. The SiO2 content is limited to 20wt% or less because it generates a pungent odor gas called 5IF4.
If it exceeds wt%, burning of slab residue occurs, so the total content of these is limited to 20 wt% or less.
Ａβ２０３はビードの波目を整えるのに有効であるが、
１０ｗｔ％未満では効果薄であり、３０ｗｔ％を越える
とビード表面にビットが生じ、ビード外観を害するため
、へβ２０３含有量は１０ｗｔ％以上、３０ Ｗ ｔ％
以下に限定した。Aβ203 is effective in adjusting the wavy pattern of beads, but
If it is less than 10 wt%, the effect is weak, and if it exceeds 30 wt%, bits will appear on the bead surface and the appearance of the bead will be damaged.
Limited to the following.
（実施例）
表１に示１組成により１０５０°Ｃ９２４分間の溶体化
処理を経て得られた板厚１４．２７ｍｍのステンレス鋼
板によりＵＯＥバイブのシーム溶接を実施した。(Example) Seam welding of a UOE vibrator was performed using a stainless steel plate with a thickness of 14.27 mm obtained through solution treatment at 1050° C. for 924 minutes with the composition shown in Table 1.
表２および表３に溶接用の電極組成およびフラックス組
成を示し、第３図に間先形゛状イし−Ｃ表４には溶接条
件を示す。Tables 2 and 3 show the electrode compositions and flux compositions for welding, Figure 3 shows the tip shape, and Table 4 shows the welding conditions.
表 ２
表 ３
表 ４
表５−に溶接金属の化学組成を示づが、酸素量は３５０
１）ｐｍで低値を示し、また溶接金属のγ量は４７〜５
３％であつｌＣ０
表 ５
表 ６
表６に比較例をも含めて実施例のしん付値を示す。この
発明による溶接金属はγ相増量および酸素量低減によっ
て良好なしん付値を示した。Table 2 Table 3 Table 4 Table 5 shows the chemical composition of the weld metal, and the oxygen content is 350.
1) Shows a low value in pm, and the amount of γ in the weld metal is 47 to 5
3% lC0 Table 5 Table 6 Table 6 shows the damping values of the examples including the comparative examples. The weld metal according to the present invention showed a good braking value due to an increase in the amount of γ phase and a decrease in the amount of oxygen.
この発明によると溶接作業性も良好であり、たとえばＵ
ＯＥパイプ製造のためのシーム溶接において、工業的な
使用に十分耐えうろことが確認された。According to this invention, welding workability is also good, for example, U
It has been confirmed that the product can withstand industrial use in seam welding for OE pipe manufacturing.
【図面の簡単な説明】
第１図は、２２Ｃｒ−３Ｍｏ −Ｎ系２相ステンレス鋼
溶接電極中のＮｉ含有量と溶接金属のオースアナイｌ−
ωとの関係を示すグラフ、
である。
特許出願人 川崎製鉄株式会社
第１図
゛ 簿オ要覧オ８中のＮｉ量（％）第２図
溶鐸金尾のオーステナイト量ｃ％ン
第３図[Brief Description of the Drawings] Figure 1 shows the Ni content in a 22Cr-3Mo-N duplex stainless steel welding electrode and the austenitic content of the weld metal.
This is a graph showing the relationship with ω. Patent Applicant: Kawasaki Steel Corporation Figure 1 Ni content (%) in the book and directory O8 Figure 2 Austenite content c% of youtaku Kanao Figure 3
Claims (1)
ス鋼のサブマージアーク溶接を行う際に、Ｃ≦０．０３
０ｗｔ％ Ｓｉ≦１．０ｗｔ％ Ｍｎ≦２．０ｗｔ％ Ｐ≦０．０３０ｗｔ％ Ｓ≦０．０２０ｗｔ％ Ｎｉ：８．０〜１１．５ｗｔ％ Ｃｒ：２１．０〜２４．０ｗｔ％ Ｍｏ：２．５〜４．０ｗｔ％ Ｎ：０．０８〜０．２５ｗｔ％ 残部がＦｅと不可避的不純物からなる溶接電極に、Ｃａ
Ｆ＿２含有量が４０〜７０ｗｔ％で、かつＳｉＯ＿２を
５〜２５ｗｔ％ ＣａＯ及び／又はＭｇＯをそれらの合計にて５〜２５ｗ
ｔ％ Ａｌ＿２Ｏ＿３は１０〜３０ｗｔ％ の組成になる溶接用フラックスを組み合わせて用いるこ
とを特徴とする２相ステンレス鋼のサブマージアーク溶
接方法。[Claims] 1. When performing submerged arc welding of 22Cr-5.5Ni-3Mo-N duplex stainless steel, C≦0.03.
0wt% Si≦1.0wt% Mn≦2.0wt% P≦0.030wt% S≦0.020wt% Ni: 8.0-11.5wt% Cr: 21.0-24.0wt% Mo: 2. 5 to 4.0 wt% N: 0.08 to 0.25 wt% Ca
F_2 content is 40 to 70 wt%, and SiO_2 is 5 to 25 wt% CaO and/or MgO is 5 to 25 w in total
A submerged arc welding method for duplex stainless steel, characterized in that t% Al_2O_3 is used in combination with a welding flux having a composition of 10 to 30 wt%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP13184084A JPS6114097A (en) | 1984-06-28 | 1984-06-28 | Submerged arc welding method of two-phase stainless steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP13184084A JPS6114097A (en) | 1984-06-28 | 1984-06-28 | Submerged arc welding method of two-phase stainless steel |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS6114097A true JPS6114097A (en) | 1986-01-22 |
Family
ID=15067326
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP13184084A Pending JPS6114097A (en) | 1984-06-28 | 1984-06-28 | Submerged arc welding method of two-phase stainless steel |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6114097A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH05120653A (en) * | 1991-10-24 | 1993-05-18 | Sankyo Seiki Mfg Co Ltd | Magnetic head and production thereof |
| CN109967918A (en) * | 2017-12-27 | 2019-07-05 | 株式会社神户制钢所 | The submerged arc welding bonded flux of two phase stainless steel |
| CN111843132A (en) * | 2020-08-07 | 2020-10-30 | 江南造船(集团)有限责任公司 | Submerged arc welding process for 304L stainless steel thick plate |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5080941A (en) * | 1973-11-22 | 1975-07-01 | ||
| JPS57118893A (en) * | 1981-01-14 | 1982-07-23 | Kawasaki Steel Corp | Submerged arc welding method for ni-contg. ultra-low temperature steel |
| JPS5893593A (en) * | 1981-11-27 | 1983-06-03 | Sumitomo Metal Ind Ltd | Welding material for high chromium low nickel two phase stainless steel |
-
1984
- 1984-06-28 JP JP13184084A patent/JPS6114097A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5080941A (en) * | 1973-11-22 | 1975-07-01 | ||
| JPS57118893A (en) * | 1981-01-14 | 1982-07-23 | Kawasaki Steel Corp | Submerged arc welding method for ni-contg. ultra-low temperature steel |
| JPS5893593A (en) * | 1981-11-27 | 1983-06-03 | Sumitomo Metal Ind Ltd | Welding material for high chromium low nickel two phase stainless steel |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH05120653A (en) * | 1991-10-24 | 1993-05-18 | Sankyo Seiki Mfg Co Ltd | Magnetic head and production thereof |
| CN109967918A (en) * | 2017-12-27 | 2019-07-05 | 株式会社神户制钢所 | The submerged arc welding bonded flux of two phase stainless steel |
| KR20190079532A (en) | 2017-12-27 | 2019-07-05 | 가부시키가이샤 고베 세이코쇼 | Bonded flux for submerged arc welding of duplex stainless steel |
| CN111843132A (en) * | 2020-08-07 | 2020-10-30 | 江南造船(集团)有限责任公司 | Submerged arc welding process for 304L stainless steel thick plate |
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