JPH0481291A - Submerged arc welding wire - Google Patents
Submerged arc welding wireInfo
- Publication number
- JPH0481291A JPH0481291A JP19445490A JP19445490A JPH0481291A JP H0481291 A JPH0481291 A JP H0481291A JP 19445490 A JP19445490 A JP 19445490A JP 19445490 A JP19445490 A JP 19445490A JP H0481291 A JPH0481291 A JP H0481291A
- Authority
- JP
- Japan
- Prior art keywords
- welding
- wire
- content
- overlay
- steel
- 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.)
- Granted
Links
- 238000003466 welding Methods 0.000 title claims abstract description 64
- 239000000463 material Substances 0.000 claims abstract description 27
- 239000000126 substance Substances 0.000 claims abstract description 21
- 239000000843 powder Substances 0.000 claims abstract description 20
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 18
- 239000010959 steel Substances 0.000 claims abstract description 18
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 17
- 229910001209 Low-carbon steel Inorganic materials 0.000 claims abstract description 8
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 6
- 239000002184 metal Substances 0.000 claims description 54
- 229910052751 metal Inorganic materials 0.000 claims description 54
- 229910052742 iron Inorganic materials 0.000 claims description 2
- 229910052799 carbon Inorganic materials 0.000 abstract description 3
- 238000012856 packing Methods 0.000 abstract 1
- 238000005336 cracking Methods 0.000 description 28
- 239000010410 layer Substances 0.000 description 17
- 239000000203 mixture Substances 0.000 description 17
- 230000007547 defect Effects 0.000 description 12
- 238000000034 method Methods 0.000 description 10
- 238000012360 testing method Methods 0.000 description 10
- 230000004907 flux Effects 0.000 description 9
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 7
- 229910000851 Alloy steel Inorganic materials 0.000 description 6
- 229910052720 vanadium Inorganic materials 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 239000010953 base metal Substances 0.000 description 3
- 238000001514 detection method Methods 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 238000009826 distribution Methods 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 238000002474 experimental method Methods 0.000 description 3
- 238000011835 investigation Methods 0.000 description 3
- 230000035945 sensitivity Effects 0.000 description 3
- 239000002344 surface layer Substances 0.000 description 3
- 238000000137 annealing Methods 0.000 description 2
- 239000011324 bead Substances 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 230000004927 fusion Effects 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 238000009863 impact test Methods 0.000 description 2
- 239000011229 interlayer Substances 0.000 description 2
- 239000006249 magnetic particle Substances 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 229910052750 molybdenum Inorganic materials 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 238000005491 wire drawing Methods 0.000 description 2
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- 241001391944 Commicarpus scandens Species 0.000 description 1
- 229910000616 Ferromanganese Inorganic materials 0.000 description 1
- 229910000519 Ferrosilicon Inorganic materials 0.000 description 1
- 235000016623 Fragaria vesca Nutrition 0.000 description 1
- 240000009088 Fragaria x ananassa Species 0.000 description 1
- 235000011363 Fragaria x ananassa Nutrition 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 102100034184 Macrophage scavenger receptor types I and II Human genes 0.000 description 1
- 101710134306 Macrophage scavenger receptor types I and II Proteins 0.000 description 1
- -1 Si: 0.3% or less Substances 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 239000010962 carbon steel Substances 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000008021 deposition Effects 0.000 description 1
- 238000010790 dilution Methods 0.000 description 1
- 239000012895 dilution Substances 0.000 description 1
- 238000001125 extrusion Methods 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 238000007542 hardness measurement Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 238000007689 inspection Methods 0.000 description 1
- DALUDRGQOYMVLD-UHFFFAOYSA-N iron manganese Chemical compound [Mn].[Fe] DALUDRGQOYMVLD-UHFFFAOYSA-N 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 238000011056 performance test Methods 0.000 description 1
- 238000010248 power generation Methods 0.000 description 1
- 230000002265 prevention Effects 0.000 description 1
- 230000005855 radiation Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 231100000817 safety factor Toxicity 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- 230000037303 wrinkles Effects 0.000 description 1
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は」２％Ｃｒ鋼製蒸気タービンロータシャフトに
おけるジャーナル部の肉盛溶接材料に関する。DETAILED DESCRIPTION OF THE INVENTION (Field of Industrial Application) The present invention relates to a welding material for overlaying a journal portion of a 2% Cr steel steam turbine rotor shaft.
（従来の技術）
火力発電機に使用される蒸気タービンロータシャフトは
、近年、発電効率向上を図るために高い蒸気温度のもと
で使用される傾向がある。これに伴い、使用温度に耐え
る材料として、クリープ強度の高い、いわゆる１２％Ｃ
ｒ鋼がしばしば適用されている。(Prior Art) In recent years, steam turbine rotor shafts used in thermal power generators tend to be used at high steam temperatures in order to improve power generation efficiency. Along with this, so-called 12%C, which has high creep strength, is being used as a material that can withstand usage temperatures.
r steel is often applied.
しかしながら、１２％Ｃｒ鋼のタービンロータシャフト
は、低合金鋼のものに比べて、軸受特性が劣ることから
、使用中にジャーナル部が焼付きを起こし易いという問
題がある。これを防止するため、ジャーナル部に低合金
鋼のスリーブを焼きばめしたタイプのタービンロータシ
ャフトが実用化されているが、このタイプのタービンロ
ータシャフトは、使用中、焼きばめ部が緩み、ガタッキ
が生じるという問題が残されている。このような背景か
ら、最近、ジャーナル部に低合金鋼を肉盛溶接する技術
が検討され、一部実用化されている模様である。However, a turbine rotor shaft made of 12% Cr steel has poorer bearing characteristics than one made of low-alloy steel, so there is a problem in that the journal portion tends to seize during use. To prevent this, a type of turbine rotor shaft with a low-alloy steel sleeve shrink-fitted to the journal part has been put into practical use, but the shrink-fit part of this type of turbine rotor shaft loosens during use. There remains the problem that looseness occurs. Against this background, a technique for overlaying low-alloy steel on the journal portion has recently been studied and appears to have been put into practical use in some cases.
（発明が解決しようとする課題）
ジャーナル部に肉盛溶接を施すタービンロータシャフト
或いは肉盛材料については、特開昭５５−１６７４４号
、特開昭５６−１９９７６号、特開昭５７−１３７４５
６号などに提案されているものがあるが、それぞれ次の
ような理由により、充分満足できる肉盛部が得られない
。(Problems to be Solved by the Invention) Regarding the turbine rotor shaft or overlay material for applying overlay welding to the journal portion, Japanese Patent Application Laid-Open No. 55-16744, JP-A No. 56-19976, and JP-A No. 57-13745 are disclosed.
Although some methods have been proposed, such as No. 6, a fully satisfactory built-up part cannot be obtained for the following reasons.
特開昭５５−１６７４４号：
２層目以降の肉盛溶接棒として、Ｃ：０．１〜０゜３％
、Ｓｉ：０．３％以下、Ｍｎ：１．５−２．０％、Ｃｒ
：０．０５−０．１％、Ｐ：０．０３％以下、Ｓ二０．
０３％以下の成分のものが挙げられている。JP-A-55-16744: C: 0.1 to 0°3% as overlay welding rod for second and subsequent layers
, Si: 0.3% or less, Mn: 1.5-2.0%, Cr
: 0.05-0.1%, P: 0.03% or less, S20.
0.3% or less of ingredients are listed.
しかしながら、Ｃについては、０．３％の溶接棒では溶
接金属の高温割れを防止することは困難である。一方、
Ｃが０．１％では、他の合金元素との関連から溶接金属
の強度が不足する。勿論、１２％Ｃｒ鋼母材の稀釈が比
較的多い肉盛下層では、母材からＣｒが溶接金属に補給
されることが考えられるが、このような層は高Ｃｒであ
ることから、軸受特性が不満足となる。また、ジャーナ
ル部における肉盛部は、通常１０ｍｍ以上と、比較的厚
い肉盛厚さが要求されるため、肉盛表層では母材からの
成分補充は期待できないことから、前述の強度不足を生
じることは避けられない。したがって、このような成分
組成の溶接棒では、強度不足や溶接金属の高温割れが生
じ、満足な肉盛溶接部が得られない。However, with regard to C, it is difficult to prevent hot cracking of the weld metal with a welding rod containing 0.3%. on the other hand,
If C is 0.1%, the strength of the weld metal will be insufficient due to the relationship with other alloying elements. Of course, in the lower layer of overlay where the dilution of the 12% Cr steel base metal is relatively high, it is possible that Cr is replenished from the base metal to the weld metal, but since such a layer is high in Cr, the bearing characteristics becomes unsatisfied. In addition, since the build-up part in the journal part is required to have a relatively thick build-up thickness of 10 mm or more, the build-up surface layer cannot be expected to replenish components from the base material, resulting in the aforementioned lack of strength. That is inevitable. Therefore, with a welding rod having such a chemical composition, insufficient strength and hot cracking of the weld metal occur, making it impossible to obtain a satisfactory overlay weld.
特 昭５６−１９９７６°：
溶接肉盛材における低合金鋼の化学成分については、高
温割れは発生しにくい組成になっているものの、Ｃ含有
量が低いことから、溶接金属の強度が不足する。炭素鋼
についても同様であり、通常の肉盛厚さを必要とする場
合、特に問題となる。Special 1987-19976: Although the chemical composition of low alloy steel in weld overlay materials is such that hot cracking is unlikely to occur, the strength of the weld metal is insufficient due to the low C content. The same applies to carbon steel, which is particularly problematic when a normal build-up thickness is required.
また、肉盛部のＣｒ量を５％以内を目標としているが、
焼付きの面からは過剰であり、より低いレベルに抑えな
いと問題となる。In addition, the target is to keep the Cr content in the build-up part within 5%.
This is excessive in terms of burn-in and will become a problem unless it is reduced to a lower level.
５７−１３７４５６号：
Ｃ：０．０５〜０．３５％、Ｓｉ：０．１０〜１．００
％、Ｍｎ：０．１０−１．００％、Ｃｒ：０．３０−２
．８０％、Ｍｏ：０．１０〜２．００％、Ｖ：Ｏ，Ｏ５
〜０．３５％、Ｎｉ：０．５０〜４．００％、残部：鉄
からなる肉盛合金を軸受部に肉盛溶接する方法が示され
ているが、Ｃが含有量の範囲が広いことから、０．０５
％では実際には強度不足となり、一方、０．３５％では
溶接金属の高温割れは避けられない。また、Ｃｒ含有量
についても、０．３０％では強度不足が生じ、２．８０
％と高いと、充分な軸受特性が発揮されない危険性があ
る。更に、■を含有しているが、例えば、溶接金属の化
学成分が上記範囲内であるｃ：０．２５％、Ｃｒ： １
、２％、Ｍｏ：１．５％、Ｖ：０．３％といった組成
を想定した場合、高温割れもさることながら、ＳＲ割れ
感受性が極めて高い成分系であることがら、ＳＲ割れ発
生の危険性が高くなる。No. 57-137456: C: 0.05-0.35%, Si: 0.10-1.00
%, Mn: 0.10-1.00%, Cr: 0.30-2
．． 80%, Mo: 0.10-2.00%, V: O, O5
A method of overlay welding an overlay alloy consisting of ~0.35% Ni, 0.50~4.00% Ni, and the balance iron to the bearing part is shown, but the C content ranges widely. From, 0.05
% actually results in insufficient strength, while at 0.35% hot cracking of the weld metal is unavoidable. Also, regarding the Cr content, 0.30% causes insufficient strength, and 2.80%
If it is as high as %, there is a risk that sufficient bearing characteristics will not be exhibited. Furthermore, it contains ■, but for example, the chemical composition of the weld metal is within the above range c: 0.25%, Cr: 1
, 2%, Mo: 1.5%, V: 0.3%, there is a risk of SR cracking as the composition is extremely susceptible to SR cracking as well as high temperature cracking. becomes higher.
叙上のように、従来のジャーナル部における肉盛溶接金
属或いは肉盛溶接材料は、溶接部の高温割れ防止、強度
の確保、軸受特性の確保、更にはＳＲ割れ防止の面で充
分検討されたものとは云えず、健全かつ高品質のタービ
ンロータシャツ１−・ジャーナル部肉盛技術として完成
されていないのが現状である。As mentioned above, the conventional overlay weld metal or overlay welding material for the journal part has been thoroughly studied in terms of preventing hot cracking of the weld, ensuring strength, ensuring bearing characteristics, and further preventing SR cracking. Unfortunately, the current state of the art is that a sound and high-quality turbine rotor shirt/journal overlay technology has not been perfected.
本発明は、か−る状況のもとでなされたものであって、
１２％Ｃｒ鋼製蒸気タービンロータシャフト・ジャーナ
ル部の肉盛溶接技術において、高温割れ、ＳＲ割れが発
生せず、かつジャーナル部に充分な強度及び軸受特性を
付与し得る溶接材料を提供することを目的とするもので
ある。The present invention was made under such circumstances, and
An object of the present invention is to provide a welding material that does not cause hot cracking or SR cracking and can impart sufficient strength and bearing properties to the journal part in overlay welding technology for a 12% Cr steel steam turbine rotor shaft journal part. This is the purpose.
（課題を解決するための手段）
本発明者等は、前記課題を解決するために、まず、溶接
材料について検討した。(Means for Solving the Problems) In order to solve the above problems, the inventors first studied welding materials.
すなわち、１２％Ｃｒ鋼製蒸気タービンロータシャフト
におけジャーナル部の肉盛量は、１本当り２００〜３０
０ｋｇ程度であり、この量詮仮りに５ｋｇ／ｈｒの溶着
速度条件で溶接すると、４０〜６Ｏ−ｈｒのアーク時間
となる。このような肉盛量ＧＭＡ（ガスメタルアーク）
溶接で行うとすると、短時間でシールドノズルにスパッ
タが付着し、シールド性が劣化するため、頻繁にアーク
を停止し、清掃する必要が生じる。これは、溶接能率の
低下のみならず、ビード継ぎ個所（欠陥が発生し易い個
所である）の増加に伴う欠陥発生機会の増加につながる
。また、１２％Ｃｒ鋼は低温割れ感受性が高いことから
、通常２００°Ｃ以上の予熱及び層間温度で溶接される
が、この加熱用熱源或いは本体からの放熱流によってア
ーク点のガスシールド性を損なうことがある。勿論、通
常外気からの風によってシールド性が劣化する危険性も
高い。In other words, the amount of build-up on the journal portion of a 12% Cr steel steam turbine rotor shaft is 200 to 30
If this amount were to be welded at a deposition rate of 5 kg/hr, the arc time would be 40 to 6 O-hr. This kind of overlay amount GMA (gas metal arc)
If welding is used, spatter will adhere to the shield nozzle in a short period of time and the shielding performance will deteriorate, making it necessary to frequently stop the arc and clean it. This not only reduces welding efficiency, but also increases the chance of defects occurring due to the increase in bead joint locations (locations where defects are likely to occur). In addition, since 12% Cr steel has a high sensitivity to cold cracking, it is usually welded with preheating and interlayer temperature of 200°C or higher, but the heat radiation from the heating heat source or the main body impairs the gas shielding property of the arc point. Sometimes. Of course, there is also a high risk that the shielding performance will deteriorate due to the wind from the outside air.
そこで、本発明者等は、溶接方法として、長時間の連続
溶接が可能で、かつ風、熱流の影響が少ないサブマージ
アーク溶接法を適用することにした。Therefore, the present inventors decided to apply a submerged arc welding method as a welding method, which allows continuous welding for a long time and is less affected by wind and heat flow.
次に、サブマージアーク溶接用ワイヤについて検討した
。Next, we investigated wire for submerged arc welding.
一般にサブマージアーク溶接用のワイヤとしては、いわ
ゆるソリッドワイヤが多く用いられているが、これは材
料の溶解→圧延（押出し）→伸線といった工程で製造さ
れ、伸線工程には焼鈍も含まれている。Ｃ含有量が通常
のものより高いものは伸線性が悪く、焼鈍回数を増す必
要があり、更に生産性が低下する。Generally, so-called solid wire is often used as wire for submerged arc welding, but this is manufactured through a process of melting the material → rolling (extrusion) → wire drawing, and the wire drawing process also includes annealing. There is. Wires with a higher C content than normal have poor wire drawability, require an increased number of annealing cycles, and further reduce productivity.
そこで、本発明者等は、軟鋼製シース内に合金成分を含
んだ金属粉を充填する、いわゆるコアドワイヤに着目し
、種々の溶接ワイヤを試作したうえで、溶接施工試験、
性能試験を推進した。Therefore, the present inventors focused on so-called cored wires, in which a mild steel sheath is filled with metal powder containing alloy components, and after prototyping various welding wires, welding tests and
Promoted performance testing.
その結果、特定の化学成分を有する溶接ワイヤをフラッ
クスと組合せて使用することにより、可能であることを
見出し、ここに本発明をなしたものである。As a result, it was discovered that this is possible by using a welding wire having a specific chemical composition in combination with a flux, and the present invention has been made based on this finding.
すなわち、本発明は、１２％Ｃｒ鋼製蒸気タービンロー
タシャフト・ジャーナル部の肉盛溶接材料において、軟
鋼製シース内に金属粉が充填されたコアドワイヤであっ
て、
（、）軟鋼製シースが
Ｃ：０．０２〜０．０４％
Ｓｉ：０．０１〜０．０３％
Ｍｎ：０．１−０．３％
Ｐ：０．０２０％以下
Ｓ：０．０１０％以下
残部：実質的にＦｅ
からなる化学成分を有し、
（ｂ）充填金属粉が
Ｃ：（０，１２〜０．２２）ｘ １００／Ｒ８ｉ：（０
，２５〜０．８０）ｘ １００／ＲＭｎ：（０．７〜２
．４）×１００／ＲＣｒ：（］、、２−１．７）Ｘｌ−
００／ＲＭｏ：（０，１〜０．５）Ｘ１００／Ｒ残部：
実質的にＦｅ
（但し、Ｒはワイヤ全重量当りの金属粉の重量％で、１
０％≦Ｒ≦３０％）
からなる化学成分を有することを特徴とする１２％Ｃ，
ｒｔｌＩｔ製蒸気タービンロータシャフト・ジャーナル
部の肉盛用サブマージアーク溶接ワイヤを要旨とするも
のである。That is, the present invention provides a cored wire in which a mild steel sheath is filled with metal powder in an overlay welding material for a steam turbine rotor shaft journal portion made of 12% Cr steel, wherein the mild steel sheath is C: 0.02-0.04% Si: 0.01-0.03% Mn: 0.1-0.3% P: 0.020% or less S: 0.010% or less Balance: Substantially composed of Fe (b) The filling metal powder is C: (0,12 to 0.22) x 100/R8i: (0
,25~0.80)x100/RMn:(0.7~2
．． 4)×100/RCr: (], , 2-1.7)Xl-
00/RMo: (0,1~0.5)X100/R remainder:
Substantially Fe (where R is the weight percent of metal powder based on the total weight of the wire, and 1
12%C, characterized by having a chemical component consisting of (0%≦R≦30%),
The gist of this article is a submerged arc welding wire for overlaying a steam turbine rotor shaft journal made by rtlIt.
以下に本発明を更に詳細に説明する。The present invention will be explained in more detail below.
（作用）
１２％Ｃｒ鋼製蒸気タービンロータシャフト・ジャーナ
ル部の肉盛溶接部に要求される特性としては、強度、靭
性及び軸受特性があるが、強度はＳＲ処理後の溶接金属
硬さによって判断でき、本発明が対象としているタービ
ンロータシャフトでは、ビッカース硬さ（Ｈｖ）で２０
０〜２６０の範囲が適正硬さである。(Function) The properties required for the overlay welded part of the 12% Cr steel steam turbine rotor shaft/journal part include strength, toughness, and bearing properties, but the strength is determined by the hardness of the weld metal after SR treatment. The turbine rotor shaft targeted by the present invention has a Vickers hardness (Hv) of 20
A range of 0 to 260 is an appropriate hardness.
軸受特性における耐焼付き性には、材料のＣｒ含有量が
主として影響し、Ｃｒ含有量が低い方が有利である。従
来のタービンロータシャツ１−においてジャーナル部の
焼付き事故が発生していないのは、実績として低合金鋼
のＣｒ−Ｍｏ−Ｖ鋼であり、３％或いは４％Ｃｒ材での
連続運転実績はない状況である。したがって、強度が確
保されることを前提とすれば、Ｃｒ含有量は従来の低合
金鋼製タービンロータシャフトのレベル、すなわち、１
．６％以下に抑える必要がある。The seizure resistance in bearing properties is mainly influenced by the Cr content of the material, and a lower Cr content is advantageous. In the conventional turbine rotor shirt 1-, the journal part seizing accident has not occurred with Cr-Mo-V steel, which is a low alloy steel, and there is a track record of continuous operation with 3% or 4% Cr material. There is no such situation. Therefore, assuming that the strength is maintained, the Cr content should be at the level of conventional low-alloy steel turbine rotor shafts, that is, 1
．． It is necessary to keep it below 6%.
更に、肉盛溶接部においては、融合不良、ブローホール
、低温割れ、高温割れ、ＳＲ割れといった欠陥が存在し
てはならない。特に高温割れについては、溶接ビードに
沿って円周上に連続して発生することから、強度特性を
著しく劣化させるため、特に注意を要する。Furthermore, defects such as poor fusion, blowholes, cold cracks, hot cracks, and SR cracks must not exist in the overlay weld. Particular attention must be paid to hot cracking, as it occurs continuously on the circumference along the weld bead and significantly deteriorates the strength properties.
以上のような必要特性に対して満足し得る溶接材料を見
出すに至った基礎実験について説明する。The basic experiments that led to the discovery of a welding material that satisfies the above-mentioned required properties will be explained.
まず、溶接欠陥のうち、特に注意を要する高温割れにつ
いて、本発明者等は、ｃ、ｓ、ｐ含有量を変化させた溶
接材料を試作し、サブマージアーク溶接を行い、溶接金
属の高温割れと成分組成との関係を調べた。First, among welding defects, hot cracking, which requires special attention, was investigated by the present inventors by prototyping welding materials with varying c, s, and p contents and performing submerged arc welding. The relationship with component composition was investigated.
第１表に試作溶接材料により得た溶接金属の化学成分を
示す。溶接試験板はＡ３８７ Ｇｒ、１１（１，２５Ｃ
ｒ〜０．５Ｍｏ鋼）の板厚５０ｍｍ鋼板にＶ形の溝開先
を施したものを用いた。溶接条件を第２表に示す。Table 1 shows the chemical composition of the weld metal obtained from the prototype welding material. The welding test plate is A387 Gr, 11 (1,25C
A 50 mm thick steel plate (r~0.5Mo steel) with a V-shaped groove groove was used. The welding conditions are shown in Table 2.
第１図（ａ）、（ｂ）はそれぞれ溶接金属のＣ含有量及
びＳ含有量と割れとの関係、並びにＣ含有量及びＰ含有
量と割れとの関係を示しものである。同図に示すように
、高温割れはＣ含有量によりほぼ一義的に影響され、Ｃ
含有量が０．１８％以上では割れが発生することがわか
る。また、Ｃ含有量が０．１７％では、Ｓ又はＰが高い
場合にのみ割れが発生する傾向がみられる。FIGS. 1(a) and 1(b) respectively show the relationship between the C content and S content of the weld metal and cracking, and the relationship between the C content and P content and cracking. As shown in the figure, hot cracking is almost uniquely affected by the C content;
It can be seen that cracks occur when the content is 0.18% or more. Furthermore, when the C content is 0.17%, cracks tend to occur only when S or P is high.
この結果から、溶接金属のＣ含有量は０．１７％以下と
する必要があり、Ｓ含有量は０．０１５％以下とし、Ｐ
含有量は０．０３％以下に抑えることが望ましいことが
判明した。From this result, the C content of the weld metal should be 0.17% or less, the S content should be 0.015% or less, and the P
It has been found that it is desirable to suppress the content to 0.03% or less.
次に、溶接金属の性能について、種々の溶接材料を試作
して調査した結果について示す。Next, we will discuss the results of investigating the performance of weld metal by making prototypes of various welding materials.
調査方法は、Ａ３８７ Ｇｒ、１１鋼板にそれぞれの溶
接材料で５層肉盛溶接したうえで、表層部から第２図に
示すＳＲ割れ試験片を採取すると共に、６５０℃Ｘ１５
ｈｒのＳＲ処理を施し、表層部から衝撃試験片及び硬さ
測定用の試験片を採取した。The investigation method was to perform 5-layer overlay welding on A387 Gr, 11 steel plate using each welding material, and then collect the SR crack test piece shown in Figure 2 from the surface layer.
SR treatment was performed for hr, and an impact test piece and a test piece for hardness measurement were taken from the surface layer.
ＳＲ割れ試験は、試験片のスリット部を圧着し、反対側
に位置する切欠底部を負荷した状態でＴＩＧｒａ接で固
定し、この試験片を６５０℃Ｘ２ｈｒのＳＲ処理を施し
た後、切欠底部におけるＳＲ割れの有無を調べる方法を
適用した。In the SR cracking test, the slit part of the test piece is crimped, the notch bottom located on the opposite side is fixed with TIGra contact under load, and the test piece is subjected to SR treatment at 650°C for 2 hours. A method was applied to check for the presence of SR cracks.
また、衝撃試験は、２ｍｍＶノツチのシャルピー試験に
よって行い、設計上の仕様及び安全率を加味して、常温
での吸収エネルギが４ｋｇｆ−ｍ以上有するものを合格
とした。溶接金属硬さはＨｖ＝２００〜２６０の範囲を
合格とした。The impact test was conducted using a Charpy test with a 2 mm V notch, and taking design specifications and safety factors into consideration, those with absorbed energy of 4 kgf-m or more at room temperature were considered to have passed. Weld metal hardness in the range of Hv=200 to 260 was considered acceptable.
第３表に各溶接材料で得られた溶接金属の化学成分と各
性能試験での判定結果を示す。その結果、以下のことが
判明した。Table 3 shows the chemical composition of the weld metal obtained with each welding material and the judgment results of each performance test. As a result, the following was found.
溶接金属のＣ含有量が０．１０％以下では禮さ不足とな
る。Ｓｉは０．２％以下では硬さが不足し、０．６％を
超えると靭性が劣化する。Ｍｎは１．０％未満では硬さ
が不足し、２．５％を超えると硬さが高くなりすぎると
共に靭性が不合格となる。If the C content of the weld metal is less than 0.10%, the weld metal will be insufficiently smooth. If Si is less than 0.2%, the hardness will be insufficient, and if it exceeds 0.6%, the toughness will deteriorate. If Mn is less than 1.0%, the hardness will be insufficient, and if it exceeds 2.5%, the hardness will be too high and the toughness will fail.
Ｃｒは１．０％以下では硬さが不足した。Ｍｏは焼もど
し軟化抵抗を高めるのに効果があり、この効果は０．１
％以上で発揮される。しかしながら、０．５％を超える
と、僅かのＶの共存により、ＳＲ割れ感受性が高くなり
、ＳＲ割れが発生した。When Cr was 1.0% or less, hardness was insufficient. Mo is effective in increasing the tempering softening resistance, and this effect is 0.1
% or more. However, when it exceeds 0.5%, SR cracking sensitivity increases due to the coexistence of a small amount of V, and SR cracking occurs.
ＶはＳＲ割れ感受性を著しく高めるため、０．０４％以
下に抑えるのが好ましい。Since V significantly increases SR cracking sensitivity, it is preferable to suppress it to 0.04% or less.
以上の基礎実験の結果並びに前述の高温割れ、軸受特性
との関連から、ジャーナル部における肉盛溶接部の最適
な化学成分は、以下のようなものであることが明らかと
なった。From the results of the above basic experiments and the relationship with the hot cracking and bearing characteristics described above, it has become clear that the optimal chemical composition of the overlay weld in the journal part is as follows.
Ｃ：０．１１〜０．１７％、Ｓｉ：０．２〜０．６％、
Ｍｎ：１．０−２．５％、 ｐ：ｏ、ｏ３％以下、Ｓ
：０．０１５％以下、 Ｃｒ：１．１−−１．６％、Ｍ
ｏ：０．１−０．５％、 Ｖ：０．０４％以下、残部
：実質的にＦｅ
【以下余白１
以上の知見に基づき、本発明者等は、上記要求性能を有
する肉盛溶接金属が得られる溶接材料として、コアドワ
イヤを開発したものである。なお、コアドワイヤは、ワ
イヤの成形性、生産性並びに溶接時の合金成分歩留りを
考慮したものでなければ実用に耐えないものであり、ま
た、材料の成分バラツキが少ないことも重要である。こ
れらの事項をも考慮した本発明ワイヤの構成及び作用に
ついて以下に説明する。C: 0.11-0.17%, Si: 0.2-0.6%,
Mn: 1.0-2.5%, p: o, o 3% or less, S
: 0.015% or less, Cr: 1.1--1.6%, M
o: 0.1-0.5%, V: 0.04% or less, balance: substantially Fe [Margin below 1] Based on the above findings, the present inventors have developed an overlay weld metal having the above-mentioned required performance. A cored wire has been developed as a welding material that provides the following. Note that a cored wire cannot be put into practical use unless consideration is given to wire formability, productivity, and yield of alloy components during welding, and it is also important that there be little variation in material components. The structure and operation of the wire of the present invention will be explained below, taking these matters into account.
軟鋼 シースのヒ学 ：
Ｃ：０．０２〜０．０４％、Ｓｉ：０．０１〜０．０３
％、Ｍｎ：０．１〜０．３％に規定した範囲のそれぞれ
の下限値は、シース素材が特に高コストとならない値で
あり、それぞれの下限値は、コアドヮイヤを製造する際
に断線や形状不良が発生せず、優れた成形性及び伸線性
を確保するための値である。Mild steel sheath properties: C: 0.02-0.04%, Si: 0.01-0.03
%, Mn: 0.1 to 0.3%, each lower limit value is a value that does not make the sheath material particularly expensive, and each lower limit value is a value that does not cause wire breakage or shape when manufacturing the core wire. This value is to ensure excellent moldability and wire drawability without causing any defects.
Ｐについては、Ｐはシース内に充填される金属粉原料及
び溶接時のフラックスからも溶接金属に浸入するため、
シースは０．０２０％以下のＰ含有量のものを使用しな
いと、溶接金属のＰ含有量を０．０３％以下に抑えるこ
とが難しい。したがって、シースのＰ含有量は０．０２
０％以下とする。Regarding P, since P also penetrates into the weld metal from the metal powder raw material filled in the sheath and the flux during welding,
Unless a sheath with a P content of 0.020% or less is used, it is difficult to suppress the P content of the weld metal to 0.03% or less. Therefore, the P content of the sheath is 0.02
0% or less.
Ｓについても、同様の理由から、Ｓ含有量が０゜０１０
％以下のシースを使用しないと、溶接金属のＳ含有量を
０．０１５％以下に抑えることが難しいので、シースの
Ｓ含有量は０．０１０％以下とする。Regarding S, for the same reason, the S content is 0°010
% or less, it is difficult to suppress the S content of the weld metal to 0.015% or less, so the S content of the sheath is set to 0.010% or less.
Ｒワイヤ全重量 りの金 の重量％ ：Ｒが１０％未
満の場合、シースで金属粉を包んだ際に内部の空隙が過
大となるため、金属粉が流動し、均一なワイヤができな
くなる。また、ワイヤ表面にしわや折れ込みが生じ易く
なる。一方、Ｒが３０％を超えると、充填粉が過剰とな
るため、シースの重ね部に金属粉が噛み込み、成形時に
断線し易くなる。したがって、適正なＲの範囲は、１０
〜３０％である。Total weight of R wire Weight % of gold: If R is less than 10%, when metal powder is wrapped in a sheath, internal voids become too large, causing metal powder to flow and making it impossible to form a uniform wire. Furthermore, wrinkles and folds tend to occur on the wire surface. On the other hand, if R exceeds 30%, the filling powder will be excessive, and the metal powder will get caught in the overlapped portion of the sheath, making it easy to break the wire during molding. Therefore, the appropriate range of R is 10
~30%.
金属 のヒ学 ：
溶接金属の硬さ及び高温割れ防止の面での溶接金属のＣ
量を適正な範囲（０，１１〜０．１７％）とするには、
シース成分及び溶接時の歩留りを考慮すると、金属粉中
にＣを（０，１２〜０．２２）Ｘ １００／Ｒ％含有さ
せる必要がある。Metal science: C of weld metal in terms of hardness of weld metal and prevention of hot cracking
To keep the amount within the appropriate range (0.11-0.17%),
Considering the sheath components and the yield during welding, it is necessary to include C in the metal powder in an amount of (0.12 to 0.22) x 100/R%.
溶接金属のＳｉ量を適正な範囲（０，２〜０．６％）と
するには、シース成分及び溶接時の歩留りを考慮すると
、金属粉中にＳｉを（０，２５〜０．８０）Ｘ １００
／Ｒ％含有させる必要がある。In order to keep the amount of Si in the weld metal in an appropriate range (0.2% to 0.6%), considering the sheath component and the yield during welding, Si should be added to the metal powder (0.25% to 0.80%). X 100
/R% must be contained.
溶接金属のＭｎ量を適正な範囲（１，０〜２．５％）と
するには、シース成分及び溶接時の歩留りを考慮すると
、金属粉中にＭｎを（０，７〜２．４）Ｘ １００／Ｒ
％含有させる必要がある。In order to keep the Mn content in the weld metal in an appropriate range (1.0 to 2.5%), considering the sheath components and the yield during welding, it is necessary to add Mn in the metal powder to an appropriate range (0.7 to 2.4%). X 100/R
It is necessary to contain %.
溶接金属の硬さ及び軸受特性面での溶接金属のＣｒ量を
適正な範囲（１，１〜１．６％）とするには、溶接時の
歩留りを考慮すると、金属粉中にＣｒを（１，２〜１．
７）Ｘ１００／Ｒ％含有させる必要がある。In order to keep the Cr content of the weld metal in an appropriate range (1.1 to 1.6%) in terms of the hardness of the weld metal and bearing characteristics, considering the yield during welding, it is necessary to add Cr ( 1,2~1.
7) It is necessary to contain X100/R%.
溶接金属のＭｏ量を適正な範囲（０，１〜０．５％）と
するには、金属粉中にＭｏを（０，１〜０．５）Ｘ１０
０／Ｒ％含有させる必要がある。In order to keep the amount of Mo in the weld metal in an appropriate range (0.1 to 0.5%), add Mo to the metal powder by (0.1 to 0.5) x 10
It is necessary to contain 0/R%.
Ｆｅについては、ワイヤの製造に支障を来さないＲの範
囲が１０〜３０％であり、ワイヤ全重量当りの金属粉の
重量（Ｒ）がこの範囲となるように、上記成分の残部は
Ｆｅで補填する必要がある。Regarding Fe, the range of R that does not interfere with wire manufacturing is 10 to 30%, and the rest of the above components are Fe so that the weight (R) of metal powder per total weight of wire is within this range. need to be compensated for.
なお、金属粉としては、金属Ｓｉ、金属Ｍｎ等の形で充
填してもよいが、フェロシリコン、フェロマンガン等の
形で充填する方がコスト的には有利である。Although the metal powder may be filled in the form of metal Si, metal Mn, etc., it is more advantageous in terms of cost to fill it in the form of ferrosilicon, ferromanganese, etc.
なお、本発明の溶接ワイヤとフラックスとの組合せでサ
ブマージアーク溶接を行う際の留意点について説明する
。Note that points to be noted when performing submerged arc welding using a combination of the welding wire and flux of the present invention will be explained.
まず、前述の高温割れ以外の溶接欠陥、すなわち、低温
割れ、ブローホール、融合不良等の溶接欠陥が発生しに
くい条件で施工する必要がある。First, it is necessary to conduct the welding under conditions in which welding defects other than the above-mentioned hot cracking, ie, welding defects such as cold cracking, blowholes, and poor fusion, are unlikely to occur.
ジャーナル部における肉盛厚さは、熱伝導率等を考慮す
ると、１０ｍｍ以上にすることが設計的に好ましく、か
つ、少なくともジャーナル表面から深さ方向４〜５ｍｍ
までは所定の低Ｃｒ含有量からなる溶接金属で占められ
ている必要がある。The build-up thickness in the journal part is preferably 10 mm or more in terms of design considering thermal conductivity, and at least 4 to 5 mm in the depth direction from the journal surface.
It is necessary that the weld metal has a predetermined low Cr content.
このような要件を満足させるには、多層盛で溶接施工す
ることになり、本発明の溶接ワイヤで初層から肉盛する
ことも支障はないが、より少ない層数で所定の低Ｃｒ溶
接金属を形成するには、初層をＣｒ含有量が低い（例え
ば、０．２％以下）溶接ワイヤで肉盛し、以降の層を本
発明の溶接ワイヤで肉盛する方法が有効である。In order to satisfy these requirements, welding must be carried out using multi-layer welding, and although it is possible to build up from the first layer using the welding wire of the present invention, it is possible to build up from the first layer using the welding wire of the present invention, but it is possible to weld with a predetermined low Cr weld metal using a smaller number of layers. To form this, an effective method is to build up the first layer with a welding wire with a low Cr content (for example, 0.2% or less) and build up the subsequent layers with the welding wire of the present invention.
また、溶接ワイヤト組合せるフラックスについては、焼
結型フラックスの方が有利である。これは、焼結型フラ
ックスは溶融型フラックスに比べて溶接金属中の拡散性
水素量が低く、低温割れ防止予熱温度が低いため、より
低い予熱、層間温度での作業が可能となるためである。Furthermore, as for the flux to be combined with welding wire, sintered flux is more advantageous. This is because sintered flux has a lower amount of diffusible hydrogen in the weld metal than molten flux, and has a lower preheating temperature to prevent cold cracking, making it possible to work at lower preheating and interlayer temperatures. .
以下に本発明の実施例を示す。なお、前述の基礎実験結
果の一部も実施例たり得ることは云うまでもない。Examples of the present invention are shown below. It goes without saying that some of the results of the basic experiments described above can also be used as examples.
（実施例）
第４表に示す化学成分を有する１２％Ｃｒ鋼の軸材（５
００φ×１０００Ｑ）を用いて、タービンロータシャツ
１−のジャーナル部模擬溶接試験を行った・
溶接方法はサブマージアーク溶接とし、第５表に示す化
学成分を有する低Ｃｒ含有量の溶接ワイヤ（３，２φ）
で１層下盛溶接した後、第６表に示す化学成分を有する
本発明の溶接ワイヤを用いて第７表の溶接条件で６層肉
盛溶接した。フラックスはそれぞれ焼結型フラックスを
用いた。(Example) Shaft material of 12% Cr steel having the chemical composition shown in Table 4 (5
00φ 2φ)
After one layer of overlay welding was performed, six layers of overlay welding were performed using the welding wire of the present invention having the chemical composition shown in Table 6 under the welding conditions shown in Table 7. Sintered type flux was used for each flux.
以上の施工方法で肉盛溶接した後、肉盛軸材を６５０℃
Ｘ１５ｈｒのＳＲ処理を施し、肉盛部の欠陥調査、化学
成分調査、硬さ分布測定をそれぞれ行った。After overlay welding using the above construction method, the overlay shaft material was heated to 650℃.
SR treatment was performed for 15 hours, and defects in the built-up part, chemical composition, and hardness distribution were measured.
なお、化学成分調査は、肉盛各層毎に切粉を採取し、分
析することにより行った。肉盛部の欠陥調査は、肉盛最
終層面を平滑に機械加工仕上げしたうえで、超音波探傷
、カラーチエツク、磁粉探傷を行った。The chemical composition investigation was conducted by collecting chips from each layer of overlay and analyzing them. Defects in the build-up area were investigated by performing ultrasonic flaw detection, color check, and magnetic particle flaw detection after the final build-up layer surface was machined to a smooth finish.
肉盛部の欠陥調査の結果、機械加工後の表面については
、カラーチエツク及び磁粉探傷共にインジケーシミンが
認められなかった。As a result of defect investigation of the built-up part, no indicia was found on the surface after machining in both color check and magnetic particle inspection.
肉盛部について超音波探傷を行ったところ、何らの欠陥
エコーも検出されず、健全な肉盛部であ２す
ることか確認された。When ultrasonic flaw detection was performed on the build-up part, no defect echo was detected, confirming that it was a healthy build-up part.
肉盛各層の化学成分については、第８表にその分析結果
を示すように、３層目の溶接金属でほぼ所望の化学成分
となり、４層目以降は安定して適正な化学成分となって
いることがわかる。As for the chemical composition of each layer of overlay, as shown in Table 8, the chemical composition of the third layer of weld metal is almost the desired, and the chemical composition of the fourth and subsequent layers is stable and appropriate. I know that there is.
硬さについては、第３図に肉盛溶接部における半径方向
の硬さ分布測定結果を示すように、母材熱影響部の硬さ
が最も高く、肉盛厚さが増すにつれて漸減するが、５ｍ
ｍ以上の肉盛厚さではほぼ一定の硬さとなっている。As for hardness, as shown in Fig. 3, which shows the hardness distribution measurement results in the radial direction in the overlay weld, the hardness of the heat affected zone of the base metal is the highest, and gradually decreases as the overlay thickness increases. 5m
At a build-up thickness of m or more, the hardness is almost constant.
以上のことから、ジャーナル部の所望肉盛厚さが１０ｍ
ｍとした場合、表面及び表面から深さ５ｍｍ程度までは
、適正な硬さ並びに化学成分が得られることがわかる。From the above, the desired build-up thickness of the journal part is 10 m.
It can be seen that appropriate hardness and chemical components can be obtained from the surface and from the surface to a depth of about 5 mm when m is the surface.
所望肉盛厚さが更に大きくなった場合も、何ら支障はな
く、表面からの適正肉盛域が増すのみである。Even if the desired build-up thickness becomes even larger, there will be no problem, and the appropriate build-up area from the surface will only increase.
【以下余白］
（発明の効果）
以上詳述したように、本発明によれば、１２％Ｃｒ２％
Ｃｒ鋼製蒸気タービンロータシャツ１〜ナル部の肉盛溶
接技術において、高温割れ、ＳＲ割れ、ブローホール等
の欠陥がなく、しかもジャーナル部として充分な強度と
化学成分を有する肉盛溶接部が得られる溶接材料を提供
することができる。[Margin below] (Effect of the invention) As detailed above, according to the present invention, 12%Cr2%
In the build-up welding technology for the null part of steam turbine rotor shirt 1 made of Cr steel, a build-up welded part that is free from defects such as hot cracks, SR cracks, and blowholes and has sufficient strength and chemical composition as a journal part can be obtained. It is possible to provide welding materials that can be used.
第１図（ａ）、（ｂ）はそれぞれ溶接金属のＣ含有量及
びＳ含有量と割れとの関係、並びにＣ含有量及びＰ含有
量と割れとの関係を示す図、
第２図はＳＲ割れ試験片を示す図で、（ａ）は断面図、
（ｂ）は平面図、（ｃ）はノツチの拡大図であり、第３
図は実施例で得られた肉盛溶接部における半径方向の硬
さ分布を示す図である。
特許出願人 株式会社神戸製鋼所
代理人弁理士 中 村 尚
（ｙＡ＋’ｌ冬９
（％）：ｔ’を苺Figures 1 (a) and (b) are diagrams showing the relationship between the C content and S content of weld metal and cracking, and the relationship between C content and P content and cracking, respectively. Figure 2 is SR A diagram showing a crack test piece, (a) is a cross-sectional view,
(b) is a plan view, (c) is an enlarged view of the notch, and
The figure is a diagram showing the hardness distribution in the radial direction in the overlay welded portion obtained in the example. Patent applicant Hisashi Nakamura, patent attorney representing Kobe Steel, Ltd. (yA+'lwinter9 (%): t' stands for strawberry)
Claims (1)
ル部の肉盛溶接材料において、軟鋼製シース内に金属粉
が充填されたコアドワイヤであって、重量％で（以下、
同じ）、 （ａ）軟鋼製シースが Ｃ：０．０２〜０．０４％ Ｓｉ：０．０１〜０．０３％ Ｍｎ：０．１〜０．３％ Ｐ：０．０２０％以下 Ｓ：０．０１０％以下 残部：実質的にＦｅ からなる化学成分を有し、 （ｂ）充填金属粉が Ｃ：（０．１２〜０．２２）×１００／Ｒ Ｓｉ：（０．２５〜０．８０）×１００／ＲＭｎ：（０
．７〜２．４）×１００／Ｒ Ｃｒ：（１．２〜１．７）×１００／Ｒ Ｍｏ：（０．１〜０．５）×１００／Ｒ 残部：実質的にＦｅ （但し、Ｒはワイヤ全重量当りの金属粉の重量％で、１
０％≦Ｒ≦３０％） からなる化学成分を有することを特徴とする１２％Ｃｒ
鋼製蒸気タービンロータシャフト・ジャーナル部の肉盛
用サブマージアーク溶接ワイヤ。[Scope of Claims] A cored wire in which metal powder is filled in a mild steel sheath in an overlay welding material for a steam turbine rotor shaft journal portion made of 12% Cr steel, which is expressed in weight % (hereinafter referred to as
Same), (a) Mild steel sheath C: 0.02-0.04% Si: 0.01-0.03% Mn: 0.1-0.3% P: 0.020% or less S: 0 .010% or less Remainder: Has a chemical component substantially consisting of Fe, (b) The filling metal powder is C: (0.12 to 0.22) x 100/R Si: (0.25 to 0.80 )×100/RMn:(0
．． 7-2.4)×100/R Cr: (1.2-1.7)×100/R Mo: (0.1-0.5)×100/R Balance: Substantially Fe (However, R is the weight percent of metal powder based on the total weight of the wire, and is 1
12% Cr characterized by having a chemical component consisting of (0%≦R≦30%)
Submerged arc welding wire for overlaying steel steam turbine rotor shaft journal parts.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP19445490A JPH0647192B2 (en) | 1990-07-23 | 1990-07-23 | Submerged arc welding wire |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP19445490A JPH0647192B2 (en) | 1990-07-23 | 1990-07-23 | Submerged arc welding wire |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0481291A true JPH0481291A (en) | 1992-03-13 |
| JPH0647192B2 JPH0647192B2 (en) | 1994-06-22 |
Family
ID=16324839
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP19445490A Expired - Lifetime JPH0647192B2 (en) | 1990-07-23 | 1990-07-23 | Submerged arc welding wire |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0647192B2 (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2013024901A1 (en) * | 2011-08-17 | 2013-02-21 | 株式会社日本製鋼所 | FIRST LAYER OR OVERLAYING LAYER WELDING SECTION OF HIGH Cr STEEL TURBINE ROTOR, CLADDING WELDING MATERIAL FOR WELDING SECTION, AND METHOD FOR MANUFACTURING CLADDING WELDING SECTION |
| CN104139254A (en) * | 2014-08-06 | 2014-11-12 | 广东省工业技术研究院(广州有色金属研究院) | Bead-weld flux-cored welding wire |
| WO2017192623A1 (en) | 2016-05-02 | 2017-11-09 | Exxon Mobil Research And Engineering Company | High manganese steel pipe with step-out weld zone erosion-corrosion resistance and method of making the same |
| CN112917041A (en) * | 2021-01-26 | 2021-06-08 | 西安理工大学 | Gas-shielded metal type flux-cored wire for X100 pipeline steel and preparation method thereof |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100455399C (en) * | 2006-03-24 | 2009-01-28 | 宝山钢铁股份有限公司 | Welding wire and wire rod for submerged-arc welding for the building having high performance |
-
1990
- 1990-07-23 JP JP19445490A patent/JPH0647192B2/en not_active Expired - Lifetime
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2013024901A1 (en) * | 2011-08-17 | 2013-02-21 | 株式会社日本製鋼所 | FIRST LAYER OR OVERLAYING LAYER WELDING SECTION OF HIGH Cr STEEL TURBINE ROTOR, CLADDING WELDING MATERIAL FOR WELDING SECTION, AND METHOD FOR MANUFACTURING CLADDING WELDING SECTION |
| JP2013039602A (en) * | 2011-08-17 | 2013-02-28 | Japan Steel Works Ltd:The | FIRST LAYER WELDING SECTION OF HIGH Cr STEEL TURBINE ROTOR, WELDING MATERIAL FOR FIRST LAYER WELDING SECTION, BUILD-UP LAYER WELDING SECTION, WELDING MATERIAL FOR BUILD-UP WELDING SECTION AND METHOD FOR MANUFACTURING MULTILAYER OVERLAY WELDING SECTION |
| CN104139254A (en) * | 2014-08-06 | 2014-11-12 | 广东省工业技术研究院(广州有色金属研究院) | Bead-weld flux-cored welding wire |
| WO2017192623A1 (en) | 2016-05-02 | 2017-11-09 | Exxon Mobil Research And Engineering Company | High manganese steel pipe with step-out weld zone erosion-corrosion resistance and method of making the same |
| US10493570B2 (en) | 2016-05-02 | 2019-12-03 | Exxonmobil Research And Engineering Company | High manganese steel pipe with step-out weld zone erosion-corrosion resistance and method of making the same |
| EP3452249A4 (en) * | 2016-05-02 | 2019-12-18 | Exxonmobil Research And Engineering Company | High manganese steel pipe with step-out weld zone erosion-corrosion resistance and method of making the same |
| US11883906B2 (en) | 2016-05-02 | 2024-01-30 | Exxonmobil Research And Engineering Company | High manganese steel pipe with step-out weld zone erosion-corrosion resistance and method of making the same |
| CN112917041A (en) * | 2021-01-26 | 2021-06-08 | 西安理工大学 | Gas-shielded metal type flux-cored wire for X100 pipeline steel and preparation method thereof |
| CN112917041B (en) * | 2021-01-26 | 2022-07-01 | 西安理工大学 | Gas-shielded metal type flux-cored wire for X100 pipeline steel and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0647192B2 (en) | 1994-06-22 |
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