JPH08300184A - Coated electrode of austenitic stainless steel for high temperature - Google Patents
Coated electrode of austenitic stainless steel for high temperatureInfo
- Publication number
- JPH08300184A JPH08300184A JP13572395A JP13572395A JPH08300184A JP H08300184 A JPH08300184 A JP H08300184A JP 13572395 A JP13572395 A JP 13572395A JP 13572395 A JP13572395 A JP 13572395A JP H08300184 A JPH08300184 A JP H08300184A
- Authority
- JP
- Japan
- Prior art keywords
- core wire
- creep rupture
- coating material
- high temperature
- stainless 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
Landscapes
- Nonmetallic Welding Materials (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、原子力関連分野などで
高温で長時間使用される高温特性の優れたＭｏを含有す
るオーステナイト系ステンレス鋼の溶接に用いる被覆ア
ーク溶接棒に係わるものである。詳しくは、５００℃以
上の高温において溶接金属が優れたクリープ破断強度お
よびクリープ破断延性を有するＭｏを含有するオーステ
ナイト系ステンレス鋼被覆アーク溶接棒に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a coated arc welding rod used for welding Mo-containing austenitic stainless steel having excellent high-temperature characteristics which is used at high temperature for a long time in fields related to nuclear power. More specifically, the present invention relates to an austenitic stainless steel-coated arc welding rod containing Mo, which has excellent creep rupture strength and creep rupture ductility at a high temperature of 500 ° C. or higher.
【０００２】[0002]
【従来の技術】Ｍｏを含有するオーステナイト系ステン
レス鋼は高温での諸特性が優れており、化学プラント、
原子力関連施設などの各種耐熱部材として利用されてい
る。最近は、このような高温での用途に対して、長寿命
化を目指し高温クリープ特性の特に破断強度および破断
延性を改善した鋼材が開発されつつあるが、このような
鋼材に適用する溶接材料においても、母材と同様に優れ
た高温クリープ破断強度と破断延性を有するものが要求
されている。2. Description of the Related Art Mo-containing austenitic stainless steels have excellent properties at high temperatures,
It is used as various heat resistant materials for nuclear facilities. Recently, for such applications at high temperatures, steel materials with improved high-temperature creep properties, especially rupture strength and rupture ductility, are being developed with the aim of extending the service life. Also, a material having excellent high temperature creep rupture strength and rupture ductility similar to the base material is required.
【０００３】しかし、各種溶接材料の中でも被覆アーク
溶接棒は、いわゆる溶接作業性を確保するための被覆剤
中のガス発生剤、スラグ剤などの存在もあり、溶接金属
中の酸素量が他の溶接材料・溶接方法に比較して高く、
特に優れた高温クリープ破断強度と破断延性の両特性を
同時に確保することが極めて困難であった。However, among various welding materials, the coated arc welding rod has a gas generating agent, a slag agent, etc. in the coating material for ensuring the so-called welding workability, so that the amount of oxygen in the weld metal is different. Higher than welding materials and methods
It was extremely difficult to simultaneously secure both excellent high temperature creep rupture strength and rupture ductility.
【０００４】[0004]
【発明が解決しようとする課題】本発明は、高温特性の
優れたＭｏ含有オーステナイト系ステンレス鋼の溶接に
際し、５００℃以上の高温において優れたクリープ破断
強度とクリープ破断延性を有する溶接金属を確保するこ
とのできるＭｏ含有オーステナイト系ステンレス鋼被覆
アーク溶接棒を提供することにある。SUMMARY OF THE INVENTION The present invention secures a weld metal having excellent creep rupture strength and creep rupture ductility at a high temperature of 500 ° C. or higher when welding Mo-containing austenitic stainless steel having excellent high temperature properties. The present invention provides a Mo-containing austenitic stainless steel-coated arc welding rod.
【０００５】[0005]
【課題を解決するための手段】本発明は前記課題を解決
するものであつて、高温用オーステナイト系ステンレス
鋼被覆アーク溶接棒において、心線全重量に対して重量
％で（以下同じ）、Ｃが０．０２５％以下、Ｃｒが１
５．０〜２１．０％、Ｎｉが７．０〜１４．０％、Ｍｏ
が１．２〜３．２％、残りはＦｅおよび不可避的不純物
からなるオーステナイト系ステンレス鋼を心線とし、そ
の心線の周囲に、被覆剤全重量に対して、チタン酸化物
を２５〜５５％、金属炭酸塩を５〜２５％、金属弗化物
を４〜２０％、珪酸塩化合物を１〜１５％、金属粉末を
１〜３５％含有する被覆剤が被覆率２０〜４０％で被覆
され、かつ、心線と被覆剤の一方または両方に、心線重
量比で、Ｐを０．０１５〜０．０４４％、Ｎを０．０３
〜０．２５＆、Ｖを０．０３〜０．８０％含有し、Ｎｂ
を０．１０％未満に制限し、さらにＮｂ／Ｖの値が０．
２５以下、Ｎ／（５Ｎｂ＋Ｖ）の値が０．３０以上とな
るように制御したことを特徴とする高温用オーステナイ
ト系ステンレス鋼被覆アーク溶接棒である。Means for Solving the Problems The present invention is to solve the above-mentioned problems, and in an austenitic stainless steel-coated arc welding rod for high temperature, in% by weight with respect to the total weight of the core wire (hereinafter the same), C Is 0.025% or less, Cr is 1
5.0-21.0%, Ni 7.0-14.0%, Mo
Of 1.2 to 3.2% and the balance being Fe and unavoidable impurities as an austenitic stainless steel as a core wire, and titanium oxide in an amount of 25 to 55 around the core wire with respect to the total weight of the coating material. %, 5 to 25% of metal carbonate, 4 to 20% of metal fluoride, 1 to 15% of silicate compound, and 1 to 35% of metal powder are coated at a coating rate of 20 to 40%. And, in one or both of the core wire and the coating material, P is 0.015 to 0.044% and N is 0.03 in the core wire weight ratio.
~ 0.25 &, containing 0.03 ~ 0.80% V, Nb
Is limited to less than 0.10%, and the value of Nb / V is less than 0.1.
It is an austenitic stainless steel-coated arc welding rod for high temperature, which is controlled so that the value of N / (5Nb + V) is 25 or less and 0.3 / or more.
【０００６】なお、ここでいう心線重量比とは、次式の
関係で示されるものを指し、かつ同式中の被覆剤配合比
とは被覆剤全重量比に対して添加原料が占める配合割合
を意味し、さらに被覆率とは溶接棒全重量に対する被覆
剤の重量％を意味する。る。 心線重量比＝心線中の含有量（重量％）＋被覆剤配合比
（重量％）×被覆率（重量％）／（１００−被覆率）Here, the core wire weight ratio refers to the one represented by the following equation, and the coating agent compounding ratio in the equation is the compounding ratio of the additive raw material to the total coating agent weight ratio. Further, the term "coverage" means the weight% of the coating material with respect to the total weight of the welding rod. It Core wire weight ratio = content in core wire (wt%) + coating agent compounding ratio (wt%) × coverage ratio (wt%) / (100−coverage ratio)
【０００７】[0007]
【作用】本発明は、Ｍｏ含有オーステナイト系ステンレ
ス鋼被覆アーク溶接棒の溶接金属の高温クリープ破断強
度およびクリープ破断延性の両特性を向上させるため、
心線および被覆剤組成上からＰ量、Ｎ量、Ｖ量を特定
し、さらにＮｂ量を制限し、かつＮｂ／Ｖ，Ｎ／（５Ｎ
ｂ＋Ｖ）の値を制御することにより、溶接金属のＰ量、
Ｎ量、Ｖ量およびＮｂ量を最適な範囲に制御するもので
ある。The present invention improves both the high temperature creep rupture strength and the creep rupture ductility of the weld metal of a Mo-containing austenitic stainless steel-coated arc welding rod.
The amount of P, the amount of N, and the amount of V are specified from the viewpoint of the core wire and the composition of the coating material, and the amount of Nb is further limited, and Nb / V, N / (5N
By controlling the value of b + V), the P amount of the weld metal,
The amount of N, the amount of V, and the amount of Nb are controlled within an optimum range.
【０００８】本発明者らは、溶接作業性を損なわずに母
材なみの優れたクリープ破断強度と破断延性を有する溶
接金属を確保できるＭｏ含有オーステナイト系ステンレ
ス鋼被覆アーク溶接棒を得ることを目的として、心線の
組成およびチタン酸化物、金属炭酸塩、金属弗化物を主
成分としたいわゆるライムチタニヤ系被覆剤の組成上か
ら種々の検討を実施した。その結果、以下の知見を得る
に至った。The inventors of the present invention have an object to obtain a Mo-containing austenitic stainless steel-coated arc welding rod capable of ensuring a weld metal having excellent creep rupture strength and fracture ductility similar to that of the base metal without impairing the welding workability. As a result, various studies were carried out from the viewpoint of the composition of the core wire and the composition of a so-called lime titania-based coating material containing titanium oxide, metal carbonate and metal fluoride as main components. As a result, the following findings have been obtained.
【０００９】Ｍｏを含有するオーステナイト系ステンレ
ス鋼の被覆アーク溶接棒による溶接金属において、５０
０℃以上の高温におけるクリープ破断強度を向上するた
めには、Ｐ，Ｎ，Ｖ，ＣおよびＮｂの添加が有効であ
る。一方、クリープ破断延性を向上するのに、Ｐの添加
が若干効果があり、Ｎ，Ｖはクリープ破断延性に大きな
影響を及ぼさず、Ｎｂ，Ｃは微量でも顕著にクリープ破
断延性を低下させる。また、クリープ破断延性の低下傾
向はＮｂ／Ｖの値に大きく影響を受けること、さらにク
リープ破断強度と破断延性の両特性を同時に確保するた
めにはＮ／（５Ｎｂ＋Ｖ）の値を制御しなければならな
いことが判明した。In the weld metal of the austenitic stainless steel containing Mo with a covered arc welding rod, 50
The addition of P, N, V, C and Nb is effective for improving the creep rupture strength at a high temperature of 0 ° C. or higher. On the other hand, the addition of P has a slight effect on improving the creep rupture ductility, N and V do not have a great influence on the creep rupture ductility, and Nb and C remarkably reduce the creep rupture ductility. Further, the decreasing tendency of creep rupture ductility is greatly influenced by the value of Nb / V. Furthermore, in order to secure both properties of creep rupture strength and rupture ductility at the same time, the value of N / (5Nb + V) must be controlled. It turned out not to be.
【００１０】以下に本発明をさらに詳細に説明する。ま
ず本発明における心線は、基本的に高温特性の優れたＭ
ｏを含有するオーステナイト系ステンレス鋼であればよ
いが、心線中のＣ量については、被覆剤中から混入する
分をも考慮して、溶接金属のクリープ破断延性の低下を
防止するために溶接金属中のＣを０．０６％以下に抑え
ることが望ましく、そのためには心線中のＣ量は低けれ
ば低い程良いが、心線中のＣを０．０２５％以下に制限
すれば、後に述べるごとくチタン酸化物を主成分とする
いわゆるライムチタニヤ系の被覆剤を被覆することと相
まって溶接金属中のＣを０．０６％以下に保つことがで
きる。従って心線中のＣを０．０２５％以下に制限す
る。The present invention will be described in more detail below. First, the core wire in the present invention is basically M which has excellent high temperature characteristics.
Any austenitic stainless steel containing o may be used, but regarding the amount of C in the core wire, in consideration of the amount mixed in from the coating material, welding is performed in order to prevent a decrease in creep rupture ductility of the weld metal. It is desirable to suppress C in the metal to 0.06% or less. For that purpose, the lower the amount of C in the core, the better. However, if C in the core is limited to 0.025% or less, As described above, the C content in the weld metal can be maintained at 0.06% or less in combination with the coating with a so-called lime titania coating material containing titanium oxide as a main component. Therefore, C in the core wire is limited to 0.025% or less.
【００１１】また、心線のＣ以外の成分は、基本的に高
温において優れた引張強度特性、クリープ破断特性、時
効靱性などの高温特性を有するＭｏ含有オーステナイト
組織の溶接金属とするため、心線全重量に対して、Ｃｒ
が１５．０〜２１．０％、Ｎｉが７．０〜１４．０％、
Ｍｏが１．２〜３．２％、残りはＦｅおよび不可避的不
純物からなるものとする。なお、これら成分の他に、心
線の生産性、溶接作業性、溶接金属の耐高温割れ性など
を改善する目的でＳｉ；０．７５％以下、Ｍｎ；２．５
％以下の範囲で適宜含有しても本発明の特徴は損なわれ
ない。In addition, since the components other than C of the core wire are basically a weld metal of Mo-containing austenite structure having high temperature characteristics such as excellent tensile strength characteristics, creep rupture characteristics, and aging toughness at high temperatures, Cr based on total weight
Is 15.0 to 21.0%, Ni is 7.0 to 14.0%,
It is assumed that Mo is 1.2 to 3.2%, and the balance is Fe and inevitable impurities. In addition to these components, Si: 0.75% or less, Mn: 2.5 for the purpose of improving the productivity of the core wire, the workability of welding, the hot crack resistance of the weld metal, and the like.
The content of the present invention is not impaired even if it is appropriately contained within the range of%.
【００１２】次に、心線と被覆剤の一方または両方に心
線重量比でＰを０．０１５〜０．０４４％、Ｎを０．０
３〜０．２５％、Ｖを０．０３〜０．８０％含有し、Ｎ
ｂを０．１０％未満に制限し、さらに、Ｎｂ／Ｖの値が
０．２５以下、Ｎ／（５Ｎｂ＋Ｖ）の値が０．３０以上
となるよう制御することが、本発明の主要な構成要件で
ある。Next, in one or both of the core wire and the coating material, P is 0.015 to 0.044% and N is 0.0 in the core wire weight ratio.
3 to 0.25%, V content of 0.03 to 0.80%, N
The main constitution of the present invention is to limit b to less than 0.10% and to control so that the value of Nb / V is 0.25 or less and the value of N / (5Nb + V) is 0.30 or more. It is a requirement.
【００１３】心線および被覆剤の一方または両方に含有
させる元素のうち、Ｐは溶接金属中に侵入型の固溶ある
いは燐化物の形で存在するが、その存在によって高温に
おけるクリープ破断強度を向上しさらには溶接金属の結
晶粒界の移動を容易にするなどの効果からクリープ破断
延性を向上させる。しかし、心線および被覆剤の一方ま
たは両方に心線重量比で０．０１５％未満では効果が少
なく、０．０４４％を超えると溶接金属の耐高温割れ性
が劣化する。従って、心線重量比で０．０１５〜０．０
４４％に制御する。Of the elements contained in one or both of the core wire and the coating, P is present in the weld metal in the form of an interstitial solid solution or a phosphide, and its presence improves the creep rupture strength at high temperatures. Further, the creep rupture ductility is improved due to the effect of facilitating the movement of the crystal grain boundaries of the weld metal. However, if the weight ratio of the core wire and / or the coating material to the core wire is less than 0.015%, the effect is small, and if it exceeds 0.044%, the hot metal resistance to hot cracking is deteriorated. Therefore, the core weight ratio is 0.015 to 0.0
Control to 44%.
【００１４】Ｎは、溶接金属中に侵入型の固溶あるいは
窒化物の形で存在するが、その存在によって高温におけ
るクリープ破断強度を向上させる。しかし、心線および
被覆剤の一方または両方に心線重量比で０．０３％未満
では効果が少なく、０．２５％を超えるとクリープ破断
延性が低下するようになると共にスラグの剥離性などの
溶接作業性が劣化する。従って、心線重量比で０．０３
〜０．２５％に制御する。N exists in the weld metal in the form of an interstitial solid solution or a nitride, and its presence improves the creep rupture strength at high temperatures. However, if the weight ratio of the core wire and / or the coating material to the core wire is less than 0.03%, the effect is small, and if it exceeds 0.25%, the creep rupture ductility is deteriorated and the slag releasability is reduced. Welding workability deteriorates. Therefore, the core weight ratio is 0.03
Control to ~ 0.25%.
【００１５】Ｖは、溶接金属中に置換型の固溶あるいは
窒化物、炭化物、酸化物などの形で存在するが、その存
在によって高温におけるクリープ破断強度を向上させ
る。しかし、心線および被覆剤の一方または両方に心線
重量比で０．０３％未満では効果が少なく、０．８０％
を超えるとクリープ破断延性が低下するようになる。従
って、心線重量比で０．０３〜０．８０％に制御する。V is present in the weld metal in the form of substitutional solid solution or in the form of nitride, carbide, oxide or the like, and its presence improves the creep rupture strength at high temperature. However, less than 0.03% by weight of the core wire and / or the coating agent has a small effect, and 0.80%
If it exceeds, the creep rupture ductility will decrease. Therefore, the core wire weight ratio is controlled to 0.03 to 0.80%.
【００１６】Ｎｂは、溶接金属中に置換型の固溶あるい
は窒化物、炭化物、酸化物などの形で存在するが、その
存在が微量であっても高温におけるクリープ破断延性を
著しく劣化させる。クリープ破断延性の著しい劣化を防
止するためには、Ｎｂ量は低ければ低い程良いが、心線
および被覆剤の一方または両方で０．１０％以上でクリ
ープ破断延性の劣化が特に著しくなる。従って、心線お
よび被覆剤の一方または両方のＮｂ量は心線重量比で
０．１０％未満に制限する。Nb is present in the weld metal in the form of substitutional solid solution or in the form of nitrides, carbides, oxides, etc. Even if the amount of Nb is very small, the creep rupture ductility at high temperature is significantly deteriorated. In order to prevent remarkable deterioration of creep rupture ductility, the lower the amount of Nb, the better. However, when 0.10% or more of one or both of the core wire and the coating material, the deterioration of creep rupture ductility becomes particularly remarkable. Therefore, the Nb amount of one or both of the core wire and the coating material is limited to less than 0.10% by weight of the core wire.
【００１７】さらに、ＮｂとＶは、溶接金属において窒
化物、炭化物、酸化物など類似の形態で存在し易いこと
から、Ｖの添加はＮｂによるクリープ破断延性の著しい
劣化を抑制する効果があるが、Ｎｂ含有量とＶ添加量と
の比が０．２５を超えるとＶによるＮｂのクリープ破断
延性劣化防止効果がほとんど認められなくなる。従っ
て、Ｎｂ／Ｖの値を０．２５以下とする。Further, since Nb and V are likely to exist in a weld metal in a similar form such as nitride, carbide, and oxide, addition of V has an effect of suppressing remarkable deterioration of creep rupture ductility due to Nb. , If the ratio between the Nb content and the V addition amount exceeds 0.25, the effect of preventing the creep rupture ductility deterioration of Nb by V is hardly recognized. Therefore, the value of Nb / V is set to 0.25 or less.
【００１８】Ｎは前述のごとく、溶接金属において固
溶、窒化物いずれの形でもクリープ破断強度を向上させ
る。この場合、窒化物の形で存在しているほうがクリー
プ破断強度の向上効果が大きいが、クリープ破断延性の
低下傾向は大きい。一方、固溶している方がクリープ破
断延性を損う程度が小さいが、クリープ破断強度の向上
効果はやや小さい。このことから、窒化物を形成し易い
Ｎｂ，Ｖとの比率が０．３０未満ではＮの大部分が窒化
物となりクリープ破断延性の劣化が著しくなる。従っ
て、Ｎ／（５Ｎｂ＋Ｖ）の値を０．３０以上に制御す
る。As described above, N improves creep rupture strength in the form of solid solution or nitride in weld metal. In this case, the presence in the form of nitride has a larger effect of improving the creep rupture strength, but the tendency of decreasing the creep rupture ductility is large. On the other hand, when the solid solution is present, the extent to which the creep rupture ductility is impaired is small, but the effect of improving the creep rupture strength is rather small. From this, if the ratio of Nb and V that easily form a nitride is less than 0.30, most of N becomes a nitride and the creep rupture ductility deteriorates significantly. Therefore, the value of N / (5Nb + V) is controlled to 0.30 or more.
【００１９】また被覆剤については、基本的に全姿勢で
の溶接作業性が良好でかつ被覆剤からの溶接金属中への
Ｃの混入が比較的少ないいわゆるライムチタニヤ系の被
覆剤、すなわち被覆剤全重量に対して重量％で、チタン
酸化物を２５〜５５％、金属炭酸塩を５〜２５％、金属
弗化物を４〜２０％、珪酸塩化合物を１〜１５％、金属
粉末を１〜３５％含有する被覆剤とし、被覆率は２０〜
４０％とすることが望ましい。なお、これら被覆剤成分
のうち、特にチタン酸化物については、不純物としてＮ
ｂを含有する原料が多いので、Ｎｂ含有量が少ない原料
を厳選して使用することが望ましい。Regarding the coating material, basically, the so-called lime titania type coating material, that is, the welding workability in all postures is good and the content of C in the weld metal from the coating material is relatively small, that is, all the coating materials % By weight based on weight, titanium oxide 25-55%, metal carbonate 5-25%, metal fluoride 4-20%, silicate compound 1-15%, metal powder 1-35. % Coating agent, and the coverage is 20 to
It is desirable to set it to 40%. Among these coating material components, especially titanium oxide, N as an impurity.
Since many raw materials contain b, it is desirable to carefully select and use raw materials with a low Nb content.
【００２０】その他、本発明溶接棒における良好な溶接
作業性の確保、あるいは生産性の向上を目的として、Ａ
ｌ2 Ｏ3 ，ＺｒＯ2 ，Ｋ2 Ｏ，Ｎａ2 Ｏ，ＣａＯ，Ｍｇ
Ｏ等の金属酸化物を被覆剤に含有することができる。In addition, for the purpose of ensuring good welding workability or improving productivity in the welding rod of the present invention, A
l 2 O 3 , ZrO 2 , K 2 O, Na 2 O, CaO, Mg
A metal oxide such as O can be contained in the coating agent.
【００２１】以上のように、本発明による高温用オース
テナイト系ステンレス鋼被覆アーク溶接棒は、低炭素Ｍ
ｏ含有オーステナイト系ステンレス鋼心線にいわゆるラ
イムチタニヤ系の被覆剤を被覆し、心線および被覆剤の
一方または両方に添加する微量成分のＰ，Ｎ，Ｖの含有
量を適正範囲に制御し、同時にＮｂ含有量を極めて低く
制限し、さらにＮｂ／ＶおよびＮ／（Ｎｂ＋Ｖ）の値を
制御することによって、これらすべての相乗効果から５
００℃以上の高温においても優れたクリープ破断強度、
クリープ破断延性などの特性を有する溶接金属を容易に
得ることができる。As described above, the high temperature austenitic stainless steel-coated arc welding rod according to the present invention has a low carbon M content.
The o-containing austenitic stainless steel core wire is coated with a so-called lime titania-based coating material, and the P, N, and V contents of trace components added to one or both of the core wire and the coating material are controlled within an appropriate range. By limiting the Nb content to very low and controlling the values of Nb / V and N / (Nb + V), all these synergistic effects can
Excellent creep rupture strength even at high temperatures above 00 ° C,
A weld metal having characteristics such as creep rupture ductility can be easily obtained.
【００２２】ここで溶接棒の製造方法について言及する
と、心線およびＮｂ含有量の少ない厳選したチタン酸化
物（望ましくは不純物としてのＮｂ含有量は０．２重量
％以下）原料などを配合し乾式混合した被覆剤の粉末を
準備し、被覆剤粉末を水ガラス（珪酸カリおよび珪酸ソ
ーダの水溶液）のバインダーで湿式混合してから、心線
外周へ塗装した後、１５０〜４５０℃で約１時間の乾
燥、焼成を行う。The method of manufacturing the welding rod will be described below. A dry method is used in which a core wire and carefully selected titanium oxide having a small Nb content (preferably an Nb content as an impurity is 0.2% by weight or less) are mixed. Prepare mixed powder of coating material, wet mix the coating material powder with a binder of water glass (potassium silicate and sodium silicate solution), and then coat on the outer circumference of the core wire, and then at 150 to 450 ° C for about 1 hour. Is dried and baked.
【００２３】[0023]
【実施例】以下に本発明の実施例について述べる。表１
に供試心線の化学成分を示す。このうち心線記号Ｔ１〜
Ｔ４は本発明であり、Ｔ５およびＴ６は比較例である。
また表２〜表４に供試心線と被覆剤の組み合わせによる
被覆アーク溶接棒の組成を示す。表５には使用した母材
の化学成分を示す。また表６〜表８に、表２ないし表４
の被覆アーク溶接棒と表５の母材を用いて実施した溶接
金属の成分分析結果および６００℃における引張試験と
６００および６５０℃におけるクリープ破断試験の結果
を示す。これらの表において下線のあるデータは本発明
範囲外のものであることを示す。EXAMPLES Examples of the present invention will be described below. Table 1
Shows the chemical components of the test core wire. Of these, the core symbol T1
T4 is the present invention, and T5 and T6 are comparative examples.
Tables 2 to 4 show the compositions of the coated arc welding rods obtained by combining the test core wire and the coating material. Table 5 shows the chemical composition of the base material used. Further, Tables 6 to 8 show Tables 2 to 4
2 shows the results of component analysis of the weld metal carried out using the coated arc welding rod of No. 1 and the base metal of Table 5, and the results of the tensile test at 600 ° C. and the creep rupture test at 600 and 650 ° C. Underlined data in these tables indicates that they are outside the scope of the invention.
【００２４】[0024]
【表１】 [Table 1]
【００２５】[0025]
【表２】 [Table 2]
【００２６】[0026]
【表３】 [Table 3]
【００２７】[0027]
【表４】 [Table 4]
【００２８】[0028]
【表５】 [Table 5]
【００２９】[0029]
【表６】 [Table 6]
【００３０】[0030]
【表７】 [Table 7]
【００３１】[0031]
【表８】 [Table 8]
【００３２】溶接試験は、棒径４．０ｍｍの溶接棒を用
い、溶接電流１４０Ａ（ＡＣ）、アーク電圧２２〜２６
Ｖ、溶接速度１５０〜２２０ｍｍ／ｍｉｎ、下向姿勢で
図１に示す開先形状の試験板に溶接した。図１において
１は母材、２は裏当て金で板厚ｔ＝２０ｍｍ、開先角度
θ＝４５°、ルートギャップＧ＝１２ｍｍとした。In the welding test, a welding rod having a diameter of 4.0 mm was used, a welding current of 140 A (AC) and an arc voltage of 22 to 26.
V was welded to the groove-shaped test plate shown in FIG. 1 in a downward posture at a welding speed of 150 to 220 mm / min. In FIG. 1, 1 is a base material, 2 is a backing plate, the plate thickness t = 20 mm, the groove angle θ = 45 °, and the root gap G = 12 mm.
【００３３】溶接金属３の高温引張試験片は、図２の要
領で平行部径６．０ｍｍ、平行部長さ２５ｍｍの試験片
４を採取した。また、クリープ破断試験片は同じく図２
の要領で平行部径６．０ｍｍ、平行部長さ３０ｍｍの試
験片４を採取した。As the high temperature tensile test piece of the weld metal 3, a test piece 4 having a parallel part diameter of 6.0 mm and a parallel part length of 25 mm was taken as in the procedure of FIG. The creep rupture test piece is also shown in Fig. 2.
A test piece 4 having a parallel part diameter of 6.0 mm and a parallel part length of 30 mm was sampled in the same manner as described above.
【００３４】表６ないし表８からも明らかなように、本
発明の被覆アーク溶接棒記号Ｎｏ．１〜１４、Ｎｏ．１
６，１８および２０はいずれも６００℃，６５０℃での
クリープ破断試験における破断時間が長く、破断伸びも
大きく高温でのクリープ破断強度および破断延性が優れ
ていることが明らかである。また６００℃での引張試験
における０．２％耐力、引張強さ、伸びも良好であっ
た。As is apparent from Tables 6 to 8, the coated arc welding rod symbol No. of the present invention was used. 1-14, No. 1
It is clear that all of 6, 18 and 20 have a long rupture time in a creep rupture test at 600 ° C. and 650 ° C., a large elongation at break, and excellent creep rupture strength and rupture ductility at high temperatures. The 0.2% proof stress, tensile strength and elongation in a tensile test at 600 ° C were also good.
【００３５】これに対して、被覆アーク溶接棒記号Ｎ
ｏ．１５，１９および２６はＮ／（５Ｎｂ＋Ｖ）の値が
０．３０未満のため高温クリープ破断伸びが低い。また
Ｎｏ．１７はＰ量が心線重量比で０．０１５％未満のた
め高温クリープ破断伸びが低い。On the other hand, the covered arc welding rod symbol N
o. Nos. 15, 19 and 26 have a low N / (5Nb + V) value of less than 0.30 and thus have a low high temperature creep rupture elongation. In addition, No. In No. 17, the P content is less than 0.015% in terms of the weight ratio of the cord, so that the high temperature creep rupture elongation is low.
【００３６】Ｎｏ．２１はＮｂ量が心線重量比で０．１
０％以上で、Ｎｂ／Ｖの値が０．２５を超え、Ｎ／（５
Ｎｂ＋Ｖ）の値が０．３０未満のため高温クリープ破断
伸びが低い。またＮｏ．２２はＣ量が０．０２５％を超
える比較例の心線を使用したため溶接金属のＣ量が０．
０６％を超え、高温クリープ破断伸びが低い。なおＮ
ｏ．２２による溶接金属中にはミクロ割れが認められ
た。No. No. 21 has a Nb content of 0.1 in terms of core weight ratio.
At 0% or more, the value of Nb / V exceeds 0.25, and N / (5
Since the value of (Nb + V) is less than 0.30, the high temperature creep rupture elongation is low. In addition, No. No. 22 used the core wire of the comparative example having a C content of more than 0.025%, so the C content of the weld metal was 0.2.
It exceeds 06% and the high temperature creep rupture elongation is low. N
o. Micro cracks were observed in the weld metal of No. 22.
【００３７】Ｎｏ．２３はＰ量が心線重量比で０．０４
４％を超え、Ｎｂ量が心線重量比で０．１０％以上のた
め高温クリープ破断伸びが低い。またＮｏ．２４はＶ量
が心線重量比で０．８０％を超え、Ｎ／（５Ｎｂ＋Ｖ）
の値が０．３０未満のため高温クリープ破断伸びが低
い。No. In No. 23, the amount of P is 0.04 in terms of core weight ratio
Since it exceeds 4% and the Nb content is 0.10% or more in terms of the core weight ratio, the high temperature creep rupture elongation is low. In addition, No. No. 24, V amount exceeds 0.80% in core weight ratio, N / (5Nb + V)
Value is less than 0.30, the high temperature creep rupture elongation is low.
【００３８】Ｎｏ．２５はＮｂ／Ｖの値が０．２５を超
え高温クリープ破断伸びが低い。またＮｏ．２７はＰ量
が心線重量比で０．０１５％未満で、Ｎ量が心線重量比
で０．０３％未満のため高温クリープ破断時間が短い。No. In No. 25, the Nb / V value exceeds 0.25 and the high temperature creep rupture elongation is low. In addition, No. In No. 27, the P content is less than 0.015% in the core wire weight ratio and the N content is less than 0.03% in the core wire weight ratio, so that the high temperature creep rupture time is short.
【００３９】Ｎｏ．２８はＶ量が０．０３％未満のため
高温クリープ破断時間が短い。Ｎｏ．２９は被覆剤が本
発明外の金属炭酸塩と金属弗化物を主成分とするいわゆ
るライム系のため溶接金属のＣ量が０．０６％を超え、
高温クリープ破断伸びが低い。またＮｏ．２９はスラグ
の剥離性、ビード形状等溶接作業性が劣っていた。No. No. 28 has a V content of less than 0.03% and therefore has a short high temperature creep rupture time. No. In No. 29, the coating material is a so-called lime system whose main component is a metal carbonate and a metal fluoride other than the present invention, so the C content of the weld metal exceeds 0.06%,
High temperature creep rupture elongation is low. In addition, No. No. 29 was inferior in slag peelability and welding workability such as bead shape.
【００４０】[0040]
【発明の効果】以上のように本発明の高温用オーステナ
イト系ステンレス鋼被覆アーク溶接棒は、５００℃以上
の高温において優れたクリープ破断強度とクリープ破断
延性を有する溶接金属が得られ、しかも溶接作業性も良
好である。従って、原子力関連分野など高温環境で使用
される構造物の溶接に適用することにより、従来に無い
長寿命の溶接部が確保できる。INDUSTRIAL APPLICABILITY As described above, the high temperature austenitic stainless steel-coated arc welding rod of the present invention can obtain a weld metal having excellent creep rupture strength and creep rupture ductility at a high temperature of 500 ° C. or more, and can be used for welding work. The property is also good. Therefore, by applying it to welding of a structure used in a high temperature environment such as a field related to nuclear power, it is possible to secure a welded portion having a long life which has never existed before.
【図１】実施例における試験板の開先形状を示す断面図FIG. 1 is a sectional view showing a groove shape of a test plate in an example.
【図２】溶接金属の高温引張試験片および高温クリープ
破断試験片の採取位置を示す断面図FIG. 2 is a cross-sectional view showing sampling positions of a high temperature tensile test piece and a high temperature creep rupture test piece of weld metal.
Claims (1)
覆アーク溶接棒において、心線全重量に対して重量％
で、、Ｃが０．０２５％以下、Ｃｒが１５．０〜２１．
０％、Ｎｉが７．０〜１４．０％、Ｍｏが１．２〜３．
２％、残りはＦｅおよび不可避的不純物からなるオース
テナイト系ステンレス鋼を心線とし、その心線の周囲
に、被覆剤全重量に対して、チタン酸化物を２５〜５５
％、金属炭酸塩を５〜２５％、金属弗化物を４〜２０
％、珪酸塩化合物を１〜１５％、金属粉末を１〜３５％
含有する被覆剤が被覆率２０〜４０％で被覆され、か
つ、心線と被覆剤の一方または両方に、心線重量比で、
Ｐを０．０１５〜０．０４４％、Ｎを０．０３〜０．２
５％、Ｖを０．０３〜０．８０％含有し、Ｎｂを０．１
０％未満に制限し、さらに、Ｎｂ／Ｖの値が０．２５以
下、Ｎ／（５Ｎｂ＋Ｖ）の値が０．３０以上となるよう
に制御したことを特徴とする高温用オーステナイト系ス
テンレス鋼被覆アーク溶接棒。1. A high-temperature austenitic stainless steel-coated arc welding rod for use in high temperature, in% by weight based on the total weight of the core wire.
And, C is 0.025% or less and Cr is 15.0 to 21.
0%, Ni 7.0 to 14.0%, Mo 1.2 to 3.
Austenitic stainless steel consisting of 2% and the balance Fe and unavoidable impurities is used as a core wire, and titanium oxide is added in an amount of 25 to 55 around the core wire, based on the total weight of the coating material.
%, Metal carbonate 5 to 25%, metal fluoride 4 to 20
%, Silicate compound 1 to 15%, metal powder 1 to 35%
The coating material contained is coated at a coverage of 20 to 40%, and one or both of the core wire and the coating material are provided in a weight ratio of the core wire,
P is 0.015 to 0.044%, N is 0.03 to 0.2
5%, 0.03 to 0.80% V, Nb 0.1%
Austenitic stainless steel coating for high temperature, characterized by being controlled to be less than 0% and further controlled so that the value of Nb / V is 0.25 or less and the value of N / (5Nb + V) is 0.30 or more. Arc welding rod.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP13572395A JP3483657B2 (en) | 1995-05-10 | 1995-05-10 | Austenitic stainless steel coated arc welding rod for high temperature |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP13572395A JP3483657B2 (en) | 1995-05-10 | 1995-05-10 | Austenitic stainless steel coated arc welding rod for high temperature |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH08300184A true JPH08300184A (en) | 1996-11-19 |
| JP3483657B2 JP3483657B2 (en) | 2004-01-06 |
Family
ID=15158383
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP13572395A Expired - Lifetime JP3483657B2 (en) | 1995-05-10 | 1995-05-10 | Austenitic stainless steel coated arc welding rod for high temperature |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3483657B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000052089A (en) * | 1998-08-14 | 2000-02-22 | Nippon Steel Corp | Austenite system stainless steel filler rod with excellent high temperature characteristic |
| CN102886623A (en) * | 2012-10-29 | 2013-01-23 | 海门市威菱焊材制造有限公司 | Martensite stainless steel flux-cored wire |
-
1995
- 1995-05-10 JP JP13572395A patent/JP3483657B2/en not_active Expired - Lifetime
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000052089A (en) * | 1998-08-14 | 2000-02-22 | Nippon Steel Corp | Austenite system stainless steel filler rod with excellent high temperature characteristic |
| CN102886623A (en) * | 2012-10-29 | 2013-01-23 | 海门市威菱焊材制造有限公司 | Martensite stainless steel flux-cored wire |
Also Published As
| Publication number | Publication date |
|---|---|
| JP3483657B2 (en) | 2004-01-06 |
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