JP2800661B2 - Welding material for high Cr high N austenitic steel - Google Patents
Welding material for high Cr high N austenitic steelInfo
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- JP2800661B2 JP2800661B2 JP5286390A JP28639093A JP2800661B2 JP 2800661 B2 JP2800661 B2 JP 2800661B2 JP 5286390 A JP5286390 A JP 5286390A JP 28639093 A JP28639093 A JP 28639093A JP 2800661 B2 JP2800661 B2 JP 2800661B2
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Description
【０００１】[0001]
【産業上の利用分野】本発明は、発電用ボイラ、高温用
装置等高温強度に優れた高Cr高Ｎオーステナイト鋼に使
用され、優れた溶接施工性および溶接部の高温強度を有
する溶接材料に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a welding material which is used for high Cr high N austenitic steel having excellent high temperature strength, such as a power generation boiler and a high temperature apparatus, and has excellent welding workability and high temperature strength of a welded portion. .
【０００２】[0002]
【従来の技術】従来、発電用ボイラ、高温用装置等には
主に18Cr−８Ni系のオーステナイトステンレス鋼が使用
されてきた。しかし、近年のボイラ等での運転条件の苛
酷化、即ち高温、高圧化されるに伴い、より高温強度お
よび耐食性に優れた材料が必要とされるようになった。
このような要求から例えば特開昭57−164972号公報およ
び特開昭59−64752 号公報に開示されているように高Cr
でＮ、Nb、Ｂを添加することにより高温強度および耐食
性の改善を図った高Cr高Ｎを特徴としたオーステナイト
鋼が提案されている。2. Description of the Related Art Conventionally, 18Cr-8Ni-based austenitic stainless steel has been mainly used for power generation boilers, high-temperature devices and the like. However, as operating conditions in boilers and the like have become more severe in recent years, that is, higher temperatures and higher pressures, materials having higher high-temperature strength and corrosion resistance have been required.
From such demands, for example, as disclosed in JP-A-57-164972 and JP-A-59-64752, high Cr
There is proposed an austenitic steel characterized by high Cr and high N in which high temperature strength and corrosion resistance are improved by adding N, Nb and B.
【０００３】そして、このような高Cr高Ｎオーステナイ
ト鋼用溶接材料としては母材をそのまま加工したもの
や、高Ni合金用のもの（例えば、JIS 溶接棒 DNiCr系）
の使用が考えられている。しかし、高Cr高Ｎオーステナ
イト鋼の母材は、溶製後、圧延、熱処理により組織の調
整を受けて高温強度の確保が図られるのに対し、溶接金
属部はほとんどの場合、凝固ままの組織で使用されるた
め、母材に比べ高温強度を高めることは本質的に容易で
はない。そのため、母材をそのまま線引加工した溶接材
料では溶接金属に優れた高温強度を付与することは困難
であった。[0003] As such welding materials for high Cr high N austenitic steel, those obtained by directly processing a base material or those for high Ni alloys (for example, JIS welding rod DNiCr).
The use of is considered. However, the base material of high-Cr high-N austenitic steel is made by melting, rolling, and heat-treating to adjust the structure to ensure high-temperature strength, while in most cases, the weld metal has a solidified structure. Therefore, it is essentially not easy to increase the high-temperature strength as compared with the base material. Therefore, it has been difficult to impart excellent high-temperature strength to the weld metal using a welding material obtained by drawing the base material as it is.
【０００４】一方、高Ni合金用の溶接材料は高価であ
り、経済性の観点から好ましくない。On the other hand, welding materials for high Ni alloys are expensive and are not preferred from the viewpoint of economy.
【０００５】そのため本発明者らは、Ｎ、Nb、Moを含有
させることで高温強度を高め、Ｂ（ボロン）を排除し、
ＰとＳを少なく制限して、Mgを含有させることにより耐
溶接高温割れ性を高めた高Cr高Ｎオーステナイト鋼用溶
接材料（特開平５−69187 号公報）を提案した。Therefore, the present inventors increased the high-temperature strength by including N, Nb, and Mo, eliminated B (boron),
We have proposed a welding material for high Cr high N austenitic steel in which P and S are limited to a small amount and Mg is contained to improve the high temperature crack resistance in welding (Japanese Patent Laid-Open No. 5-69187).
【０００６】上記特開平５−69187 号公報に開示されて
いる溶接材料は高温強度に優れた溶接材料として提案さ
れているものの必ずしも優れた溶接施工性を有していな
い。Although the welding material disclosed in the above-mentioned Japanese Patent Application Laid-Open No. 5-69187 has been proposed as a welding material having excellent high-temperature strength, it does not necessarily have excellent welding workability.
【０００７】また、高温強度を高めるＢは溶接割れ感受
性を高めることから含有させていないため、高温強度の
さらなる向上は期待できない。さらに溶接高温割れ感受
性に対する配慮はあるが、溶接施工性、即ちアークが安
定で、均一な溶接ビードの得られやすさ、裏波形成のし
やすさおよび溶接金属の湯流れなどの、実際の溶接作業
の容易さ、溶接ビードの形状の良い悪いに対する配慮が
なされておらず、溶接施工時に問題があった。[0007] Further, B, which enhances high-temperature strength, is not included because it enhances weld cracking susceptibility, so that further improvement in high-temperature strength cannot be expected. In addition, there are considerations for welding hot cracking susceptibility, but actual welding such as welding workability, that is, stable arc, easy to obtain a uniform weld bead, easy to form backwash, and molten metal flow. No consideration was given to the ease of operation and the good and bad shape of the weld bead, and there was a problem during welding.
【０００８】[0008]
【発明が解決しようとする課題】本発明の目的は、溶接
施工性に優れ、かつ溶接部の高温強度に優れた高Cr高Ｎ
オーステナイト鋼用溶接材料を提供することにある。SUMMARY OF THE INVENTION It is an object of the present invention to provide a high Cr high N steel which is excellent in welding workability and excellent in high temperature strength of a welded portion.
An object of the present invention is to provide a welding material for austenitic steel.
【０００９】[0009]
【課題を解決するための手段】本発明者らは高Cr高Ｎオ
ーステナイト鋼を溶接するときの溶接施工性について種
々研究した結果、溶接材料としてＳ、Siの関係、及び
Al、Ｏ（酸素）の関係が溶接施工性に影響しているこ
とを知見し、本発明を完成した。以下、成分含有量の％
は「重量％」を意味する。The present inventors have conducted various studies on welding workability when welding a high Cr high N austenitic steel, and have found that the relationship between S and Si as welding materials, and
The inventors have found that the relationship between Al and O (oxygen) affects the welding workability, and completed the present invention. Below,% of component content
Means "% by weight".
【００１０】図１は、後述する実施例の結果から溶接
ビード幅の変動と溶接材料中のＳ含有量との関係を示す
図であるが、同図からＳ含有量が0.005 ％以上となると
溶接ビード幅の変動が大きくなり、均一な溶接ビードが
得られなくなることがわかった。FIG. 1 is a diagram showing the relationship between the variation of the weld bead width and the S content in the welding material based on the results of the examples described later. From the same figure, when the S content becomes 0.005% or more, welding is performed. It was found that the variation of the bead width became large and a uniform weld bead could not be obtained.
【００１１】図２は、後述する実施例の結果から溶接
材料中のSi及びＳの含有量が溶接高温割れ性及び溶接施
工性（溶接ビード幅の変動及び裏波形成）とにどのよう
に影響するかを示す図であるが、同図からSi含有量が多
くなると溶接高温割れが発生し、Si含有量の少ない領域
では裏波の形成が不十分となることがわかった。FIG. 2 shows how the contents of Si and S in the welding material affect the welding hot cracking property and the welding workability (fluctuation of the weld bead width and formation of a backwash) from the results of the examples described later. This figure shows that when the Si content is increased, high-temperature cracking occurs in the weld, and in the region where the Si content is small, formation of the backwash is insufficient.
【００１２】図３は、後述する実施例の結果から溶接
材料中のAl及びＯ含有量が溶融金属の湯流れに及ぼす影
響を示す図であるが、同図からAl及びＯ含有量を適量に
することにより、湯流れが良くなることがわかる。FIG. 3 is a graph showing the effect of the Al and O contents in the welding material on the molten metal flow from the results of the examples described later. It can be seen that the flow of the hot water is improved by doing.
【００１３】以上の、及びからＳを少なく制限
し、SiをＳとの関連で適量含有させること、Al及びＯ含
有量を適量にすることにより溶接施工性が改善されるこ
とを知見し、本発明を完成した。From the above, it was found that by limiting the amount of S to a small amount, to contain an appropriate amount of Si in relation to S, and to make the Al and O contents appropriate, welding workability is improved. Completed the invention.
【００１４】本発明は、次の溶接材料を要旨としてい
る。The gist of the present invention is the following welding materials.
【００１５】『(1) Ｃ：0.03〜0.10％、Mn：1.20〜8.00
％、Ｂ：0.01％以下、Nb：0.01〜0.70％、Cr：23.0〜2
8.0％、Ni：18.0〜30.0％、Mo：0.50〜1.50％、Ｎ：0.2
0〜0.40％、Al：0.01％以下、およびSi：(0.3−40Ｓ)
〜0.50％を含有し、残部がFeおよび不可避的不純物から
なり、不純物としてのＰは0.01％以下、Ｓは 0.005％以
下であり、かつAl＋Ｏが0.02％以下である高Ｃｒ高Ｎオ
ーステナイト鋼用溶接材料。[(1) C: 0.03 to 0.10%, Mn: 1.20 to 8.00
%, B: 0.01% or less, Nb: 0.01 to 0.70%, Cr: 23.0 to 2
8.0%, Ni: 18.0-30.0%, Mo: 0.50-1.50%, N: 0.2
0 to 0.40%, Al: 0.01% or less, and Si: (0.3-40S)
Welding for high Cr high N austenitic steels containing up to 0.50%, with the balance being Fe and unavoidable impurities, P as impurities being 0.01% or less, S being 0.005% or less, and Al + O being 0.02% or less. material.
【００１６】(2) (1) の材料において、Ｃ：0.10％を超
えて0.24％まで、Mn：8.00％以下及びＮ：0.15〜0.35％
とした高Ｃｒ高Ｎオーステナイト鋼用溶接材料。(2) In the material of (1), C: more than 0.10% to 0.24%, Mn: 8.00% or less, and N: 0.15 to 0.35%
Welding material for high Cr high N austenitic steel.
【００１７】上記(1) 及び(2) の材料には、必要に応じ
てMg：0.02％以下、Ca：0.02％以下の１種または２種、
またはCu：1.00〜4.0 ％を含有させることができる。』The materials (1) and (2) may include one or two of Mg: 0.02% or less and Ca: 0.02% or less, if necessary.
Alternatively, Cu: 1.00 to 4.0% can be contained. 』
【００１８】[0018]
【作用】次に、本発明の溶接材料の構成成分しとて限定
した理由について述べる。Next, the reason why the components of the welding material of the present invention are limited will be described.
【００１９】Ｃ：0.03〜0.10％または0.10％を超えて0.
24％まで Ｃは、高温引張強度およびクリープ強度の向上に寄与す
る元素である。しかし、過剰に含有すると炭窒化物とし
て析出し、高温引張強度およびクリープ強度の低下を招
くので、Ｎ量が0.20〜0.40％の時にはＣ：0.03〜0.10
％、Ｎ量が0.15〜0.35％の時、Ｃ：0.10〜0.24％とし
た。C: 0.03 to 0.10% or more than 0.10%
Up to 24% C is an element that contributes to the improvement of high temperature tensile strength and creep strength. However, if it is contained excessively, it precipitates as carbonitride and lowers the high-temperature tensile strength and creep strength. Therefore, when the N content is 0.20 to 0.40%, C: 0.03 to 0.10
%, When the N content is 0.15 to 0.35%, C: 0.10 to 0.24%.
【００２０】Mn：1.20〜8.00％または8.00％以下 Mnは、溶接材料の溶製時に脱酸剤として添加され、また
溶接時にＳを固定して高温割れ感受性の低減に寄与する
元素である。さらに、溶融金属中のＮの活量を下げる作
用があり、アーク雰囲気中へのＮの飛散を抑制し、溶接
金属中へのＮの歩留をよくし、高温引張強度およびクリ
ープ強度の向上に寄与する。従って、Ｎ含有量が0.20〜
0.40％の時には下限を1.20％とする。ただし、過度の含
有は溶接金属の脆化を招くためその上限を8.00％とし、
好ましいＭｎの含有量は1.20〜6.00％である。Mn: 1.20 to 8.00% or 8.00% or less Mn is an element that is added as a deoxidizer during melting of a welding material and fixes S during welding to contribute to a reduction in susceptibility to hot cracking. Furthermore, it has the effect of reducing the activity of N in the molten metal, suppresses the scattering of N in the arc atmosphere, improves the yield of N in the weld metal, and improves the high-temperature tensile strength and creep strength. Contribute. Therefore, the N content is 0.20 to
When it is 0.40%, the lower limit is 1.20%. However, excessive content causes embrittlement of the weld metal, so the upper limit is 8.00%,
The preferred Mn content is 1.20 to 6.00%.
【００２１】Cr：23.0〜28.0％ Crは、溶接金属の高温強度、耐酸化性、耐食性の確保の
ために必要であるが、過剰に含有させると溶接材料とし
て線材に加工するときの熱間加工性を損なう元素であ
る。したがって、その含有量は23.0〜28.0％とした。Cr: 23.0-28.0% Cr is necessary for securing the high-temperature strength, oxidation resistance, and corrosion resistance of the weld metal. However, if it is contained excessively, hot working when working into a wire as a welding material is required. It is an element that impairs the properties. Therefore, the content was set to 23.0 to 28.0%.
【００２２】Ni：18.0〜30.0％ Niは、溶接金属のオーステナイトを安定にし、高温強度
の向上に寄与する元素である。また、δフェライトを晶
出させて溶接高温割れ感受性を低下させるが、その一方
でδフェライトは高温使用中での脆化の原因となる。そ
こで本発明ではδフェライトの晶出を抑制し、高温脆化
を防止するとともにNiは高価な元素であるため経済性の
観点から18.0〜30.0％とした。Ni: 18.0-30.0% Ni is an element that stabilizes austenite of a weld metal and contributes to improvement in high-temperature strength. In addition, δ ferrite is crystallized to reduce welding hot cracking sensitivity, while δ ferrite causes embrittlement during high temperature use. Therefore, in the present invention, crystallization of δ-ferrite is suppressed, high-temperature embrittlement is prevented, and Ni is an expensive element.
【００２３】Nb：0.01〜0.70％ Nbは、溶接金属中で炭窒化物として微細析出することに
より高温強度の向上に寄与する元素である。しかし、過
剰に含有すると溶接高温割れ感受性を高め、δフェライ
トを晶出させない条件下では特に大きく影響を及ぼす。
そこでその含有量は0.01〜0.70％とした。Nb: 0.01 to 0.70% Nb is an element that contributes to improvement in high-temperature strength by being finely precipitated as a carbonitride in a weld metal. However, if the content is excessive, the susceptibility to welding hot cracking is increased, and particularly under conditions where δ ferrite is not crystallized, there is a significant effect.
Therefore, the content is set to 0.01 to 0.70%.
【００２４】Mo：0.50〜1.50％ Moは、凝固組織のマトリックスに固溶し、溶接金属の高
温強度を高める元素である。しかし、0.50％未満ではそ
の効果が小さく、また、1.50％を超えるとその効果が飽
和するばかりか、耐食性劣化の原因となるため0.50〜1.
50％とした。Mo: 0.50-1.50% Mo is an element that forms a solid solution in the matrix of the solidified structure and increases the high-temperature strength of the weld metal. However, if the content is less than 0.50%, the effect is small, and if it exceeds 1.50%, the effect is not only saturated, but also causes deterioration of corrosion resistance.
50%.
【００２５】Ｂ：0.01％以下 Ｂは、溶接金属のオーステナイトの粒界に偏析してクリ
ープ強度の向上に寄与する元素である。しかし、過剰に
含有させると溶接高温割れを助長するため0.01％以下と
した。B: 0.01% or less B is an element that segregates at the austenite grain boundary of the weld metal and contributes to improvement in creep strength. However, if it is contained excessively, it promotes welding hot cracking, so that the content is made 0.01% or less.
【００２６】Ｎ：0.20〜0.40％、または0.15〜0.35％ Ｎは、凝固組織のマトリックスに固溶してこれを強化す
るとともに一部は窒化物として析出し、析出強化を行
い、溶接金属の高温強度を高める元素である。しかし、
過剰に含有させると高温使用中に多量の炭窒化物を析出
させるため脆化の原因となる。そのため、Ｃ含有量が0.
03〜0.10％のときＮを0.20〜0.40％、Ｃ含有量が0.10〜
0.24％のときＮを0.15〜0.35％とした。N: 0.20 to 0.40% or 0.15 to 0.35% N forms a solid solution in the matrix of the solidification structure and strengthens it, and also precipitates partly as nitrides, performs precipitation strengthening, and enhances the high temperature of the weld metal. It is an element that increases strength. But,
If it is contained excessively, a large amount of carbonitride is precipitated during use at a high temperature, which causes embrittlement. Therefore, C content is 0.
When the concentration is 03 to 0.10%, N is 0.20 to 0.40%, and the C content is 0.10 to
When it is 0.24%, N is set to 0.15 to 0.35%.
【００２７】Al：0.01％以下 Alは、溶接材料の溶製時に脱酸剤として添加されるが、
多量に含有すると溶接中にスラグの生成を促し、溶接金
属の湯流れおよび溶接ビードの均一性を劣化させ、溶接
施工性を著しく低下させる。さらに、裏波形成する溶接
条件領域を狭くするためAl含有量は0.01％以下とした。Al: 0.01% or less Al is added as a deoxidizer at the time of melting the welding material.
If contained in a large amount, slag is promoted during welding, the molten metal flow and the uniformity of the weld bead are deteriorated, and the weldability is significantly reduced. Further, the Al content was set to 0.01% or less in order to narrow the welding condition region in which a backwash was formed.
【００２８】Ｐ：0.01％以下 Ｐは、不純物として溶接材料に含有される元素であり、
溶接中の溶接金属が凝固時に低融点の共晶物を形成する
ので、溶接高温割れを発生させる。そのため許しえる含
有量を0.01％以下とした。本発明では、溶接金属の高温
強度を確保するためNb、Ｂを含有させる。しかし、Nb、
Ｂは高温割れ感受性を高める元素であるので、本発明で
はＰ含有量を低くするのが好ましい。P: 0.01% or less P is an element contained in the welding material as an impurity,
Since the weld metal during welding forms a low melting point eutectic during solidification, hot cracking occurs. Therefore, the allowable content is set to 0.01% or less. In the present invention, Nb and B are contained to secure the high-temperature strength of the weld metal. But Nb,
Since B is an element that enhances hot cracking susceptibility, it is preferable in the present invention to reduce the P content.
【００２９】Ｓ：0.005 ％以下 Ｓは、溶接時の裏波を形成する溶接条件領域を拡大する
元素として知られているが、後述する実施例の結果から
得た図１からわかるように、過剰に含有させるとアーク
の安定性を欠き溶融池を不安定にし、溶接ビード幅の均
一性を劣化させる。さらに、溶接金属の凝固時に低融点
の共晶物を形成し、Ｐ＋Ｓが0.02％を超えると溶接高温
割れを発生させる。そのため、溶接施工性と耐溶接高温
割れ性の観点から、その許しえるＳ含有量を 0.005％以
下とした。Ｓ含有量を 0.005％以下とすると裏波形成能
は低下するが、Si含有量をＳ含有量との関係で調整する
ことにより裏波形成能の改善を図った。S: 0.005% or less S is known as an element that expands a welding condition region for forming a backwash at the time of welding. However, as can be seen from FIG. If it is contained, the stability of the arc is lacking and the molten pool becomes unstable, and the uniformity of the weld bead width is deteriorated. Further, a eutectic having a low melting point is formed during the solidification of the weld metal, and when P + S exceeds 0.02%, high-temperature welding cracks occur. Therefore, the allowable S content is set to 0.005% or less from the viewpoint of welding workability and resistance to hot cracking. When the S content is set to 0.005% or less, the backwashing ability decreases, but by adjusting the Si content in relation to the S content, the backwashing ability is improved.
【００３０】Si：(0.3−40Ｓ) 〜0.50％ Siは、溶接材料の溶製時に脱酸剤として添加されるが、
溶接時にはＳと同様に裏波を形成する溶接条件領域を拡
大する元素である。したがって、後述する実施例の結果
から得た図２からわかるように、Ｓ含有量との関係でSi
含有量は(0.3−40Ｓ) ％以上必要である。しかし、過剰
に含有すると溶接高温割れ感受性を高めるので0.50％以
下とした。Si: (0.3-40S) -0.50% Si is added as a deoxidizer at the time of melting the welding material.
At the time of welding, like S, it is an element that expands the welding condition region that forms a backwash. Therefore, as can be seen from FIG. 2 obtained from the results of the examples described below, Si
The content must be (0.3-40S)% or more. However, if it is contained excessively, the susceptibility to welding hot cracking increases, so the content was made 0.50% or less.
【００３１】Ca、Mg：それぞれ0.02％以下 Ca、Mgは、必要に応じ添加される元素であり、溶接金属
の溶接高温割れ感受性の低減および溶接材料としての線
材加工時の熱間加工性の改善に有効である。しかし、過
剰に含有させると溶接金属中の介在物が増加し、高温強
度を害するため0.02％以下とした。Ca, Mg: 0.02% or less, respectively Ca and Mg are elements that are added as necessary, and reduce the susceptibility of the weld metal to high-temperature welding and improve the hot workability during wire processing as a welding material. It is effective for However, if it is contained excessively, inclusions in the weld metal increase, and the high-temperature strength is impaired.
【００３２】Cu：1.0 〜4.0 ％ Cuも必要に応じ添加される元素であり、溶接金属中にCu
富化層として微細析出し、高温引張強さおよびクリープ
強度の向上に寄与する。しかし、その含有量が1.0 ％未
満ではその効果がなく、4.0 ％を超えると延性を低下さ
せるので、その含有量を1.0 〜4.0 ％とした。Cu: 1.0-4.0% Cu is also an element added as necessary, and Cu is contained in the weld metal.
It finely precipitates as an enriched layer and contributes to improvement of high temperature tensile strength and creep strength. However, if the content is less than 1.0%, the effect is not obtained, and if it exceeds 4.0%, the ductility is reduced. Therefore, the content is set to 1.0 to 4.0%.
【００３３】Al＋Ｏ：0.02％以下 Ｏは溶接材料の溶製中に不可避的に含有される元素であ
る。しかし、後述する実施例の結果から得た図３からわ
かるように、Al含有量が低い場合でもＯを過度に含有す
ると、溶接中に溶融金属中のスラグの生成を助長し、湯
流れを劣化させ溶接施工性を低下させる。特にAl系のス
ラグは湯流れを劣化させるためAl＋Ｏを0.02％以下とし
た。Al + O: 0.02% or less O is an element inevitably contained during melting of the welding material. However, as can be seen from FIG. 3 obtained from the results of the examples described later, even when the Al content is low, if O is excessively contained, it promotes the generation of slag in the molten metal during welding and deteriorates the molten metal flow. To reduce welding workability. In particular, in Al-based slag, Al + O is set to 0.02% or less in order to deteriorate the flow of molten metal.
【００３４】なお、本発明の溶接材料を用いて溶接する
材料（母材）は、例えば主要合金成分がCr：17〜28％、
Ni：18〜25％、Ｃ：0.02〜0.1 ％、Ｎ：0.15〜0.3 ％、
Nb：0.2〜0.8 ％、Ｂ： 0.002〜0.006 ％の高Cr高Ｎ系
のオーステナイト鋼である。The material (base metal) to be welded using the welding material of the present invention is, for example, a main alloy component having a Cr content of 17 to 28%,
Ni: 18 to 25%, C: 0.02 to 0.1%, N: 0.15 to 0.3%,
Nb: 0.2-0.8%, B: 0.002-0.006% High Cr high N austenitic steel.
【００３５】[0035]
【実施例】以下、本発明の実施例を比較例と対比させ
て、更に詳しく説明する。EXAMPLES Examples of the present invention will be described in more detail in comparison with comparative examples.
【００３６】溶接母材として表１に示す化学組成を有す
る高Cr高Ｎ系のオーステナイト鋼を用い、タングステン
・イナートガス溶接法（ＴＩＧ溶接）により、表２に示
す各種溶接材料の性能比較を行った。なお、この母材は
高Cr高ＮでかつNb、Ｂを含み600℃での 105時間クリー
プ強度が 18.5kgf/mm2のボイラ用鋼管である。Using a high Cr high N austenitic steel having a chemical composition shown in Table 1 as a welding base material, the performance of various welding materials shown in Table 2 was compared by a tungsten inert gas welding method (TIG welding). . Incidentally, the base material is high Cr and high N a and Nb, 10 5 h creep strength at 600 ° C. include B is boiler steel tube 18.5kgf / mm 2.
【００３７】[0037]
【表１】 [Table 1]
【００３８】溶接材料は表２〜表５に示す組成を有する
32種類の溶接材料であり、すべて実験室で真空溶製後、
外径２mmの線材に加工し溶接に供した。The welding materials have the compositions shown in Tables 2 to 5.
32 kinds of welding materials, all of which are vacuum-melted in the laboratory,
It was processed into a wire rod having an outer diameter of 2 mm and provided for welding.
【００３９】[0039]
【表２】 [Table 2]
【００４０】[0040]
【表３】 [Table 3]
【００４１】[0041]
【表４】 [Table 4]
【００４２】[0042]
【表５】 [Table 5]
【００４３】図４、図５及び図６は、溶接継手性能を評
価するための開先加工形状と溶接割れ試験材及び溶接継
手強度、溶接施工性試験材の製作を説明するための図で
ある。FIGS. 4, 5 and 6 are diagrams for explaining the production of a grooved shape, a weld crack test material, a weld joint strength, and a weldability test material for evaluating weld joint performance. .
【００４４】溶接割れ試験材は、図４に示した60°の開
先４の加工を施した母材１（鋼管）を、図５に示すよう
に鋼からなる拘束棒２に拘束溶接部３ですみ肉溶接して
製作した。溶接施工は、図５に示す溶接割れ試験材の開
先部４に対して供試溶接材料を用いて、試験材を回転さ
せながら下向きのＴＩＧ溶接法により多層盛り溶接を行
った。その際、拘束されているために溶接による熱応力
が生じて割れが発生しやすくなる。As shown in FIG. 4, the welding crack test material is obtained by bonding a base material 1 (steel pipe) having a groove 4 of 60 ° shown in FIG. 4 to a restraining rod 2 made of steel as shown in FIG. It was made by welding with fillet. In the welding operation, multi-layer welding was performed on the groove 4 of the weld crack test material shown in FIG. 5 by using a test welding material by a downward TIG welding method while rotating the test material. At this time, since it is constrained, thermal stress is generated by welding, and cracks are likely to occur.
【００４５】溶接継手強度、溶接施工性試験材は図４に
示した60°の開先４の加工を施した母材１（鋼管）を、
図６に示すように突き合わせ、開先部４に対して供試溶
接材料を用いて試験材を回転させながら下向きＴＩＧ溶
接法により多層盛り溶接を行った。The base material 1 (steel pipe) subjected to the processing of the groove 4 at 60 ° shown in FIG.
As shown in FIG. 6, multi-layer welding was performed by the downward TIG welding method while the test material was rotated with respect to the groove 4 using the test welding material.
【００４６】図７は、溶接部の側曲げ試験片を示す図で
あるが、同図に示すように溶接金属が試験片の中央にな
るように試験片を採取した。これは溶接高温割れの有無
を調べるための試験であり、側曲げ試験片の溶接金属部
を、試験片厚さの２倍の曲げ半径(10mm)で 180°に曲
げ、溶接金属での割れの有無を調べるものである。FIG. 7 is a view showing a side bending test piece at the welded portion. The test piece was sampled so that the weld metal was at the center of the test piece as shown in FIG. This is a test to check for weld hot cracks. The weld metal of the side bending test piece was bent to 180 ° with a bending radius (10 mm) twice the thickness of the test piece, This is to check for the presence or absence.
【００４７】高温引張試験は、上記側曲げ試験にて割れ
のないものについて、JIS Z2201 に規定されている試験
片を採取し、 600℃にて行い、母材の設計基準となる許
容応力値以上を保障する 47.2kgf/mm2を判定基準とし、
これを超えるものを合格とした。In the high-temperature tensile test, a test piece specified in JIS Z2201 was sampled for a sample having no crack in the above-mentioned side bending test, and the test piece was subjected to a temperature of 600 ° C. the guarantee 47.2kgf / mm 2 and a determination reference,
Those exceeding this were judged to be acceptable.
【００４８】クリープ破断試験は、母材の破断時間が約
3000時間となる条件、即ち試験温度600℃、荷重 30kgf/
mm2の条件で試験を行い、破断時間を調べた。評価の判
断は、母材の破断時間の80％である2400時間とし、これ
に達しないものをクリープ強度不足とした。In the creep rupture test, the rupture time of the base material was about
Conditions for 3000 hours, ie, test temperature 600 ° C, load 30kgf /
The test was performed under the condition of mm 2 to determine the rupture time. The evaluation was judged to be 2400 hours, which is 80% of the fracture time of the base material, and those that did not reach this were regarded as insufficient creep strength.
【００４９】次に、溶接施工性の評価は、溶接ビード
幅の均一性、裏波形成能及び溶融池における湯流れ
の良否で行った。Next, the weldability was evaluated based on the uniformity of the weld bead width, the ability to form a backwash, and the quality of the molten metal flow in the molten pool.
【００５０】溶接ビードの均一性は、得られた全円周の
溶接ビード部のビード幅を等間隔に測定し、最大ビード
幅と最小ビード幅の差が３mm以下を合格とした。Regarding the uniformity of the weld bead, the bead width of the obtained weld bead portion on the entire circumference was measured at regular intervals, and the difference between the maximum bead width and the minimum bead width was 3 mm or less.
【００５１】裏波形成能は、初層溶接で全周にわたり裏
ビードが形成されるか否かで良否判定を行った。The quality of the underside formation was determined by whether or not a back bead was formed over the entire circumference by the first layer welding.
【００５２】湯流れの良否判定は、溶接中の溶融池の様
子を高速ビデオカメラにより直接観察し判定した。The quality of the molten metal flow was determined by directly observing the state of the molten pool during welding with a high-speed video camera.
【００５３】表６及び表７は、継手性能および溶接施工
性の評価結果を示したものである。Tables 6 and 7 show the evaluation results of the joint performance and welding workability.
【００５４】溶接高温割れの○は割れなし、×は割れあ
りを示す。高温引張強度およびクリープ強度の○は強度
十分、×は強度不足を示す。さらに、溶接施工性に関し
ては○は良好、×は不良を示す。In the high-temperature welding cracks, ○ indicates no cracking and X indicates cracking. ○ of high temperature tensile strength and creep strength indicates sufficient strength, and X indicates insufficient strength. Further, regarding welding workability, ○ indicates good, and X indicates poor.
【００５５】[0055]
【表６】 [Table 6]
【００５６】[0056]
【表７】 [Table 7]
【００５７】表６の継手No. JA１〜JA17より明らかなよ
うに、本発明例の溶接材料Ａ１〜Ａ14は、溶接入熱13kJ
/cm 、層間温度 250℃の苛酷な条件においても溶接高温
割れの発生がなく、引張強さ及びクリープ強度も十分で
あり、溶接施工性も全ての項目で良好である。また、溶
接材料Ａ１では溶接入熱９〜13kJ/cm 、層間温度 150〜
250 ℃、管サイズ40〜60mmの広範な溶接条件にて優れた
高温強度および溶接施工性を有している。As is clear from the joint Nos. JA1 to JA17 in Table 6, the welding materials A1 to A14 of the present invention have a welding heat input of 13 kJ.
Even under severe conditions of / cm 2 and an interlayer temperature of 250 ° C, there is no occurrence of hot cracking, sufficient tensile strength and creep strength, and good weldability in all items. The welding material A1 has a welding heat input of 9 to 13 kJ / cm and an interlayer temperature of 150 to 130 kJ / cm.
It has excellent high-temperature strength and weldability under a wide range of welding conditions at 250 ° C and a pipe size of 40 to 60 mm.
【００５８】これに対して比較例の溶接材料では、表７
に示すようにＢ１、Ｂ３は、Ｓ含有量が0.008 、0.020
％と高く、アークの安定性に欠け溶接ビード幅の変動が
3.6、4.6 mmと大きく、溶接ビード幅は不均一となっ
た。また、Ｂ３ではＰ＋Ｓが0.023 ％と高いため、高温
割れが発生した。On the other hand, in the welding material of the comparative example, Table 7
As shown in Table 1, B1 and B3 have S contents of 0.008 and 0.020.
%, And lacks arc stability, causing variations in weld bead width
It was large, 3.6 and 4.6 mm, and the weld bead width was uneven. Further, in B3, since P + S was as high as 0.023%, hot cracking occurred.
【００５９】Ｂ２は、Ｃ含有量が0.01％と低いため、高
温引張強さ、クリープ破断寿命ともに低く、またＳ含有
量が0.012 ％と高いため、アークの安定性に欠け溶接ビ
ード幅の変動が4.2 mmと大きく、溶接ビード幅は不均一
となった。B2 has a low C content of 0.01% and therefore has a low high-temperature tensile strength and a low creep rupture life, and a high S content of 0.012% and lacks arc stability. As large as 4.2 mm, the weld bead width was not uniform.
【００６０】Ｂ４は、Si含有量の下限が(0.3−40S)＝0.
18％に対して0.11と低く、裏波が十分形成されなかっ
た。Ｂ５は、Si含有量の下限が(0.3−40S)＝0.10％に対
して0.09と低く、裏波が十分形成されず、またAl＋Ｏ含
有量が0.023 ％と高いため、スラグの生成を助長して湯
流れが悪い。B4 has a lower limit of the Si content of (0.3-40S) = 0.
It was as low as 0.11 with respect to 18%, and the backwash was not sufficiently formed. In B5, the lower limit of the Si content is as low as 0.09 with respect to (0.3-40S) = 0.10%, and the backwash is not sufficiently formed, and the Al + O content is as high as 0.023%. Hot water is poor.
【００６１】Ｂ６は、Al含有量が0.035 ％と高いため、
スラグの生成を助長して湯流れが悪く、また裏波が十分
形成されなかった。さらに、ヒード幅の変動も3.2mm と
大きく、溶接ビード幅は不均一となった。Since B6 has a high Al content of 0.035%,
The formation of slag was promoted, the flow of the molten metal was poor, and the backwash was not sufficiently formed. Furthermore, the variation of the head width was as large as 3.2 mm, and the weld bead width became uneven.
【００６２】Ｂ７は、Ｎ含有量が0.18％と低いため、高
温引張強さ、クリープ強度ともに不十分であり、またAl
＋Ｏ含有量が0.022 ％と高いため、スラグの生成を助長
して湯流れが悪い。Ｂ８は、Ｃ含有量が0.01％と低いた
め、高温引張強さ、クリープ強度ともに不十分であっ
た。Since B7 has a low N content of 0.18%, both the high-temperature tensile strength and the creep strength are insufficient.
Since the + O content is as high as 0.022%, slag formation is promoted, and the molten metal flow is poor. In B8, since the C content was as low as 0.01%, both the high temperature tensile strength and the creep strength were insufficient.
【００６３】Ｂ９は、Ｐ含有量が0.015 ％と高いため、
溶接施工性は良好であったが、溶接高温割れが発生し
て、溶接継手部の強度評価ができなかった。Ｂ10は、Si
含有量が0.81％と高いため、溶接施工性は良好であった
が、溶接高温割れが発生した。Since B9 has a high P content of 0.015%,
Although the weldability was good, high-temperature cracking occurred and the strength of the welded joint could not be evaluated. B10 is Si
Since the content was as high as 0.81%, weldability was good, but hot cracking occurred.
【００６４】これについては溶接継手部の強度評価をし
なかった。Regarding this, the strength of the welded joint was not evaluated.
【００６５】Ｂ11は、Mn含有量が0.71％と低いため、高
温引張強さ、クリープ強度ともに不十分であった。Ｂ12
は、Nb含有量が0.002 ％と低いため、クリープ強度が不
十分であった。Ｂ13は、Ｎ含有量が0.11％と低いため、
高温引張強さ、クリープ強度ともに不十分であった。B11 was insufficient in both high-temperature tensile strength and creep strength because the Mn content was as low as 0.71%. B12
Has a low Nb content of 0.002%, and therefore has insufficient creep strength. B13 has a low N content of 0.11%,
Both high temperature tensile strength and creep strength were insufficient.
【００６６】Ｂ14は、Ｓ含有量が0.011 ％と高く、アー
クの安定性に欠け溶接ビード幅の変動が4.0 mmと大き
く、溶接ビード幅は不均一となった。Ｂ15は、Si含有量
の下限が(0.3−40S)＝0.10％に対して0.07％と低く、Al
及びAl＋Ｏ含有量が0.012 及び0.022 ％と高いため、ス
ラグの生成を助長して湯流れが悪く、また十分な裏波が
形成できない。さらに、ビード変動幅も3.2mm と大き
く、溶接ビード幅は不均一となった。B14 had a high S content of 0.011%, lacked arc stability, and had a large variation in weld bead width of 4.0 mm, resulting in a non-uniform weld bead width. In B15, the lower limit of the Si content is as low as 0.07% with respect to (0.3-40S) = 0.10%.
Also, since the Al + O content is as high as 0.012 and 0.022%, slag formation is promoted, the flow of the molten metal is poor, and a sufficient backwash cannot be formed. In addition, the bead fluctuation width was as large as 3.2 mm, and the weld bead width became uneven.
【００６７】Ｂ16は、Ｃ含有量が0.35％、Ｐ含有量が0.
012 ％と高いため、溶接施工性は良好であったが、溶接
高温割れが発生した。これについては溶接継手部の強度
評価をしなかった。B16 has a C content of 0.35% and a P content of 0.3%.
The weldability was good because of the high 012%, but welding hot cracking occurred. For this, the strength of the welded joint was not evaluated.
【００６８】Ｂ17は、Ｎ含有量が0.11％と低いため、高
温引張強さ、クリープ強度ともに不十分であった。Ｂ18
は、Ｎ含有量が0.37％と高いため、高温引張強さ、クリ
ープ強度ともに不十分であった。Since B17 had a low N content of 0.11%, both the high temperature tensile strength and the creep strength were insufficient. B18
Since the N content was as high as 0.37%, both the high temperature tensile strength and the creep strength were insufficient.
【００６９】これらの結果から溶接施工性及び溶接高温
割れ性と溶接材料の成分元素との関係を図により説明す
る。From these results, the relationship between the welding workability and the weld hot cracking property and the constituent elements of the welding material will be described with reference to the drawings.
【００７０】図１は、溶接ビード幅の均一性と溶接材料
のＳ含有量との関係を示す図であるが、同図に示すよう
にＳ含有量が0.005 ％を超えると溶接ビード幅の変動が
３mmよりも大きくなり、溶接施工性が悪くなることがわ
かる。FIG. 1 is a graph showing the relationship between the uniformity of the weld bead width and the S content of the welding material. As shown in FIG. 1, when the S content exceeds 0.005%, the variation of the weld bead width is varied. Is larger than 3 mm, which indicates that the welding workability is deteriorated.
【００７１】図２は、溶接材料のSi及びＳ含有量と溶接
高温割れ、溶接ビード幅及び裏波形成性との関係を示す
図であるが、同図に示すようにSi含有量が高くなると溶
接高温割れが発生し、Ｓ含有量が高くなると前述のよう
に溶接ビード幅の変動が大きくなる。また、Si含有量が
低くなると裏波の形成が悪くなるので、Ｓ含有量との関
係で（ 0.3−40Ｓ）以上含有させる必要があることがわ
かる。FIG. 2 is a graph showing the relationship between the Si and S contents of the welding material and the hot cracking, the width of the weld bead, and the formation of the undercut. As shown in FIG. As described above, when welding high-temperature cracking occurs and the S content increases, the fluctuation of the weld bead width increases. In addition, the lower the Si content is, the worse the formation of a backside impairment. Therefore, it can be seen that it is necessary to contain Si (0.3-40S) or more in relation to the S content.
【００７２】図３は、溶接材料のAl及びＯ含有量と溶融
金属の湯流れとの関係を示す図であるが、同図に示すよ
うにAl及びＯ含有量が高くなると溶融金属の湯流れが悪
くなる。またAl含有量が低い場合でもＯ含有量が高くな
ると溶融金属の湯流れが悪くなり、Al＋Ｏ含有量を0.02
％以下にするのが好ましいことがわかる。FIG. 3 is a diagram showing the relationship between the Al and O contents of the welding material and the molten metal flow. As shown in FIG. 3, as the Al and O contents increase, the molten metal flow increases. Gets worse. Also, even when the Al content is low, if the O content is high, the molten metal flow becomes worse, and the Al + O content is reduced to 0.02.
% Is preferable.
【００７３】[0073]
【発明の効果】本発明の高Cr高Ｎオーステナイト鋼用溶
接材料は、ほぼ母材と同成分の組成を有するので、従来
の高Ni合金用溶接材料に比して安価である。また、広範
な溶接条件下で優れた溶接施工性を有し、かつ溶接継手
部は母材に匹敵する優れた高温強度を有するものであ
る。The welding material for high Cr high N austenitic steel according to the present invention has a composition substantially the same as that of the base metal, and therefore is less expensive than conventional welding materials for high Ni alloys. Further, it has excellent welding workability under a wide range of welding conditions, and the welded joint has excellent high-temperature strength comparable to that of the base metal.
【図１】溶接材料のＳ含有量と溶接ビード幅の均一性と
の関係を示す図である。FIG. 1 is a diagram showing the relationship between the S content of a welding material and the uniformity of a weld bead width.
【図２】溶接材料のＳ及びSi含有量が溶接高温割れと溶
接施工性に及ぼす影響を示す図である。FIG. 2 is a view showing the effect of the S and Si contents of a welding material on welding hot cracking and welding workability.
【図３】溶接材料のAl及びＯ含有量が湯流れに及ぼす影
響を示す図である。FIG. 3 is a diagram showing the effect of the Al and O contents of the welding material on the molten metal flow.
【図４】拘束割れ試験材の開先形状を示す図である。FIG. 4 is a diagram showing a groove shape of a restrained crack test material.
【図５】溶接高温割れ試験材の形状を示す図である。FIG. 5 is a view showing the shape of a weld hot crack test material.
【図６】溶接継手強度及び溶接施工性を評価する試験片
の形状を示す図である。FIG. 6 is a view showing the shape of a test piece for evaluating the strength of a weld joint and weldability.
【図７】溶接高温割れ試験後に高温割れを検出するため
に行う側曲げ試験片の形状を示す図である。FIG. 7 is a view showing the shape of a side bending test piece for detecting a hot crack after a welding hot crack test.
１．母材 ２．拘束棒
３．拘束溶接部 ４．開先 ５．溶接金属1. Base material 2. Restraint bar
3. Restraint weld 4. Groove 5 Weld metal
フロントページの続き (56)参考文献 特開 平１−202395（ＪＰ，Ａ) 特開 昭63−309392（ＪＰ，Ａ) 特開 平５−69187（ＪＰ，Ａ) 特開 平４−143255（ＪＰ，Ａ) 特開 昭62−183994（ＪＰ，Ａ) 特開 平５−311337（ＪＰ，Ａ) 特開 平７−60481（ＪＰ，Ａ) 特開 平８−71784（ＪＰ，Ａ) (58)調査した分野(Int.Cl.6，ＤＢ名) B23K 35/30Continuation of front page (56) References JP-A-1-202395 (JP, A) JP-A-63-309392 (JP, A) JP-A-5-69187 (JP, A) JP-A-4-143255 (JP) JP-A-6-183994 (JP, A) JP-A-5-311337 (JP, A) JP-A-7-60481 (JP, A) JP-A-8-71784 (JP, A) (58) Field surveyed (Int. Cl. 6 , DB name) B23K 35/30
Claims (6)
8.00％、Ｂ：0.01％以下、Nb：0.01〜0.70％、Cr：23.0
〜28.0％、Ni：18.0〜30.0％、Mo：0.50〜1.50％、Ｎ：
0.20〜0.40％、Al：0.01％以下、Si：(0.3−40Ｓ) 〜0.
50％を含有し、残部がFeおよび不可避的不純物からな
り、不純物としてのＰは0.01％以下、Ｓは 0.005％以下
であり、かつAl＋Ｏが0.02％以下であることを特徴とす
る高Cr高Nオーステナイト鋼用Ｂ含有ＴＩＧ溶接用溶接
材料。(1) C: 0.03-0.10%, Mn: 1.20-% by weight
8.00%, B: 0.01% or less, Nb: 0.01-0.70%, Cr: 23.0
28.0%, Ni: 18.0-30.0%, Mo: 0.50-1.50%, N:
0.20 to 0.40%, Al: 0.01% or less, Si: (0.3 to 40S) to 0.
High Cr high N characterized by containing 50%, the balance being Fe and unavoidable impurities, P as impurities is 0.01% or less, S is 0.005% or less, and Al + O is 0.02% or less. B-containing TIG welding material for austenitic steel.
8.00％、Ｂ：0.01％以下、Nb：0.01〜0.70％、Cr：23.0
〜28.0％、Ni：18.0〜30.0％、Mo：0.50〜1.50％、Ｎ：
0.20〜0.40％、Al：0.01％以下、Si：(0.3−40Ｓ) 〜0.
50％およびMg：0.02％以下、Ca：0.02％以下の１種また
は２種を含有し、残部がFeおよび不可避的不純物からな
り、不純物としてのＰは0.01％以下、Ｓは 0.005％以下
であり、かつAl＋Ｏが0.02％以下であることを特徴とす
る高Cr高Nオーステナイト鋼用Ｂ含有ＴＩＧ溶接用溶接
材料。2. C .: 0.03 to 0.10%, Mn: 1.20 to 0.2% by weight
8.00%, B: 0.01% or less, Nb: 0.01-0.70%, Cr: 23.0
28.0%, Ni: 18.0-30.0%, Mo: 0.50-1.50%, N:
0.20 to 0.40%, Al: 0.01% or less, Si: (0.3 to 40S) to 0.
One or two of 50%, Mg: 0.02% or less, and Ca: 0.02% or less, with the balance being Fe and unavoidable impurities. P as an impurity is 0.01% or less and S is 0.005% or less. A B-containing TIG welding material for high Cr high N austenitic steel, wherein Al + O is 0.02% or less.
8.00％、Ｂ：0.01％以下、Nb：0.01〜0.70％、Cr：23.0
〜28.0％、Ni：18.0〜30.0％、Mo：0.50〜1.50％、Ｎ：
0.20〜0.40％、Al：0.01％以下、Cu：1.0 〜4.0 ％、S
i：(0.3−40Ｓ) 〜0.50％を含有し、残部がFeおよび不
可避的不純物からなり、不純物としてのＰは0.01％以
下、Ｓは 0.005％以下であり、かつAl＋Ｏが0.02％以下
であることを特徴とする高Cr高Nオーステナイト鋼用Ｂ
含有ＴＩＧ溶接用溶接材料。3. C .: 0.03-0.10%, Mn: 1.20-% by weight
8.00%, B: 0.01% or less, Nb: 0.01-0.70%, Cr: 23.0
28.0%, Ni: 18.0-30.0%, Mo: 0.50-1.50%, N:
0.20 to 0.40%, Al: 0.01% or less, Cu: 1.0 to 4.0%, S
i: contains (0.3-40S) to 0.50%, the balance being Fe and unavoidable impurities, P as impurities is 0.01% or less, S is 0.005% or less, and Al + O is 0.02% or less. B for high Cr high N austenitic steel, characterized by
Containing welding material for TIG welding .
8.00％、Ｂ：0.01％以下、Nb：0.01〜0.70％、Cr：23.0
〜28.0％、Ni：18.0〜30.0％、Mo：0.50〜1.50％、Ｎ：
0.20〜0.40％、Al：0.01％以下、Cu：1.0 〜4.0 ％、S
i：(0.3−40Ｓ) 〜0.50％およびMg：0.02％以下、Ca：
0.02％以下の１種または２種を含有し、残部がFeおよび
不可避的不純物からなり、不純物としてのＰは0.01％以
下、Ｓは 0.005％以下であり、かつAl＋Ｏが0.02％以下
であることを特徴とする高Cr高Nオーステナイト鋼用Ｂ
含有ＴＩＧ溶接用溶接材料。4. C .: 0.03-0.10%, Mn: 1.20-% by weight
8.00%, B: 0.01% or less, Nb: 0.01-0.70%, Cr: 23.0
28.0%, Ni: 18.0-30.0%, Mo: 0.50-1.50%, N:
0.20 to 0.40%, Al: 0.01% or less, Cu: 1.0 to 4.0%, S
i: (0.3-40S) -0.50% and Mg: 0.02% or less, Ca:
It contains one or two kinds of not more than 0.02%, the balance being Fe and unavoidable impurities, P as impurities is not more than 0.01%, S is not more than 0.005%, and Al + O is not more than 0.02%. Characteristic B for high Cr high N austenitic steel
Containing welding material for TIG welding .
で、Mn：8.00％以下、Ｂ：0.01％以下、Nb：0.01〜0.70
％、Cr：23.0〜28.0％、Ni：18.0〜30.0％、Mo：0.50〜
1.50％、Ｎ：0.15〜0.35％、Al：0.01％以下、Si：(0.3
−40Ｓ) 〜0.50％を含有し、残部がFeおよび不可避的不
純物からなり、不純物としてのＰは0.01％以下、Ｓは
0.005％以下であり、かつAl＋Ｏが0.02％以下であるこ
とを特徴とする高Cr高Nオーステナイト鋼用Ｂ含有ＴＩ
Ｇ溶接用溶接材料。5. In weight%, C: more than 0.10% to 0.24%, Mn: 8.00% or less, B: 0.01% or less, Nb: 0.01 to 0.70%.
%, Cr: 23.0-28.0%, Ni: 18.0-30.0%, Mo: 0.50 ~
1.50%, N: 0.15 to 0.35%, Al: 0.01% or less, Si: (0.3
-40S) to 0.50%, the balance being Fe and unavoidable impurities, P as an impurity is 0.01% or less, and S is
B-containing TI for high Cr high N austenitic steel characterized by being not more than 0.005% and Al + O being not more than 0.02%
G welding material.
で、Mn：8.00％以下、Ｂ：0.01％以下、Nb：0.01〜0.70
％、Cr：23.0〜28.0％、Ni：18.0〜30.0％、Mo：0.50〜
1.50％、Ｎ：0.15〜0.35％、Al：0.01％以下、Si：(0.3
−40Ｓ) 〜0.50％およびMg：0.02％以下、Ca：0.02％以
下の１種または２種を含有し、残部がFeおよび不可避的
不純物からなり、不純物としてのＰは0.01％以下、Ｓは
0.005％以下であり、かつAl＋Ｏが0.02％以下であるこ
とを特徴とする高Cr高Nオーステナイト鋼用Ｂ含有ＴＩ
Ｇ溶接用溶接材料。6. In% by weight, C: more than 0.10% to 0.24%, Mn: 8.00% or less, B: 0.01% or less, Nb: 0.01 to 0.70%.
%, Cr: 23.0-28.0%, Ni: 18.0-30.0%, Mo: 0.50 ~
1.50%, N: 0.15 to 0.35%, Al: 0.01% or less, Si: (0.3
-40S) 0.50.50%, Mg: 0.02% or less, Ca: 0.02% or less, the balance consists of Fe and unavoidable impurities, P as impurities is 0.01% or less, and S is
B-containing TI for high Cr high N austenitic steel characterized by being not more than 0.005% and Al + O being not more than 0.02%
G welding material.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5286390A JP2800661B2 (en) | 1993-11-16 | 1993-11-16 | Welding material for high Cr high N austenitic steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5286390A JP2800661B2 (en) | 1993-11-16 | 1993-11-16 | Welding material for high Cr high N austenitic steel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH07136793A JPH07136793A (en) | 1995-05-30 |
| JP2800661B2 true JP2800661B2 (en) | 1998-09-21 |
Family
ID=17703783
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP5286390A Expired - Lifetime JP2800661B2 (en) | 1993-11-16 | 1993-11-16 | Welding material for high Cr high N austenitic steel |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2800661B2 (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP5326862B2 (en) * | 2008-09-08 | 2013-10-30 | 日産自動車株式会社 | Dissimilar metal joining method of magnesium alloy and steel |
| JP6241234B2 (en) * | 2013-12-04 | 2017-12-06 | 新日鐵住金株式会社 | Welding material for austenitic heat resistant steel, weld metal and welded joint using the same |
| JP6638002B2 (en) * | 2015-08-12 | 2020-01-29 | レール・リキード−ソシエテ・アノニム・プール・レテュード・エ・レクスプロワタシオン・デ・プロセデ・ジョルジュ・クロード | Manufacturing method of welding joint and welding method |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0724948B2 (en) * | 1986-02-10 | 1995-03-22 | 新日本製鐵株式会社 | Stainless steel TIG welding wire |
| JP2583238B2 (en) * | 1987-06-11 | 1997-02-19 | 新日本製鐵株式会社 | Filler metal for TIG welding for heat-resistant austenitic stainless steel alloys |
| JP2660708B2 (en) * | 1988-02-04 | 1997-10-08 | 新日本製鐵株式会社 | Stainless steel gas shielded arc welding wire |
| JP2533968B2 (en) * | 1990-10-05 | 1996-09-11 | 新日本製鐵株式会社 | Austenitic stainless wire with excellent MIG welding workability |
| JP2722893B2 (en) * | 1991-09-12 | 1998-03-09 | 住友金属工業株式会社 | Welding material for high Cr high N austenitic steel |
-
1993
- 1993-11-16 JP JP5286390A patent/JP2800661B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH07136793A (en) | 1995-05-30 |
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