JP2000343274A - Coated electrode for high chromium steel and welding method of high chromium steel - Google Patents
Coated electrode for high chromium steel and welding method of high chromium steelInfo
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- JP2000343274A JP2000343274A JP11158290A JP15829099A JP2000343274A JP 2000343274 A JP2000343274 A JP 2000343274A JP 11158290 A JP11158290 A JP 11158290A JP 15829099 A JP15829099 A JP 15829099A JP 2000343274 A JP2000343274 A JP 2000343274A
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- welding rod
- welding
- steel
- high chromium
- chromium steel
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、石油・天然ガスの
輸送に使用されるラインパイプ、貯蔵に使用される容器
等に使用される高Ｃｒ鋼、さらに詳しくは７．５〜１
２．０％のＣｒを含有し、ミクロ組織がマルテンサイト
単相またはマルテンサイト５０％以上および残部フェラ
イトからなる高Ｃｒ鋼を溶接するにあたり、予・後熱処
理が不要で良好な強度、衝撃靱性、耐食性、耐低高温割
れ性の得られる溶接金属を得ることができる高Ｃｒ鋼用
被覆アーク溶接棒に関する。[0001] The present invention relates to a high Cr steel used for line pipes used for transportation of oil and natural gas, containers used for storage, etc., and more specifically, 7.5 to 1%.
When welding a high Cr steel containing 2.0% Cr and having a microstructure of 50% or more of martensite single phase or martensite and the balance of ferrite, pre- and post-heat treatment is not required, and good strength, impact toughness, The present invention relates to a coated arc welding rod for high Cr steel capable of obtaining a weld metal having corrosion resistance and low high temperature crack resistance.
【０００２】[0002]
【従来の技術】近年生産される石油・天然ガスでは、湿
潤な炭酸ガスや硫化水素を含有するものが増加してい
る。この様な環境下では、炭素鋼や低合金鋼は著しく腐
食してしまうことは周知の事実である。従って、その様
な環境下で使用される鋼種は優れた耐食性を有し、溶接
性にも優れた鋼が多く提案されている。これらの鋼種の
中に、炭酸ガス含有環境での耐食性を得るために１１〜
１５％のＣｒを含有し、溶接性を改善する目的でＣを低
減し、強度と靱性を確保するために焼入れ−焼鈍熱処理
を施して組織を焼戻マルテンサイトとしたものである。
この様な鋼板または鋼管を溶接する場合、溶接材料には
共金系の溶材が考えられるが、溶接金属の低温割れ感受
性が高いため、予熱および後熱処理が必須条件となり施
工上困難な状況となる。また、強度の高いＣｒ系溶材が
用いられる場合が多いがＣｒ系溶材では溶接金属の強度
が母材よりも低いため、外部応力が負荷された場合に溶
接金属が変形し破壊に至るおそれが考えられる。そこ
で、高Ｃｒ鋼を溶接するに際して予熱、後熱を必要とせ
ず耐低・高温割れ性に優れ、高強度、高衝撃靱性が得ら
れ、炭酸ガス含有環境下でも良好な耐食性を有する溶接
金属が得られる溶接棒が強く望まれていた。2. Description of the Related Art In recent years, an increasing number of petroleum and natural gas containing moist carbon dioxide and hydrogen sulfide have been increasing. It is a well-known fact that carbon steel and low alloy steel are significantly corroded in such an environment. Therefore, steels used in such an environment have excellent corrosion resistance and many steels excellent in weldability have been proposed. Among these steel grades, in order to obtain corrosion resistance in an environment containing carbon dioxide, 11-
It contains 15% Cr, reduces C for the purpose of improving weldability, and is subjected to quenching-annealing heat treatment to secure strength and toughness, whereby the structure becomes tempered martensite.
When welding such a steel plate or steel pipe, a common metal-based welding material can be used as the welding material, but since the low-temperature cracking susceptibility of the weld metal is high, preheating and post-heat treatment are indispensable conditions, and it is difficult to construct. . In addition, a high-strength Cr-based material is often used, but since the strength of the weld metal is lower than that of the base material in the case of the Cr-based material, there is a possibility that the weld metal is deformed and breaks when an external stress is applied. Can be Therefore, when welding high Cr steels, welding metal that does not require preheating and postheating, has excellent low / high temperature crack resistance, high strength and high impact toughness, and has good corrosion resistance even in an environment containing carbon dioxide gas. The resulting welding rod was strongly desired.
【０００３】[0003]
【発明が解決しようとする課題】本発明は、７．５〜１
２％のＣｒを含有し、ミクロ組織がマルテンサイト単相
またはマルテンサイト５０％以上および残部フェライト
からなる高Ｃｒ鋼の溶接において、予熱、後熱を必要と
せず耐低高温割れ性に優れ、高強度、高衝撃靱性が得ら
れ、炭酸ガス含有環境下でも良好な耐食性を有する溶接
金属が得られる溶接棒を提供することを目的とする。DISCLOSURE OF THE INVENTION The present invention relates to a method for controlling a temperature of 7.5 to 1
In welding high Cr steels containing 2% Cr and having a microstructure of 50% or more of martensite single phase or martensite and the balance of ferrite, it does not require preheating and post-heating and has excellent low-temperature cracking resistance. An object of the present invention is to provide a welding rod capable of obtaining strength and high impact toughness and obtaining a weld metal having good corrosion resistance even in an environment containing carbon dioxide gas.
【０００４】[0004]
【課題を解決するための手段】本発明は、前記課題を解
決するためになされたものであり、その要旨とするとこ
ろは以下の通りである。 （１）溶接棒心線および被覆剤からなる溶接棒におい
て、溶接棒全体に対する重量％で、 Ｃ ：０．００５〜０．１％、 Ｓｉ：０．３〜１％、 Ｍｎ：０．２５〜３．５％、 Ｃｒ：１０〜１９％、 Ｎｉ：３．５〜８％、 Ｍｏ：１〜２．５％、 Ｎ ：０．００１〜０．２％ 含有することを特徴とする高Ｃｒ鋼用被覆アーク溶接
棒。SUMMARY OF THE INVENTION The present invention has been made to solve the above-mentioned problems, and the gist thereof is as follows. (1) In a welding rod composed of a welding rod core wire and a coating agent, C: 0.005 to 0.1%, Si: 0.3 to 1%, and Mn: 0.25 to 5% by weight based on the entire welding rod. High Cr steel characterized by containing 3.5%, Cr: 10 to 19%, Ni: 3.5 to 8%, Mo: 1 to 2.5%, N: 0.001 to 0.2%. For coated arc welding rod.
【０００５】（２）さらに、溶接棒中のＣ、Ｓｉ、Ｍ
ｎ、Ｃｒ、Ｎｉ、Ｍｏ、Ｎの含有量が溶接棒全体に対す
る重量％で、下記の（１）〜（３）式を満足することを
特徴とする上記（１）に記載の高Ｃｒ鋼用被覆アーク溶
接棒。 １４≦ Ｃｒ＋Ｍｏ＋１．５Ｓｉ ≦２２ （１） ４≦ Ｎｉ＋０．５Ｍｎ＋３０Ｃ＋３０Ｎ ≦１４ （２） ０．２５≦（Ｎｉ＋０．５Ｍｎ＋３０Ｃ＋３０Ｎ） ／（Ｃｒ＋Ｍｏ＋１．５Ｓｉ）≦０．８ （３）(2) Further, C, Si, M in the welding rod
The content for n, Cr, Ni, Mo, and N is expressed in terms of% by weight based on the entire welding rod and satisfies the following formulas (1) to (3). Covered arc welding rod. 14 ≦ Cr + Mo + 1.5Si ≦ 22 (1) 4 ≦ Ni + 0.5Mn + 30C + 30N ≦ 14 (2) 0.25 ≦ (Ni + 0.5Mn + 30C + 30N) / (Cr + Mo + 1.5Si) ≦ 0.8 (3)
【０００６】（３）（１）または（２）に記載の被覆ア
ーク溶接棒を使用して、７．５〜１２．０％Ｃｒを含有
する鋼を溶接するさい、予熱処理、後熱処理のいずれも
行なわないことを特徴とする高Ｃｒ鋼の溶接方法。(3) When welding steel containing 7.5 to 12.0% Cr using the coated arc welding rod according to (1) or (2), any of pre-heat treatment and post-heat treatment A method for welding high Cr steels, characterized in that no welding is performed.
【０００７】[0007]
【発明の実施の形態】以下に、本発明の高Ｃｒ鋼用被覆
アーク溶接棒における成分の限定理由を述べる。なお、
以下において、％は溶接棒全体に対する重量％を示す。DESCRIPTION OF THE PREFERRED EMBODIMENTS The reasons for limiting the components in the coated arc welding rod for high Cr steel of the present invention will be described below. In addition,
In the following,% indicates the weight% with respect to the entire welding rod.
【０００８】Ｃ：Ｃは溶接金属の強度を向上させると共
に、オーステナイト生成元素として添加する必要がある
が、０．００５％未満ではその効果は顕著に現れないた
め０．０３％以上添加する必要がある。ＣはＣｒ炭化物
を生成して耐食性を劣化させる元素であるが、０．１％
以下であれば耐食性の低下は顕著に現れないため０．１
％以下とした。C: C is required to improve the strength of the weld metal and to be added as an austenite-forming element, but if it is less than 0.005%, the effect is not remarkable, so it is necessary to add 0.03% or more. is there. C is an element that generates Cr carbide and deteriorates corrosion resistance, but 0.1%
If it is less than 0.1, the decrease in corrosion resistance does not appear remarkably, so 0.1
% Or less.
【０００９】Ｓｉ：Ｓｉは溶接金属の脱酸および強化元
素として添加する必要があるが、０．３％未満ではその
効果が十分ではないため０．３％以上添加する必要があ
る。また、１％を超えて添加してもその効果は飽和され
るので１％以下とした。Si: Si must be added as a deoxidizing and strengthening element of the weld metal, but if it is less than 0.3%, its effect is not sufficient, so it is necessary to add 0.3% or more. The effect is saturated even if it is added in excess of 1%.
【００１０】Ｍｎ：Ｍｎは溶接金属の脱酸およびオース
テナイト生成元素として添加する必要があるが、０．２
５％未満ではその効果が顕著に現れないなめ０．２５％
以上添加する必要がある。また、３．５％を超えて添加
してもその効果は飽和するため３．５％以下とした。Mn: Mn needs to be added as an element for deoxidizing the weld metal and forming austenite.
If it is less than 5%, the effect does not appear remarkably 0.25%
It is necessary to add above. The effect is saturated even if it is added in excess of 3.5%, so that the content is set to 3.5% or less.
【００１１】Ｃｒ：Ｃｒは耐食性と強度を向上させるに
必要な元素であるが、１０％未満ではその効果が顕著に
現れないため１０％以上とした。また、１９％を超えて
添加するとマルテンサイト組織の生成が困難となるため
１９％以下とした。Cr: Cr is an element necessary for improving corrosion resistance and strength, but if its content is less than 10%, its effect is not remarkably exhibited, so Cr is set to 10% or more. Further, if it is added in excess of 19%, it becomes difficult to form a martensite structure.
【００１２】Ｎｉ：Ｎｉはオーステナイト組織を安定さ
せ、衝撃靱性と耐食性を得るのに必要な元素であるが。
３．５％未満では衝撃靱性が十分に得られない。また、
８％を超えて添加しても靱性を向上させる効果は飽和状
態となるため８％以下とした。Ni: Ni is an element necessary for stabilizing the austenite structure and obtaining impact toughness and corrosion resistance.
If it is less than 3.5%, sufficient impact toughness cannot be obtained. Also,
Even if it is added in excess of 8%, the effect of improving toughness is saturated, so that it is set to 8% or less.
【００１３】Ｍｏ：Ｍｏは耐食性と強度を向上させるに
必要な元素であるが、１％未満ではその効果は顕著に現
れない。また、２．５％を超えて添加しても金属間化合
物が生成し易くなり衝撃靱性が低下するため２．５％以
下とした。Mo: Mo is an element necessary for improving corrosion resistance and strength, but if less than 1%, its effect is not remarkably exhibited. Further, even if it is added in excess of 2.5%, an intermetallic compound is likely to be formed, and the impact toughness is reduced.
【００１４】Ｎ：Ｎは耐食性と強度を向上させ、またオ
ーステナイトを生成させるに必要な元素であるが、０．
００１％未満ではその効果は顕著に現れない。また、
０．２％を超えて添加すると、強度が過剰となるばかり
か、溶接金属内にブローホールが残り易くなるので０．
２％以下とした。N: N is an element necessary for improving corrosion resistance and strength and for forming austenite.
If it is less than 001%, the effect is not remarkably exhibited. Also,
If added in excess of 0.2%, not only will the strength become excessive, but blowholes will easily remain in the weld metal.
2% or less.
【００１５】なお、本発明の溶接棒の被覆剤中には上記
合金成分の他に溶接作業性を確保するためのＴｉＯ2 、
ＳｉＯ2 、ＺｒＯ2 、ＭｇＯ、ＣａＣＯ3 、Ｋ2 Ｏ、Ｃ
ａＯ、Ｌｉ2 ＣＯ3 、Ｎａ2 Ｏ等の酸化物や、Ｃａ
Ｆ2 、ＮａＦ等のフッ化物を添加することができる。In addition, in addition to the above alloy components, TiO 2 for securing welding workability is contained in the coating material for the welding rod of the present invention. ,
SiO 2 , ZrO 2 , MgO, CaCO 3 , K 2 O, C
aO, Li 2 CO 3 , Na 2 Oxides such as O,
F 2 , NaF or the like can be added.
【００１６】次に、本発明の溶接棒中のＣ、Ｓｉ、Ｍ
ｎ、Ｃｒ、Ｎｉ、Ｍｏ、Ｎの含有量を下記の（１）〜
（３）式で規定する理由について述べる。 １４≦ Ｃｒ当量 ≦２２ （１） ４≦ Ｎｉ当量 ≦１４ （２） ０．２５≦ Ｎｉ当量 ／ Ｃｒ当量 ≦０．８ （３） ここで、Ｃｒ当量＝ Ｃｒ＋Ｍｏ＋１．５Ｓｉ、 Ｎｉ当
量＝Ｎｉ＋０．５Ｍｎ＋３０Ｃ＋３０Ｎ。Next, C, Si, M in the welding rod of the present invention are described.
The contents of n, Cr, Ni, Mo, and N are set in the following (1) to
The reason specified by the expression (3) will be described. 14 ≦ Cr equivalent ≦ 22 (1) 4 ≦ Ni equivalent ≦ 14 (2) 0.25 ≦ Ni equivalent / Cr equivalent ≦ 0.8 (3) Here, Cr equivalent = Cr + Mo + 1.5Si, Ni equivalent = Ni + 0.5Mn + 30C + 30N .
【００１７】本発明では、溶接金属の耐低高温割れ性、
強度、衝撃靱性、耐食性をそれぞれ同時に満足するため
に、溶接金属組織をオーステナイト相＋フェライト相＋
マルテンサイト相の３相組織にする必要がある。オース
テナイト単相では、強度が不足し高温割れの虞れがあ
り、フェライト単相では、衝撃靱性が悪く、マルテンサ
イト単相では、衝撃靱性が悪く低温割れの虞れがある。
また、オーステナイト相＋フェライト相の２相組織で
は、衝撃靱性は良好なものの、強度が不足し、フェライ
ト相＋マルテンサイト相の２相組織では、低温割れの危
険があり、また衝撃靱性が乏しく、オーステナイト相＋
マルテンサイト相の２相組織では、高温割れの危険があ
る。In the present invention, the low-temperature cracking resistance of the weld metal
In order to simultaneously satisfy strength, impact toughness and corrosion resistance, the weld metal structure must be austenitic + ferrite +
It is necessary to have a three-phase structure of a martensite phase. The austenitic single phase has insufficient strength and may cause high-temperature cracking, the ferrite single phase has poor impact toughness, and the martensite single phase has poor impact toughness and may cause low-temperature cracking.
In the two-phase structure of austenite phase + ferrite phase, although the impact toughness is good, the strength is insufficient, and in the two-phase structure of ferrite phase + martensite phase, there is a risk of low-temperature cracking, and the impact toughness is poor. Austenitic phase +
In the two-phase structure of the martensite phase, there is a risk of hot cracking.
【００１８】以上の理由から本発明では、溶接金属組織
がオーステナイト相＋フェライト相＋マルテンサイト相
の３相組織になる様にＣｒ当量：１４〜２２、Ｎｉ当
量：４〜１４と規定した。また、さらに、本発明では、
Ｎｉ当量／Ｃｒ当量を０．２５〜０．８に規定するが、
この理由は、０．２５未満では、フェライト相、マルテ
ンサイト相が増加し衝撃靱性が劣化し、また、０．８を
越えるとオーステナイト相、マルテンサイト相が増加し
高温割れの危険性が高まるためである。For the above reasons, in the present invention, the Cr equivalent: 14 to 22 and the Ni equivalent: 4 to 14 are specified so that the weld metal structure has a three-phase structure of austenite phase + ferrite phase + martensite phase. Further, in the present invention,
Ni equivalent / Cr equivalent is defined as 0.25 to 0.8,
The reason is that if it is less than 0.25, the ferrite phase and martensite phase increase and the impact toughness deteriorates, and if it exceeds 0.8, the austenite phase and martensite phase increase and the risk of hot cracking increases. It is.
【００１９】上記した成分、成分範囲は、個々に使用し
てもその効果を得るのは困難であり、併用して使用する
ことにより、その効果を得るものである。また、本発明
の溶接棒とは、配合・混合した被覆剤と固着剤（珪酸カ
リウムおよび珪酸ナトリウムからなる水溶液）とを湿式
混合し、溶接棒心線の周囲にその被覆剤を塗布し、その
後１００〜４００℃で乾燥・焼成を行う方法で製造した
ものである。It is difficult to obtain the effects of the above-mentioned components and component ranges even when used individually, and the effects can be obtained by using them in combination. Further, the welding rod of the present invention is obtained by wet-mixing the blended and mixed coating agent and a fixing agent (aqueous solution composed of potassium silicate and sodium silicate), applying the coating agent around the welding rod core, and thereafter applying It is manufactured by a method of drying and firing at 100 to 400 ° C.
【００２０】[0020]
【実施例】以下に実施例により本発明の効果を具体的に
説明する。表１に示す高Ｃｒ鋼（焼入れ−焼鈍熱処理を
施したもの、７１０Ｎ／ｍｍ2 の降伏強度を有する）を
図１に示す開先形状（板厚１４．５ｍｍ、開先角度６０
°、ルートギャップ５ｍｍ、裏当て金の板厚６ｍｍ）の
試験板に作製し、表２に示す成分の溶接棒により下向溶
接を行った。溶接条件は溶接電流１２０〜１５０Ａ、溶
接電圧２２〜２６Ｖ、溶接速度１００〜２００ｍｍ／ｍ
ｉｎである。EXAMPLES The effects of the present invention will be specifically described below with reference to examples. The high Cr steel shown in Table 1 (hardened and subjected to annealing heat treatment and having a yield strength of 710 N / mm 2 ) was prepared with the groove shape (plate thickness 14.5 mm, groove angle 60) shown in FIG.
°, a root gap of 5 mm, and a backing metal plate thickness of 6 mm), and were subjected to downward welding with a welding rod having the components shown in Table 2. The welding conditions are welding current 120-150A, welding voltage 22-26V, welding speed 100-200mm / m.
in.
【００２１】[0021]
【表１】 [Table 1]
【００２２】[0022]
【表２】 [Table 2]
【００２３】溶接終了後、図２に示すような位置（方向
は接合ビードに直角）から、ＪＩＳＡ５号引張試験片、
ＪＩＳＡ４号衝撃試験片、腐食試験片（３ｍｍｔ×３０
ｍｍｌ×３０ｍｍｗ）を採取しそれぞれ試験を行った。
なお、腐食試験は１２０℃のオートクレーブ中で、炭酸
ガス４０気圧の条件で５％ＮａＣｌ水溶液中に３０日間
浸漬して、試験前後の重量変化から腐食速度を算出しし
評価した。また、高温割れ試験にはＪＩＳ Ｚ３１５５
に記載のＦＩＳＣＯ割れ試験を、低温割れ試験にはＪＩ
Ｓ Ｚ３１５７に記載のＵ型溶接割れ試験を採用した。After the welding is completed, a JIS No. 5 tensile test piece is taken from a position as shown in FIG. 2 (direction is perpendicular to the joining bead).
JISA No.4 impact test specimen, corrosion test specimen (3mmt × 30
(mm × 30 mmw) were collected and tested.
The corrosion test was performed by immersing in a 5% NaCl aqueous solution for 30 days in an autoclave at 120 ° C. and 40 atm of carbon dioxide gas, and calculating and evaluating the corrosion rate from the weight change before and after the test. In addition, JIS Z3155 is used for the hot crack test.
The FISCO cracking test described in
The U-shaped weld crack test described in SZ3157 was adopted.
【００２４】試験結果を表３に示す。表３中の○は良好
で、×は不可である。評価基準はそれぞれ、引張試験は
母材破断で○、溶接金属部破断で×、衝撃試験は破面遷
移温度が−３０℃以下で○、破面遷移温度が−３０℃を
超えているものは×で示した。腐食試験は、一般にある
環境におけるある材料の腐食速度が０．１ｍｍ／ｙ未満
の場合、材料は十分に耐食的であり使用可能であると考
えられていることから、０．１ｍｍ／ｙ未満で○、０．
１ｍｍ／ｙ以上で×と示した。高温割れ、低温割れ試験
においては、割れのないものは○、割れのあるものは×
で示した。Table 3 shows the test results. In Table 3, ○ indicates good and × indicates unacceptable. The evaluation criteria are as follows. Tensile test is ○ for base material fracture, × for weld metal fracture, and impact test is ○ for fracture surface transition temperature of -30 ° C or lower, and those for which fracture surface transition temperature exceeds -30 ° C. Indicated by x. Corrosion tests generally indicate that if the corrosion rate of a material in an environment is less than 0.1 mm / y, then the material is considered to be sufficiently corrosion resistant and usable, and therefore, less than 0.1 mm / y. ○, 0.
At 1 mm / y or more, it was indicated as x. In the high-temperature cracking and low-temperature cracking tests, those with no cracks were marked with "O" and those with cracks were marked with "x".
Indicated by
【００２５】[0025]
【表３】 [Table 3]
【００２６】表２、表３において、記号１〜７は本発明
例であり、いずれも良好な結果を示した。それに対し、
記号８〜１５は本発明の要件を外れた比較例であり、記
号８はＣ量が過剰なため強度が出過ぎて破面遷移温度が
−３０℃を超えた。また、Ｃｒ炭化物を生成して耐食性
が劣化した。記号９はＳｉ量が少ないため脱酸できず破
面遷移温度が−３０℃を超えた。記号１０はＭｎ量が過
剰なため溶接金属中のオーステナイト相が増加し強度不
足となり溶接金属部で破断した。記号１１はＣｒ量が過
剰なためフェライト相が増加し破面遷移温度が−３０℃
を超えた。記号１２はＮｉ量が過剰なためオーステナイ
ト相が増加し強度不足となり溶接金属部で破断した。ま
た、高温割れを起こした。記号１３はＭｏ量が少ないた
め耐食性が悪い。記号１４はＮ量が過剰なためオーステ
ナイト相が増加し高温割れを起こした。記号１５はＮｉ
当量／Ｃｒ当量が高いためオーステナイト相が増加し高
温割れを起こした。In Tables 2 and 3, symbols 1 to 7 are examples of the present invention, and all showed good results. For it,
Symbols 8 to 15 are comparative examples that do not satisfy the requirements of the present invention, and symbol 8 has an excessive amount of C, resulting in excessive strength and a fracture surface transition temperature exceeding −30 ° C. In addition, Cr carbide was generated and the corrosion resistance was deteriorated. Symbol 9 could not be deoxidized because the amount of Si was small, and the fracture surface transition temperature exceeded -30 ° C. In the symbol 10, since the amount of Mn was excessive, the austenite phase in the weld metal increased and the strength became insufficient, and the weld fractured at the weld metal. Symbol 11 shows that the ferrite phase increased due to the excessive amount of Cr and the fracture surface transition temperature was -30 ° C.
Exceeded. In the case of symbol 12, the austenite phase increased due to the excessive amount of Ni, resulting in insufficient strength, and fractured at the weld metal. In addition, hot cracking occurred. Symbol 13 has low corrosion resistance due to a small amount of Mo. In the case of symbol 14, the austenite phase increased due to an excessive amount of N, causing hot cracking. Symbol 15 is Ni
Since the equivalent weight / Cr equivalent weight was high, the austenite phase increased and hot cracking occurred.
【００２７】[0027]
【発明の効果】以上のように、本発明の高Ｃｒ溶接棒
は、高Ｃｒ鋼の溶接において予後熱処理を必要とせず耐
低高温割れ性に優れ、高強度、高衝撃靱性が得られ、炭
酸ガス含有環境下でも良好な耐食性を有する溶接金属が
得られるものであり、高Ｃｒ鋼の構造物の健全性に大き
く貢献できるものである。As described above, the high Cr welding rod of the present invention does not require prognostic heat treatment in welding of high Cr steel, has excellent low-temperature cracking resistance, high strength, high impact toughness, A weld metal having good corrosion resistance can be obtained even in a gas-containing environment, and can greatly contribute to the soundness of a high Cr steel structure.
【図１】試験板の開先形状を示す図FIG. 1 shows a groove shape of a test plate.
【図２】試験片の採取位置を示す図FIG. 2 is a diagram showing a sampling position of a test piece.
Ｔ 板厚 θ 開先角度 ｔ 裏当て金の板厚 ｗ ルートギャップ Ｓ 試験片 T Plate thickness θ Groove angle t Plate thickness of backing metal w Root gap S Test piece
フロントページの続き (72)発明者 長崎 肇 千葉県富津市新富20−１ 新日本製鐵株式 会社技術開発本部内 (72)発明者 渡邊 大祐 千葉県富津市新富20−１ 新日本製鐵株式 会社技術開発本部内 Ｆターム(参考） 4E001 AA03 BB01 CA07 DC01 EA05Continued on the front page (72) Inventor Hajime Nagasaki 20-1 Shintomi, Futtsu-shi, Chiba Nippon Steel Corporation Technology Development Division (72) Inventor Daisuke Watanabe 20-1 Shintomi, Futtsu-shi, Chiba Nippon Steel Corporation F-term in the Technology Development Division (reference) 4E001 AA03 BB01 CA07 DC01 EA05
Claims (3)
において、溶接棒全体に対する重量％で、 Ｃ ：０．００５〜０．１％、 Ｓｉ：０．３〜１％、 Ｍｎ：０．２５〜３．５％、 Ｃｒ：１０〜１９％、 Ｎｉ：３．５〜８％、 Ｍｏ：１〜２．５％、 Ｎ ：０．００１〜０．２％ 含有することを特徴とする高Ｃｒ鋼用被覆アーク溶接
棒。1. A welding rod comprising a welding rod core wire and a coating agent, wherein: C: 0.005 to 0.1%, Si: 0.3 to 1%, Mn: 0. 25 to 3.5%, Cr: 10 to 19%, Ni: 3.5 to 8%, Mo: 1 to 2.5%, N: 0.001 to 0.2% Covered arc welding rod for Cr steel.
ｒ、Ｎｉ、Ｍｏ、Ｎの含有量が溶接棒全体に対する重量
％で、下記の（１）〜（３）式を満足することを特徴と
する請求項１に記載の高Ｃｒ鋼用被覆アーク溶接棒。 １４≦ Ｃｒ＋Ｍｏ＋１．５Ｓｉ ≦２２ （１） ４≦ Ｎｉ＋０．５Ｍｎ＋３０Ｃ＋３０Ｎ ≦１４ （２） ０．２５≦（Ｎｉ＋０．５Ｍｎ＋３０Ｃ＋３０Ｎ） ／（Ｃｒ＋Ｍｏ＋１．５Ｓｉ）≦０．８ （３）2. C, Si, Mn, C in the welding rod.
2. The coated arc welding for high Cr steel according to claim 1, wherein the content of r, Ni, Mo, and N satisfies the following equations (1) to (3) in weight% based on the entire welding rod. rod. 14 ≦ Cr + Mo + 1.5Si ≦ 22 (1) 4 ≦ Ni + 0.5Mn + 30C + 30N ≦ 14 (2) 0.25 ≦ (Ni + 0.5Mn + 30C + 30N) / (Cr + Mo + 1.5Si) ≦ 0.8 (3)
接棒を使用して、７．５〜１２．０％Ｃｒを含有する鋼
を溶接するさい、予熱処理、後熱処理のいずれも行なわ
ないことを特徴とする高Ｃｒ鋼の溶接方法。3. When the steel containing 7.5 to 12.0% Cr is welded using the coated arc welding rod according to claim 1 or 2, neither pre-heat treatment nor post-heat treatment is performed. A method for welding high Cr steel, characterized in that:
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11158290A JP2000343274A (en) | 1999-06-04 | 1999-06-04 | Coated electrode for high chromium steel and welding method of high chromium steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11158290A JP2000343274A (en) | 1999-06-04 | 1999-06-04 | Coated electrode for high chromium steel and welding method of high chromium steel |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JP2000343274A true JP2000343274A (en) | 2000-12-12 |
Family
ID=15668381
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP11158290A Withdrawn JP2000343274A (en) | 1999-06-04 | 1999-06-04 | Coated electrode for high chromium steel and welding method of high chromium steel |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2000343274A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108274149A (en) * | 2017-12-15 | 2018-07-13 | 武汉铁锚焊接材料股份有限公司 | A kind of 20 control chromium steel welding rods of nuclear power |
| KR102197132B1 (en) * | 2019-11-26 | 2020-12-31 | 주식회사 세아에삽 | Stainless steel flux cored wire for welding LNG tank |
| WO2021107581A1 (en) * | 2019-11-26 | 2021-06-03 | 주식회사 세아에삽 | Stainless steel welding wire for use in lng tank manufacturing |
-
1999
- 1999-06-04 JP JP11158290A patent/JP2000343274A/en not_active Withdrawn
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108274149A (en) * | 2017-12-15 | 2018-07-13 | 武汉铁锚焊接材料股份有限公司 | A kind of 20 control chromium steel welding rods of nuclear power |
| KR102197132B1 (en) * | 2019-11-26 | 2020-12-31 | 주식회사 세아에삽 | Stainless steel flux cored wire for welding LNG tank |
| WO2021107581A1 (en) * | 2019-11-26 | 2021-06-03 | 주식회사 세아에삽 | Stainless steel welding wire for use in lng tank manufacturing |
| WO2021107579A1 (en) * | 2019-11-26 | 2021-06-03 | 주식회사 세아에삽 | Stainless steel flux cored wire for manufacturing lng tank |
| US20220281038A1 (en) * | 2019-11-26 | 2022-09-08 | Esab Seah Corp. | Stainless steel welding wire for use in lng tank manufacturing |
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