JPH09122972A - Coated electrode for high-cr ferrite heat resisting steel - Google Patents
Coated electrode for high-cr ferrite heat resisting steelInfo
- Publication number
- JPH09122972A JPH09122972A JP7303361A JP30336195A JPH09122972A JP H09122972 A JPH09122972 A JP H09122972A JP 7303361 A JP7303361 A JP 7303361A JP 30336195 A JP30336195 A JP 30336195A JP H09122972 A JPH09122972 A JP H09122972A
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- Prior art keywords
- welding rod
- toughness
- strength
- steel
- arc welding
- 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.)
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Abstract
Description
【0001】[0001]
【発明の属する技術分野】本発明は高Crフェライト系
高強度耐熱鋼用の溶接材料に関するものであり、さらに
詳しくは高温におけるクリープ特性、靱性、耐割れ性に
優れた溶接金属を得る被覆アーク溶接棒に係わるもので
ある。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a welding material for high-Cr ferritic high-strength heat-resistant steel, and more specifically, coated arc welding for obtaining a weld metal having excellent creep characteristics, toughness, and crack resistance at high temperatures. It is related to a stick.
【0002】[0002]
【従来の技術】高温型のエネルギープラント用鋼材とし
て、クリープ強度が極めて優れ、かつオーステナイト系
ステンレス鋼に見られるような応力腐食割れの心配が少
ないフェライト系耐熱鋼が使用され始めており、この種
の耐熱鋼用の溶接材として、例えば特開昭55−303
54号公報に開示されているCr−Mo系鋼用被覆アー
ク溶接棒のごとく、NiやMn等の添加量を限定し、オ
ーステナイト相安定化元素を含有させ、溶接金属中の粗
大フェライト相を減少させる方法が提案されているが、
Niを多量に含有させた場合には長時間クリープ破断強
度が低下し、また必要以上のNiやMnは溶接金属の耐
割れ性を低下させるので、目標とする高性能の溶接継手
を得ることはできない。2. Description of the Related Art Ferritic heat-resisting steels, which have extremely high creep strength and have less fear of stress corrosion cracking as seen in austenitic stainless steels, have begun to be used as high-temperature type energy plant steel materials. As a welding material for heat-resistant steel, for example, JP-A-55-303
Like the coated arc welding rod for Cr-Mo steel disclosed in Japanese Patent Publication No. 54, the addition amount of Ni, Mn, etc. is limited, and the austenite phase stabilizing element is contained to reduce the coarse ferrite phase in the weld metal. Although a method to make it is proposed,
When a large amount of Ni is contained, the creep rupture strength decreases for a long time, and Ni and Mn more than necessary decrease the crack resistance of the weld metal. Therefore, it is difficult to obtain a target high performance welded joint. Can not.
【0003】また、特開昭62−220300号公報で
は、9%Cr系鋼の溶接において溶接棒中に適量のWを
添加するとともにWをMo量との関係で限定共存させる
ことにより、溶接金属に析出する炭化物の粗大化をV4
C3 、NbCの析出で長時間にわたり抑制するととも
に、さらにMo2 C、W2 Cの析出バランスを適正な範
囲に保つことによって高温長時間側のクリープ強度を向
上させている。さらに、特開平2−280993号公報
では9〜12%Cr系溶接材料のごとく、C、Si、M
n、Cr、Ni、Mo、W、V、Nb、Al、N添加量
を限定し、クロム当量Creq(Creq=%Cr+6%S
i+4%Mo+1.5%W+11%V+5%Nb+8%
Ti+12%Al−40%C−30%N−4%Ni−2
%Mn−%Cu−2%Co)を13%以下とする溶接材
料が提案されている。しかしながらこれらの技術は大幅
にクリープ強度を向上させるものではなく、一方、マル
テンサイト相中にδフェライトが存在するため靱性が著
しく低下するという欠点を有する。δフェライト相は基
地中マルテンサイトより著しく軟らかい相であり、この
ような軟らかい第二相が硬い基地中に分散する場合、全
体の衝撃特性は著しく低下する。In Japanese Patent Application Laid-Open No. 62-220300, in welding 9% Cr steel, an appropriate amount of W is added to a welding rod and W is limitedly coexisted in relation to the amount of Mo. V 4
Suppresses over time at C 3, NbC precipitation, thereby improving the creep strength of the high-temperature long-time side by keeping further Mo 2 C, the precipitation balance of W 2 C in a proper range. Further, in JP-A-2-280993, C, Si, M, such as 9 to 12% Cr-based welding material, is used.
n, Cr, Ni, Mo, W, V, Nb, Al, N addition amount is limited, chromium equivalent Cr eq (Cr eq =% Cr + 6% S
i + 4% Mo + 1.5% W + 11% V + 5% Nb + 8%
Ti + 12% Al-40% C-30% N-4% Ni-2
A welding material has been proposed in which (% Mn-% Cu-2% Co) is 13% or less. However, these techniques do not significantly improve the creep strength, but on the other hand, they have a drawback that the toughness is remarkably lowered due to the presence of δ ferrite in the martensite phase. The δ ferrite phase is a significantly softer phase than the martensite in the matrix, and if such a soft second phase is dispersed in the hard matrix, the overall impact properties are significantly reduced.
【0004】[0004]
【発明が解決しようとする課題】本発明は上記のような
事情に着目し、高温強度や高温クリープ破断強度さらに
は耐割れ性等を損なうことなく粗大フェライト相を減少
し、母材に匹敵する強度、靱性および耐割れ性を有する
溶接金属を確保できる高Crフェライト系耐熱鋼用被覆
アーク溶接棒を提供することにある。The present invention focuses on the above circumstances and reduces the coarse ferrite phase without impairing the high temperature strength, high temperature creep rupture strength, crack resistance, etc., and is comparable to the base metal. It is an object of the present invention to provide a coated arc welding rod for high Cr ferritic heat resistant steel capable of ensuring a weld metal having strength, toughness and crack resistance.
【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
するものであって、高Crフェライト系耐熱鋼用被覆ア
−ク溶接棒において、被覆アーク溶接棒全重量に対して
重量%で(以下すべて同様)、C:0.01〜0.12
%、Si:0.1〜2.4%、Mn:0.3〜1.9
%、Cr:5.8〜14%、Mo:0.1〜1.6%、
W:0.5〜3.5%、V:0.03〜0.40%、N
b:0.01〜0.15%、Ni:0.05〜1.2
%、Cu:0.5〜4.0%、N:0.01〜0.08
%、Ta:0.001〜3.0%を含有し、さらに必要
に応じてCo:0.5〜5.0%を含有し、残部はFe
および不可避的不純物からなる鋼心線に、金属炭酸塩、
金属弗化物、アーク安定剤、スラグ生成剤、脱酸剤、粘
結剤を含む被覆剤を含有せしめ、被覆率(溶接棒全重量
に対する被覆剤重量の割合)が25〜35重量%となる
ように被覆したことを特徴とする高Crフェライト系耐
熱鋼用被覆アーク溶接棒である。SUMMARY OF THE INVENTION The present invention is to solve the above-mentioned problems, and in a coated arc welding rod for high Cr ferritic heat-resistant steel, the weight percentage of the total weight of the coated arc welding rod is ( The same applies hereinafter), C: 0.01 to 0.12
%, Si: 0.1 to 2.4%, Mn: 0.3 to 1.9
%, Cr: 5.8-14%, Mo: 0.1-1.6%,
W: 0.5-3.5%, V: 0.03-0.40%, N
b: 0.01 to 0.15%, Ni: 0.05 to 1.2
%, Cu: 0.5 to 4.0%, N: 0.01 to 0.08
%, Ta: 0.001 to 3.0%, and optionally Co: 0.5 to 5.0%, and the balance Fe.
And steel core wire consisting of inevitable impurities, metal carbonate,
Contains a coating material containing a metal fluoride, an arc stabilizer, a slag generator, a deoxidizer, and a binder so that the coverage (the ratio of the coating material weight to the total weight of the welding rod) is 25 to 35% by weight. It is a coated arc welding rod for high Cr ferritic heat resistant steel, which is characterized by being coated on.
【0006】[0006]
【発明の実施の形態】本発明の最大の特徴は高Crフェ
ライト系耐熱鋼用被覆アーク溶接棒において、溶接して
得られる溶接金属のδフェライトの生成を抑制して靱性
低下を抑制し、クリープ破断強度を格段に高めたところ
にある。なお、本発明においては、前述のC、Si、M
n、V、Nb、N、Cr、Ni、Mo、W、Cu、T
a、Coは鋼心線中に含有させる場合が多いが、被覆剤
中に含有させても近似的な効果が得られる。鋼心線に
は、前述の成分の他には、P:0.02%以下、S:
0.02%以下、Ti:0.02%以下、O:0.05
%以下を含有することもあり、残部がFeおよび不可避
的不純物からなるものである。以下に本発明における成
分限定の理由を詳細に説明する。BEST MODE FOR CARRYING OUT THE INVENTION The greatest feature of the present invention is that in a coated arc welding rod for high Cr ferritic heat-resistant steel, the formation of δ ferrite in the weld metal obtained by welding is suppressed to suppress deterioration of toughness, and creep It is in the place where the breaking strength is remarkably increased. In the present invention, the above-mentioned C, Si, M
n, V, Nb, N, Cr, Ni, Mo, W, Cu, T
Although a and Co are often contained in the steel core wire, even if they are contained in the coating material, an approximate effect can be obtained. For the steel core wire, in addition to the above components, P: 0.02% or less, S:
0.02% or less, Ti: 0.02% or less, O: 0.05
% Or less, the balance consists of Fe and inevitable impurities. The reason for limiting the components in the present invention will be described in detail below.
【0007】C:0.01〜0.12% Cは焼入れ性と強度確保のため0.01%以上必要であ
るが、耐割れ性の観点から上限を0.12%とした。C: 0.01 to 0.12% C is required to be 0.01% or more in order to secure hardenability and strength, but the upper limit was made 0.12% from the viewpoint of crack resistance.
【0008】Si:0.1〜2.4% Siは脱酸剤として添加するものであるが、溶接作業性
確保の上からも必要である。0.1%未満では脱酸不足
によって溶接金属中に気孔が発生しやすく、一方2.4
%を超えると靱性の低下を招くので上限を2.4%と定
めた。Si: 0.1 to 2.4% Si is added as a deoxidizer, but it is also necessary from the viewpoint of ensuring welding workability. If it is less than 0.1%, porosity is likely to occur in the weld metal due to insufficient deoxidation, while 2.4
%, The toughness is deteriorated, so the upper limit was set to 2.4%.
【0009】Mn:0.3〜1.9重量% Mnは脱酸のためのみでなく、強度保持上も必要な成分
である。上限を1.9%としたのは、これを超すと靱性
の点から好ましくないからであり、下限は脱酸に必要な
量として 0.3%と定めた。Mn: 0.3 to 1.9% by weight Mn is a component necessary not only for deoxidation but also for maintaining strength. The upper limit is set to 1.9% because if it exceeds this, it is not preferable from the viewpoint of toughness, and the lower limit is set to 0.3% as the amount required for deoxidation.
【0010】Cr:5.8〜14% Crは耐酸化性と焼き入れ性を確保する上で非常に重要
な元素であるため最低5.8%必要であるが14%を超
すと耐割れ性を損なうと同時にδフェライトを晶出させ
靱性の劣化が著しくなるので上限は14%とした。Cr: 5.8 to 14% Cr is a very important element for securing the oxidation resistance and hardenability, so at least 5.8% is required, but if it exceeds 14%, crack resistance is high. Is impaired and δ-ferrite is crystallized and toughness is significantly deteriorated, so the upper limit was made 14%.
【0011】Mo:0.1〜1.6% Moは固溶体強化により高温強度を顕著に高める元素
で、使用温度、圧力の上昇に対する耐高温強度特性向上
の目的で添加するが、多量に添加された場合溶接性を損
ない、かつδフェライトを晶出させるため靱性の低下を
招く。したがって添加範囲として上限を1.6%とし
た。一方、Wとの共存において、高温強度、特に高温長
時間側でのクリープ破断強度の向上に効果のあるのは
0.1%以上であるので下限を0.1%とした。Mo: 0.1 to 1.6% Mo is an element that remarkably enhances high temperature strength by solid solution strengthening. It is added for the purpose of improving high temperature strength resistance characteristics against increase in operating temperature and pressure, but a large amount is added. In that case, the weldability is impaired and δ-ferrite is crystallized, resulting in a decrease in toughness. Therefore, the upper limit of the addition range is set to 1.6%. On the other hand, in the coexistence with W, 0.1% or more is effective in improving the high temperature strength, especially the creep rupture strength on the high temperature long time side, so the lower limit was made 0.1%.
【0012】W:0.5〜3.5% Wはフェライト系溶接金属のクリープ破断強度に寄与す
る固溶体強化元素として最も優れた元素である。特に、
高温長時間でのクリープ破断強度向上の効果は極めて大
きい。しかしながら0.5%未満ではMoとの共存にお
いて効果は発揮できないので下限を0.5%と定めた。
しかし過剰に添加するとδフェライトを晶出させ溶接金
属の靱性が低下し、溶接作業性も劣化するので上限を
3.5%とした。W: 0.5 to 3.5% W is the most excellent element as a solid solution strengthening element that contributes to the creep rupture strength of a ferritic weld metal. Especially,
The effect of improving the creep rupture strength at high temperature for a long time is extremely large. However, if it is less than 0.5%, the effect cannot be exhibited in the coexistence with Mo, so the lower limit was set to 0.5%.
However, if added excessively, δ ferrite is crystallized to reduce the toughness of the weld metal and the welding workability is deteriorated, so the upper limit was made 3.5%.
【0013】V:0.03〜0.40% Vは炭窒化物として析出させて強度を確保する上で最低
0.03%が必要であるが、他方0.40%を超えると
かえって強度低下を生じるので上限を0.40%とし
た。V: 0.03 to 0.40% V is required to be at least 0.03% in order to be precipitated as carbonitride to secure the strength, but on the other hand, when it exceeds 0.40%, the strength is rather lowered. Therefore, the upper limit was made 0.40%.
【0014】Nb:0.01〜0.15% NbはVと同様に炭窒化物として析出して強度を確保す
るほか、結晶粒を微細化して靱性を高める元素としても
重要であるため最低0.01%が必要である。しかし、
0.15%を超えるとその効果は飽和してしまうだけで
なく溶接性の低下も招くので上限を0.15%とした。Nb: 0.01 to 0.15% Nb is precipitated as a carbonitride similarly to V to secure strength, and is also important as an element for refining crystal grains to enhance toughness, so that it is at least 0. 0.01% is required. But,
If it exceeds 0.15%, not only the effect is saturated but also the weldability is deteriorated, so the upper limit was made 0.15%.
【0015】Ni:0.05〜1.2% Niはフェライトの生成を抑制し、使用中の脆化軽減に
有効な元素であり、高温で長時間使用される用途に対し
ては必須の元素であるが、0.05%未満ではその効果
は得られない。他方1.2%を超すと高温クリープ特性
を劣化させるので上限を1.2%とした。Ni: 0.05 to 1.2% Ni is an element that suppresses the formation of ferrite and is effective in reducing embrittlement during use, and is an essential element for applications that are used at high temperatures for a long time. However, if less than 0.05%, the effect cannot be obtained. On the other hand, if it exceeds 1.2%, the high temperature creep property is deteriorated, so the upper limit was made 1.2%.
【0016】Cu:0.5〜4.0% CuはMo、Wによって生じるδフェライトの晶出とい
う問題点を相殺する元素であり、最低0.5%以上を必
要とする。しかし過剰添加すると、高温焼戻しが不可能
となり組織の安定化処理ができなくなるので上限を4.
0%とした。Cu: 0.5 to 4.0% Cu is an element that offsets the problem of crystallization of δ ferrite generated by Mo and W, and is required to be at least 0.5%. However, if added excessively, high temperature tempering becomes impossible and the structure cannot be stabilized, so the upper limit is set to 4.
0%.
【0017】N:0.01〜0.08% Nは基地中に固溶しても、また窒化物として析出しても
著しく耐クリープ性に寄与するがそのためには最低0.
01%を必要とする。一方、0.08%を超えると窒化
物が多量に析出して、逆に靱性が劣化するなどの問題が
生じるので上限を0.08%と定めた。N: 0.01 to 0.08% N contributes significantly to the creep resistance even if it forms a solid solution in the matrix or precipitates as a nitride.
Requires 01%. On the other hand, if it exceeds 0.08%, a large amount of nitride precipitates, which causes problems such as deterioration of toughness. Therefore, the upper limit was set to 0.08%.
【0018】Ta:0.001〜3.0% Taは高温強度およびクリープ破断強度を著しく高める
成分であり、TaCが析出し、特に高温長時間でのクリ
ープ破断強度向上への効果が極めて大きい。しかし0.
001%未満では効果が得られず、一方3.0%を超え
ると靱性の劣化が顕著になるので上限を3.0%と定め
た。Ta: 0.001 to 3.0% Ta is a component that remarkably enhances the high temperature strength and the creep rupture strength, and TaC is precipitated, and the effect of improving the creep rupture strength particularly at high temperature for a long time is extremely large. But 0.
If it is less than 001%, no effect is obtained, while if it exceeds 3.0%, the toughness is significantly deteriorated, so the upper limit was set to 3.0%.
【0019】Co:0.1〜5.0% Coは必要に応じて添加し、Cuと同様にMo、W添加
によって生じるδフェライトの晶出という問題点を相殺
する元素であるが、この効果を得るには最低0.1%以
上を必要とする。しかし過剰に添加するとAC1点を下げ
るため高温焼戻しが不可能となり、組織の安定化処理が
できなくなるという欠点を有するので、上限を5.0%
と定めた。Co: 0.1 to 5.0% Co is an element that is added if necessary and cancels out the problem of crystallization of δ ferrite caused by the addition of Mo and W like Cu, but this effect In order to obtain, at least 0.1% is required. However, if added excessively, the A C1 point will be lowered and tempering at a high temperature will not be possible, and there is a drawback that the structure cannot be stabilized.
It was decided.
【0020】本発明では上記各成分を溶接棒全体として
調整する必要がある。この場合、溶接棒全体の各成分の
量は、炭素の場合を例にとると、下記被覆率A(%)を
考慮して、次式で表される量である。In the present invention, it is necessary to adjust each of the above components as a whole welding rod. In this case, the amount of each component of the entire welding rod is the amount represented by the following formula in consideration of the following coverage A (%), taking carbon as an example.
【0021】[溶接棒のC](%)=[心線中のC]×
(100−A)/100+[被覆剤中のC]×A/10
0[C of welding rod] (%) = [C in core wire] ×
(100-A) / 100 + [C in coating agent] × A / 10
0
【0022】本発明の被覆アーク溶接棒は、前述の成分
の他に金属炭酸塩、金属弗化物、アーク安定剤、スラグ
生成剤として被覆剤中に石灰、蛍石、アルミナ、鉄粉、
アルカリ成分、ルチル等を添加する。被覆アーク溶接棒
全重量に対する被覆剤の重量%(被覆率)の範囲は、2
5〜35%にする必要がある。25%未満では保護筒と
しての機能が不十分になってスパッタが増加したり、生
成スラグ量の不足によってビード外観が悪化する。一方
35%を超えるとスラグ量が多くなり過ぎるためにスラ
グ巻き込み等の欠陥が発生し易くなると共に、開先幅の
狭い溶接継手に適用した場合に運棒が困難になる。さら
に粘結剤としては、主に珪酸ソーダ、珪酸カリを含有す
る水ガラスを用いるものである。本発明の被覆アーク溶
接棒は、通常の溶接棒塗装機により被覆塗装した後、水
分を除去するために300〜550℃で焼成して製造す
る。The coated arc welding rod according to the present invention is characterized in that, in addition to the above-described components, lime, fluorite, alumina, iron powder,
Add alkaline components, rutile, etc. The range of the coating agent weight% (coverage ratio) based on the total weight of the coated arc welding rod is 2
It should be 5 to 35%. If it is less than 25%, the function as a protective cylinder becomes insufficient and spatter increases, or the bead appearance deteriorates due to insufficient amount of slag produced. On the other hand, if it exceeds 35%, the amount of slag becomes too large and defects such as slag entrainment are likely to occur, and when it is applied to a welded joint having a narrow groove width, it becomes difficult to carry. Further, as the binder, water glass mainly containing sodium silicate and potassium silicate is used. The coated arc welding rod of the present invention is manufactured by coating and coating with an ordinary welding rod coating machine and then firing at 300 to 550 ° C. to remove water.
【0023】[0023]
【実施例】以下に本発明の実施例を説明する。この実施
例においては本発明に従って規定される元素を含有させ
た表1、表2の鋼心線(4.0mm径)の外周に被覆率
30%となるように表2、表3の組成の被覆剤を塗布
し、被覆アーク溶接棒を製造した。得られた各被覆アー
ク溶接棒を用い、供試母材として厚さ20mmのAST
M規格A387 Gr.22,9Cr−1Mo鋼、9C
r−1Mo−Nb−V−W鋼、9Cr−0.5Mo−N
b−V−W鋼、11Cr−0.2Mo−Nb−V−W−
Co鋼、12Cr−Nb−V−W鋼を図1に示すような
開先(被溶接材1の厚さT=20mm、開先角度θ=2
0゜、裏当材2を用いル−トギャップL=12mm)を
形成し、アーク溶接を行った。なお溶接条件は、溶接電
流160アンペア、溶接入熱20kJ/cm、予熱・パ
ス間温度150〜200℃、下向き姿勢で溶接継手を作
製した。得られた溶接金属を760℃で5時間の後熱処
理をした後、600℃、250N/mm2 の応力でのク
リ−プ破断試験および試験温度0℃での2mmVノッチ
衝撃試験を行った。Embodiments of the present invention will be described below. In this example, the composition of Tables 2 and 3 was adjusted so that the outer periphery of the steel core wires (4.0 mm diameter) of Tables 1 and 2 containing the elements specified according to the present invention had a coverage of 30%. The coating agent was applied to produce a coated arc welding rod. Using each of the obtained coated arc welding rods, AST with a thickness of 20 mm as the test base metal
M standard A387 Gr. 22,9Cr-1Mo steel, 9C
r-1Mo-Nb-V-W steel, 9Cr-0.5Mo-N
b-V-W steel, 11Cr-0.2Mo-Nb-V-W-
Grooves such as Co steel and 12Cr-Nb-V-W steel as shown in FIG. 1 (thickness T of welded material 1 = 20 mm, groove angle θ = 2)
A root gap L = 12 mm was formed using the backing material 2 at 0 ° and arc welding was performed. The welding conditions were as follows: a welding current of 160 amperes, a welding heat input of 20 kJ / cm, a preheating / pass temperature of 150 to 200 ° C., and a welded joint in a downward posture. After the post-heat treatment of the obtained weld metal at 760 ° C. for 5 hours, a creep rupture test under a stress of 600 ° C. and 250 N / mm 2 and a 2 mmV notch impact test at a test temperature of 0 ° C. were performed.
【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】表4に上記クリープ破断試験結果を破断時
間(hr)で示し、また衝撃試験結果をvE0℃(J)
で示す。LT1〜LT10はいずれも本発明の要件をす
べて満たしており、溶接金属組織はδフェライトの晶出
はなくマルテンサイト単相組織であり、後熱処理後の靱
性およびクリ−プ破断特性が良好で、かつ溶接性の優れ
た溶接金属を得ることができた。Table 4 shows the results of the creep rupture test in terms of rupture time (hr), and the results of the impact test are vE0 ° C (J).
Indicated by All of LT1 to LT10 satisfy all the requirements of the present invention, the weld metal structure is a martensite single phase structure without crystallization of δ ferrite, and the toughness and creep rupture properties after the post heat treatment are good, Moreover, a weld metal having excellent weldability could be obtained.
【0029】溶接棒LT11〜LT20は比較例を示
す。溶接棒LT11は通常の耐熱鋼用として使用されて
いる2.25%Cr−1%Mo系溶接棒の例であり、溶
接棒LT12はさらに耐高温腐食性を向上させた熱交換
器用溶接棒であるが、いずれも本発明溶接棒に比べ、著
しくクリ−プ破断強度が低い。The welding rods LT11 to LT20 show comparative examples. The welding rod LT11 is an example of a 2.25% Cr-1% Mo-based welding rod that is used for ordinary heat resistant steel, and the welding rod LT12 is a welding rod for a heat exchanger with further improved high temperature corrosion resistance. However, in both cases, the creep rupture strength is significantly lower than that of the welding rod of the present invention.
【0030】溶接棒LT13〜LT15は9Cr−1M
o−Nb−V−W系の溶接棒の例である。LT13はC
量が本発明溶接棒に比べて著しく高いので、溶接時に割
れが発生し、耐割れ性および衝撃値が低下した。The welding rods LT13 to LT15 are 9Cr-1M.
It is an example of an o-Nb-V-W welding rod. LT13 is C
Since the amount was significantly higher than that of the welding rod of the present invention, cracking occurred during welding, and the crack resistance and impact value decreased.
【0031】溶接棒LT14はCuが含まれていないう
え、Mo量が上限を上回りδフェライトを生じ、さらに
N量がその上限を超えているので靱性が劣化した。また
溶接棒LT15はSi、Mnが下限を下回っているため
脱酸効果が十分に得られず溶接金属にピットが発生し
た。またTa量が上限を上回り、靱性が乏しかった。The welding rod LT14 contained no Cu, the Mo content exceeded the upper limit, and δ ferrite was produced. Further, the N content exceeded the upper limit, so that the toughness deteriorated. Further, since the welding rod LT15 had Si and Mn below the lower limits, a sufficient deoxidizing effect was not obtained, and pits were generated in the weld metal. Further, the Ta amount exceeded the upper limit, and the toughness was poor.
【0032】溶接棒LT16、LT18〜LT20は9
Cr−0.5Mo−Nb−V−W系、またLT17は1
2Cr−0.5Mo−Nb−V−W系の溶接棒である。
溶接棒LT16はNi量が上限を超えるもので高温クリ
−プ破断強度が低い。また溶接棒LT17はV量および
Nb量が上限を上回っており、高温強度および靱性が低
くまた作業性も劣った。The welding rods LT16, LT18 to LT20 are 9
Cr-0.5Mo-Nb-VW system, LT17 is 1
2Cr-0.5Mo-Nb-VW-based welding rod.
The welding rod LT16 has a Ni content exceeding the upper limit and has a low high temperature creep rupture strength. In addition, the welding rod LT17 had V content and Nb content exceeding the upper limits, so the high temperature strength and toughness were low and the workability was poor.
【0033】溶接棒LT18はW量が上限を上回ってお
りδフェライトが生じ靱性が低下した。また溶接棒LT
19はCo量が、LT20はCu量が上限を上回り、高
温焼戻しが不可能となり組織の安定化処理ができなくな
り靱性が低下した。In the welding rod LT18, the W content exceeded the upper limit, and δ ferrite was produced to lower the toughness. Welding rod LT
No. 19 had a Co content and LT20 had a Cu content exceeding the upper limit, and high temperature tempering was impossible, so that the structure could not be stabilized and the toughness deteriorated.
【0034】[0034]
【発明の効果】本発明溶接材料は従来の9%〜12%C
r鋼用被覆アーク溶接棒と比較して、高温でのクリ−プ
強度を著しく高めたものであり、靱性および溶接性など
の特性にも優れている。例えば、表1ないし表4に示し
たように本発明の要件を満たすものは、本発明の要件を
満たさないもの(比較例)と比べて高温クリ−プ特性だ
けでなく、高温引張強さ、靱性および溶接性に優れてい
ることは明らかである。各種発電ボイラ、化学圧力容器
などに使用される9〜12%Cr系鋼等を溶接する場合
に本発明に係わる溶接材料を使用することにより、溶接
継手の信頼性を大幅に向上することができる。The welding material of the present invention has a conventional 9% to 12% C
Compared with the coated arc welding rod for r steel, the creep strength at high temperature is remarkably enhanced, and it has excellent characteristics such as toughness and weldability. For example, as shown in Tables 1 to 4, those satisfying the requirements of the present invention have not only high temperature creep properties but also high temperature tensile strength as compared with those not satisfying the requirements of the present invention (Comparative Examples), It is clear that it has excellent toughness and weldability. The reliability of welded joints can be greatly improved by using the welding material according to the present invention when welding 9 to 12% Cr-based steel used in various power generation boilers, chemical pressure vessels, and the like. .
【図1】実施例に用いた溶接部の開先形状を示す断面図FIG. 1 is a sectional view showing a groove shape of a welded portion used in an embodiment.
1 被溶接材 2 裏当材 1 Material to be welded 2 Backing material
Claims (2)
溶接棒において、被覆アーク溶接棒全重量に対して重量
%で、 C :0.01〜0.12% Si:0.1〜2.4% Mn:0.3〜1.9% Cr:5.8〜14% Mo:0.1〜1.6% W :0.5〜3.5% V :0.03〜0.40% Nb:0.01〜0.15% Ni:0.05〜1.2% Cu:0.5〜4.0% N :0.01〜0.08% Ta:0.001〜3.0% を含有し、残部はFeおよび不可避的不純物からなる鋼
心線に、金属炭酸塩、金属弗化物、アーク安定剤、スラ
グ生成剤、脱酸剤、粘結剤を含む被覆剤を含有せしめ、
被覆率(溶接棒全重量に対する被覆剤重量の割合)が2
5〜35重量%となるように被覆したことを特徴とする
高Crフェライト系耐熱鋼用被覆アーク溶接棒。1. In a coated arc welding rod for high Cr ferritic heat-resistant steel, C: 0.01 to 0.12% Si: 0.1 to 2 in% by weight based on the total weight of the coated arc welding rod. 0.4% Mn: 0.3 to 1.9% Cr: 5.8 to 14% Mo: 0.1 to 1.6% W: 0.5 to 3.5% V: 0.03 to 0.40 % Nb: 0.01 to 0.15% Ni: 0.05 to 1.2% Cu: 0.5 to 4.0% N: 0.01 to 0.08% Ta: 0.001 to 3.0 %, With the balance being Fe and unavoidable impurities, and a coating material containing a metal carbonate, a metal fluoride, an arc stabilizer, a slag generator, a deoxidizer, and a binder.
Coverage (ratio of coating weight to total welding rod weight) is 2
A coated arc welding rod for high Cr ferritic heat-resistant steel, which is coated so as to be 5 to 35% by weight.
で、さらにCo:0.5〜5.0%を添加したことを特
徴とする請求項1記載の高Crフェライト系耐熱鋼用被
覆ア−ク溶接棒。2. A weight percentage based on the total weight of the coated arc welding rod.
2. The coated arc welding rod for high Cr ferritic heat-resistant steel according to claim 1, further comprising Co: 0.5 to 5.0%.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP7303361A JPH09122972A (en) | 1995-10-30 | 1995-10-30 | Coated electrode for high-cr ferrite heat resisting steel |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP7303361A JPH09122972A (en) | 1995-10-30 | 1995-10-30 | Coated electrode for high-cr ferrite heat resisting steel |
Publications (1)
Publication Number | Publication Date |
---|---|
JPH09122972A true JPH09122972A (en) | 1997-05-13 |
Family
ID=17920068
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP7303361A Pending JPH09122972A (en) | 1995-10-30 | 1995-10-30 | Coated electrode for high-cr ferrite heat resisting steel |
Country Status (1)
Country | Link |
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JP (1) | JPH09122972A (en) |
Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH11170087A (en) * | 1997-12-05 | 1999-06-29 | Kobe Steel Ltd | Low hydrogen coated electrode for high cr ferritic heat resisting steel |
EP0930127A1 (en) * | 1998-01-20 | 1999-07-21 | Mitsubishi Heavy Industries, Ltd. | Welding materials for high-Cr steels |
JP2000301377A (en) * | 1999-04-16 | 2000-10-31 | Sumitomo Metal Ind Ltd | Welded joint of ferritic heat resistant steel and welding material |
CN102943209A (en) * | 2012-11-16 | 2013-02-27 | 中国科学院金属研究所 | Radiation-resistant martensite heat-resistant steel having excellent compatibility with Pb and Pb-Bi |
CN103898411A (en) * | 2012-12-28 | 2014-07-02 | 中国科学院金属研究所 | Liquid metal corrosion resistance martensite structural material for high temperature and preparation method of material |
EP3919221A4 (en) * | 2019-03-26 | 2022-05-04 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Covered electrode for high-cr ferritic heat-resistant steels |
Citations (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH01215491A (en) * | 1988-02-24 | 1989-08-29 | Nkk Corp | Covered arc welding electrode for cr-mo low alloy steel |
JPH04305396A (en) * | 1991-03-29 | 1992-10-28 | Nippon Steel Corp | Low hydrogen type coated arc welding rod |
JPH04365838A (en) * | 1991-06-14 | 1992-12-17 | Kawasaki Steel Corp | Ferritic heat resisting steel excellent in hot workability and strength at high temperature |
JPH05261589A (en) * | 1992-03-17 | 1993-10-12 | Nippon Steel Corp | Coated electrode for high-cr ferritic heat resisting steel |
JPH07155988A (en) * | 1993-12-03 | 1995-06-20 | Nippon Steel Corp | Coated arc electrode for high-cr ferritic heat resisting steel |
JPH07204885A (en) * | 1994-01-14 | 1995-08-08 | Sumitomo Metal Ind Ltd | Ferrite steel welding material having excellent high-temperature weld crack resistance |
JPH07268562A (en) * | 1994-03-30 | 1995-10-17 | Nippon Steel Corp | Coated rod for arc welding used for high cr ferritic heat resistant steel |
JPH09122971A (en) * | 1995-10-26 | 1997-05-13 | Sumitomo Metal Ind Ltd | Welding material for high-strength, high-corrosion resistant steel having excellent welding procedure characteristic |
-
1995
- 1995-10-30 JP JP7303361A patent/JPH09122972A/en active Pending
Patent Citations (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH01215491A (en) * | 1988-02-24 | 1989-08-29 | Nkk Corp | Covered arc welding electrode for cr-mo low alloy steel |
JPH04305396A (en) * | 1991-03-29 | 1992-10-28 | Nippon Steel Corp | Low hydrogen type coated arc welding rod |
JPH04365838A (en) * | 1991-06-14 | 1992-12-17 | Kawasaki Steel Corp | Ferritic heat resisting steel excellent in hot workability and strength at high temperature |
JPH05261589A (en) * | 1992-03-17 | 1993-10-12 | Nippon Steel Corp | Coated electrode for high-cr ferritic heat resisting steel |
JPH07155988A (en) * | 1993-12-03 | 1995-06-20 | Nippon Steel Corp | Coated arc electrode for high-cr ferritic heat resisting steel |
JPH07204885A (en) * | 1994-01-14 | 1995-08-08 | Sumitomo Metal Ind Ltd | Ferrite steel welding material having excellent high-temperature weld crack resistance |
JPH07268562A (en) * | 1994-03-30 | 1995-10-17 | Nippon Steel Corp | Coated rod for arc welding used for high cr ferritic heat resistant steel |
JPH09122971A (en) * | 1995-10-26 | 1997-05-13 | Sumitomo Metal Ind Ltd | Welding material for high-strength, high-corrosion resistant steel having excellent welding procedure characteristic |
Cited By (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH11170087A (en) * | 1997-12-05 | 1999-06-29 | Kobe Steel Ltd | Low hydrogen coated electrode for high cr ferritic heat resisting steel |
EP0930127A1 (en) * | 1998-01-20 | 1999-07-21 | Mitsubishi Heavy Industries, Ltd. | Welding materials for high-Cr steels |
US6290904B1 (en) | 1998-01-20 | 2001-09-18 | Mitsubishi Heavy Industries, Ltd. | Welding materials for high-Cr steels |
JP2000301377A (en) * | 1999-04-16 | 2000-10-31 | Sumitomo Metal Ind Ltd | Welded joint of ferritic heat resistant steel and welding material |
CN102943209A (en) * | 2012-11-16 | 2013-02-27 | 中国科学院金属研究所 | Radiation-resistant martensite heat-resistant steel having excellent compatibility with Pb and Pb-Bi |
CN103898411A (en) * | 2012-12-28 | 2014-07-02 | 中国科学院金属研究所 | Liquid metal corrosion resistance martensite structural material for high temperature and preparation method of material |
CN103898411B (en) * | 2012-12-28 | 2016-01-13 | 中国科学院金属研究所 | The high temperature martensitic structure of resistance to liquid metal corrosion material and preparation method |
EP3919221A4 (en) * | 2019-03-26 | 2022-05-04 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Covered electrode for high-cr ferritic heat-resistant steels |
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