JPH106079A - Welding material for ferritic heat resistant steel - Google Patents
Welding material for ferritic heat resistant steelInfo
- Publication number
- JPH106079A JPH106079A JP15931496A JP15931496A JPH106079A JP H106079 A JPH106079 A JP H106079A JP 15931496 A JP15931496 A JP 15931496A JP 15931496 A JP15931496 A JP 15931496A JP H106079 A JPH106079 A JP H106079A
- Authority
- JP
- Japan
- Prior art keywords
- strength
- welding
- welding material
- content
- resistant steel
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 238000003466 welding Methods 0.000 title claims abstract description 39
- 239000000463 material Substances 0.000 title claims abstract description 22
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 21
- 239000010959 steel Substances 0.000 title claims abstract description 21
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 7
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 7
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 7
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 6
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 5
- 229910052702 rhenium Inorganic materials 0.000 claims abstract description 5
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 5
- 229910052742 iron Inorganic materials 0.000 claims abstract description 4
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 4
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 3
- 239000002184 metal Substances 0.000 abstract description 14
- 229910052751 metal Inorganic materials 0.000 abstract description 14
- 229910052799 carbon Inorganic materials 0.000 abstract description 5
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 4
- 230000000694 effects Effects 0.000 description 12
- 230000000052 comparative effect Effects 0.000 description 5
- 230000001771 impaired effect Effects 0.000 description 5
- 150000001247 metal acetylides Chemical class 0.000 description 4
- 230000000087 stabilizing effect Effects 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 3
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- 229910001566 austenite Inorganic materials 0.000 description 2
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 2
- 229910001563 bainite Inorganic materials 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000009863 impact test Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 230000003111 delayed effect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 238000010248 power generation Methods 0.000 description 1
- 238000012827 research and development Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
Landscapes
- Arc Welding In General (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は高温高圧下で使用さ
れる蒸気発生器，ボイラ等の熱交換器など、特に５００
℃以上の高温環境下で使用される高強度フェライト系耐
熱鋼の溶接に好適な溶接材料に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a heat generator such as a steam generator or a boiler used under a high temperature and a high pressure.
The present invention relates to a welding material suitable for welding high-strength ferritic heat-resistant steel used in a high-temperature environment of not less than ° C.
【０００２】[0002]
【従来の技術】ボイラ，化学工業，原子力用などの高温
耐熱耐圧部材としては、オーステナイト系ステンレス
鋼，Ｃｒ含有量が９〜１２％の高Ｃｒフェライト鋼，２
・１／４Ｃｒ−１Ｍｏ鋼に代表される低Ｃｒフェライト
鋼，炭素鋼などがあるが（以下、合金成分の含有量はす
べて重量％を意味する）、これらは対象部材の使用温
度，圧力，使用環境などに応じ、かつ経済性を考慮して
選択されている。フェライト系耐熱鋼はオーステナイト
系ステンレス鋼に比べ、ＣｒおよびＮｉ元素の含有量が
少ないため安価であるという特徴がある。近年、経済性
の観点からフェライト鋼の研究開発が盛んに行われ、高
強度のフェライト鋼が開発されているが、それに見合う
特性を有する溶接材料の開発は遅れている。2. Description of the Related Art Austenitic stainless steel, high Cr ferrite steel containing 9 to 12% of Cr,
・ There are low Cr ferritic steels and carbon steels represented by 1 / 4Cr-1Mo steels (the content of alloying components means all weight%), but these are used temperature, pressure and usage of the target member. The selection is made according to the environment and economics. Ferritic heat-resistant steel has a feature that it is inexpensive because it contains less Cr and Ni elements than austenitic stainless steel. In recent years, research and development of ferritic steels have been actively conducted from the viewpoint of economy, and high-strength ferritic steels have been developed. However, development of welding materials having properties corresponding thereto has been delayed.
【０００３】[0003]
【発明が解決しようとする課題】そこで本発明は溶接後
の溶接金属が既存の高強度フェライト系耐熱鋼と同等以
上の高温強度を有し、かつ靱性に優れた溶接材料を提供
しようとするものである。SUMMARY OF THE INVENTION Accordingly, an object of the present invention is to provide a welding material in which the weld metal after welding has a high temperature strength equal to or higher than that of existing high-strength ferritic heat-resistant steel and has excellent toughness. It is.
【０００４】[0004]
【課題を解決するための手段】本発明は従来添加元素と
して用いられていなかったＲｅ元素を添加した組成を有
する溶接材料であって、重量％で、Ｃ：０．０３〜０．
１２％、Ｓｉ：０．１〜０．７％、Ｍｎ：０．１〜１
％、Ｐ：０．００２〜０．０２５％、Ｓ：０．００１〜
０．０１５％、Ｃｒ：０．８〜３％、Ｎｉ：０．０１〜
１％、Ｍｏ：０．１〜３％、Ｖ：０．０１〜０．５％、
Ｗ：０．１〜３％、Ｎｂ：０．０１〜０．２％、Ｒｅ：
０．１〜１．５％、Ａｌ：０．００３〜０．０５％、
Ｂ：０．０００１〜０．０１％、Ｎ：０．００３〜０．
０３％を含み残部は鉄および不可避的不純物からなる高
温強度と靱性に優れたことを特徴とする高強度フェライ
ト系耐熱鋼用溶接材料を提供するものである。以下に各
成分の作用とその含有量の選定理由を説明する。SUMMARY OF THE INVENTION The present invention relates to a welding material having a composition to which a Re element, which has not been used as an additional element in the past, is added.
12%, Si: 0.1 to 0.7%, Mn: 0.1 to 1
%, P: 0.002 to 0.025%, S: 0.001 to
0.015%, Cr: 0.8-3%, Ni: 0.01-
1%, Mo: 0.1 to 3%, V: 0.01 to 0.5%,
W: 0.1-3%, Nb: 0.01-0.2%, Re:
0.1-1.5%, Al: 0.003-0.05%,
B: 0.0001 to 0.01%, N: 0.003 to 0.
An object of the present invention is to provide a welding material for high-strength ferritic heat-resistant steel, which is characterized by having excellent high-temperature strength and toughness including iron and unavoidable impurities, the balance being 0.3%. The function of each component and the reason for selecting the content will be described below.
【０００５】[0005]
【発明の実施の形態】ＣはＣｒ，Ｆｅ，Ｗ，Ｖ，Ｎｂと
結合して炭化物を形成し高温強度に寄与するとともに、
それ自身がオーステナイト安定化元素として組織を安定
化する。０．０３％未満では炭化物析出が不十分でクリ
ープ破断強度が低く、また、０．１２％を越える場合は
炭化物が過剰析出して溶接金属が著しく硬化し衝撃特性
が悪化する。また、溶接作業性もＣの添加量に比例して
悪くなるため、Ｃの適正含有量は０．０３〜０．１２％
である。BEST MODE FOR CARRYING OUT THE INVENTION C combines with Cr, Fe, W, V and Nb to form carbides and contributes to high-temperature strength.
As such, it stabilizes the structure as an austenite stabilizing element. If it is less than 0.03%, the precipitation of carbides is insufficient and the creep rupture strength is low. If it exceeds 0.12%, carbides are excessively precipitated and the weld metal is remarkably hardened to deteriorate the impact characteristics. Further, since the welding workability also deteriorates in proportion to the added amount of C, the appropriate content of C is 0.03 to 0.12%.
It is.
【０００６】Ｓｉは脱酸剤として働き０．７％を越える
と靱性が著しく低下し、強度に対しても有害である。Ｓ
ｉの含有量は０．１〜０．７％とする。[0006] Si acts as a deoxidizing agent, and when it exceeds 0.7%, toughness is remarkably reduced, and is harmful to strength. S
The content of i is 0.1 to 0.7%.
【０００７】Ｍｎは組織の安定化に有効であるが、０．
１％未満では十分な効果が得られず、１％を越えると溶
接金属を硬化させる。よってＭｎの含有量は０．１〜１
％とする。[0007] Mn is effective for stabilizing the structure.
If it is less than 1%, a sufficient effect cannot be obtained, and if it exceeds 1%, the weld metal is hardened. Therefore, the content of Mn is 0.1 to 1
%.
【０００８】Ｐ，Ｓはいずれも靱性、加工性に有害な元
素で、Ｓが極微量であっても粒界やＣｒ2 Ｏ3 スケール
皮膜を不安定にし、強度、靱性低下の原因となるから、
許容範囲内でもできるだけ少ないほうがよい。不可避な
含有量として、Ｐは０．００２〜０．０２５％、Ｓは
０．００１〜０．０１５％とした。Both P and S are harmful elements for toughness and workability. Even if the amount of S is extremely small, P and S destabilize the grain boundaries and Cr 2 O 3 scale film, and cause reduction in strength and toughness. ,
It is better to be as small as possible even within the allowable range. As inevitable contents, P was set to 0.002 to 0.025% and S was set to 0.001 to 0.015%.
【０００９】Ｃｒは耐熱鋼の耐酸化性、高温腐食性の点
から不可欠な元素であり、その含有量が０．８％未満で
は十分な耐酸化性、高温腐食性が得られない。一方３％
を越えて添加すると、むしろ強度と靱性を損ない経済性
の観点からも不利となる。従って、Ｃｒの含有量は０．
８〜３％とする。[0009] Cr is an indispensable element from the viewpoint of the oxidation resistance and high-temperature corrosion resistance of heat-resistant steel. If its content is less than 0.8%, sufficient oxidation resistance and high-temperature corrosion resistance cannot be obtained. 3%
If it is added in excess of the above, the strength and toughness are impaired, which is disadvantageous from the viewpoint of economy. Therefore, the content of Cr is 0.1.
8 to 3%.
【００１０】Ｎｉはオーステナイト安定化元素であり、
かつ靱性改善に寄与するが、その含有量が１％を越える
と高温クリープ強度を損なう。また経済性を鑑みても大
量添加は不利である。従ってＮｉの含有量は０．０１〜
１％とする。Ni is an austenite stabilizing element,
And it contributes to improvement of toughness, but if its content exceeds 1%, the high temperature creep strength is impaired. Also, in view of economy, large-scale addition is disadvantageous. Therefore, the content of Ni is 0.01 to
1%.
【００１１】Ｍｏはクリープ強度の向上に有効である
が、０．１％以下では十分な効果が得られず、３％を越
えると高温で金属間化合物が析出し靱性が低下するだけ
でなく、強度に対しても効果がなくなる。従って、０．
１〜３％とした。Mo is effective in improving the creep strength. However, if it is less than 0.1%, a sufficient effect cannot be obtained. If it exceeds 3%, not only intermetallic compounds are precipitated at a high temperature but the toughness is lowered, No effect on strength. Therefore, 0.
1-3%.
【００１２】ＶはＣ，Ｎと結合してＶ（Ｃ，Ｎ）等の微
細析出物を形成する。この析出物は高温での長時間クリ
ープ強度の向上に大きく寄与するが、０．０１％未満で
は十分な効果が得られず、０．５％を越える場合にはか
えってクリープ強度と靱性を損なう。よって、Ｖの適正
含有量は０．０１〜０．５％である。V combines with C and N to form fine precipitates such as V (C, N). These precipitates greatly contribute to the improvement of long-term creep strength at high temperatures. However, if the content is less than 0.01%, a sufficient effect cannot be obtained, and if it exceeds 0.5%, the creep strength and toughness are rather deteriorated. Therefore, the appropriate content of V is 0.01 to 0.5%.
【００１３】Ｗは固溶強化および微細炭化物析出強化元
素としてクリープ強度の向上に有効であり、特にＭｏと
の複合添加により、さらにクリープ強度を高めることが
できる。０．１％未満では効果がなく、３％を越えると
鋼を硬化させ溶接作業性も損なうため、０．１〜３％の
範囲とする。W is effective for improving the creep strength as a solid solution strengthening element and a fine carbide precipitation strengthening element. In particular, the addition of Mo in combination with Mo can further increase the creep strength. If it is less than 0.1%, there is no effect, and if it exceeds 3%, the steel is hardened and welding workability is impaired.
【００１４】ＮｂはＶと同様Ｃ，Ｎと結合してＮｂ
（Ｃ，Ｎ）を形成しクリープ強度に寄与する。特に６０
０℃以下の比較的低温では著しい強度改善効果を示す。
また、溶接金属の組織を微細化する効果もあり、適量で
あれば靱性改善にも効果がある。０．０１％未満では上
記の効果が得られず、また０．２％を越える場合は未固
溶ＮｂＣが増えクリープ強度と靱性を損なう。従って、
Ｎｂ含有量は０．０１〜０．２％が適当である。Nb is bonded to C and N like V to form Nb
It forms (C, N) and contributes to creep strength. Especially 60
At a relatively low temperature of 0 ° C. or less, a remarkable strength improving effect is exhibited.
In addition, it also has the effect of making the structure of the weld metal finer, and an appropriate amount is also effective in improving toughness. If it is less than 0.01%, the above effects cannot be obtained, and if it exceeds 0.2%, undissolved NbC increases to impair creep strength and toughness. Therefore,
The Nb content is suitably from 0.01 to 0.2%.
【００１５】Ｒｅの添加は本発明ワイヤ成分の特徴であ
り、添加量に比例してクリープ強度を高めることを見い
だした。これは固溶強化によるものであるが、重要なこ
とは同様の働きをするＭｏやＷと同時添加しても、さら
にクリープ強度が増すことである。よって、経済性を考
え０．１〜１．５％とするのが適当である。The addition of Re is a feature of the wire component of the present invention, and has been found to increase the creep strength in proportion to the amount of Re added. This is due to solid solution strengthening, but what is important is that the creep strength is further increased even when Mo and W having the same function are added simultaneously. Therefore, it is appropriate to set the value to 0.1 to 1.5% in consideration of economy.
【００１６】Ａｌは脱酸素元素として必須であり、含有
量として０．００３％以下では効果がなく、０．０５％
を越える場合はクリープ強度を損なうため、Ａｌの含有
量は０．００３〜０．０５％とする。Al is essential as a deoxidizing element, and has no effect when its content is 0.003% or less.
If it exceeds, the creep strength is impaired, so the Al content is made 0.003 to 0.05%.
【００１７】Ｂは極微量の添加により炭化物の分散、安
定化させる効果がある。０．０００１％未満ではその効
果が小さく、０．０１％を越えると加工性を損なうか
ら、Ｂの添加はその含有量を０．０００１〜０．０１％
の範囲にするのがよい。B has the effect of dispersing and stabilizing carbides by adding a very small amount. If it is less than 0.0001%, the effect is small, and if it exceeds 0.01%, processability is impaired. Therefore, the addition of B reduces the content to 0.0001 to 0.01%.
Should be within the range.
【００１８】ＮはＶ，Ｎｂとの炭窒化物形成に必要で
０．００３％未満ではその効果がない。しかしながら、
０．０３％を越える場合は組織が微細化するとともに窒
化物が粗大化し強度と靱性を損なう。よってＮの含有量
は０．０３％以下とし０．００３〜０．０３％とする。N is necessary for the formation of carbonitrides with V and Nb, and its effect is less than 0.003%. However,
If the content exceeds 0.03%, the structure becomes finer and the nitride becomes coarse, thus impairing the strength and toughness. Therefore, the N content is set to 0.03% or less and 0.003 to 0.03%.
【００１９】[0019]
【実施例】厚さ：２０ｍｍの２．２５Ｃｒ−１Ｍｏ鋼，
２．２５Ｃｒ−０．１Ｍｏ−１．６Ｗ−Ｖ−Ｎｂ鋼，９
Ｃｒ−１Ｍｏ−Ｖ−Ｎｂ鋼で図１に示すような開先（被
溶接材１の厚さｔ＝２０ｍｍ、開先角度θ＝２０o 、裏
当材２使用でルートギャップＬ＝２０ｍｍ）を形成し、
表１に示す成分組成のワイヤ径：１．６ｍｍの溶接ワイ
ヤを用い、表２に示す母材との組合わせと、表３に示す
溶接条件でＴＩＧ溶接した。得られた溶接金属に７１５
℃、２時間の後熱処理をした後、溶接金属のクリープ破
断強度と衝撃特性を調査するため、溶接金属よりクリー
プ破断試験片とシャルピー衝撃試験片を採取した。クリ
ープ破断試験は試験温度を６５０℃とし、応力は７０Ｍ
Ｐａおよび１００ＭＰａとした。シャルピー衝撃試験は
０℃にて２ｍｍＶノッチ試験片にて、ノッチ位置を溶接
金属中央として衝撃試験を実施した。また、溶接時に溶
接作業性について評価した。表２に試験結果を併せて示
す。表２における溶接作業性の記号中、◎は既存の溶接
材料より優れているものを、○は既存の溶接材料と同等
のものを、△は既存の溶接材料より少し劣っているもの
を、×は既存の溶接材料より悪いものを示す。EXAMPLE: 2.25Cr-1Mo steel with a thickness of 20 mm,
2.25Cr-0.1Mo-1.6W-V-Nb steel, 9
The groove as shown in FIG. 1 (the thickness t of the material to be welded 1 = 20 mm, the groove angle θ = 20 ° , and the root gap L = 20 mm when the backing material 2 is used) is shown in FIG. 1 for Cr-1Mo-V-Nb steel. Forming
Using a welding wire having a component composition shown in Table 1 and a wire diameter of 1.6 mm, TIG welding was performed in combination with the base material shown in Table 2 and welding conditions shown in Table 3. 715 on the resulting weld metal
After a post-heat treatment at 2 ° C. for 2 hours, a creep rupture test specimen and a Charpy impact test specimen were collected from the weld metal in order to investigate the creep rupture strength and impact characteristics of the weld metal. The creep rupture test was conducted at a test temperature of 650 ° C and a stress of 70M.
Pa and 100 MPa. The Charpy impact test was performed at 0 ° C. on a 2 mm V notch test piece with the notch position being the center of the weld metal. In addition, welding workability was evaluated during welding. Table 2 also shows the test results. In the symbols of welding workability in Table 2, ◎ indicates that the welding material is superior to the existing welding material, ○ indicates that the welding material is equivalent to the existing welding material, Δ indicates that the welding material is slightly inferior, and × Indicates worse than existing welding consumables.
【００２０】[0020]
【表１】 [Table 1]
【００２１】[0021]
【表２】 [Table 2]
【００２２】[0022]
【表３】 [Table 3]
【００２３】ワイヤＴ１〜Ｔ９はいずれも本発明の要件
を満たしており、溶接金属はベイナイト単相組織となっ
た。溶接作業性は既存の溶接材料と同等以上であり、試
験結果より、後熱処理後のクリープ破断特性は近年開発
された高強度フェライト鋼の強度をも越えている。ま
た、衝撃特性についても、吸収エネルギーで１５０Ｊ以
上と高強度と靱性を兼ね備えた溶接材料であることが確
認された。The wires T1 to T9 all satisfied the requirements of the present invention, and the weld metal had a bainite single phase structure. The welding workability is equal to or higher than that of the existing welding materials, and the test results show that the creep rupture characteristics after post-heat treatment exceed the strength of the recently developed high-strength ferritic steel. Further, it was confirmed that the welding material had high strength and toughness with an absorbed energy of 150 J or more in terms of impact characteristics.
【００２４】ワイヤＴ１０〜Ｔ１９は比較例を示す。ワ
イヤＴ１０は通常の耐熱鋼用として使用されている２．
２５Ｃｒ−１Ｍｏ系ワイヤの例であり、Ｔ１１は９Ｃｒ
−１Ｍｏ−Ｖ−Ｎｂ系ワイヤの例である。Ｔ１２〜Ｔ１
９はワイヤの成分を本発明範囲外としたものである。Wires T10 to T19 show a comparative example. 1. Wire T10 is used for ordinary heat-resistant steel.
This is an example of a 25Cr-1Mo-based wire, and T11 is 9Cr.
It is an example of a -1Mo-V-Nb-based wire. T12-T1
Reference numeral 9 designates a component of the wire outside the scope of the present invention.
【００２５】Ｔ１０の衝撃特性は他の比較例よりは良好
であるが、本発明ワイヤに比べ衝撃特性、クリープ破断
特性とも著しく劣っている。Ｔ１１はクリープ破断特性
は他の比較例よりは良好であるが衝撃特性が悪く溶接作
業性がＴ１０に比べ劣っていた。Although the impact characteristics of T10 are better than those of the other comparative examples, both the impact characteristics and the creep rupture characteristics of the wire of the present invention are remarkably inferior. T11 had better creep rupture properties than the other comparative examples, but had poor impact properties and was inferior in welding workability to T10.
【００２６】Ｔ１２はＴ１０にＷを添加したものである
が、ＮｂやＲｅ元素を含有しないため、Ｔ１０よりクリ
ープ破断特性はわずかに改善されたのみである。Ｔ１３
はＮｉの添加量を本発明ワイヤのＮｉ量の上限より多く
したものであるが、Ｔ１１を除く他の比較例よりは衝撃
特性は改善されるものの、他の比較例よりもクリープ破
断特性は劣化している。Ｔ１４はＭｏ量が本発明ワイヤ
のＭｏ量の上限を越えたものであって、溶接金属の硬さ
が著しく硬化し、吸収エネルギーが著しく低く、衝撃特
性はとうてい本発明ワイヤのそれに対して著しく悪い。
Ｔ１５はＮ量が本発明ワイヤのＮ量の上限を越えるもの
であって、溶接金属にブローホールが発生するとともに
衝撃特性に乏しい。Ｔ１６は本発明ワイヤのＣ量より低
いもので、溶接作業性は良好であったが、溶接金属の組
織がフェライトとベイナイトの二相組織となり、クリー
プ破断特性が本発明のそれに比し悪い。また、衝撃特性
もＴ１０より劣っている。T12 is obtained by adding W to T10, but since it does not contain Nb or Re element, the creep rupture characteristic is only slightly improved as compared with T10. T13
Indicates that the amount of Ni added is larger than the upper limit of the amount of Ni of the wire of the present invention. However, although the impact characteristics are improved as compared with the other comparative examples except T11, the creep rupture characteristics are deteriorated as compared with the other comparative examples. doing. In T14, the Mo content exceeds the upper limit of the Mo content of the wire of the present invention, and the hardness of the weld metal is remarkably hardened, the absorbed energy is extremely low, and the impact properties are extremely remarkably worse than those of the wire of the present invention. .
T15 is one in which the N content exceeds the upper limit of the N content of the wire of the present invention, and a blow hole is generated in the weld metal and the impact characteristics are poor. T16 was lower than the C content of the wire of the present invention, and the welding workability was good, but the structure of the weld metal was a two-phase structure of ferrite and bainite, and the creep rupture characteristics were inferior to those of the present invention. Also, the impact characteristics are inferior to T10.
【００２７】Ｔ１７はＭｏ，Ｗ，Ｖ，ＮｂおよびＲｅな
ど、クリープ破断特性を改善する元素が添加されている
が、Ｃｒ量が本発明ワイヤのＣｒ量の上限を越えてお
り、溶接金属中にフェライトが生成し衝撃特性が悪い。
また、溶接作業性もＴ１１と同様に悪いものであった。
Ｔ１８はＲｅを本発明ワイヤのＲｅ量の上限を越えて、
大量に添加したものである。クリープ破断特性は改善さ
れているが、溶接作業性が悪く、衝撃特性も低い。Ｔ１
９はＣ量が本発明ワイヤのＣ量の上限を越えて添加され
ており、溶接時に割れが発生した。溶接金属も著しく硬
化し、衝撃特性も劣っている。T17 contains elements that improve creep rupture characteristics, such as Mo, W, V, Nb, and Re, but the amount of Cr exceeds the upper limit of the amount of Cr in the wire of the present invention. Ferrite is formed and impact characteristics are poor.
Also, the welding workability was as bad as T11.
T18 exceeds the upper limit of the amount of Re of the wire of the present invention,
It was added in large quantities. Although creep rupture properties are improved, welding workability is poor and impact properties are low. T1
In No. 9, the C content was added exceeding the upper limit of the C content of the wire of the present invention, and cracks occurred during welding. The weld metal also hardens significantly and has poor impact properties.
【００２８】[0028]
【発明の効果】本発明溶接材料は従来の２．２５Ｃｒ−
１Ｍｏ系および９〜１２Ｃｒ鋼用溶接ワイヤと比較し
て、高温でのクリープ強度を著しく高めたものであり、
靱性および作業性などの特性にも優れている。各種発電
用ボイラ、化学圧力容器などに使用される低Ｃｒフェラ
イト系耐熱鋼を溶接する際に本発明の溶接材料を使用す
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 is a conventional 2.25Cr-
In comparison with 1Mo-based and 9-12Cr steel welding wires, the creep strength at high temperatures is significantly increased,
Excellent properties such as toughness and workability. By using the welding material of the present invention when welding low Cr ferritic heat-resistant steel used for various power generation boilers, chemical pressure vessels, and the like, the reliability of the welded joint can be significantly improved.
【図１】本発明の溶接材料を用いて溶接する際の開先形
状を示す図。FIG. 1 is a view showing a groove shape when welding is performed using the welding material of the present invention.
Claims (1)
Ｓｉ：０．１〜０．７％、Ｍｎ：０．１〜１％、Ｐ：
０．００２〜０．０２５％、Ｓ：０．００１〜０．０１
５％、Ｃｒ：０．８〜３％、Ｎｉ：０．０１〜１％、Ｍ
ｏ：０．１〜３％、Ｖ：０．０１〜０．５％、Ｗ：０．
１〜３％、Ｎｂ：０．０１〜０．２％、Ｒｅ：０．１〜
１．５％、Ａｌ：０．００３〜０．０５％、Ｂ：０．０
００１〜０．０１％、Ｎ：０．００３〜０．０３％を含
み残部は鉄および不可避的不純物からなる高温強度と靱
性に優れたことを特徴とするフェライト系耐熱鋼用溶接
材料。C .: 0.03 to 0.12% by weight,
Si: 0.1 to 0.7%, Mn: 0.1 to 1%, P:
0.002 to 0.025%, S: 0.001 to 0.01
5%, Cr: 0.8-3%, Ni: 0.01-1%, M
o: 0.1-3%, V: 0.01-0.5%, W: 0.
1 to 3%, Nb: 0.01 to 0.2%, Re: 0.1 to
1.5%, Al: 0.003 to 0.05%, B: 0.0
A welding material for heat-resistant ferritic steel, comprising 001 to 0.01%, N: 0.003 to 0.03%, and the balance being iron and unavoidable impurities and having excellent high-temperature strength and toughness.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP15931496A JP3367824B2 (en) | 1996-06-20 | 1996-06-20 | Welding material for heat resistant ferritic steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP15931496A JP3367824B2 (en) | 1996-06-20 | 1996-06-20 | Welding material for heat resistant ferritic steel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH106079A true JPH106079A (en) | 1998-01-13 |
| JP3367824B2 JP3367824B2 (en) | 2003-01-20 |
Family
ID=15691096
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP15931496A Expired - Fee Related JP3367824B2 (en) | 1996-06-20 | 1996-06-20 | Welding material for heat resistant ferritic steel |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3367824B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB2383336A (en) * | 2001-12-21 | 2003-06-25 | Alstom | Rotor and method for welding an element of a rotor |
| WO2013191208A1 (en) * | 2012-06-22 | 2013-12-27 | 新日鐵住金株式会社 | Duplex stainless steel |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP3426880B2 (en) | 1996-11-28 | 2003-07-14 | 三菱重工業株式会社 | Welding material for high strength ferritic heat resistant steel |
-
1996
- 1996-06-20 JP JP15931496A patent/JP3367824B2/en not_active Expired - Fee Related
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB2383336A (en) * | 2001-12-21 | 2003-06-25 | Alstom | Rotor and method for welding an element of a rotor |
| US6713722B2 (en) | 2001-12-21 | 2004-03-30 | Alstom Technology Ltd | Rotor and method for welding an element of a rotor |
| GB2383336B (en) * | 2001-12-21 | 2005-08-31 | Alstom | Rotor and method for welding an element of a rotor |
| WO2013191208A1 (en) * | 2012-06-22 | 2013-12-27 | 新日鐵住金株式会社 | Duplex stainless steel |
| JP5403192B1 (en) * | 2012-06-22 | 2014-01-29 | 新日鐵住金株式会社 | Duplex stainless steel |
| US10202675B2 (en) | 2012-06-22 | 2019-02-12 | Nippon Steel & Sumitomo Metal Corporation | Duplex stainless steel |
Also Published As
| Publication number | Publication date |
|---|---|
| JP3367824B2 (en) | 2003-01-20 |
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