JPH0577086A - Flux cored wire for gas shielded arc welding for 0.5 mo steel, mn-mo steel and mn-mo-ni steel - Google Patents
Flux cored wire for gas shielded arc welding for 0.5 mo steel, mn-mo steel and mn-mo-ni steelInfo
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- JPH0577086A JPH0577086A JP3268815A JP26881591A JPH0577086A JP H0577086 A JPH0577086 A JP H0577086A JP 3268815 A JP3268815 A JP 3268815A JP 26881591 A JP26881591 A JP 26881591A JP H0577086 A JPH0577086 A JP H0577086A
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- steel
- added
- toughness
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、フラックス入りワイヤ
の優れた特徴を活かした０.５Ｍo鋼用、Ｍn−Ｍo鋼用及
びＭn−Ｍo−Ｎi鋼用ガスシールドアーク溶接用フラッ
クス入りワイヤに係り、より詳細には、長時間の溶接後
熱処理(以下、「ＰＷＨＴ」と称する)を行ってもフェラ
イト粒の粗大化やフェライトバンドの発生の程度が小さ
く、優れた機械的性能を示す溶接金属を得ることのでき
る０.５Ｍo鋼用、Ｍn−Ｍo鋼用及びＭn−Ｍo−Ｎi鋼用
ガスシールドアーク溶接用フラックス入りワイヤに関す
るものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a flux-cored wire for gas shielded arc welding for 0.5Mo steel, Mn-Mo steel and Mn-Mo-Ni steel, which takes advantage of the excellent features of the flux-cored wire. , To be more precise, even after performing a long-time post-weld heat treatment (hereinafter referred to as "PWHT"), the degree of coarsening of ferrite grains and the occurrence of ferrite bands is small, and a weld metal exhibiting excellent mechanical performance is obtained. The present invention relates to a flux-cored wire for gas shield arc welding for 0.5 Mo steel, Mn-Mo steel and Mn-Mo-Ni steel, which can be obtained.
【０００２】[0002]
【従来の技術及び発明が解決しようとする課題】ガスシ
ールドアーク溶接ワイヤは、被覆アーク溶接棒に比較し
て、高能率で溶接でき、経済性も良く、低合金鋼の溶接
においても、その採用の割合が益々増加してきている。2. Description of the Related Art Gas shielded arc welding wires can be welded with high efficiency and are economical as compared with coated arc welding rods, and are also used for welding low alloy steels. The ratio of is increasing more and more.
【０００３】ガスシールドアーク溶接用ワイヤには、ソ
リッドワイヤとフラックス入りワイヤがあるが、フラッ
クス入りワイヤは、ソリッドワイヤに比較して溶接作業
性に優れ、スラグがビード表面を覆うことによりビード
形状及び外観が良好であるという長所がある。しかしな
がら、低合金である０.５Ｍo鋼や、更に強度・靭性を考
慮したＭn−Ｍo鋼及びＭn−Ｍo−Ｎi鋼は、化学工業、
火力発電及び原子力発電プラント等で使用されている
が、これらの鋼種に対するフラックス入りワイヤは未だ
十分な検討がなされていなかった。The gas shielded arc welding wire includes a solid wire and a flux-cored wire. The flux-cored wire is superior to the solid wire in welding workability, and the bead shape and the bead shape are formed by the slag covering the bead surface. It has the advantage of good appearance. However, the low alloy 0.5Mo steel, and Mn-Mo steel and Mn-Mo-Ni steel in consideration of strength and toughness, are used in the chemical industry,
Although used in thermal power plants and nuclear power plants, flux-cored wires for these steel types have not yet been sufficiently studied.
【０００４】また、一般に低合金鋼用溶接材料による溶
接金属は、長時間のＰＷＨＴによりフェライト粒の粗大
化やフェライトバンドの発生が生じ、機械的性能が劣化
することが指摘されている。そのため、長時間のＰＷＨ
Ｔを行っても安定した溶接金属組織及び優れた機械的性
能が得られる０.５Ｍo鋼用、Ｍn−Ｍo鋼用及びＭn−Ｍo
−Ｎi鋼用フラックス入りワイヤが切望されていた。It has been pointed out that generally, in a weld metal made of a welding material for a low alloy steel, PWHT for a long time causes coarsening of ferrite grains and generation of ferrite bands, resulting in deterioration of mechanical performance. Therefore, PWH for a long time
Stable weld metal structure and excellent mechanical performance can be obtained even if T is performed. For 0.5Mo steel, Mn-Mo steel and Mn-Mo steel.
-A flux-cored wire for Ni steel has been earnestly desired.
【０００５】本発明は、上記の事情に鑑みてなされたも
のであって、その目的とするところは、長時間のＰＷＨ
Ｔを行っても溶接金属中のフェライト粒の粗大化やフェ
ライトバンドの発生の程度が小さく、優れた機械的性能
の溶接金属を得ることのできる０.５Ｍo鋼用、Ｍn−Ｍo
鋼用及びＭn−Ｍo−Ｎi鋼用ガスシールドアーク溶接用
フラックス入りワイヤを提供することにある。The present invention has been made in view of the above circumstances, and its purpose is to provide a PWH for a long time.
Even if T is performed, the degree of coarsening of ferrite grains in the weld metal and the occurrence of ferrite bands are small, and a weld metal with excellent mechanical performance can be obtained. For 0.5 Mo steel, Mn-Mo
A flux-cored wire for gas shielded arc welding for steel and Mn-Mo-Ni steel.
【０００６】[0006]
【課題を解決するための手段】本発明者は、前記課題を
解決するため鋭意研究を重ねた結果、フラックス入りワ
イヤに添加する成分組成並びにフラックスの成分組成等
を規制することにより可能であることを見い出し、ここ
に本発明を完成したものである。Means for Solving the Problems As a result of intensive studies to solve the above problems, the present inventor can achieve this by controlling the component composition added to the flux-cored wire and the component composition of the flux. The present invention has been completed and the present invention has been completed here.
【０００７】すなわち、本発明に係る０.５Ｍo鋼用、Ｍ
n−Ｍo鋼用及びＭn−Ｍo−Ｎi鋼用ガスシールドアーク
溶接用フラックス入りワイヤは、ワイヤ全重量に対する
重量％で、金属外皮又はフラックスのいずれか一方或い
は両方に、Ｃ:０.０１〜０.３％、Ｓi:０.０１〜１.５
％、Ｍn:０.８〜８.５％、Ｍo:０.２〜１.５％、Ｎb:
０.００５〜０.０５％及びＶ:０.００５〜０.０５％が
添加されており、一方、フラックスにはＴiＯ2:１.８〜
７.５％、１５％未満の鉄粉を含み、残部がアーク安定
剤を含めたスラグ生成剤である該フラックスを充填率
(ワイヤ全重量に対する重量比)が１０〜２５％となるよ
うに金属外皮内に充填してなることを特徴とするもので
ある。That is, for 0.5 Mo steel according to the present invention, M
The flux-cored wire for gas shielded arc welding for n-Mo steel and Mn-Mo-Ni steel is C: 0.01 to 0 in either or both of the metal shell and the flux, in% by weight based on the total weight of the wire. 0.3%, Si: 0.01 to 1.5
%, Mn: 0.8 to 8.5%, Mo: 0.2 to 1.5%, Nb:
0.005 to 0.05% and V: 0.005 to 0.05% are added, while the flux TiO 2: 1.8 to
The filling rate of the flux is 7.5%, less than 15% of iron powder, and the balance is a slag-forming agent including an arc stabilizer.
It is characterized in that the metal outer shell is filled so that the (weight ratio to the total weight of the wire) is 10 to 25%.
【０００８】また、他の本発明は、更に、金属外皮又は
フラックスのいずれか一方或いは両方に、Ｎi:０.１〜
３％及びＣr:１％未満の１種又は２種が添加されている
ことを特徴とするものである。Another aspect of the present invention is that, in either or both of the metal shell and the flux, Ni: 0.1 to 0.1.
One or two of 3% and Cr: less than 1% are added.
【０００９】更に他の本発明は、更に金属外皮及びフラ
ックス中に含まれる全Ｎ量が０.０１５％以下であるこ
とを特徴とするものである。Still another feature of the present invention is that the total amount of N contained in the metal shell and the flux is 0.015% or less.
【００１０】更に他の本発明は、金属外皮又はフラック
スのいずれか一方或いは両方に、更にＴi:０.０５〜０.
３％及びＢ:０.００５〜０.０１５％のうちの少なくと
も１種以上が添加されていることを特徴とするものであ
る。In still another aspect of the present invention, either or both of the metal shell and the flux, and Ti: 0.05 to 0.5.
3% and B: 0.005 to 0.015%, at least one or more kinds are added.
【００１１】以下に本発明を更に詳述する。The present invention will be described in more detail below.
【００１２】本発明は、上述のように、金属外皮又はフ
ラックスのいずれか一方或いは両方に、各種成分を添加
すると共に、フラックスに所定の成分を添加した０.５
Ｍo鋼用、Ｍn−Ｍo鋼用及びＭn−Ｍo−Ｎi鋼用ガスシー
ルドアーク溶接用フラックス入りワイヤである。以下に
添加成分の作用並びに成分量の限定理由について説明す
る。According to the present invention, as described above, various components are added to either or both of the metal shell and the flux, and a predetermined component is added to the flux to 0.5.
A flux cored wire for gas shield arc welding for Mo steel, Mn-Mo steel and Mn-Mo-Ni steel. The effects of the added components and the reasons for limiting the amounts of the components will be described below.
【００１３】（Ｃ：０.０１〜０.３％）Ｃは溶接金属の
強度及び靭性の調整の目的で金属外皮又はフラックスの
いずれか一方或いは両方に添加する。しかし、０.０１
％未満では十分な強度及び靭性が得られない。また、
０.３％を超えると溶接金属の靭性の低下が大きくな
り、耐割れ性も低下する。したがって、添加するＣ量は
０.０１〜０.３％の範囲とする。(C: 0.01 to 0.3%) C is added to either or both of the metal shell and the flux for the purpose of adjusting the strength and toughness of the weld metal. But 0.01
If it is less than%, sufficient strength and toughness cannot be obtained. Also,
If it exceeds 0.3%, the toughness of the weld metal is greatly reduced and the crack resistance is also reduced. Therefore, the amount of C to be added is in the range of 0.01 to 0.3%.
【００１４】（Ｓi：０.０１〜１.５％、Ｍn：０.８〜
８.５％）Ｓi、Ｍnはいずれも溶接金属の脱酸及び強度・
靭性の調整のために金属外皮又はフラックスのいずれか
一方或いは両方に添加する。しかし、Ｓiが０.０１％未
満、Ｍnが０.８％未満では十分な添加効果がない。ま
た、Ｓiが１.５％を超え、Ｍnが８.５％を超えると溶接
金属の靭性が低下する。したがって、添加するＳi量は
０.０１〜１.５％、Ｍn量は０.８〜８.５％の範囲とす
る。(Si: 0.01 to 1.5%, Mn: 0.8 to
8.5%) Si and Mn are both deoxidizing and strength of weld metal
It is added to either or both of the metal shell and the flux for adjusting the toughness. However, if Si is less than 0.01% and Mn is less than 0.8%, there is no sufficient effect of addition. If Si exceeds 1.5% and Mn exceeds 8.5%, the toughness of the weld metal decreases. Therefore, the amount of Si to be added is in the range of 0.01 to 1.5% and the amount of Mn is in the range of 0.8 to 8.5%.
【００１５】（Ｍo：０.２〜１.５％）Ｍoは溶接金属の
耐食性の改善及び強度・靭性の調整のために金属外皮又
はフラックスのいずれか一方或いは両方に添加する。し
かし、０.２％未満では十分な強度が得られない。ま
た、１.５％を超えると靭性の低下が大きくなる。した
がって、添加するＭo量は０.２〜１.５％の範囲とす
る。(Mo: 0.2-1.5%) Mo is added to either or both of the metal shell and the flux in order to improve the corrosion resistance of the weld metal and adjust the strength and toughness. However, if it is less than 0.2%, sufficient strength cannot be obtained. On the other hand, if it exceeds 1.5%, the toughness is greatly reduced. Therefore, the amount of Mo to be added is in the range of 0.2 to 1.5%.
【００１６】（Ｎb：０.００５〜０.０５％、Ｖ：０.０
０５〜０.０５％）Ｎb及びＶは強い炭化物形成元素であ
り、適量の添加でビードとビードの境界付近の炭素を固
定してフェライト粒の粗大化及びフェライトバンドの発
生を低く抑えることができる。しかし、Ｎb、Ｖがそれ
ぞれ０.００５％未満では十分な効果が得られない。ま
た、Ｎb、Ｖがそれぞれ０.０５％を超えると、強度が高
くなり、靭性が低下する。したがって、金属外皮又はフ
ラックスのいずれか一方或いは両方に添加するＮb量は
０.００５〜０.０５％、またＶ量は０.００５〜０.０５
％の範囲とする。なお、Ｎb及びＶをフラックスから添
加する場合には、金属単体、合金及び酸化物のいずれの
形態でも可能である。(Nb: 0.005-0.05%, V: 0.0
(05-0.05%) Nb and V are strong carbide forming elements, and by adding an appropriate amount of carbon, it is possible to fix carbon in the vicinity of the boundary between beads and suppress the coarsening of ferrite grains and the occurrence of ferrite bands. .. However, if Nb and V are each less than 0.005%, a sufficient effect cannot be obtained. When Nb and V exceed 0.05%, the strength is increased and the toughness is reduced. Therefore, the amount of Nb added to either or both of the metal shell and the flux is 0.005 to 0.05%, and the amount of V is 0.005 to 0.05.
The range is%. When Nb and V are added from the flux, any form of a simple metal, an alloy and an oxide can be used.
【００１７】以上の成分が金属外皮又はフラックスのい
ずれか一方或いは両方に添加する必須の成分であるが、
以下のＮi及びＣrの１種又は２種、或いはＴi及びＢの
１種又は２種を必要に応じて添加することができる。ま
た、必要に応じてＮ量を規制するのが好ましい。The above components are essential components to be added to either or both of the metal shell and the flux.
One or two of the following Ni and Cr, or one or two of Ti and B can be added as required. Moreover, it is preferable to regulate the amount of N as needed.
【００１８】（Ｎi：０.１〜３.０％）Ｎiを０.１〜３.
０％の範囲で金属外皮又はフラックスのいずれか一方或
いは両方に添加すると、溶接金属のマトリックスが強化
され、靭性が向上する。しかし、０.１％未満では効果
がなく、また３.０％を超えると強度が高くなり、靭性
が低下すると共に、耐高温割れや耐脆化特性も劣化す
る。(Ni: 0.1 to 3.0%) Ni is 0.1 to 3.
When added to either or both of the metal shell and the flux in the range of 0%, the matrix of the weld metal is strengthened and the toughness is improved. However, if it is less than 0.1%, there is no effect, and if it exceeds 3.0%, the strength becomes high, the toughness decreases, and the hot crack resistance and embrittlement resistance also deteriorate.
【００１８】（Ｃr：１％未満）Ｃrを１％未満の範囲で
金属外皮又はフラックスのいずれか一方或いは両方に添
加すると、溶接金属の耐食性の改善及び強度・靭性の調
整を行うことができる。しかし、１％以上添加すると、
溶接金属の強度が大きくなり靭性が低下する。(Cr: less than 1%) When Cr is added to either one or both of the metal shell and the flux in the range of less than 1%, the corrosion resistance of the weld metal and the strength / toughness can be adjusted. However, if 1% or more is added,
The strength of the weld metal increases and the toughness decreases.
【００１９】（Ｎ：０.０１５％以下）金属外皮及びフ
ラックス中に含まれる全Ｎ量を０.０１５％以下にする
と、靭性が飛躍的に向上することが判明した。しかし、
全Ｎ量が０.０１５％を超えると靭性が低下し始め、溶
接金属中にブローホール等の欠陥が多数発生し、機械的
性能が極端に悪くなるので好ましくない。(N: 0.015% or less) It has been found that the toughness is remarkably improved when the total amount of N contained in the metal shell and the flux is set to 0.015% or less. But,
If the total N content exceeds 0.015%, the toughness starts to decrease, a large number of defects such as blowholes occur in the weld metal, and the mechanical performance becomes extremely poor, which is not preferable.
【００２０】（Ｔi：０.０５〜０.３％）Ｔiはアークの
安定化及び溶接金属の靭性向上のために金属外皮又はフ
ラックスのいずれか一方或いは両方に添加することがで
きる。添加する場合、０.０５％未満では十分な効果が
得られず、また０.３％を超えて添加すると強度が高く
なり、靭性が低下する。したがって、添加するＴi量は
０.０５〜０.３％の範囲とする。なお、Ｔiをフラック
スから添加する場合には、金属単体やＦe−Ｔi合金等の
ＴiＯ2以外の形態で添加する。(Ti: 0.05 to 0.3%) Ti can be added to either or both of the metal shell and the flux for stabilizing the arc and improving the toughness of the weld metal. When it is added, if it is less than 0.05%, a sufficient effect cannot be obtained, and if it exceeds 0.3%, the strength is increased and the toughness is lowered. Therefore, the amount of Ti to be added is in the range of 0.05 to 0.3%. In the case of adding Ti from the flux is added in TiO 2 other forms such as simple metal or Fe-Ti alloy.
【００２１】（Ｂ：０.００５〜０.０１５％）Ｂは溶接
金属の靭性向上のために金属外皮又はフラックスのいず
れか一方或いは両方に添加することができる。添加する
場合、０.００５％未満では十分な効果がなく、また０.
０１５％を超えると強度が高くなり靭性が低下する。し
たがって、添加するＢ量は０.００５〜０.０１５％の範
囲とする。なお、Ｂをフラックスから添加する場合に
は、金属単体、合金及び酸化物のいずれの形態でも可能
である。(B: 0.005 to 0.015%) B can be added to either or both of the metal shell and the flux in order to improve the toughness of the weld metal. When it is added, if it is less than 0.005%, there is no sufficient effect, and if it is 0.005%.
If it exceeds 015%, the strength is increased and the toughness is reduced. Therefore, the amount of B to be added is in the range of 0.005 to 0.015%. When B is added from the flux, any form of a simple metal, an alloy and an oxide can be used.
【００２２】更に、フラックスには以下の成分を必須成
分として添加する。Further, the following components are added to the flux as essential components.
【００２３】（ＴiＯ2：１.８〜７.５％）ＴiＯ2はスラ
グ形成剤及びアーク安定剤としてフラックスに添加す
る。しかし、１.８％未満ではスラグの被包性が悪く、
溶接作業性が実用に耐えない。また、７.５％を超える
とスラグの粘性が極端に大きくなり、スラグの巻き込み
等の問題が生じる。したがって、フラックス中のＴiＯ2
量は１.８〜７.５％の範囲とする。(TiO 2 : 1.8 to 7.5%) TiO 2 is added to the flux as a slag former and an arc stabilizer. However, if it is less than 1.8%, the encapsulation of slag is poor,
Welding workability is not practical. Further, if it exceeds 7.5%, the viscosity of the slag becomes extremely large, which causes a problem such as slag entrapment. Therefore, the TiO 2 in the flux
The amount should be in the range of 1.8 to 7.5%.
【００２４】（１５％未満の鉄粉及びスラグ生成剤(ア
ーク安定剤含む)）フラックスには、上記成分のほか、
１５％未満の鉄粉及びアーク安定剤を含めたスラグ生成
剤を添加する。鉄粉はアークの安定化と溶接効率向上の
ために添加するものであり、１５％以上添加すると他の
合金成分が不足するので１５％以下が望ましい。また、
フラックスの残部に添加するアーク安定剤を含めたスラ
グ生成剤としては種々のものが可能であり、ＺrＯ2、Ｓ
iＯ2、鉄酸化物(ＦeＯ、Ｆe2Ｏ3等)のほか、Ｍg、Ｍg
Ｏ、Ａl−Ｍg合金、Ａl2Ｏ3、Ｋ2Ｏ、Ｎa2Ｏ、ＭnＯ2、
ＣaＦ2、ＮaＦ等々が挙げられ、適宜選択して添加され
る。(Flux of less than 15% and slag generator (including arc stabilizer)) The flux contains
Add slag generator including less than 15% iron powder and arc stabilizer. Iron powder is added to stabilize the arc and improve welding efficiency. If 15% or more is added, other alloy components become insufficient, so 15% or less is desirable. Also,
Various slag-forming agents including an arc stabilizer added to the balance of the flux can be used. ZrO 2 , S
In addition to iO 2 and iron oxides (FeO, Fe 2 O 3 etc.), Mg, Mg
O, Al-Mg alloy, Al 2 O 3, K 2 O, Na 2 O, MnO 2,
CaF 2 , NaF and the like are mentioned, and they are appropriately selected and added.
【００２５】（フラックス充填率：１０〜２５％）上記
成分組成のフラックスは、ワイヤ全重量に対する重量比
が１０〜２５％となるように金属外皮内に充填する。１
０％未満ではスラグ生成剤の量が不十分であり、スラグ
の被包性が悪く、ビード外観が不良となり、また２５％
を超えるとワイヤの成形時や伸線時に断線し易くなるの
で好ましくない。(Flux filling rate: 10 to 25%) The flux having the above-mentioned component composition is filled in the metal shell so that the weight ratio with respect to the total weight of the wire is 10 to 25%. 1
If it is less than 0%, the amount of the slag-forming agent is insufficient, the slag encapsulation is poor, the bead appearance is poor, and the content is 25%.
If it exceeds the range, the wire is likely to be broken at the time of forming or drawing the wire, which is not preferable.
【００２６】なお、シールドガスとしては、ＣＯ2を初
めとし、ＡrとＣＯ2の混合ガス、更にＯ2を添加した混
合ガス等々、いずれの組成でも使用可能である。また、
金属外皮は軟鋼及び合金鋼のいずれも使用できるのは勿
論のことであり、その断面形状は特に規定されず、合わ
せ目があってもなくても何れでもよい。被溶接材は、い
わゆる０.５Ｍo鋼、Ｍn−Ｍo鋼、Ｍn−Ｍo−Ｎi鋼に属
する鋼種であることは云うまでもない。[0026] As the shielding gas, the CO 2 and the beginning, a mixed gas of Ar and CO 2, the gas mixture so that further addition of O 2, it can be used in any composition. Also,
As a matter of course, both a mild steel and an alloy steel can be used for the metal skin, and the cross-sectional shape thereof is not particularly limited, and it may be either with or without seams. Needless to say, the material to be welded belongs to the so-called 0.5 Mo steel, Mn-Mo steel, and Mn-Mo-Ni steel.
【００２７】次に本発明の実施例を示す。Next, examples of the present invention will be described.
【００２８】[0028]
【表１】 、[Table 1] ,
【表２】 及び[Table 2] as well as
【表３】 に示す１.２mmφのフラックス入りワイヤを製作し、軟
鋼板にそれぞれのワイヤで２層バタリングした図１に示
す開先形状、[Table 3] The 1.2 mmφ flux-cored wire shown in Fig. 1 was manufactured, and the groove shape shown in Fig. 1 was obtained by buttering two layers of each wire on a mild steel plate,
【表４】 に示す溶接条件で試験板を作成した後、各種のＰＷＨＴ
を施した。本発明の範囲内のワイヤ(本発明例)はＮo.
８、Ｎo.９、Ｎo.１２、Ｎo.１３、Ｎo.１６、Ｎo.１
７、Ｎo.１９、Ｎo.２１、Ｎo.２２、Ｎo.２５及びＮo.
２６である。[Table 4] After creating a test plate under the welding conditions shown in, various PWHT
Was applied. Wires within the scope of the present invention (examples of the present invention) are No.
8, No. 9, No. 12, No. 13, No. 16, No. 1
7, No. 19, No. 21, No. 22, No. 25 and No.
26.
【００２９】その後、試験板の板厚中央からＪＩＳ Ｚ
３１１１ Ａ１号引張試験片と、ＪＩＳ Ｚ３１１１ ４
号シャルピー衝撃試験片(２mmＶノッチ)を採取し、機械
試験を行った。その結果、得られた溶接金属の化学成分
(Then, from the center of the thickness of the test plate to JIS Z
3111 A1 tensile test piece and JIS Z3111 4
A Charpy impact test piece (2 mm V notch) was sampled and subjected to a mechanical test. As a result, the chemical composition of the obtained weld metal
(
【表５】 及び[Table 5] as well as
【表６】 )、作業性及び機械的性能([Table 6] ), Workability and mechanical performance (
【表７】 )から、次のように考察できる。[Table 7] ), The following can be considered.
【００３０】比較例Ｎo.１及びＮo.２:Ｎo.１及びＮo.
２は溶接作業性を左右するＴiＯ2量の成分範囲を調整す
るために試作したワイヤである。Ｎo.１はＴiＯ2量が
１.８％未満であり、スラグの被包性が悪いため、溶接
作業性やビード外観が悪かった。Ｎo.２はＴiＯ2量が
７.５％を超えるものであり、スラグの粘性が極端に大
きく、ビード外観が悪くなり、またスラグの巻き込み等
も生じた。なお、溶接金属の化学分析及び機械試験は行
っていない。Comparative Examples No. 1 and No. 2: No. 1 and No.
Reference numeral 2 is a wire trial-produced for adjusting the composition range of the amount of TiO 2 that affects the welding workability. In No. 1, the amount of TiO 2 was less than 1.8% and the slag encapsulation was poor, so the welding workability and bead appearance were poor. In No. 2, the amount of TiO 2 was more than 7.5%, the viscosity of the slag was extremely large, the bead appearance was deteriorated, and slag entrainment occurred. No chemical analysis or mechanical test was performed on the weld metal.
【００３１】比較例Ｎo.３及びＮo.４:Ｎo.３はＣ量が
０.０１％未満のため、焼入れ性が悪く、強度及び靭性
とも十分な結果が得られない。Ｎo.４はＣ量が０.３％
を超えるため、強度が大きくなり、靭性が悪い。Comparative Examples No. 3 and No. 4: No. 3 had a C content of less than 0.01%, and therefore had poor hardenability and could not provide sufficient strength and toughness results. No. 4 has a C content of 0.3%
Therefore, the strength is increased and the toughness is poor.
【００３２】比較例Ｎo.５及びＮo.６:Ｎo.５はＳi及び
Ｍn量がそれぞれ０.０１％及び０.８％未満であり、十
分な脱酸効果がなく、靭性が悪い。Ｎo.６はＳi及びＭn
量がそれぞれ１.５％及び８.５％を超えるため、強度が
高くなり、靭性が悪い。Comparative Examples No. 5 and No. 6: No. 5 had Si and Mn contents of less than 0.01% and 0.8%, respectively, and had no sufficient deoxidizing effect and poor toughness. No. 6 is Si and Mn
Since the amounts exceed 1.5% and 8.5%, respectively, the strength is high and the toughness is poor.
【００３３】比較例Ｎo.７、本発明例Ｎo.８及びＮo.
９、比較例Ｎo.１０:Ｎo.７はＭo量が０.２％未満であ
り、強度及び靭性とも十分でない。Ｎo.８及びＮo.９は
Ｍo量が本発明範囲内のため強度及び靭性とも良好であ
る。Ｎo.１０はＭo量が１.５％を超えるため、強度が高
くなり、靭性が悪い。Comparative Example No. 7, Invention Examples No. 8 and No.
9, Comparative Example No. 10: No. 7 had a Mo content of less than 0.2%, and the strength and toughness were not sufficient. Since No. 8 and No. 9 have the Mo amount within the range of the present invention, both strength and toughness are good. Since No. 10 has a Mo content of more than 1.5%, it has high strength and poor toughness.
【００３４】比較例Ｎo.１１、本発明例Ｎo.１２及びＮ
o.１３、比較例Ｎo.１４:Ｎo.１１はＮb及びＶ量がいず
れも０.００５％未満であり、６５０℃×２４hrのＰＷ
ＨＴで既にフェライトバンドが生じている。Ｎo.１２及
びＮo.１３はＮb及びＶ量が本発明範囲内のため、６５
０℃×２４hrのＰＷＨＴでもフェライトバンドは発生し
ていない。また、機械的性能も良好である。Ｎo.１４
は、Ｎb及びＶ量が０.０５％を超えるため、強度が高く
なり、靭性が低下する。したがって、Ｎb及びＶを０.０
０５〜０.０５％で添加すると、フェライトバンドの発
生の程度を低く抑えることができ、溶接金属の機械的性
能も良好であることが確認された。Comparative Example No. 11, Inventive Examples No. 12 and N
No. 13 and Comparative Example No. 14: No. 11 had Nb and V contents of less than 0.005%, respectively, and had a PW of 650 ° C. × 24 hr.
The ferrite band has already formed in HT. Since No. 12 and No. 13 have Nb and V amounts within the range of the present invention, 65
No ferrite band was generated even in PWHT at 0 ° C for 24 hours. Also, the mechanical performance is good. No.14
Since the Nb and V contents exceed 0.05%, the strength is high and the toughness is low. Therefore, Nb and V are set to 0.0
It was confirmed that when added in an amount of 05 to 0.05%, the degree of ferrite band generation can be suppressed to a low level, and the weld metal has good mechanical performance.
【００３５】比較例Ｎo.１５、本発明例Ｎo.１６及びＮ
o.１７、比較例Ｎo.１８:Ｎo.１５〜Ｎo.１８はＮiの靭
性向上への寄与を調査したものである。Ｎo.１５はＮi
量が０.１％未満のため、靭性への寄与は認められな
い。Ｎo.１６及びＮo.１７はＮi量が本発明範囲内であ
り、Ｎo.８やＮo.９と比較するとＮiの添加により靭性
の向上が認められる。Ｎo.１８はＮi量が３.０％を超え
るため、強度が高くなり、靭性が低下する。Comparative Example No. 15, Invention Examples No. 16 and N
O.17 and Comparative Examples No. 18: No. 15 to No. 18 are investigations of contribution of Ni to the improvement of toughness. No.15 is Ni
Since the amount is less than 0.1%, no contribution to the toughness is recognized. No. 16 and No. 17 have a Ni content within the range of the present invention, and an improvement in toughness is recognized by the addition of Ni as compared with No. 8 and No. 9. Since No. 18 has a Ni content of more than 3.0%, the strength is increased and the toughness is reduced.
【００３６】本発明例Ｎo.１９、比較例Ｎo.２０:Ｎo.
１９及びＮo.２０は、Ｎo.１６に対して、Ｃrによる耐
食性の改善と強度・靭性の調整の効果を確認したもので
ある。Ｎo.１９はＣr量が本発明範囲内であり、機械的
性能は良好である。Ｎo.１８はＣr量が１％を超えるた
め、強度が高くなり、靭性が低下する。Inventive Example No. 19, Comparative Example No. 20: No.
No. 19 and No. 20 confirm the effects of improving the corrosion resistance and adjusting the strength and toughness by Cr with respect to No. 16. No. 19 has a Cr content within the range of the present invention and has good mechanical performance. Since the Cr content of No. 18 exceeds 1%, the strength is increased and the toughness is reduced.
【００３７】本発明例Ｎo.２１及びＮo.２２、比較例Ｎ
o.２３:Ｎo.２１は金属外皮及びフラックス中に含まれ
る全Ｎ量がＮo.８の場合よりも少なく、Ｎo.８よりも靭
性は良好である。Ｎo.２２は全Ｎ量が０.０１５％であ
り、靭性は若干低下傾向を示している。Ｎo.２３は全Ｎ
量が０.０２１％であり、溶接金属中に多数のブローホ
ール等の欠陥が観察され、引張試験に際しては伸びがな
く、脆性破断し、靭性も極端に悪い。Inventive Examples No. 21 and No. 22, Comparative Example N
No. 23: No. 21 has less total N content in the metal shell and flux than No. 8 and has better toughness than No. 8. No. 22 has a total N content of 0.015%, and the toughness shows a tendency to slightly decrease. No.23 is all N
The amount was 0.021%, a large number of defects such as blowholes were observed in the weld metal, there was no elongation in the tensile test, brittle fracture, and toughness were extremely poor.
【００３８】比較例Ｎo.２４、本発明例Ｎo.２５及びＮ
o.２６、比較例Ｎo.２７:Ｎo.２４はＴi量が０.０５％
未満及びＢ量が０.００５％未満のため、靭性向上への
寄与は認められない。Ｎo.２５及びＮo.２６はＴi量及
びＢ量が本発明範囲内のため、Ｎo.８に比べ靭性は良好
である。Ｎo.２７はＴi量が０.３％を超え及びＢ量が
０.０１５％を超えるため、強度が高くなり、靭性が低
下する。Comparative Example No. 24, Inventive Examples No. 25 and N
No. 26, Comparative Example No. 27: No. 24 had a Ti content of 0.05%.
And the B content is less than 0.005%, no contribution to the improvement of toughness is recognized. Since No. 25 and No. 26 have Ti amount and B amount within the range of the present invention, the toughness is better than No. 8. In No. 27, the Ti content exceeds 0.3% and the B content exceeds 0.015%, so that the strength is increased and the toughness is reduced.
【００３９】[0039]
【発明の効果】以上詳述したように、本発明の０.５Ｍo
鋼用、Ｍn−Ｍo鋼用及びＭn−Ｍo−Ｎi鋼用ガスシール
ドアーク溶接用フラックス入りワイヤによれば、長時間
の溶接後熱処理を行っても、フェライト粒の粗大化やフ
ェライトバンドの発生の程度が小さく、優れた機械的性
能を示す溶接金属を得ることができる。As described above in detail, 0.5 Mo of the present invention is obtained.
According to the flux-cored wire for steel, Mn-Mo steel, and Mn-Mo-Ni steel for gas shielded arc welding, even if the heat treatment after welding for a long time is performed, coarsening of ferrite grains and generation of ferrite bands occur. It is possible to obtain a weld metal having a small degree and excellent mechanical performance.
【図１】供試鋼板の開先形状を示す断面図である。FIG. 1 is a sectional view showing a groove shape of a test steel plate.
Claims (4)
同じ)、金属外皮又はフラックスのいずれか一方或いは
両方に、Ｃ:０.０１〜０.３％、Ｓi:０.０１〜１.５
％、Ｍn:０.８〜８.５％、Ｍo:０.２〜１.５％、Ｎb:
０.００５〜０.０５％及びＶ:０.００５〜０.０５％が
添加されており、一方、フラックスにはＴiＯ2:１.８〜
７.５％、１５％未満の鉄粉を含み、残部がアーク安定
剤を含めたスラグ生成剤である該フラックスを充填率
(ワイヤ全重量に対する重量比)が１０〜２５％となるよ
うに金属外皮内に充填してなることを特徴とする０.５
Ｍo鋼用、Ｍn−Ｍo鋼用及びＭn−Ｍo−Ｎi鋼用ガスシー
ルドアーク溶接用フラックス入りワイヤ。1. In weight% relative to the total weight of the wire (hereinafter,
The same), either or both of the metal shell and the flux, C: 0.01 to 0.3%, Si: 0.01 to 1.5
%, Mn: 0.8 to 8.5%, Mo: 0.2 to 1.5%, Nb:
0.005 to 0.05% and V: 0.005 to 0.05% are added, while the flux TiO 2: 1.8 to
The filling rate of the flux is 7.5%, less than 15% of iron powder, and the balance is a slag-forming agent including an arc stabilizer.
0.5 is characterized by being filled in the metal shell so that (weight ratio to the total weight of the wire) is 10 to 25%.
Flux-cored wire for gas shield arc welding for Mo steel, Mn-Mo steel and Mn-Mo-Ni steel.
或いは両方に、Ｎi:０.１〜３％及びＣr:１％未満の１
種又は２種が添加されている請求項１に記載のフラック
ス入りワイヤ。2. One or both of the metal shell and the flux, Ni: 0.1 to 3% and Cr: less than 1% of 1
The flux-cored wire according to claim 1, wherein two or more species are added.
Ｎ量が０.０１５％以下である請求項１又は２に記載の
フラックス入りワイヤ。3. The flux-cored wire according to claim 1, wherein the total amount of N contained in the metal shell and the flux is 0.015% or less.
或いは両方に、更にＴi:０.０５〜０.３％及びＢ:０.０
０５〜０.０１５％のうちの少なくとも１種以上が添加
されている請求項１、２又は３に記載のフラックス入り
ワイヤ。4. Either or both of the metal shell and the flux, and further Ti: 0.05-0.3% and B: 0.0.
The flux-cored wire according to claim 1, 2 or 3, to which at least one or more of 0.05 to 0.015% is added.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3268815A JPH0825063B2 (en) | 1991-09-20 | 1991-09-20 | Flux-cored wire for 0.5Mo steel, Mn-Mo steel and Mn-Mo-Ni steel for gas shielded arc welding |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3268815A JPH0825063B2 (en) | 1991-09-20 | 1991-09-20 | Flux-cored wire for 0.5Mo steel, Mn-Mo steel and Mn-Mo-Ni steel for gas shielded arc welding |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0577086A true JPH0577086A (en) | 1993-03-30 |
| JPH0825063B2 JPH0825063B2 (en) | 1996-03-13 |
Family
ID=17463642
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3268815A Expired - Fee Related JPH0825063B2 (en) | 1991-09-20 | 1991-09-20 | Flux-cored wire for 0.5Mo steel, Mn-Mo steel and Mn-Mo-Ni steel for gas shielded arc welding |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0825063B2 (en) |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0688630A1 (en) * | 1994-06-24 | 1995-12-27 | KABUSHIKI KAISHA KOBE SEIKO SHO also known as Kobe Steel Ltd. | Flux-cored wire for gas shielded arc welding |
| JPH0810982A (en) * | 1994-06-24 | 1996-01-16 | Kobe Steel Ltd | Flux cored wire for gas shielded arc welding |
| JPH0899193A (en) * | 1994-09-30 | 1996-04-16 | Kobe Steel Ltd | Flux cored wire for gas shielded arc welding |
| US6479796B2 (en) | 2000-05-01 | 2002-11-12 | Kobe Steel, Ltd. | Flux-cored wire for gas-shielded arc welding of heat resisting steel |
| JP2007289965A (en) * | 2006-04-20 | 2007-11-08 | Kobe Steel Ltd | Flux-cored wire for gas shielded arc welding and welding method |
| JP2009028765A (en) * | 2007-07-27 | 2009-02-12 | Kobe Steel Ltd | Weld metal and titania-based flux cored wire |
| US8574381B2 (en) | 2009-03-26 | 2013-11-05 | Kobe Steel, Ltd. | Weld metal and welded structure having weld joints using the same |
| KR20160078621A (en) * | 2014-12-24 | 2016-07-05 | 주식회사 포스코 | Tungsten inert gas welding material for high manganese steel |
| JP2016526486A (en) * | 2013-07-08 | 2016-09-05 | リンカーン グローバル，インコーポレイテッド | High fracture toughness welds on thick workpieces |
| CN111417489A (en) * | 2017-11-24 | 2020-07-14 | 株式会社神户制钢所 | Flux-cored wire for gas-shielded arc welding and welding method |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS632592A (en) * | 1986-06-19 | 1988-01-07 | Kobe Steel Ltd | Flux cored wire for low alloy heat resistant steel welding |
| JPH02192894A (en) * | 1989-01-20 | 1990-07-30 | Nippon Steel Corp | Flux-cored wire for gas shielded arc welding for fireproof steel |
| JPH02205298A (en) * | 1989-02-01 | 1990-08-15 | Nippon Steel Corp | Flux cored wire for gas shielded arc welding of refractory steel |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS58119490A (en) * | 1982-01-09 | 1983-07-15 | Nippon Steel Corp | Composite wire for gas shield welding |
-
1991
- 1991-09-20 JP JP3268815A patent/JPH0825063B2/en not_active Expired - Fee Related
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS632592A (en) * | 1986-06-19 | 1988-01-07 | Kobe Steel Ltd | Flux cored wire for low alloy heat resistant steel welding |
| JPH02192894A (en) * | 1989-01-20 | 1990-07-30 | Nippon Steel Corp | Flux-cored wire for gas shielded arc welding for fireproof steel |
| JPH02205298A (en) * | 1989-02-01 | 1990-08-15 | Nippon Steel Corp | Flux cored wire for gas shielded arc welding of refractory steel |
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0688630A1 (en) * | 1994-06-24 | 1995-12-27 | KABUSHIKI KAISHA KOBE SEIKO SHO also known as Kobe Steel Ltd. | Flux-cored wire for gas shielded arc welding |
| JPH0810982A (en) * | 1994-06-24 | 1996-01-16 | Kobe Steel Ltd | Flux cored wire for gas shielded arc welding |
| EP0688630B2 (en) † | 1994-06-24 | 2010-06-09 | KABUSHIKI KAISHA KOBE SEIKO SHO also known as Kobe Steel Ltd. | Flux-cored wire for gas shielded arc welding |
| JPH0899193A (en) * | 1994-09-30 | 1996-04-16 | Kobe Steel Ltd | Flux cored wire for gas shielded arc welding |
| US6479796B2 (en) | 2000-05-01 | 2002-11-12 | Kobe Steel, Ltd. | Flux-cored wire for gas-shielded arc welding of heat resisting steel |
| JP2007289965A (en) * | 2006-04-20 | 2007-11-08 | Kobe Steel Ltd | Flux-cored wire for gas shielded arc welding and welding method |
| JP2009028765A (en) * | 2007-07-27 | 2009-02-12 | Kobe Steel Ltd | Weld metal and titania-based flux cored wire |
| US8574381B2 (en) | 2009-03-26 | 2013-11-05 | Kobe Steel, Ltd. | Weld metal and welded structure having weld joints using the same |
| JP2016526486A (en) * | 2013-07-08 | 2016-09-05 | リンカーン グローバル，インコーポレイテッド | High fracture toughness welds on thick workpieces |
| KR20160078621A (en) * | 2014-12-24 | 2016-07-05 | 주식회사 포스코 | Tungsten inert gas welding material for high manganese steel |
| CN111417489A (en) * | 2017-11-24 | 2020-07-14 | 株式会社神户制钢所 | Flux-cored wire for gas-shielded arc welding and welding method |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0825063B2 (en) | 1996-03-13 |
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