JP5153421B2 - Flux-cored wire for gas shielded arc welding - Google Patents
Flux-cored wire for gas shielded arc welding Download PDFInfo
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- JP5153421B2 JP5153421B2 JP2008099325A JP2008099325A JP5153421B2 JP 5153421 B2 JP5153421 B2 JP 5153421B2 JP 2008099325 A JP2008099325 A JP 2008099325A JP 2008099325 A JP2008099325 A JP 2008099325A JP 5153421 B2 JP5153421 B2 JP 5153421B2
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- 238000003466 welding Methods 0.000 title claims description 42
- 229910000831 Steel Inorganic materials 0.000 claims description 18
- 239000010959 steel Substances 0.000 claims description 18
- 229910004298 SiO 2 Inorganic materials 0.000 claims description 16
- 230000004907 flux Effects 0.000 claims description 16
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 12
- 229910001512 metal fluoride Inorganic materials 0.000 claims description 9
- 229910010413 TiO 2 Inorganic materials 0.000 claims description 8
- 229910018072 Al 2 O 3 Inorganic materials 0.000 claims description 6
- 229910000640 Fe alloy Inorganic materials 0.000 claims description 4
- 239000003381 stabilizer Substances 0.000 claims description 4
- 239000000843 powder Substances 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 2
- 238000006243 chemical reaction Methods 0.000 claims 1
- 229910052751 metal Inorganic materials 0.000 description 67
- 239000002184 metal Substances 0.000 description 67
- 239000002893 slag Substances 0.000 description 17
- 230000000694 effects Effects 0.000 description 14
- 239000011324 bead Substances 0.000 description 10
- 239000007789 gas Substances 0.000 description 8
- 239000010936 titanium Substances 0.000 description 8
- 229910052760 oxygen Inorganic materials 0.000 description 6
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 5
- 239000001301 oxygen Substances 0.000 description 5
- 238000000034 method Methods 0.000 description 4
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N titanium dioxide Inorganic materials O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 230000004927 fusion Effects 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 238000005538 encapsulation Methods 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 230000008014 freezing Effects 0.000 description 2
- 238000007710 freezing Methods 0.000 description 2
- 239000003517 fume Substances 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 230000000717 retained effect Effects 0.000 description 2
- 229910004261 CaF 2 Inorganic materials 0.000 description 1
- 229910002551 Fe-Mn Inorganic materials 0.000 description 1
- 229910017082 Fe-Si Inorganic materials 0.000 description 1
- 229910017133 Fe—Si Inorganic materials 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 229910000272 alkali metal oxide Inorganic materials 0.000 description 1
- 229910000287 alkaline earth metal oxide Inorganic materials 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000009863 impact test Methods 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- OGIDPMRJRNCKJF-UHFFFAOYSA-N titanium oxide Inorganic materials [Ti]=O OGIDPMRJRNCKJF-UHFFFAOYSA-N 0.000 description 1
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- Nonmetallic Welding Materials (AREA)
Description
本発明は、鋼構造物等を溶接するにあたり、全姿勢溶接が可能で、かつ低温靭性に優れる溶接金属が得られる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。 TECHNICAL FIELD The present invention relates to a flux-cored wire for gas shielded arc welding that can be welded in all positions when welding a steel structure or the like and obtains a weld metal having excellent low-temperature toughness.
鋼を被溶接材とするガスシールドアーク溶接に用いられるルチール系フラックス入りワイヤは、溶接能率、姿勢溶接性、溶接作業性において非常に優れているので、造船、橋梁、海洋構造物、鉄骨など広く適用されている。 The rutile flux cored wire used for gas shielded arc welding with steel as the material to be welded is very excellent in welding efficiency, posture weldability and welding workability. Has been applied.
しかし、ルチール系フラックス入りワイヤは、ＴｉＯ２をはじめとする酸化物主体のフラックスが鋼製外皮中に充填されているために、溶接金属中の酸素量が多く、低温靭性が得られない。したがって、ルチール系フラックス入りワイヤの低温靭性を向上させる技術がいろいろと検討されている。たとえば、特許第２９０８５８５号公報（特許文献１）には、低温靭性が優れる溶接金属を得るための技術が開示されているが、本発明者らが求める低温靭性レベルにはない。また、特許第３２０３５２７号公報（特許文献２）にも、低温靭性が優れる溶接金属を得るための技術が開示されているが、強脱酸剤として添加されているＣａは、溶接時にアークを不安定にして多量のスパッタを発生させるため、溶接作業性が不良となる。さらに、特許第２６７９８８０号公報（特許文献３）には、低温靭性が優れる溶接金属を得るための技術が開示されているが、金属フッ化物が多く添加されているため、溶接時にアークが不安定になり、多量のスパッタが発生するため、良好な溶接作業性が得られないという問題があった。 However, since the rutile flux-cored wire is filled with an oxide-based flux such as TiO 2 in the steel outer shell, the amount of oxygen in the weld metal is large and low temperature toughness cannot be obtained. Therefore, various techniques for improving the low temperature toughness of the rutile flux cored wire have been studied. For example, Japanese Patent No. 2908585 (Patent Document 1) discloses a technique for obtaining a weld metal having excellent low-temperature toughness, but it is not at the low-temperature toughness level required by the present inventors. Also, Japanese Patent No. 3203527 (Patent Document 2) discloses a technique for obtaining a weld metal having excellent low temperature toughness, but Ca added as a strong deoxidizer does not cause an arc during welding. Since a large amount of spatter is generated stably, welding workability becomes poor. Furthermore, Japanese Patent No. 2679880 (Patent Document 3) discloses a technique for obtaining a weld metal having excellent low-temperature toughness, but since a large amount of metal fluoride is added, the arc is unstable during welding. Therefore, since a large amount of spatter is generated, there is a problem that good welding workability cannot be obtained.
本発明は、全姿勢溶接で溶接作業性が良好で、かつ低温靭性の優れる溶接金属を得ることができる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を目的とする。 An object of this invention is to provide the flux cored wire for gas shielded arc welding which can obtain the weld metal which is excellent in welding workability | operativity by all position welding, and is excellent in low-temperature toughness.
本発明の要旨は、鋼製外皮にフラックスを充填してなるガスシールドアーク溶接用フラックス入りワイヤにおいて、ワイヤ全質量に対する質量％で、鋼製外皮とフラックスの両方の合計で、Ｃ：０．０３〜０．０８％、Ｓｉ：０．０１〜０．４％、Ｍｎ：１．２〜２．５％、Ｍｇ：０．２〜０．８％、Ｂ：０．００１〜０．０１５％で、フラックスに、ＴｉＯ２：４〜７％、ＳｉＯ２：０．０１〜０．５％を含有し、Ｔｉ：０．２％以下、Ａｌ：０．０３％以下、Ａｌ２Ｏ３：０．５％以下、ＺｒＯ２：１％以下、金属フッ化物のＦ換算値：０．３％以下、かつ、ＳｉＯ２＋２×Ｓｉ＋５０×Ａｌ：０．０５〜２．３で、残部は鋼製外皮のＦｅ、鉄粉、鉄合金粉のＦｅ分、アーク安定剤および不可避不純物からなることを特徴とする。 The gist of the present invention is, in a flux-cored wire for gas shielded arc welding, in which a steel outer shell is filled with a flux, in mass% with respect to the total mass of the wire, and the total of both the steel outer shell and the flux, C: 0.03 -0.08%, Si: 0.01-0.4%, Mn: 1.2-2.5%, Mg: 0.2-0.8%, B: 0.001-0.015% The flux contains TiO 2 : 4 to 7%, SiO 2 : 0.01 to 0.5%, Ti: 0.2% or less, Al: 0.03% or less, Al 2 O 3 : 0. 5% or less, ZrO 2 : 1% or less, F converted value of metal fluoride: 0.3% or less, and SiO 2 + 2 × Si + 50 × Al: 0.05 to 2.3, with the balance being a steel shell Fe, iron powder, Fe content of iron alloy powder, arc stabilizer and inevitable impurities.
また、鋼製外皮とフラックスの両方の合計で、Ｎｉ：３．０％以下を含有することも特徴とするガスシールドアーク溶接用フラックス入りワイヤにある。 Moreover, it exists in the flux-cored wire for gas shield arc welding characterized by containing Ni: 3.0% or less in the sum total of both a steel outer shell and a flux.
本発明の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、全姿勢溶接で溶接作業性が良好で、また−６０〜―８０℃における低温靭性が良好な溶接金属が得られるなど、溶接部の品質の向上を図ることができる。 According to the flux-cored wire for gas shielded arc welding of the present invention, a weld metal having good welding workability in all position welding and good low temperature toughness at -60 to -80 ° C can be obtained. Can be improved.
本発明者らは、全姿勢溶接が可能なガスシールドアーク溶接用フラックス入りワイヤについて、溶接して得られる溶接金属の低温靭性が良好で、かつ溶接作業性が良好なワイヤ成分を得るべく、ワイヤ成分組成について種々検討を行った。
その結果、ＴｉＯ２を主成分とした酸化物、金属フッ化物、合金成分および脱酸剤の適正添加量を見出した。
以下、本発明のガスシールドアーク溶接用フラックス入りワイヤの成分組成の限定理由を説明する。なお、成分についての％は質量％を表している。
In order to obtain a wire component having good low-temperature toughness and good welding workability of a weld metal obtained by welding with respect to a flux-cored wire for gas shielded arc welding capable of all-position welding, the present inventors Various investigations were made on the component composition.
As a result, the proper addition amount of the oxide, metal fluoride, alloy component and deoxidizer mainly composed of TiO 2 was found.
Hereinafter, the reasons for limiting the component composition of the flux-cored wire for gas shielded arc welding of the present invention will be described. In addition,% about a component represents the mass%.
（Ｃ：０．０３〜０．０８％）
Ｃは、溶接金属の酸素量を低減し、溶接時のアークを安定にする。鋼製外皮とフラックスの合計（以下、ワイヤ成分という。）のＣが０．０３質量％（以下、％という。）未満では上記効果が得られず、０．０８％を超えるとＣが溶接金属に過剰に歩留まり、強度が過剰になり、低温靭性が低下する。したがって、Ｃは０．０３〜０．０８％とした。
(C: 0.03-0.08%)
C reduces the oxygen content of the weld metal and stabilizes the arc during welding. The above effect cannot be obtained if the total amount of steel outer shell and flux (hereinafter referred to as wire component) is less than 0.03% by mass (hereinafter referred to as%), and if it exceeds 0.08%, C is a weld metal. Excessive yield, strength becomes excessive, and low temperature toughness decreases. Therefore, C is set to 0.03 to 0.08%.
（Ｓｉ：０．０１〜０．４％）
Ｓｉは、溶接時に酸化して溶接スラグとなり、溶接ビードの外観や形状を良好にする。また、溶接金属に歩留り、溶接金属の強度を高める効果がある。ワイヤ成分のＳｉが０．０１％未満であると、これらの効果が得られない。一方、０．４％を超えると溶接金属のミクロ組織中の硬化相生成を促進して低温靭性を低下させる。
(Si: 0.01-0.4%)
Si is oxidized during welding to form a welding slag, and the appearance and shape of the weld bead are improved. Moreover, there is an effect of increasing the yield of the weld metal and increasing the strength of the weld metal. If the wire component Si is less than 0.01%, these effects cannot be obtained. On the other hand, if it exceeds 0.4%, the formation of a hardened phase in the microstructure of the weld metal is promoted to lower the low temperature toughness.
（Ｍｎ：１．２〜２．５％）
Ｍｎは、Ｓｉと同様に溶接時に酸化して溶接スラグとなり、溶接ビードの外観や形状を良好にする。また、溶接金属の脱酸を促進するとともに溶接金属に歩留り、溶接金属の強度と靭性を高める効果がある。１．２％未満ではこれらの効果が得られず、２．５％を超えると強度が過剰になり、低温靭性が低下する。
(Mn: 1.2-2.5%)
Mn is oxidized during welding to form a welding slag in the same manner as Si, and makes the appearance and shape of the weld bead good. Moreover, it has the effect of promoting the deoxidation of the weld metal and increasing the yield and yield of the weld metal, thereby increasing the strength and toughness of the weld metal. If it is less than 1.2%, these effects cannot be obtained. If it exceeds 2.5%, the strength becomes excessive and the low-temperature toughness is lowered.
（Ｍｇ：０．２〜０．８％）
Ｍｇは、強脱酸剤として、溶接金属の酸素を低減し、溶接金属の低温靭性を高める効果がある。０．２％未満では上記効果が得られず、０．８％を超えるとアーク中で激しく酸素と反応しスパッタやヒューム発生量が多くなる。
(Mg: 0.2-0.8%)
Mg, as a strong deoxidizer, has the effect of reducing oxygen in the weld metal and increasing the low temperature toughness of the weld metal. If it is less than 0.2%, the above-mentioned effect cannot be obtained. If it exceeds 0.8%, it reacts violently with oxygen in the arc and the amount of spatter and fumes generated increases.
（Ｂ：０．００１〜０．０１５％）
Ｂは、微量の添加で溶接金属のミクロ組織を微細にし、低温靭性を向上させる。０．００１％未満では上記効果が得られず、０．０１５％を超えると溶接金属が過度に硬化し低温靭性が低下するとともに、溶接金属に高温割れが発生しやすくなる。
(B: 0.001 to 0.015%)
B makes the microstructure of the weld metal fine by adding a small amount and improves the low temperature toughness. If the content is less than 0.001%, the above effect cannot be obtained. If the content exceeds 0.015%, the weld metal is excessively hardened and the low-temperature toughness is lowered, and high-temperature cracking is likely to occur in the weld metal.
（ＴｉＯ２：４〜７％）
ＴｉＯ２は、アーク安定剤であるとともに、スラグ剤の主成分であり、溶接時に溶融金属を被包してビード外観を良好にする。また、立向上進溶接においては適度な粘性と融点により溶融メタルが垂れるのを防止する。さらに、一部がＴｉ酸化物として溶接金属に歩留まり、溶接金属のミクロ組織を微細化して低温靭性を向上させる。４％未満では立向上進において溶融メタルが垂れやすくなり、７％を超えるとスラグ量が過剰になりスラグ巻き込みが発生したり、溶接金属中に過剰に歩留まり非金属介在物が増加して低温靭性が低下したりする。
(TiO 2: 4~7%)
TiO 2 is an arc stabilizer and a main component of the slag agent, and encapsulates molten metal during welding to improve the bead appearance. Also, in vertical welding, molten metal is prevented from dripping due to an appropriate viscosity and melting point. In addition, a part of the titanium oxide is retained in the weld metal, and the microstructure of the weld metal is refined to improve the low temperature toughness. If it is less than 4%, the molten metal tends to sag in the progress of standing up, and if it exceeds 7%, the amount of slag becomes excessive and slag entrainment occurs, or the yield is increased in the weld metal and non-metallic inclusions increase, resulting in low temperature toughness. Or drop.
（ＳｉＯ２：０．０１〜０．５％）
ＳｉＯ２は、溶融スラグの粘性を高めスラグ被包性を向上させてスラグ剥離性を向上する。また溶接時に還元されて溶接金属中に一部歩留まり、強度を高める効果がある。０．０１％未満では上記効果が得られず、０．５％を超えると溶接金属のミクロ組織中の硬化相生成を促進して溶接金属の低温靭性が低下する。
(SiO 2: 0.01~0.5%)
SiO 2 increases the viscosity of the molten slag and improves the slag encapsulation, thereby improving the slag peelability. Moreover, it is reduced at the time of welding and has an effect of increasing the yield by partially yielding in the weld metal. If the content is less than 0.01%, the above effect cannot be obtained. If the content exceeds 0.5%, formation of a hardened phase in the microstructure of the weld metal is promoted and the low temperature toughness of the weld metal is lowered.
（Ｔｉ：０．２％以下）
Ｔｉは、０．００５％以上添加することにより一部がＴｉ酸化物として溶接金属に歩留まり、溶接金属のミクロ組織を微細化して低温靭性を向上させるが、溶接金属中に固溶Ｔｉとして存在し、溶接金属が過度に硬化して低温靭性が低下するため、０．２％以下に制限する。
(Ti: 0.2% or less)
When Ti is added in an amount of 0.005% or more, a part of Ti is retained in the weld metal as a Ti oxide, and the microstructure of the weld metal is refined to improve low temperature toughness. However, Ti exists in the weld metal as solute Ti. In addition, since the weld metal is excessively hardened and the low temperature toughness is lowered, the content is limited to 0.2% or less.
（Ａｌ：０．０３％以下）
Ａｌは、０．００５％以上添加することにより溶接金属中の酸素量を減らす脱酸剤としての効果があるが、形成されたＡｌ酸化物は非金属介在物として溶接金属に取り込まれて低温靭性を低下させるため、０．０３％以下とする。
(Al: 0.03% or less)
Al is effective as a deoxidizer that reduces the amount of oxygen in the weld metal by adding 0.005% or more, but the formed Al oxide is incorporated into the weld metal as non-metallic inclusions and low temperature toughness In order to reduce the amount, 0.03% or less.
（Ａｌ２Ｏ３：０．５％以下）
Ａｌ２Ｏ３は、溶融スラグの粘性および凝固点を調整し、スラグ被包性を高める作用を有する。しかし、過度に添加すると溶接金属中に非金属介在物として残留して低温靭性が低下するため０．５％以下に制限した。なお、好ましい範囲は０．１〜０．４％である。
(Al 2 O 3 : 0.5% or less)
Al 2 O 3 has the effect of adjusting the viscosity and freezing point of the molten slag, increasing the slag encapsulated. However, when it is added excessively, it remains as a non-metallic inclusion in the weld metal and the low-temperature toughness is lowered, so it is limited to 0.5% or less. In addition, a preferable range is 0.1 to 0.4%.
（ＺｒＯ２：１％以下）
ＺｒＯ２は、Ａｌ２Ｏ３と同様に溶融スラグの粘性および凝固点を調整し、スラグ被包性を高める作用を有する。しかし、過度に添加すると溶接ビード形状が凸状になり、スラグ巻き込みや融合不良が発生しやすくなるため１％以下に制限した。なお、好ましい範囲は０．２〜０．７％である。
(ZrO 2 : 1% or less)
ZrO 2 has the function of adjusting the viscosity and freezing point of molten slag and increasing the slag encapsulation, like Al 2 O 3 . However, if added excessively, the weld bead shape becomes convex, and slag entrainment or poor fusion tends to occur, so it was limited to 1% or less. In addition, a preferable range is 0.2 to 0.7%.
（金属フッ化物のＦ換算値：０．３％以下）
金属フッ化物は、アークを安定にさせる作用がある。しかし、金属フッ化物のＦ換算値が０．３％を超えると、逆にアークが不安定になりスパッタが多く発生するため０．３％以下に制限した。なお、金属フッ化物には、ＣａＦ２、ＮａＦ、ＫＦ、ＬｉＦ、ＭｇＦ２等があり、Ｆ換算値はそれらに含有されるＦの量である。なお、好ましい範囲は０．０１〜０．１５％である。
(F value of metal fluoride: 0.3% or less)
The metal fluoride has the effect of stabilizing the arc. However, if the F-converted value of the metal fluoride exceeds 0.3%, the arc becomes unstable and a lot of spatter is generated. Incidentally, the metal fluoride, there is CaF 2, NaF, KF, LiF , MgF 2 , etc., F converted value is the amount of F contained in them. In addition, a preferable range is 0.01 to 0.15%.
（ＳｉＯ２＋２×Ｓｉ＋５０×Ａｌ：０．０５〜２．３）
良好な溶接作業性を維持しつつ溶接金属の低温靭性をいかに高レベルに維持するか検討した結果、Ｓｉ、ＳｉＯ２、Ａｌの添加量を相互に制御することが重要であることがわかった。ＳｉおよびＳｉＯ２は良好な溶接作業性を得るために必要であるが、先に述べたように、溶接金属の低温靭性は低下させる。また、その作用はＡｌに大きく影響され、Ａｌの添加量が増加するとともに溶接金属中に残存するＳｉが増え溶接金属の低温靭性が低下する。したがって、ＳｉＯ２、ＳｉおよびＡｌの添加量を溶接金属の低温靭性に対する作用の寄与率に応じて、ＳｉＯ２＋２×Ｓｉ＋５０×Ａｌで制御する必要がある。ＳｉＯ２＋２×Ｓｉ＋５０×Ａｌが０．０５未満では、溶接ビードの外観や形状が劣化し、２．３を超えると低温靭性が低下する。
(SiO 2 + 2 × Si + 50 × Al: 0.05 to 2.3)
As a result of examining how to maintain the low temperature toughness of the weld metal at a high level while maintaining good welding workability, it was found that it is important to mutually control the addition amounts of Si, SiO 2 and Al. Si and SiO 2 are necessary to obtain good welding workability, but as described above, the low temperature toughness of the weld metal is lowered. In addition, the effect is greatly influenced by Al, and the amount of Al added increases, Si remaining in the weld metal increases, and the low temperature toughness of the weld metal decreases. Therefore, it is necessary to control the addition amount of SiO 2 , Si and Al by SiO 2 + 2 × Si + 50 × Al in accordance with the contribution ratio of the action to the low temperature toughness of the weld metal. When SiO 2 + 2 × Si + 50 × Al is less than 0.05, the appearance and shape of the weld bead deteriorate, and when it exceeds 2.3, the low temperature toughness decreases.
（Ｎｉ：３％以下）
Ｎｉは、０．１％以上添加することによって溶接金属の低温靭性をさらに向上させる。しかし、３％を超えて添加すると、高温割れが発生しやすくなり健全な溶接金属が得られなくなる。
なお、フラックス中の合金成分は、鋼製外皮の成分とその含有量を考慮してフラックス中の合金成分を調整することにより、目的とする強度、低温靭性が得られるフラックス入りワイヤとすることができる。
(Ni: 3% or less)
Ni further improves the low temperature toughness of the weld metal by adding 0.1% or more. However, if added over 3%, hot cracking tends to occur and a sound weld metal cannot be obtained.
In addition, the alloy component in the flux may be a flux-cored wire that can achieve the desired strength and low temperature toughness by adjusting the alloy component in the flux in consideration of the steel outer shell component and its content. it can.
また、ＰおよびＳは溶接金属中において低融点化合物を生成して粒界の強度を低下させ、溶接金属の靭性を低下させるため、できるだけ低いことが望ましい。
フラックス充填率は特に制限しないが、ワイヤ全質量に対して８〜２０％とするのが生産性から好ましい。
Further, P and S are desirably as low as possible because they generate a low melting point compound in the weld metal to lower the grain boundary strength and lower the toughness of the weld metal.
The flux filling rate is not particularly limited, but is preferably 8 to 20% with respect to the total mass of the wire from the viewpoint of productivity.
また、残部についての鋼製外皮のＦｅは鋼製外皮中のＦｅで、鉄粉は成分調整のために添加した鉄粉で、鉄合金粉のＦｅ分は成分元素を鉄合金、例えばＦｅ-Ｓｉ、Ｆｅ-Ｍｎ等として添加した場合のＦｅ分を意味する。アーク安定剤としては、アルカリ金属の酸化物やアルカリ土類金属の酸化物等、例えばＮａ２Ｏ、Ｋ２Ｏ等の公知のものである。 In addition, Fe of the steel outer shell for the balance is Fe in the steel outer shell, iron powder is iron powder added for component adjustment, and the Fe content of the iron alloy powder is a component element of an iron alloy such as Fe-Si. , Meaning Fe content when added as Fe-Mn or the like. Examples of the arc stabilizer include alkali metal oxides and alkaline earth metal oxides such as Na 2 O and K 2 O.
以下、本発明の効果を実施例により具体的に説明する。 Hereinafter, the effect of the present invention will be described in detail with reference to examples.
鋼製外皮にＪＩＳ Ｇ３１４１ ＳＰＣＣを使用して表１に示すワイヤ径１．２ｍｍの各種成分のフラックス入りワイヤを試作した。 JIS G3141 SPCC was used for the steel outer skin, and various components of flux-cored wires having a wire diameter of 1.2 mm shown in Table 1 were made as trial products.
表１に示す試作したワイヤを用いて、板厚１２ｍｍの鋼板（ＪＩＳ Ｇ３０１６ ＳＭ４９０Ａ）をＴ字すみ肉試験体とし、表２に示す溶接作業性評価の条件で立向上進すみ肉溶接による溶接作業性の評価を行うとともに、ＪＩＳ Ｚ３３１３に準じて、板厚２０ｍｍの鋼板（ＪＩＳ Ｇ３１２６ ＳＬＡ２３５Ｂ）を用いて表２に示す溶着金属試験の条件で溶着金属試験を行った。 Using a prototyped wire shown in Table 1, a 12 mm-thick steel plate (JIS G3016 SM490A) is used as a T-shaped fillet specimen, and welding work by fillet welding is progressed under the conditions of welding workability evaluation shown in Table 2. The weld metal test was conducted under the conditions of the weld metal test shown in Table 2 using a steel plate having a thickness of 20 mm (JIS G3126 SLA235B) according to JIS Z3313.
立向上進すみ肉溶接は、半自動溶接で行い、アークの安定性、メタル垂れの有無、スパッタ発生状況、ビード形状およびビード外観について評価した後、マクロ断面を各5断面採取してスラグ巻込みや融合不良の有無を調べた。 Stand-up progress fillet welding is carried out by semi-automatic welding, and after evaluating the stability of the arc, the presence or absence of metal sag, the occurrence of spatter, the bead shape and the bead appearance, five macro sections are sampled and slag entrainment is performed. The presence or absence of poor fusion was examined.
溶着金属試験では、引張試験片と衝撃試験片（ＪＩＳ Ｚ ３１１１）をそれぞれ溶着金属の板厚中央から採取して試験に供した。機械的性質の評価は、−６０℃における吸収エネルギーが７０Ｊ以上を合格とした。これらの結果を表３に示す。 In the weld metal test, a tensile test piece and an impact test piece (JIS Z 3111) were collected from the center of the thickness of the weld metal and used for the test. In the evaluation of mechanical properties, the absorbed energy at −60 ° C. was 70 J or more. These results are shown in Table 3.
表１および表３のワイヤ記号１〜１１が本発明例、ワイヤ記号１２〜２６は比較例である。本発明例であるワイヤ記号１〜１１は、各成分が適量であるので、溶接作業性が良好で、溶着金属の−６０℃の吸収エネルギーも良好な値が得られ、さらに、Ｎｉを適量含むワイヤ記号１、３、５、７および８については、溶着金属の−８０℃における吸収エネルギーも良好な値が得られ、極めて満足な結果であった。 The wire symbols 1 to 11 in Tables 1 and 3 are examples of the present invention, and the wire symbols 12 to 26 are comparative examples. In the wire symbols 1 to 11 of the present invention, each component has an appropriate amount, so that the welding workability is good, the absorption energy at −60 ° C. of the weld metal is also good, and an appropriate amount of Ni is included. For the wire symbols 1, 3, 5, 7 and 8, good values were also obtained for the absorbed energy of the weld metal at −80 ° C., which was a very satisfactory result.
比較例中ワイヤ記号１２は、Ｃが少ないのでアークが不安定であった。また、Ａｌ２Ｏ３が多いので溶着金属の吸収エネルギーが低値であった。 In the comparative example, since the wire symbol 12 had a small amount of C, the arc was unstable. Further, the absorbed energy of the weld metal was lower because Al 2 O 3 is large.
ワイヤ記号１３は、ＳｉＯ２＋２×Ｓｉ＋５０×Ａｌが低いのでビード外観および形状が不良であった。また、Ｃが多いので溶着金属の引張強さが高くなり吸収エネルギーが低値であった。 Since the wire symbol 13 is low in SiO 2 + 2 × Si + 50 × Al, the bead appearance and shape were poor. Moreover, since there is much C, the tensile strength of the weld metal became high and the absorbed energy was low.
ワイヤ記号１４は、Ｓｉが少ないのでビード外観および形状が不良であった。また、Ａｌが多いので溶着金属の吸収エネルギーが低値であった。 The wire symbol 14 had poor bead appearance and shape due to a small amount of Si. Moreover, since there is much Al, the absorbed energy of the weld metal was low.
ワイヤ記号１５は、ＴｉＯ２が少ないのでメタル垂れが生じた。また、Ｓｉが多いので溶着金属の吸収エネルギーが低値であった。 Since the wire symbol 15 has a small amount of TiO 2 , metal dripping occurred. Moreover, since there is much Si, the absorbed energy of the weld metal was low.
ワイヤ記号１６は、Ｍｎが少ないのでビード外観および形状が不良で溶着金属の吸収エネルギーが低値であった。また、Ｍｇが多いのでスパッタおよびヒュームの発生量が多かった。 Since the wire symbol 16 had a small amount of Mn, the bead appearance and shape were poor, and the absorbed energy of the weld metal was low. Moreover, since there was much Mg, the generation amount of spatter and fumes was large.
ワイヤ記号１７は、Ｍｎが多いので溶着金属の引張強さが高くなり吸収エネルギーが低値であった。 Since the wire symbol 17 had a large amount of Mn, the tensile strength of the deposited metal was high and the absorbed energy was low.
ワイヤ記号１８は、Ｍｇが少ないので溶着金属の吸収エネルギーが低値であった。 Since the wire symbol 18 has a small amount of Mg, the absorbed energy of the weld metal was low.
ワイヤ記号１９は、ＳｉＯ２が少ないのでスラグ剥離性が不良であった。また、Ｂが少ないので溶着金属の吸収エネルギーが低値であった。 The wire symbol 19 had poor slag removability because of a small amount of SiO 2 . Further, since B is small, the absorbed energy of the weld metal was low.
ワイヤ記号２０は、Ｂが多いのでクレータ部に割れが生じた。また、溶着金属の吸収エネルギーが低値であった。 Since the wire symbol 20 has many B, the crater part was cracked. Also, the absorbed energy of the weld metal was low.
ワイヤ記号２１は、ＴｉＯ２が多いのでマクロ断面にスラグ巻き込みがあった。また、溶着金属の吸収エネルギーが低値であった。 Since the wire symbol 21 has a large amount of TiO 2 , slag was caught in the macro cross section. Also, the absorbed energy of the weld metal was low.
ワイヤ記号２２は、ＳｉＯ２が多いので溶着金属の吸収エネルギーが低値であった。 Since the wire symbol 22 has a large amount of SiO 2 , the absorbed energy of the deposited metal was low.
ワイヤ記号２３は、ＳｉＯ２＋２×Ｓｉ＋５０×Ａｌが高いので溶着金属の吸収エネルギーが低値であった。 Since the wire symbol 23 is high in SiO 2 + 2 × Si + 50 × Al, the absorbed energy of the weld metal was low.
ワイヤ記号２４は、Ｔｉが多いので溶着金属の引張強さが高くなり吸収エネルギーが低値であった。 Since the wire symbol 24 has a large amount of Ti, the tensile strength of the deposited metal was high and the absorbed energy was low.
ワイヤ記号２５は、ＺｒＯ２が多いのでマクロ断面にスラグ巻き込みおよび融合不良があった。 Since the wire symbol 25 contains a large amount of ZrO 2 , slag was caught in the macro cross section and poor fusion occurred.
ワイヤ記号２６は、金属フッ化物のＦ換算値が多いのでアークが不安定でスパッタ発生量が多かった。また、Ｎｉが多いのでクレータ部に割れが生じた。 The wire symbol 26 had a large F-converted value of metal fluoride, so the arc was unstable and the amount of spatter generated was large. Moreover, since there was much Ni, the crater part cracked.
Claims (2)
Ｃ：０．０３〜０．０８％、
Ｓｉ：０．０１〜０．４％、
Ｍｎ：１．２〜２．５％、
Ｍｇ：０．２〜０．８％、
Ｂ：０．００１〜０．０１５％で、フラックスに、
ＴｉＯ２：４〜７％、
ＳｉＯ２：０．０１〜０．５％を含有し、
Ｔｉ：０．２％以下、
Ａｌ：０．０３％以下、
Ａｌ２Ｏ３：０．５％以下、
ＺｒＯ２：１％以下、
金属フッ化物のＦ換算値：０．３％以下、
かつ、ＳｉＯ２＋２×Ｓｉ＋５０×Ａｌ：０．０５〜２．３で、
残部は鋼製外皮のＦｅ、鉄粉、鉄合金粉のＦｅ分、アーク安定剤および不可避不純物からなることを特徴とするガスシールドアーク溶接用フラックス入りワイヤ。 In the flux-cored wire for gas shielded arc welding, in which the steel outer shell is filled with flux, in mass% with respect to the total mass of the wire, the total of both the steel outer shell and the flux,
C: 0.03-0.08%,
Si: 0.01-0.4%
Mn: 1.2 to 2.5%
Mg: 0.2-0.8%
B: 0.001 to 0.015%, in flux,
TiO 2: 4~7%,
Containing 0.01~0.5%,: SiO 2
Ti: 0.2% or less,
Al: 0.03% or less,
Al 2 O 3 : 0.5% or less,
ZrO 2 : 1% or less,
F conversion value of metal fluoride: 0.3% or less,
And SiO 2 + 2 × Si + 50 × Al: 0.05 to 2.3,
The balance is a flux-cored wire for gas shielded arc welding, characterized in that the balance consists of Fe in steel outer shell, iron powder, Fe content in iron alloy powder, arc stabilizer and inevitable impurities.
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| JP6382117B2 (en) * | 2015-01-16 | 2018-08-29 | 日鐵住金溶接工業株式会社 | Flux-cored wire for Ar-CO2 mixed gas shielded arc welding |
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| JP6385879B2 (en) * | 2015-04-15 | 2018-09-05 | 日鐵住金溶接工業株式会社 | Flux-cored wire for gas shielded arc welding |
| JP6437419B2 (en) * | 2015-11-11 | 2018-12-12 | 日鐵住金溶接工業株式会社 | Flux-cored wire for carbon dioxide shielded arc welding |
| JP2017094360A (en) | 2015-11-25 | 2017-06-01 | 日鐵住金溶接工業株式会社 | Flux-cored wire for shield-arc welding using argon-carbon dioxide gas mixture |
| KR101783415B1 (en) * | 2016-01-06 | 2017-09-29 | 현대종합금속 주식회사 | Flux cored wire for gas shielded arc welding |
| JP6786427B2 (en) * | 2017-03-21 | 2020-11-18 | 日鉄溶接工業株式会社 | Flux-filled wire for gas shielded arc welding |
| KR102283346B1 (en) * | 2019-09-19 | 2021-07-30 | 현대종합금속 주식회사 | Titania Based Flux Cored Wire of Gas Shielded Arc Welding for superior impact toughness at ultra low temperature |
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