JP2021070051A - Flux-cored wire for gas shield arc welding - Google Patents
Flux-cored wire for gas shield arc welding Download PDFInfo
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- 238000003466 welding Methods 0.000 title claims abstract description 147
- 230000004907 flux Effects 0.000 claims abstract description 63
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 53
- 239000010959 steel Substances 0.000 claims abstract description 53
- 238000006243 chemical reaction Methods 0.000 claims abstract description 31
- KRHYYFGTRYWZRS-UHFFFAOYSA-M Fluoride anion Chemical compound [F-] KRHYYFGTRYWZRS-UHFFFAOYSA-M 0.000 claims description 20
- 229910001512 metal fluoride Inorganic materials 0.000 claims description 15
- 229910004298 SiO 2 Inorganic materials 0.000 claims description 12
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 11
- 239000012535 impurity Substances 0.000 claims description 4
- 229910000640 Fe alloy Inorganic materials 0.000 claims description 2
- 229910052751 metal Inorganic materials 0.000 abstract description 71
- 239000002184 metal Substances 0.000 abstract description 71
- 230000007547 defect Effects 0.000 abstract description 17
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 abstract 2
- 229910052681 coesite Inorganic materials 0.000 abstract 1
- 229910052906 cristobalite Inorganic materials 0.000 abstract 1
- 239000000377 silicon dioxide Substances 0.000 abstract 1
- 235000012239 silicon dioxide Nutrition 0.000 abstract 1
- 229910052682 stishovite Inorganic materials 0.000 abstract 1
- 229910052905 tridymite Inorganic materials 0.000 abstract 1
- 239000011734 sodium Substances 0.000 description 34
- 239000002893 slag Substances 0.000 description 20
- 239000007787 solid Substances 0.000 description 19
- 239000007789 gas Substances 0.000 description 17
- 238000010276 construction Methods 0.000 description 16
- 239000011324 bead Substances 0.000 description 14
- 230000000694 effects Effects 0.000 description 11
- 239000010410 layer Substances 0.000 description 11
- 239000000463 material Substances 0.000 description 9
- 239000000843 powder Substances 0.000 description 9
- 229910045601 alloy Inorganic materials 0.000 description 8
- 239000000956 alloy Substances 0.000 description 8
- 238000005336 cracking Methods 0.000 description 6
- 229910052748 manganese Inorganic materials 0.000 description 6
- 230000000052 comparative effect Effects 0.000 description 4
- 230000007423 decrease Effects 0.000 description 4
- 150000002222 fluorine compounds Chemical class 0.000 description 4
- 238000009863 impact test Methods 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 235000019353 potassium silicate Nutrition 0.000 description 4
- NTHWMYGWWRZVTN-UHFFFAOYSA-N sodium silicate Chemical compound [Na+].[Na+].[O-][Si]([O-])=O NTHWMYGWWRZVTN-UHFFFAOYSA-N 0.000 description 4
- 229910052799 carbon Inorganic materials 0.000 description 3
- 229910018134 Al-Mg Inorganic materials 0.000 description 2
- 229910018467 Al—Mg Inorganic materials 0.000 description 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 2
- 229910002551 Fe-Mn Inorganic materials 0.000 description 2
- 229910017082 Fe-Si Inorganic materials 0.000 description 2
- 229910002593 Fe-Ti Inorganic materials 0.000 description 2
- 229910017133 Fe—Si Inorganic materials 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- 239000004111 Potassium silicate Substances 0.000 description 2
- 229910006639 Si—Mn Inorganic materials 0.000 description 2
- 239000004115 Sodium Silicate Substances 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 230000005540 biological transmission Effects 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 239000000314 lubricant Substances 0.000 description 2
- 150000002739 metals Chemical class 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 229910052913 potassium silicate Inorganic materials 0.000 description 2
- NNHHDJVEYQHLHG-UHFFFAOYSA-N potassium silicate Chemical compound [K+].[K+].[O-][Si]([O-])=O NNHHDJVEYQHLHG-UHFFFAOYSA-N 0.000 description 2
- PUZPDOWCWNUUKD-UHFFFAOYSA-M sodium fluoride Chemical compound [F-].[Na+] PUZPDOWCWNUUKD-UHFFFAOYSA-M 0.000 description 2
- 229910052911 sodium silicate Inorganic materials 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- BXVSAYBZSGIURM-UHFFFAOYSA-N 2-phenoxy-4h-1,3,2$l^{5}-benzodioxaphosphinine 2-oxide Chemical compound O1CC2=CC=CC=C2OP1(=O)OC1=CC=CC=C1 BXVSAYBZSGIURM-UHFFFAOYSA-N 0.000 description 1
- 229910016569 AlF 3 Inorganic materials 0.000 description 1
- 229910004261 CaF 2 Inorganic materials 0.000 description 1
- -1 Fe-Si Chemical compound 0.000 description 1
- 229910008423 Si—B Inorganic materials 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 229910052783 alkali metal Inorganic materials 0.000 description 1
- 150000001340 alkali metals Chemical class 0.000 description 1
- 229910002092 carbon dioxide Inorganic materials 0.000 description 1
- 239000001569 carbon dioxide Substances 0.000 description 1
- 239000000919 ceramic Substances 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- CWQXQMHSOZUFJS-UHFFFAOYSA-N molybdenum disulfide Chemical compound S=[Mo]=S CWQXQMHSOZUFJS-UHFFFAOYSA-N 0.000 description 1
- 229910052982 molybdenum disulfide Inorganic materials 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 150000003904 phospholipids Chemical class 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 229910052708 sodium Inorganic materials 0.000 description 1
- 239000011775 sodium fluoride Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 230000002195 synergetic effect Effects 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
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- Nonmetallic Welding Materials (AREA)
Abstract
Description
本発明は、４９０〜５５０ＭＰａ級鋼のガスシールドアーク溶接用フラックス入りワイヤに関し、特に固形裏当材を用いた片面溶接の初層溶接において生じやすいブローホールの発生が無く、小入熱溶接から大電流溶接で溶接作業性に優れ、さらに、大入熱・高パス間温度の溶接施工条件においても機械的性能に優れた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に関する。 The present invention relates to a flux-filled wire for gas shielded arc welding of 490 to 550 MPa class steel, and does not generate blowholes that are likely to occur in the first layer welding of single-sided welding using a solid backing material, and is large from small heat input welding. The present invention relates to a flux-containing wire for gas shielded arc welding, which is excellent in welding workability by current welding and can obtain a welded metal having excellent mechanical performance even under welding construction conditions of large heat input and high interpass temperature.
建築鉄骨分野において、溶接施工の能率向上を図るため、溶接用ソリッドワイヤを用いた高電流域でのガスシールドアーク溶接が行われている。溶接用ソリッドワイヤでの高電流溶接では、一層毎の溶着量が多いので溶接の高能率化が可能であるが、アークが不安定でスパッタ発生量が多く、ビード外観・形状が不良であるなど溶接作業性が悪いという問題がある。また、スパッタが大粒になるため、鋼板表面に付着したスパッタを除去作業も困難となり作業効率も不良であった。 In the field of building steel frames, gas shielded arc welding is performed in a high current range using solid wires for welding in order to improve the efficiency of welding work. In high-current welding with solid wire for welding, it is possible to improve the efficiency of welding because the amount of welding for each layer is large, but the arc is unstable, the amount of spatter generated is large, and the bead appearance and shape are poor. There is a problem that welding workability is poor. In addition, since the spatter becomes large, it is difficult to remove the spatter adhering to the surface of the steel sheet, and the work efficiency is also poor.
これら問題を解決する手段として、スパッタ発生量が少ないガスシールドアーク溶接用ソリッドワイヤの開発が行われている。例えば特許文献１には、ワイヤ表面に二硫化モリブデン、リン脂質及び常温で液体の潤滑剤からなる送給潤滑剤を適量付着させることでワイヤ送給性を良好にし、溶接時のスパッタ発生量を低減する技術が開示されている。また、特許文献２には、ワイヤ表層下にアルカリ金属含浸部を有することでスパッタ発生量を低減できる溶接用ソリッドワイヤが開示されている。しかし、溶接用ソリッドワイヤでの高電流溶接では、発生するスパッタ自体が多いため、たとえワイヤ送給性が良好になってもスパッタ発生量を十分に低減できず、また、ビード外観・形状も改善されないという問題があった。 As a means for solving these problems, a solid wire for gas shielded arc welding with a small amount of spatter generated has been developed. For example, in Patent Document 1, the wire feeding property is improved by adhering an appropriate amount of a feeding lubricant composed of molybdenum disulfide, phospholipid, and a lubricant liquid at room temperature to the wire surface, and the amount of spatter generated during welding is increased. Techniques for reduction are disclosed. Further, Patent Document 2 discloses a solid wire for welding that can reduce the amount of spatter generated by having an alkali metal impregnated portion under the wire surface layer. However, in high-current welding with solid wire for welding, a large amount of spatter is generated, so even if the wire feedability is improved, the amount of spatter generated cannot be sufficiently reduced, and the appearance and shape of the bead are also improved. There was a problem that it was not done.
また近年では、更なる溶接施工の高能率化を目的から、大入熱・高パス間温度の溶接施工条件に対応するガスシールドアーク溶接用ソリッドワイヤが開発されており、例えば、特許文献３、特許文献４及び特許文献５等にあるように、ワイヤ中にＭｏ、Ｃｒ等を多く含有したものが開示されている。これらソリッドワイヤによれば、大入熱・高パス間温度の溶接施工条件においても、溶接金属の強度及び靭性を確保することが可能であるが、やはりアークが不安定でスパッタ発生量が多く、ビード外観・形状が不良であるなど溶接作業性が悪いという問題があった。 Further, in recent years, for the purpose of further improving the efficiency of welding work, solid wires for gas shielded arc welding corresponding to welding work conditions of large heat input and high inter-pass temperature have been developed. For example, Patent Document 3 and 3. As described in Patent Document 4 and Patent Document 5, a wire containing a large amount of Mo, Cr, etc. is disclosed. According to these solid wires, it is possible to secure the strength and toughness of the weld metal even under welding construction conditions with large heat input and high interpass temperature, but the arc is still unstable and the amount of spatter generated is large. There was a problem that welding workability was poor, such as poor bead appearance and shape.
大入熱・高パス間温度の溶接施工条件で溶接金属の強度及び靭性を確保しつつ、溶接作業性が良好なガスシールドアーク溶接用ワイヤとして、例えば、特許文献６、特許文献７には、大入熱・高パス間温度の溶接施工条件の下で、良好な溶接作業性が得られるとともに、機械的性能に優れた溶接金属が得られるフラックス入りワイヤが開示されている。しかし、これらのフラックス入りワイヤでは、溶接用ソリッドワイヤでの高電流溶接よりもスパッタ発生量は減少できるものの、やはりスパッタ発生量は総じて多く、また、スラグ発生量が多いので、スラグ巻込み等の溶接欠陥が発生しやすくなるという問題があった。 As a gas shielded arc welding wire with good welding workability while ensuring the strength and toughness of the weld metal under welding construction conditions with large heat input and high interpass temperature, for example, Patent Document 6 and Patent Document 7 A flux-filled wire is disclosed in which good welding workability can be obtained and a weld metal having excellent mechanical performance can be obtained under welding construction conditions of high heat input and high interpass temperature. However, although these flux-cored wires can reduce the amount of spatter generated compared to high-current welding with solid wires for welding, the amount of spatter generated is generally large and the amount of slag generated is large, so slag entrainment, etc. There is a problem that welding defects are likely to occur.
一方、本発明者らは特許文献８において、高電流、大入熱・高パス間温度の溶接施工条件の下で、スパッタ発生量が少ない等良好な溶接作業性が得られるとともに、機械的性能の優れた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を提案した。しかし、特許文献８に提案したガスシールドアーク溶接用フラックス入りワイヤを用いて、固形裏当材を用いた片面溶接の初層溶接においてはブローホールが生じやすいという問題があった。 On the other hand, in Patent Document 8, the present inventors can obtain good welding workability such as a small amount of spatter generation under welding construction conditions of high current, large heat input and high inter-pass temperature, and mechanical performance. We have proposed a flux-cored wire for gas shielded arc welding that can obtain excellent weld metal. However, there is a problem that blow holes are likely to occur in the first layer welding of single-sided welding using a solid backing material using the flux-cored wire for gas shielded arc welding proposed in Patent Document 8.
そこで本発明は、上記問題点に鑑みて案出されたものであり、４９０〜５５０ＭＰａ級鋼の固形裏当材を用いた片面溶接の初層溶接時に生じやすいブローホールの発生が無く、小入熱溶接から高電流溶接でスパッタ発生量が少なく、アークの安定性及びビード外観・形状が良好で、スラグ巻き込み等の溶接欠陥が少ないなど溶接作業性に優れ、さらに、大入熱及び高パス間温度の溶接施工条件で適正な強度と靭性を有す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を提供することを目的とする。 Therefore, the present invention has been devised in view of the above problems, and there is no blow hole that is likely to occur during the first layer welding of single-sided welding using a solid backing material of 490-550 MPa class steel, and a small amount is inserted. From hot welding to high current welding, the amount of spatter generated is small, the arc stability and bead appearance and shape are good, welding defects such as slag entrainment are few, and welding workability is excellent. It is an object of the present invention to provide a flux-filled wire for gas shielded arc welding, which can obtain a welded metal having appropriate strength and toughness under hot welding conditions.
本発明者らは、上記課題を解決するために、４９０〜５５０ＭＰａ級鋼の固形裏当材を用いた片面溶接、高電流溶接、さらに大入熱・高パス間温度でのガスシールドアーク溶接において、適正な強度及び靭性を有する溶接金属が得られるとともに、ブローホールの発生が無く、アークが安定し、スパッタ発生量が少なく、ビード外観・形状が良好で、溶接欠陥が防止できるなど良好な溶接作業性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の成分組成について詳細に検討した。 In order to solve the above problems, the present inventors perform single-sided welding using a solid backing material of 490-550 MPa class steel, high-current welding, and gas-shielded arc welding at a large heat input and a high interpass temperature. Welding metal with appropriate strength and toughness can be obtained, no blow holes are generated, arc is stable, spatter generation amount is small, bead appearance and shape are good, and welding defects can be prevented. The composition of the flux-filled wire for gas-shielded arc welding, which provides workability, was examined in detail.
その結果、下向姿勢や横向姿勢等での固形裏当材を用いた片面溶接の初層溶接において生じやすいブローホールは、Ａｌ及びＭｇの一方または両方の合計を適量含有させることによって生じなくなることを見出した。 As a result, blow holes that are likely to occur in the first layer welding of single-sided welding using a solid backing material in a downward posture or a sideways posture are eliminated by containing an appropriate amount of one or both of Al and Mg. I found.
また、高電流での溶接施工条件において、アークの安定性及びスパッタ発生量の低減は、Ｎａ酸化物、Ｎａ弗化物、Ｋ酸化物及びＫ弗化物のＮａ換算値とＫ換算値の合計量及び金属弗化物のＦ換算値の合計量を適正にすることで良好になることを見出した。 Further, under welding construction conditions at a high current, the stability of the arc and the reduction of the amount of spatter generated are determined by the total amount of the Na conversion value and the K conversion value of Na oxide, Na fluoride, K oxide and K fluoride. It was found that it becomes better by adjusting the total amount of F-converted values of the metal fluoride.
高電流での溶接施工条件における溶接金属の適正な強度と同時に安定した靭性の向上をも同時に達成させるためには、ワイヤ中のスラグ生成剤である酸化物を極力減らし、合金成分のＣ、Ｓｉ、Ｍｎ、Ｔｉのそれぞれの適正化、さらにＢの適量添加が有効であることを知見した。 In order to achieve the proper strength of the weld metal and the stable improvement of toughness under the welding construction conditions at high current, the oxide which is a slag generating agent in the wire is reduced as much as possible, and the alloy components C and Si are used. , Mn, and Ti were optimized, and it was found that the addition of an appropriate amount of B was effective.
さらに、ワイヤ中のＭｏ量を適正にすることにより、大入熱・高パス間温度の溶接施工条件においても、溶接金属の高強度化が、Ｂの適量添加で靭性の向上が可能であることも知見した。 Furthermore, by optimizing the amount of Mo in the wire, it is possible to increase the strength of the weld metal and improve the toughness by adding an appropriate amount of B even under welding construction conditions with large heat input and high interpass temperature. Also found.
すなわち、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合計で、Ｃ：０．０４〜０．１８％、Ｓｉ：０．１〜１．２％、Ｍｎ：１．５〜２．５％、Ｔｉ：０．１〜０．３％、Ａｌ及びＭｇの一方または両方の合計：０．０８超〜０．２５％を含有し、さらに、ワイヤ全質量に対する質量％で、フラックス中に、金属弗化物のＦ換算値の合計：０．００５〜０．０５０％、Ｎａ酸化物、Ｎａ弗化物、Ｋ酸化物及びＫ弗化物の１種または２種以上：Ｎａ換算値とＫ換算値の合計で０．０１〜０．１０％を含有し、ＳｉＯ2：０．２０％以下で、残部は鋼製外皮のＦｅ、フラックス中の鉄粉、鉄合金からのＦｅ分及び不可避的不純物からなることを特徴とする。 That is, the gist of the present invention is a flux-cored wire for gas shielded arc welding in which a steel outer skin is filled with flux, in which the mass% of the total weight of the wire is the total of the steel outer skin and the flux, C: 0.04. ~ 0.18%, Si: 0.1 to 1.2%, Mn: 1.5 to 2.5%, Ti: 0.1 to 0.3%, total of one or both of Al and Mg: 0 It contains more than .08 to 0.25%, and in mass% with respect to the total mass of the wire, the total F-converted value of the metal flux in the flux: 0.005 to 0.050%, Na oxide, Na. One or more types of flux, K oxide and K flux: 0.01 to 0.10% in total of Na conversion value and K conversion value, SiO 2 : 0.20% or less. The balance is characterized by being composed of Fe in a steel outer skin, iron powder in a flux, Fe content from an iron alloy, and unavoidable impurities.
また、ワイヤ全質量に対する質量％で、鋼製外皮とフラックスの合計で、Ｂ：０．００２〜０．０１０％をさらに含有することも特徴とする。 It is also characterized in that it further contains B: 0.002 to 0.010% in total of the steel outer skin and the flux in mass% with respect to the total mass of the wire.
さらに、ワイヤ全質量に対する質量％で、鋼製外皮とフラックスの合計で、Ｍｏ：０．１５〜０．５０％をさらに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。 Further, the flux-cored wire for gas shielded arc welding is further characterized by further containing Mo: 0.15 to 0.50% in total of the steel outer skin and the flux in mass% with respect to the total mass of the wire.
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、固形裏当材を用いた片面溶接の初層溶接におけるブローホールの発生が無く、小入熱溶接から高電流溶接において、アークの安定性及びビード外観・形状が優れ、スパッタ発生量が少なく、スラグ生成量が少なく溶接欠陥が防止できるなど溶接作業性が良好で、さらに、大入熱・高パス間温度の溶接施工条件においても溶接金属の強度及び靭性を十分に確保し、高品質な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を提供することができる。 According to the flux-filled wire for gas shielded arc welding of the present invention, there is no blow hole in the first layer welding of single-sided welding using a solid backing material, and arc stability is achieved from small heat input welding to high current welding. The appearance and shape of the bead are excellent, the amount of spatter generated is small, the amount of slag generated is small, and welding defects can be prevented. It is possible to provide a flux-filled wire for gas-shielded arc welding, which can sufficiently secure the strength and toughness of the material and obtain high-quality weld metal.
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は、各成分組成それぞれの単独及び共存による相乗効果によりなし得たもので、以下にそれぞれの各成分組成の限定理由を述べる。なお、各成分組成の含有率は、フラックス入りワイヤ全質量に対する質量％で表すものとし、その質量％に関する記載を単に％と記載して表すこととする。 The flux-cored wire for gas shielded arc welding of the present invention can be achieved by the synergistic effect of each component composition alone or coexisting, and the reasons for limiting each component composition will be described below. The content of each component composition shall be expressed in% by mass with respect to the total mass of the flux-cored wire, and the description regarding the mass% shall be simply expressed as%.
［鋼製外皮とフラックスの合計でＣ：０．０４〜０．１８％］
Ｃは、固溶強化により溶接金属の強度を向上するために必要な元素である。Ｃが０．０４％未満であると、高電流及び大入熱・高パス間温度での溶接施工条件で溶接金属の強度が得られない。一方、Ｃが０．１８％を超えると、溶接金属の強度が過剰に高くなり、靭性が低下する。また、高温割れ感受性が高くなる。従って、鋼製外皮とフラックスの合計でＣは０．０４〜０．１８％とする。なお、Ｃは、鋼製外皮に含まれる成分の他、フラックスから金属粉及び合金粉等から添加できる。
[Total of steel outer skin and flux C: 0.04 to 0.18%]
C is an element necessary for improving the strength of the weld metal by strengthening the solid solution. If C is less than 0.04%, the strength of the weld metal cannot be obtained under the welding construction conditions of high current, large heat input, and high interpass temperature. On the other hand, when C exceeds 0.18%, the strength of the weld metal becomes excessively high and the toughness decreases. In addition, the sensitivity to high temperature cracking increases. Therefore, the total of the steel outer skin and the flux is set to 0.04 to 0.18%. In addition to the components contained in the steel outer skin, C can be added from flux, metal powder, alloy powder, or the like.
［鋼製外皮とフラックスの合計でＳｉ：０．１〜１．２％］
Ｓｉは、溶接金属の脱酸及び溶接金属の強度確保のために添加する。高電流及び大入熱・高パス間温度での溶接施工条件ではＳｉの消耗が多いが、Ｓｉが適量溶接金属に歩留まって強度を確保する必要がある。Ｓｉが０．１％未満であると、溶接金属が脱酸不足となり、溶接金属の強度及び靭性が低下する。一方、Ｓｉが１．２％を超えると、溶接金属の強度が過剰に高くなり、靭性が安定して得られない。また、溶接時に生成するスラグ量が増加してスラグ巻込み等の溶接欠陥が発生しやすくなる。従って、鋼製外皮とフラックスの合計でＳｉは０．１〜１．２％とする。なお、Ｓｉは、鋼製外皮に含まれる成分の他、フラックスから金属Ｓｉ、Ｆｅ−Ｓｉ、Ｆｅ−Ｓｉ−Ｍｎ等の合金粉から添加できる。
[Total of steel outer skin and flux Si: 0.1 to 1.2%]
Si is added to deoxidize the weld metal and ensure the strength of the weld metal. Under welding construction conditions with high current, large heat input, and high interpass temperature, Si is consumed a lot, but it is necessary to ensure the strength by retaining an appropriate amount of Si in the weld metal. If Si is less than 0.1%, the weld metal becomes insufficiently deoxidized, and the strength and toughness of the weld metal decrease. On the other hand, if Si exceeds 1.2%, the strength of the weld metal becomes excessively high, and the toughness cannot be stably obtained. In addition, the amount of slag generated during welding increases, and welding defects such as slag entrainment are likely to occur. Therefore, the total of the steel outer skin and the flux is 0.1 to 1.2%. In addition to the components contained in the steel outer skin, Si can be added from alloy powders such as metal Si, Fe-Si, and Fe-Si-Mn from the flux.
［鋼製外皮とフラックスの合計でＭｎ：１．５〜２．５％］
Ｍｎは、溶接金属の靭性確保と強度向上のために添加する。Ｍｎが１．５％未満であると、高電流及び大入熱・高パス間温度での溶接施工条件でＭｎの消耗が多くなり溶接金属の強度が低く、また、靭性が十分に確保できなくなる。一方、Ｍｎが２．５％を超えると、溶接金属の靭性が安定して得られない。また、生成スラグ量が増加してスラグ巻込み等の溶接欠陥が発生しやすくなる。従って、鋼製外皮とフラックスの合計でＭｎは１．５〜２．５％とする。なお、Ｍｎは、鋼製外皮に含まれる成分の他、フラックスからの金属Ｍｎ、Ｆｅ−Ｍｎ、Ｆｅ−Ｓｉ−Ｍｎ等の合金粉末から添加できる。
[Mn: 1.5 to 2.5% in total of steel outer skin and flux]
Mn is added to ensure the toughness and improve the strength of the weld metal. If Mn is less than 1.5%, Mn is consumed more under welding construction conditions with high current, large heat input, and high interpass temperature, the strength of the weld metal is low, and sufficient toughness cannot be ensured. .. On the other hand, if Mn exceeds 2.5%, the toughness of the weld metal cannot be stably obtained. In addition, the amount of generated slag increases, and welding defects such as slag entrainment are likely to occur. Therefore, the total Mn of the steel outer skin and the flux is 1.5 to 2.5%. In addition to the components contained in the steel outer skin, Mn can be added from alloy powders such as metal Mn, Fe-Mn, and Fe-Si-Mn from flux.
［鋼製外皮とフラックスの合計でＴｉ：０．１〜０．３％］
Ｔｉは、脱酸剤として作用するとともに、溶接金属中にＴｉの微細酸化物を生成し溶接金属の靭性をより向上させる。Ｔｉが０．１％未満であると、溶接金属の靭性が低下する。一方、Ｔｉが０．３％を超えると、スラグ生成量が多くなってスラグ巻き込み欠陥が生じやすくなる。また、溶接金属中に靭性を阻害するＴｉＣが析出し、靭性が低下する。従って、鋼製外皮とフラックスの合計でＴｉは０．１〜０．３％とする。なお、Ｔｉは、鋼製外皮に含まれる成分の他、フラックスからの金属Ｔｉ、Ｆｅ−Ｔｉ等の合金粉から添加できる。
[Total of steel outer skin and flux Ti: 0.1 to 0.3%]
Ti acts as a deoxidizer and forms fine oxides of Ti in the weld metal to further improve the toughness of the weld metal. If Ti is less than 0.1%, the toughness of the weld metal decreases. On the other hand, when Ti exceeds 0.3%, the amount of slag generated increases and slag entrainment defects are likely to occur. In addition, TiC that inhibits toughness is deposited in the weld metal, and the toughness is lowered. Therefore, the total of the steel outer skin and the flux is set to 0.1 to 0.3%. In addition to the components contained in the steel outer skin, Ti can be added from alloy powders such as metal Ti and Fe-Ti from flux.
［鋼製外皮とフラックスの合計でＡｌ及びＭｇの一方または両方の合計：０．０８超〜０．２５％］
Ａｌ及びＭｇは、強脱酸剤であり固形裏当材を用いた片面溶接の初層溶接でのブローホール発生を抑える。また、溶接金属の酸素量を低減して靭性を高める効果がある。Ａｌ及びＭｇの一方または両方の合計が０．０８％以下であると、固形裏当材を用いた片面溶接の初層溶接でブローホールが生じやすくなる。一方、Ａｌ及びＭｇの一方または両方の合計が０．２５％を超えると、アークが不安定になりスパッタ発生量が多くなる。従って、Ａｌ及びＭｇの一方または両方の合計は０．０８超〜０．２５％とする。なお、Ａｌは、鋼製外皮に含まれる成分の他、金属Ａｌ、Ｆｅ−Ａｌ、Ａｌ−Ｍｇ等から、Ｍｇは、鋼製外皮に含まれる成分の他、金属Ｍｇ、Ａｌ−Ｍｇ等から添加できる。
[Total of steel outer skin and flux: Total of one or both of Al and Mg: Over 0.08 to 0.25%]
Al and Mg are strong deoxidizers and suppress the occurrence of blow holes in the first layer welding of single-sided welding using a solid backing material. It also has the effect of reducing the amount of oxygen in the weld metal and increasing toughness. When the total of one or both of Al and Mg is 0.08% or less, blow holes are likely to occur in the initial layer welding of single-sided welding using the solid backing material. On the other hand, if the total of one or both of Al and Mg exceeds 0.25%, the arc becomes unstable and the amount of spatter generated increases. Therefore, the total of one or both of Al and Mg is set to more than 0.08 to 0.25%. Al is added from metals Al, Fe-Al, Al-Mg, etc. in addition to the components contained in the steel outer skin, and Mg is added from metals Mg, Al-Mg, etc. in addition to the components contained in the steel outer skin. it can.
［フラックス中に含有する金属弗化物のＦ換算値の合計：０．００５〜０．０５０％］
金属弗化物は、アークを集中させて安定させる効果がある。金属弗化物のＦ換算値の合計が０．００５％未満では、この効果が得られず、アークが不安定でスパッタ発生量が多くなる。一方、金属弗化物のＦ換算値の合計が０．０５０％を超えると、アークが荒く不安定になり、スパッタ発生量が多くなる。従って、フラックス中に含有する金属弗化物のＦ換算値の合計は０．００５〜０．０５０％とする。なお、金属弗化物は、フラックスからのＣａＦ2、ＮａＦ、ＬｉＦ、ＭｇＦ2、Ｋ2ＳｉＦ6、Ｋ2ＺｒＦ6、Ｎａ3ＡｌＦ6、ＡｌＦ3等から添加でき、Ｆ換算値はそれらに含有されるＦ量の合計である。
[Total F-converted value of metal fluoride contained in flux: 0.005 to 0.050%]
Metal fluoride has the effect of concentrating and stabilizing the arc. If the total F conversion value of the metal fluoride is less than 0.005%, this effect cannot be obtained, the arc is unstable, and the amount of spatter generated increases. On the other hand, when the total F conversion value of the metal fluoride exceeds 0.050%, the arc becomes rough and unstable, and the amount of spatter generated increases. Therefore, the total F-converted value of the metal fluoride contained in the flux is 0.005 to 0.050%. The metal fluoride can be added from CaF 2 , NaF, LiF, MgF 2 , K 2 SiF 6 , K 2 ZrF 6 , Na 3 AlF 6 , AlF 3, etc. from the flux, and the F conversion value is contained in them. It is the total amount of F.
［フラックス中に含有するＮａ酸化物、Ｎａ弗化物、Ｋ酸化物及びＫ弗化物の１種または２種以上：Ｎａ換算値とＫ換算値の合計０．０１〜０．１０％］
Ｎａ酸化物、Ｎａ弗化物、Ｋ酸化物及びＫ弗化物は、アークをソフトにして安定にする。Ｎａ酸化物、Ｎａ弗化物、Ｋ酸化物及びＫ弗化物の１種または２種以上のＮａ換算値とＫ換算値の合計が０．０１％未満であると、アークが不安定になりスパッタ発生量が多くなる。一方、Ｎａ酸化物、Ｎａ弗化物、Ｋ酸化物及びＫ弗化物１種または２種以上のＮａ換算値とＫ換算値の合計が０．１０％を超えると、アークが強くなりすぎ、スパッタ発生量が多くなる。また、ビード止端部のなじみが悪くなり、ビード外観・形状が不良となる。従って、フラックス中に含有するＮａ酸化物、Ｎａ弗化物、Ｋ酸化物及びＫ弗化物の１種または２種以上のＮａ換算値とＫ換算値の合計は０．０１〜０．１０％とする。なお、Ｎａ酸化物、Ｎａ弗化物、Ｋ酸化物及びＫ弗化物は、珪酸ソーダ及び珪酸カリウムからなる水ガラスの固質酸化物成分、ＮａＦ、Ｋ2ＳｉＦ6、Ｋ2ＺｒＦ6、Ｎａ3ＡｌＦ6等の弗化物の粉末から添加できる。
[One or more of Na oxide, Na fluoride, K oxide and K fluoride contained in the flux: 0.01 to 0.10% of the total of Na conversion value and K conversion value]
Na oxides, Na fluorides, K oxides and K fluorides soften and stabilize the arc. If the sum of the Na-equivalent value and the K-equivalent value of one or more of Na oxide, Na fluoride, K oxide and K fluoride is less than 0.01%, the arc becomes unstable and spatter occurs. The amount will increase. On the other hand, if the sum of the Na conversion value and the K conversion value of one or more Na oxides, Na fluorides, K oxides and K fluorides exceeds 0.10%, the arc becomes too strong and spatter occurs. The amount will increase. In addition, the fit of the toe of the bead becomes poor, and the appearance and shape of the bead become poor. Therefore, the sum of the Na-equivalent value and the K-equivalent value of one or more kinds of Na oxide, Na fluoride, K oxide and K fluoride contained in the flux is 0.01 to 0.10%. .. In addition, Na oxide, Na fluoride, K oxide and K fluoride are solid oxide components of water glass composed of sodium silicate and potassium silicate, NaF, K 2 SiF 6 , K 2 ZrF 6 , Na 3 AlF. It can be added from fluoride powder of 6 mag.
［フラックス中に含有するＳｉＯ2：０．２０％以下］
ＳｉＯ2は、微量でビード止端部のなじみを良好にするが、フラックス中のＳｉＯ2が０．２０％を超えると、溶接金属中の酸素量が増加して靭性が低下する。また、スラグ量が多くなり、スラグ巻込み等の溶接欠陥が発生しやすくなる。従って、フラックス中に含有するＳｉＯ2は０．２０％以下とする。なお、ＳｉＯ2は、フラックスから珪酸ソーダ及び珪酸カリウムからなる水ガラスの固質成分等から微量添加されるが、ＳｉＯ2は必須の成分ではなく、含有量が０％でもよい。
[SiO 2 : contained in flux: 0.20% or less]
SiO 2 is to improve the conformability of the bead toe portion in trace amounts, the SiO 2 in the flux is more than 0.20%, the amount of oxygen in the weld metal is toughness is lowered increases. In addition, the amount of slag increases, and welding defects such as slag entrainment are likely to occur. Therefore, the SiO 2 contained in the flux is set to 0.20% or less. Incidentally, SiO 2 is added small amount from the solid matter component of the water glass consisting of sodium silicate and potassium silicate from the flux etc., SiO 2 is not an essential component, the content may be 0%.
［鋼製外皮とフラックスの合計でＢ：０．００２〜０．０１０％］
Ｂは、高電流及び大入熱・高パス間温度での溶接施工条件での溶接金属の組織を微細化して靭性を向上させる。Ｂが０．００２％未満であると、その効果が得られず、高電流及び大入熱・高パス間温度での溶接施工条件で溶接金属の靭性向上の効果が得られない。一方、Ｂが０．０１０％を超えると、溶接金属の強度が過剰に高くなると共に、粒界が脆化して靭性が低下する。また、高温割れが生じるようになる。従って、鋼製外皮とフラックスの合計でＢは０．００２〜０．０１０％とする。なお、Ｂは、鋼製外皮に含まれる成分の他、Ｆｅ−Ｓｉ−Ｂ、Ｆｅ−Ｍｎ−Ｂ等の合金粉から添加できる。
[Total of steel outer skin and flux B: 0.002 to 0.010%]
B improves the toughness by refining the structure of the weld metal under welding construction conditions at a high current, a large heat input, and a high interpass temperature. If B is less than 0.002%, the effect cannot be obtained, and the effect of improving the toughness of the weld metal cannot be obtained under welding construction conditions at a high current and a large heat input / high interpass temperature. On the other hand, when B exceeds 0.010%, the strength of the weld metal becomes excessively high, the grain boundaries become brittle, and the toughness decreases. In addition, high temperature cracking will occur. Therefore, the total of the steel outer skin and the flux is set to 0.002 to 0.010%. In addition to the components contained in the steel outer skin, B can be added from alloy powders such as Fe-Si-B and Fe-Mn-B.
［鋼製外皮とフラックスの合計でＭｏ：０．１５〜０．５０％］
Ｍｏは、大入熱・高パス間温度の溶接施工条件で、溶接金属の強度を確保するうえで重要な元素である。Ｍｏが０．１５％未満であると、これらの効果が十分に得られず、大入熱・高パス間温度での溶接施工条件で溶接金属の必要な強度が得られない。一方、Ｍｏが０．５０％を超えると、溶接金属の強度が過剰に高くなり、靭性が安定して得られない。従って、鋼製外皮とフラックスの合計でＭｏは０．１５〜０．５０％とする。なお、Ｍｏは、鋼製外皮に含まれる成分の他、フラックスからの金属Ｍｏ粉から添加できる。
[Total of steel outer skin and flux Mo: 0.15 to 0.50%]
Mo is an important element for ensuring the strength of the weld metal under welding construction conditions with large heat input and high interpass temperature. If Mo is less than 0.15%, these effects cannot be sufficiently obtained, and the required strength of the weld metal cannot be obtained under welding construction conditions at a large heat input and a high interpass temperature. On the other hand, when Mo exceeds 0.50%, the strength of the weld metal becomes excessively high, and the toughness cannot be stably obtained. Therefore, the total Mo of the steel outer skin and the flux is 0.15 to 0.50%. In addition to the components contained in the steel outer skin, Mo can be added from the metal Mo powder from the 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は、鋼製外皮をパイプ状に成型し、その内部にフラックスを充填した構造である。ワイヤの種類としては、成形した鋼製外皮の合わせ目を溶接して得られる鋼製外皮に継目の無いワイヤと、鋼製外皮に合わせ目の溶接を行わないままとした鋼製外皮に継目を有するワイヤとに大別できる。本発明においては、何れの断面構造のワイヤを採用することができるが、鋼製外皮に継目を有するワイヤは、溶接金属の強度が高くなると低温割れが生じやすくなるので水分含有量の少ない原材料を用いる必要がある。一方、鋼製外皮に継目が無いワイヤは、ワイヤ中の全水素量を低減することを目的とした熱処理が可能であり、また製造後のフラックスの吸湿が無いため、溶接金属の拡散性水素量を低減し、耐低温割れ性の向上を図ることができる。さらに、鋼製外皮に継目が無いワイヤは、ワイヤ表面にＣｕめっきを施すことができ防錆及びワイヤ送給性の向上からも、より好ましい。 The flux-cored wire for gas shielded arc welding of the present invention has a structure in which a steel outer skin is molded into a pipe shape and the inside thereof is filled with flux. As for the types of wires, seamless wires are used for the steel outer skin obtained by welding the seams of the molded steel outer skin, and seams are used for the steel outer skin without welding the seams to the steel outer skin. It can be roughly divided into the wires it has. In the present invention, a wire having any cross-sectional structure can be adopted, but a wire having a seam on a steel outer skin is a raw material having a low water content because low-temperature cracking is likely to occur as the strength of the weld metal increases. Need to be used. On the other hand, a wire with a seamless steel outer skin can be heat-treated for the purpose of reducing the total amount of hydrogen in the wire, and since there is no moisture absorption of flux after production, the amount of diffusible hydrogen in the weld metal Can be reduced and the low temperature cracking resistance can be improved. Further, a wire having a seamless steel outer skin is more preferable because the surface of the wire can be Cu-plated to prevent rust and improve the wire feeding property.
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残部は、鋼製外皮のＦｅ、成分調整のために添加する８％以下の鉄粉、Ｆｅ−Ｓｉ、Ｆｅ−Ｍｎ、Ｆｅ−Ｔｉ合金などの鉄合金粉のＦｅ分及び不可避的不純物である。不可避不純物については特に限定しないが、高温割れ防止の観点からＰ及びＳは、それぞれ０．０２０％以下とする。 The rest of the flux-filled wire for gas shielded arc welding of the present invention is Fe of the steel outer skin, iron powder of 8% or less added for component adjustment, and iron such as Fe-Si, Fe-Mn, and Fe-Ti alloy. Fe content of alloy powder and unavoidable impurities. The unavoidable impurities are not particularly limited, but P and S are 0.020% or less, respectively, from the viewpoint of preventing high temperature cracking.
また、フラックス充填率は特に限定しないが、生産性の観点からワイヤ全質量に対して８〜２０％とするのが好ましい。 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.
なお、シールドガスは、炭酸ガスとし、シールドガスの流量は耐欠陥性及び大気からの窒素の混入を防ぐために２０〜３５リットル／分であることが好ましい。 The shield gas is carbon dioxide, and the flow rate of the shield gas is preferably 20 to 35 liters / minute in order to withstand defects and prevent nitrogen from entering the atmosphere.
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 effects of the present invention will be specifically described with reference to Examples.
ＪＩＳ Ｇ３１４１に規定されるＳＰＣＣを鋼製外皮（Ｃ：０．０１〜０．０５％）として使用し、鋼製外皮を成形する工程でＵ字型に成形した後フラックスを充填し、鋼製外皮の合わせ目を溶接した継目が無いワイヤを造管して伸線し、表１に示す各種成分のフラックス入りワイヤを試作した。ワイヤ径は１．２ｍｍとした。 SPCC specified in JIS G3141 is used as a steel outer skin (C: 0.01 to 0.05%), and after forming into a U shape in the process of forming the steel outer skin, it is filled with flux and the steel outer skin is filled. A seamless wire with welded seams was formed and drawn, and a flux-cored wire having various components shown in Table 1 was prototyped. The wire diameter was 1.2 mm.
表１に示す試作したフラックス入りワイヤを用いて、表２に示すＴ１の片面横向溶接試験で、４０°Ｖ形開先、ルートギャップ６ｍｍ、セラミックタイプの固形裏当付きの開先で横向多層盛の溶接金属試験を実施した。調査項目は溶接時の溶接作業性と溶接後Ｘ線透過試験を実施して欠陥の有無を調査した。 Using the sampled flux-cored wire shown in Table 1, in the single-sided lateral welding test of T1 shown in Table 2, a 40 ° V-shaped groove, a root gap of 6 mm, and a groove with a ceramic type solid backing were used for lateral multi-layer welding. Weld metal test was carried out. The survey items were welding workability during welding and an X-ray transmission test after welding to investigate the presence or absence of defects.
次いで、表２に示すＴ２の高電流溶接試験で、３５°レ形開先、ルートギャップ８ｍｍの裏当金付きの開先を多層盛の溶接金属試験を実施した。調査項目は溶接時のアークの安定性、ビード外観・形状、スパッタ発生量を調査した。また、溶接後板厚中央部の溶接金属部から引張試験片（ＪＩＳ Ｚ ２２０１ Ａ２号）及び衝撃試験片（ＪＩＳ Ｚ ２２０２ ４号）を採取して機械的性能を調査した。 Next, in the high-current welding test of T2 shown in Table 2, a multi-layer weld metal test was carried out on a groove with a 35 ° re-shaped groove and a backing metal with a root gap of 8 mm. The survey items were arc stability during welding, bead appearance / shape, and spatter generation amount. In addition, a tensile test piece (JIS Z 2201 A2) and an impact test piece (JIS Z 22024) were collected from the weld metal part at the center of the plate thickness after welding, and the mechanical performance was investigated.
引張強さの評価は４９０〜６９０ＭＰａ、靭性の評価は、０℃におけるシャルピー衝撃試験を各５本実施し、吸収エネルギーの平均値は８０Ｊ以上、個々の最低値は６０Ｊ以上を良好とした。それらの結果を表３にまとめて示す。 Tensile strength was evaluated at 490 to 690 MPa, and toughness was evaluated by performing five Charpy impact tests at 0 ° C., and the average value of absorbed energy was 80 J or more, and the minimum value of each was 60 J or more. The results are summarized in Table 3.
表１及び表３中のワイヤ記号１〜１０が本発明例、ワイヤ記号１１〜２０は比較例である。本発明例であるワイヤ記号１〜１０は、フラックス入りワイヤ中のＣ、Ｓｉ、Ｍｎ、Ｔｉ及びＡｌとＭｇの一方または両方の合計が適正で、フラックス中の金属弗化物のＦ換算値の合計、Ｎａ酸化物、Ｎａ弗化物、Ｋ酸化物及びＫ弗化物の１種または２種以上のＮａ換算値とＫ換算値の合計及びＳｉＯ2が適量であるので、片面横向溶接において溶接作業性が良好でＸ線透過試験においても欠陥はなかった。また、高電流溶接試験においてもアークが安定してビード外観・形状が良好で、スパッタ発生量が少なく、溶接金属の引張強さ及び吸収エネルギーの平均値及び最低値ともに良好であった。なお、ワイヤ記号１、３、４、７、９は、Ｂを適量含んでいるので吸収エネルギーの平均値及び最低値ともに高値が得られ、極めて満足な結果であった。 Wire symbols 1 to 10 in Tables 1 and 3 are examples of the present invention, and wire symbols 11 to 20 are comparative examples. In the wire symbols 1 to 10 of the examples of the present invention, the total of one or both of C, Si, Mn, Ti and Al and Mg in the flux-cored wire is appropriate, and the total of the F-converted values of the metal fluoride in the flux. , Na oxide, Na fluoride, K oxide and K fluoride, the sum of Na conversion value and K conversion value of one or more kinds and SiO 2 is an appropriate amount, so welding workability is improved in single-sided sideways welding. It was good and there were no defects in the X-ray transmission test. Further, even in the high current welding test, the arc was stable, the bead appearance and shape were good, the amount of spatter generated was small, and both the average value and the minimum value of the tensile strength and absorbed energy of the weld metal were good. Since the wire symbols 1, 3, 4, 7, and 9 contained an appropriate amount of B, high values were obtained for both the average value and the minimum value of the absorbed energy, which was an extremely satisfactory result.
比較例中ワイヤ記号１１は、Ｃが少ないので、高電流溶接での溶接金属の引張強さが低かった。また、ＳｉＯ2が多いので、スラグ生成量が多く、片面横向溶接でスラグ巻き込み欠陥が生じた。さらに、ＳｉＯ2が多いので、高電流溶接での溶接金属の吸収エネルギーが低値であった。 In the comparative example, the wire symbol 11 has a small amount of C, so that the tensile strength of the weld metal in high current welding is low. In addition, since the amount of SiO 2 is large, the amount of slag generated is large, and slag entrainment defects occur in single-sided lateral welding. Further, since the amount of SiO 2 is large, the absorbed energy of the weld metal in high current welding is low.
ワイヤ記号１２は、Ｃが多いので、高電流溶接で溶接金属の引張強さが高く吸収エネルギーが低値であった。また、クレータ部に割れが生じた。さらに、Ａｌ及びＭｇの一方または両方の合計が多いので、片面横向溶接及び鋼電流溶接ともにアークが不安定でスパッタ発生量が多かった。 Since the wire symbol 12 has a large amount of C, the tensile strength of the weld metal is high and the absorbed energy is low in high current welding. In addition, cracks occurred in the crater portion. Further, since the total of one or both of Al and Mg is large, the arc is unstable and the amount of spatter generated is large in both single-sided lateral welding and steel current welding.
ワイヤ記号１３は、Ｓｉが少ないので、高電流溶接で溶接金属の引張強さが低く吸収エネルギーも低値であった。また、Ａｌ及びＭｇの一方または両方の合計が少ないので、片面横向溶接でブローホールが生じ、高電流溶接で溶接金属の吸収エネルギーを向上する効果は得られなかった。さらに、金属弗化物のＦ換算値の合計が少ないので、片面横向溶接及び高電流溶接ともにアークが不安定でスパッタ発生量が多かった。 Since the wire symbol 13 contains a small amount of Si, the tensile strength of the weld metal is low and the absorbed energy is also low in high current welding. Further, since the total of one or both of Al and Mg is small, blowholes are generated in the one-sided lateral welding, and the effect of improving the absorbed energy of the weld metal in the high current welding cannot be obtained. Further, since the total F conversion value of the metal fluoride is small, the arc is unstable and the amount of spatter generated is large in both the single-sided sideways welding and the high current welding.
ワイヤ記号１４は、Ｓｉが多いので、スラグ生成量が多くなって片面横向溶接でスラグ巻き込み欠陥が生じた。また、Ｓｉが多いので、高電流溶接で溶接金属の引張強さが高く吸収エネルギーの最低値が低かった。さらに、金属弗化物のＦ換算値の合計が多いので、片面横向溶接及び高電流溶接ともにアークが荒く不安定でスパッタ発生量が多かった。 Since the wire symbol 14 contains a large amount of Si, the amount of slag generated is large, and slag entrainment defects occur in single-sided lateral welding. Further, since the amount of Si is large, the tensile strength of the weld metal is high and the minimum value of absorbed energy is low in high current welding. Further, since the total F conversion value of the metal fluoride is large, the arc is rough and unstable in both the single-sided sideways welding and the high current welding, and the amount of spatter generated is large.
ワイヤ記号１５は、Ｍｎが少ないので、高電流溶接で溶接金属の引張強さが低く吸収エネルギーも低値であった。また、Ｎａ酸化物、Ｎａ弗化物、Ｋ酸化物及びＫ弗化物の１種または２種以上のＮａ換算値とＫ換算値の合計が少ないので、片面横向溶接及び高電流溶接ともにアークが不安定でスパッタ発生量が多かった。 Since the wire symbol 15 has a small amount of Mn, the tensile strength of the weld metal is low and the absorbed energy is also low in high current welding. In addition, since the sum of the Na conversion value and the K conversion value of one or more types of Na oxide, Na fluoride, K oxide and K fluoride is small, the arc is unstable in both single-sided lateral welding and high current welding. The amount of spatter generated was large.
ワイヤ記号１６は、Ｍｎが多いので、スラグ生成量が多くなって片面横向溶接でスラグ巻き込み欠陥が生じた。また、Ｍｎが多いので、高電流溶接で溶接金属の吸収エネルギーの最低値が低かった。さらに、Ｎａ酸化物、Ｎａ弗化物、Ｋ酸化物及びＫ弗化物の１種または２種以上のＮａ換算値とＫ換算値の合計が多いので、片面横向溶接及び高電流溶接ともにアークが強くスパッタ発生量が多かった。また、ビード外観・形状が不良であった。 Since the wire symbol 16 has a large amount of Mn, the amount of slag generated is large, and slag entrainment defects occur in single-sided lateral welding. Further, since Mn is large, the minimum value of the absorbed energy of the weld metal is low in high current welding. Furthermore, since the sum of the Na conversion value and the K conversion value of one or more types of Na oxide, Na fluoride, K oxide and K fluoride is large, the arc is strongly sputtered in both single-sided lateral welding and high current welding. The amount generated was large. In addition, the appearance and shape of the bead were poor.
ワイヤ記号１７は、金属弗化物のＦ換算値の合計が少ないので、片面横向溶接及び高電流溶接ともにアークが不安定でスパッタ発生量が多かった。 Since the total F conversion value of the metal fluoride of the wire symbol 17 is small, the arc is unstable and the amount of spatter generated is large in both the single-sided lateral welding and the high current welding.
ワイヤ記号１８は、Ｔｉが少ないので、高電流溶接で溶接金属の吸収エネルギーが低値であった。また、Ａｌ及びＭｇの一方または両方の合計が少ないので、片面横向溶接でブローホールが生じ、高電流溶接で溶接金属の吸収エネルギーを向上する効果は得られなかった。 Since the wire symbol 18 has a small amount of Ti, the absorbed energy of the weld metal is low in high current welding. Further, since the total of one or both of Al and Mg is small, blowholes are generated in the one-sided lateral welding, and the effect of improving the absorbed energy of the weld metal in the high current welding cannot be obtained.
ワイヤ記号１９は、Ｔｉが多いので、高電流溶接で溶接金属の吸収エネルギーが低値であった。また、Ｔｉが多いので、片面横向溶接でスラグ巻き込み欠陥が生じた。さらに、Ｂが少ないので、高電流溶接で溶接金属の吸収エネルギーを良好にする効果は得られなかった。 Since the wire symbol 19 has a large amount of Ti, the absorbed energy of the weld metal is low in high current welding. In addition, since there is a large amount of Ti, a slag entanglement defect has occurred in single-sided lateral welding. Further, since B is small, the effect of improving the absorbed energy of the weld metal by high current welding could not be obtained.
ワイヤ記号２０は、Ａｌ及びＭｇの一方または両方の合計が多いので、片面横向溶接及び高電流溶接ともにアークが不安定でスパッタ発生量が多かった。また、Ｂが多いので、高電流溶接でクレータ割れが生じ、溶接金属の強度が高く吸収エネルギーが低値であった。 Since the wire symbol 20 has a large total of one or both of Al and Mg, the arc is unstable and the amount of spatter generated is large in both single-sided lateral welding and high-current welding. Further, since there is a large amount of B, crater cracking occurs in high current welding, the strength of the weld metal is high, and the absorbed energy is low.
実施例１と同様にＪＩＳ Ｇ３１４１に規定されるＳＰＣＣを鋼製外皮（Ｃ：０．０４％）として使用し、鋼製外皮を成形する工程でＵ字型に成形した後フラックスを充填し、鋼製外皮の合わせ目を溶接した継目が無いワイヤを造管して伸線し、表４に示す各種成分のフラックス入りワイヤを試作した。ワイヤ径は１．４ｍｍとした。 Similar to Example 1, SPCC specified in JIS G3141 is used as a steel outer skin (C: 0.04%), and after forming into a U shape in the step of forming the steel outer skin, it is filled with flux and steel. A seamless wire in which the seams of the outer skin were welded was formed and drawn, and a wire containing flux of various components shown in Table 4 was prototyped. The wire diameter was 1.4 mm.
表４に示す試作したフラックス入りワイヤを用いて、表２に示す条件Ｎｏ．Ｔ３の大入熱・高パス間温度溶接試験で、３５°レ開先、ルートギャップ８ｍｍの裏当金付きの開先を多層盛の溶接金属試験を実施した。調査項目は溶接時のアークの安定性、ビード外観・形状、スパッタ発生量を調査した。また、溶接後板厚中央部の溶接金属部から引張試験片（ＪＩＳ Ｚ ２２０１ Ａ２号）及び衝撃試験片（ＪＩＳ Ｚ ２２０２ ４号）を採取して機械的性能を調査した。 Using the flux-cored wire shown in Table 4, the condition No. 1 shown in Table 2 was used. In the large heat input / high pass temperature welding test of T3, a multi-layer weld metal test was carried out on a groove with a 35 ° clearance groove and a backing metal with a root gap of 8 mm. The survey items were arc stability during welding, bead appearance / shape, and spatter generation amount. In addition, a tensile test piece (JIS Z 2201 A2) and an impact test piece (JIS Z 22024) were collected from the weld metal part at the center of the plate thickness after welding, and the mechanical performance was investigated.
引張強さの評価は５２０〜７２０ＭＰａ、靭性の評価は、０℃におけるシャルピー衝撃試験を各５本実施し、吸収エネルギーの平均値は８０Ｊ以上、最低値は６０Ｊ以上を良好とした。それらの結果を表５にまとめて示す。 The tensile strength was evaluated at 520 to 720 MPa, and the toughness was evaluated by performing five Charpy impact tests at 0 ° C., and the average value of absorbed energy was 80 J or more, and the minimum value was 60 J or more. The results are summarized in Table 5.
表４及び表５中のワイヤ記号２１〜２４が本発明例、ワイヤ記号２５〜２７は比較例である。本発明例であるワイヤ記号２１〜２４は、フラックス入りワイヤ中のＣ、Ｓｉ、Ｍｎ、Ｔｉ、Ａｌ及びＭｇの一方または両方の合計及びＭｏが適正で、フラックス中の金属弗化物のＦ換算値の合計、Ｎａ酸化物、Ｎａ弗化物、Ｋ酸化物及びＫ弗化物の１種または２種以上のＮａ換算値とＫ換算値の合計及びＳｉＯ2が適量であるので、大入熱・高パス間温度の溶接施工条件においてもアークが安定してビード外観・形状が良好で、スパッタ発生量が少なく、溶接欠陥がなく、溶接金属の引張強さ及び吸収エネルギーの平均値及び最低値ともに良好であった。また、ワイヤ記号２２及び２４は、Ｂを適量含んでいるので吸収エネルギーの平均値及び最低値ともに高値が得られ、極めて満足な結果であった。 Wire symbols 21 to 24 in Tables 4 and 5 are examples of the present invention, and wire symbols 25 to 27 are comparative examples. In the wire symbols 21 to 24 of the examples of the present invention, the sum and Mo of one or both of C, Si, Mn, Ti, Al and Mg in the flux-cored wire are appropriate, and the F conversion value of the metal fluoride in the flux is appropriate. The total of Na oxide, Na fluoride, K oxide and K flux, the sum of Na conversion value and K conversion value of one or more kinds, and SiO 2 are appropriate amounts, so large heat input and high pass The arc is stable and the bead appearance and shape are good even under the welding construction conditions of inter-temperature, the amount of spatter generated is small, there are no welding defects, and the average and minimum values of the tensile strength and absorbed energy of the weld metal are both good. there were. Further, since the wire symbols 22 and 24 contained an appropriate amount of B, high values were obtained for both the average value and the minimum value of the absorbed energy, which was an extremely satisfactory result.
比較例中ワイヤ記号２５は、Ｍｏが少ないので、溶接金属の引張強さが低値であった。また、金属弗化物のＦ換算値の合計が少ないので、アークが不安定でスパッタ発生量が多かった。 In the comparative example, the wire symbol 25 had a small amount of Mo, so that the tensile strength of the weld metal was low. Further, since the total F conversion value of the metal fluoride was small, the arc was unstable and the amount of spatter generated was large.
ワイヤ記号２６は、Ｍｏが多いので、溶接金属の引張強さが高く吸収エネルギーの最低値が低かった。なお、Ｂが少ないので、溶接金属の吸収エネルギーを向上する効果は得られなかった。さらに、金属弗化物のＦ換算値の合計が多いので、アークが荒く不安定でスパッタ発生量が多かった。 Since the wire symbol 26 has a large amount of Mo, the tensile strength of the weld metal is high and the minimum value of absorbed energy is low. Since B was small, the effect of improving the absorbed energy of the weld metal could not be obtained. Further, since the total F conversion value of the metal fluoride is large, the arc is rough and unstable, and the amount of spatter generated is large.
ワイヤ記号２７は、Ｍｏが少ないので、溶接金属の引張強さが低値であった。また、Ａｌ及びＭｇの一方または両方の合計が多いので、アークが不安定でスパッタ発生量が多かった。 Since the wire symbol 27 has a small amount of Mo, the tensile strength of the weld metal was low. Further, since the total of one or both of Al and Mg is large, the arc is unstable and the amount of spatter generated is large.
Claims (3)
Ｃ：０．０４〜０．１８％、
Ｓｉ：０．１〜１．２％、
Ｍｎ：１．５〜２．５％、
Ｔｉ：０．１〜０．３％、
Ａｌ及びＭｇの一方または両方の合計：０．０８超〜０．２５％を含有し、
さらに、ワイヤ全質量に対する質量％で、フラックス中に、
金属弗化物のＦ換算値の合計：０．００５〜０．０５０％、
Ｎａ酸化物、Ｎａ弗化物、Ｋ酸化物及びＫ弗化物の１種または２種以上：Ｎａ換算値とＫ換算値の合計で０．０１〜０．１０％を含有し、
ＳｉＯ2：０．２０％以下であり、
残部は鋼製外皮のＦｅ、フラックス中の鉄粉、鉄合金からのＦｅ分及び不可避的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 a wire containing flux for gas shielded arc welding in which the steel outer skin is filled with flux, the total of the steel outer skin and the flux is the mass% of the total mass of the wire.
C: 0.04 to 0.18%,
Si: 0.1 to 1.2%,
Mn: 1.5-2.5%,
Ti: 0.1 to 0.3%,
Total of one or both of Al and Mg: Containing more than 0.08 to 0.25%,
In addition, in the flux, in mass% of the total mass of the wire,
Total F conversion value of metal fluoride: 0.005 to 0.050%,
One or more of Na oxide, Na fluoride, K oxide and K fluoride: Contains 0.01 to 0.10% in total of Na conversion value and K conversion value.
SiO 2 : 0.20% or less,
The balance is a flux-cored wire for gas shielded arc welding, which is composed of Fe of a steel outer skin, iron powder in a flux, Fe content from an iron alloy, and unavoidable impurities.
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Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2016203234A (en) * | 2015-04-28 | 2016-12-08 | 日鐵住金溶接工業株式会社 | Flux-cored wire for gas-shielded arc welding |
| JP2019058938A (en) * | 2017-09-27 | 2019-04-18 | 新日鐵住金株式会社 | Flux-cored wire for gas shield arc-welding, and manufacturing method of weld joint |
| JP2019107673A (en) * | 2017-12-19 | 2019-07-04 | 日本製鉄株式会社 | Flux-cored wire for gas shield arc welding of corrosion-resistant steel, and production method for weld joint |
| JP2020157315A (en) * | 2019-03-25 | 2020-10-01 | 日鉄溶接工業株式会社 | Flux cored wire for electro-gas arc welding |
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Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2016203234A (en) * | 2015-04-28 | 2016-12-08 | 日鐵住金溶接工業株式会社 | Flux-cored wire for gas-shielded arc welding |
| JP2019058938A (en) * | 2017-09-27 | 2019-04-18 | 新日鐵住金株式会社 | Flux-cored wire for gas shield arc-welding, and manufacturing method of weld joint |
| JP2019107673A (en) * | 2017-12-19 | 2019-07-04 | 日本製鉄株式会社 | Flux-cored wire for gas shield arc welding of corrosion-resistant steel, and production method for weld joint |
| JP2020157315A (en) * | 2019-03-25 | 2020-10-01 | 日鉄溶接工業株式会社 | Flux cored wire for electro-gas arc welding |
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| JP7244399B2 (en) | 2023-03-22 |
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