JP2017185521A - Gas shield arc welding flux-cored wire - Google Patents
Gas shield arc welding flux-cored wire Download PDFInfo
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- 238000003466 welding Methods 0.000 title claims abstract description 79
- 230000004907 flux Effects 0.000 claims abstract description 69
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 58
- 239000010959 steel Substances 0.000 claims abstract description 58
- 238000006243 chemical reaction Methods 0.000 claims description 22
- 150000001875 compounds Chemical class 0.000 claims description 20
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 20
- 239000000843 powder Substances 0.000 claims description 13
- 150000002222 fluorine compounds Chemical class 0.000 claims description 10
- 229910018072 Al 2 O 3 Inorganic materials 0.000 claims description 8
- 229910004298 SiO 2 Inorganic materials 0.000 claims description 8
- 229910010413 TiO 2 Inorganic materials 0.000 claims description 8
- 239000012535 impurity Substances 0.000 claims description 5
- 229910000640 Fe alloy Inorganic materials 0.000 claims description 3
- 229910052751 metal Inorganic materials 0.000 abstract description 110
- 239000002184 metal Substances 0.000 abstract description 110
- 229910052719 titanium Inorganic materials 0.000 abstract description 11
- 229910052782 aluminium Inorganic materials 0.000 abstract description 6
- 229910052710 silicon Inorganic materials 0.000 abstract description 6
- 229910052720 vanadium Inorganic materials 0.000 abstract description 6
- 229910052796 boron Inorganic materials 0.000 abstract description 5
- 229910052748 manganese Inorganic materials 0.000 abstract description 5
- 229910052759 nickel Inorganic materials 0.000 abstract description 4
- 229910052749 magnesium Inorganic materials 0.000 abstract description 3
- 239000010936 titanium Substances 0.000 description 36
- 239000002893 slag Substances 0.000 description 26
- 230000000694 effects Effects 0.000 description 24
- 239000011324 bead Substances 0.000 description 17
- 239000011734 sodium Substances 0.000 description 17
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N Iron oxide Chemical compound [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 description 16
- 230000007423 decrease Effects 0.000 description 16
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N titanium dioxide Inorganic materials O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 description 14
- 239000007789 gas Substances 0.000 description 11
- 229910045601 alloy Inorganic materials 0.000 description 10
- 239000000956 alloy Substances 0.000 description 10
- 238000000034 method Methods 0.000 description 6
- 239000000203 mixture Substances 0.000 description 6
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 5
- 229910052758 niobium Inorganic materials 0.000 description 5
- 239000001301 oxygen Substances 0.000 description 5
- 229910052760 oxygen Inorganic materials 0.000 description 5
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 4
- 238000002844 melting Methods 0.000 description 4
- 230000008018 melting Effects 0.000 description 4
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 3
- 229910052799 carbon Inorganic materials 0.000 description 3
- 238000005336 cracking Methods 0.000 description 3
- 238000005538 encapsulation Methods 0.000 description 3
- 238000011156 evaluation Methods 0.000 description 3
- 239000003517 fume Substances 0.000 description 3
- YDZQQRWRVYGNER-UHFFFAOYSA-N iron;titanium;trihydrate Chemical compound O.O.O.[Ti].[Fe] YDZQQRWRVYGNER-UHFFFAOYSA-N 0.000 description 3
- 235000019353 potassium silicate Nutrition 0.000 description 3
- NTHWMYGWWRZVTN-UHFFFAOYSA-N sodium silicate Chemical compound [Na+].[Na+].[O-][Si]([O-])=O NTHWMYGWWRZVTN-UHFFFAOYSA-N 0.000 description 3
- 230000006641 stabilisation Effects 0.000 description 3
- 238000011105 stabilization Methods 0.000 description 3
- 229910018134 Al-Mg Inorganic materials 0.000 description 2
- 229910018467 Al—Mg Inorganic materials 0.000 description 2
- 229910002551 Fe-Mn Inorganic materials 0.000 description 2
- 229910017082 Fe-Si Inorganic materials 0.000 description 2
- 229910017133 Fe—Si Inorganic materials 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
- 230000000052 comparative effect Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000009863 impact test Methods 0.000 description 2
- 150000004767 nitrides Chemical class 0.000 description 2
- NNHHDJVEYQHLHG-UHFFFAOYSA-N potassium silicate Chemical compound [K+].[K+].[O-][Si]([O-])=O NNHHDJVEYQHLHG-UHFFFAOYSA-N 0.000 description 2
- 229910052913 potassium silicate Inorganic materials 0.000 description 2
- 238000007665 sagging Methods 0.000 description 2
- 229910052911 sodium silicate Inorganic materials 0.000 description 2
- 230000000087 stabilizing effect Effects 0.000 description 2
- OGIDPMRJRNCKJF-UHFFFAOYSA-N titanium oxide Inorganic materials [Ti]=O OGIDPMRJRNCKJF-UHFFFAOYSA-N 0.000 description 2
- 229910016569 AlF 3 Inorganic materials 0.000 description 1
- 229910004261 CaF 2 Inorganic materials 0.000 description 1
- 229910002593 Fe-Ti Inorganic materials 0.000 description 1
- 229910017116 Fe—Mo Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910001030 Iron–nickel alloy Inorganic materials 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- NJLLQSBAHIKGKF-UHFFFAOYSA-N dipotassium dioxido(oxo)titanium Chemical compound [K+].[K+].[O-][Ti]([O-])=O NJLLQSBAHIKGKF-UHFFFAOYSA-N 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 239000004576 sand Substances 0.000 description 1
- 239000000377 silicon dioxide Substances 0.000 description 1
- GROMGGTZECPEKN-UHFFFAOYSA-N sodium metatitanate Chemical compound [Na+].[Na+].[O-][Ti](=O)O[Ti](=O)O[Ti]([O-])=O GROMGGTZECPEKN-UHFFFAOYSA-N 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000003381 stabilizer Substances 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
Abstract
Description
本発明は、鋼構造物等に使用される鋼を溶接するにあたって全姿勢溶接での溶接作業性が良好であり、溶接のまま（以下、ＡＷという。）及び溶接後熱処理（溶接熱影響部の軟化、溶接部の靭性改善及び溶接残留応力の除去を目的に行われる熱処理：以下、ＰＷＨＴという。）後の強度及び低温靭性に優れた溶接金属を得るうえで好適な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 has good welding workability in all-position welding when welding steel used for steel structures and the like, and remains welded (hereinafter referred to as AW) and post-weld heat treatment (welding heat affected zone). Heat treatment for the purpose of softening, improving toughness of welds and removing welding residual stress (hereinafter referred to as PWHT)) Suitable flux shield for gas shielded arc welding to obtain weld metal with excellent strength and low temperature toughness Regarding wires.
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フラックス入りワイヤとしては、例えば、ルチール系フラックス入りワイヤや塩基性系フラックスワイヤが知られている。 As a flux cored wire used for gas shielded arc welding using steel as a material to be welded, for example, a rutile flux cored wire or a basic flux wire is known.
ルチール系フラックス入りワイヤは、溶接能率、全姿勢溶接での溶接作業性が非常に優れているので、造船、橋梁、海洋構造物、鉄骨等の広い分野で適用されている。しかし、ルチール系フラックス入りワイヤの主原料であるルチールには不純物としてＮｂ及びＶが含まれており、これらはＰＷＨＴ後の溶接金属の低温靭性を劣化させるため、ルチール系フラックス入りワイヤはＰＷＨＴ仕様の鋼構造物の溶接にはあまり適用されていなかった。 Rutile flux-cored wires have excellent welding efficiency and welding workability in all-position welding, and are therefore applied in a wide range of fields such as shipbuilding, bridges, offshore structures, and steel frames. However, rutile, which is the main raw material for rutile flux-cored wire, contains Nb and V as impurities, and these deteriorate the low-temperature toughness of the weld metal after PWHT. Therefore, the rutile flux-cored wire has PWHT specifications. It has not been applied much to the welding of steel structures.
一方、塩基性系フラックス入りワイヤは、溶接金属の酸素量が低く、ＡＷ及びＰＷＨＴ後のいずれにおいても良好な低温靭性の溶接金属が得られるが、全姿勢溶接での溶接作業性がルチール系フラックス入りワイヤに比べ劣るため、実用化が困難であった。 On the other hand, the basic flux-cored wire has a low oxygen content in the weld metal, and a good low-temperature toughness weld metal can be obtained after both AW and PWHT, but the welding workability in all-position welding is a rutile flux. Since it is inferior to the corrugated wire, it was difficult to put it to practical use.
ルチール系フラックス入りワイヤを用いて、ＰＷＨＴ後の低温靭性に優れた溶接金属を得るための技術は過去に検討されている。例えば、特許文献１には、ルチールの代わりに不純物としてのＮｂ、Ｖが非常に少ない酸化チタンを使用することにより、ＰＷＨＴ後の低温靭性に優れた溶接金属を得るという技術が開示されている。しかし、特許文献1に記載の技術では、全姿勢溶接においてのアークの安定性、ビード外観・形状、スラグ剥離性等の良好な溶接作業性が得られないという問題点があった。 Techniques for obtaining a weld metal excellent in low temperature toughness after PWHT using a rutile flux cored wire have been studied in the past. For example, Patent Document 1 discloses a technique for obtaining a weld metal having excellent low-temperature toughness after PWHT by using titanium oxide having very little Nb and V as impurities instead of rutile. However, the technique described in Patent Document 1 has a problem in that good welding workability such as arc stability, bead appearance / shape, and slag peelability in all-position welding cannot be obtained.
また、特許文献２及び特許文献３には、全ワイヤ中のＮｂ、Ｖの含有量を制限することにより、ＰＷＨＴ後の低温靭性に優れた溶接金属を得るという技術が開示されている。しかし、特許文献２及び特許文献３に記載の技術においても、特許文献１と同様、全姿勢溶接においてのアークの安定性、ビード外観・形状、スラグ剥離性等の良好な溶接作業性が得られないという問題点があった。 Patent Documents 2 and 3 disclose a technique for obtaining a weld metal having excellent low-temperature toughness after PWHT by limiting the contents of Nb and V in all wires. However, in the techniques described in Patent Document 2 and Patent Document 3, as in Patent Document 1, good welding workability such as arc stability, bead appearance / shape, and slag peelability in all-position welding can be obtained. There was no problem.
一方、特許文献４には、Ｖの含有量を適正化することでＡＷ及びＰＷＨＴ後の強度及び低温靭性に優れた溶接金属が得られるとともに、ＰＷＨＴ後の溶接金属の強度がＡＷのものより大きく低下することを抑制すること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の開示がある。しかし、この特許文献４の開示技術によれば、全姿勢溶接における溶接作業性は十分ではなく、−５０℃の低温域での強度、低温靭性はある程度確認できているものの、−６０℃のような低温域でのＡＷ及びＰＷＨＴ後の強度及び低温靭性を得ることができないという問題点があった。 On the other hand, in Patent Document 4, a weld metal excellent in strength and low-temperature toughness after AW and PWHT is obtained by optimizing the content of V, and the strength of the weld metal after PWHT is larger than that of AW. There is a disclosure of a flux-cored wire for gas shielded arc welding capable of suppressing the decrease. However, according to the technique disclosed in Patent Document 4, welding workability in all-position welding is not sufficient, and although strength and low temperature toughness in a low temperature region of −50 ° C. have been confirmed to some extent, it seems to be −60 ° C. There was a problem that the strength and low temperature toughness after AW and PWHT in a low temperature range could not be obtained.
本発明は、上述した問題点に鑑みて案出されたものであり、鋼構造物等に使用される鋼を溶接するにあたって全姿勢溶接での溶接作業性が良好であり、ＡＷ及びＰＷＨＴ後の強度及び低温靭性に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供することを目的とする。 The present invention has been devised in view of the above-mentioned problems, and has good welding workability in all-position welding when welding steel used for steel structures and the like, and after AW and PWHT. An object of the present invention is to provide a flux-cored wire for gas shielded arc welding from which a weld metal having excellent strength and low temperature toughness can be obtained.
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：０．０１〜０．０８％、Ｓｉ：０．１〜１．０％Ｍｎ：１．５〜３．０％、Ｎｉ：０．１〜３．０％、Ｔｉ：０．０１〜０．１５％、Ｂ：０．００２〜０．０１５％、Ａｌ：０．０１〜０．５％を含有し、Ｖ：０．０２０％以下、Ｎｂ：０．０１５以下であり、さらに、ワイヤ全質量に対する質量％で、フラックス中に、Ｔｉ酸化物のＴｉＯ2換算値の合計：３〜８％、 Ｓｉ酸化物のＳｉＯ2換算値の合計：０．１〜１．０％、Ａｌ酸化物のＡｌ2Ｏ3換算値の合計：０．１〜１．２％、Ｆｅ酸化物のＦｅＯ換算値の合計：０．０１〜０．２５％、Ｍｇ：０．１〜０．８％、弗素化合物のＦ換算値の合計：０．０１〜０．３０％、Ｎａ化合物のＮａ2Ｏ換算値及びＫ化合物のＫ2Ｏ換算値の１種または２種の合計：０．０５〜０．２０％を含有し、Ｚｒ酸化物のＺｒＯ2換算値の合計：０．１％以下であり、残部が、鋼製外皮のＦｅ、鉄粉、鉄合金粉のＦｅ分及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 shield 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 the steel outer shell and the flux, C: 0.01 to 0 0.08%, Si: 0.1-1.0% Mn: 1.5-3.0%, Ni: 0.1-3.0%, Ti: 0.01-0.15%, B: 0 0.002 to 0.015%, Al: 0.01 to 0.5%, V: 0.020% or less, Nb: 0.015 or less, and further, the flux in mass% with respect to the total mass of the wire. during the total of TiO 2 converted value of Ti oxides: 3-8%, the total of SiO 2 converted value of Si oxide: 0.1% to 1.0%, of the terms of Al 2 O 3 value of Al oxide Total: 0.1-1.2%, FeO equivalent value of Fe oxide: 0.01-0.25%, Mg: 0 .1～0.8%, the sum of the F converted value of the fluorine compound: 0.01 to 0.30%, of K 2 O conversion value of terms of Na 2 O values and K compounds of Na compound (s) of Total: 0.05 to 0.20%, the total of ZrO 2 converted value of the Zr oxide is 0.1% or less, and the balance is Fe of steel outer shell, iron powder, Fe of iron alloy powder It consists of minute and inevitable 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、Ｍｏ：０．０２〜０．３０％を更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 present invention provides a flux-cored wire for gas shielded arc welding, which further contains Mo: 0.02 to 0.30% in terms of mass% with respect to the total mass of the wire, in total of the steel outer sheath and 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によれば、全姿勢溶接での溶接作業性が良好であり、ＡＷ及びＰＷＨＴ後の強度及び低温靱性に優れた溶接金属が安定して得られる。従って、溶接能率の向上及び溶接部の品質向上を図ることが可能となる。 According to the flux-cored wire for gas shielded arc welding of the present invention, welding workability in all-position welding is good, and a weld metal excellent in strength and low-temperature toughness after AW and PWHT can be obtained stably. Accordingly, it is possible to improve the welding efficiency and the quality of the welded portion.
本発明者らは、ルチール系の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、全姿勢溶接での溶接作業性が良好であり、ＡＷ及びＰＷＨＴ後の強度及び低温靱性に非常に優れた溶接金属が得られるワイヤ成分組成について、種々検討を行った。 The present inventors have obtained a weld metal that is excellent in welding workability in all-position welding, and has excellent strength and low-temperature toughness after AW and PWHT with respect to a flux cored wire for gas shield arc welding of rutile type. Various studies were made on the wire component composition.
その結果、特にＶ及びＮｂの含有量を少なくすることによりＰＷＨＴ後の低温靭性を更に向上させることができることを見出した。 As a result, it was found that the low temperature toughness after PWHT can be further improved by reducing the contents of V and Nb in particular.
また、Ｃ、Ｓｉ、Ｍｎ、Ｎｉ、Ｂ、Ｔｉ、Ａｌ、ＭｇとＴｉ酸化物の含有量を適量とすることによって、ＡＷ及びＰＷＨＴ後の強度及び低温靭性に優れた溶接金属が安定して得られることを見出した。 In addition, by adjusting the contents of C, Si, Mn, Ni, B, Ti, Al, Mg and Ti oxides to appropriate amounts, a weld metal excellent in strength and low-temperature toughness after AW and PWHT can be stably obtained. I found out that
さらに、Ｃ、Ｓｉ、Ｍｎ、Ｔｉ及びＡｌとＴｉ酸化物、Ａｌ酸化物、Ｓｉ酸化物、Ｆｅ酸化物の含有量を適正量とし、さらに、Ｚｒ酸化物の含有量を制限することで、アークが安定し、特に全姿勢溶接での溶接作業性が良好となることを見出した。 Furthermore, the content of C, Si, Mn, Ti, and Al and Ti oxide, Al oxide, Si oxide, and Fe oxide is set to an appropriate amount, and further, the content of Zr oxide is limited, so that the arc Has been found to be stable, and in particular, welding workability in all-position welding is improved.
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及びその含有率と、各成分組成の限定理由とについて説明する。なお、各成分組成の含有率は、ワイヤ全質量に対する質量％で表すこととし、その質量％を表すときには単に％と記載して表すこととする。 Hereinafter, the component composition and content of the flux-cored wire for gas shielded arc welding of the present invention and the reasons for limitation of each component composition will be described. In addition, the content rate of each component composition shall be represented by the mass% with respect to the total mass of a wire, and when expressing the mass%, it shall represent only by describing as%.
［鋼製外皮とフラックスの合計でＣ：０．０１〜０．０８％］
Ｃは、溶接時にアークの安定化に寄与する効果がある。しかし、Ｃが０．０１％未満では、アークが不安定になる。一方、Ｃが０．０８％超では、Ｃが溶接金属中に過剰に歩留まることにより、ＡＷ及びＰＷＨＴ後ともに溶接金属の低温靱性が低下する。従って、鋼製外皮とフラックスの合計でＣは０．０１〜０．０８％とする。なお、Ｃは、鋼製外皮に含まれる成分の他、フラックスからの金属粉及び合金粉等から添加される。
[C: 0.01 to 0.08% in total of steel outer shell and flux]
C has an effect of contributing to arc stabilization during welding. However, if C is less than 0.01%, the arc becomes unstable. On the other hand, if C exceeds 0.08%, C is excessively yielded in the weld metal, so that the low temperature toughness of the weld metal decreases after both AW and PWHT. Therefore, C is 0.01 to 0.08% in total of the steel outer shell and the flux. In addition, C is added from the metal powder, alloy powder, etc. from a flux other than the component contained in a steel outer shell.
［鋼製外皮とフラックスの合計でＳｉ：０．１〜１．０％］
Ｓｉは、溶接時に一部が溶接スラグとなることによりビード外観や形状を良好にし、溶接作業性の向上に寄与する。しかし、Ｓｉが０．１％未満では、ビード外観や形状を良好にする効果が十分に得られない。一方、Ｓｉが１．０％超では、Ｓｉが溶接金属中に過剰に歩留まることにより、ＡＷ及びＰＷＨＴ後ともに溶接金属の低温靱性が低下する。従って、鋼製外皮とフラックスの合計でＳｉは０．１〜１．０％とする。なお、Ｓｉは、鋼製外皮に含まれる成分の他、フラックスからの金属Ｓｉ、Ｆｅ−Ｓｉ、Ｆｅ−Ｓｉ−Ｍｎ等の合金粉から添加される。
[Si: 0.1 to 1.0% in total of steel outer shell and flux]
Si improves the bead appearance and shape by partially becoming weld slag at the time of welding, and contributes to the improvement of welding workability. However, if Si is less than 0.1%, the effect of improving the bead appearance and shape cannot be obtained sufficiently. On the other hand, when Si exceeds 1.0%, Si is excessively yielded in the weld metal, so that the low temperature toughness of the weld metal decreases after both AW and PWHT. Therefore, Si is 0.1 to 1.0% in total of the steel outer shell and the flux. Si is added from alloy powders such as metal Si, Fe-Si, Fe-Si-Mn, etc. from the flux in addition to the components contained in the steel outer shell.
［鋼製外皮とフラックスの合計でＭｎ：１．５〜３．０％］
Ｍｎは、Ｓｉと同様、溶接時に一部が溶接スラグとなることによりビード外観や形状を良好にし、溶接作業性の向上に寄与する。また、Ｍｎは、溶接金属に歩留まることにより、溶接金属の強度と低温靱性を高める効果がある。しかし、Ｍｎが１．５％未満では、ビード外観や形状が不良で、ＡＷ及びＰＷＨＴ後ともに溶接金属の強度及び低温靭性が低下する。一方、Ｍｎが３．０％超では、Ｍｎが溶接金属中に過剰に歩留まり、ＡＷ及びＰＷＨＴ後ともに溶接金属の強度が過剰になることにより、かえって低温靱性が低下する。従って、Ｍｎは１．５〜３．０％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Ｆｅ−Ｍｎ、Ｆｅ−Ｓｉ−Ｍｎ等の合金粉から添加される。
[Mn: 1.5 to 3.0% in total of steel outer shell and flux]
Mn, like Si, partially becomes weld slag during welding, thereby improving the bead appearance and shape and contributing to the improvement of welding workability. Further, Mn has an effect of increasing the strength and low temperature toughness of the weld metal by yielding on the weld metal. However, if Mn is less than 1.5%, the bead appearance and shape are poor, and the strength and low temperature toughness of the weld metal decrease after AW and PWHT. On the other hand, if Mn exceeds 3.0%, Mn is excessively yielded in the weld metal, and the strength of the weld metal becomes excessive after both AW and PWHT, thereby lowering the low temperature toughness. Therefore, Mn is 1.5 to 3.0%. In addition, Mn is added from alloy powders, such as Fe-Mn from a flux, Fe-Si-Mn other than the component contained in a steel outer shell.
［鋼製外皮とフラックスの合計でＮｉ：０．１〜３．０％］
Ｎｉは、溶接金属の低温靱性を向上させる効果がある。しかし、Ｎｉが０．１％未満では、ＡＷ及びＰＷＨＴ後ともに溶接金属の低温靭性が低下する。一方、Ｎｉが３．０％超では、ＰＷＨＴ後の溶接金属の低温靭性が低下し、溶接金属に高温割れが発生し易くなる。従って、鋼製外皮とフラックスの合計でＮｉは０．１〜３．０％とする。なお、Ｎｉは、鋼製外皮に含まれる成分の他、フラックスからの金属Ｎｉ、Ｆｅ−Ｎｉ等の合金粉から添加される。
[Ni: 0.1 to 3.0% in total of steel outer shell and flux]
Ni has the effect of improving the low temperature toughness of the weld metal. However, if Ni is less than 0.1%, the low temperature toughness of the weld metal decreases after both AW and PWHT. On the other hand, if Ni exceeds 3.0%, the low temperature toughness of the weld metal after PWHT is lowered, and hot cracks are likely to occur in the weld metal. Therefore, Ni is 0.1 to 3.0% in total of the steel outer shell and the flux. Ni is added from alloy powder such as metal Ni, Fe-Ni, etc. from the flux in addition to the components contained in the steel outer shell.
［鋼製外皮とフラックスの合計でＴｉ：０．０１〜０．１５％］
Ｔｉは、溶接時にアークの安定化に寄与するとともに、その一部がＴｉ酸化物として溶接金属中に歩留まることにより、溶接金属のミクロ組織を微細化し、溶接金属の低温靱性を向上させる効果もある。しかし、Ｔｉが０．０１％未満では、これらの効果が十分に得られず、アークが不安でスパッタ発生量が多く、ＰＷＨＴ後の溶接金属の低温靭性が低下する。一方、Ｔｉが０．１５％超では、アークが安定してスパッタ発生量も少ないが、溶接金属にＴｉ酸化物が過剰に残存することにより、ＡＷ及びＰＷＨＴ後ともに低温靱性が低下する。従って、鋼製外皮とフラックスの合計でＴｉは０．０１〜０．１５％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される。
[Ti: 0.01 to 0.15% in total of steel outer shell and flux]
Ti contributes to the stabilization of the arc during welding, and part of it is retained in the weld metal as a Ti oxide, thereby making the microstructure of the weld metal finer and improving the low-temperature toughness of the weld metal. is there. However, if Ti is less than 0.01%, these effects cannot be obtained sufficiently, the arc is uneasy, the amount of spatter is large, and the low temperature toughness of the weld metal after PWHT is lowered. On the other hand, if Ti exceeds 0.15%, the arc is stable and the amount of spatter generated is small, but the Ti oxide remains excessively in the weld metal, so that the low temperature toughness decreases after both AW and PWHT. Therefore, Ti is 0.01 to 0.15% in total of the steel outer shell and the flux. Ti is added from alloy powders such as metal Ti and Fe-Ti from the flux in addition to the components contained in the steel outer shell.
［鋼製外皮とフラックスの合計でＢ：０．００２〜０．０１５％］
Ｂは、微量の添加により溶接金属のミクロ組織を微細化し、溶接金属の低温靱性を向上させる効果がある。しかし、Ｂが０．００２％未満では、この効果が十分に得られず、ＡＷ及びＰＷＨＴ後ともに溶接金属の低温靭性が低下する。一方、Ｂが０．０１５％超では、溶接金属が過度に硬化することによりＡＷ及びＰＷＨＴ後ともに低温靱性が低下する。また、溶接金属に高温割れが発生し易くなる。従って、鋼製外皮とフラックスの合計でＢは０．００２〜０．０１５％とする。なお、Ｂは、鋼製外皮に含まれる成分の他、フラックスからの金属Ｂ、Ｆｅ−Ｂ、Ｍｎ−Ｂ等の合金粉から添加される。
[B: 0.002 to 0.015% in total of steel outer shell and flux]
B has the effect of refining the microstructure of the weld metal by adding a small amount and improving the low temperature toughness of the weld metal. However, if B is less than 0.002%, this effect cannot be sufficiently obtained, and the low temperature toughness of the weld metal decreases after both AW and PWHT. On the other hand, if B exceeds 0.015%, the weld metal is excessively hardened, so that the low temperature toughness decreases after both AW and PWHT. In addition, hot cracks are likely to occur in the weld metal. Therefore, B is 0.002 to 0.015% in total of the steel outer shell and the flux. B is added from alloy powder such as metal B, Fe-B, Mn-B, etc. from the flux in addition to the components contained in the steel outer shell.
［鋼製外皮とフラックスの合計でＡｌ：０．０１〜０．５％］
Ａｌは、溶接時にＡｌ酸化物として溶接スラグに含まれることによって、溶融スラグの粘性や融点を調整し、特に立向上進溶接においては溶融メタルが垂れ落ちるのを防ぐ効果がある。しかし、Ａｌが０．０１％未満では、この効果が十分に得られず、立向上進溶接において溶融メタルが垂れ落ちる。一方、Ａｌが０．５％を超えると、酸化物として過度に溶接金属に残留してＡＷ及びＰＷＨＴ後ともに溶接金属の低温靭性が低下する。従って、鋼製外皮とフラックスの合計でＡｌは０．０１〜０．５％とする。なお、Ａｌは、鋼製外皮に含まれる成分の他、フラックスからの金属Ａｌ、Ｆｅ−Ａｌ、Ａｌ−Ｍｇ等の合金粉から添加される。
[A total of steel shell and flux: Al: 0.01 to 0.5%]
Al is contained in the welding slag as an Al oxide during welding, thereby adjusting the viscosity and melting point of the molten slag, and has an effect of preventing the molten metal from dripping particularly in the vertical improvement welding. However, if the Al content is less than 0.01%, this effect cannot be obtained sufficiently, and the molten metal drips in the vertical improvement welding. On the other hand, when Al exceeds 0.5%, the low-temperature toughness of the weld metal is lowered after AW and PWHT due to excessively remaining in the weld metal as an oxide. Therefore, Al is 0.01 to 0.5% in total of the steel outer shell and the flux. Al is added from the alloy powder such as metal Al, Fe—Al, Al—Mg, etc. from the flux in addition to the components contained in the steel outer shell.
［鋼製外皮とフラックスの合計でＶ：０．０２０％以下］
Ｖは、ＰＷＨＴにより溶接金属中にＶ炭化物やＶ窒化物を形成し、特にＰＷＨＴ後の溶接金属の低温靱性を低下させる元素である。Ｖが０．０２０％以下であれば、溶接金属の低温靭性について許容できる範囲となる。従って、鋼製外皮とフラックスの合計でＶは０．０２０％以下とする。なお、Ｖは、鋼製外皮に含まれる成分の他、フラックス中のルチール、チタンスラグ、イルメナイト等のＴｉ酸化物に微量含まれるので、鋼製外皮及び酸化物から厳選したものを用いる。
[Total of steel outer shell and flux V: 0.020% or less]
V is an element that forms V carbide or V nitride in the weld metal by PWHT, and particularly lowers the low temperature toughness of the weld metal after PWHT. If V is 0.020% or less, it becomes an allowable range for the low temperature toughness of the weld metal. Therefore, V is 0.020% or less in total of the steel outer shell and the flux. V is contained in trace amounts in Ti oxides such as rutile, titanium slag, ilmenite, etc. in addition to the components contained in the steel outer shell, so that V is carefully selected from the steel outer shell and oxide.
［鋼製外皮とフラックスの合計でＮｂ：０．０１５％以下］
Ｎｂは、ＰＷＨＴにより溶接金属中にＮｂ炭化物やＮｂ窒化物を形成し、特にＰＷＨＴ後の溶接金属の低温靱性を低下させる元素である。Ｎｂが０．０１５％以下であれば、溶接金属の低温靭性について許容できる範囲となる。従って、鋼製外皮とフラックスの合計でＮｂは０．０１５％以下とする。なお、Ｎｂは、鋼製外皮に含まれる成分の他、フラックスからのルチール、チタンスラグ及びイルメナイト等のＴｉ酸化物に微量含まれるので、鋼製外皮及び酸化物から厳選したものを用いる。
[Nb: 0.015% or less in total of steel outer shell and flux]
Nb is an element that forms Nb carbide or Nb nitride in the weld metal by PWHT, and particularly lowers the low temperature toughness of the weld metal after PWHT. If Nb is 0.015% or less, it becomes an allowable range for the low temperature toughness of the weld metal. Therefore, Nb is set to 0.015% or less in total of the steel outer shell and the flux. In addition, since Nb is contained in trace amounts in Ti oxides such as rutile, titanium slag, and ilmenite from the flux in addition to the components contained in the steel outer shell, Nb is carefully selected from the steel outer shell and oxide.
［フラックス中のＴｉ酸化物のＴｉＯ2換算値の合計：３〜８％］
Ｔｉ酸化物は、溶接時にアークの安定化に寄与するとともに、溶接時に溶接スラグとなることにより溶接ビードの形状を良好にし、溶接作業性の向上に寄与する効果がある。また、Ｔｉ酸化物は、その一部が溶接金属中に歩留まることにより、溶接金属のミクロ組織を微細化し、溶接金属の低温靱性を向上させる効果もある。また、Ｔｉ酸化物は、立向上進溶接において、溶接スラグにＴｉ酸化物として含まれることによって溶融スラグの粘性や融点を調整し、溶融メタルが垂れるのを防ぐ効果がある。しかし、Ｔｉ酸化物のＴｉＯ2換算値の合計が３％未満では、これらの効果が十分に得られず、アークが不安定で、スパッタ発生量が多くビード外観及び形状が劣化し、ＰＷＨＴ後の溶接金属の低温靭性も低下する。また、立向上進溶接において溶融メタルが垂れて溶接の継続が困難になる。一方、Ｔｉ酸化物のＴｉＯ2換算値の合計が８％超では、アークが安定してスパッタ発生量も少ないが、溶接金属にＴｉ酸化物が過剰に残存することにより、ＡＷ及びＰＷＨＴ後ともに低温靱性が低下する。従って、フラックス中のＴｉ酸化物のＴｉＯ2換算値の合計は３〜８％とする。なお、Ｔｉ酸化物は、フラックスからのルチール、酸化チタン、チタンスラグ、イルメナイト等から添加される。
[Total of TiO 2 converted values of Ti oxide in flux: 3 to 8%]
Ti oxide contributes to the stabilization of the arc during welding and also has the effect of improving the welding workability by making the shape of the weld bead good by forming a welding slag during welding. Moreover, Ti oxide has the effect of making the microstructure of a weld metal finer and improving the low-temperature toughness of the weld metal by partially retaining the weld metal in the weld metal. Further, Ti oxide has an effect of preventing the molten metal from dripping by adjusting the viscosity and melting point of the molten slag by being contained in the weld slag as Ti oxide in the vertical welding. However, if the total TiO 2 conversion value of the Ti oxide is less than 3%, these effects cannot be sufficiently obtained, the arc is unstable, the spatter generation amount is large, the bead appearance and the shape are deteriorated, and the PWHT is deteriorated. The low temperature toughness of the weld metal also decreases. In addition, the molten metal drips in the vertical improvement welding, making it difficult to continue welding. On the other hand, if the total value of Ti oxide converted to TiO 2 exceeds 8%, the arc is stable and the amount of spatter generated is small, but the Ti oxide remains excessively in the weld metal, so that both the AW and PWHT are low in temperature. Toughness decreases. Therefore, the total of the TiO 2 conversion values of the Ti oxide in the flux is 3 to 8%. The Ti oxide is added from rutile, titanium oxide, titanium slag, ilmenite, etc. from the flux.
［フラックス中のＳｉ酸化物のＳｉＯ2換算値の合計：０．１〜１．０％］
Ｓｉ酸化物は、溶融スラグの粘性や融点を調整してスラグ被包性を向上させる効果がある。しかし、Ｓｉ酸化物のＳｉＯ2換算値の合計が０．１％未満では、スラグ被包性が悪くビード外観が不良となる。一方、Ｓｉ酸化物のＳｉＯ2換算値の合計が１．０％超では、溶融スラグの塩基度が低下することにより、溶接金属の酸素量が増加してＡＷ及びＰＷＨＴ後ともに低温靭性が低下する。従って、フラックス中のＳｉ酸化物のＳｉＯ2換算値の合計は０．１〜１．０％とする。なお、Ｓｉ酸化物は、フラックスからの珪砂、珪酸カリ及び珪酸ソーダ等から添加される。
[Total of SiO 2 conversion value of Si oxide in flux: 0.1 to 1.0%]
Si oxide has the effect of improving the slag encapsulation by adjusting the viscosity and melting point of the molten slag. However, if the total SiO 2 conversion value of the Si oxide is less than 0.1%, the slag encapsulation is poor and the bead appearance is poor. On the other hand, if the total SiO 2 conversion value of the Si oxide exceeds 1.0%, the basicity of the molten slag decreases, so that the oxygen content of the weld metal increases and low temperature toughness decreases after both AW and PWHT. . Therefore, the total of SiO 2 conversion values of the Si oxide in the flux is 0.1 to 1.0%. Si oxide is added from silica sand, potassium silicate, sodium silicate and the like from the flux.
［フラックス中のＡｌ酸化物のＡｌ2Ｏ3換算値の合計：０．１〜１．２％］
Ａｌ酸化物は、溶接時に溶接スラグに含まれることによって溶融スラグの粘性や融点を調整し、特に立向上進溶接における溶融メタルが垂れるのを防ぐ効果がある。しかし、Ａｌ酸化物のＡｌ2Ｏ3換算値の合計が０．１％未満では、立向上進溶接で溶融メタルが垂れる。一方、Ａｌ酸化物のＡｌ2Ｏ3換算値の合計が１．２％を超えると、溶接金属中にＡｌ酸化物が過剰に残存することにより、ＡＷ及びＰＷＨＴ後ともに低温靱性が低下する。従って、フラックス中のＡｌ酸化物のＡｌ2Ｏ3換算値の合計は０．１〜１．２％とする。なお、Ａｌ酸化物は、フラックスからのアルミナ等から添加される。
[Total of Al 2 O 3 converted values of Al oxide in flux: 0.1 to 1.2%]
Al oxide is included in the welding slag during welding, thereby adjusting the viscosity and melting point of the molten slag, and in particular, has an effect of preventing the molten metal from dripping in the vertical improvement welding. However, when the total Al 2 O 3 conversion value of the Al oxide is less than 0.1%, the molten metal drips in the vertical improvement welding. On the other hand, if the total Al 2 O 3 conversion value of the Al oxide exceeds 1.2%, the Al oxide excessively remains in the weld metal, so that the low temperature toughness decreases after AW and PWHT. Therefore, the total of Al 2 O 3 conversion values of the Al oxide in the flux is 0.1 to 1.2%. The Al oxide is added from alumina or the like from the flux.
［フラックス中のＦｅ酸化物のＦｅＯ換算値の合計：０．０１〜０．２５％］
Ｆｅ酸化物は、アークを安定させる効果がある。しかし、Ｆｅ酸化物のＦｅＯ換算値の合計が０．０１％未満では、アークが不安定となる。一方、Ｆｅ酸化物のＦｅＯ換算値の合計が０．２５％を超えると、溶接金属の酸素量が増加してＡＷ及びＰＷＨＴ後ともに低温靭性が低下する。従って、フラックス中のＦｅ酸化物のＦｅＯ換算値の合計は０．０１〜０．２５％とする。なお、Ｆｅ酸化物は、フラックスからの酸化鉄、チタンスラグ及びイルミナイト等から添加される。
[Total of FeO equivalent value of Fe oxide in flux: 0.01 to 0.25%]
Fe oxide has the effect of stabilizing the arc. However, when the total FeO equivalent value of Fe oxide is less than 0.01%, the arc becomes unstable. On the other hand, if the total FeO equivalent value of the Fe oxide exceeds 0.25%, the oxygen content of the weld metal increases and the low temperature toughness decreases after both AW and PWHT. Therefore, the total FeO equivalent value of the Fe oxide in the flux is set to 0.01 to 0.25%. The Fe oxide is added from iron oxide, titanium slag, illuminite, etc. from the flux.
［フラックス中のＭｇ：０．１〜０．８％］
Ｍｇは、強脱酸剤として機能することにより溶接金属中の酸素を低減し、溶接金属の低温靱性を高める効果がある。しかし、Ｍｇが０．１％未満では、この効果が十分に得られず、ＡＷ及びＰＷＨＴ後ともに溶接金属の低温靭性が低下する。一方、Ｍｇが０．８％超では、溶接時にアーク中で激しく酸素と反応してスパッタやヒュームの発生量が多くなる。従って、フラックス中のＭｇは０．１〜０．８％とする。なお、Ｍｇは、フラックスからの金属Ｍｇ、Ａｌ−Ｍｇ等の合金粉から添加される。
[Mg in flux: 0.1-0.8%]
Mg has the effect of reducing oxygen in the weld metal and increasing the low temperature toughness of the weld metal by functioning as a strong deoxidizer. However, if Mg is less than 0.1%, this effect cannot be sufficiently obtained, and the low temperature toughness of the weld metal decreases after both AW and PWHT. On the other hand, if Mg exceeds 0.8%, it reacts violently with oxygen in the arc during welding, and the amount of spatter and fumes generated increases. Therefore, Mg in the flux is 0.1 to 0.8%. In addition, Mg is added from alloy powders, such as metal Mg from a flux, Al-Mg.
［フラックス中の弗素化合物のＦ換算値の合計：０．０１〜０．３０％］
弗素化合物は、アークを安定させる効果がある。しかし、弗素化合物のＦ換算値の合計が０．０１％未満では、この効果が十分に得られず、アークが不安定になる。一方、弗素化合物のＦ換算値の合計が０．３０％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。また、立向上進溶接ではメタル垂れが発生しやすくなる。従って、フラックス中の弗素化合物のＦ換算値の合計は０．０１〜０．３０％とする。なお、弗素化合物は、ＣａＦ2、ＮａＦ、ＬｉＦ、ＭｇＦ2、Ｋ2ＳｉＦ6、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 fluorine compounds in flux: 0.01 to 0.30%]
The fluorine compound has an effect of stabilizing the arc. However, if the total F converted value of the fluorine compound is less than 0.01%, this effect cannot be obtained sufficiently and the arc becomes unstable. On the other hand, if the total F converted value of the fluorine compound exceeds 0.30%, the arc becomes unstable and the amount of spatter generated increases. In addition, metal sag is likely to occur in vertical improvement welding. Accordingly, the total F converted value of the fluorine compound in the flux is set to 0.01 to 0.30%. The fluorine compound can be added from CaF 2 , NaF, LiF, MgF 2 , K 2 SiF 6 , Na 3 AlF 6 , AlF 3, etc., and the F converted value is the total amount of F contained therein.
［フラックス中のＮａ化合物のＮａ2Ｏ換算値及びＫ化合物のＫ2Ｏ換算値の１種または２種以上の合計：０．０５〜０．２０％］
Ｎａ化合物及びＫ化合物は、アーク安定剤及びスラグ形成剤として作用する。しかし、Ｎａ化合物のＮａ2Ｏ換算値及びＫ化合物のＫ2Ｏ換算値の１種または２種の合計が０．０５％未満であると、アークが不安定となり、スパッタ発生量が多くなる。また、ビード形状及び外観も不良になる。一方、Ｎａ化合物のＮａ2Ｏ換算値及びＫ化合物のＫ2Ｏ換算値の１種または２種の合計が０．２０％を超えると、スラグ剥離性が不良となる。また、立向上進溶接ではメタル垂れが発生しやすくなる。従って、フラックス中のＮａ化合物のＮａ2Ｏ換算値及びＫ化合物のＫ2Ｏ換算値の１種または２種の合計は０．０５〜０．２０％とする。なお、Ｎａ化合物及びとＫ化合物は、珪酸ソーダ及び珪酸カリからなる水ガラスの固質成分、チタン酸カリウム、チタン酸ナトリウム等から添加できる。
[One or more of the sum of K 2 O conversion value of terms of Na 2 O values and K compounds of Na compounds in the flux: 0.05 to 0.20%]
Na compound and K compound act as an arc stabilizer and a slag forming agent. However, when the total of one or two of K 2 O conversion value of terms of Na 2 O values and K compounds of Na compound is less than 0.05%, the arc becomes unstable, it becomes large spatter. Also, the bead shape and appearance are poor. On the other hand, if the total of one or two of K 2 O conversion value of terms of Na 2 O values and K compounds of Na compound exceeds 0.20%, the slag removability becomes poor. In addition, metal sag is likely to occur in vertical improvement welding. Therefore, the sum of one or two of K 2 O conversion value of terms of Na 2 O values and K compounds of Na compound in the flux is set to 0.05 to 0.20%. The Na compound and the K compound can be added from a solid component of water glass composed of sodium silicate and potassium silicate, potassium titanate, sodium titanate and the like.
［フラックス中のＺｒ酸化物のＺｒＯ2換算値の合計：０．１％以下］
Ｚｒ酸化物は、Ｔｉ酸化物に微量含有する場合がある。しかし、Ｚｒ酸化物は、スラグ剥離性を不良にし、特にＺｒ酸化物のＺｒＯ2換算値の合計が０．１％を超えるとスラグ剥離性が著しく不良になる。従って、フラックス中のＺｒ酸化物のＺｒＯ2換算値の合計は０．１％以下とする。なお、Ｚｒ酸化物は、必須の成分ではなく、含有率がＺｒＯ2換算値で０％とされていてもよい。
[Total of ZrO 2 converted values of Zr oxide in flux: 0.1% or less]
Zr oxide may be contained in a small amount in Ti oxide. However, the Zr oxide makes the slag peelability poor. In particular, when the total of ZrO 2 converted values of the Zr oxide exceeds 0.1%, the slag peelability becomes extremely poor. Therefore, the total of ZrO 2 converted values of the Zr oxide in the flux is set to 0.1% or less. The Zr oxide is not an essential component, and the content may be 0% in terms of ZrO 2 .
［鋼製外皮とフラックスの合計でＭｏ：０．０２〜０．３０％］
Ｍｏは、溶接金属の強度を高める効果がある。しかし、Ｍｏが０．０２％未満では、この効果が十分に得られない。一方、Ｍｏが０．３０％超では、ＡＷ及びＰＷＨＴ後ともに溶接金属の強度が高くなりすぎ、かえって溶接金属の低温靱性が低下する。従って、鋼製外皮とフラックスの合計でＭｏを含有させる場合、その含有量は０．０２〜０．３０％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、Ｆｅ−Ｍｏ等の合金粉から添加される。
[Mo is 0.02 to 0.30% in total of steel outer shell and flux]
Mo has the effect of increasing the strength of the weld metal. However, if Mo is less than 0.02%, this effect cannot be sufficiently obtained. On the other hand, if Mo exceeds 0.30%, the strength of the weld metal becomes too high after AW and PWHT, and the low-temperature toughness of the weld metal decreases. Therefore, when Mo is contained in the total of the steel outer shell and the flux, the content is set to 0.02 to 0.30%. In addition, Mo is added from alloy powders, such as metal Mo from a flux, Fe-Mo other than the component contained in a steel outer shell.
本発明に係る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形し、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ぎ目の無いワイヤと、鋼製外皮の合わせ目の溶接を行わないままとした鋼製外皮に継ぎ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してもよい。但し、鋼製外皮に継ぎ目が無いワイヤは、ワイヤ中の水分量を低減することを目的に５００〜１０００℃での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ので、鋼製外皮に継ぎ目が無いワイヤを用いるのが好ましい。 The flux-cored wire for gas shielded arc welding according to the present invention has a structure in which a steel outer shell is formed into a pipe shape and the inside thereof is filled with flux. As for the types of wires, there are two types of wires: a seamless wire in the steel skin obtained by welding the seam of the molded steel skin, and a seam in the steel skin that is left unwelded in the steel skin. It can be roughly divided into wires. In the present invention, a wire having any cross-sectional structure may be adopted. However, a wire with a seamless steel outer sheath can be heat-treated at 500 to 1000 ° C. for the purpose of reducing the amount of moisture in the wire, and since there is no moisture absorption of the flux after manufacture, Since the amount of diffusible hydrogen can be reduced and the cold cracking resistance can be improved, it is preferable to use a wire having no seam in the steel outer sheath.
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鉄粉、Ｆｅ−Ｍｎ、Ｆｅ−Ｓｉ合金等の鉄合金粉のＦｅ分及び不可避不純物である。また、フラックス充填率は特に制限はしないが、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 balance of the flux-cored wire for gas shielded arc welding according to the present invention includes Fe in the steel outer sheath, iron powder added for component adjustment, Fe content of iron alloy powder such as Fe-Mn, Fe-Si alloy, and inevitable impurities It is. 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.
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 Ｇ ３１４１ ＳＰＣＣを使用して、表１及び表２に示す各種成分組成の鋼製外皮に継目のないワイヤ径１．２ｍｍのフラックス入りワイヤを試作した。 JIS G 3141 SPCC was used for the steel outer sheath, and a flux cored wire having a wire diameter of 1.2 mm, which was seamless with the steel outer sheath having various component compositions shown in Tables 1 and 2, was manufactured.
表１に示すフラックス入りワイヤを用いて、板厚１２ｍｍの鋼板（ＪＩＳ Ｇ ３１０６ ＳＭ４９０Ａ）をＴ継手の試験体として、表３に示す溶接作業性評価の溶接条件で立向上進溶接による溶接作業性評価を行った。また、ＪＩＳ Ｚ ３１１１に準じて、板厚２０ｍｍの鋼板（ＪＩＳ Ｇ ３１２６ ＳＬＡ３２５Ａ）を試験体として、表３に示す溶着金属試験の溶接条件で溶着金属試験を行った。 Using the flux-cored wire shown in Table 1, a 12 mm-thick steel plate (JIS G 3106 SM490A) was used as a T-joint test piece, and welding workability by standing-up advance welding under the welding conditions of welding workability evaluation shown in Table 3 Evaluation was performed. Further, in accordance with JIS Z 3111, a weld metal test was conducted under the welding conditions of the weld metal test shown in Table 3 using a steel plate having a thickness of 20 mm (JIS G 3126 SLA325A) as a test body.
立向上進溶接による溶接作業性の評価は、アークの安定性、スパッタ発生状態、ヒューム発生状態、ビード形状、ビード外観及び溶融メタル垂れ状況について調査した。 For the evaluation of welding workability by vertical welding, we investigated the arc stability, spatter generation state, fume generation state, bead shape, bead appearance and molten metal sag.
溶着金属試験は、ＡＷの溶着金属と、ＰＷＨＴ後の溶着金属とを評価対象とした。ＰＷＨＴは、６２０℃、４時間の条件で行った。溶着金属の板厚方向中央部から引張試験（Ａ１号）、衝撃試験（Ｖノッチ試験片）を採取して各試験に供した。機械的性質の評価は、ＡＷ及びＰＷＨＴ後の溶着金属について、−６０℃におけるシャルピー衝撃試験を行い、各々繰り返し３本の吸収エネルギーの平均が５０Ｊ以上、ＡＷの引張強さ（以下、ＴＳＡという。）とＰＷＨＴ後の引張強さ（以下、ＴＳＰという。）がいずれも４９０〜６５０ＭＰａのものを合格とした。これらの結果を表４にまとめて示す。 In the weld metal test, an AW weld metal and a weld metal after PWHT were evaluated. PWHT was performed at 620 ° C. for 4 hours. A tensile test (No. A1) and an impact test (V-notch test piece) were sampled from the central part of the weld metal in the plate thickness direction and used for each test. The mechanical properties were evaluated by conducting a Charpy impact test at −60 ° C. on the weld metal after AW and PWHT, and the average of the three absorbed energy was 50 J or more and the tensile strength of AW (hereinafter referred to as TSA). ) And the tensile strength after PWHT (hereinafter referred to as TSP) are 490 to 650 MPa. These results are summarized in Table 4.
表１、表２及び表４のワイヤ記号Ａ０１〜１７は本発明例、ワイヤ記号Ｂ０１〜１９は比較例である。本発明例であるワイヤ記号Ａ０１〜１７は、各成分の組成が本発明において規定した範囲内であるので、溶接作業性が良好であるとともに、溶着金属のＴＳＡ、ＴＳＰ、ＡＷ及びＰＷＨＴ後の吸収エネルギーも良好な値が得られるなど極めて満足な結果であった。 In Tables 1, 2 and 4, wire symbols A01 to A17 are examples of the present invention, and wire symbols B01 to B19 are comparative examples. Since the wire symbols A01 to 17 which are examples of the present invention have the composition of each component within the range specified in the present invention, the welding workability is good and the weld metal is absorbed after TSA, TSP, AW and PWHT. The results were extremely satisfactory, such as good energy values.
比較例中ワイヤ記号Ｂ０１は、Ｃが多いので、溶着金属のＡＷ及びＰＷＨＴ後の吸収エネルギーが低値であった。また、Ａｌが少ないで、溶融メタルに垂れが生じた。 Since the wire symbol B01 in the comparative example had a large amount of C, the absorbed energy after AW and PWHT of the weld metal was low. Moreover, since there was little Al, dripping occurred in the molten metal.
ワイヤ記号Ｂ０２は、Ｃが少ないので、アークが不安定であった。また、Ｎｉが少ないので、溶着金属のＡＷ及びＰＷＨＴ後の吸収エネルギーが低値であった。 Since the wire symbol B02 has a small amount of C, the arc is unstable. Moreover, since there is little Ni, the absorbed energy after AW of PWHT and PWHT was a low value.
ワイヤ記号Ｂ０３は、Ｓｉが多いので、溶着金属のＡＷ及びＰＷＨＴ後の吸収エネルギーが低値であった。また、Ｓｉ酸化物のＳｉＯ2換算値の合計が少ないので、スラグ被包性が悪くビード外観が不良であった。 Since the wire symbol B03 has a large amount of Si, the absorbed energy after AW and PWHT of the weld metal was low. Further, since the total of SiO 2 conversion values of the Si oxide was small, the slag encapsulation was poor and the bead appearance was poor.
ワイヤ記号Ｂ０４は、Ｓｉが少ないので、ビード外観及び形状が不良であった。また、Ｂが少ないので、溶着金属のＡＷ及びＰＷＨＴ後の吸収エネルギーが低値であった。 The wire symbol B04 had a poor bead appearance and shape because of a small amount of Si. Further, since B is small, the absorbed energy after AW and PWHT of the weld metal was low.
ワイヤ記号Ｂ０５は、Ｍｎが多いので、溶着金属のＴＳＡ及びＴＳＰが高くなり、ＡＷ及びＰＷＨＴ後の吸収エネルギーが低値であった。また、Ａｌ酸化物のＡｌ2Ｏ3換算値の合計が少ないので、溶融メタルに垂れが生じた。 Since the wire symbol B05 has a large amount of Mn, the TSA and TSP of the deposited metal were high, and the absorbed energy after AW and PWHT was low. Moreover, since the total of Al 2 O 3 conversion values of Al oxide was small, dripping occurred in the molten metal.
ワイヤ記号Ｂ０６は、Ｍｎが少ないので、ビード外観及び形状が不良であり、溶着金属のＴＳＡ及びＴＳＰが低値で、かつＡＷ及びＰＷＨＴ後の吸収エネルギーも低値であった。また、Ｍｏが少ないので、溶着金属のＴＳＡ及びＴＳＰの向上効果が得られなかった。 Since the wire symbol B06 had a small amount of Mn, the bead appearance and shape were poor, the TSA and TSP of the weld metal were low, and the absorbed energy after AW and PWHT was also low. Moreover, since there is little Mo, the improvement effect of TSA and TSP of a weld metal was not acquired.
ワイヤ記号Ｂ０７は、Ｎｉが多いので、高温割れが発生した。また、溶着金属のＰＷＨＴ後の吸収エネルギーが低値であった。さらに、Ｍｇが多いので、スパッタ及びヒュームの発生量が多かった。 Since the wire symbol B07 contains a large amount of Ni, hot cracking occurred. Moreover, the absorbed energy after PWHT of the weld metal was low. Furthermore, since there was much Mg, the amount of spatters and fumes generated was large.
ワイヤ記号Ｂ０８は、Ｔｉが多いので、溶着金属のＡＷ及びＰＷＨＴ後の吸収エネルギーが低値であった。また、弗素化合物のＦ換算値の合計が多いので、アークが不安定でスパッタ発生量が多かった。さらに、溶融メタルに垂れが生じた。 Since the wire symbol B08 has a large amount of Ti, the absorbed energy after AW and PWHT of the weld metal was low. Moreover, since the total of F converted values of the fluorine compound is large, the arc is unstable and the amount of spatter generated is large. Furthermore, dripping occurred in the molten metal.
ワイヤ記号Ｂ０９は、Ｔｉ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。また、溶着金属のＰＷＨＴ後の吸収エネルギーが低値であった。さらに、Ｚｒ酸化物のＺｒＯ2換算値の合計が多いので、スラグ剥離性が不良であった。 Since the wire symbol B09 had a small amount of Ti, the arc was unstable and the amount of spatter generated was large. Moreover, the absorbed energy after PWHT of the weld metal was low. Furthermore, since the total of ZrO 2 converted values of the Zr oxide is large, the slag peelability was poor.
ワイヤ記号Ｂ１０は、Ｂが多いので、高温割れが発生した。また、溶着金属のＡＷ及びＰＷＨＴ後の吸収エネルギーが低値であった。さらに、弗素化合物のＦ換算値の合計が少ないので、アークが不安定であった。 Since the wire symbol B10 has a large amount of B, hot cracking occurred. Moreover, the absorbed energy after AW and PWHT of the weld metal was low. Furthermore, since the total F converted value of the fluorine compound is small, the arc was unstable.
ワイヤ記号Ｂ１１は、Ａｌが多いので、溶着金属のＡＷ及びＰＷＨＴ後の吸収エネルギーが低値であった。また、Ｎａ化合物のＮａ2Ｏ換算値及びＫ化合物のＫ2Ｏ換算値の合計が多いので、メタル垂れが発生し、スラグ剥離性も不良であった。 Since the wire symbol B11 contains a large amount of Al, the absorbed energy after AW and PWHT of the weld metal was low. Further, since the sum of K 2 O conversion value of terms of Na 2 O values and K compounds of Na compound is large, the metal sagging occurs and the slag removability was also poor.
ワイヤ記号Ｂ１２は、Ｖが多いので、溶着金属のＰＷＨＴ後の吸収エネルギーが低値であった。 Since the wire symbol B12 has a large amount of V, the absorbed energy after PWHT of the weld metal was low.
ワイヤ記号Ｂ１３は、Ｎｂが多いので、溶着金属のＰＷＨＴ後の吸収エネルギーが低値であった。 Since the wire symbol B13 has a large amount of Nb, the absorbed energy after PWHT of the weld metal was low.
ワイヤ記号Ｂ１４は、Ｔｉ酸化物のＴｉＯ2換算値の合計が多いので、溶着金属のＡＷ及びＰＷＨＴ後の吸収エネルギーが低値であった。また、Ｎａ化合物のＮａ2Ｏ換算値及びＫ化合物のＫ2Ｏ換算値の合計が少ないので、アークが不安定で、ビード外観及び形状が不良であり、スパッタ発生量も多かった。 Since the wire symbol B14 has a large total of TiO 2 converted values of Ti oxide, the absorbed energy after AW and PWHT of the weld metal was low. Further, since the sum of K 2 O conversion value of terms of Na 2 O values and K compounds of Na compound is small, the arc is unstable, a bead appearance and shape defects, amount were many spatters.
ワイヤ記号Ｂ１５は、Ｔｉ酸化物のＴｉＯ2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く、ビード外観・形状も不良であり、溶融メタル垂れも生じた。また、溶着金属のＰＷＨＴ後の吸収エネルギーが低値であった。 In the wire symbol B15, since the total of TiO 2 converted values of Ti oxide was small, the arc was unstable, the amount of spatter was large, the bead appearance and shape were poor, and molten metal sagging also occurred. Moreover, the absorbed energy after PWHT of the weld metal was low.
ワイヤ記号Ｂ１６は、Ｓｉ酸化物のＳｉＯ2換算値の合計が多いので、溶着金属のＡＷ及びＰＷＨＴ後の吸収エネルギーが低値であった。 Since the wire symbol B16 has a large total of SiO 2 converted values of Si oxide, the absorbed energy after AW and PWHT of the weld metal was low.
ワイヤ記号Ｂ１７は、Ａｌ酸化物のＡｌ2Ｏ3換算値の合計が多いので、溶着金属のＡＷ及びＰＷＨＴ後の吸収エネルギーが低値であった。 Since the wire symbol B17 has a large total of Al 2 O 3 conversion values of the Al oxide, the absorbed energy after the AW and PWHT of the weld metal was low.
ワイヤ記号Ｂ１８は、Ｆｅ酸化物のＦｅＯ換算値の合計が多いので、溶着金属のＡＷ及びＰＷＨＴ後の吸収エネルギーが低値であった。 Since the wire symbol B18 had a large total of FeO equivalent values of Fe oxide, the absorbed energy after AW and PWHT of the weld metal was low.
ワイヤ記号Ｂ１９は、Ｍｇが少ないので、溶着金属のＡＷ及びＰＷＨＴ後の吸収エネルギーが低値であった。 Since the wire symbol B19 has a small amount of Mg, the absorbed energy after AW and PWHT of the weld metal was low.
ワイヤ記号Ｂ２０は、Ｆｅ酸化物のＦｅＯ換算値の合計が少ないので、アークが不安定であった。また、Ｍｏが多いので、溶着金属のＴＳＡ及びＴＳＰが高くなり、ＡＷ及びＰＷＨＴ後の吸収エネルギーが低値であった。 The wire symbol B20 had an unstable arc because the total FeO equivalent value of Fe oxide was small. Moreover, since there was much Mo, TSA and TSP of the weld metal became high, and the absorbed energy after AW and PWHT was low.
Claims (2)
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：０．０１〜０．０８％、
Ｓｉ：０．１〜１．０％
Ｍｎ：１．５〜３．０％、
Ｎｉ：０．１〜３．０％、
Ｔｉ：０．０１〜０．１５％
Ｂ：０．００２〜０．０１５％、
Ａｌ：０．０１〜０．５％を含有し、
Ｖ：０．０２０％以下、
Ｎｂ：０．０１５以下であり、
さらに、ワイヤ全質量に対する質量％で、フラックス中に、
Ｔｉ酸化物のＴｉＯ2換算値の合計：３〜８％、
Ｓｉ酸化物のＳｉＯ2換算値の合計：０．１〜１．０％、
Ａｌ酸化物のＡｌ2Ｏ3換算値の合計：０．１〜１．２％、
Ｆｅ酸化物のＦｅＯ換算値の合計：０．０１〜０．２５％
Ｍｇ：０．１〜０．８％、
弗素化合物のＦ換算値の合計：０．０１〜０．３０％、
Ｎａ化合物のＮａ2Ｏ換算値及びＫ化合物のＫ2Ｏ換算値の１種または２種の合計：０．０５〜０．２０％を含有し、
Ｚｒ酸化物のＺｒＯ2換算値の合計：０．１％以下であり、
残部が、鋼製外皮のＦｅ、鉄粉、鉄合金粉のＦｅ分及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 shield arc welding, which is formed by filling the steel outer shell with flux,
It is the mass% with respect to the total mass of the wire.
C: 0.01 to 0.08%,
Si: 0.1 to 1.0%
Mn: 1.5-3.0%
Ni: 0.1 to 3.0%,
Ti: 0.01 to 0.15%
B: 0.002 to 0.015%,
Al: 0.01 to 0.5% is contained,
V: 0.020% or less,
Nb: 0.015 or less,
Furthermore, in the flux in mass% relative to the total mass of wire
Total of TiO 2 conversion value of Ti oxide: 3 to 8%,
Total of SiO 2 conversion value of Si oxide: 0.1 to 1.0%,
Total terms of Al 2 O 3 value of Al oxide: 0.1 to 1.2%,
Total FeO equivalent value of Fe oxide: 0.01 to 0.25%
Mg: 0.1 to 0.8%
Total F converted value of fluorine compound: 0.01 to 0.30%,
One or of the sum of K 2 O conversion value of terms of Na 2 O values and K compounds of Na compound: containing 0.05 to 0.20%,
Total of ZrO 2 converted values of Zr oxide: 0.1% or less,
A flux-cored wire for gas shielded arc welding, characterized in that the balance is made of Fe of steel outer shell, iron powder, Fe content of iron alloy powder and inevitable impurities.
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| JP2019162642A (en) * | 2018-03-19 | 2019-09-26 | 日鉄溶接工業株式会社 | Flux-cored wire for hardfacing gas shield arc welding |
| KR102056637B1 (en) | 2018-01-12 | 2019-12-17 | 현대종합금속 주식회사 | Flux cored wire for gas shield |
| JP2020022990A (en) * | 2018-08-08 | 2020-02-13 | 日鉄溶接工業株式会社 | Flux-cored wire for carbonic acid gas shield arc-welding |
| JP2020121335A (en) * | 2019-01-31 | 2020-08-13 | 日鉄溶接工業株式会社 | Flux-cored wire for carbon dioxide gas shield arc welding of high tensile steel |
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| JP7175784B2 (en) | 2019-01-31 | 2022-11-21 | 日鉄溶接工業株式会社 | Flux-cored wire for carbon dioxide shielded arc welding of high-strength steel |
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