JP6309485B2 - Flux-cored wire for Ar-CO2 mixed gas shielded arc welding - Google Patents
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- 150000001336 alkenes Chemical class 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
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- NJLLQSBAHIKGKF-UHFFFAOYSA-N dipotassium dioxido(oxo)titanium Chemical compound [K+].[K+].[O-][Ti]([O-])=O NJLLQSBAHIKGKF-UHFFFAOYSA-N 0.000 description 1
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- NNHHDJVEYQHLHG-UHFFFAOYSA-N potassium silicate Chemical compound [K+].[K+].[O-][Si]([O-])=O NNHHDJVEYQHLHG-UHFFFAOYSA-N 0.000 description 1
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- 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
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- Nonmetallic Welding Materials (AREA)
Description
本発明は、耐力が６９０ＭＰａ以上の高張力鋼を溶接するにあたり、全姿勢溶接での溶接作業性が良好であり、かつ耐低温割れ性及び低温靭性等に優れる溶接金属が得られるＡｒ−ＣＯ2混合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。 In the present invention, when welding a high-strength steel having a proof stress of 690 MPa or more, Ar—CO 2 from which welding workability in all-position welding is good and a weld metal excellent in low-temperature cracking resistance and low-temperature toughness is obtained. The present invention relates to a flux-cored wire for mixed gas shielded arc welding.
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等が知られている。塩基性系フラックス入りワイヤを用いた溶接は、溶接金属の酸素量を低減できるので低温靭性は優れているものの、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て劣るので一般に用いられることが少ない。 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. Welding using basic flux-cored wire is generally used because it can reduce the oxygen content of the weld metal and has excellent low-temperature toughness, but welding workability in all-position welding is inferior to that of rutile flux-cored wire. There is little to be done.
一方、ルチール系フラックス入りワイヤを用いたガスシールドアーク溶接は、溶接能率、全姿勢溶接での溶接作業性において非常に優れた能力を発揮するため、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。 On the other hand, gas shielded arc welding using rutile flux-cored wire exhibits excellent performance in welding efficiency and welding workability in all-position welding, so it is widely used in shipbuilding, bridges, offshore structures, steel frames, etc. Applied in the field.
しかし、ルチール系フラックス入りワイヤは、ＴｉＯ2をはじめとする金属酸化物主体のフラックスが鋼製外皮中に充填されているために、溶接金属中の酸素量が多く、低温靭性を得にくい。 However, the rutile flux-cored wire has a large amount of oxygen in the weld metal and is difficult to obtain low-temperature toughness because a flux mainly composed of metal oxide such as TiO 2 is filled in the steel outer shell.
また、これらフラックス入りワイヤは、フラックス原料に含有される水分やワイヤ保管時の吸湿により、溶接金属中の拡散性水素量がソリッドワイヤに比べ高くなることから、溶接金属の低温割れが懸念され、板厚の厚い鋼板の溶接時には１００℃程度の予熱をする必要があり、溶接能率を低下させる原因となっている。 In addition, these flux-cored wires have high diffusible hydrogen content in the weld metal due to moisture contained in the flux raw material and moisture absorption during wire storage, so there is concern about cold cracking of the weld metal, At the time of welding a thick steel plate, it is necessary to preheat to about 100 ° C., which causes a reduction in welding efficiency.
０．２％耐力が６９０ＭＰａ以上の高張力鋼溶接用ルチール系フラックス入りワイヤについては、これまで種々の開発が進められている。例えば、特許文献１には、全姿勢溶接が可能で、耐割れ性に優れ、かつ低温靭性が良好な耐力６９０ＭＰａ以上の高強度鋼溶接用フラックス入りワイヤが開示されている。しかし、特許文献１の開示技術は、Ｃ、Ｂ、Ｓｉ、Ｍｎ、Ｎｉ、Ｃｒ等の合金成分を最適化することにより低温靭性を得る技術であり、金属酸化物の添加量の適正化により低温靭性の向上を図る点については特段考慮されていない。 Various developments have so far been made on a high-strength steel-welded rutile flux cored wire having a 0.2% proof stress of 690 MPa or more. For example, Patent Literature 1 discloses a flux-cored wire for welding high-strength steel having a proof stress of 690 MPa or more that can be welded in all positions, has excellent crack resistance, and has low temperature toughness. However, the technique disclosed in Patent Document 1 is a technique for obtaining low temperature toughness by optimizing alloy components such as C, B, Si, Mn, Ni, Cr, etc., and low temperature by optimizing the addition amount of metal oxide. No particular consideration is given to the improvement of toughness.
また特許文献２には、スラグ剤に弗素化合物を使用することにより、溶接金属中の酸素量を低減させて低温靭性を向上させる技術が開示されている。しかし、特許文献１の開示技術と同じく、スラグ剤中の金属酸化物の適正化による低温靭性向上については考慮されていない。 Patent Document 2 discloses a technique for improving the low temperature toughness by reducing the amount of oxygen in the weld metal by using a fluorine compound as the slag agent. However, as with the technology disclosed in Patent Document 1, no consideration is given to improving low-temperature toughness by optimizing the metal oxide in the slag agent.
また特許文献３には、低温靭性が優れる溶接金属を得る技術が開示されているが、溶接金属中の酸素量を低減するために添加されているＭｇＯは、溶接時にアークを不安定にしてスパッタ発生量を増加させるなど溶接作業性が不良となる。また特許文献３の開示技術では、耐低温割れ性については考慮されていない。 Patent Document 3 discloses a technique for obtaining a weld metal with excellent low-temperature toughness, but MgO added to reduce the amount of oxygen in the weld metal makes the arc unstable during welding and causes sputtering. Welding workability becomes poor by increasing the amount of generation. In addition, the disclosed technology disclosed in Patent Document 3 does not consider cold crack resistance.
さらに、特許文献４には、ワイヤ中のＮｂ、Ｖ及びＰの量を制限して、溶接のまま及び溶接後熱処理のいずれにおいても低温靭性に優れる溶接金属を得る技術が開示されている。しかし、特許文献４に記載の技術においても、全姿勢溶接時の溶接作業性は十分ではないという問題があった。 Further, Patent Document 4 discloses a technique for limiting the amounts of Nb, V, and P in a wire to obtain a weld metal that is excellent in low temperature toughness as it is in welding and in heat treatment after welding. However, the technique described in Patent Document 4 also has a problem that the welding workability at the time of all-position welding is not sufficient.
そこで本発明は、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０．２％耐力６９０ＭＰａ以上の高張力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、かつ、耐低温割れ性及び低温靭性に優れる溶接金属を得ることができるＡｒ−ＣＯ2混合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-mentioned problems, and welding work in all-position welding is performed when welding high-tensile steel with 0.2% proof stress of 690 MPa or more used for steel structures and the like. It is an object of the present invention to provide a flux-cored wire for Ar—CO 2 mixed gas shielded arc welding, which can obtain a weld metal having good properties and excellent cold cracking resistance and low temperature toughness.
本発明者らは、０．２％耐力が６９０ＭＰａ以上の高張力鋼用のルチール系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、−４０℃での靭性が安定して得られ、かつ、耐低温割れ性に優れた溶接金属を得るべく、種々検討を行った。 The present inventors have good welding workability in all-position welding with respect to a flux cored wire for high-strength steel having a 0.2% proof stress of 690 MPa or more and welding at all positions, and at −40 ° C. Various studies were conducted in order to obtain a weld metal that has stable toughness and excellent cold cracking resistance.
その結果、ＴｉＯ2を主成分とした金属酸化物の添加量の適正化や、Ｎａ及びＫを含む弗素化合物からなるスラグ成分と最適な合金成分及び脱酸剤を含む化学成分とすることによって、全姿勢における溶接作業性が良好で、高強度でありながら低温靭性に優れた溶接金属を得ることができ、さらに、鋼製外皮の継目を無くすことにより、耐低温割れ性を改善できることを見出した。 As a result, by optimizing the addition amount of the metal oxide mainly composed of TiO 2 , and by making it a chemical component including a slag component composed of a fluorine compound containing Na and K, and an optimal alloy component and deoxidizer, We found that weld metal with good welding workability in all positions, high strength and excellent low-temperature toughness can be obtained, and further, by eliminating the joint of the steel outer shell, the cold crack resistance can be improved. .
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Ａｒ−ＣＯ2混合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：０．０２〜０．０９％、Ｓｉ：０．２〜０．６％、Ｍｎ：１．５〜３．３％、Ｎｉ：１．５〜３．５％、Ｍｏ：０．２１〜０．５％、Ｔｉ：０．０１〜０．１％、Ｂ：０．００２〜０．０１５％を含有し、Ａｌ：０．０５％以下、Ｎｂ：０．０１５％以下、Ｖ：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：０．１〜０．５％、Ｍｇ：０．３〜０．８％、弗素化合物のＦ換算値の合計：０．０５〜０．５％、弗素化合物中におけるＮａ及びＫのＮａ換算値及びＫ換算値の１種または２種の合計：０．０５〜０．２％、Ｎａ2Ｏ及びＫ2Ｏの１種または２種の合計：０．０５〜０．２％を含有し、Ｚｒ酸化物のＺｒＯ2換算値の合計：０．２％以下、Ａｌ酸化物のＡｌ2Ｏ3換算値の合計：０．１％以下であり、残部は鋼製外皮の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。 That is, the gist of the present invention is the flux-cored wire for Ar-CO 2 mixed gas shielded arc welding in which the steel outer shell is filled with flux, in mass% with respect to the total mass of the wire, and the total of the steel outer shell and the flux, C: 0.02-0.09%, Si: 0.2-0.6%, Mn: 1.5-3.3%, Ni: 1.5-3.5%, Mo: 0.21- 0.5%, Ti: 0.01 to 0.1%, B: 0.002 to 0.015%, Al: 0.05% or less, Nb: 0.015% or less, V: 0.0. 015% or less, and further, in mass% with respect to the total mass of the wire, in the flux, the total of TiO 2 conversion value of Ti oxide: 3 to 8%, the total of SiO 2 conversion value of Si oxide: 0.1 -0.5%, Mg: 0.3-0.8%, the total of F converted values of fluorine compounds: 0.05-0. %, Of one or of the sum of the Na converted value and K converted value of Na and K in the fluorine compound: 0.05% to 0.2%, the total of one or Na 2 O and K 2 O : contains 0.05% to 0.2%, the total of ZrO 2 conversion value of Zr oxide: 0.2% or less, the total in terms of Al 2 O 3 value of Al oxide: Yes 0.1% or less The remainder is characterized by being composed of Fe of steel outer shell, iron powder, Fe content of iron alloy powder and inevitable impurities.
また、成形した鋼製外皮の合わせ目を溶接することで鋼製外皮に継目を無くし、さらに、ワイヤ表面に送給潤滑剤をワイヤ１０ｋｇ当り０．０５〜１．５０ｇ有することも特徴とするＡｒ−ＣＯ2混合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。 In addition, the welded seam of the formed steel skin is welded to eliminate the seam of the steel skin, and the wire lubricant is further provided with 0.05 to 1.50 g of feed lubricant per 10 kg of wire. in -CO 2 mixed gas shielded arc welding flux cored wire.
本発明のＡｒ−ＣＯ2混合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、また、０．２％耐力が６９０ＭＰａ以上の高強度で−４０℃における靭性が良好で、耐低温割れ性が優れた溶接金属が得られるなど、溶接能率及び溶接部の品質の向上を図ることが可能である。 According to the flux-cored wire for Ar—CO 2 mixed gas shielded arc welding of the present invention, the welding workability in all positions welding is good, and the 0.2% proof stress is 690 MPa or more at a high strength of −40 ° C. It is possible to improve the welding efficiency and the quality of the welded part, for example, by obtaining a weld metal having good toughness and low-temperature cracking resistance.
以下、本発明のＡｒ−ＣＯ2混合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量と、各成分組成の限定理由について説明する。なお、各成分組成の含有量は、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 Ar—CO 2 mixed gas shielded arc welding of the present invention and the reasons for limitation of each component composition will be described. The content of each component composition is expressed by mass% with respect to the total mass of the wire. When expressing the mass%, it is simply expressed as%.
［鋼製外皮とフラックスの合計でＣ：０．０２〜０．０９％］
Ｃは、溶接時にアークの安定化に寄与するとともに、溶接金属の強度向上の効果がある。しかし、Ｃが０．０２％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とともに、必要な溶接金属の強度が得られない。一方、Ｃが０．０９％を超えると、Ｃが溶接金属中に過剰に歩留まることにより、溶接金属の強度が過剰に高くなり、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０．０２〜０．０９％とする。なお、Ｃは、鋼製外皮に含まれる成分の他、フラックスから鉄粉及び鉄合金粉等から添加できる。
[C: 0.02 to 0.09% in total of steel outer shell and flux]
C contributes to the stabilization of the arc during welding and has the effect of improving the strength of the weld metal. However, if C is less than 0.02%, this effect cannot be obtained sufficiently, the arc becomes unstable, and the required weld metal strength cannot be obtained. On the other hand, when C exceeds 0.09%, the strength of the weld metal becomes excessively high due to the excessive yield of C in the weld metal, and the low-temperature toughness decreases. Therefore, C is 0.02 to 0.09% in total of the steel outer shell and the flux. In addition to the components contained in the steel outer sheath, C can be added from iron powder, iron alloy powder, etc. from the flux.
［鋼製外皮とフラックスの合計でＳｉ：０．２〜０．６％］
Ｓｉは、溶接時に一部が溶接スラグとなることにより溶接ビードの形状や外観を良好にし、溶接作業性の向上に寄与する。しかし、Ｓｉが０．２％未満では、溶接ビードの形状や外観を良好にする効果が十分に得られない。一方、Ｓｉが０．６％を超えると、Ｓｉが溶接金属中に過剰に歩留まることにより、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０．２〜０．６％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等の合金粉末から添加できる。
[The total amount of steel shell and flux is Si: 0.2-0.6%]
Si partially improves the shape and appearance of the weld bead by being part of the weld slag during welding, and contributes to improvement in welding workability. However, if Si is less than 0.2%, the effect of improving the shape and appearance of the weld bead cannot be obtained sufficiently. On the other hand, when Si exceeds 0.6%, Si is excessively yielded in the weld metal, so that the low temperature toughness of the weld metal is lowered. Therefore, Si is 0.2 to 0.6% in total of the steel outer shell and the flux. Si can be added from an alloy powder such as metal Si, Fe—Si, or Fe—Si—Mn from a flux in addition to components contained in the steel outer sheath.
［鋼製外皮とフラックスの合計でＭｎ：１．５〜３．３％］
Ｍｎは、溶接金属中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、これらの効果が十分に得られず、必要な溶接金属の強度及び低温靭性が得られない。一方、Ｍｎが３．３％を超えると、Ｍｎが溶接金属中に過剰に歩留まり、溶接金属の強度が過剰に高くなり、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Ｍｎは１．５〜３．３％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 3.3% in total of steel outer shell and flux]
Mn has the effect of increasing the strength and low temperature toughness of the weld metal by yielding in the weld metal. However, if Mn is less than 1.5%, these effects cannot be obtained sufficiently, and the required weld metal strength and low temperature toughness cannot be obtained. On the other hand, when Mn exceeds 3.3%, Mn is excessively yielded in the weld metal, the strength of the weld metal is excessively increased, and the low temperature toughness is lowered. Accordingly, the total of the steel outer shell and the flux is set to 1.5 to 3.3%. Mn can be added from an alloy powder such as metal Mn, Fe—Mn, and Fe—Si—Mn from a flux in addition to components contained in the steel outer sheath.
［鋼製外皮とフラックスの合計でＮｉ：１．５〜３．５％］
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１．５％未満では、この効果が十分に得られず、溶接金属の低温靭性が得られない。一方、Ｎｉが３．５％を超えると、溶接金属に高温割れ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Ｎｉは１．５〜３．５％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等の合金粉末から添加できる。
[Ni in total of steel shell and flux: 1.5-3.5%]
Ni has the effect of improving the low temperature toughness of the weld metal. However, if Ni is less than 1.5%, this effect cannot be sufficiently obtained, and the low temperature toughness of the weld metal cannot be obtained. On the other hand, if Ni exceeds 3.5%, hot cracking is likely to occur in the weld metal. Therefore, Ni is 1.5 to 3.5% in total of the steel outer shell and the flux. Ni can be added from alloy powders such as metal Ni and Fe-Ni from the flux in addition to components contained in the steel outer sheath.
［鋼製外皮とフラックスの合計でＭｏ：０．２１〜０．５％］
Ｍｏは、溶接金属の強度を向上させる効果がある。しかし、Ｍｏが０．２１％未満では、この効果が十分に得られず、必要な溶接金属の強度が得られない。一方、Ｍｏが０．５％を超えると、溶接金属の強度が過剰に高くなり、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Ｍｏは０．２１〜０．５％とする。なお、Ｍｏは、フラックスからの金属Ｍｏ、Ｆｅ−Ｍｏ等の合金粉末から添加できる。
[Total of steel outer shell and flux: Mo: 0.21-0.5%]
Mo has the effect of improving the strength of the weld metal. However, if Mo is less than 0.21%, this effect cannot be obtained sufficiently, and the required weld metal strength cannot be obtained. On the other hand, if Mo exceeds 0.5%, the strength of the weld metal becomes excessively high and the low-temperature toughness decreases. Therefore, Mo is 0.21 to 0.5% in total of the steel outer shell and the flux. In addition, Mo can be added from alloy powders, such as metal Mo from a flux, and Fe-Mo.
［鋼製外皮とフラックスの合計でＴｉ：０．０１〜０．１％］
Ｔｉは、溶接金属の組織を微細化して低温靭性を向上させる効果がある。しかし、Ｔｉが０．０１％未満では、この効果が十分に得られず、溶接金属の低温靭性が得られない。一方、Ｔｉが０．１％を超えると、靭性を阻害する上部ベイナイト組織を生成し、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Ｔｉは０．０１〜０．１％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等の合金粉末から添加できる。
[Ti: 0.01 to 0.1% in total of steel outer shell and flux]
Ti has the effect of reducing the microstructure of the weld metal and improving the low temperature toughness. However, if Ti is less than 0.01%, this effect cannot be sufficiently obtained, and the low temperature toughness of the weld metal cannot be obtained. On the other hand, when Ti exceeds 0.1%, an upper bainite structure that inhibits toughness is generated, and the low-temperature toughness of the weld metal decreases. Therefore, Ti is 0.01 to 0.1% in total of the steel outer shell and the flux. Ti can be added from an alloy powder such as metal Ti or Fe—Ti from a flux in addition to 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、溶接金属の低温靭性が得られない。一方、Ｂが０．０１５％を超えると、溶接金属の低温靱性が低下するとともに、溶接金属中に高温割れが発生しやすくなる。従って、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、Ｆｅ−Ｍｎ−Ｂ等の合金粉末から添加できる。
[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 cannot be obtained. On the other hand, when B exceeds 0.015%, the low temperature toughness of the weld metal is lowered, and hot cracks are likely to occur in the weld metal. Therefore, B is 0.002 to 0.015%. B can be added from an alloy powder such as metal B, Fe-B, Fe-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：０．０５％以下］
Ａｌは、０．０５％を超えると酸化物として溶接金属に残留して溶接金属の低温靭性を低下させる。従って、Ａｌは０．０５％以下とする。
[A total of steel shell and flux: Al: 0.05% or less]
If Al exceeds 0.05%, it remains as an oxide in the weld metal and lowers the low temperature toughness of the weld metal. Therefore, Al is made 0.05% or less.
［鋼製外皮とフラックスの合計でＮｂ：０．０１５％以下］
Ｎｂは、０．０１５％を超えると溶接金属に残留して溶接金属の低温靭性を低下させる。従って、Ｎｂは０．０１５％以下とする。
[Nb: 0.015% or less in total of steel outer shell and flux]
If Nb exceeds 0.015%, it remains in the weld metal and lowers the low temperature toughness of the weld metal. Therefore, Nb is made 0.015% or less.
［鋼製外皮とフラックスの合計でＶ：０．０１５％以下］
Ｖは、０．０１５％を超えると溶接金属に残留して溶接金属の強度を過剰に高くし、低温靭性を低下させる。従って、Ｖは０．０１５％以下とする。
[Total of steel outer shell and flux: V: 0.015% or less]
When V exceeds 0.015%, it remains in the weld metal, excessively increases the strength of the weld metal, and lowers the low temperature toughness. Therefore, V is set to 0.015% or less.
［フラックス中に含有する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、溶接ビードの形状及び外観を良好にし、溶接作業性の向上に寄与する効果がある。また、立向上進溶接において、溶融スラグの粘性や融点を調整し、メタル垂れを防ぐ効果がある。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、溶接ビード形状及び外観が不良になる。またＴｉ酸化物のＴｉＯ2換算値の合計が３％未満では、立向上進溶接においてメタル垂れが発生しやすくなる。一方、Ｔｉ酸化物のＴｉＯ2換算値の合計が８％を超えると、アークが安定してスパッタ発生量も少ないが、溶接金属中にＴｉ酸化物が過剰に残存することにより、溶接金属の低温靱性が低下する。従って、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 value of Ti oxide contained in flux: 3 to 8%]
Ti oxide contributes to the stabilization of the arc during welding, has the effect of improving the welding bead shape and appearance, and improving welding workability. Further, in vertical welding, there is an effect of adjusting the viscosity and melting point of the molten slag and preventing metal dripping. However, if the total of TiO 2 converted values of Ti oxide is less than 3%, these effects cannot be obtained sufficiently, the arc is unstable, the amount of spatter is large, and the weld bead shape and appearance are poor. In addition, when the total of the TiO 2 conversion values of the Ti oxide is less than 3%, metal sag is likely to occur in vertical improvement welding. On the other hand, when the total TiO 2 conversion value of the Ti oxide 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 the low temperature of the weld metal Toughness decreases. Therefore, the total of TiO 2 converted values of Ti oxide is 3 to 8%. The Ti oxide is added from rutile, titanium oxide, titanium slag, ilmenite, etc. from the flux.
［フラックス中に含有するＳｉ酸化物のＳｉＯ2換算値の合計：０．１〜０．５％］
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、この効果が十分に得られず、スラグ被包性が不良になり、ビード形状及び外観が不良となる。一方、Ｓｉ酸化物のＳｉＯ2換算値の合計が０．５％を超えると、溶融スラグの塩基度が低下することにより、溶接金属中の酸素量が増加して低温靭性が低下する。従って、Ｓｉ酸化物のＳｉＯ2換算値の合計は０．１〜０．５％とする。なお、Ｓｉ酸化物は、フラックスから珪砂、ジルコンサンド、珪酸ソーダ等から添加できる。
[Total of SiO 2 conversion values of Si oxide contained in flux: 0.1 to 0.5%]
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 of SiO 2 conversion values of Si oxides is less than 0.1%, this effect cannot be obtained sufficiently, and the slag encapsulation is poor, and the bead shape and appearance are poor. On the other hand, when the total of SiO 2 conversion values of the Si oxide exceeds 0.5%, the basicity of the molten slag is lowered, so that the amount of oxygen in the weld metal is increased and the low temperature toughness is lowered. Therefore, the total of SiO 2 conversion values of Si oxide is 0.1 to 0.5%. In addition, Si oxide can be added from a flux from silica sand, zircon sand, sodium silicate, or the like.
［フラックス中に含有するＭｇ：０．３〜０．８％］
Ｍｇは、強脱酸剤として機能して溶接金属中の酸素量を低減し、溶接金属の低温靱性を高める効果がある。しかし、Ｍｇが０．３％未満では、この効果が十分に得られず、溶接金属の低温靭性が得られない。一方、Ｍｇが０．８％を超えると、溶接時にアーク中で激しく酸素と反応してアークが粗くなり、スパッタ及びヒューム発生量が多くなる。従って、Ｍｇは０．３〜０．８％とする。なお、Ｍｇは、フラックスから金属Ｍｇ、Ａｌ−Ｍｇ等の合金粉末から添加できる。
[Mg contained in flux: 0.3 to 0.8%]
Mg functions as a strong deoxidizer, reduces the amount of oxygen in the weld metal, and has the effect of increasing the low temperature toughness of the weld metal. However, if Mg is less than 0.3%, this effect cannot be sufficiently obtained, and the low temperature toughness of the weld metal cannot be obtained. On the other hand, if Mg exceeds 0.8%, it reacts violently with oxygen in the arc during welding, and the arc becomes rough, resulting in an increase in spatter and fume generation. Therefore, Mg is 0.3 to 0.8%. In addition, Mg can be added from alloy powders, such as metal Mg and Al-Mg, from a flux.
［フラックス中に含有する弗素化合物のＦ換算値の合計：０．０５〜０．５％］
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０．０５％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０．５％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、弗素化合物のＦ換算値の合計は０．０５〜０．５％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 contained in flux: 0.05 to 0.5%]
The fluorine compound has an effect of stabilizing the arc. However, if the total F converted value of the fluorine compound is less than 0.05%, 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 0.5%, the arc becomes unstable and the amount of spatter generated increases. In addition, metal sag is likely to occur in vertical improvement welding. Therefore, the total F converted value of the fluorine compound is set to 0.05 to 0.5%. 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.
［フラックス中に含有する弗素化合物中におけるＮａ及びＫのＮａ換算値及びＫ換算値の１種または２種の合計：０．０５〜０．２％］
弗素化合物中のＮａ及びＫは、Ｍｇのみでは不可能であった溶接金属中の酸素量をさらに低減し、溶接金属の低温靱性を高める効果がある。しかし、弗素化合物中のＮａ換算値及びＫ換算値の１種または２種の合計が０．０５％未満では、この効果が十分に得られず、溶接金属の低温靭性が得られない。一方、弗素化合物中のＮａ換算値及びＫ換算値の１種または２種の合計が０．２％を超えると、アーク中の溶滴移行が不安定になり、スパッタ発生量が多くなる。従って、弗素化合物中のＮａ換算値及びＫ換算値の１種または２種の合計は０．０５〜０．２％とする。なお、弗素化合物中のＮａ及びＫは、ＮａＦ、Ｋ2ＳｉＦ6、Ｎａ3ＡｌＦ6等から添加でき、Ｎａ換算値及びＫ換算値はそれらに含有されるＮａ及びＫの合計である。
[Na and K converted to Na in the fluorine compound contained in the flux, and one or two of the K converted values: 0.05 to 0.2%]
Na and K in the fluorine compound have the effect of further reducing the amount of oxygen in the weld metal, which was impossible with Mg alone, and increasing the low temperature toughness of the weld metal. However, when the total of one or two of Na converted value and K converted value in the fluorine compound is less than 0.05%, this effect cannot be sufficiently obtained, and the low temperature toughness of the weld metal cannot be obtained. On the other hand, when the total of one or two of Na converted value and K converted value in the fluorine compound exceeds 0.2%, droplet transfer in the arc becomes unstable and the amount of spatter generated increases. Therefore, the total of one or two of Na converted value and K converted value in the fluorine compound is 0.05 to 0.2%. Na and K in the fluorine compound can be added from NaF, K 2 SiF 6 , Na 3 AlF 6 or the like, and the Na converted value and the K converted value are the total of Na and K contained therein.
［フラックス中に含有するＮａ2Ｏ及びＫ2Ｏの１種または２種の合計：０．０５〜０．２％］
Ｎａ2Ｏ及びＫ2Ｏ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、Ｎａ2Ｏ及びＫ2Ｏ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、Ｎａ2Ｏ及びＫ2Ｏの１種または２種の合計が０．２％を超えると、スラグ剥離性が不良となり、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、Ｎａ2Ｏ及びとＫ2Ｏの１種または２種の合計は０．０５〜０．２％とする。なお、Ｎａ2Ｏ及びとＫ2Ｏ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。
[Total of one or two kinds of Na 2 O and K 2 O contained in the flux: 0.05 to 0.2%]
Na 2 O and K 2 O act as arc stabilizers and slag formers. However, if the total of one or two of Na 2 O and K 2 O is less than 0.05%, the arc becomes unstable and the amount of spatter generated increases. Also, the bead shape and appearance are poor. On the other hand, if the total of one or two of Na 2 O and K 2 O exceeds 0.2%, the slag peelability becomes poor, and metal dripping is likely to occur in the vertical improvement welding. Therefore, the total of one or two of Na 2 O and K 2 O is 0.05 to 0.2%. Na 2 O and K 2 O can be added from a solid component of water glass composed of sodium silicate and potassium silicate, potassium titanate, sodium titanate and the like.
［フラックス中に含有するＺｒ酸化物のＺｒＯ2換算値の合計：０．２％以下］
Ｚｒ酸化物は、ジルコンサンドや酸化ジルコニウムから添加され、或いはＴｉ酸化物中に微量含有する。しかし、Ｚｒ酸化物のＺｒＯ2換算値の合計が０．２％を超えるとスラグ剥離性を不良にする。従って、Ｚｒ酸化物のＺｒＯ2換算値の合計は０．２％以下とする。
[Total of ZrO 2 converted values of Zr oxide contained in flux: 0.2% or less]
Zr oxide is added from zircon sand or zirconium oxide, or contained in a small amount in Ti oxide. However, if the total of ZrO 2 converted values of the Zr oxide exceeds 0.2%, the slag peelability becomes poor. Therefore, the total of ZrO 2 converted values of the Zr oxide is 0.2% or less.
［フラックス中に含有するＡｌ酸化物のＡｌ2Ｏ3換算値の合計：０．１％以下］
Ａｌ酸化物は、溶接時に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メタル垂れを防止する効果があるが、酸化物として溶接金属に残存しやすく、溶接金属の低温靭性が低下する原因となる。Ａｌ酸化物のＡｌ2Ｏ3換算値の合計が０．１％を超えると、溶接金属中に残存したＡｌ酸化物による低温靭性の低下が著しくなる。従って、Ａｌ酸化物のＡｌ2Ｏ3換算値の合計は０．１％以下とする。なお、Ａｌ酸化物は、フラックスからのアルミナ等から添加できる。
[Total Al 2 O 3 conversion value of Al oxide contained in flux: 0.1% or less]
Al oxide adjusts the viscosity and melting point of molten slag during welding, and has the effect of preventing metal sag especially in vertical welding, but it tends to remain in the weld metal as an oxide, reducing the low-temperature toughness of the weld metal. Cause. When the total of Al 2 O 3 converted values of the Al oxide exceeds 0.1%, the low temperature toughness due to the Al oxide remaining in the weld metal is remarkably reduced. Therefore, the total in terms of Al 2 O 3 value of Al oxide is 0.1% or less. In addition, Al oxide can be added from the alumina etc. from a flux.
［鋼製外皮に継目が無いこと］
本発明のＡｒ−ＣＯ2混合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ので、より好ましい。
[Seamless steel outer skin]
The flux-cored wire for Ar—CO 2 mixed gas shielded arc welding of 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. There are two types of wire: a seamless wire in the steel skin obtained by welding the seam of the formed 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 can be used, but a wire without a seamless steel outer sheath can be heat-treated for the purpose of reducing the total amount of hydrogen in the wire. Since there is no moisture absorption of the flux after manufacture, the amount of diffusible hydrogen in the weld metal can be reduced and the cold cracking resistance can be improved, which is more preferable.
［ワイヤ表面の送給潤滑剤：ワイヤ１０ｋｇ当たり０．０５〜１．５０ｇ］
送給潤滑剤は、ワイヤの送給性を良好にし、アークを安定させてスパッタ発生量を少なくする効果があり、ワイヤ表面に塗布することが好ましい。ワイヤ表面の送給潤滑剤がワイヤ１０ｋｇ当り０．０５ｇ未満では、ワイヤ送給性が不良となり、アークが不安定になってスパッタ発生量が多くなる。一方、ワイヤ表面の送給潤滑剤がワイヤ１０ｋｇ当り１．５０ｇを超えると、ワイヤ送給装置の送給ローラ部でワイヤがスリップし、アークが不安定となってスパッタ発生量が多くなる。従って、ワイヤ表面の送給潤滑剤はワイヤ１０ｋｇ当り０．０５〜１．５０ｇとすることが好ましい。
[Wire feed lubricant: 0.05 to 1.50 g per 10 kg of wire]
The feed lubricant has the effect of improving the feedability of the wire, stabilizing the arc and reducing the amount of spatter generated, and is preferably applied to the wire surface. If the feed lubricant on the wire surface is less than 0.05 g per 10 kg of wire, the wire feedability becomes poor, the arc becomes unstable, and the amount of spatter generated increases. On the other hand, when the feed lubricant on the wire surface exceeds 1.50 g per 10 kg of the wire, the wire slips at the feed roller portion of the wire feed device, the arc becomes unstable, and the amount of spatter generated increases. Therefore, the feed lubricant on the wire surface is preferably 0.05 to 1.50 g per 10 kg of wire.
なお、送給潤滑剤は、動植物油、鉱物油あるいは合成油の何れでもよい。動植物油としては、パーム油、菜種油、ひまし油、豚油、牛油、魚油等を用い、鉱物油としては、マシン油、タービン油、スピンドル油等を用いることができる。合成油としては、炭化水素系、エステル系、ポリグリコール系、ポリフェノール系、シリコーン系、フロロカーボン系を用いることができる。また、油脂またはエステルの１種以上の基油に硫黄を含有する硫化油脂、硫化エステル、硫化脂肪酸または硫化オレフィンの１種または２種以上である硫黄含有の潤滑油を用いることもできる。 The feed lubricant may be animal or vegetable oil, mineral oil or synthetic oil. Palm oil, rapeseed oil, castor oil, pig oil, cow oil, fish oil, etc. can be used as the animal and vegetable oil, and machine oil, turbine oil, spindle oil, etc. can be used as the mineral oil. As the synthetic oil, hydrocarbon type, ester type, polyglycol type, polyphenol type, silicone type and fluorocarbon type can be used. In addition, sulfur-containing lubricating oils that are one or more of sulfurized fats and oils, sulfurized esters, sulfurized fatty acids or sulfurized olefins containing sulfur in one or more base oils of fats or esters can also be used.
本発明のＡｒ−ＣＯ2混合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、Ｆｅ−Ｓｉ−Ｍｎ、Ｆｅ−Ｎｉ、Ｆｅ−Ｍｏ、Ｆｅ−Ｔｉ合金等の鉄合金粉のＦｅ分及び不可避不純物である。不可避不純物について、特に規定しないが、耐高温割れ性の観点から、Ｐは０．０１０％以下、Ｓは０．０１０％以下が好ましい。 The balance of the flux-cored wire for Ar—CO 2 mixed gas shielded arc welding of the present invention is Fe of steel outer shell, iron powder added for component adjustment, Fe—Mn, Fe—Si, Fe—Si—Mn, Fe content and unavoidable impurities of iron alloy powders such as Fe-Ni, Fe-Mo, Fe-Ti alloy. The inevitable impurities are not particularly defined, but from the viewpoint of hot cracking resistance, P is preferably 0.010% or less, and S is preferably 0.010% or less.
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 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.
溶接時のシールドガスは、溶接金属の酸素量を低減するためにＡｒ＋５〜２５％ＣＯ2の混合ガスとする。 The shielding gas at the time of welding is a mixed gas of Ar + 5 to 25% CO 2 in order to reduce the oxygen content of the weld metal.
以下、本発明の効果を実施例により具体的に説明する。 Hereinafter, the effect of the present invention will be described in detail with reference to examples.
鋼製外皮にＪＩＳ Ｇ３１４１に規定されるＳＰＣＣを使用して、鋼製外皮を成形する工程でＵ字型に成形した後、鋼製外皮の合わせ目を溶接した継目が無いワイヤと、溶接しない隙間が有るワイヤとを造管及び伸線し、表１及び表２に示すワイヤ径１．２ｍｍの各種成分のフラックス入りワイヤを試作した。なお、フラックス充填率は１０〜１８％とした。 After using the SPCC specified in JIS G3141 for the steel outer shell and forming it into a U shape in the process of forming the steel outer shell, the seamless wire welded with the seam of the steel outer shell and the gap not to be welded The wire with the wire was piped and drawn, and flux-cored wires of various components having a wire diameter of 1.2 mm shown in Tables 1 and 2 were made as trial products. The flux filling rate was 10 to 18%.
試作したワイヤで、ＪＩＳ Ｇ３１２６ ＳＬＡ３６５に規定される鋼板を用いて立向上進すみ肉溶接による溶接作業性、溶接割れ試験及び溶着金属試験を実施した。 With the prototyped wire, welding workability, weld cracking test, and weld metal test were conducted by fillet welding with vertical improvement using a steel plate specified in JIS G3126 SLA365.
溶接作業性の評価は、表３に示す溶接条件で立向上進溶接を行い、アークの安定性、スパッタ及びヒューム発生状態、スラグ被包性、スラグ剥離性、ビード形状及び外観の良否及びメタル垂れ及び高温割れの有無について調査した。 Welding workability was evaluated by standing up welding under the welding conditions shown in Table 3, arc stability, spatter and fume generation state, slag encapsulation, slag peelability, bead shape and quality and metal sag. And the presence or absence of hot cracking was investigated.
溶接割れ試験は、Ｕ形溶接割れ試験方法（ＪＩＳ Ｚ ３１５７）に準拠し、試験体を５０℃に予熱して溶接を実施し、高温割れの有無を調査した後、低温割れの調査については、溶接後７２時間経過した試験体について、表面割れ及び断面割れ（５断面）の発生の有無を浸透探傷試験（ＪＩＳ Ｚ ２３４３）により調査した。 The weld crack test is based on the U-shaped weld crack test method (JIS Z 3157), the test specimen is preheated to 50 ° C. and welded, and the presence or absence of hot cracks is investigated. About the test body which 72 hours passed after welding, the presence or absence of the generation | occurrence | production of a surface crack and a cross-section crack (5 cross sections) was investigated by the penetration test (JIS Z 2343).
溶着金属試験は、ＪＩＳ Ｚ ３１１１に準じ、表３に示す溶接条件で実施し、溶着金属の板厚方向の中心部から引張試験（Ａ０号）及び衝撃試験（Ｖノッチ試験片）を採取して、機械試験を実施した。引張強さの評価は、０．２％耐力が６９０ＭＰａ以上、引張強さが７８０〜９００ＭＰａのものを良好とした。靭性の評価は、試験温度−４０℃でシャルピー衝撃試験を行い、３本の吸収エネルギーの平均値が６９Ｊ以上を良好とした。これらの結果を表４にまとめて示す。 The weld metal test was conducted in accordance with JIS Z 3111 under the welding conditions shown in Table 3, and a tensile test (A0) and impact test (V notch test piece) were taken from the center of the weld metal in the plate thickness direction. A mechanical test was conducted. The tensile strength was evaluated as good when the 0.2% proof stress was 690 MPa or more and the tensile strength was 780 to 900 MPa. For the evaluation of toughness, a Charpy impact test was performed at a test temperature of −40 ° C., and the average value of the three absorbed energy was 69 J or more. These results are summarized in Table 4.
表１、表２及び表４のワイヤ記号Ａ１〜Ａ９は本発明例、ワイヤ記号Ｂ１〜Ｂ１８は比較例である。 The wire symbols A1 to A9 in Tables 1, 2 and 4 are examples of the present invention, and the wire symbols B1 to B18 are comparative examples.
本発明例であるワイヤ記号Ａ１〜Ａ９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、Ｕ形溶接割れ試験で割れが発生せず、溶着金属の０．２％耐力、引張強さ及び吸収エネルギーも良好であるなど極めて満足な結果であった。 The wire symbols A1 to A9, which are examples of the present invention, have good welding workability because the composition of each component is within the range specified in the present invention, and cracks do not occur in the U-shaped weld cracking test. The results were extremely satisfactory, such as 0.2% proof stress, tensile strength and good energy absorption of the metal.
なお、ワイヤ記号Ａ２はワイヤ表面の送給潤滑剤量が多く、ワイヤ記号Ａ７はワイヤ表面の送給潤滑剤量が少ないので、ややアークが不安定であったが、格別問題とはならなかった。 Since the wire symbol A2 has a large amount of feed lubricant on the wire surface and the wire symbol A7 has a small amount of feed lubricant on the wire surface, the arc was somewhat unstable, but this was not a problem. .
比較例中ワイヤ記号Ｂ１は、Ｃが多いので、溶着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、Ｎｉが多いので、クレータ部に高温割れが生じた。さらに、鋼製外皮に継目を有し溶着金属の引張強さが高いので、Ｕ形溶接割れ試験において溶接部に割れが生じた。 Since the wire symbol B1 in the comparative example had a large amount of C, the tensile strength of the weld metal was high and the absorbed energy was low. Moreover, since there was much Ni, the hot crack occurred in the crater part. Furthermore, since the steel outer skin has a seam and the tensile strength of the weld metal is high, cracks occurred in the weld in the U-shaped weld cracking test.
ワイヤ記号Ｂ２は、Ｓｉが多いので、溶着金属の吸収エネルギーが低値であった。また、Ｍｇが多いので、アークが不安定でスパッタ発生量及びヒューム発生量が多かった。さらに、ワイヤ表面の送給潤滑剤が少ないので、ワイヤ送給性が不良で、アークを安定にしてスパッタ発生量を低減する効果は得られなかった。 Since the wire symbol B2 contains a large amount of Si, the absorbed energy of the weld metal was low. Moreover, since there was much Mg, the arc was unstable and there was much spatter generation amount and fume generation amount. Furthermore, since there is little supply lubricant on the surface of the wire, the wire supply performance is poor, and the effect of stabilizing the arc and reducing the amount of spatter generated cannot be obtained.
ワイヤ記号Ｂ３は、Ｍｎが多いので、溶着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、Ｎａ2Ｏ及びＫ2Ｏの合計が少ないので、アークは不安定でスパッタ発生量が多く、ビード形状及び外観が不良であった。さらに、鋼製外皮に継目を有し溶着金属の引張強さが高いので、Ｕ形割れ試験において溶接部に割れが生じた。 Since the wire symbol B3 has a large amount of Mn, the tensile strength of the deposited metal was high and the absorbed energy was low. Further, since the total amount of Na 2 O and K 2 O was small, the arc was unstable, the amount of spatter was large, and the bead shape and appearance were poor. Furthermore, since the steel outer skin has a seam and the tensile strength of the weld metal is high, cracks occurred in the welded part in the U-shaped crack test.
ワイヤ記号Ｂ４は、Ｍｎが少ないので、溶着金属の０．２％耐力及び引張強さが低く、吸収エネルギーが低値であった。また、Ｓｉ酸化物のＳｉＯ2換算値が少ないので、スラグ被包性が悪く、ビード形状及び外観が不良であった。 Since the wire symbol B4 had a small amount of Mn, the 0.2% proof stress and tensile strength of the deposited metal were low, and the absorbed energy was low. Further, since the SiO 2 converted value of Si oxide is small, poor slag encapsulated, bead shape and appearance was poor.
ワイヤ記号Ｂ５は、Ｎｉが少ないので、溶着金属の吸収エネルギーが低値であった。また、弗素化合物のＦ換算値が多いので、アークが不安定でスパッタ発生量が多く、メタル垂れが生じた。 Since the wire symbol B5 has a small amount of Ni, the absorbed energy of the weld metal was low. In addition, since the F-converted value of the fluorine compound is large, the arc is unstable, the amount of spatter generated is large, and metal dripping occurs.
ワイヤ記号Ｂ６は、Ｍｏが多いので、溶着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、弗素化合物のＦ換算値が少ないので、アークが不安定であった。さらに、鋼製外皮に継目を有し溶着金属の引張強さが高いので、Ｕ形割れ試験において溶接部に割れが生じた。 Since the wire symbol B6 has a large amount of Mo, the tensile strength of the deposited metal was high and the absorbed energy was low. Further, since the F-converted value of the fluorine compound is small, the arc is unstable. Furthermore, since the steel outer skin has a seam and the tensile strength of the weld metal is high, cracks occurred in the welded part in the U-shaped crack test.
ワイヤ記号Ｂ７は、Ｓｉが少ないので、ビード形状及び外観が不良であった。また、Ｔｉが多いので、溶着金属の吸収エネルギーが低値であった。 Since the wire symbol B7 has little Si, the bead shape and appearance were poor. Moreover, since there is much Ti, the absorbed energy of the weld metal was low.
ワイヤ記号Ｂ８は、Ｍｏが少ないので、溶着金属の０．２％耐力及び引張強さが低かった。また、Ｔｉが少ないので、溶着金属の吸収エネルギーが低値であった。さらに、Ｎａ2ＯとＫ2Ｏの合計が多いので、スラグ剥離性が悪く、メタル垂れが生じた。 Since the wire symbol B8 has a small amount of Mo, the 0.2% proof stress and tensile strength of the deposited metal were low. Further, since Ti is small, the absorbed energy of the deposited metal was low. Further, since the total amount of Na 2 O and K 2 O was large, slag peelability was poor and metal dripping occurred.
ワイヤ記号Ｂ９は、Bが多いので、溶着金属の吸収エネルギーが低値で、クレータ部に高温割れが生じた。 Since the wire symbol B9 has a large amount of B, the absorbed energy of the weld metal is low, and high-temperature cracking occurs in the crater portion.
ワイヤ記号Ｂ１０は、Bが少ないので、溶着金属の吸収エネルギーが低値であった。また、Ｚｒ酸化物のＺｒＯ2換算値が多いので、スラグ剥離性が不良であった。 Since the wire symbol B10 has a small amount of B, the absorbed energy of the weld metal was low. Further, since the terms of ZrO 2 value of Zr oxide is large, the slag removability was poor.
ワイヤ記号Ｂ１１は、Ａｌが多いので、溶着金属の吸収エネルギーが低値であった。また、弗素化合物中のＮａ換算値及びK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、ワイヤ表面の送給潤滑剤が多いので、ワイヤ送給性を向上させる効果は得られず、アークも不安定のままでスパッタ発生量も低減されなかった。 Since the wire symbol B11 has a large amount of Al, the absorbed energy of the deposited metal was low. Further, since the total of Na converted value and K converted value in the fluorine compound is large, the arc is unstable and the amount of spatter generated is large. Furthermore, since there are many feed lubricants on the wire surface, the effect of improving the wire feedability was not obtained, the arc remained unstable, and the amount of spatter generation was not reduced.
ワイヤ記号Ｂ１２は、Ｎｂが多いので、溶着金属の吸収エネルギーが低値であった。 Since the wire symbol B12 has a large amount of Nb, the absorbed energy of the weld metal was low.
ワイヤ記号Ｂ１３は、Ｖが高いので、溶着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、鋼製外皮に継目を有し溶着金属の引張強さが高いので、Ｕ形割れ試験において溶接部に割れが生じた。 Since the wire symbol B13 had a high V, the tensile strength of the deposited metal was high and the absorbed energy was low. In addition, since the steel outer skin has a seam and the tensile strength of the weld metal is high, cracks occurred in the weld in the U-shaped crack test.
ワイヤ記号Ｂ１４は、Ｃが低いので、アークが不安定で、溶着金属の０．２％耐力及び引張強さが低値であった。また、Ｍｇが少ないので、溶着金属の吸収エネルギーが低値であった。 In the wire symbol B14, since C was low, the arc was unstable, and the 0.2% proof stress and tensile strength of the deposited metal were low. Further, since the amount of Mg is small, the absorbed energy of the deposited metal was low.
ワイヤ記号Ｂ１５は、Ｔｉ酸化物のＴｉＯ2換算値の合計が多いので、溶着金属の吸収エネルギーが低値であった。 Since the wire symbol B15 has a large total of TiO 2 converted values of Ti oxide, the absorbed energy 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 of the deposited metal was low.
ワイヤ記号Ｂ１７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、ビード形状及び外観が不良で、メタル垂れが生じた。また、弗素化合物中のＮａ換算値及びＫ換算値の合計が少ないので、溶着金属の吸収エネルギーが低値であった。 In wire symbol B17, the total of TiO 2 converted values of Ti oxide was small, so the arc was unstable, the amount of spatter was large, the bead shape and appearance were poor, and metal dripping occurred. Further, since the total of Na converted value and K converted value in the fluorine compound is small, the absorbed energy of the weld metal was low.
ワイヤ記号Ｂ１８は、Ａｌ酸化物のＡｌ2Ｏ3換算値の合計が多いので、溶着金属の吸収エネルギーが低値であった。 Since the wire symbol B18 has a large total of Al 2 O 3 conversion values of Al oxide, the absorbed energy of the deposited metal was low.
Claims (3)
ワイヤ全質量に対する質量％で、鋼製外皮とフラックスとの合計で、
Ｃ：０．０２〜０．０９％、
Ｓｉ：０．２〜０．６％、
Ｍｎ：１．５〜３．３％、
Ｎｉ：１．５〜３．５％、
Ｍｏ：０．２１〜０．５％、
Ｔｉ：０．０１〜０．１％、
Ｂ：０．００２〜０．０１５％を含有し、
Ａｌ：０．０５％以下、
Ｎｂ：０．０１５％以下、
Ｖ：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：０．１〜０．５％、
Ｍｇ：０．３〜０．８％、
弗素化合物のＦ換算値の合計：０．０５〜０．５％、
弗素化合物中におけるＮａ及びＫのＮａ換算値及びＫ換算値の１種または２種の合計：０．０５〜０．２％、
Ｎａ2Ｏ及びＫ2Ｏの１種または２種の合計：０．０５〜０．２％を含有し、
Ｚｒ酸化物のＺｒＯ2換算値の合計：０．２％以下、
Ａｌ酸化物のＡｌ2Ｏ3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Ａｒ−ＣＯ2混合ガスシールドアーク溶接用フラックス入りワイヤ。 In a flux cored wire for Ar—CO 2 mixed gas shielded arc welding formed by filling a steel sheath with flux,
It is the mass% with respect to the total mass of the wire.
C: 0.02 to 0.09%,
Si: 0.2-0.6%
Mn: 1.5-3.3%
Ni: 1.5-3.5%,
Mo: 0.21 to 0.5%,
Ti: 0.01 to 0.1%,
B: contains 0.002 to 0.015%,
Al: 0.05% or less,
Nb: 0.015% or less,
V: 0.015% or less,
Furthermore, in the flux in mass% with respect to the total mass of the 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 0.5%,
Mg: 0.3-0.8%
Total F converted value of fluorine compound: 0.05 to 0.5%,
Na- and K-converted values of Na and K in the fluorine compound and the total of one or two of the K-converted values: 0.05 to 0.2%,
A total of one or two of Na 2 O and K 2 O: 0.05 to 0.2%,
Total of ZrO 2 converted values of Zr oxide: 0.2% or less,
Total terms of Al 2 O 3 value of Al oxide: is 0.1% or less,
A flux cored wire for Ar—CO 2 mixed gas shielded arc welding, characterized in that the balance consists of Fe in steel outer shell, iron powder, Fe in iron alloy powder and inevitable impurities.
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| JP6953870B2 (en) * | 2017-07-31 | 2021-10-27 | 日本製鉄株式会社 | Flux-cored wire for gas shielded arc welding and welding joint manufacturing method |
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| JP7027859B2 (en) * | 2017-12-12 | 2022-03-02 | 日本製鉄株式会社 | Gas shield arc Welding flux-cored wire and welding joint manufacturing method |
| JP6939574B2 (en) * | 2018-01-05 | 2021-09-22 | 日本製鉄株式会社 | Flux-cored wire for gas shielded arc welding and welding joint manufacturing method |
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