JP6188621B2 - Flux-cored wire for carbon dioxide shielded arc welding - Google Patents
Flux-cored wire for carbon dioxide shielded arc welding Download PDFInfo
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本発明は、各種鋼構造物の溶接に用いるガスシールド溶接用フラックス入りワイヤに関し、大入熱、高パス間温度の溶接施工条件においても良好な溶接作業性を有し、溶接金属の機械的性能が安定して得られる炭酸ガスシールドアーク溶接用フラックス入りワイヤに関する。 The present invention relates to a flux-cored wire for gas shield welding used for welding various steel structures, and has good welding workability even under welding conditions of high heat input and high-pass temperature, and the mechanical performance of the weld metal. The present invention relates to a flux-cored wire for carbon dioxide shielded arc welding that can be stably obtained.
近年、建築鉄骨分野において、溶接施工の更なる能率向上を図るため、大入熱および高パス間温度の溶接施工条件に対応するガスシールドアーク溶接用ソリッドワイヤが開発され、ＪＩＳ Ｚ３３１２ ＹＧＷ１８に規定されている。このような溶接施工条件に対応したガスシールドアーク溶接用ソリッドワイヤは、例えば特開平１０−２３０３８７号公報（特許文献１）、特開２００２−３４６７８９号公報（特許文献２）や特開２００６−８８１８７号公報（特許文献３）に開示されている。 In recent years, in order to further improve the efficiency of welding in the building steel frame field, a solid wire for gas shielded arc welding corresponding to welding conditions of high heat input and high-pass temperature has been developed and specified in JIS Z3312 YGW18. ing. The solid wire for gas shielded arc welding corresponding to such welding conditions is disclosed in, for example, Japanese Patent Application Laid-Open No. 10-230387 (Patent Document 1), Japanese Patent Application Laid-Open No. 2002-346789 (Patent Document 2) and Japanese Patent Application Laid-Open No. 2006-88187. (Patent Document 3).
これらのガスシールドアーク溶接用ソリッドワイヤは、溶着効率に優れる反面、スパッタ発生量が多く溶接作業性が劣るという問題がある。一方でガスシールドアーク溶接用フラックス入りワイヤは溶接作業性に優れる特性を有しているが、大入熱、高パス間温度の溶接施工条件においては、溶接金属の機械的性能が劣化するという問題がある。 These solid wires for gas shielded arc welding are excellent in welding efficiency, but have a problem that the amount of spatter is large and welding workability is inferior. On the other hand, the flux-cored wire for gas shielded arc welding has excellent welding workability, but the mechanical performance of the weld metal deteriorates under welding conditions with high heat input and high interpass temperature. There is.
このような大入熱、高パス間温度の溶接施工条件に対応したガスシールド溶接用フラックス入りワイヤは、例えば特開２０１１−２５２９８号公報（特許文献４）に示されている。これによると高い溶接能率を有し、スパッタ発生量が少なく溶接作業性が良好で、溶接金属の機械的性能が優れる高品質な溶接部が得られるガスシールドアーク溶接方法が開示されているが、スラグ生成量が多くスラグ剥離性が不良で機械的性能も満足できるものではなかった。 A flux-cored wire for gas shield welding corresponding to such high heat input and high interpass temperature welding conditions is disclosed in, for example, Japanese Patent Application Laid-Open No. 2011-25298 (Patent Document 4). According to this, there is disclosed a gas shielded arc welding method that has a high welding efficiency, a low spatter generation amount, good welding workability, and a high-quality welded portion with excellent mechanical performance of the weld metal. The amount of slag produced was large, the slag peelability was poor, and the mechanical performance was not satisfactory.
一方、メタル系ガスシールド溶接用フラックス入りワイヤを用いて、大入熱、高パス間温度の溶接施工条件で機械的性能を満足する技術が特開２００５−２７９６８３号公報（特許文献５）に開示されているが、スパッタ発生量が多いという問題があった。 On the other hand, Japanese Patent Application Laid-Open No. 2005-279683 (Patent Document 5) discloses a technique that uses a metal-based gas shield welding flux-cored wire to satisfy mechanical performance under welding conditions of high heat input and high pass temperature. However, there was a problem that a large amount of spatter was generated.
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、大入熱、高パス間温度の溶接施工条件においても溶接金属の強度低下、靭性の劣化等がなく、ソリッドワイヤの高溶着性能、低スラグ発生量と、フラックス入りワイヤの安定した溶接作業性等の諸性能とを兼ね備えた炭酸ガスシールド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 there is no reduction in weld metal strength, toughness deterioration, etc. even under welding conditions of high heat input and high pass temperature, An object of the present invention is to provide a flux-cored wire for carbon dioxide shield welding, which has high welding performance, low slag generation amount, and various performances such as stable welding workability of the flux-cored wire.
本発明者らは、シールドガスとして炭酸ガスを用いる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、アーク安定剤および特定範囲に限定されたＣ、Ｓｉ、Ｍｎ、Ｃｕ、Ｍｏ、Ｔｉ、Ｂおよび少量の金属酸化物を含み、さらにＭｇを添加することにより大入熱、高パス間温度の溶接においてより改善された効果が得られることを見出した。 The inventors of the present invention have disclosed a flux-cored wire for gas shielded arc welding using carbon dioxide gas as a shielding gas. It has been found that an improved effect can be obtained in welding with high heat input and high pass temperature by adding an oxide and further adding Mg.
すなわち、本発明の要旨は、
（１）鋼製外皮にフラックスを充填してなる炭酸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、鋼製外皮とフラックスの一方または両方に、ワイヤ全質量に対す る質量％で、Ｃ：０．０８〜０．１５％、Ｓｉ：０．５〜１．５％、Ｍｎ：１〜２．５ ％、Ｃｕ：０．１〜０．５％、Ｍｏ：０．１〜０．３５％、Ｔｉ：０．１〜０．３５％ 、Ｂ：０．００２〜０．０１％を含有し、フラックスに、ワイヤ全質量に対する質量％ で、Ｎａ化合物およびＫ化合物のＮａ2Ｏ換算値とＫ2Ｏ換算値の合計：０．０５〜０ ．２％、Ｓｉ酸化物のＳｉＯ2換算値の合計：０．１〜１％を含有し、残部は鋼製外皮 のＦｅ、鉄合金粉のＦｅ分、鉄粉および不可避不純物からなることを特徴とする炭酸ガ スシールドアーク溶接用フラックス入りワイヤ。
（２）フラックスに、ワイヤ全質量に対する質量％で、Ｍｇ：０．０４〜０．０８％を 更に含有することを特徴とする（１）に記載の炭酸ガスシールドアーク溶接用フラック ス入りワイヤ。
（３）フラックスに、ワイヤ全質量に対する質量％で、Ａｌ酸化物のＡｌ2Ｏ3換算値 の合計：０．１〜０．５％を更に含有することを特徴とする（１）または（２）に記載 の炭酸ガスシールドアーク溶接用フラックス入りワイヤ。
（４）フラックスに、ワイヤ全質量に対する質量％で、弗素化合物のＦ換算値の合計： ０．０１〜０．２％を更に含有することを特徴とする（１）ないし（３）の何れかに記 載の炭酸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。
That is, the gist of the present invention is as follows.
(1) In a flux-cored wire for carbon dioxide shielded arc welding in which a steel sheath is filled with flux, either or both of the steel sheath and the flux are in mass% with respect to the total mass of the wire, C: 0.08 -0.15%, Si: 0.5-1.5%, Mn: 1-2.5%, Cu: 0.1-0.5%, Mo: 0.1-0.35%, Ti: 0.1 to 0.35%, B: containing 0.002 to 0.01%, the flux, by mass% with respect to total mass of the wire, Na 2 O conversion value of Na compounds and K compounds and K 2 O in terms Sum of values: 0.05-0. 2%, total of SiO 2 equivalent value of Si oxide: 0.1 to 1%, the balance is made of Fe of steel outer shell, Fe content of iron alloy powder, iron powder and inevitable impurities Flux-cored wire for carbon dioxide shielded arc welding.
(2) The flux-containing wire for carbon dioxide shielded arc welding according to (1), wherein the flux further contains Mg: 0.04 to 0.08% in mass% with respect to the total mass of the wire.
(3) The flux further contains, in mass% with respect to the total mass of the wire, a total of Al 2 O 3 converted value of Al oxide: 0.1 to 0.5% (1) or (2 ) Flux-cored wire for carbon dioxide shielded arc welding.
(4) Any one of (1) to (3) , wherein the flux further contains, in mass% with respect to the total mass of the wire, a total F-converted value of the fluorine compound: 0.01 to 0.2% The flux-cored wire for carbon dioxide shielded arc welding described in 1.
本発明の炭酸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、大入熱、高パス間温度の溶接施工条件においても良好な溶接作業性を有し、また、溶接金属の機械的性能を改善するなど、溶接能率およ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 carbon dioxide shielded arc welding of the present invention, it has good welding workability even under welding conditions of high heat input and high pass temperature, and improves the mechanical performance of the weld metal. It is possible to improve the welding efficiency and the quality of the welded part.
本発明者等は、前記の問題点を解決するために、種々成分を変化させた炭酸ガスシ−ルドアーク溶接用フラックス入りを試作して大入熱、高パス間温度の溶接施工条件において、溶接作業性および溶接金属の強度と靭性の安定化に及ぼす影響因子を明確にし、以下に示す知見を得た。 In order to solve the above-mentioned problems, the inventors made a prototype of carbon dioxide shielded arc welding flux with various components changed, and under the welding conditions of high heat input and high pass temperature, welding work The influencing factors on the stability and stability of weld metal strength and toughness were clarified, and the following findings were obtained.
大入熱・高パス間温度の溶接施工条件での溶接における溶接金属の強度と安定した靭性を得ることについては、Ｃ、Ｓｉ、Ｍｎ、Ｃｕ、Ｍｏ、ＴｉおよびＢの適量添加および調整により効果を得ることができることを知見した。
また、大入熱、高パス間温度での溶接施工条件では、アーク状態の劣化およびスパッタ発生量の増加という問題があり、これら溶接作業性はＣ、ＮａおよびＫ化合物の適量添加と少量のＳｉＯ２の添加により良好となることを見出した。
For obtaining weld metal strength and stable toughness in welding under high heat input and high pass temperature welding conditions, it is effective by adding and adjusting appropriate amounts of C, Si, Mn, Cu, Mo, Ti and B It was found that can be obtained.
Moreover, under welding conditions with high heat input and high pass temperature, there is a problem of deterioration of the arc state and an increase in the amount of spatter generated. These welding workability results in the addition of appropriate amounts of C, Na and K compounds and a small amount of SiO. It has been found that the addition of 2 makes it better.
以下、本発明の炭酸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と、その組成の限定理由とについて説明する。なお、各成分の含有量は、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 components of the flux-cored wire for carbon dioxide shielded arc welding of the present invention and the reasons for limiting the composition will be described. The content of each component is expressed by mass% with respect to the total mass of the wire, and when expressing the mass%, it is simply expressed as%.
以下の成分は鋼製外皮とフラックスの一方または両方に含有させ得るものである。
［Ｃ：０．０８〜０．１５％］
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。ここで、Ｃが０．０８％未満では、アークが不安定で溶接金属の強度が得られない。一方、Ｃが０．１５％を超えると、溶接金属中に過剰に歩留まることにより、溶接金属の強度が高くなり過ぎ靱性が低下する。従って、鋼製外皮とフラックスの合計でＣは０．０８〜０．１５％とする。なお、Ｃは、鋼製外皮に含まれる成分の他、フラックスから金属粉および合金粉等で添加できる。
The following components can be contained in one or both of the steel outer sheath and the flux.
[C: 0.08 to 0.15%]
C contributes to the stabilization of the arc during welding and has the effect of improving the strength of the weld metal. Here, if C is less than 0.08%, the arc is unstable and the strength of the weld metal cannot be obtained. On the other hand, when C exceeds 0.15%, the yield of the weld metal is excessively increased, so that the strength of the weld metal becomes too high and the toughness is lowered. Therefore, C is 0.08 to 0.15% 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 the flux as metal powder, alloy powder, or the like.
［Ｓｉ：０．５〜１．５％］
Ｓｉは、溶接時に一部がスラグとなってビードの外観や形状を良好にし、溶接作業性の向上に寄与する。ここで、Ｓｉが０．５％未満では、ビードの外観や形状が不良となる。一方、Ｓｉが１．５％を超えると、溶接金属中に過剰に歩留まることにより、溶接金属の靱性が低下する。従って、鋼製外皮とフラックスの合計でＳｉは０．５〜１．５％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等の合金粉末で添加できる。
[Si: 0.5 to 1.5%]
Si partly becomes slag during welding to improve the appearance and shape of the bead and contribute to the improvement of welding workability. Here, when Si is less than 0.5%, the appearance and shape of the bead are poor. On the other hand, when Si exceeds 1.5%, the toughness of the weld metal decreases due to excessive yield in the weld metal. Therefore, Si is 0.5 to 1.5% in total of the steel outer shell and the flux. Si can be added as an alloy powder such as metal Si, Fe—Si, or Fe—Si—Mn from the flux in addition to the components contained in the steel outer sheath.
［Ｍｎ：１〜２．５％］
Ｍｎは、Ｓｉと同様、溶接時に一部がスラグとなってビードの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、溶接金属の強度と靱性を高める効果がある。ここで、Ｍｎが１％未満では、溶接ビードの外観や形状が不良となる。また、溶接金属の強度および靭性が不十分である。一方、Ｍｎが２．５％を超えると、溶接金属中に過剰に歩留まり、溶接金属の強度が高くなることにより、かえって靱性が低下する。従って、鋼製外皮とフラックスの合計でＭｎは１〜２．５％とする。なお、Ｍｎは、鋼製外皮に含まれる成分の他、フラックスから金属Ｍｎ、Ｆｅ−Ｍｎ、Ｆｅ−Ｓｉ−Ｍｎ等の合金粉末で添加できる。
[Mn: 1 to 2.5%]
Mn, like Si, becomes part of the slag during welding to improve the appearance and shape of the bead and contribute to the improvement of welding workability. Further, Mn has an effect of increasing the strength and toughness of the weld metal by yielding on the weld metal. Here, if Mn is less than 1%, the appearance and shape of the weld bead are poor. Moreover, the strength and toughness of the weld metal are insufficient. On the other hand, if Mn exceeds 2.5%, the yield is excessively increased in the weld metal, and the strength of the weld metal is increased. Therefore, Mn is 1 to 2.5% in total of the steel outer shell and the flux. Mn can be added as an alloy powder such as metal Mn, Fe-Mn, Fe-Si-Mn, etc. from the flux in addition to the components contained in the steel outer sheath.
［Ｃｕ：０．１〜０．５％］
Ｃｕは、溶接金属の組織を微細化し、靭性および強度を高める効果がある。ここで、Ｃｕが０．１％未満では、溶接金属の強度および靭性が不十分である。一方、Ｃｕが０．５％を超えると、溶接金属の強度が高くなり靭性が低下する。従って、鋼製外皮とフラックスの合計でＣｕは０．１〜０．５％とする。なお、Ｃｕは、鋼製外皮およびワイヤ表面に施したＣｕめっき分の他、フラックスから金属Ｃｕ、Ｆｅ−Ｓｉ−Ｃｕ等の合金粉末で添加できる。
[Cu: 0.1 to 0.5%]
Cu has the effect of refining the structure of the weld metal and increasing the toughness and strength. Here, if Cu is less than 0.1%, the strength and toughness of the weld metal are insufficient. On the other hand, when Cu exceeds 0.5%, the strength of the weld metal increases and the toughness decreases. Therefore, Cu is 0.1 to 0.5% in total of the steel outer shell and the flux. Cu can be added as an alloy powder such as metal Cu, Fe—Si—Cu, etc. from the flux in addition to the Cu plating applied to the steel outer sheath and the wire surface.
［Ｍｏ：０．１〜０．３５％］
Ｍｏは、溶接金属の焼入れ性を高める元素である。特に大入熱、高パス間温度の溶接施工条件では溶接金属の焼入れ効果が不足するので、強度を確保するうえで必須の元素である。Ｍｏが０．１％未満であると、溶接金属の強度が低下する。一方、Ｍｏが０．３５％を超えると、強度が高くなりすぎて靭性が低下する。従って、鋼製外皮とフラックスの合計でＭｏは０．１〜０．３５％とする。Ｍｏは、鋼製外皮およびフラックスから金属Ｍｏ、Ｆｅ−Ｍｏ等の合金粉末で添加できる。
[Mo: 0.1 to 0.35%]
Mo is an element that enhances the hardenability of the weld metal. In particular, it is an indispensable element for securing strength because the quenching effect of the weld metal is insufficient under the welding conditions of high heat input and high pass temperature. If the Mo content is less than 0.1%, the strength of the weld metal decreases. On the other hand, if Mo exceeds 0.35%, the strength becomes too high and the toughness decreases. Therefore, Mo is 0.1 to 0.35% in total of the steel outer shell and the flux. Mo can be added as an alloy powder such as metal Mo or Fe—Mo from a steel outer shell and flux.
［Ｔｉ：０．１〜０．３５％］
Ｔｉは、溶接金属の組織を微細化して靭性を向上させる効果がある。しかし、Ｔｉが０．１％未満では、溶接金属の靭性が不十分である。一方、Ｔｉが０．３５％を超えると、溶接金属の靭性を阻害する上部ベイナイト組織を生成し靭性が低くなる。従って、鋼製外皮とフラックスの合計でＴｉは０．１〜０．３５％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等の合金粉末で添加できる。
[Ti: 0.1 to 0.35%]
Ti has the effect of reducing the microstructure of the weld metal and improving toughness. However, if Ti is less than 0.1%, the toughness of the weld metal is insufficient. On the other hand, if Ti exceeds 0.35%, an upper bainite structure that inhibits the toughness of the weld metal is generated and the toughness is lowered. Therefore, Ti is 0.1 to 0.35% in total of the steel outer shell and the flux. Ti can be added as an alloy powder such as metal Ti or Fe—Ti from a flux in addition to components contained in the steel outer shell.
［Ｂ：０．００２〜０．０１％］
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、溶接金属の靱性を向上させる効果がある。しかし、Ｂが０．００２％未満では、溶接金属の靭性を向上する効果が得られない。一方、Ｂが０．０１％を超えると、溶接金属が過度に硬化することにより靱性が低下するとともに、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０．００２〜０．０１％とする。なお、Ｂは、鋼製外皮に含まれる成分の他、フラックスから金属Ｂ、Ｆｅ−Ｂ、Ｆｅ−Ｍｎ−Ｂ等で添加できる。
[B: 0.002 to 0.01%]
B has an effect of refining the microstructure of the weld metal by adding a small amount and improving the toughness of the weld metal. However, if B is less than 0.002%, the effect of improving the toughness of the weld metal cannot be obtained. On the other hand, if B exceeds 0.01%, the weld metal is excessively hardened and the toughness is lowered, and hot cracking is likely to occur. Therefore, B is 0.002 to 0.01% in total of the steel outer shell and the flux. B can be added from the flux as a metal B, Fe-B, Fe-Mn-B or the like in addition to the components contained in the steel outer sheath.
以下の成分はもっぱらフラックスに含有させるものであるが、各成分の含有量は既述の成分と同様にワイヤ全質量に対する質量％で表す。
［Ｎａ化合物およびＫ化合物のＮａ２Ｏ換算値とＫ２Ｏ換算値の合計：０．０５〜０．２％］
Ｎａ化合物およびＫ化合物は、アーク安定剤およびスラグ形成剤としてとして作用する。Ｎａ化合物およびＫ化合物のＮａ２Ｏ換算値とＫ２Ｏ換算値の合計が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、ビード外観も不良になる。一方、Ｎａ化合物およびＫ化合物のＮａ２Ｏ換算値とＫ２Ｏ換算値の合計が０．２％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が垂れやすくなる。従って、フラックスに含有するＮａ化合物およびＫ化合物のＮａ２Ｏ換算値とＫ２Ｏ換算値の合計は０．０５〜０．２％とする。なお、Ｎａ化合物およびＫ化合物は、カリ長石、弗化ソーダ、珪弗化カリウム等の粉末、ならびに珪酸ソーダおよび珪酸カリからなる水ガラスの固質成分から添加できる。
The following components are exclusively contained in the flux, but the content of each component is expressed in terms of mass% with respect to the total mass of the wire in the same manner as the components described above.
[Total of Na 2 O converted value and K 2 O converted value of Na compound and K compound: 0.05 to 0.2%]
Na and K compounds act as arc stabilizers and slag formers. When the total of Na 2 O converted value and K 2 O converted value of Na compound and K compound is less than 0.05%, the arc becomes unstable and the amount of spatter generated increases. Also, the bead appearance is poor. On the other hand, when the total of Na 2 O converted value and K 2 O converted value of Na compound and K compound exceeds 0.2%, the slag peelability becomes poor. In addition, the metal tends to sag in the vertical improvement welding. Therefore, the total of Na 2 O equivalent value and K 2 O equivalent value of Na compound and K compound contained in the flux is 0.05 to 0.2%. The Na compound and K compound can be added from a solid component of water glass composed of powders such as potassium feldspar, sodium fluoride, potassium silicofluoride, etc., and sodium silicate and potassium silicate.
［Ｓｉ酸化物のＳｉＯ２換算値の合計：０．１〜１％］
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の外観や形状が不良となる。一方、Ｓｉ酸化物のＳｉＯ２換算値の合計が１％を超えると、溶融スラグの塩基度が低下することにより、溶接金属の酸素量が増加して靭性が低下する。従って、フラックスに含有するＳｉ酸化物のＳｉＯ２換算値の合計は０．１〜１％とする。なお、Ｓｉ酸化物は、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 equivalent value of Si oxide: 0.1 to 1%]
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 oxide is less than 0.1%, the slag encapsulation is poor and the appearance and shape of the bead are poor. On the other hand, if the total SiO 2 equivalent value of the Si oxide exceeds 1%, the basicity of the molten slag is lowered, so that the oxygen content of the weld metal is increased and the toughness is lowered. Therefore, the total of SiO 2 conversion values of the Si oxide contained in the flux is 0.1 to 1%. Si oxide can be added from silica sand, zircon sand, sodium silicate, or the like.
［Ｍｇ：０．０４〜０．０８％］
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、溶接金属の靱性を高める効果がある。しかし、Ｍｇが０．０４％未満では、溶接金属の靭性の向上効果が十分に得られない。一方、Ｍｇが０．０８％を超えると、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、フラックスに含有するＭｇは０．０４〜０．０８％とする。なお、Ｍｇは、金属Ｍｇ、Ａｌ−Ｍｇ等の合金粉末から添加できる。
[Mg: 0.04-0.08%]
Mg functions as a strong deoxidizer to reduce oxygen in the weld metal and to increase the toughness of the weld metal. However, if Mg is less than 0.04%, the effect of improving the toughness of the weld metal cannot be obtained sufficiently. On the other hand, if Mg exceeds 0.08%, it reacts violently with oxygen in the arc during welding, and the amount of spatter and fumes generated increases. Therefore, Mg contained in the flux is 0.04 to 0.08%. In addition, Mg can be added from alloy powders, such as metal Mg and Al-Mg.
［Ａｌ酸化物のＡｌ２Ｏ３換算値の合計：０．１〜０．５％］
Ａｌ酸化物は、溶接時に溶接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溶融メタルが垂れるのを防ぐ効果がある。また、ビード外観を良好にする効果もある。しかし、Ａｌ酸化物のＡｌ２Ｏ３換算値の合計が０．１％未満では、立向上進溶接における溶融メタルが垂れるのを防ぐ効果およびビード外観を良好にする効果が十分に得られない。一方、Ａｌ酸化物のＡｌ２Ｏ３換算値の合計が０．５％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、靱性が低下する。従って、フラックスに含有するＡｌ酸化物のＡｌ２Ｏ３換算値の合計は０．１〜０．５％とする。なお、Ａｌ酸化物は、アルミナ等から添加できる。
[Total of Al 2 O 3 converted values of Al oxide: 0.1 to 0.5%]
The Al oxide has an effect of adjusting the viscosity and melting point of the welding slag during welding, and preventing the molten metal from dripping particularly in vertical improvement welding. It also has the effect of improving the bead appearance. However, if the total of Al 2 O 3 conversion values of Al oxides is less than 0.1%, the effect of preventing the molten metal from dripping and the effect of improving the bead appearance cannot be obtained sufficiently. On the other hand, if the total of Al 2 O 3 converted values of Al oxides exceeds 0.5%, the toughness decreases due to excessive Al oxide remaining in the weld metal. Therefore, the total of Al 2 O 3 conversion values of the Al oxide contained in the flux is 0.1 to 0.5%. The Al oxide can be added from alumina or the like.
［弗素化合物のＦ換算値の合計：０．０１〜０．２％］
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、アークを安定にする効果が十分に得られない。一方、弗素化合物のＦ換算値の合計が０．２％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、立向上進溶接では溶融メタル垂れが発生しやすくなる。従って、フラックスに含有する弗素化合物のＦ換算値の合計は０．０１〜０．２％とする。なお、弗素化合物は、ＣａＦ２、ＮａＦ、ＫＦ、ＬｉＦ、ＭｇＦ２、Ｋ２ＳｉＦ６、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 values of fluorine compounds: 0.01 to 0.2%]
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%, the effect of stabilizing the arc cannot be sufficiently obtained. On the other hand, if the total F converted value of the fluorine compound exceeds 0.2%, the arc becomes unstable and the amount of spatter generated increases. Further, molten metal dripping is likely to occur in the vertical improvement welding. Therefore, the total F converted value of the fluorine compound contained in the flux is 0.01 to 0.2%. The fluorine compound can be added from CaF 2 , NaF, KF, LiF, MgF 2 , K 2 SiF 6 , AlF 3, etc., and the F converted value is the total amount of F contained therein.
なお、本発明の炭酸ガスシールドアーク溶接用フラックス入りワイヤは、帯状の鋼製外皮をパイプ状に成形しつつ、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貫通した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貫通した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もできるが、鋼製外皮に貫通した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。 The flux-cored wire for carbon dioxide shielded arc welding according to the present invention has a structure in which a strip-shaped steel outer sheath is formed into a pipe shape and the inside thereof is filled with flux. There are two types of wires: a seamless wire that penetrates the steel outer shell obtained by welding the seam of the molded steel outer shell, and a steel outer shell that is left unwelded to the steel outer seam. It can be roughly divided into wires having a penetrated seam. In the present invention, a wire having any cross-sectional structure can be used, but a seamless wire that penetrates the steel outer shell can be heat-treated for the purpose of reducing the total amount of hydrogen in the wire. Moreover, since there is no moisture absorption of the flux after production, the amount of diffusible hydrogen in the weld metal can be reduced, and the cold cracking resistance can be improved, which is more preferable.
本発明の炭酸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、上記の成分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分およ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。溶接時のシールドガスは、鋼構造物の溶接施工に一般的に用いられている炭酸ガスとする。 In the flux-cored wire for carbon dioxide shielded arc welding of the present invention, the balance of the above components is Fe of steel outer sheath, iron powder added for component adjustment, Fe-Mn, Fe-Si alloy and other iron alloy powders Fe content and inevitable impurities. 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. Shielding gas at the time of welding is carbon dioxide gas generally used for welding construction of steel structures.
以下、本発明の効果を具体的に説明する。
ＪＩＳ Ｇ ３１４１に規定されるＳＰＣＣを鋼製外皮として使用して、鋼製外皮を成形する工程でＵ型に成形した状態で、各種フラックスを充填した。鋼製外皮の合わせ目を溶接して伸線し、貫通した継目が無いワイヤとすることにより、表１に示す各種成分のフラックス入りワイヤを試作した。ワイヤ径は１．２ｍｍとした。
The effects of the present invention will be specifically described below.
Using SPCC defined in JIS G 3141 as a steel outer shell, various fluxes were filled in a state of being formed into a U shape in the process of forming the steel outer shell. By welding and drawing a seam of a steel outer shell to obtain a wire without a penetrating seam, flux-cored wires having various components shown in Table 1 were prototyped. The wire diameter was 1.2 mm.
ＪＩＳ Ｇ ３１０６に規定される板厚２５ｍｍの鋼板ＳＭ４９０Ａを、ギャップ７ｍｍ、開先角度３５°のレ型の裏当金付開先として、試作ワイヤを使用して表２に示す溶接条件で多層盛溶接し、溶接作業性および溶接金属の機械的性能を評価した。溶接姿勢は下向であるが、結果の説明にも記載されているようにビード形状やビード外観の調査については立向上進溶接も行なった。 Using a steel wire SM490A with a thickness of 25 mm as defined in JIS G 3106 as a grooved backing groove with a gap of 7 mm and a groove angle of 35 °, using a prototype wire, multilayer welding is carried out as shown in Table 2. Welding was performed to evaluate the welding workability and the mechanical performance of the weld metal. Although the welding posture was downward, as described in the explanation of the results, vertical improvement welding was also conducted for the investigation of the bead shape and the bead appearance.
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、高温割れの有無について調査した。
溶接金属の機械的性能の試験は、溶接金属の板厚方向中央部から引張試験片（Ａ１号）および衝撃試験片（Ｖノッチ試験片）を採取して実施した。靭性の評価は、−２０℃におけるシャルピー衝撃試験により行い、各々繰返し３本の吸収エネルギーの平均が１００Ｊ以上を良好とした。引張試験の評価は、引張強さが６００ＭＰａ以上のものを良好とした。これらの結果を表３にまとめて示す。
Welding workability was evaluated by examining arc stability, spatter generation state, fume generation state, bead shape, bead appearance, and presence of hot cracks.
The test of the mechanical performance of the weld metal was carried out by collecting a tensile test piece (A1) and an impact test piece (V-notch test piece) from the central part in the plate thickness direction of the weld metal. The toughness was evaluated by a Charpy impact test at −20 ° C., and the average of the three absorbed energy was 100 J or more. The tensile test was evaluated as good when the tensile strength was 600 MPa or more. These results are summarized in Table 3.
表１および表３中ワイヤ記号１〜１２は本発明例、ワイヤ記号１３〜２５は比較例である。本発明例であるワイヤ記号１〜１２は、Ｃ、Ｓｉ、Ｍｎ、Ｃｕ、Ｍｏ、Ｔｉ、Ｂ、Ｎａ２Ｏ換算値とＫ２Ｏ換算値の合計およびＳｉＯ２換算値の合計が本発明において規定した範囲内であるので、アークの安定性、ビード外観・形状が良好であるとともに、溶接割れが無く、スパッタやヒュームの発生も少なく、溶接金属の引張強さおよび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 and 3, wire symbols 1 to 12 are examples of the present invention, and wire symbols 13 to 25 are comparative examples. In the present invention, wire symbols 1 to 12 are C, Si, Mn, Cu, Mo, Ti, B, the sum of Na 2 O converted value and K 2 O converted value, and the total of SiO 2 converted value in the present invention. Because it is within the specified range, the arc stability, bead appearance and shape are good, there are no weld cracks, spatter and fume are few, and the tensile strength and absorbed energy of the weld metal are also good. The result was extremely satisfactory.
比較例中ワイヤ記号１３は、Ｃが少ないので、アークが不安定で、溶接金属の引張強さが低かった。また、Ａｌ酸化物のＡｌ２Ｏ３換算値の合計が多いので、溶接金属の吸収エネルギーが低値であった。
ワイヤ記号１４は、Ｃが多いので、溶接金属の引張強さが高くなり吸収エネルギーが低値であった。
In the comparative example, the wire symbol 13 had less C, so the arc was unstable and the tensile strength of the weld metal was low. Moreover, since the total of Al 2 O 3 conversion values of Al oxide is large, the absorbed energy of the weld metal was low.
Since the wire symbol 14 has a large amount of C, the tensile strength of the weld metal was high and the absorbed energy was low.
ワイヤ記号１５は、Ｓｉが少ないので、ビードの外観および形状が不良であった。また、Ｓｉ酸化物のＳｉＯ２換算値の合計が多いので、溶接金属の吸収エネルギーが低値であった。
ワイヤ記号１６は、Ｓｉが多いので、溶接金属の吸収エネルギーが低値であった。また、Ｎａ化合物およびＫ化合物のＮａ２Ｏ換算値と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が不良で、スパッタ発生量も多かった。なお、弗素化合物を添加したがＦ換算値の合計が少ないので、アークを安定にする効果は得られなかった。
Since the wire symbol 15 has a small amount of Si, the appearance and shape of the bead were poor. Further, since the sum of SiO 2 converted value of Si oxide is large, the absorption energy of the weld metal was low.
Since the wire symbol 16 contains a large amount of Si, the absorbed energy of the weld metal was low. Further, since the total of Na 2 O converted value and K 2 O converted value of Na compound and K compound was small, the arc was unstable, the bead appearance was poor, and the amount of spatter was large. Although a fluorine compound was added, the total of F conversion values was small, so that the effect of stabilizing the arc could not be obtained.
ワイヤ記号１７は、Ｍｎが少ないので、ビードの外観および形状が不良であるとともに、溶接金属の引張強さが低く吸収エネルギーも低値であった。なお、Ａｌ酸化物を添加したがＡｌ２Ｏ３換算値の合計が少ないので、ビード外観および形状を良好にする効果は得られなかった。さらに、別途実施した立向上進溶接でメタル垂れが生じた。
ワイヤ記号１８は、Ｍｎが多いので、溶接金属の引張強さが高くなり吸収エネルギーが低値であった。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および形状が不良であった。
Since the wire symbol 17 had a small amount of Mn, the appearance and shape of the bead were poor, and the tensile strength of the weld metal was low and the absorbed energy was also low. Although the addition of Al oxide since the sum is small in terms of Al 2 O 3 value, the effect of improving the bead appearance and shape was not obtained. In addition, metal dripping occurred in the stand-up improvement welding that was performed separately.
Since the wire symbol 18 has a large amount of Mn, the tensile strength of the weld metal was high and the absorbed energy was low. Further, since the sum of SiO 2 converted value of Si oxide is small, the bead appearance and shape poor slag encapsulating was poor.
ワイヤ記号１９は、Ｃｕが少ないので、溶接金属の引張強さが低く吸収エネルギーも低値であった。また、ＮａおよびＫ化合物のＮａ２Ｏ換算値とＫ２Ｏ換算値の合計が多いので、スラグ剥離性が不良であった。
ワイヤ記号２０は、Ｃｕが多いので、溶接金属の引張強さが高くなり吸収エネルギーが低値であった。また、Ｍｇが多いので、スパッタおよびヒュームの発生量が多かった。
Since the wire symbol 19 has little Cu, the tensile strength of the weld metal was low and the absorbed energy was also low. Further, since the sum of the terms of Na 2 O values and K 2 O conversion value of Na and K compounds are often, slag removability was poor.
Since the wire symbol 20 has a large amount of Cu, the tensile strength of the weld metal was high and the absorbed energy was low. Moreover, since there was much Mg, the generation amount of spatter and fumes was large.
ワイヤ記号２１は、Ｍｏが少ないので、溶接金属の引張強さが低かった。また、Ｂが少ないので、溶接金属の吸収エネルギーが低値であった。
ワイヤ記号２２は、Ｍｏが多いので、溶接金属の引張強さが高くなり吸収エネルギーが低値であった。
Since the wire symbol 21 has little Mo, the tensile strength of the weld metal was low. Further, since B is small, the absorbed energy of the weld metal was low.
Since the wire symbol 22 has a large amount of Mo, the tensile strength of the weld metal was high and the absorbed energy was low.
ワイヤ記号２３は、Ｔｉが少ないので、溶接金属の吸収エネルギーが低値であった。また、Ｍｇが少ないので、溶接金属の吸収エネルギーを良好にする効果は得られなかった。
ワイヤ記号２４は、Ｔｉが多いので、クレータ部に高温割れが生じ、溶接金属の吸収エネルギーが低値であった。
Since the wire symbol 23 has a small amount of Ti, the absorbed energy of the weld metal was low. Moreover, since there was little Mg, the effect which makes the absorbed energy of a weld metal favorable was not acquired.
Since the wire symbol 24 has a large amount of Ti, high-temperature cracking occurred in the crater portion, and the absorbed energy of the weld metal was low.
ワイヤ記号２５は、Ｂが多いので、クレータ部に高温割れが生じ、溶接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換算値の合計が多いので、アークが不安定でスパッタの発生量が多かった。さらに、別途実施した立向上進溶接でメタル垂れが生じた。 Since the wire symbol 25 has a large amount of B, high-temperature cracking occurred in the crater portion, and the absorbed energy of the weld metal was low. In addition, since the total F converted value of the fluorine compound is large, the arc is unstable and the amount of spatter generated is large. In addition, metal dripping occurred in the stand-up improvement welding that was performed separately.
Claims (4)
ワイヤにおいて、鋼製外皮とフラックスの一方または両方に、ワイヤ全質量に対する質
量％で、
Ｃ ：０．０８〜０．１５％、
Ｓｉ：０．５〜１．５％、
Ｍｎ：１〜２．５％、
Ｃｕ：０．１〜０．５％、
Ｍｏ：０．１〜０．３５％、
Ｔｉ：０．１〜０．３５％、
Ｂ ：０．００２〜０．０１％
を含有し、フラックスに、ワイヤ全質量に対する質量％で、
Ｎａ化合物およびＫ化合物のＮａ2Ｏ換算値とＫ2Ｏ換算値の合計：０．０５〜０．２％、
Ｓｉ酸化物のＳｉＯ2換算値の合計：０．１〜１％
を含有し、残部は鋼製外皮のＦｅ、鉄合金粉のＦｅ分、鉄粉および不可避不純物からなることを特徴とする炭酸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 carbon dioxide shielded arc welding formed by filling a steel outer shell with flux, in one or both of the steel outer shell and the flux, in mass% with respect to the total mass of the wire,
C: 0.08 to 0.15%,
Si: 0.5 to 1.5%
Mn: 1 to 2.5%
Cu: 0.1 to 0.5%,
Mo: 0.1 to 0.35%,
Ti: 0.1 to 0.35%,
B: 0.002 to 0.01%
In the flux, the mass% relative to the total mass of the wire,
Total of Na 2 O converted value and K 2 O converted value of Na compound and K compound: 0.05 to 0.2%,
Total of SiO 2 conversion value of Si oxide: 0.1 to 1%
A balance-cored wire for carbon dioxide shielded arc welding, wherein the balance is made of Fe of steel outer shell, Fe content of iron alloy powder, iron powder and inevitable impurities.
含有することを特徴とする請求項１に記載の炭酸ガスシールドアーク溶接用フラックス 入りワイヤ。 The flux-cored wire for carbon dioxide shielded arc welding according to claim 1, wherein the flux further contains Mg: 0.04 to 0.08% by mass% with respect to the total mass of the wire.
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| JP6437378B2 (en) * | 2015-04-28 | 2018-12-12 | 日鐵住金溶接工業株式会社 | Flux-cored wire for gas shielded arc welding |
| JP6486844B2 (en) * | 2016-01-28 | 2019-03-20 | 日鐵住金溶接工業株式会社 | Flux-cored wire for gas shielded arc welding |
| JP6599808B2 (en) * | 2016-03-25 | 2019-10-30 | 日鉄溶接工業株式会社 | Flux-cored wire for electroslag welding of high strength steel |
| JP6663327B2 (en) * | 2016-08-25 | 2020-03-11 | 日鉄溶接工業株式会社 | Flux-cored wire for electroslag welding |
| JP6688192B2 (en) * | 2016-08-25 | 2020-04-28 | 日鉄溶接工業株式会社 | Flux-cored wire for electroslag welding |
| JP6988323B2 (en) * | 2017-09-27 | 2022-01-05 | 日本製鉄株式会社 | Gas shield arc Welding flux-cored wire and welding joint manufacturing method |
| JP6988324B2 (en) * | 2017-09-27 | 2022-01-05 | 日本製鉄株式会社 | Gas shield arc Welding flux-cored wire and welding joint manufacturing method |
| 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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| JP4676940B2 (en) * | 2005-10-20 | 2011-04-27 | 新日本製鐵株式会社 | Manufacturing method of metal-based flux cored wire with low slag and high fatigue strength welded joint |
| JP5194593B2 (en) * | 2007-07-10 | 2013-05-08 | 新日鐵住金株式会社 | Flux-cored welding wire for gas shielded arc welding of refractory steel |
| JP2009178737A (en) * | 2008-01-30 | 2009-08-13 | Kobe Steel Ltd | Solid wire for carbon dioxide shielded arc welding |
| JP5310108B2 (en) * | 2008-03-28 | 2013-10-09 | 新日鐵住金株式会社 | Flux-filled ultra-low hydrogen welding wire and manufacturing method thereof |
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