JP6661516B2 - Non-consumable nozzle type electroslag welding method and method for manufacturing electroslag welding joint - Google Patents
Non-consumable nozzle type electroslag welding method and method for manufacturing electroslag welding joint Download PDFInfo
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Description
本発明は、溶接入熱が４００ｋＪ／ｃｍ以上１１００ｋＪ／ｃｍ以下の非消耗ノズル式エレクトロスラグ溶接方法に関し、特にフラックス入りワイヤを用いて良好な溶接性と良好な溶接金属靭性値を得ることを可能とする非消耗ノズル式エレクトロスラグ溶接方法及びエレクトロスラグ溶接継手の製造方法に関する。 The present invention relates to a non-consumable nozzle type electroslag welding method having a welding heat input of 400 kJ / cm or more and 1100 kJ / cm or less, and in particular, it is possible to obtain good weldability and good weld metal toughness using a flux-cored wire. The present invention relates to a non-consumable nozzle type electroslag welding method and a method for manufacturing an electroslag welding joint.
エレクトロスラグ溶接は、大入熱の１パス溶接による高能率な溶接が可能であるため、鉄骨の四面ＢＯＸ柱における内ダイアフラムの立向溶接に多く用いられている溶接方法である。近年は溶接の容易さや溶接能率の観点から、非消耗ノズル式のエレクトロスラグ溶接が普及している。ところで、非消耗ノズル式のエレクトロスラグ溶接（特許文献１）では消耗ノズル式のエレクトロスラグ溶接に比べて溶接中にアークが発生する問題が発生しやすい。 Electroslag welding is a welding method widely used for vertical welding of an inner diaphragm in a four-sided BOX column of a steel frame because highly efficient welding by one-pass welding with large heat input is possible. In recent years, non-consumable nozzle type electroslag welding has become widespread from the viewpoint of ease of welding and welding efficiency. By the way, in non-consumable nozzle type electroslag welding (Patent Document 1), a problem that an arc is generated during welding is more likely to occur than in consumable nozzle type electroslag welding.
エレクトロスラグ溶接では、溶接金属に微量のＴｉとＢを添加させることにより、溶接金属の組織を微細化し、溶接金属の靭性を改善する方法があるが、アークが発生することにより、溶接金属が窒素吸収し、溶接金属の靭性が劣化する問題がある。
さらにアークが発生すると、溶融スラグの温度が低下するため、溶け込みが減少し、連続して発生すると溶け込み不足の欠陥が生じる問題がある。
In electroslag welding, there is a method of adding a small amount of Ti and B to the weld metal to refine the structure of the weld metal and improve the toughness of the weld metal. There is a problem of absorption and deterioration of the toughness of the weld metal.
Further, when an arc is generated, the temperature of the molten slag is lowered, so that the penetration is reduced. When the arc is generated continuously, there is a problem that a defect of insufficient penetration occurs.
そこで、エレクトロスラグ溶接における溶接性改善を目的とした技術が、特許文献２に開示されている。特許文献２では、フラックス入りワイヤを使用することにより、溶接時の矯正が容易で非消耗ノズル部及び矯正ローラ部での送給抵抗を小さくすることが可能になると開示されている。 Therefore, a technique for improving the weldability in electroslag welding is disclosed in Patent Document 2. Patent Literature 2 discloses that the use of a flux-cored wire facilitates correction during welding and makes it possible to reduce feed resistance at a non-consumable nozzle portion and a correction roller portion.
しかしながら、特許文献２に記載の技術では、溶接長全長に渡って安定したエレクトロスラグ溶接を行うことが出来ない。溶接長６００ｍｍを超える溶接後半になると、溶接中にアークが発生しやすく、溶接性が安定せず、溶接線方向での安定した溶け込みや靭性値を得ることができるとはいえない。 However, the technique described in Patent Document 2 cannot perform stable electroslag welding over the entire welding length. In the latter half of welding with a welding length of more than 600 mm, an arc is easily generated during welding, the weldability is not stable, and it cannot be said that stable penetration and toughness value in the weld line direction can be obtained.
本発明はかかる問題点に鑑みてなされたものであって、入熱が４００ｋＪ／ｃｍ以上１１００ｋＪ／ｃｍ以下の大入熱エレクトロスラグ溶接においても、溶接継手方向で安定した溶接性と溶接金属の高靭性値を得ることができる非消耗ノズル式エレクトロスラグ溶接方法及びエレクトロスラグ溶接継手の製造方法を提供することを課題とする。 The present invention has been made in view of such a problem, and even in a large heat input electroslag welding having a heat input of 400 kJ / cm or more and 1100 kJ / cm or less, stable weldability in the weld joint direction and high weld metal. An object of the present invention is to provide a non-consumable nozzle type electroslag welding method and a method for manufacturing an electroslag welded joint capable of obtaining a toughness value.
本発明に係る非消耗ノズル式エレクトロスラグ溶接方法は、鋼製外皮の内部にフラックスを充填してなる溶接ワイヤおよび前記フラックスとは別に溶接箇所に投入される溶接フラックスを用い、前記溶接ワイヤは、ワイヤ全質量に対して、Ｃ：０．０１０乃至０．１０質量％、Ｓｉ：０．８質量％以下、Ｍｎ：０．９乃至２．８質量％、Ｍｏ：０．１０乃至２．００質量％、Ａｌ：０．００５乃至０．０４０質量％、Ｔｉ：０．０５乃至０．１４質量％、Ｂ：０．０１１０乃至０．０２７０質量％を含有し、Ｎｉ：３．００質量％以下、Ｃｕ：３．００質量％以下、Ｃｒ：０．３０質量％以下、Ｖ：０．０３０質量％以下、Ｎｂ：０．０３０質量％以下の１種または２種以上を含有し、残部がＦｅ及び不可避的不純物からなる組成を有するメタル系フラックス入りワイヤであり、前記溶接フラックスが、溶接フラックス全質量に対して、ＳｉＯ2：１５乃至４５質量％、ＣａＯ：５乃至２１質量％、ＣａＦ2：１乃至１３質量％、ＭｇＯ：１６質量％以下、Ａｌ2Ｏ3：１７質量％以下、ＭｎＯ：２５質量％以下、ＴｉＯ2：２乃至１５質量％、ＦｅＯ：４．５質量％以下、Ｂ 2 Ｏ 3 ：１．５質量％以下を含有し、残部が不可避的不純物からなる組成を有し、溶接後のスラグが、スラグ全質量に対して、ＳｉＯ2：１５乃至４５質量％、ＣａＯ：５乃至２１質量％、ＣａＦ2：１乃至１３質量％、ＭｇＯ：１６質量％以下、Ａｌ2Ｏ3：１７質量％以下、ＭｎＯ：２５質量％以下、ＴｉＯ2：２乃至１５質量％、ＦｅＯ：４．５質量％以下、Ｂ 2 Ｏ 3 ：１．５質量％以下を含有し、残部が不可避的不純物からなる組成を有する。 The non-consumable nozzle type electroslag welding method according to the present invention uses a welding wire formed by filling a flux inside a steel sheath and a welding flux that is fed to a welding location separately from the flux, and the welding wire is C: 0.010 to 0.10% by mass, Si: 0.8% by mass or less, Mn: 0.9 to 2.8% by mass, Mo: 0.10 to 2.00% by mass based on the total mass of the wire. %, Al: 0.005 to 0.040% by mass, Ti: 0.05 to 0.14% by mass, B: 0.0110 to 0.0270% by mass, Ni: 3.00% by mass or less, Cu: 3.00% by mass or less, Cr: 0.30% by mass or less, V: 0.030% by mass or less, Nb: One or more types of 0.030% by mass or less, with the balance being Fe and A material having a composition consisting of unavoidable impurities A Le-based flux cored wire, the welding flux, relative to the welding flux to the total mass, SiO 2: 15 to 45 wt%, CaO: 5 to 21 wt%, CaF 2: 1 to 13 wt%, MgO: 16 mass% or less, Al 2 O 3: 17 wt% or less, MnO: 25 wt% or less, TiO 2: 2 to 15 wt%, FeO: 4.5 wt% or less, B 2 O 3: 1.5 wt% or less contain, comprises the balance consisting of unavoidable impurities, slag after welding, with respect to slag total weight, SiO 2: 15 to 45 wt%, CaO: 5 to 21 wt%, CaF 2: 1 to 13 wt%, MgO: 16 wt% or less, Al 2 O 3: 17 wt% or less, MnO: 25 wt% or less, TiO 2: 2 to 15 wt%, FeO: 4.5 wt% or less, B 2 O 3 : 1.5% by mass or less , The balance has a composition consisting of unavoidable impurities .
また、前記非消耗ノズル式エレクトロスラグ溶接方法において、溶接電流を３５０乃至４１０Ａ、溶接電圧を４４乃至５４Ｖとし、ワイヤ送給速度を６．５乃至１１．０ｍ／ｍｉｎとして、溶接ワイヤの曲率を直径で５００乃至２３００ｍｍの範囲に調整して溶接する。 Further, in the non-consumable nozzle type electroslag welding method, the welding current is 350 to 410 A, the welding voltage is 44 to 54 V, the wire feeding speed is 6.5 to 11.0 m / min, and the curvature of the welding wire is a diameter. Is adjusted to a range of 500 to 2300 mm by welding.
本発明に係るエレクトロスラグ溶接継手の製造方法は、前記非消耗ノズル式エレクトロスラグ溶接方法により作製する。 The method for manufacturing an electroslag welding joint according to the present invention is manufactured by the non-consumable nozzle type electroslag welding method.
本発明の非消耗ノズル式エレクトロスラグ溶接方法及びエレクトロスラグ溶接継手の溶接方法によれば、大入熱エレクトロスラグ溶接においても、溶接継手方向で安定した溶接性と高靭性を確保することができるという効果を奏する。 According to the non-consumable nozzle electroslag welding method and the electroslag welding joint welding method of the present invention, it is possible to secure stable weldability and high toughness in the direction of the weld joint even in large heat input electroslag welding. It works.
本発明者等は、入熱が４００ｋＪ／ｃｍ以上１１００ｋＪ／ｃｍ以下の大入熱エレクトロスラグ溶接においても、溶接継手方向で安定した溶接性と高靭性を確保することができる非消耗ノズル式エレクトロスラグ溶接方法及びエレクトロスラグ溶接継手の製造方法を開発すべく、鋭意実験研究を行った。その結果、エレクトロスラグ溶接中のスラグ成分の変化が溶接作業性に大きな影響を及ぼすことを知見し、溶接中のスラグ成分をコントロールすることが、溶接長全長に渡って、特に溶接長が長い場合において安定した溶接作業性と高靭性の確保に必須であることを見出した。 The present inventors have developed a non-consumable nozzle type electroslag capable of securing stable weldability and high toughness in the direction of a weld joint even in large heat input electroslag welding having a heat input of 400 kJ / cm or more and 1100 kJ / cm or less. In order to develop a welding method and a method for manufacturing an electroslag welded joint, intensive experimental research was conducted. As a result, it was found that the change of the slag component during electroslag welding has a great effect on the welding workability, and that controlling the slag component during welding can be performed over the entire welding length, especially when the welding length is long. It was found that it was indispensable to ensure stable welding workability and high toughness.
更に、溶接ワイヤの形態を、鋼製外皮の内部にフラックスを充填してなるメタル系フラックス入りワイヤとすることで、従来のソリッドワイヤよりもワイヤの送給抵抗を低減させることが可能となり、その結果、溶接作業性の安定化と、溶接金属の靭性を安定化するのに有利であることを見出し、本発明を完成させた。 Furthermore, by making the form of the welding wire a metal-based flux-cored wire obtained by filling the inside of a steel sheath with a flux, it becomes possible to reduce the feed resistance of the wire compared to a conventional solid wire. As a result, they have found that it is advantageous to stabilize the welding workability and stabilize the toughness of the weld metal, and have completed the present invention.
以下に、本発明の非消耗ノズル式エレクトロスラグ溶接方法について詳細に説明する。 Hereinafter, the non-consumable nozzle type electroslag welding method of the present invention will be described in detail.
先ず、非消耗ノズル式エレクトロスラグ溶接方法にて使用する溶接ワイヤであるメタル系フラックス入りワイヤについて、説明する。 First, a metal flux cored wire which is a welding wire used in the non-consumable nozzle type electroslag welding method will be described.
メタル系フラックス入りワイヤの組成（即ち、鋼製外皮とその内部に充填した金属粉末とを総合した成分の組成）は、所定量のＣ、Ｓｉ、Ｍｎ、Ｍｏ、Ａｌ、Ｔｉ、Ｂを含有し、所定量のＮｉ、Ｃｕ、Ｃｒ、Ｖ、Ｎｂの１種または２種以上を含有し、残部がＦｅ及び不可避的不純物からなる。その限定理由について説明する。 The composition of the metal-based flux-cored wire (that is, the composition of the components obtained by integrating the steel sheath and the metal powder filled therein) contains predetermined amounts of C, Si, Mn, Mo, Al, Ti, and B. , A predetermined amount of one or more of Ni, Cu, Cr, V, and Nb, with the balance being Fe and unavoidable impurities. The reason for the limitation will be described.
「Ｃ：０．０１０乃至０．１０質量％」
Ｃは、溶接金属の強度と靭性を確保するために有効な元素であるが、Ｃ含有量が０．０１０質量％未満では、その効果が得られない。一方、Ｃ含有量が０．１０質量％を超えると硬化組織が増大し、靭性が低下する。よって、Ｃ含有量は０．０１０乃至０．１０質量％とする。Ｃ源としては、鋼製外皮、グラファイト、鉄粉、Ｆｅ−Ｍｎ等の金属粉、合金粉を用いる。なお、より好ましい範囲としては、Ｃ：０．０１０乃至０．０５０質量％である。
"C: 0.010 to 0.10% by mass"
C is an element effective for securing the strength and toughness of the weld metal. However, if the C content is less than 0.010% by mass, the effect cannot be obtained. On the other hand, if the C content exceeds 0.10% by mass, the hardened structure increases and the toughness decreases. Therefore, the C content is set to 0.010 to 0.10% by mass. As the C source, a steel shell, graphite, iron powder, metal powder such as Fe-Mn, or alloy powder is used. Note that a more preferable range is C: 0.010 to 0.050 mass%.
「Ｓｉ：０．８質量％以下」
Ｓｉは、Ｓｉ含有量が０．８質量％を超えると、溶接金属の高温割れが発生しやすくなり、更に島状マルテンサイトという低靭性組織の生成が顕著となり、溶接金属の靭性が著しく劣化する。よって、Ｓｉ含有量は０．８質量％以下とする。Ｓｉ源としては、鋼製外皮、Ｆｅ−Ｓｉ、Ｆｅ−Ｓｉ−Ｍｎ等の合金粉を用いる。
"Si: 0.8% by mass or less"
When the Si content exceeds 0.8% by mass, high-temperature cracking of the weld metal is liable to occur, and further, the formation of a low toughness structure called island-like martensite becomes remarkable, and the toughness of the weld metal remarkably deteriorates. . Therefore, the Si content is set to 0.8% by mass or less. As the Si source, a steel shell, alloy powder such as Fe-Si, Fe-Si-Mn is used.
「Ｍｎ：０．９乃至２．８質量％」
Ｍｎは、脱酸剤として作用すると共に焼入れ性を向上させる効果があり、溶接金属の靭性安定化のために必要な元素である。しかし、Ｍｎ含有量が０．９質量％未満の場合、十分な焼入れ性、靭性が得られない。一方、Ｍｎ含有量が２．８質量％を超えると、焼入れ性が高くなり過ぎ、強度が上がり、耐高温割れ性が劣化すると共に、靭性が劣化する。よ
って、Ｍｎ含有量は０．９乃至２．８質量％とする。Ｍｎ源としては、外皮金属、金属Ｍｎ、Ｆｅ−Ｍｎ、Ｆｅ−Ｓｉ−Ｍｎ等の金属粉、合金粉を用いる。
"Mn: 0.9 to 2.8 mass%"
Mn acts as a deoxidizing agent and has an effect of improving hardenability, and is an element necessary for stabilizing the toughness of a weld metal. However, when the Mn content is less than 0.9% by mass, sufficient hardenability and toughness cannot be obtained. On the other hand, if the Mn content exceeds 2.8% by mass, the hardenability becomes too high, the strength increases, the hot cracking resistance deteriorates, and the toughness deteriorates. Therefore, the Mn content is set to 0.9 to 2.8% by mass. As the Mn source, a metal powder such as a shell metal, metal Mn, Fe-Mn, and Fe-Si-Mn, or an alloy powder is used.
「Ｍｏ：０．１０乃至２．００質量％」
Ｍｏは、焼入れ性を高め、溶接金属の強度と靭性の向上に大きな効果があるが、Ｍｏ含有量が０．１０質量％未満であると、上記効果が期待できない。一方、Ｍｏ含有量が２．００質量％を超えると、溶接金属の高温割れが発生する可能性があり、かつ、過剰な硬化により溶接金属の靭性が劣化する。よって、Ｍｏ含有量は０．１０乃至２．００質量％とする。Ｍｏ源としては、Ｆｅ−Ｍｏ等合金粉を用いる。
"Mo: 0.10 to 2.00 mass%"
Mo has a significant effect on enhancing the hardenability and improving the strength and toughness of the weld metal, but if the Mo content is less than 0.10% by mass, the above effects cannot be expected. On the other hand, if the Mo content exceeds 2.00% by mass, hot cracking of the weld metal may occur and the toughness of the weld metal deteriorates due to excessive hardening. Therefore, the Mo content is set to 0.10 to 2.00% by mass. An alloy powder such as Fe-Mo is used as the Mo source.
「Ａｌ：０．００５乃至０．０４０質量％」
Ａｌは、溶接金属の脱酸効果のため含有される元素である。しかし、Ａｌ含有量が０．００５質量％未満の場合、その効果が発揮されず、溶接金属の焼入れ性が低下し、靭性の劣化が生じる。一方、Ａｌ含有量が０．０４０質量％を超えると、Ａｌ酸化物が多量に形成され、アシキュラーフェライトの生成核となるＴｉ酸化物の生成を阻害するため、靭性が劣化する。また、スラグ中のＳｉＯ２が低下し、溶接停止などの問題が発生する。よって、Ａｌ含有量は０．００５乃至０．０４０質量％とする。Ａｌ源としては、金属Ａｌ、Ｆｅ−Ａｌ等の金属粉及び合金粉を用いる。
"Al: 0.005 to 0.040 mass%"
Al is an element contained for the deoxidizing effect of the weld metal. However, when the Al content is less than 0.005% by mass, the effect is not exhibited, the hardenability of the weld metal is reduced, and the toughness is deteriorated. On the other hand, if the Al content exceeds 0.040% by mass, a large amount of Al oxide is formed, which inhibits the generation of Ti oxide, which is a nucleus for producing acicular ferrite, and thus deteriorates toughness. In addition, SiO 2 in the slag is reduced, and problems such as stopping welding occur. Therefore, the Al content is set to 0.005 to 0.040% by mass. As the Al source, metal powders such as metal Al and Fe-Al and alloy powders are used.
「Ｔｉ：０．０５乃至０．１４質量％」
Ｔｉは、脱酸材として作用し、溶接中のスラグ組成に大きな影響を与える元素であり、さらにはＴｉ酸化物としてアシキュラーフェライトを生成する核となり、粗大な粒界フェライトの生成を防止するために必要な元素である。しかし、Ｔｉ含有量が０．０５質量％未満の場合、酸化物の生成が不十分で、溶接金属の靭性向上が得られない。一方、Ｔｉ含有量が０．１４質量％を超えると、溶接中のスラグにおけるＴｉ酸化物の割合が増大し、かつスラグ中のＳｉＯ２の割合が減少するため、スラグの電気伝導度が低下し、わずかのワイヤ送給速度変動によりアークが発生するようになり、溶接性の劣化と窒素の吸収による靭性の劣化が生じる。よって、Ｔｉ含有量は０．０５乃至０．１４質量％とする。Ｔｉ源としては、Ｆｅ−Ｔｉ等の合金粉を用いる。
"Ti: 0.05 to 0.14 mass%"
Ti is an element that acts as a deoxidizing material and has a great effect on the slag composition during welding, and further serves as a nucleus for producing an acicular ferrite as a Ti oxide and for preventing the production of coarse grain boundary ferrite. Element required for However, when the Ti content is less than 0.05% by mass, the generation of oxides is insufficient, and the improvement in toughness of the weld metal cannot be obtained. On the other hand, if the Ti content exceeds 0.14% by mass, the proportion of Ti oxide in the slag during welding increases, and the proportion of SiO 2 in the slag decreases, so that the electrical conductivity of the slag decreases. An arc is generated due to a slight fluctuation in the wire feeding speed, so that weldability is deteriorated and toughness is deteriorated due to nitrogen absorption. Therefore, the Ti content is set to 0.05 to 0.14% by mass. An alloy powder such as Fe-Ti is used as a Ti source.
「Ｂ：０．０１１０乃至０．０２７０質量％」
Ｂは、溶接金属の焼入れ性を向上させ、初析フェライトの成長の抑制により、靭性を向上させる元素である。しかし、Ｂ含有量が０．０１１０質量％未満の場合、上記効果が期待できない。一方、Ｂ含有量が０．０２７０質量％を超えると、溶接金属の焼入れ性が過剰となるため、高温割れが発生しやすくなるとともに、マルテンサイト相の生成により溶
接金属の靭性が劣化する。よって、Ｂ含有量は０．０１１０乃至０．０２７０質量％とする。なお、より好ましい範囲としては、Ｂ：０．０１３０乃至０．０２００質量％である。Ｂ源としてはＦｅ−Ｂ、Ｆｅ−Ｓｉ−Ｂ等の合金粉、特殊ガラス等の複合酸化物を用いる。
"B: 0.0110 to 0.0270 mass%"
B is an element that improves the hardenability of the weld metal and suppresses the growth of proeutectoid ferrite, thereby improving the toughness. However, when the B content is less than 0.0110% by mass, the above effects cannot be expected. On the other hand, if the B content exceeds 0.0270% by mass, the hardenability of the weld metal becomes excessive, so that hot cracking is likely to occur, and the toughness of the weld metal deteriorates due to the formation of a martensite phase. Therefore, the B content is set to 0.0110 to 0.0270% by mass. A more preferable range is B: 0.0130 to 0.0200% by mass. As the B source, alloy powders such as Fe-B and Fe-Si-B, and composite oxides such as special glass are used.
「Ｎｉ：３．００質量％以下」
Ｎｉは、溶接金属の靭性を高める効果があるが、Ｎｉ含有量が３．００質量％を超えると、Ａ３変態点の低下により、固液共存域を増加させ、結果として耐高温割れ性が劣化する。よって、Ｎｉ含有量は３．００質量％以下とする。Ｎｉ源としては、金属Ｎｉ、Ｎｉ−Ｍｇ等の金属粉、合金粉を用いる。
"Ni: 3.00 mass% or less"
Ni has the effect of increasing the toughness of the weld metal, but when the Ni content exceeds 3.00 mass%, the solid-liquid coexistence region increases due to a decrease in the A3 transformation point, and as a result, the hot crack resistance deteriorates. I do. Therefore, the Ni content is set to 3.00% by mass or less. As the Ni source, metal powder such as metal Ni, Ni—Mg, or alloy powder is used.
「Ｃｕ：３．００質量％以下」
Ｃｕは、溶接金属の強度を高める働きがあるが、Ｃｕ含有量が３．００質量％を超えると、溶接金属の高温割れが発生する危険性が増大するばかりでなく、過剰な硬化が生じて溶接金属の靭性が劣化する。よって、Ｃｕ含有量は３．００質量％以下とする。Ｃｕ源としては、フラックス入りワイヤの表面へのＣｕ鍍金又はＣｕ粉を用いる。
"Cu: 3.00% by mass or less"
Cu has the function of increasing the strength of the weld metal, but if the Cu content exceeds 3.00 mass%, not only does the risk of hot cracking of the weld metal increase, but also excessive hardening occurs. The toughness of the weld metal deteriorates. Therefore, the Cu content is set to 3.00% by mass or less. As the Cu source, Cu plating or Cu powder on the surface of the flux-cored wire is used.
「Ｃｒ：０．３０質量％以下」
Ｃｒは、溶接金属の組織を微細化し、かつ強度を高める働きがあるが、Ｃｒ含有量が０．３０質量％を超えると、溶接金属が硬化して靭性が劣化する。よって、Ｃｒ含有量は０．３０質量％以下とする。Ｃｒ源としては、金属Ｃｒ、Ｆｅ−Ｃｒ、Ｆｅ−Ｓｉ−Ｃｒ等の金属粉、合金粉を用いる。
"Cr: 0.30% by mass or less"
Cr has the function of refining the structure of the weld metal and increasing the strength. However, if the Cr content exceeds 0.30% by mass, the weld metal hardens and the toughness deteriorates. Therefore, the Cr content is set to 0.30% by mass or less. As the Cr source, metal powders such as metal Cr, Fe—Cr, and Fe—Si—Cr, and alloy powders are used.
「Ｖ：０．０３０質量％以下」
Ｖは、溶接金属の強度靭性の向上のために添加できるが、Ｖ含有量が０．０３０質量％を超えると、溶接金属が硬化して靭性が劣化する。よって、Ｖ含有量は０．０３０質量％以下とする。Ｖ源としては、Ｆｅ−Ｖ等の合金粉を用いる。
"V: 0.030% by mass or less"
V can be added to improve the strength and toughness of the weld metal. However, if the V content exceeds 0.030% by mass, the weld metal hardens and the toughness deteriorates. Therefore, the V content is set to 0.030% by mass or less. An alloy powder such as Fe-V is used as the V source.
「Ｎｂ：０．０３０質量％以下」
Ｎｂは、同様に溶接金属の強度靭性を向上するために添加できるが、Ｎｂ含有量が０．０３０質量％を超えると、溶接金属が硬化して靭性が劣化する。よって、Ｎｂ含有量は０．０３０質量％以下とする。Ｎｂ源としては、Ｆｅ−Ｎｂ等の合金粉を用いる。
"Nb: 0.030% by mass or less"
Nb can be similarly added to improve the strength and toughness of the weld metal. However, if the Nb content exceeds 0.030% by mass, the weld metal hardens and the toughness deteriorates. Therefore, the Nb content is set to 0.030% by mass or less. An alloy powder such as Fe-Nb is used as the Nb source.
本発明の溶接ワイヤであるフラックス入りワイヤでは、上記の成分に加えて、希土類元素（ＲＥＭ）の１種又は２種以上を合計量（希土類元素換算値）で０．０５０質量％以下を含有してもよい。 The flux cored wire which is the welding wire of the present invention contains, in addition to the above components, one or more rare earth elements (REM) in a total amount (rare earth element conversion value) of 0.050 mass% or less. You may.
「希土類元素の１種又は２種以上の合計量（希土類元素換算値）：０．０５０質量％以下」
希土類元素（ＲＥＭ）は、硫化物を生成することによってＳを固定し、Ｓに起因する溶接金属の靭性向上作用を有する。また、強脱酸剤でもあり、靭性向上効果作用を有する。ＲＥＭ含有量が０．０５０質量％を超えると、溶接金属中のＳｉ、Ｍｎ、Ｔｉ等の脱酸剤の歩留まりが大きくなり、強度が高くなり、靭性向上効果が小さくなることから、ＲＥＭを添加する場合は０．０５０質量％以下とする。ここでいう、希土類元素とは、周期律表の３族（Ｓｃ、Ｙ及び原子番号５７（Ｌａ）乃至７１（Ｌｕ））に属する元素である。また、希土類元素は希土類化合物として含有され、希土類化合物とは、希土類元素の酸化物（Ｎｄ２Ｏ３，Ｌａ２Ｏ３，Ｙ２Ｏ３，ＣｅＯ３，Ｃｅ２Ｏ３、Ｓｃ２Ｏ３等の単体の酸化物及びこれらの複合酸化物並びにモナザイト、バストネサイト、アラナイト、セライト、ゼノタイム、ガドリナイト等の希土類酸化物の鉱石を含む）、弗化物（ＣｅＦ３，ＬｎＦ３，ＰｍＦ３，ＳｍＦ３，ＧｄＦ３，ＴｂＦ３等）及び合金（希土類元素−Ｆｅ、希土類元素−Ｆｅ−Ｂ，希土類元素−Ｆｅ−Ｃｏ、希土類元素−Ｆｅ−Ｓｉ、希土類元素−Ｃａ−Ｓｉ等）をいう。
"Total amount of one or more rare earth elements (rare earth element conversion value): 0.050 mass% or less"
The rare earth element (REM) fixes S by generating sulfide, and has an effect of improving the toughness of the weld metal caused by S. Also, it is a strong deoxidizing agent and has an effect of improving toughness. When the REM content exceeds 0.050% by mass, the yield of deoxidizing agents such as Si, Mn, and Ti in the weld metal increases, the strength increases, and the effect of improving toughness decreases. In this case, the content is 0.050% by mass or less. Here, the rare earth element is an element belonging to Group 3 of the periodic table (Sc, Y and atomic numbers 57 (La) to 71 (Lu)). The rare earth element is contained as a rare earth compound. The rare earth compound is a rare earth element oxide (Nd 2 O 3 , La 2 O 3 , Y 2 O 3 , CeO 3 , Ce 2 O 3 , Sc 2 O 3, etc. And oxides thereof, and ores of rare earth oxides such as monazite, bastnaesite, alanite, celite, xenotime, and gadolinite, and fluorides (CeF 3 , LnF 3 , PmF 3 , SmF 3). refers GdF 3, TbF 3, etc.) and alloys (rare earth element -Fe, rare earth elements -Fe-B, rare earth elements -Fe-Co, rare earth elements -Fe-Si, a rare earth element -Ca-Si, etc.).
次に、このフラックス入りワイヤの鋼製外皮の成分であるが、次の範囲とするのが望ましい。 Next, the composition of the steel sheath of the flux-cored wire is preferably within the following range.
「Ｃ：０．０５質量％以下」
Ｃは、鋼製外皮の強度を確保する上で重要な元素である。しかし、Ｃ含有量が０．０５質量％を超えると、鋼製外皮が硬化してエレクトロスラグ溶接時における溶接ワイヤの矯正に必要な荷重が大きくなり、溶接ワイヤの送給性が不良となる。また、非消耗ノズルの先端から溶接ワイヤが曲がった状態で供給され、溶接金属の片溶けが発生する。よって、Ｃ含有量は０．０５質量％以下が望ましい。
"C: 0.05% by mass or less"
C is an important element for securing the strength of the steel outer skin. However, when the C content exceeds 0.05% by mass, the steel sheath is hardened, and the load required for correcting the welding wire during electroslag welding increases, resulting in poor feedability of the welding wire. In addition, the welding wire is supplied in a bent state from the tip of the non-consumable nozzle, and the welding metal is partially melted. Therefore, the C content is desirably 0.05% by mass or less.
「Ｓｉ：０．２質量％以下」
Ｓｉは、鋼製外皮の強度を確保する上で重要な元素である。しかし、Ｓｉ含有量が０．２質量％を超えると、鋼製外皮が硬化してエレクトロスラグ溶接時における溶接ワイヤの矯正に必要な荷重が大きくなり、溶接ワイヤの送給性が不良となる。よって、Ｓｉ含有量は０．２質量％以下が望ましい。
"Si: 0.2% by mass or less"
Si is an important element for securing the strength of the steel outer cover. However, when the Si content exceeds 0.2% by mass, the steel sheath is hardened, and the load required to correct the welding wire during electroslag welding increases, resulting in poor feedability of the welding wire. Therefore, the Si content is desirably 0.2% by mass or less.
「Ｍｎ：０．６質量％以下」
Ｍｎは、鋼製外皮の強度を確保する上で重要な元素である。しかし、Ｍｎ含有量が０．６質量％を超えると、鋼製外皮が硬化してエレクトロスラグ溶接時における溶接ワイヤの矯正に必要な荷重が大きくなり、溶接ワイヤの送給性が不良となる。よって、Ｍｎ含有量は０．６質量％以下が望ましい。
"Mn: 0.6% by mass or less"
Mn is an important element for ensuring the strength of the steel outer cover. However, when the Mn content exceeds 0.6% by mass, the steel sheath is hardened, and the load required for correcting the welding wire at the time of electroslag welding increases, resulting in poor feedability of the welding wire. Therefore, the Mn content is desirably 0.6% by mass or less.
上記した鋼製外皮の成分以外の残部は、Ｆｅ及び不可避的不純物である。 The balance other than the components of the above-mentioned steel shell is Fe and inevitable impurities.
なお、本発明の溶接ワイヤであるフラックス入りワイヤの形態としては、合わせ目有りのシームタイプ、又は合わせ目無しシームレスタイプのいずれのタイプも適用できる。また、本発明のフラックス入りワイヤに充填されるフラックスの充填率は、５乃至３０質量％である。フラックス充填率が５質量％未満では、フラックス入りワイヤの剛性が高いために溶接ワイヤの矯正に必要な荷重が大きくなり、フラックス入りワイヤの送給性が劣化し、アークの発生などが生じる。また、充填率が３０質量％超では、フラックス入りワイヤの製造中に断線が多発したり、溶接ワイヤの矯正ローラ部で座屈したりする。また、スラグ形成剤は実質充填しないが、溶接時に銅当て金を使用する場合は銅当て金にフラックスが付着してスラグを消費して溶融スラグ浴深さが変化するので、スラグ形成剤は、２．０質量％以下の範囲で添加することが可能である。 In addition, as a form of the flux cored wire which is the welding wire of the present invention, any of a seam type having a seam and a seamless type having no seam can be applied. The filling rate of the flux filled in the flux-cored wire of the present invention is 5 to 30% by mass. If the flux filling rate is less than 5% by mass, the load required for correcting the welding wire becomes large due to the high rigidity of the flux-cored wire, and the feedability of the flux-cored wire deteriorates, causing arcing and the like. On the other hand, if the filling rate exceeds 30% by mass, the wire breakage frequently occurs during the production of the flux-cored wire, or the wire buckles at the straightening roller portion of the welding wire. In addition, although the slag forming agent is not substantially filled, when a copper backing is used at the time of welding, flux adheres to the copper backing and consumes slag to change the molten slag bath depth. It can be added in a range of 2.0% by mass or less.
本発明の溶接ワイヤであるフラックス入りワイヤの不可避不純物としては、Ｐ、Ｓ、Ｓｎが挙げられ、夫々各不純物は０．０３０質量％以下に規制される。 Inevitable impurities of the flux-cored wire which is the welding wire of the present invention include P, S, and Sn, and each of the impurities is regulated to 0.030% by mass or less.
次に、本発明にて使用する溶接フラックスおよび溶接中のスラグの各々の組成は、所定量のＳｉＯ２、ＣａＯ、ＣａＦ２、ＭｇＯ、Ａｌ２Ｏ３、ＭｎＯ、ＴｉＯ２を含有し、残部が不可避的不純物からなる。その限定理由について説明する。
溶接フラックスは溶接熱で溶解し、溶接スラグとなるが、サブマージアーク溶接などのフラックスを用いるアーク溶接とは異なり、エレクトロスラグ溶接においては、そのスラグ組成はスラグ−メタル反応により時々刻々と変化するので、スラグの流動性や電気伝導性、塩基度を良好な範囲に制御し、安定な溶接を実現するにはフラックス組成を規定するのみならず、溶接中のスラグ組成もコントロールしなければならない。溶接長全長に渡って良好な溶接性を保つには溶接フラックス、ならびに溶接中のスラグ組成を以下の範囲とすることが必要である。そして、本発明においては、溶接中のスラグ組成は、溶接後のスラグ組成で定義することとする。
Next, the composition of each of the welding flux and the slag during welding used in the present invention contains a predetermined amount of SiO 2 , CaO, CaF 2 , MgO, Al 2 O 3 , MnO, and TiO 2 , with the balance being the rest. Consists of unavoidable impurities. The reason for the limitation will be described.
The welding flux is melted by welding heat and becomes welding slag.Unlike arc welding using flux such as submerged arc welding, in electroslag welding, the slag composition changes every moment due to the slag-metal reaction. In order to control the fluidity, electric conductivity, and basicity of the slag in a favorable range, and to realize stable welding, not only the flux composition but also the slag composition during welding must be controlled. In order to maintain good weldability over the entire welding length, the welding flux and the slag composition during welding must be within the following ranges. In the present invention, the slag composition during welding is defined as the slag composition after welding.
「ＳｉＯ２：１５乃至４５質量％」
ＳｉＯ２は、スラグの粘度、酸素量に影響を及ぼす塩基度を制御するのに必須の成分である。特に、ＳｉＯ２は、エレクトロスラグ溶接にとって重要であり、スラグ発熱のための電気電導度に大きな影響を及ぼす。ＳｉＯ２含有量が１５質量％未満の場合、スラグの電気抵抗が低くなり、溶接時にアークが発生しやすくなる。特に、ワイヤ中のＡｌやＴｉなどの強脱酸元素の添加はスラグ中のＳｉＯ２を低下させる。一方、ＳｉＯ２含有量が４５質量％を超えると、塩基度が低くなりすぎ、溶接金属の酸素量が高くなりすぎるとともに、電気抵抗が高くなりすぎ、アークの発生など溶接が不安定化する。よって、ＳｉＯ２含有量は１５乃至４５質量％とする。
"SiO 2 : 15 to 45% by mass"
SiO 2 is an essential component for controlling the basicity that affects the viscosity and oxygen amount of slag. In particular, SiO 2 is important for electroslag welding and has a significant effect on electrical conductivity due to slag heating. When the SiO 2 content is less than 15% by mass, the electric resistance of the slag becomes low, and an arc is easily generated at the time of welding. In particular, the addition of a strong deoxidizing element such as Al or Ti in the wire lowers SiO 2 in the slag. On the other hand, if the SiO 2 content exceeds 45% by mass, the basicity becomes too low, the oxygen content of the weld metal becomes too high, and the electric resistance becomes too high, and the welding becomes unstable such as generation of an arc. Therefore, the content of SiO 2 is set to 15 to 45% by mass.
「ＣａＯ：５乃至２１質量％」
ＣａＯは、塩基性成分であり、適度に添加することでスラグの流動性を適正に保つのに有効である。ＣａＯ含有量が５質量％未満の場合、溶接金属酸素量が過大になり靱性が劣化する。一方、ＣａＯ含有量が２１質量％を超えると、スラグの流動性が低下し、通電が不安定化するため、溶け込みの不安定化やアークの発生など溶接性が低下する。よって、ＣａＯ含有量は５乃至２１質量％とする。
"CaO: 5 to 21% by mass"
CaO is a basic component, and is effective in appropriately maintaining the fluidity of the slag by being appropriately added. When the CaO content is less than 5% by mass, the amount of oxygen in the weld metal becomes excessive, and the toughness is deteriorated. On the other hand, when the CaO content exceeds 21% by mass, the fluidity of the slag decreases, and the current supply becomes unstable, so that the weldability such as instability of penetration and generation of an arc decreases. Therefore, the CaO content is set to 5 to 21% by mass.
「ＣａＦ２：１乃至１３質量％」
ＣａＦ２は、溶接金属の酸素量を低減するのに極めて有効な成分であり、スラグの流動性を適正に保つのに有効である。さらには、高温で良好な電気伝導性を示すため、スラグの電気伝導度を調整する働きがある。ＣａＦ２含有量が１質量％未満の場合、スラグの流動性の低下や通電抵抗の増加がおこり、溶接停止が発生する。一方、ＣａＦ２含有量が１３質量％を超えると、スラグの通電抵抗が低下し、アークの発生などにより溶接停止が起こりやすい。よって、ＣａＦ２含有量は１乃至１３質量％とする。
"CaF 2 : 1 to 13% by mass"
CaF 2 is a very effective component for reducing the amount of oxygen in the weld metal, and is effective for properly maintaining the fluidity of the slag. Furthermore, since it has good electrical conductivity at high temperatures, it has the function of adjusting the electrical conductivity of the slag. If the content of CaF 2 is less than 1% by mass, the slag fluidity is reduced and the current-carrying resistance is increased, and welding stops. On the other hand, if the content of CaF 2 exceeds 13% by mass, the current-carrying resistance of the slag decreases, and welding is likely to stop due to the occurrence of an arc. Therefore, the content of CaF 2 is set to 1 to 13% by mass.
「ＭｇＯ：１６質量％以下」
ＭｇＯは、塩基性成分であり、溶接金属の酸素量を低減すると共にスラグの凝固点・粘度調整のために添加される。ＭｇＯ含有量が１６質量％を超えると粘度が過大となり、流動性が悪くなるため、スラグ内の温度ばらつきが大きくなり、溶接停止が起こりやすくなる。よって、ＭｇＯ含有量は１６質量％以下とする。
"MgO: 16% by mass or less"
MgO is a basic component, and is added to reduce the oxygen content of the weld metal and adjust the solidification point and viscosity of the slag. If the MgO content exceeds 16% by mass, the viscosity becomes excessively high and the fluidity deteriorates, so that the temperature variation in the slag increases and welding stops are likely to occur. Therefore, the MgO content is set to 16% by mass or less.
「Ａｌ２Ｏ３：１７質量％以下」
Ａｌ２Ｏ３は、スラグ形成剤として作用し、溶融スラグの粘性を下げる効果があるが、この効果はＣａＯの添加により十分に補われている。一方、Ａｌ２Ｏ３含有量が１７質量％を超えると、溶融スラグの流動性が悪くなり、溶接停止が発生しやすくなる。よって、Ａｌ２Ｏ３含有量は１７質量％以下とする。
"Al 2 O 3 : 17% by mass or less"
Al 2 O 3 acts as a slag forming agent and has the effect of lowering the viscosity of the molten slag, but this effect is sufficiently compensated for by the addition of CaO. On the other hand, when the Al 2 O 3 content exceeds 17% by mass, the fluidity of the molten slag deteriorates, and welding stoppage is likely to occur. Therefore, the Al 2 O 3 content is set to 17% by mass or less.
「ＭｎＯ：２５質量％以下」
ＭｎＯは、スラグの粘性を調整するのに有効である。しかし、この効果はＳｉＯ２の添加により確保することができるため、ＭｎＯの添加は必須ではない。一方、ＭｎＯの含有量が２５質量％を超えると、スラグの粘性が増大し、溶接停止が起こりやすい。よって、ＭｎＯ含有量は２５質量％以下とする。
"MnO: 25% by mass or less"
MnO is effective in adjusting the viscosity of the slag. However, since this effect can be ensured by adding SiO 2, the addition of MnO is not essential. On the other hand, when the content of MnO exceeds 25% by mass, the viscosity of the slag increases, and welding is likely to stop. Therefore, the MnO content is 25% by mass or less.
「ＴｉＯ２：２乃至１５質量％」
ＴｉＯ２は、高温で良好な電気電導性を持つため、溶接作業性のコントロールに必須であり、スラグ−メタル反応によりワイヤからのＴｉ添加とバランスし、溶接金属へのＴｉの歩留りを安定させ、溶接金属の靭性を高める働きがある。一方、スラグ中のＴｉＯ２量が１５質量％を越えて添加されると、スラグの電気電導性が高くなりすぎ、スラグ浴中のワイヤ浸漬長さが短くなり、アークの発生などによる溶接停止や、靭性の低下が発生する。よって、ＴｉＯ２含有量は２乃至１５質量％とする。
"TiO 2 : 2 to 15% by mass"
Since TiO 2 has good electrical conductivity at high temperatures, it is indispensable for control of welding workability, balances Ti addition from wire by slag-metal reaction, stabilizes the yield of Ti to weld metal, It works to increase the toughness of the weld metal. On the other hand, if the amount of TiO 2 in the slag exceeds 15% by mass, the electric conductivity of the slag becomes too high, the wire immersion length in the slag bath becomes short, and welding stops due to the occurrence of arc or the like. , A decrease in toughness occurs. Therefore, the TiO 2 content is set to 2 to 15% by mass.
なお、溶接フラックスおよびスラグの各々の不可避的不純物としては、ＦｅＯ、Ｂ２Ｏ３等が挙げられ、ＦｅＯ含有量は、溶接金属の靭性の確保の観点から、４．５質量％以下であることが望ましい。さらに、Ｂ２Ｏ３含有量は、溶接金属の靭性確保、安定化の観点から、１．５質量％以下が望ましい。 In addition, as inevitable impurities of each of the welding flux and the slag, FeO, B 2 O 3 and the like are mentioned, and the FeO content is 4.5% by mass or less from the viewpoint of securing the toughness of the weld metal. Is desirable. Further, the content of B 2 O 3 is desirably 1.5% by mass or less from the viewpoint of securing and stabilizing the toughness of the weld metal.
前記非消耗ノズル式エレクトロスラグ溶接方法においては、１．６ｍｍφ前後のワイヤ径が一般的に適用され、ワイヤ送給速度が大きい。このため、溶接条件は以下の範囲とすることが望ましい。 In the non-consumable nozzle type electroslag welding method, a wire diameter of about 1.6 mmφ is generally applied, and a wire feeding speed is high. For this reason, it is desirable that the welding conditions be in the following ranges.
「溶接電流：３５０乃至４１０Ａ」
適正なスラグ発熱を得て、適正な溶け込みを溶接長全長に渡って得るためには、溶接電流は３５０乃至４１０Ａの範囲することが望ましい。溶接電流が３５０Ａ未満の場合、スラグ発熱が不十分となり、溶け込みが不足する。一方、溶接電流が４１０Ａを超えると、ワイヤ溶融が不安定となり、アーク発生などの溶接不安定化が生じ溶接性が劣化する。
"Welding current: 350 to 410A"
In order to obtain proper slag heat generation and obtain proper penetration over the entire welding length, the welding current is desirably in the range of 350 to 410A. When the welding current is less than 350 A, the slag heat generation becomes insufficient and the penetration becomes insufficient. On the other hand, if the welding current exceeds 410 A, the melting of the wire becomes unstable, and welding instability such as arc generation occurs, thereby deteriorating the weldability.
「溶接電圧：４４乃至５４Ｖ」
溶接電圧は、溶け込みの大きさやワイヤの突き出し長さに大きな影響を及ぼし、溶接電圧が４４Ｖ未満の場合、溶け込み不足が生じやすい。一方、溶接電圧が５４Ｖを超えると突き出し長さが短くなり、アークの発生などが生じ溶接性が劣化する。
"Welding voltage: 44 to 54 V"
The welding voltage has a large effect on the size of the penetration and the length of the wire protrusion, and when the welding voltage is less than 44 V, insufficient penetration is likely to occur. On the other hand, if the welding voltage exceeds 54 V, the protruding length is shortened, an arc is generated, and the weldability is deteriorated.
「ワイヤ送給速度：６．５乃至１１．０ｍ／ｍｉｎ」
非消耗ノズル式のエレクトロスラグ溶接では、ワイヤ送給速度を大きな範囲で設定できる。しかし、ワイヤ送給速度が６．５ｍ／ｍｉｎ未満の場合、溶接能率が低く、経済的でないだけでなく、溶接入熱が増大して溶接部の靭性が劣化しやすい。また、突き出し長さが短くなり、わずかなワイヤ送給速度の変化によりアークが発生し、溶接停止や靭性劣化が生じる。一方、ワイヤ送給速度が１１．０ｍ／ｍｉｎを超えると、溶接入熱が減少し、溶け込みが減少しやすく、突き出し長さが変化しやすいため、溶融スラグとの間にアークが発生しやすく、溶接性の劣化、ならびに溶接金属靭性の劣化が生じやすい。
"Wire feeding speed: 6.5 to 11.0 m / min"
In non-consumable nozzle type electroslag welding, the wire feed speed can be set within a large range. However, when the wire feeding speed is less than 6.5 m / min, the welding efficiency is low and not only is not economical, but also the welding heat input increases and the toughness of the weld tends to deteriorate. In addition, the protrusion length is shortened, and an arc is generated due to a slight change in the wire feeding speed, thereby stopping welding and deteriorating toughness. On the other hand, if the wire feeding speed exceeds 11.0 m / min, the welding heat input is reduced, the penetration is easily reduced, and the protrusion length is easily changed. Deterioration of weldability and deterioration of weld metal toughness are likely to occur.
「溶接ワイヤの曲率（直径）：５００乃至２３００ｍｍ」
溶接ワイヤの曲率（直径）に相当するキャスト径が５００ｍｍ未満の場合、ワイヤの送給抵抗が増大するため、ワイヤの送給速度に変化が起こりやすくなり、ワイヤがスラグ浴から離脱してアークが発生しやすくなる。一方、溶接ワイヤのキャスト径が２３００ｍｍを超えると、ワイヤの送給抵抗が減少するため、ワイヤの送給速度は不安定化し、アークの発生などによる溶接性の劣化、溶接金属の靭性劣化が生じる。
"The curvature (diameter) of the welding wire: 500 to 2300 mm"
If the casting diameter corresponding to the curvature (diameter) of the welding wire is less than 500 mm, the feed resistance of the wire increases, so that the feed speed of the wire tends to change, and the wire separates from the slag bath to cause an arc. More likely to occur. On the other hand, when the casting diameter of the welding wire exceeds 2300 mm, the feeding resistance of the wire decreases, so that the feeding speed of the wire becomes unstable, and the weldability deteriorates due to the occurrence of an arc and the toughness of the weld metal deteriorates. .
なお、本溶接方法においては、スラグ浴深さを１５乃至４０ｍｍとするのが望ましい。良好な溶け込みを得るには、スラグの発熱を効率よく得なければならない。そのため、スラグ浴深さは１５乃至４０ｍｍの範囲とすることが望ましい。スラグ浴深さが１５ｍｍ未満の場合、スラグの発熱が過大になるとともに、ワイヤがスラグ中で安定に溶解せず、アーク停止が頻発する危険が高まる。一方、スラグ浴深さが４０ｍｍを超えると、スラグの温度が低下し、ワイヤの溶融および母材の溶融が不安定化し、溶接停止や溶け込み不足が生じやすくなる。 In the present welding method, the slag bath depth is desirably 15 to 40 mm. In order to obtain good penetration, it is necessary to efficiently generate heat from the slag. Therefore, the slag bath depth is desirably in the range of 15 to 40 mm. When the slag bath depth is less than 15 mm, the heat generation of the slag becomes excessive, and the wire is not stably melted in the slag, and the danger of arc stopping frequently increases. On the other hand, when the slag bath depth exceeds 40 mm, the temperature of the slag decreases, the melting of the wire and the melting of the base metal become unstable, and welding stoppage and insufficient penetration easily occur.
次に、本発明のエレクトロスラグ溶接継手の製造方法について説明する。
ここで、エレクトロスラグ溶接継手は、図１に示すように、母材（スキンプレートａおよびダイアフラムｂ）と当金（側板ｃ）とで囲まれた開先（空間ｓ）を、溶接ワイヤ（フラックス入りワイヤ）および溶接フラックスを用いて、例えば立向上進法にて、溶接することによって作製される。
本製造方法においては、前記非消耗ノズル式エレクトロスラグ溶接方法により作製することを特徴とする。非消耗ノズル式エレクトロスラグ溶接方法の詳細については、前記のとおりであるので、説明を省略する。
Next, a method for manufacturing the electroslag welded joint of the present invention will be described.
Here, as shown in FIG. 1, the electroslag welding joint connects a groove (space s) surrounded by a base material (skin plate a and diaphragm b) and a metal (side plate c) with a welding wire (flux). It is produced by welding using, for example, a rising wire and a welding flux.
The present manufacturing method is characterized in that it is manufactured by the non-consumable nozzle type electroslag welding method. Since the details of the non-consumable nozzle type electroslag welding method are as described above, description thereof will be omitted.
次に、本発明の実施例について、本発明の特許請求の範囲から外れる比較例と比較して説明する。溶接試験を以下のようにして行った。図１に示すように、板厚６０ｍｍのスキンプレートａ上に、ＪＩＳ規格ＳＮ４９０に規定されたフラットバーを１対の側板ｃとして立設し、この側板ｃ間に５５ｍｍ厚のダイアフラムｂを挟んだ溶接継手を作製した（溶接長１２００ｍｍ）。この溶接継手における溶接箇所は、ダイアフラムｂと、側板ｃと、スキンプレートａに囲まれた空間ｓである。各部材の寸法は図１に示すとおりである。また、スキンプレートａ、ダイアフラムｂ、側板ｃの成分組成（質量％）を表１に示す。そして、表２に示す溶接条件（立向上進法）で、線径が１．６ｍｍの溶接ワイヤを使用して、エレクトロスラグ溶接を実施した。なお、溶接フラックスは、溶接開始前に、１１０ｇ投入した。また、スラグ浴深さは２５ｍｍで行った。 Next, examples of the present invention will be described in comparison with comparative examples that fall outside the scope of the claims of the present invention. The welding test was performed as follows. As shown in FIG. 1, a flat bar specified by JIS standard SN490 is erected as a pair of side plates c on a 60 mm thick skin plate a, and a 55 mm thick diaphragm b is sandwiched between the side plates c. A weld joint was produced (weld length 1200 mm). The welding location in this weld joint is a space s surrounded by the diaphragm b, the side plate c, and the skin plate a. The dimensions of each member are as shown in FIG. Table 1 shows the component compositions (% by mass) of the skin plate a, the diaphragm b, and the side plate c. Then, electroslag welding was performed using welding wires having a wire diameter of 1.6 mm under the welding conditions (standing improvement method) shown in Table 2. The welding flux was charged at 110 g before the start of welding. The slag bath depth was 25 mm.
溶接ワイヤとして用いたメタル系フラックス入りワイヤの成分組成（即ち、鋼製外皮と充填した金属粉末との総合成分）を表３、４（表において残部はＦｅ及び不可避的不純物である）に示す。また、鋼製外皮の成分組成（質量％）を表５（表において残部はＦｅ及び不可避的不純物である）に示す。溶接フラックスの成分組成（溶接フラックス全質量に対する質量％）を表６（表において残部は不可避的不純物である）に示す。溶接後のスラグの組成を表７、８（表において残部は不可避的不純物である）に示す。溶接中にフラックスの追加は行わなかった。すなわち、溶接中のスラグ組成は、溶接開始前のフラックス組成と溶接後のスラグ組成の範囲内にあることを示している。 The composition of the metal flux cored wire used as the welding wire (ie, the total composition of the steel shell and the filled metal powder) is shown in Tables 3 and 4 (the remainder in the table is Fe and inevitable impurities). Table 5 (the remainder in the table is Fe and unavoidable impurities) shows the component composition (% by mass) of the steel shell. The composition of the welding flux (% by mass relative to the total mass of the welding flux) is shown in Table 6 (the remainder in the table is inevitable impurities). The compositions of the slag after welding are shown in Tables 7 and 8 (the remainder in the table is inevitable impurities). No additional flux was added during welding. In other words, the slag composition during welding is within the range of the flux composition before the start of welding and the slag composition after welding.
溶接終了後、ＵＴ（超音波探傷試験）により高温割れ等の欠陥の有無を確認し、図２に示す採取位置で引張試験片ｄ及びシャルピー衝撃試験片ｅを採取し、溶接金属の機械的性質を調査した。引張試験片は、溶接線方向の３００ｍｍの箇所から採取し、引張試験を実施した。衝撃試験片については、溶接線方向で、２００ｍｍ、７００ｍｍ、１１００ｍｍの３箇所から採取し、試験温度を０℃として、衝撃試験を実施した。但し、衝撃吸収エネルギは、各箇所３本の試験片の衝撃値の平均値である。また、図２のｆ１、ｆ２はスキンプレートａの溶け込み深さを示しており、ｆ１とｆ２の和を溶接長１５０ｍｍ、６５０ｍｍ、１０５０ｍｍの位置で測定した。その結果を表７〜９に示した。 After welding, the presence or absence of defects such as hot cracks is confirmed by UT (ultrasonic flaw detection test). Tensile test piece d and Charpy impact test piece e are sampled at the sampling positions shown in FIG. 2, and the mechanical properties of the weld metal investigated. The tensile test piece was sampled from a location 300 mm in the direction of the welding line, and a tensile test was performed. About the impact test piece, it sampled from three places of 200 mm, 700 mm, and 1100 mm in the welding line direction, and set the test temperature to 0 degreeC, and performed the impact test. However, the impact absorption energy is the average value of the impact values of three test pieces at each location. In addition, f1 and f2 in FIG. 2 indicate the penetration depth of the skin plate a, and the sum of f1 and f2 was measured at positions of welding lengths of 150 mm, 650 mm, and 1050 mm. The results are shown in Tables 7 to 9.
実施例である表７〜９に示す記号Ｓ１〜Ｓ４およびＳ６では、溶接長１２００ｍｍ全長に渡り、アークの発生はすべて１秒以下の短時間で、発生数も３回以下で良好であった。また、高温割れ等の欠陥も無く、溶接金属の衝撃吸収エネルギ（靭性）も測定位置３位置に渡って良好な値を示した。スキンプレートａの溶け込みも十分であった。 In the symbols S1 to S4 and S6 shown in Tables 7 to 9 as examples, all arcs were generated in a short time of 1 second or less over the entire welding length of 1200 mm, and the number of generated arcs was 3 or less, which was good. Also, there were no defects such as hot cracks, and the impact absorption energy (toughness) of the weld metal showed a good value over the three measurement positions. The penetration of the skin plate a was also sufficient.
これに対し、比較例である表７〜９に示す記号Ｓ５では、好ましい溶接条件であってもワイヤのＴｉ量および溶接フラックスのＴｉＯ２量が上限値に近いため、高温割れ等の欠陥は無かったが、溶接後のスラグのＴｉＯ２量が増加した。そのため、溶接の後半にアークが発生するようになり、溶け込みの減少と溶接長１１００ｍｍ位置での溶接金属靭性低下が生じた。 In contrast, in symbol S5 shown in Table 7-9 are comparative examples, close to the amount of TiO 2 is the upper limit of the preferred a welding condition even if the wire of Ti amount and welding flux, the defect of hot cracking and the like did not However, the amount of TiO 2 in the slag after welding increased. For this reason, an arc was generated in the latter half of the welding, resulting in a decrease in penetration and a decrease in weld metal toughness at a welding length of 1100 mm.
比較例である表７〜９に示す記号Ｓ７では、ワイヤのＴｉ量が高いため、高温割れ等の欠陥はなかったが、溶接後のスラグ中のＴｉＯ２量が増加した。そのため、溶接の後半にアークの発生が頻発し、溶け込みの減少と溶接長１１００ｍｍの位置での溶接金属靭性に低下が生じた。 In symbol S7 shown in Table 7-9 is a comparative example, the Ti content of the wire is high, there were no defects hot cracking, etc., TiO 2 content in the slag after welding is increased. For this reason, the occurrence of an arc frequently occurred in the latter half of welding, resulting in a decrease in penetration and a decrease in weld metal toughness at a position of a welding length of 1100 mm.
比較例である表７〜９に示す記号Ｓ８では、ワイヤのＴｉ量が高いため、高温割れ等の欠陥は無かったが、溶接後のスラグ中のＴｉＯ２量が増加した。そのため、上記と同様に溶接の後半にアークの発生が頻発し、溶け込みの減少と溶接長１１００ｍｍの位置での溶接金属靭性に低下が生じた。 In symbol S8 shown in Table 7-9 is a comparative example, the Ti content of the wire is high, but there was no defect in high-temperature cracking, etc., TiO 2 content in the slag after welding is increased. As a result, an arc was frequently generated in the latter half of the welding as in the above case, resulting in a decrease in penetration and a decrease in weld metal toughness at a position of a welding length of 1100 mm.
ａ：スキンプレート
ｂ：ダイアフラム
ｃ：側板
ｄ：引張試験片
ｅ：シャルピー衝撃試験片
ｆ１、ｆ２：溶け込み
ｓ：空間
a: Skin plate b: Diaphragm c: Side plate d: Tensile test piece e: Charpy impact test piece f1, f2: Penetration s: Space
Claims (3)
前記溶接ワイヤは、ワイヤ全質量に対して、Ｃ：０．０１０乃至０．１０質量％、Ｓｉ：０．８質量％以下、Ｍｎ：０．９乃至２．８質量％、Ｍｏ：０．１０乃至２．００質量％、Ａｌ：０．００５乃至０．０４０質量％、Ｔｉ：０．０５乃至０．１４質量％、Ｂ：０．０１１０乃至０．０２７０質量％を含有し、Ｎｉ：３．００質量％以下、Ｃｕ：３．００質量％以下、Ｃｒ：０．３０質量％以下、Ｖ：０．０３０質量％以下、Ｎｂ：０．０３０質量％以下の１種または２種以上を含有し、残部がＦｅ及び不可避的不純物からなる組成を有するメタル系フラックス入りワイヤであり、
前記溶接フラックスが、溶接フラックス全質量に対して、ＳｉＯ2：１５乃至４５質量％、ＣａＯ：５乃至２１質量％、ＣａＦ2：１乃至１３質量％、ＭｇＯ：１６質量％以下、Ａｌ2Ｏ3：１７質量％以下、ＭｎＯ：２５質量％以下、ＴｉＯ2：２乃至１５質量％、ＦｅＯ：４．５質量％以下、Ｂ 2 Ｏ 3 ：１．５質量％以下を含有し、残部が不可避的不純物からなる組成を有し、
溶接後のスラグが、スラグ全質量に対して、ＳｉＯ2：１５乃至４５質量％、ＣａＯ：５乃至２１質量％、ＣａＦ2：１乃至１３質量％、ＭｇＯ：１６質量％以下、Ａｌ2Ｏ3：１７質量％以下、ＭｎＯ：２５質量％以下、ＴｉＯ2：２乃至１５質量％、ＦｅＯ：４．５質量％以下、Ｂ 2 Ｏ 3 ：１．５質量％以下を含有し、残部が不可避的不純物からなる組成を有することを特徴とする非消耗ノズル式エレクトロスラグ溶接方法。 In a non-consumable nozzle type electroslag welding using a welding flux charged into a welding site separately from the welding wire and the flux formed by filling a flux inside the steel outer shell ,
C: 0.010 to 0.10% by mass, Si: 0.8% by mass or less, Mn: 0.9 to 2.8% by mass, Mo: 0.10. To 2.00% by mass, Al: 0.005 to 0.040% by mass, Ti: 0.05 to 0.14% by mass, B: 0.0110 to 0.0270% by mass, and Ni: 3. One or two or more of 00 mass% or less, Cu: 3.00 mass% or less, Cr: 0.30 mass% or less, V: 0.030 mass% or less, and Nb: 0.030 mass% or less. A metal flux-cored wire having a balance of Fe and inevitable impurities,
The welding flux is 15 to 45% by mass of SiO 2 , 5 to 21% by mass of CaO, 1 to 13% by mass of CaF 2 , 16% by mass or less of MgO, and Al 2 O 3 based on the total mass of the welding flux. : 17 wt% or less, MnO: 25 wt% or less, TiO 2: 2 to 15 wt%, FeO: 4.5 wt% or less, B 2 O 3: containing 1.5 wt% or less, the balance being unavoidable Having a composition consisting of impurities ,
The slag after welding is 15 to 45% by mass of SiO 2 , 5 to 21% by mass of CaO, 1 to 13% by mass of CaF 2 , 16% by mass or less of MgO, and Al 2 O 3 based on the total mass of the slag. : 17 wt% or less, MnO: 25 wt% or less, TiO 2: 2 to 15 wt%, FeO: 4.5 wt% or less, B 2 O 3: containing 1.5 wt% or less, the balance being unavoidable A non-consumable nozzle type electroslag welding method, characterized by having a composition comprising impurities .
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