JP2011152579A - Metal powder-filled welding wire for electroslag welding - Google Patents
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本発明は、鋼製外皮に金属粉を充填することで、ワイヤの成分組成の調整がソリッドワイヤに比べて容易な、メタル粉入りエレクトロスラグ溶接用ワイヤに関し、溶接ワイヤ厚鋼板のエレクトロスラグ溶接により接合されたＴ字継手、例えば建築鉄骨における四面ボックス柱とダイヤフラムとの接合部に生じる、裏当金を用いて溶接されるＴ字継手のエレクトロスラグ溶接において、靱性の優れた溶接金属を得るために好適なものに関する。特に、溶接ワイヤの形態に関しては、鋼製外皮にシームレスパイプを用いたものか、造管時にシーム部を溶接して外気と内部の充填剤とが直接接触しないようにして伸線加工した「シームレスワイヤ」に適用することを目的とする。 The present invention relates to an electroslag welding wire containing metal powder, in which adjustment of the component composition of the wire is easier than solid wire by filling the steel outer shell with metal powder, and by electroslag welding of a thick steel plate of the welding wire To obtain a weld metal with excellent toughness in electroslag welding of T-joints that are welded using backing metal, which occurs at the joints of four-sided box columns and diaphragms in joined T-joints, for example, steel structures It is related with what is suitable for. In particular, regarding the form of the welding wire, a seamless pipe was used for the steel outer shell, or the seam was welded during pipe making so that the outside air did not come into direct contact with the filler inside, and the “seamless wire was processed seamlessly. It is intended to be applied to “wire”.
一般に、エレクトロスラグ溶接法は、大入熱１パス溶接が可能なため、他の溶接法に比べて高能率な溶接が可能であり、建築、橋梁などの溶接構造物における鉄骨のダイヤフラムなどを立向溶接する場合に多く用いられている。しかしながら、エレクトロスラグ溶接法は、その溶接入熱が５００ｋＪ／ｃｍ程度以上と、一般のアーク溶接に比べて大きいために、溶接で形成される溶接金属の冷却速度が小さく、その冷却過程でオーステナイト（以下、略称でγということもある）粒界から粗大な初析フェライト（以下、略称でαということもある）が生成されやすく、また、粒内に形成される組織も粗大化するため、溶接金属の靭性を確保することが容易ではない。 In general, the electroslag welding method can perform one-pass welding with a large heat input, so that it is possible to perform welding more efficiently than other welding methods, and can establish steel diaphragms and the like in welded structures such as buildings and bridges. It is often used for direction welding. However, the electroslag welding method has a welding heat input of about 500 kJ / cm or more, which is larger than that of general arc welding. Therefore, the cooling rate of the weld metal formed by welding is low, and austenite ( In the following, coarse pro-eutectoid ferrite (hereinafter sometimes abbreviated as α) is easily generated from the grain boundary, and the structure formed in the grains is also coarsened. It is not easy to ensure the toughness of the metal.
一方で、建築、橋梁などの溶接構造物において、地震時に脆性破壊により倒壊しないために、その溶接部の高靭性化の社会的要請が極めて大きく、母材、溶接熱影響部（Ｈｅａｔ Ａｆｆｅｃｔｅｄ Ｚｏｎｅ：ＨＡＺ）の靱性として、０℃における２ｍｍＶノッチシャルピー衝撃試験の吸収エネルギーで７０Ｊ以上を保証する高ＨＡＺ靱性鋼が開発されている。溶接継手全体の安全性を高めるためには、溶接金属においても同等のレベルが要求されてきており、本要求に応えるために、最近、エレクトロスラグ溶接時の溶接金属の高靭性化が可能なエレクトロスラグ用溶接ワイヤがいろいろと提案されてきた。 On the other hand, in a welded structure such as a building or a bridge, since it does not collapse due to brittle fracture at the time of an earthquake, the social demand for toughness of the welded part is extremely large, and the base material, the heat affected zone (Heat Affected Zone: As the toughness of HAZ), a high HAZ toughness steel has been developed that guarantees 70 J or more in the absorbed energy of the 2 mmV notch Charpy impact test at 0 ° C. In order to increase the safety of the entire welded joint, the same level has been required for weld metal, and in order to meet this demand, recently, it has become possible to increase the toughness of weld metal during electroslag welding. Various slag welding wires have been proposed.
例えば、特許文献１では凝固時のオーステナイト粒径の微細化を図ることで、引張強さ５００〜６００ＭＰａ級の溶接金属において、２ｍｍＶノッチシャルピー衝撃試験の０℃における吸収エネルギーが１００Ｊ以上の優れた靭性を達成する技術を開示している。
For example, in
一方、現在、建築分野で用いられるエレクトロスラグ溶接には、非消耗ノズル式が一般的で、溶接ワイヤには通常、鋼製の中実伸線であるソリッドワイヤが用いられるが、エレクトロスラグ溶接では母材希釈が大きいために、高強度でかつ高靭性の溶接金属を得ようとすると、鋼材組成や目標特性に応じて溶接ワイヤの組成を調整することが好ましいが、ソリッドワイヤではワイヤ素材のインゴットやスラブごとに成分が一定となってしまうため、ワイヤの成分を自由に変更することが容易でないという問題がある。 On the other hand, a non-consumable nozzle type is generally used for electroslag welding used in the construction field, and a solid wire, which is a solid steel wire, is usually used for the welding wire. Due to the large dilution of the base metal, it is preferable to adjust the composition of the welding wire according to the steel composition and target characteristics when trying to obtain a high strength and high toughness weld metal. Since the component becomes constant for each slab, there is a problem that it is not easy to freely change the component of the wire.
上記ソリッドワイヤにおける問題解決のためには、鋼製外皮からなるパイプあるいはチューブの内部にメタル粉やフラックスを充填するコアードワイヤが好ましい。なお、スラグ形成剤や脱酸材としての酸化物などのいわゆるフラックス成分を含まない成分調整用メタル粉やかさ増し材としての鉄粉のみを含むコアードワイヤもフラックス入りワイヤと呼ぶことがあり、以降、フラックス入りワイヤと称する場合は、特に断らない限りは両方を含むコアードワイヤのことを示すことし、逆にメタル粉入りワイヤという場合は、意図的にはスラグ形成剤や脱酸材としての酸化物などのフラックス成分を含まないワイヤのことを指すこととする。 In order to solve the problem in the solid wire, a cored wire in which a metal powder or flux is filled in a pipe or tube made of a steel outer shell is preferable. It should be noted that a cored wire containing only a metal powder for adjusting a component that does not include a so-called flux component such as an oxide as a slag forming agent or a deoxidizing material or an iron powder as a bulk increasing material may be referred to as a flux-cored wire. The term “cored wire” refers to a cored wire including both unless otherwise specified, and conversely, in the case of a wire containing metal powder, an oxide as a slag forming agent or a deoxidizing material is intentionally used. It refers to a wire that does not contain a flux component.
フラックス入りワイヤであれば、鋼製外皮は一定組成として、ワイヤ全体としての成分は充填剤から自由に調整が可能であるため、鋼材組成に応じた組成のワイヤを容易に製造でき、かつ、その製造コストも抑制できる利点を有する。しかしながら、充填剤は基本的に微粒または粉体であるため、表面積が大きく、表面酸化によるワイヤの酸素（Ｏ）量がソリッドワイヤに比べて極めて多くなる。そのため、単にソリッドワイヤと同じ成分になるように合金成分を充填剤から含有させただけでは、溶接金属中の酸素含有量がソリッドワイヤによるよりも非常に多くなるため、溶接金属の靭性や延性が低下する。そのため、コアードワイヤにおいて、ソリッドワイヤなみに良好な靭性や延性を得るためには、溶接金属中の酸素含有量を低減するか、無害化する新たな技術が必要である。 In the case of a flux-cored wire, the steel outer sheath has a constant composition, and the components of the entire wire can be freely adjusted from the filler, so that a wire having a composition according to the steel material composition can be easily manufactured, and There is an advantage that the manufacturing cost can be suppressed. However, since the filler is basically a fine particle or powder, the surface area is large, and the amount of oxygen (O) in the wire due to surface oxidation is extremely large compared to the solid wire. Therefore, if the alloy component is simply contained from the filler so as to be the same component as the solid wire, the oxygen content in the weld metal is much higher than that due to the solid wire, so the toughness and ductility of the weld metal is increased. descend. Therefore, in order to obtain good toughness and ductility as in a solid wire in a cored wire, a new technology for reducing or detoxifying the oxygen content in the weld metal is required.
特許文献２には、エレクトロスラグ溶接用のメタル粉入り溶接ワイヤが開示されているが、溶接金属中の酸素量には何ら注意が払われておらず、従って、溶接金属中の酸素量が多い分、靭性や延性がその溶接金属組成から期待されるよりは低下している可能性が高い。
本発明においては、エレクトロスラグ溶接用のメタル粉入り溶接ワイヤにおいて、酸素を低減あるいは無害化し、さらには、メタル粉入り溶接ワイヤであることを活かして充填剤の種類を工夫することにより、ソリッドワイヤによる溶接金属以上に溶接金属の靭性や延性を向上させるメタル粉入り溶接ワイヤを得ることを課題とする。具体的には、溶接入熱が１２００ｋＪ／ｃｍ以下の非消耗ノズル式エレクトロスラグ溶接により形成された溶接金属の２ｍｍＶノッチシャルピー衝撃試験の０℃における吸収エネルギーが７０Ｊ以上となる、充填フラックスが金属粉あるいは／および合金粉からなるメタル粉入り溶接ワイヤを得ることを課題とする。 In the present invention, in a metal powder-containing welding wire for electroslag welding, oxygen is reduced or rendered harmless, and further, by utilizing the fact that it is a metal powder-containing welding wire, a solid wire is devised. It is an object of the present invention to obtain a metal powder-containing welding wire that improves the toughness and ductility of the weld metal more than the weld metal produced by the above method. Specifically, the absorbed energy at 0 ° C. of the 2 mm V notch Charpy impact test of a weld metal formed by non-consumable nozzle type electroslag welding with a welding heat input of 1200 kJ / cm or less is 70 J or more, and the filling flux is metal powder. Alternatively, an object is to obtain a metal powder-containing welding wire made of alloy powder.
非消耗ノズル式エレクトロスラグ溶接においては、溶接の開始時に開先底部に適正量のフラックスを散布しておき、該フラックスにより形成される溶融スラグ抵抗発熱により溶接ワイヤと母材とを溶融させる溶接方法であり、溶接中は溶融状態にある溶接金属表面を一定量の溶融スラグが覆う。該スラグの量は溶接の安定性を左右し、スラグ量が多くても少なくても溶接の安定性を損ない、スパッタが多くなったり、溶接が途中で停止したり、溶け込み不良を生じる。溶接ワイヤにスラグ形成剤や酸化物を含むフラックス入りワイヤで溶接を行うと、溶接が進行するにつれて、溶融スラグの量が増加し、かつその組成も刻々変化するため、安定した溶接を最後まで行うことが困難であることが判明した。従って、本発明者らは、エレクトロスラグ溶接用のフラックス入りワイヤとしては、意図的にはスラグ形成成分を含まないメタル粉入り溶接ワイヤとすることが必須であると考え、メタル粉入りワイヤにおける溶接金属の低酸素化とさらなる靭性、延性向上のための新たな手段を種々研究した。 In non-consumable nozzle-type electroslag welding, a welding method in which an appropriate amount of flux is sprayed on the groove bottom at the start of welding, and the welding wire and the base material are melted by the molten slag resistance heat generated by the flux. During welding, a certain amount of molten slag covers the surface of the weld metal in a molten state. The amount of the slag affects the stability of welding, and even if the amount of slag is large or small, the stability of the welding is impaired, spatter increases, welding stops in the middle, or poor penetration occurs. When welding with a flux-cored wire containing a slag former and oxide on the welding wire, the amount of molten slag increases and the composition changes with time as welding progresses, so stable welding is performed to the end. It turned out to be difficult. Therefore, the present inventors consider that it is essential that the flux-cored wire for electroslag welding is a metal-cored welding wire that does not contain a slag-forming component, and welding in a metal-cored wire. Various new means for reducing oxygen and improving toughness and ductility of metals have been studied.
その結果、適正な成分組成としたメタル粉入りワイヤにおいて、脱酸元素のうち、ＴｉとＭｇは溶接金属中の酸素量低減に有効である一方、Ａｌは逆に溶接金属中の酸素量を増加させること、ＴｉとＭｇとは、さらに、溶接金属中の酸素量を低減するだけでなく、酸化物をソリッドワイヤによる溶接金属中におけるよりも大幅に微細化し、その結果、ソリッドワイヤよりも溶接金属の靭性、延性を向上させることが可能であることを新たに知見した。 As a result, in the wire containing metal powder with an appropriate component composition, among the deoxidizing elements, Ti and Mg are effective in reducing the amount of oxygen in the weld metal, while Al conversely increases the amount of oxygen in the weld metal. Ti and Mg not only reduce the amount of oxygen in the weld metal, but also make the oxide much finer than in the solid wire weld metal, resulting in a weld metal than the solid wire. It was newly discovered that the toughness and ductility of the steel can be improved.
メタル粉入りワイヤを用いてエレクトロスラグ溶接したときの溶接金属中のＯ量に及ぼすＡｌ、Ｔｉ及びＭｇの効果を具体的に図１に示す。メタル粉入りワイヤのベース組成を質量％で、Ｃ：０．０２９％、Ｓｉ：０．５８％、Ｍｎ：２．２１％、Ｐ：０．０７％、Ｓ：０．００３５％、Ｍｏ：０．５１％、Ｂ：０．００５６％、Ｎ：０．００５９％とし、Ａｌ、Ｔｉ、Ｍｇ含有量を様々に変化させた溶接ワイヤ（直径１．６ｍｍ）を試作し、板厚５０ｍｍの引張強さ４９０ＭＰａ級の溶接構造用高張力鋼板を用いて、Ｔ字継手によるエレクトロスラグ溶接を実施した（継手形状は図２参照、溶接条件は実施例の表４の通り）。溶接後の溶接金属の成分分析を行い、溶接金属中のＯ量をワイヤ中Ｔｉ、Ｍｇ量ごとに層別してワイヤ中Ａｌ含有量で整理した結果が図１である。Ｔｉ、Ｍｇ添加有無によらず、溶接金属中のＯ量はワイヤ中Ａｌ量が増加するにともなって大きく増加しており、メタル粉入りワイヤを用いて溶接したときの溶接金属中のＯ量に対して、Ａｌの悪影響が最も強い。ただし、Ｔｉ、Ｍｇが無添加、Ｔｉ、Ｍｇ各単独添加の場合は、Ａｌ量がごく少ない場合を除いて溶接金属中のＯ量は０．０１５％を超えて多く含有され、これが、特に溶接金属靭性を劣化させる要因となる。一方、Ｔｉ、Ｍｇを適正量複合添加させると、溶接ワイヤ中のＡｌ含有量の広い範囲で、安定的に溶接金属の低Ｏ化が達成され、特に、溶接ワイヤ中のＡｌ含有量が０．０３％以下では、溶接金属中のＯ含有量は０．０１５％を十分下まわり、ほぼソリッドワイヤで溶接したときの溶接金属中のＯ含有量とほぼ同等かそれ以上に低減される。また、溶接金属中のＯ量は同じでも、酸化物はソリッドワイヤによるよりも均一微細分散され、その結果、溶接金属靭性が大きく改善される。 The effect of Al, Ti and Mg on the amount of O in the weld metal when electroslag welding is performed using a wire containing metal powder is specifically shown in FIG. The base composition of the wire containing metal powder is in mass%, C: 0.029%, Si: 0.58%, Mn: 2.21%, P: 0.07%, S: 0.0035%, Mo: 0 .51%, B: 0.0056%, N: 0.0059%, a trial manufacture of welding wire (diameter 1.6mm) with various contents of Al, Ti, Mg, and tensile strength of 50mm thickness Electroslag welding with a T-shaped joint was carried out using a 490 MPa class high-strength steel sheet for welded structure (see FIG. 2 for the joint shape, and the welding conditions are as shown in Table 4 of the examples). FIG. 1 shows the result of analyzing the components of the weld metal after welding, stratifying the O content in the weld metal by the Ti content and Mg content in the wire, and arranging them by the Al content in the wire. Regardless of whether Ti or Mg is added, the amount of O in the weld metal greatly increases as the amount of Al in the wire increases, and the amount of O in the weld metal when welded using a metal powdered wire is increased. On the other hand, Al has the strongest adverse effect. However, when Ti and Mg are not added and Ti and Mg are added individually, the amount of O in the weld metal is more than 0.015% except when the amount of Al is very small. It becomes a factor which degrades metal toughness. On the other hand, when Ti and Mg are added in appropriate amounts, the weld metal can be stably reduced in O in a wide range of Al content in the welding wire. If it is less than 03%, the O content in the weld metal is well below 0.015%, and is almost equal to or more than the O content in the weld metal when welding with a solid wire. Further, even if the amount of O in the weld metal is the same, the oxide is more uniformly and finely dispersed than with the solid wire, and as a result, the weld metal toughness is greatly improved.
以上の実験結果から、メタル粉入りワイヤを用いてエレクトロスラグ溶接したときに溶接金属中のＯ量を十分低減して、溶接金属靭性を安定的に確保するためには、溶接ワイヤ中にＴｉ、Ｍｇを適正量添加した上で、溶接ワイヤ中のＡｌ含有量を０．０３％以下にすることが重要であることを新たに見出した。 From the above experimental results, in order to sufficiently reduce the amount of O in the weld metal when electroslag welding is performed using a wire containing metal powder and to ensure stable weld metal toughness, Ti, It was newly found out that it is important to make the Al content in the welding wire 0.03% or less after adding an appropriate amount of Mg.
なお、本発明は、特に、溶接ワイヤの形態に関して、鋼製外皮にシームレスパイプを用いたものか、或いは、造管時にシーム部を溶接して外気と内部の充填剤とが直接接触しないようにして伸線加工した「シームレス溶接ワイヤ」に適用することを目的とする。これは、外気との接触を遮断できない巻き締め型メタル粉入りワイヤでは、製造後、使用までの間の充填物の酸化を十分抑制することができず、本発明の成分要件を満足しても、溶接ワイヤの使用時期、保管状態によっては、溶接金属のＯ量低減を達成できない可能性があるためである。また、巻き締め型のメタル粉入りワイヤでは吸湿のために溶接金属中の拡散性水素を増加させて、鋼板や溶接金属の耐低温割れ性が劣る虞もあり、好ましくない。 In the present invention, in particular, regarding the form of the welding wire, a seamless pipe is used for the steel outer shell, or the seam portion is welded at the time of pipe making so that the outside air does not directly contact the internal filler. It is intended to be applied to "seamless welding wire" that has been drawn. This is because, with a wire with a clamped metal powder that cannot block contact with the outside air, it is not possible to sufficiently suppress the oxidation of the filling material after production until use, even if the component requirements of the present invention are satisfied. This is because there is a possibility that reduction in the amount of O of the weld metal cannot be achieved depending on the use time and storage state of the welding wire. In addition, a wire with a metal powder of a tightening type is not preferable because diffusible hydrogen in the weld metal is increased due to moisture absorption, and the cold crack resistance of the steel plate or weld metal may be deteriorated.
本発明は上記新知見に基づき、さらに、詳細な実験を加えて発明するに至ったものであり、その発明の要旨は以下の通りである。 The present invention has been made based on the above-mentioned new findings and further invented with detailed experiments, and the gist of the invention is as follows.
（１）鋼製外皮内にメタル粉を充填してなるエレクトロスラグ溶接用溶接ワイヤにおいて、前記鋼製外皮が鋼製外皮全質量に対する質量％で、
Ｃ ：０．００５〜０．１０％、
Ｓｉ：０．０１〜１．０％、
Ｍｎ：０．１〜２．５％、
Ｐ ：０．０２％以下、
Ｓ ：０．００８％以下、
Ａｌ：０．０３０％以下、
Ｎ ：０．００１〜０．０１０％、
Ｏ ：０．０１０％以下、
を含有し、残部がＦｅおよび不可避不純物からなり、さらに、溶接ワイヤ全体の成分組成が、溶接ワイヤ全質量に対する質量％で、
Ｃ ：０．００５〜０．１０％、
Ｓｉ：０．１０〜１．５％、
Ｍｎ：０．１〜２．５％、
Ｐ ：０．０２％以下、
Ｓ ：０．００８％以下、
Ａｌ：０．０３０％以下、
Ｎ ：０．００１〜０．０１０％、
Ｔｉ：０．００５〜０．３０％、
Ｍｇ：０．０１５〜０．３０％、
Ｏ ：０．１５％以下、
を含有し、残部がＦｅおよび不可避不純物からなり、かつ、［Ｍｇ］＋［Ｔｉ］／５＝０．０２０〜０．３０％であり、合わせて、前記メタル粉の充填率が溶接ワイヤ全体に対する質量％で５〜２０％であることを特徴とする、メタル粉入りエレクトロスラグ溶接用溶接ワイヤ。
ただし、［Ｍｇ］、［Ｔｉ］は各々溶接ワイヤ全体の成分組成としてのＭｇとＴｉの質量％である。
(1) In a welding wire for electroslag welding in which metal powder is filled in a steel outer shell, the steel outer shell is in mass% with respect to the total mass of the steel outer shell,
C: 0.005-0.10%,
Si: 0.01 to 1.0%,
Mn: 0.1 to 2.5%
P: 0.02% or less,
S: 0.008% or less,
Al: 0.030% or less,
N: 0.001 to 0.010%,
O: 0.010% or less,
The balance is composed of Fe and inevitable impurities, and the component composition of the entire welding wire is, in mass% with respect to the total mass of the welding wire,
C: 0.005-0.10%,
Si: 0.10 to 1.5%
Mn: 0.1 to 2.5%
P: 0.02% or less,
S: 0.008% or less,
Al: 0.030% or less,
N: 0.001 to 0.010%,
Ti: 0.005 to 0.30%,
Mg: 0.015-0.30%,
O: 0.15% or less,
And the balance consists of Fe and inevitable impurities, and [Mg] + [Ti] /5=0.020 to 0.30%, and the filling rate of the metal powder is based on the whole welding wire A welding wire for electroslag welding containing metal powder, characterized by being 5 to 20% by mass.
However, [Mg] and [Ti] are mass% of Mg and Ti as the component composition of the whole welding wire, respectively.
（２）前記溶接ワイヤが、さらに、溶接ワイヤ全体の成分組成が、溶接ワイヤ全質量に対する質量％で、
Ｃｕ：０．０１〜１．５０％、
Ｎｉ：０．０１〜６．０％、
Ｃｒ：０．０１〜２．０％、
Ｍｏ：０．０１〜２．０％、
Ｗ ：０．０１〜２．０％、
Ｎｂ：０．００２〜０．１０％、
Ｖ ：０．００５〜０．５０％、
Ｔａ：０．００５〜０．５０％、
Ｚｒ：０．００５〜０．５０％、
Ｂ ：０．０００２〜０．０１０％、
の１種または２種以上を含有することを特徴とする、前記（１）に記載のメタル粉入りエレクトロスラグ溶接用溶接ワイヤ。
(2) In the welding wire, the component composition of the entire welding wire is mass% with respect to the total mass of the welding wire,
Cu: 0.01 to 1.50%,
Ni: 0.01-6.0%,
Cr: 0.01 to 2.0%,
Mo: 0.01 to 2.0%,
W: 0.01 to 2.0%,
Nb: 0.002 to 0.10%,
V: 0.005-0.50%,
Ta: 0.005 to 0.50%,
Zr: 0.005 to 0.50%,
B: 0.0002 to 0.010%,
The welding wire for electroslag welding containing metal powder according to (1) above, comprising one or more of the above.
（３）前記溶接ワイヤが、さらに、溶接ワイヤ全体の成分組成が、溶接ワイヤ全質量に対する質量％で、
Ｃａ：０．０００２〜０．００５０％、
ＲＥＭ：０．０００２〜０．００５０％、
の１種または２種を含有することを特徴とする、前記（１）または（２）に記載のメタル粉入りエレクトロスラグ溶接用溶接ワイヤ。
(3) In the welding wire, the component composition of the entire welding wire is, in mass% with respect to the total mass of the welding wire,
Ca: 0.0002 to 0.0050%,
REM: 0.0002 to 0.0050%,
The welding wire for electroslag welding containing metal powder according to the above (1) or (2), characterized by containing one or two of the above.
（４）前記鋼製外皮が、さらに、質量％で、
Ｃｕ：０．０１〜１．５０％、
Ｎｉ：０．０１〜６．０％、
Ｃｒ：０．０１〜２．０％、
Ｍｏ：０．０１〜２．０％、
Ｗ ：０．０１〜２．０％、
Ｎｂ：０．００２〜０．１０％、
Ｖ ：０．００５〜０．５０％、
Ｔａ：０．００５〜０．５０％、
Ｚｒ：０．００５〜０．５０％、
Ｂ ：０．０００２〜０．００５０％、
の１種または２種以上を含有することを特徴とする、前記（１）〜（３）のいずれかに記載のメタル粉入りエレクトロスラグ溶接用溶接ワイヤ。
(4) The steel outer shell is further in mass%,
Cu: 0.01 to 1.50%,
Ni: 0.01-6.0%,
Cr: 0.01 to 2.0%,
Mo: 0.01 to 2.0%,
W: 0.01 to 2.0%,
Nb: 0.002 to 0.10%,
V: 0.005-0.50%,
Ta: 0.005 to 0.50%,
Zr: 0.005 to 0.50%,
B: 0.0002 to 0.0050%,
The welding wire for electroslag welding containing metal powder according to any one of the above (1) to (3), comprising one or more of the above.
（５）前記鋼製外皮が、さらに、質量％で、
Ｔｉ：０．００５〜０．０５０％、
Ｍｇ：０．００２〜０．０１０％、
Ｃａ：０．０００２〜０．００５０％、
ＲＥＭ：０．０００２〜０．００５０％、
の１種または２種以上を含有することを特徴とする、前記（１）〜（４）のいずれかに記載のメタル粉入りエレクトロスラグ溶接用溶接ワイヤ。
(5) The steel outer shell is further in mass%,
Ti: 0.005 to 0.050%,
Mg: 0.002 to 0.010%,
Ca: 0.0002 to 0.0050%,
REM: 0.0002 to 0.0050%,
The welding wire for electroslag welding containing metal powder according to any one of the above (1) to (4), comprising one or more of the following.
本発明によれば、エレクトロスラグ溶接において、鋼材の板厚や成分によらず、高靭性な溶接金属が得られる、汎用性が高く、かつ、安価な溶接ワイヤが得られ、産業上の効果は極めて顕著である。 According to the present invention, in electroslag welding, a highly versatile and inexpensive welding wire can be obtained, regardless of the plate thickness and components of the steel material, and a versatile and inexpensive welding wire can be obtained. Extremely prominent.
本発明のメタル粉入りエレクトロスラグ溶接用溶接ワイヤは、鋼製外皮と内部の充填剤からなり、本発明が目的とする効果を発揮するための成分要件は、溶接ワイヤ全体と、鋼製外皮についても必要である。溶接ワイヤ全体としてだけでなく、鋼製外皮自体の成分組成を限定するのは、溶接ワイヤに占める鋼製外皮の割合が多いため、溶接金属の成分組成を安定的に確保するには、主要な元素については鋼製外皮の成分組成としても限定することが好ましいためである。以下、鋼製外皮の成分組成の限定理由、溶接ワイヤ全体としての成分組成の限定理由、メタル粉の充填率の限定理由を順次詳細に説明する。 The welding wire for electroslag welding containing metal powder of the present invention comprises a steel outer shell and an inner filler, and the component requirements for exerting the intended effect of the present invention are the entire welding wire and the steel outer shell. Is also necessary. Limiting the component composition of the steel sheath itself, as well as the entire welding wire, is the main factor for ensuring a stable component composition of the weld metal because the ratio of the steel sheath to the welding wire is large. This is because it is preferable to limit the element composition of the steel shell. Hereinafter, the reasons for limiting the component composition of the steel outer sheath, the reasons for limiting the component composition of the entire welding wire, and the reasons for limiting the filling rate of the metal powder will be described in detail.
［鋼製外皮の成分組成］
鋼製外皮の成分組成は、鋼製外皮全質量に対する質量％で、Ｃ：０．００５〜０．１０％、Ｓｉ：０．０１〜１．０％、Ｍｎ：０．１〜２．５％、Ｐ：０．０２％以下、Ｓ：０．００８％以下、Ａｌ：０．０３０％以下、Ｎ：０．００１〜０．０１０％、Ｏ：０．０１０％以下、を含有し、必要に応じて、Ｃｕ：０．０１〜１．５０％、Ｎｉ：０．０１〜６．０％、Ｃｒ：０．０１〜２．０％、Ｍｏ：０．０１〜２．０％、Ｗ：０．０１〜２．０％、Ｎｂ：０．００２〜０．１０％、Ｖ：０．００５〜０．５０％、Ｔａ：０．００５〜０．５０％、Ｚｒ：０．００５〜０．５０％、Ｂ：０．０００２〜０．００５０％の１種または２種以上を含有し、さらに、必要に応じて、Ｔｉ：０．００５〜０．０５０％、Ｍｇ：０．００２〜０．０１０％、Ｃａ：０．０００２〜０．００５０％、ＲＥＭ：０．０００２〜０．００５０％の１種または２種以上を含有することが要件となる。
[Component composition of steel outer skin]
The component composition of the steel outer shell is% by mass with respect to the total mass of the steel outer shell, C: 0.005-0.10%, Si: 0.01-1.0%, Mn: 0.1-2.5% P: 0.02% or less, S: 0.008% or less, Al: 0.030% or less, N: 0.001 to 0.010%, O: 0.010% or less, and necessary Accordingly, Cu: 0.01 to 1.50%, Ni: 0.01 to 6.0%, Cr: 0.01 to 2.0%, Mo: 0.01 to 2.0%, W: 0 0.01-2.0%, Nb: 0.002-0.10%, V: 0.005-0.50%, Ta: 0.005-0.50%, Zr: 0.005-0.50 %, B: 0.0002 to 0.0050%, or two or more of Ti, 0.005 to 0.050%, Mg: 0.002 to 0.010, if necessary. , Ca: 0.0002~0.0050%, REM: a from 0.0002 to 0.0050% of one or requirement containing two or more.
先ず、必須要件である、Ｃ、Ｓｉ、Ｍｎ、Ｐ、Ｓ、Ａｌ、Ｎ、Ｏの限定理由を述べる。ここで、に成分についての％は質量％を意味する。 First, the reasons for limiting C, Si, Mn, P, S, Al, N, and O, which are essential requirements, will be described. Here, “%” for the component means “% by mass”.
「Ｃ：０．００５〜０．１０％」
鋼製外皮のＣは０．００５％以上とする。鋼製外皮のＣ含有量を０．００５％未満とすることは工業的には容易でないため、本発明においては鋼製外皮のＣ含有量の下限を０．００５％とする。一方、鋼製外皮のＣ含有量が０．１０％超であると、他の元素の含有量によっては鋼製外皮の強度が過度に高くなり、溶接ワイヤの製造性に問題が生じる場合があり、好ましくない。また、鋼製外皮のＣ含有量が０．１０％超であると、溶接ワイヤ全体のＣ量の調整範囲が制限されるため点も好ましくない。従って、本発明においては、鋼製外皮のＣ含有量を０．００５〜０．１０％の範囲に限定する。
"C: 0.005-0.10%"
C of the steel outer shell is 0.005% or more. Since it is not industrially easy to make the C content of the steel outer shell less than 0.005%, the lower limit of the C content of the steel outer shell is set to 0.005% in the present invention. On the other hand, if the C content of the steel outer shell exceeds 0.10%, the strength of the steel outer shell may become excessively high depending on the content of other elements, which may cause a problem in the manufacturability of the welding wire. Is not preferable. Moreover, since the adjustment range of C amount of the whole welding wire is restrict | limited as C content of steel outer shells exceeds 0.10%, a point is also unpreferable. Therefore, in the present invention, the C content of the steel outer skin is limited to a range of 0.005 to 0.10%.
「Ｓｉ：０．０１〜１．０％」
Ｓｉは脱酸元素であり、Ｏ量を低減して鋼の健全性を保つ上で必要な元素である。鋼製外皮中のＳｉ含有量が０．０１％未満であると、他の脱酸元素量によっては、Ｏ含有量が過度に高くなったり、欠陥が生じて、鋼製外皮の靭性や延性を劣化させ、鋼製外皮の製造性を損ねる虞がある。また、鋼製外皮中のＳｉ含有量が１．０％超であると、鋼中に粗大な介在物が形成されやすくなり、また、固溶強化により鋼製外皮の強度が過度に高くなるため、溶接ワイヤの製造性が阻害される可能性が高くなるため、好ましくない。そのため、本発明においては、製外皮のＳｉ含有量を０．０１〜１．０％の範囲に限定する。
"Si: 0.01-1.0%"
Si is a deoxidizing element, and is an element necessary for reducing the amount of O and maintaining the soundness of steel. If the Si content in the steel shell is less than 0.01%, depending on the amount of other deoxidizing elements, the O content may become excessively high or defects may occur, resulting in the toughness and ductility of the steel shell. There is a possibility of deteriorating and impairing the manufacturability of the steel outer skin. Further, if the Si content in the steel outer shell exceeds 1.0%, coarse inclusions are easily formed in the steel, and the strength of the steel outer shell is excessively increased by solid solution strengthening. Since the possibility that the manufacturability of the welding wire is hindered increases, it is not preferable. Therefore, in the present invention, the Si content of the outer shell is limited to a range of 0.01 to 1.0%.
「Ｍｎ：０．１〜２．５％」
Ｍｎは脱酸元素としても有用であり、Ｓｉと同様、鋼製外皮の健全性を保ち、溶接ワイヤの製造性を阻害しないために必要である。また、溶接金属に適正量含有されることで、溶接金属の強度と靭性向上に重要な元素であるため、溶接ワイヤの成分元素として必須であり、本発明においては、溶接金属のＭｎ量安定確保のために、鋼製外皮の成分範囲も限定する。鋼製外皮中のＭｎ量が０．１％未満であると、他の脱酸元素量によっては、Ｏ含有量が過度に高くなったり、欠陥が生じて、鋼製外皮の靭性や延性を劣化させ、鋼製外皮の製造性を損ねる虞がある。また、溶接ワイヤ全体としてのＭｎ量を確保するためには充填剤中のＭｎ含有量を高める必要があるが、その場合、鋼製外皮に含有させる場合よりも、溶接中のスラグ生成量が多くなって、溶接作業性に問題が生じる虞が高くなるため、好ましくない。一方、鋼製外皮中のＭｎ含有量が２．５％超になると、鋼製外皮の強度が過度に高くなったり、伸線加工中の加工硬化量が顕著となるため、溶接ワイヤの伸線中にワイヤが破断したり等、溶接ワイヤの製造性が著しく劣化するため、好ましくない。従って、本発明においては、製外皮のＭｎ含有量を０．１〜２．５％の範囲に限定する。
“Mn: 0.1 to 2.5%”
Mn is also useful as a deoxidizing element and, like Si, is necessary for maintaining the soundness of the steel outer sheath and not inhibiting the manufacturability of the welding wire. In addition, since it is an important element for improving the strength and toughness of the weld metal when it is contained in an appropriate amount in the weld metal, it is essential as a component element of the welding wire. Therefore, the component range of the steel outer shell is also limited. If the amount of Mn in the steel shell is less than 0.1%, depending on the amount of other deoxidizing elements, the O content may become excessively high or defects may occur, degrading the toughness and ductility of the steel shell. And the steel manufacturability may be impaired. Moreover, in order to ensure the amount of Mn as the whole welding wire, it is necessary to increase the Mn content in the filler, but in that case, the amount of slag generation during welding is larger than when contained in the steel outer sheath. This is not preferable because there is a high possibility of problems in welding workability. On the other hand, if the Mn content in the steel outer shell exceeds 2.5%, the strength of the steel outer shell becomes excessively high or the work hardening amount during wire drawing becomes significant, so that the wire drawing of the welding wire Since the productivity of the welding wire is significantly deteriorated, such as the wire breaking inside, it is not preferable. Therefore, in the present invention, the Mn content of the outer shell is limited to a range of 0.1 to 2.5%.
「Ｐ ：０．０２％以下」
Ｐは靭性、耐割れ性等を低下させる不純物元素であり、鋼製外皮中の含有量も少ない方が好ましい。ただし、鋼製外皮中の含有量が０．０２％以下であれば、鋼製外皮の製造性や、溶接金属の特性に対する悪影響の程度が許容できる範囲であるため、本発明においては、鋼製外皮中のＰ含有量は０．０２％以下とする。
“P: 0.02% or less”
P is an impurity element that lowers toughness, crack resistance and the like, and it is preferable that the content in the steel outer shell is small. However, if the content in the steel outer shell is 0.02% or less, the manufacturability of the steel outer shell and the degree of adverse effects on the properties of the weld metal are in an acceptable range. The P content in the outer skin is 0.02% or less.
「Ｓ ：０．００８％以下」
Ｓも不純物元素であるため、鋼製外皮中には極力含有しない方が好ましい。ただし、鋼製外皮中の含有量が０．００８％以下であれば、鋼製外皮の製造性や、溶接金属の特性に対する悪影響の程度が許容できる範囲であるため、本発明においては、鋼製外皮中のＳ含有量は０．００８％以下とする。
“S: 0.008% or less”
Since S is also an impurity element, it is preferable that S be not contained as much as possible. However, if the content in the steel outer shell is 0.008% or less, the manufacturability of the steel outer shell and the degree of adverse effects on the properties of the weld metal are in an acceptable range. The S content in the outer skin is 0.008% or less.
「Ａｌ：０．０３０％以下」
Ａｌは溶接金属中のＯ量を高めたり、溶接中のスラグを増やして、スパッタの発生等、溶接作業性を損なうため、本発明においては溶接ワイヤ中のＡｌ量は少ない方が好ましい。従って、鋼製外皮中のＡｌ量もその上限を規定する必要がある。溶接中にスラグが増加してスパッタ増加やそれに起因したワイヤの送給不良等を起こさず、また、溶接金属中のＯ量の増加が許容できる範囲内としては、溶接ワイヤにおける含有量の上限が０．０３０％であるたため、溶接ワイヤの大半を構成する鋼製外皮においてもＡｌの上限を０．０３０％とする。ただし、より確実にＡｌの悪影響を抑制するためには、鋼製外皮中のＡｌ含有量は０．０１０％未満とすることがより好ましい。
“Al: 0.030% or less”
Since Al increases the amount of O in the weld metal or increases the slag during welding and impairs the welding workability such as generation of spatter, it is preferable that the amount of Al in the welding wire is small in the present invention. Therefore, the upper limit is also required for the amount of Al in the steel outer shell. The upper limit of the content in the welding wire is within the range where the increase in the amount of O in the weld metal can be tolerated without increasing the slag during welding and causing an increase in spatter and poor wire feeding due to it. Since it is 0.030%, the upper limit of Al is set to 0.030% also in the steel outer shell constituting the majority of the welding wire. However, in order to suppress the adverse effect of Al more reliably, the Al content in the steel outer shell is more preferably less than 0.010%.
「Ｎ ：０．００１〜０．０１０％」
溶接金属中のＮは微量であれば、ＡｌやＴｉと窒化物を形成して、組織の微細化を通して、溶接金属の機械的性質を向上する効果を有する。従って、鋼製外皮中にも適正量含有させることは好ましい。鋼製外皮中のＮ含有量が０．００１％未満であると溶接金属の特性向上効果が明確でないことと、工業的に鋼中にＮ量を０．００１％未満とすることが容易でないことから、本発明においては、鋼製外皮中のＮ含有量の下限を０．００１％と定める。一方、溶接金属中にＮを過剰に含有すると、溶接金属の靭性を顕著に劣化させる。溶接金属に対するＮの悪影響が生じないとの観点から、鋼製外皮中のＮ量は０．０１０％以下とする必要がある。そのため、本発明においては、鋼製外皮のＮ含有量を０．００１〜０．０１０％の範囲に限定する。
“N: 0.001 to 0.010%”
If the amount of N in the weld metal is small, it has the effect of improving the mechanical properties of the weld metal by forming Al and Ti and nitrides and refining the structure. Therefore, it is preferable to contain an appropriate amount in the steel outer shell. If the N content in the steel shell is less than 0.001%, the effect of improving the properties of the weld metal is not clear, and it is not easy to industrially make the N content less than 0.001% in steel. Therefore, in the present invention, the lower limit of the N content in the steel outer skin is defined as 0.001%. On the other hand, when N is contained excessively in the weld metal, the toughness of the weld metal is remarkably deteriorated. From the standpoint that N does not adversely affect the weld metal, the N content in the steel outer shell needs to be 0.010% or less. Therefore, in the present invention, the N content of the steel outer skin is limited to a range of 0.001 to 0.010%.
「Ｏ ：０．０１０％以下」
Ｏも不純物元素であり、鋼の延性を低下させたり、加工性を阻害するため、極力低減することが好ましい。鋼製外皮中のＯ量が０．０１０％超であると、第一に、溶接ワイヤに伸線加工するときに加工性が劣化して、断線等を引き起こす原因となるため、好ましくない。また、溶接ワイヤとしてのＯ量増加にもつながり、結果として溶接金属のＯ量を高めて延性や靭性劣化を生じるため、好ましくない。以上の理由から、本発明においては、鋼製外皮中のＯ含有量の上限を０．０１０％とする。
“O: 0.010% or less”
O is also an impurity element, and it is preferable to reduce it as much as possible in order to reduce the ductility of the steel or impair the workability. If the amount of O in the steel outer shell is more than 0.010%, firstly, workability deteriorates when wire-drawing is performed on the welding wire, causing disconnection or the like, which is not preferable. Moreover, it leads to an increase in the amount of O as a welding wire, and as a result, the amount of O in the weld metal is increased to cause ductility and toughness deterioration. For the above reasons, in the present invention, the upper limit of the O content in the steel outer shell is set to 0.010%.
以上が、鋼製外皮の成分組成のうち、必須要件である、Ｃ、Ｓｉ、Ｍｎ、Ｐ、Ｓ、Ａｌ、Ｎ、Ｏの限定理由である。本発明においては、溶接金属の強度・靭性の調整のために、選択的に元素を用いることが可能であり、該選択元素を鋼製外皮にも必要に応じて含有させることができる。ただし、選択的に用いる場合でも、種々理由によりその含有量は限定することが必要である。以下に、鋼製外皮に含有させる選択元素の限定理由を述べる。 The above is the reason for limiting C, Si, Mn, P, S, Al, N, and O, which are essential requirements, among the component compositions of the steel outer shell. In the present invention, an element can be selectively used for adjusting the strength and toughness of the weld metal, and the selected element can be contained in the steel outer shell as necessary. However, even when it is selectively used, its content needs to be limited for various reasons. The reasons for limiting the selection elements to be contained in the steel outer shell will be described below.
「Ｃｕ：０．０１〜１．５０％」
鋼製外皮中にＣｕを含有させる場合は、その範囲は０．０１〜１．５０％とする。Ｃｕは、溶接金属の強度向上に有効な元素である。本発明においても、必要に応じて鋼製外皮中にＣｕを含有させることが可能である。溶接金属におけるＣｕの効果を明確に発揮するために、鋼製外皮に含有させる場合は、Ｃｕは鋼製外皮全質量に対する質量％で０．０１％以上含有させる必要がある。一方、鋼製外皮に１．５０％を超えて含有させると、鋼製外皮製造中や溶接ワイヤ製造中に鋼製外皮に割れを生じる虞がある。また、溶接金属の含有量が過剰となって、溶接金属の靭性や耐高温割れ性を劣化させる虞があるため、本発明においては、鋼製外皮中にＣｕを含有させる場合、鋼製外皮全質量に対する質量％で０．０１〜１．５０％に限定する。
“Cu: 0.01 to 1.50%”
When Cu is contained in the steel outer shell, the range is 0.01 to 1.50%. Cu is an element effective for improving the strength of the weld metal. Also in the present invention, Cu can be contained in the steel outer shell as necessary. In order to clearly exhibit the effect of Cu in the weld metal, when it is contained in the steel outer shell, it is necessary to contain Cu by 0.01% or more by mass% with respect to the total mass of the steel outer shell. On the other hand, if the steel outer shell contains more than 1.50%, the steel outer shell may be cracked during the manufacturing of the steel outer shell or the welding wire. In addition, since the weld metal content becomes excessive and may deteriorate the toughness and hot cracking resistance of the weld metal, in the present invention, when Cu is contained in the steel outer shell, the entire steel outer shell is included. It is limited to 0.01 to 1.50% by mass% with respect to mass.
「Ｎｉ：０．０１〜６．０％」
Ｎｉは、一般的に鋼の靭性向上に極めて有効な元素である。本発明においても、必要に応じて溶接ワイヤ中にＮｉを含有させることが可能であるため、鋼製外皮中にも含有させることができる。その場合、Ｎｉによる高靭化効果を明確に享受するためには、鋼製外皮中に０．０１％以上含有させる必要がある。一方、鋼製外皮中に６．０％を超えて含有させることは鋼製外皮の製造コストが過大となるためと、溶接ワイヤの製造性が劣化するため、好ましくない。そのため、鋼製外皮中にＮｉを含有させる場合は、鋼製外皮全質量に対する質量％で０．０１〜６．０％に限定する。
"Ni: 0.01-6.0%"
Ni is an element that is generally extremely effective for improving the toughness of steel. Also in the present invention, if necessary, Ni can be contained in the welding wire, so that it can also be contained in the steel outer sheath. In that case, in order to clearly enjoy the toughening effect of Ni, it is necessary to contain 0.01% or more in the steel outer shell. On the other hand, the content exceeding 6.0% in the steel outer shell is not preferable because the manufacturing cost of the steel outer shell becomes excessive and the manufacturability of the welding wire deteriorates. Therefore, when Ni is contained in the steel outer shell, the content is limited to 0.01 to 6.0% by mass% with respect to the total mass of the steel outer shell.
「Ｃｒ：０．０１〜２．０％」
Ｃｒは強度を高めるのに有効な元素であるため、必要に応じて溶接ワイヤ中に含有させることができる。鋼製外皮中に含有させて溶接金属の高強度化に用いる場合は、その含有量は０．０１％以上とする必要がある。鋼製外皮中の含有量が０．０１％未満であると効果が明確でない。一方、鋼製外皮中含有量が２．０％を超えると、溶接ワイヤの製造性が劣化し、また、溶接金属中に過度に含有して靭性を劣化させる虞があるため、好ましくない。そこで、本発明においては、鋼製外皮中にＣｒを含有させる場合は、鋼製外皮全質量に対する質量％で０．０１〜２．０％に限定する。
"Cr: 0.01-2.0%"
Since Cr is an effective element for increasing the strength, it can be contained in the welding wire as necessary. When it is contained in the steel outer shell and used for increasing the strength of the weld metal, its content needs to be 0.01% or more. If the content in the steel outer shell is less than 0.01%, the effect is not clear. On the other hand, when the content in the steel outer shell exceeds 2.0%, the manufacturability of the welding wire is deteriorated, and it is not preferable because it may be excessively contained in the weld metal to deteriorate the toughness. Therefore, in the present invention, when Cr is contained in the steel outer shell, the content is limited to 0.01 to 2.0% by mass% with respect to the total mass of the steel outer shell.
「Ｍｏ：０．０１〜２．０％」
Ｍｏは、焼入性を高めて溶接金属組織のベイナイトあるいはアシキュラーフェライトの微細化を通して靱性向上に有効な元素であり、かつ、固溶強化、析出強化により強度向上にも有効な元素である。この効果を得るために鋼製外皮にＭｏを含有させる場合は、０．０１％以上含有させる必要がある。しかしながら、２．０％を超えて鋼製外皮に過剰に含有されると、伸線加工中の硬化が著しくなって、伸線加工中の破断等、溶接ワイヤの製造性を阻害する可能性が高くなるため、好ましくない。そのため、本発明においては、鋼製外皮中にＭｏを含有させる場合は、鋼製外皮全質量に対する質量％で０．０１〜２．０％に限定する。
"Mo: 0.01-2.0%"
Mo is an element effective for improving toughness by increasing hardenability and making bainite or acicular ferrite fine in the weld metal structure, and is also effective for improving strength by solid solution strengthening and precipitation strengthening. In order to obtain this effect, when Mo is contained in the steel outer shell, it is necessary to contain 0.01% or more. However, if it exceeds 2.0% and is excessively contained in the steel outer sheath, the hardening during the wire drawing process becomes remarkable, and there is a possibility that the manufacturability of the welding wire, such as breakage during the wire drawing process, is hindered. Since it becomes high, it is not preferable. Therefore, in this invention, when Mo is contained in the steel outer shell, it is limited to 0.01 to 2.0% by mass% with respect to the total mass of the steel outer shell.
「Ｗ ：０．０１〜２．０％」
Ｗは溶接金属の機械的性質、溶接ワイヤの製造性に対して、Ｍｏとほぼ同一の靱性向上に有効な元素であり、かつ、固溶強化、析出強化により強度向上にも有効な効果を有するため、Ｍｏと同じ理由により、鋼製外皮中にＷを含有させる場合は、鋼製外皮全質量に対する質量％で０．０１〜２．０％に限定する。
"W: 0.01-2.0%"
W is an element effective for improving the toughness almost the same as Mo for the mechanical properties of weld metal and the manufacturability of weld wire, and also has an effect of improving the strength by solid solution strengthening and precipitation strengthening. Therefore, for the same reason as Mo, when W is contained in the steel outer shell, the content is limited to 0.01 to 2.0% by mass% with respect to the total mass of the steel outer shell.
「Ｎｂ：０．００２〜０．１０％」
Ｎｂは、溶接金属中に含有されると、焼入性向上効果、析出強化によって、溶接金属の強度向上に有効である。鋼製外皮にＮｂを含有させる場合、この効果を確実に発揮するためには、鋼製外皮中のＮｂ含有量は０．００２％以上とする必要がある。一方、鋼製外皮中のＮｂ量が０．１０％を超えると、鋼製外皮の製造において、表面割れの問題が懸念され、また、溶接ワイヤ製造における伸線加工性を劣化させる虞も大きくなるため、好ましくない。また、鋼製外皮に０．１０％を超えてＮｂが含有されると、溶接金属中のＮｂ量が過大となって、溶接金属に粗大なＮｂ析出物が形成されるために、溶接金属の靭性劣化が著しくなる可能性もあるため、好ましくない。以上の理由により、本発明においては、鋼製外皮中にＮｂを含有させる場合、Ｎｂ含有量の範囲を０．００２〜０．１０％に限定する。
“Nb: 0.002 to 0.10%”
When Nb is contained in the weld metal, it is effective in improving the strength of the weld metal due to the effect of improving hardenability and precipitation strengthening. In the case where Nb is contained in the steel outer shell, the Nb content in the steel outer shell needs to be 0.002% or more in order to reliably exhibit this effect. On the other hand, when the amount of Nb in the steel outer shell exceeds 0.10%, there is a concern about the problem of surface cracking in the manufacture of the steel outer shell, and the possibility of degrading the wire drawing workability in the welding wire manufacturing also increases. Therefore, it is not preferable. In addition, if the steel outer shell contains Nb exceeding 0.10%, the amount of Nb in the weld metal becomes excessive, and coarse Nb precipitates are formed on the weld metal. This is not preferable because there is a possibility that the toughness deteriorates significantly. For the above reasons, in the present invention, when Nb is contained in the steel outer shell, the range of Nb content is limited to 0.002 to 0.10%.
「Ｖ ：０．００５〜０．５０％」
Ｖは、溶接金属中に含有されると、主として析出強化によって、溶接金属の強度向上に有効である。鋼製外皮にＶを含有させる場合、この効果を確実に発揮するためには、鋼製外皮中のＶ含有量は０．００５％以上とする必要がある。一方、鋼製外皮のＶ含有量が０．５０％を超えて過大になると、Ｎｂと同様の理由により、鋼製外皮素材の製造性の劣化、溶接ワイヤの製造性の劣化、および、溶接金属の靭性劣化の可能性が無視できなくなるため、好ましくない。そのため、本発明においては、鋼製外皮中にＶを含有させる場合、Ｖ含有量の範囲を０．００５〜０．５０％に限定する。
“V: 0.005 to 0.50%”
When V is contained in the weld metal, it is effective for improving the strength of the weld metal mainly by precipitation strengthening. When V is contained in the steel outer shell, the V content in the steel outer shell needs to be 0.005% or more in order to reliably exhibit this effect. On the other hand, if the V content of the steel outer shell exceeds 0.50%, for the same reason as Nb, the manufacturability of the steel outer shell material, the manufacturability of the welding wire, and the weld metal are reduced. Since the possibility of deterioration of toughness cannot be ignored, it is not preferable. Therefore, in this invention, when V is contained in the steel outer shell, the range of the V content is limited to 0.005 to 0.50%.
「Ｔａ：０．００５〜０．５０％」
Ｔａは溶接金属の機械的性質、溶接ワイヤの製造性に対して、Ｖとほぼ同一の主として析出強化によって、溶接金属の強度向上に有効な効果を有するため、Ｖと同じ理由により、鋼製外皮中にＴａを含有させる場合は、鋼製外皮全質量に対する質量％で０．００５〜０．５０％に限定する。
"Ta: 0.005-0.50%"
Ta has the same effect as that of V on the mechanical properties of weld metal and the manufacturability of the weld wire, mainly by precipitation strengthening, and therefore has the effect of improving the strength of the weld metal. When Ta is contained therein, the content is limited to 0.005 to 0.50% by mass% with respect to the total mass of the steel outer shell.
「Ｚｒ：０．００５〜０．５０％」
Ｚｒも溶接金属の機械的性質、溶接ワイヤの製造性に対して、ＶやＴａとほぼ同一の主として析出強化によって、溶接金属の強度向上に有効な効果を有するため、同じ理由により、鋼製外皮中にＺｒを含有させる場合は、鋼製外皮全質量に対する質量％で０．００５〜０．５０％に限定する。
"Zr: 0.005-0.50%"
Zr also has an effective effect on improving the strength of weld metal, mainly by precipitation strengthening, which is almost the same as V and Ta, on the mechanical properties of weld metal and the manufacturability of weld wire. When Zr is contained therein, the content is limited to 0.005 to 0.50% in terms of mass% with respect to the total mass of the steel outer shell.
「Ｂ ：０．０００２〜０．００５０％」
Ｂは、溶接金属中に適正量含有されると、焼入性を高めて粗大な粒界フェライトを抑制し、靭性向上に顕著な効果を発揮するため、鋼製外皮中に適正量含有させることは好ましい。前記Ｂの効果を発揮するために鋼製外皮中にＢを含有させる場合は、０．０００２％以上含有させる必要がある。一方、０．００５０％を超えて鋼製外皮中の含有させると、鋼製外皮の素材のインゴットあるいはスラブの鋳造中で高温割れを生じる虞があり、好ましくない。そこで、本発明においては、鋼製外皮中にＢを含有させる場合は、その範囲を０．０００２〜０．００５０％に限定する。
“B: 0.0002 to 0.0050%”
When B is contained in an appropriate amount in the weld metal, it enhances hardenability and suppresses coarse grain boundary ferrite, and exerts a remarkable effect in improving toughness. Is preferred. In order to exhibit the effect of B, when containing B in the steel outer shell, it is necessary to contain 0.0002% or more. On the other hand, if the content exceeds 0.0050% in the steel outer shell, hot cracking may occur during the casting of the steel outer shell ingot or slab, which is not preferable. Therefore, in the present invention, when B is contained in the steel outer shell, the range is limited to 0.0002 to 0.0050%.
また、鋼製外皮には溶接金属のＯ量を低減するために、以下に述べるように、Ｔｉ：０．００５〜０．０５０％、Ｍｇ：０．００２〜０．０１０％、Ｃａ：０．０００２〜０．００５０％、ＲＥＭ：０．０００２〜０．００５０％の１種または２種以上を必要に応じて含有させることができる。 Further, in order to reduce the amount of O of the weld metal in the steel outer shell, as described below, Ti: 0.005 to 0.050%, Mg: 0.002 to 0.010%, Ca: 0.00. One or more of 0002 to 0.0050% and REM: 0.0002 to 0.0050% can be contained as necessary.
「Ｔｉ：０．００５〜０．０５０％」
Ｔｉは本発明が対象とするメタル粉入り溶接ワイヤにおいて、溶接金属のＯ量を低減するために、溶接ワイヤ全体として適正量含有させることが必須の元素である。また、溶接金属中にＴｉを含有する微細な酸化物を均一に分散させるため、これを変態核として微細な粒内変態組織であるアシキュラーフェライトを生成することにより靭性向上に寄与する点でも重要である。その場合、Ｔｉは鋼製外皮中、充填材中のどちらでも、あるいは、両者に含まれていても構わないが、鋼製外皮中に含有させる場合は、その範囲を０．００５％〜０．０５０％に限定する。鋼製外皮中の含有量が０．００５％未満であると、溶接金属のＯ量低減効果や、溶接金属への好ましい効果が明確でないため、鋼製外皮中にＴｉを含有させる場合の下限を０．００５％とする。一方、鋼製外皮中に０．０５０％を超えてＴｉを含有させると、粗大な析出物を形成して溶接ワイヤの製造性を阻害する懸念が大きくなるため、本発明においては、鋼製外皮中にＴｉを含有させる場合の上限を０．０５０％とする。
“Ti: 0.005 to 0.050%”
In the welding wire containing metal powder targeted by the present invention, Ti is an essential element to contain an appropriate amount of the entire welding wire in order to reduce the amount of O of the weld metal. In addition, in order to uniformly disperse fine oxides containing Ti in the weld metal, it is also important to contribute to improving toughness by generating acicular ferrite which is a fine intragranular transformation structure using this as a transformation nucleus It is. In that case, Ti may be contained in the steel outer shell, in the filler, or in both, but when included in the steel outer shell, the range is 0.005% to 0.00%. Limited to 050%. If the content in the steel outer shell is less than 0.005%, the effect of reducing the O content of the weld metal and the preferable effect on the weld metal are not clear, so the lower limit when Ti is contained in the steel outer shell is limited. 0.005%. On the other hand, if Ti exceeds 0.050% in the steel outer shell, there is a greater concern that the coarse precipitates are formed and the productivity of the welding wire is hindered. The upper limit in the case of containing Ti is 0.050%.
「Ｍｇ：０．００２〜０．０１０％」
ＭｇもＴｉと同様、溶接金属中のＯ量低減、組織微細化による靭性向上のために必要である。溶接ワイヤ全体としては含有させることが必須である。鋼製外皮に含有させるかどうかは選択できるが、鋼製外皮中に含有させる場合は、０．００２〜０．０１０％の範囲とする。これは、鋼製外皮中含有量が０．００２％未満であると、前記の溶接金属に対する効果が明確でなく、０．０１０％を超えて鋼製外皮中に含有させることは、工業的に容易でなく、また、含有させた場合には鋼製外皮の延性や靭性を劣化させて溶接ワイヤの製造性劣化を引き起こす可能性があるためである。
“Mg: 0.002 to 0.010%”
Similarly to Ti, Mg is necessary for reducing the amount of O in the weld metal and improving toughness by refining the structure. It is essential to contain the welding wire as a whole. Whether it is contained in the steel outer shell can be selected, but when it is contained in the steel outer shell, it is in the range of 0.002 to 0.010%. This is because if the content in the steel outer shell is less than 0.002%, the effect on the weld metal is not clear, and it is industrially included in the steel outer shell exceeding 0.010%. This is because it is not easy, and if contained, the ductility and toughness of the steel outer sheath may be deteriorated, which may cause deterioration in the manufacturability of the welding wire.
「Ｃａ：０．０００２〜０．００５０％」
ＣａもＭｇと同様の強脱酸元素であるが、ＴｉやＭｇのようにメタル粉入り溶接ワイヤによる溶接金属のＯ量低減効果やアシキュラーフェライト生成による靭性向上効果を示さない。ただし、Ｃａは硫化物を形成して固溶Ｓの有害性を抑制したり、介在物を微細化することで、鋼製外皮の加工性向上や溶接金属の延性向上には有用である。鋼製外皮に含有させて効果を発揮するためには少なくとも０．０００２％必要である。一方、鋼製外皮に０．００５０％を超えて含有させると粗大な介在物を形成して、逆に延性を劣化させ、その結果、溶接ワイヤの製造性を阻害する。そのため、本発明においては、鋼製外皮にＣａを含有させる場合には０．０００２〜０．００５０％の範囲に限定する。
“Ca: 0.0002 to 0.0050%”
Ca is also a strong deoxidizing element similar to Mg, but does not show the effect of reducing the amount of O of weld metal by a metal powder-containing welding wire or the effect of improving toughness by the generation of acicular ferrite, like Ti and Mg. However, Ca is useful for improving the workability of the steel outer shell and improving the ductility of the weld metal by forming sulfides to suppress the harmfulness of the solid solution S or by miniaturizing the inclusions. At least 0.0002% is necessary for the effect to be contained in the steel outer shell. On the other hand, if it is contained in the steel outer shell in an amount exceeding 0.0050%, coarse inclusions are formed, and on the contrary, ductility is deteriorated, and as a result, the manufacturability of the welding wire is hindered. Therefore, in this invention, when making a steel outer shell contain Ca, it limits to 0.0002 to 0.0050% of range.
「ＲＥＭ：０．０００２〜０．００５０％」
ＲＥＭも強脱酸元素であり、Ｃａと同様の作用効果を有する元素であるため、前記Ｃａと同じ理由により、鋼製外皮中に含有させる場合の含有量は０．０００２〜０．００５０％の範囲に限定する。
"REM: 0.0002-0.0050%"
Since REM is also a strong deoxidizing element and is an element having the same effect as Ca, for the same reason as Ca, the content when contained in the steel outer skin is 0.0002 to 0.0050%. Limited to range.
以上が、鋼製外皮の成分組成の限定理由である。 The above is the reason for limiting the component composition of the steel outer shell.
［溶接ワイヤの成分組成］
本発明範囲の成分組成を有する鋼製外皮を用い、メタル粉の充填率を５〜２０％に限定した上で、溶接ワイヤ全体としての成分組成も限定する必要がある。その要件は、溶接ワイヤ全質量に対する質量％で、Ｃ：０．００５〜０．１０％、Ｓｉ：０．１０〜１．５％、Ｍｎ：０．１〜２．５％、Ｐ：０．０２％以下、Ｓ：０．００８％以下、Ａｌ：０．０３０％以下、Ｎ：０．００１〜０．０１０％、Ｔｉ：０．００５〜０．３０％、Ｍｇ：０．０１５〜０．３０％、Ｏ：０．１５％以下、を含有し、かつ、［Ｍｇ］＋［Ｔｉ］／５＝０．０２０〜０．３０％であり、必要に応じて、Ｃｕ：０．０１〜１．５０％、Ｎｉ：０．０１〜６．０％、Ｃｒ：０．０１〜２．０％、Ｍｏ：０．０１〜２．０％、Ｗ：０．０１〜２．０％、Ｎｂ：０．００２〜０．１０％、Ｖ：０．００５〜０．５０％、Ｔａ：０．００５〜０．５０％、Ｚｒ：０．００５〜０．５０％、Ｂ：０．０００２〜０．０１０％、の１種または２種以上を含有し、さらに必要に応じて、Ｃａ：０．０００２〜０．００５０％、ＲＥＭ：０．０００２〜０．００５０％、の１種または２種を含有することにある。
[Composition composition of welding wire]
It is necessary to limit the component composition of the welding wire as a whole after limiting the filling rate of the metal powder to 5 to 20% using a steel outer shell having a component composition within the range of the present invention. The requirements are mass% with respect to the total mass of the welding wire, C: 0.005 to 0.10%, Si: 0.10 to 1.5%, Mn: 0.1 to 2.5%, P: 0.00. 02% or less, S: 0.008% or less, Al: 0.030% or less, N: 0.001-0.010%, Ti: 0.005-0.30%, Mg: 0.015-0. 30%, O: 0.15% or less, and [Mg] + [Ti] /5=0.020 to 0.30%, and if necessary, Cu: 0.01 to 1 .50%, Ni: 0.01 to 6.0%, Cr: 0.01 to 2.0%, Mo: 0.01 to 2.0%, W: 0.01 to 2.0%, Nb: 0.002-0.10%, V: 0.005-0.50%, Ta: 0.005-0.50%, Zr: 0.005-0.50%, B: 0.0002-0. 010% Contain more species or two or, if necessary, Ca: 0.0002~0.0050%, REM: 0.0002~0.0050%, it is to contain one or two.
先ず、必須要件である、Ｃ、Ｓｉ、Ｍｎ、Ｐ、Ｓ、Ａｌ、Ｎ、Ｔｉ、Ｍｇ、Ｏの限定理由を述べる。 First, the reasons for limiting C, Si, Mn, P, S, Al, N, Ti, Mg, and O, which are essential requirements, will be described.
「Ｃ ：０．００５〜０．１０％」
溶接ワイヤのＣは、溶接金属の強度を向上させるために必要な成分であり、建築用途に用いられる引張強さが４００〜７８０ＭＰａ級まで溶接金属の強度を確保しようとすると、溶接ワイヤ中には０．００５％以上含有する必要がある。しかしながら、溶接ワイヤ中のＣが０．１０％を超えて含有されると、溶接金属中のＣ量も過大となり、溶接金属の靭性を劣化させるため、好ましくない。従って、本発明においては溶接ワイヤ中のＣ量は０．００５〜０．１０％に限定する。なお、溶接金属の靭性は溶接金属中のＣ量に強く影響されるため、強度を達成できる範囲で少ない方が好ましい。例えば、引張強さ４９０ＭＰａ級で、０℃におけるシャルピー衝撃試験の吸収エネルギーが１００Ｊ以上の高靱性を得ようとする場合には、溶接ワイヤのＣ含有量の上限を０．０３％未満に制限することがより好ましい。
"C: 0.005-0.10%"
C of the welding wire is a component necessary for improving the strength of the weld metal, and when the tensile strength used for building applications is to secure the weld metal strength to 400 to 780 MPa class, It is necessary to contain 0.005% or more. However, if the content of C in the welding wire exceeds 0.10%, the amount of C in the weld metal becomes excessive and the toughness of the weld metal is deteriorated. Therefore, in the present invention, the amount of C in the welding wire is limited to 0.005 to 0.10%. In addition, since the toughness of the weld metal is strongly influenced by the amount of C in the weld metal, it is preferable that the toughness is as small as possible in the range where the strength can be achieved. For example, when the tensile strength is 490 MPa class and the absorbed energy of the Charpy impact test at 0 ° C. is to obtain high toughness of 100 J or more, the upper limit of the C content of the welding wire is limited to less than 0.03%. It is more preferable.
「Ｓｉ：０．１０〜１．５％」
Ｓｉは脱酸元素として、溶接金属中のＯ量を低減するために必須の元素である。溶接金属中に含有されれば、固溶強化により強度向上にも有効である。効果を発揮するためには、溶接ワイヤに０．１０％以上含有させる必要がある。一方、溶接ワイヤ中の含有量が１．５％を超えると、溶接金属中の含有量が増加して靭性を劣化させ、また、溶接中のスラグ量を若干ながら増加させて、溶接作業性を劣化させる可能性があるため、好ましくない。そのため、本発明においては、溶接ワイヤのＳｉ含有量を０．１０〜１．５％に限定する。
“Si: 0.10 to 1.5%”
Si is an essential element for reducing the amount of O in the weld metal as a deoxidizing element. If contained in the weld metal, it is also effective for improving the strength by solid solution strengthening. In order to exert the effect, it is necessary to contain 0.10% or more in the welding wire. On the other hand, if the content in the welding wire exceeds 1.5%, the content in the weld metal increases and the toughness is deteriorated, and the slag amount during welding is slightly increased to improve welding workability. Since it may deteriorate, it is not preferable. Therefore, in this invention, Si content of a welding wire is limited to 0.10 to 1.5%.
「Ｍｎ：０．１〜２．５％」
溶接ワイヤのＭｎは、溶接金属の強度の向上及び脱酸作用を有するが、溶接ワイヤ中の含有量が０．１％を下回ると、十分な脱酸作用と溶接金属の十分な強度が得られず、また、溶接金属の酸素量が高くなるためと、溶接金属の組織粗大化により溶接金属の靭性を劣化させる。そのため、ワイヤ中の含有量の下限を０．１％とする。一方ワイヤ中のＭｎ含有量が２．５％を超えると、溶接金属組織が粗大なベイナイト組織となって靭性が劣化する可能性が高くなるため、本発明においては、溶接ワイヤ中のＭｎ含有量の上限を２．５％とする。なお、溶接ワイヤ中のＭｎ量が多くなると、溶接中にスラグが増加する方向であるため、溶接中にスパッタが増加して、そのために溶接作業性を阻害する可能性がないとは言えない。溶接作業性を重視するのであれば、溶接ワイヤ中のＭｎ含有量は１．５％未満に制限するのがとり好ましい。
“Mn: 0.1 to 2.5%”
Mn of the welding wire has an improvement in the strength of the weld metal and a deoxidizing action. However, if the content in the welding wire is less than 0.1%, a sufficient deoxidizing action and a sufficient strength of the welding metal can be obtained. In addition, the oxygen content of the weld metal is increased, and the toughness of the weld metal is deteriorated due to the coarsening of the structure of the weld metal. Therefore, the lower limit of the content in the wire is 0.1%. On the other hand, if the Mn content in the wire exceeds 2.5%, the weld metal structure becomes a coarse bainite structure and the toughness is likely to deteriorate. Therefore, in the present invention, the Mn content in the welding wire Is set to 2.5%. Note that when the amount of Mn in the welding wire increases, the slag increases in the direction of welding. Therefore, it cannot be said that there is a possibility that spatter increases during welding and that the workability of welding is not hindered. If importance is placed on welding workability, the Mn content in the welding wire is preferably limited to less than 1.5%.
「Ｐ ：０．０２％以下」
Ｐは靭性、耐割れ性等を低下させる不純物元素であり、溶接ワイヤ全体としての含有量も少ない方が好ましい。ただし、溶接ワイヤ中の含有量が０．０２％以下であれば、溶接金属の特性に対する悪影響の程度が許容できる範囲であるため、本発明においては、溶接ワイヤ中のＰ含有量は０．０２％以下とする。
“P: 0.02% or less”
P is an impurity element that lowers toughness, crack resistance, etc., and it is preferable that the content of the entire welding wire is small. However, if the content in the welding wire is 0.02% or less, the adverse effect on the properties of the weld metal is within an acceptable range. Therefore, in the present invention, the P content in the welding wire is 0.02%. % Or less.
「Ｓ ：０．００８％以下」
Ｓも靭性、延性等を低下させる不純物元素であり、溶接ワイヤ全体としての含有量も少ない方が好ましい。ただし、溶接ワイヤ中の含有量が０．００８％以下であれば、溶接金属の特性に対する悪影響の程度が許容できる範囲であるため、本発明においては、溶接ワイヤ中のＳ含有量は０．０２％以下とする。
“S: 0.008% or less”
S is also an impurity element that lowers toughness, ductility and the like, and it is preferable that the content of the entire welding wire is small. However, if the content in the welding wire is 0.008% or less, the adverse effect on the properties of the weld metal is within an acceptable range. Therefore, in the present invention, the S content in the welding wire is 0.02%. % Or less.
「Ａｌ：０．０３０％以下」
Ａｌは溶接金属中のＯ量を高めて溶接金属の延性や靭性を劣化させ、かつ、溶接中のスラグを増やして、スパッタの発生等、溶接作業性を損なうため、本発明においては溶接ワイヤ中のＡｌ量は少ない方が好ましい。溶接ワイヤ中のＡｌ含有量が０．０３０％以下であれば、材質や作業性の劣化が許容できるため、本発明においては、溶接ワイヤ中のＡｌ含有量は０．０３０％以下とする。ただし、より確実にＡｌの悪影響を抑制するためには、溶接ワイヤ中のＡｌ含有量は０．０１０％未満とすることがより好ましい。
“Al: 0.030% or less”
Al increases the amount of O in the weld metal to deteriorate the ductility and toughness of the weld metal, and increases the slag during welding to impair welding workability such as spatter generation. It is preferable that the amount of Al is small. If the Al content in the welding wire is 0.030% or less, deterioration of the material and workability is acceptable. Therefore, in the present invention, the Al content in the welding wire is 0.030% or less. However, in order to suppress the adverse effect of Al more reliably, the Al content in the welding wire is more preferably less than 0.010%.
「Ｎ ：０．００１〜０．０１０％」
溶接金属中のＮは微量であれば、ＡｌやＴｉと窒化物を形成して、組織の微細化を通して、溶接金属の機械的性質を向上する効果を有する。溶接ワイヤ中のＮ含有量が０．００１％未満であると溶接金属の特性向上効果が明確でないことと、工業的に鋼中にＮ量を０．００１％未満とすることが容易でないことから、本発明においては、溶接ワイヤ中のＮ含有量の下限を０．００１％とする。一方、溶接金属中にＮを過剰に含有すると、溶接金属の靭性を顕著に劣化させる。溶接ワイヤ中のＮ含有量が０．０１０％未満であれば、溶接金属に対するＮの悪影響が許容範囲内であることから、溶接ワイヤ中のＮ量の上限を０．０１０％とする。
“N: 0.001 to 0.010%”
If the amount of N in the weld metal is small, it has the effect of improving the mechanical properties of the weld metal by forming Al and Ti and nitrides and refining the structure. If the N content in the welding wire is less than 0.001%, the effect of improving the properties of the weld metal is not clear, and it is not easy to industrially make the N content in the steel less than 0.001%. In the present invention, the lower limit of the N content in the welding wire is 0.001%. On the other hand, when N is contained excessively in the weld metal, the toughness of the weld metal is remarkably deteriorated. If the N content in the welding wire is less than 0.010%, the adverse effect of N on the weld metal is within the allowable range, so the upper limit of the N amount in the welding wire is 0.010%.
「Ｔｉ：０．００５〜０．３０％」
Ｔｉは、本発明が対象とするメタル粉入り溶接ワイヤにおいて、溶接金属のＯ量を低減するために、溶接ワイヤ全体として適正量含有させることが必須の元素である。また、溶接金属中にＴｉを含有する微細な酸化物を均一に分散させるため、これを変態核として微細な粒内変態組織であるアシキュラーフェライトを生成することにより靭性向上に寄与する点でも重要である。溶接ワイヤ中の含有量が０．００５％未満であると、溶接金属のＯ量低減効果や、溶接金属の靭性向上効果が明確でないため、下限を０．００５％とする。一方、溶接ワイヤ中に０．３０％を超えてＴｉを含有させると、溶接金属中に粗大な析出物を形成して溶接金属の靭性を劣化させるため、本発明においては、溶接ワイヤ中のＴｉ含有量の上限を０．３０％とする。
“Ti: 0.005 to 0.30%”
In the welding wire containing metal powder targeted by the present invention, Ti is an element that is essential to contain an appropriate amount as a whole welding wire in order to reduce the amount of O of the welding metal. In addition, in order to uniformly disperse fine oxides containing Ti in the weld metal, it is also important to contribute to improving toughness by generating acicular ferrite which is a fine intragranular transformation structure using this as a transformation nucleus It is. If the content in the welding wire is less than 0.005%, the effect of reducing the O content of the weld metal and the effect of improving the toughness of the weld metal are not clear, so the lower limit is made 0.005%. On the other hand, if Ti is contained in the welding wire in an amount exceeding 0.30%, coarse precipitates are formed in the weld metal to deteriorate the toughness of the weld metal. The upper limit of the content is 0.30%.
「Ｍｇ：０．０１５〜０．３０％」
Ｍｇも、本発明が対象とするメタル粉入り溶接ワイヤにおいて、溶接金属のＯ量を低減するために、溶接ワイヤ全体として適正量含有させることが必須の元素である。また、Ｔｉと同じ効果により組織微細化により靭性を向上させる。溶接ワイヤ中の含有量が０．０１５％未満であると、溶接金属のＯ量低減効果、靭性向上効果が明確でないため、下限を０．０１５％とする。特に、溶接金属中の酸化物微細化とそれによるの組織微細化を通した靭性向上効果は、Ｍｇが０．０１４％以下の微量ではほとんど効果が発揮されない。一方、溶接ワイヤ中に０．３０％を超えてＭｇを含有させると、溶接金属中のＭｇ量が過大となって、溶接金属の靭性を劣化させるため、本発明においては、溶接ワイヤ中のＭｇ含有量の上限を０．３０％とする。なお、Ｍｇによる溶接金属のＯ量低減効果、靭性向上効果をより確実に発揮するためには、溶接ワイヤ中のＭｇ含有量は０．０３０％以上とすることがより好ましい。
“Mg: 0.015 to 0.30%”
Mg is also an essential element in the welding wire containing metal powder which is the subject of the present invention, in order to reduce the amount of O of the weld metal in an appropriate amount as a whole welding wire. Moreover, toughness is improved by refinement of the structure by the same effect as Ti. If the content in the welding wire is less than 0.015%, the effect of reducing the amount of O of weld metal and the effect of improving toughness are not clear, so the lower limit is made 0.015%. In particular, the effect of improving the toughness through the refinement of oxide in the weld metal and the resulting refinement of the structure is hardly exhibited when Mg is 0.014% or less. On the other hand, if Mg exceeds 0.30% in the welding wire, the amount of Mg in the weld metal becomes excessive and deteriorates the toughness of the weld metal. The upper limit of the content is 0.30%. In order to more reliably exhibit the effect of reducing the amount of O of weld metal and improving the toughness due to Mg, the Mg content in the welding wire is more preferably 0.030% or more.
「Ｍｇ＋Ｔｉ／５＝０．０２０〜０．３０％」
メタル粉入り溶接ワイヤにより溶接するに際して溶接金属中のＯ量をソリッドワイヤなみとするためには、前記のように、溶接ワイヤ中のＡｌを制限した上で、Ｔｉ、Ｍｇ各々を適正範囲内で含有させるが、Ｔｉ、ＭｇによるＯ低減効果を確実にするためには、ＭｇとＴｉの合計量をＭｇ＋Ｔｉ／５＝０．０２０〜０．３０％とする必要がある。Ｍｇ＋Ｔｉ／５が０．０２０％未満であると、各々の含有量が本発明範囲内であっても、溶接ワイヤの成分組成や溶接条件によっては溶接金属中のＯ量が過大となる虞がある。また、アシキュラーフェライトの生成核となる酸化物の個数が十分でなく、靭性が劣る可能性も生じる。一方、Ｍｇ＋Ｔｉ／５が０．３０％超であると、粗大な酸化物の形成やＴｉの析出脆化により、溶接金属の靭性劣化が著しくなる虞が大きくなる。そのため、本発明においては、溶接ワイヤのＴｉ、Ｍｇの含有量を、Ｍｇ＋Ｔｉ／５で０．００２〜０．３０％に制限する。
“Mg + Ti / 5 = 0.020-0.30%”
In order to make the amount of O in the weld metal equal to that of a solid wire when welding with a metal powder-containing welding wire, as described above, after limiting Al in the welding wire, within a proper range of Ti and Mg, respectively. In order to ensure the effect of reducing O by Ti and Mg, the total amount of Mg and Ti needs to be Mg + Ti / 5 = 0.020 to 0.30%. If Mg + Ti / 5 is less than 0.020%, even if the respective contents are within the range of the present invention, the amount of O in the weld metal may be excessive depending on the composition of the welding wire and the welding conditions. . In addition, there is a possibility that the number of oxides serving as nuclei of acicular ferrite is not sufficient and the toughness is inferior. On the other hand, when Mg + Ti / 5 is more than 0.30%, there is a high possibility that the toughness deterioration of the weld metal becomes remarkable due to the formation of coarse oxides and precipitation embrittlement of Ti. Therefore, in the present invention, the content of Ti and Mg in the welding wire is limited to 0.002 to 0.30% with Mg + Ti / 5.
「Ｏ ：０．１５％以下」
Ｏは不純物元素であり、鋼の延性を低下させたり、加工性を阻害するため、極力低減することが好ましい。溶接ワイヤ中のＯ量が０．０１５％超であると、溶接金属のＯ量を高めて延性や靭性劣化を生じるため、好ましくない。そのため、本発明においては、溶接ワイヤ全体としてはＯ含有量を０．０１５％以下に制限する。
“O: 0.15% or less”
O is an impurity element and is preferably reduced as much as possible in order to reduce the ductility of the steel or impair the workability. If the amount of O in the welding wire is more than 0.015%, the amount of O of the weld metal is increased and ductility and toughness are deteriorated. Therefore, in this invention, O content is restrict | limited to 0.015% or less as the whole welding wire.
以上が、溶接ワイヤの成分組成のうち、必須要件である、Ｃ、Ｓｉ、Ｍｎ、Ｐ、Ｓ、Ａｌ、Ｎ、Ｔｉ、Ｍｇ、Ｏの限定理由である。本発明においては、溶接金属の強度・靭性の調整のために、選択的に元素を用いることが可能であり、該選択元素を溶接ワイヤに必要に応じて含有させることができる。ただし、選択的に用いる場合でも、種々理由によりその含有量は限定することが必要である。以下に、溶接ワイヤに含有させる選択元素の限定理由を述べる。 The above is the reason for limiting C, Si, Mn, P, S, Al, N, Ti, Mg, and O, which are essential requirements, among the component compositions of the welding wire. In the present invention, an element can be selectively used for adjusting the strength and toughness of the weld metal, and the selected element can be contained in the welding wire as necessary. However, even when it is selectively used, its content needs to be limited for various reasons. The reasons for limiting the selection elements to be included in the welding wire will be described below.
「Ｃｕ：０．０１〜１．５０％」
溶接ワイヤ中にＣｕを含有させる場合は、その範囲は０．０１〜１．５０％とする。Ｃｕは、溶接金属の強度向上に有効な元素である。本発明においても、必要に応じて溶接ワイヤ中にＣｕを含有させることが可能である。溶接金属におけるＣｕの効果を明確に発揮するためには、Ｃｕは溶接ワイヤ全質量に対する質量％で０．０１％以上含有させる必要がある。一方、溶接ワイヤに１．５０％を超えて含有させると、溶接金属の含有量が過剰となって、溶接金属の靭性や耐高温割れ性を劣化させる虞があるため、本発明においては、溶接ワイヤ中にＣｕを含有させる場合、溶接ワイヤ全質量に対する質量％で０．０１〜１．５０％に限定する。なお、溶接ワイヤ表面にＣｕめっきを施す場合、本発明においては、Ｃｕめっき分も溶接ワイヤのＣｕ含有量に含む。
“Cu: 0.01 to 1.50%”
When Cu is contained in the welding wire, the range is 0.01 to 1.50%. Cu is an element effective for improving the strength of the weld metal. Also in this invention, it is possible to contain Cu in a welding wire as needed. In order to clearly exhibit the effect of Cu in the weld metal, it is necessary to contain Cu by 0.01% or more by mass% with respect to the total mass of the welding wire. On the other hand, if the welding wire contains more than 1.50%, the content of the weld metal becomes excessive, which may deteriorate the toughness and hot cracking resistance of the weld metal. When Cu is contained in the wire, the content is limited to 0.01 to 1.50% by mass% with respect to the total mass of the welding wire. When Cu plating is performed on the surface of the welding wire, in the present invention, the Cu plating content is also included in the Cu content of the welding wire.
「Ｎｉ：０．０１〜６．０％」
Ｎｉは、一般的に鋼の靭性向上に極めて有効な元素であるため、本発明においても、溶接金属の靭性向上のために、必要に応じて溶接ワイヤ中にＮｉを含有させることが可能である。その場合、Ｎｉによる高靭化効果を明確に享受するためには、溶接ワイヤ中に０．０１％以上含有させる必要がある。一方、溶接ワイヤ中に６．０％を超えて含有させることは、効果が飽和する一方で、溶接ワイヤの製造コストを過度に高めるため、好ましくない。そのため、溶接ワイヤにＮｉを含有させる場合は、溶接ワイヤ全質量に対する質量％で０．０１〜６．０％に限定する。
"Ni: 0.01-6.0%"
Since Ni is an element that is generally extremely effective for improving the toughness of steel, in the present invention, it is possible to contain Ni in the welding wire as necessary in order to improve the toughness of the weld metal. . In that case, in order to enjoy the toughening effect by Ni clearly, it is necessary to make it contain 0.01% or more in a welding wire. On the other hand, containing more than 6.0% in the welding wire is not preferable because the effect is saturated, but the manufacturing cost of the welding wire is excessively increased. Therefore, when making a welding wire contain Ni, it limits to 0.01-6.0% by the mass% with respect to the total mass of a welding wire.
「Ｃｒ：０．０１〜２．０％」
Ｃｒは強度を高めるのに有効な元素であるため、必要に応じて溶接ワイヤ中に含有させることができる。溶接金属の高強度化に用いる場合は、溶接ワイヤ中の含有量が０．０１％未満であると効果が明確でないため、溶接ワイヤ中にＣｒを含有させる場合は、含有量の下限を０．０１％とする必要がある。一方、溶接ワイヤ中の含有量が２．０％を超えると、溶接金属に粗大なベイナイトや硬質相を生成して溶接金属の靭性を劣化させる虞があるため、好ましくない。そこで、本発明においては、溶接ワイヤ中にＣｒを含有させる場合は、溶接ワイヤ全質量に対する質量％で０．０１〜２．０％に限定する。
"Cr: 0.01-2.0%"
Since Cr is an effective element for increasing the strength, it can be contained in the welding wire as necessary. When it is used for increasing the strength of the weld metal, the effect is not clear if the content in the welding wire is less than 0.01%. Therefore, when Cr is contained in the welding wire, the lower limit of the content is set to 0. It needs to be 01%. On the other hand, if the content in the welding wire exceeds 2.0%, coarse bainite or a hard phase may be generated in the weld metal to deteriorate the toughness of the weld metal, which is not preferable. Therefore, in the present invention, when Cr is contained in the welding wire, it is limited to 0.01 to 2.0% by mass% with respect to the total mass of the welding wire.
「Ｍｏ：０．０１〜２．０％」
Ｍｏは、焼入性を高めて溶接金属組織のベイナイトあるいはアシキュラーフェライトの微細化を通して靱性向上に有効な元素であり、かつ、固溶強化、析出強化により強度向上にも有効な元素である。この効果を得るために溶接ワイヤにＭｏを含有させる場合は、０．０１％以上含有させる必要がある。溶接ワイヤ中のＭｏ含有量が０．０１％未満では溶接金属の強度向上効果が明確でない。一方、２．０％を超えて溶接ワイヤに過剰に含有されると、溶接金属中のＭｏ含有量が過大となって、溶接金属の靭性が著しく劣化する可能性が大きくなるため、本発明において、溶接ワイヤにＭｏを含有させる場合、その上限は２．０％に制限する。
"Mo: 0.01-2.0%"
Mo is an element effective for improving toughness by increasing hardenability and making bainite or acicular ferrite fine in the weld metal structure, and is also effective for improving strength by solid solution strengthening and precipitation strengthening. In order to acquire this effect, when making Mo contain in a welding wire, it is necessary to make it contain 0.01% or more. If the Mo content in the welding wire is less than 0.01%, the effect of improving the strength of the weld metal is not clear. On the other hand, if it exceeds 2.0% and is excessively contained in the welding wire, the Mo content in the weld metal becomes excessive, and the possibility that the toughness of the weld metal deteriorates significantly increases. When Mo is contained in the welding wire, the upper limit is limited to 2.0%.
「Ｗ ：０．０１〜２．０％」
Ｗは溶接金属の機械的性質に対して、焼入性を高めて溶接金属組織のベイナイトあるいはアシキュラーフェライトの微細化を通して靱性向上に有効な元素であり、かつ、固溶強化、析出強化により強度向上にも有効なＭｏとほぼ同一の効果を有するため、Ｍｏと同じ理由により、溶接ワイヤ中にＷを含有させる場合は、溶接ワイヤ全質量に対する質量％で０．０１〜２．０％に限定する。
"W: 0.01-2.0%"
W is an element effective for improving the toughness by increasing the hardenability and making the weld metal microstructure bainite or acicular ferrite finer with respect to the mechanical properties of the weld metal. Since it has almost the same effect as Mo which is effective for improvement, when W is contained in the welding wire for the same reason as Mo, it is limited to 0.01 to 2.0% by mass% with respect to the total mass of the welding wire. To do.
「Ｎｂ：０．００２〜０．１０％」
Ｎｂは、溶接金属中に含有されると、焼入性向上効果、析出強化によって、溶接金属の強度向上に有効である。溶接ワイヤにＮｂを含有させる場合、この効果を確実に発揮するためには、溶接ワイヤ中のＮｂ含有量は０．００２％以上とする必要がある。一方、溶接ワイヤ中のＮｂ量が０．１０％を超えると、溶接金属中のＮｂ量が過大となって、溶接金属に粗大なＮｂ析出物が形成されるために、溶接金属の靭性劣化が著しくなる可能性もあるため、好ましくない。以上の理由により、本発明においては、溶接ワイヤ中にＮｂを含有させる場合、Ｎｂ含有量の範囲を０．００２〜０．１０％に限定する。
“Nb: 0.002 to 0.10%”
When Nb is contained in the weld metal, it is effective in improving the strength of the weld metal due to the effect of improving hardenability and precipitation strengthening. When Nb is contained in the welding wire, the Nb content in the welding wire needs to be 0.002% or more in order to reliably exhibit this effect. On the other hand, if the Nb amount in the welding wire exceeds 0.10%, the Nb amount in the weld metal becomes excessive, and coarse Nb precipitates are formed on the weld metal. Since it may become remarkable, it is not preferable. For the above reasons, in the present invention, when Nb is contained in the welding wire, the range of Nb content is limited to 0.002 to 0.10%.
「Ｖ ：０．００５〜０．５０％」
Ｖは、溶接金属中に含有されると、主として析出強化によって、溶接金属の強度向上に有効である。溶接ワイヤにＶを含有させる場合、この効果を確実に発揮するためには、溶接ワイヤ中のＶ含有量は０．００５％以上とする必要がある。一方、溶接ワイヤのＶ含有量が０．５０％を超えて過大になると、Ｎｂと同様の理由により、溶接金属の靭性劣化の可能性が無視できなくなるため、好ましくない。そのため、本発明においては、溶接ワイヤ中にＶを含有させる場合、Ｖ含有量の範囲を０．００５〜０．５０％に限定する。
“V: 0.005 to 0.50%”
When V is contained in the weld metal, it is effective for improving the strength of the weld metal mainly by precipitation strengthening. When V is contained in the welding wire, the V content in the welding wire needs to be 0.005% or more in order to reliably exhibit this effect. On the other hand, if the V content of the welding wire exceeds 0.50%, the possibility of deterioration of the toughness of the weld metal cannot be ignored for the same reason as Nb, which is not preferable. Therefore, in this invention, when containing V in a welding wire, the range of V content is limited to 0.005-0.50%.
「Ｔａ：０．００５〜０．５０％」
Ｔａは溶接金属の機械的性質に対して、Ｖとほぼ同一主として析出強化によって、溶接金属の強度向上に有効な効果を有するため、Ｖと同じ理由により、溶接ワイヤ中にＴａを含有させる場合は、溶接ワイヤ全質量に対する質量％で０．００５〜０．５０％に限定する。
"Ta: 0.005-0.50%"
Ta has almost the same effect as V on the mechanical properties of the weld metal, mainly by precipitation strengthening, and has an effective effect on improving the strength of the weld metal. For the same reason as V, when Ta is contained in the weld wire, The mass% is limited to 0.005 to 0.50% with respect to the total mass of the welding wire.
「Ｚｒ：０．００５〜０．５０％」
Ｚｒも溶接金属の機械的性質に対して、ＶやＴａとほぼ同一の主として析出強化によって、溶接金属の強度向上に有効な効果を有するため、ＶやＴａと同じ理由により、溶接ワイヤ中にＺｒを含有させる場合は、溶接ワイヤ全質量に対する質量％で０．００５〜０．５０％に限定する。
"Zr: 0.005-0.50%"
Zr also has an effective effect on improving the strength of the weld metal mainly by precipitation strengthening, which is almost the same as V and Ta, with respect to the mechanical properties of the weld metal. For the same reason as V and Ta, Zr is contained in the weld wire. Is contained, it is limited to 0.005 to 0.50% by mass% with respect to the total mass of the welding wire.
「Ｂ ：０．０００２〜０．０１０％」
Ｂは、溶接金属中に適正量含有されると、焼入性を高めて粗大な粒界フェライトを抑制し、靭性向上に顕著な効果を発揮するため、溶接ワイヤ中に適正量含有させることは好ましい。前記Ｂの効果を発揮するために溶接ワイヤ中にＢを含有させる場合は、０．０００２％以上含有させる必要がある。一方、０．０１０％を超えて溶接ワイヤ中に含有させると、溶接金属中のＢ含有量も過大となり、焼入性が過大となって、粗大なベイナイトや硬質のマルテンサイト相が生成して靭性を劣化させる虞があるため、好ましくない。そこで、本発明においては、溶接ワイヤ中にＢを含有させる場合は、その範囲を０．０００２〜０．０１０％に限定する。
“B: 0.0002 to 0.010%”
When B is contained in an appropriate amount in the weld metal, it enhances hardenability and suppresses coarse grain boundary ferrite, and exerts a remarkable effect in improving toughness. preferable. In order to exhibit the effect of B, when containing B in the welding wire, it is necessary to contain 0.0002% or more. On the other hand, if the content exceeds 0.010% in the welding wire, the B content in the weld metal becomes excessive, the hardenability becomes excessive, and coarse bainite or hard martensite phase is generated. Since there is a possibility that the toughness is deteriorated, it is not preferable. Therefore, in the present invention, when B is contained in the welding wire, the range is limited to 0.0002 to 0.010%.
また、Ｃａ：０．０００２〜０．００５０％、ＲＥＭ：０．０００２〜０．００５０％、の１種または２種を必要に応じて含有させることができる。 Moreover, 1 type or 2 types of Ca: 0.0002-0.0050% and REM: 0.0002-0.0050% can be contained as needed.
「Ｃａ：０．０００２〜０．００５０％」
ＣａはＭｇと同様の強脱酸元素であるが、ＴｉやＭｇのようにメタル粉入り溶接ワイヤによる溶接金属のＯ量低減効果やアシキュラーフェライト生成による靭性向上効果を示さない。ただし、Ｃａは硫化物を形成して固溶Ｓの有害性を抑制したり、介在物を微細化することで、鋼製外皮の加工性向上や溶接金属の延性向上には有用である。溶接ワイヤに含有させて効果を発揮するためには少なくとも０．０００２％必要である。一方、溶接ワイヤに０．００５０％を超えて含有させると溶接金属中に粗大な介在物を形成して、溶接金属の延性や靭性を劣化させる虞がある。そのため、本発明においては、鋼製外皮にＣａを含有させる場合には、その溶接ワイヤ中の含有量は０．０００２〜０．００５０％の範囲に限定する。
“Ca: 0.0002 to 0.0050%”
Although Ca is a strong deoxidizing element similar to Mg, it does not show the effect of reducing the amount of O of weld metal by a metal powder-containing welding wire or the effect of improving toughness by the generation of acicular ferrite like Ti and Mg. However, Ca is useful for improving the workability of the steel outer shell and improving the ductility of the weld metal by forming sulfides to suppress the harmfulness of the solid solution S or by miniaturizing the inclusions. At least 0.0002% is necessary for the effect to be contained in the welding wire. On the other hand, if the content exceeds 0.0050% in the welding wire, coarse inclusions are formed in the weld metal, which may deteriorate the ductility and toughness of the weld metal. Therefore, in the present invention, when Ca is contained in the steel outer sheath, the content in the welding wire is limited to a range of 0.0002 to 0.0050%.
「ＲＥＭ：０．０００２〜０．００５０％」
ＲＥＭもＣａと同様の強脱酸元素であり、硫化物を形成して固溶Ｓの有害性を抑制したり、介在物を微細化することで、鋼製外皮の加工性向上や溶接金属の延性向上には有用であるため、前記Ｃａと同じ理由により、溶接ワイヤ中に含有させる場合の含有量は０．０００２〜０．００５０％の範囲に限定する。
"REM: 0.0002-0.0050%"
REM is also a strong deoxidizing element similar to Ca. It suppresses the harmful effects of solute S by forming sulfides and refines inclusions to improve the workability of steel outer shells and weld metals. Since it is useful for improving ductility, for the same reason as Ca, the content when contained in the welding wire is limited to a range of 0.0002 to 0.0050%.
［メタル粉の充填率］
以上が本発明のメタル粉入り溶接ワイヤにおける、鋼製外皮ならびに溶接ワイヤ全体としての成分組成の限定理由である。なお、鋼製外皮と溶接ワイヤの成分組成が本発明範囲内であっても、下記の理由により、メタル粉の充填率も限定する必要がある。すなわち、メタル粉の質量％が５％未満であると、溶接ワイヤの成分組成の変化が限定されるため、溶接ワイヤの成分組成の調整が容易に行えるとのメタル粉入り溶接ワイヤの大きな利点の一つが著しく制限されるため、本発明においては、メタル粉の充填率の下限を５％とする。一方、メタル粉の充填率が２０％を超えると、溶接ワイヤの成分組成が本発明の範囲内であっても、溶接ワイヤの伸線加工中の断線率が無視できない程度に高くなるため、また、溶接中のスラグの増加が多く、溶接作業性を阻害する可能性が高くなるため、本発明においては、メタル粉の充填率の上限を２０％とする。なお、本発明においては、メタル粉の充填率は、溶接ワイヤ全質量に対するメタル粉の質量％で表す。
[Metal powder filling rate]
The above is the reason for limiting the component composition of the steel outer sheath and the entire welding wire in the welding wire containing metal powder of the present invention. In addition, even if the component composition of the steel outer sheath and the welding wire is within the range of the present invention, it is necessary to limit the filling rate of the metal powder for the following reason. That is, when the mass% of the metal powder is less than 5%, since the change in the composition of the welding wire is limited, the great advantage of the welding wire containing metal powder that the adjustment of the composition of the welding wire can be easily performed. Since one is remarkably restricted, the lower limit of the filling rate of the metal powder is set to 5% in the present invention. On the other hand, if the filling rate of the metal powder exceeds 20%, even if the component composition of the welding wire is within the range of the present invention, the disconnection rate during wire drawing of the welding wire becomes so high that it cannot be ignored. In the present invention, the upper limit of the metal powder filling rate is set to 20% because there is a large increase in slag during welding and the possibility of hindering welding workability is increased. In the present invention, the filling rate of the metal powder is represented by mass% of the metal powder with respect to the total mass of the welding wire.
以下、本発明に係るメタル粉入りエレクトロスラグ溶接用溶接ワイヤについての実施例を挙げ、本発明をより具体的に説明するが、本発明は、もとより下記実施例に限定されるものではなく、前、後記の趣旨に適合し得る範囲で適当に変更を加えて実施することも可能であり、それらはいずれも本発明の技術的範囲に含まれるものである。 Hereinafter, examples of the welding wire for electroslag welding containing metal powder according to the present invention will be given and the present invention will be described more specifically. However, the present invention is not limited to the following examples, It is also possible to carry out the present invention with appropriate modifications within a range that can be adapted to the gist described below, and these are all included in the technical scope of the present invention.
実施例には、種々の化学組成のメタル粉入り溶接ワイヤ、鋼板を用い、高層建築構造物の柱によく用いられる、スキンプレートとダイヤフラムとからなる４面ボックス柱を模した、図２に示すような鋼板（スキンプレート）１と鋼板（ダイや不ラム）２とを開先幅ａにて対向させ、裏当金３を排泄させたＴ字継手により溶接継手を作製し、図３に示す位置から引張試験片５および２ｍｍＶノッチシャルピー衝撃試験片６を採取して、開先中央の溶接金属の強度、靱性を調べた。強度は室温の丸棒引張試験により評価し、靭性は２ｍｍＶノッチシャルピー衝撃試験の０℃における吸収エネルギーで評価した。また、溶接中状況を目視観察し、スパッタの多少により、溶接作業性を比較した。
In the examples, welding wires and steel plates containing metal powders of various chemical compositions are used, and a four-sided box column composed of a skin plate and a diaphragm, which is often used as a column of a high-rise building structure, is shown in FIG. Such a steel plate (skin plate) 1 and a steel plate (die or non-ram) 2 are opposed to each other with a groove width a, and a welded joint is produced by a T-shaped joint from which the
表１に鋼板の化学組成を示す。種々組成、製造方法による板厚５０ｍｍあるいは６０ｍｍの鋼板を用いた。一つの溶接継手においては、ダイヤフラム相当鋼板とスキンプレート相当鋼板とには同一の鋼板を用いた。鋼板素組成については、その組成に合わせて本願発明の溶接ワイヤの組成を適宜調整することで溶接金属の特性を確保することが可能であるため、鋼板組成により本願発明の効果が損なわれることはない。ただし、エレクトロスラグ溶接は母材希釈が比較的大きいため、鋼板組成も一定範囲内に限定することが好ましい。具体的には、Ｃ：０．０３〜０．１５％、Ｓｉ：１．０％以下、Ｍｎ：０．１〜２．５％、Ｐ：０．０２％以下、Ｓ：０．００８％以下、Ａｌ：０．０７％以下、Ｎ：０．０１０％以下、を含有し、炭素当量：０．２５〜０．６０％の範囲内で必要に応じてＮｉ、Ｃｒ、Ｍｏ、Ｖの１種または２種以上含有し、さらに必要に応じて、Ｃｕ：０．０１〜１．５％、Ｔｉ：０／００２〜０．０５％、Ｎｂ：０．００２〜０．１０％、Ｂ：０．０００２〜０．０２０％、Ｃａ：０．０００２〜０．０２０％の１種または２種以上を含有する鋼板組成とすることがより好ましい。ただし、炭素当量（Ｃｅｑ．）は、Ｃｅｑ．＝Ｃ（質量％）＋Ｓｉ（質量％）／２４＋Ｍｎ（質量％）／６＋Ｎｉ（質量％）／４０＋Ｃｒ（質量％）／５＋Ｍｏ（質量％）／４＋Ｖ（質量％）／１４、の式により求めた値である。 Table 1 shows the chemical composition of the steel sheet. Steel plates having a thickness of 50 mm or 60 mm according to various compositions and manufacturing methods were used. In one welded joint, the same steel plate was used as the diaphragm equivalent steel plate and the skin plate equivalent steel plate. About the steel plate element composition, it is possible to ensure the characteristics of the weld metal by appropriately adjusting the composition of the welding wire of the present invention in accordance with the composition, so that the effect of the present invention is impaired by the steel plate composition. Absent. However, since electroslag welding has a relatively large base material dilution, it is preferable to limit the steel plate composition within a certain range. Specifically, C: 0.03-0.15%, Si: 1.0% or less, Mn: 0.1-2.5%, P: 0.02% or less, S: 0.008% or less , Al: 0.07% or less, N: 0.010% or less, and carbon equivalent: within the range of 0.25 to 0.60%, one of Ni, Cr, Mo, V as required Or it contains 2 or more types, and also Cu: 0.01-1.5%, Ti: 0 / 002-0.05%, Nb: 0.002-0.10%, B: 0. It is more preferable to set it as the steel plate composition containing 1 type, or 2 or more types of 0002-0.020% and Ca: 0.0002-0.020%. However, the carbon equivalent (Ceq.) Is Ceq. = C (mass%) + Si (mass%) / 24 + Mn (mass%) / 6 + Ni (mass%) / 40 + Cr (mass%) / 5 + Mo (mass%) / 4 + V (mass%) / 14 It is.
メタル粉入り溶接ワイヤは表２に化学組成を示す鋼製外皮を用い、メタル粉の成分組成や充填率を調整することによって、ワイヤ全体の組成が表３−１および表３−２のような溶接ワイヤに製造した。鋼製外皮は板厚０．８ｍｍの帯鋼とし、連続的にＵ形に冷間成型しつつメタル粉を充填し、さらに冷間により断面がほぼ円形になるようにした後、端部を連続的にシーム溶接して、シームレスの充填管に造管し、さらに冷間伸線により最終径１．６ｍｍの溶接ワイヤに製造した。成分調整のメタル粉添加量と充填率との差の調整は鉄粉により行った。また、メタル粉は純金属または鉄合金または種々合金で添加した。Ｃを添加する場合はグラファイトまたはＣを多めに含有した鉄合金を用いた。なお、表３−１および表３−２のうち、Ｃｕについては、鋼製外皮とメタル粉、さらには表面をＣｕめっきした場合にはこのめっき成分も含めた割合を示している。表２の鋼製外皮の内、外皮記号ＨＡ１〜ＨＡ２４は本発明の鋼製外皮に係わる要件を満足しているものであり、外皮記号ＨＢ１〜ＨＢ１７は本発明の鋼製外皮に係わる要件を満足していない例である。また、表３−１の溶接ワイヤのうち、溶接ワイヤ記号ＷＡ１〜ＷＡ３４は本発明の要件を満足している例であり、表３−２の比較例のうち、溶接ワイヤ記号ＷＢ１〜ＷＢ２９は本発明の要件を満足していない比較例である。なお、溶接ワイヤ記号ＷＢ１、ＷＢ３、ＷＢ５、ＷＢ２８及びＷＢ２９は溶接ワイヤの伸線加工段階において、断線が頻発して、溶接に供することができる溶接ワイヤを製造できなったため、溶接継手の作製、溶接金属特性の調査を実施しなかった。他の比較例でも溶接ワイヤの伸線加工中に断線を生じるものはあったが、溶接金属特性が評価可能な程度の溶接長を確保できた溶接ワイヤについては一応溶接継手作製、溶接金属特性調査を実施している。 As for the welding wire containing metal powder, the composition of the whole wire is as shown in Table 3-1 and Table 3-2 by adjusting the component composition and filling rate of the metal powder using a steel outer sheath having a chemical composition shown in Table 2. Manufactured into a welding wire. The steel outer shell is a steel strip with a thickness of 0.8 mm, filled with metal powder while continuously cold-formed into a U shape, and then the end is continuous after the cross-section is made substantially circular by cold. Then, seam welding was performed to form a seamless filled tube, and further, a weld wire having a final diameter of 1.6 mm was manufactured by cold drawing. The adjustment of the difference between the metal powder addition amount and the filling rate of the component adjustment was performed with iron powder. Metal powder was added as pure metal, iron alloy, or various alloys. When adding C, graphite or an iron alloy containing a large amount of C was used. In Tables 3-1 and 3-2, for Cu, the ratio including the plating component when the steel outer shell and the metal powder are plated with Cu. Among the steel skins in Table 2, the skin symbols HA1 to HA24 satisfy the requirements related to the steel skin of the present invention, and the skin symbols HB1 to HB17 satisfy the requirements related to the steel skin of the present invention. This is not an example. Of the welding wires in Table 3-1, welding wire symbols WA1 to WA34 are examples that satisfy the requirements of the present invention, and among the comparative examples in Table 3-2, welding wire symbols WB1 to WB29 are present. It is a comparative example that does not satisfy the requirements of the invention. It should be noted that welding wire symbols WB1, WB3, WB5, WB28 and WB29 were frequently broken at the wire drawing stage of the welding wire, making it impossible to produce a welding wire that can be used for welding. No investigation of metal properties was performed. In other comparative examples, there were breaks that occurred during the wire drawing of the welding wire, but for welding wires that could secure a weld length that allowed evaluation of the weld metal properties, welded joints were prepared and the weld metal properties were investigated. Has been implemented.
溶接は図２に示すＴ字継手を組み立て、表４に示す溶接条件により、定常部を十分確保できるよう、５００ｍｍ以上の溶接ビードができるまで溶接した。溶接条件を表４に示すように、鋼板板厚５０ｍｍと板厚６０ｍｍとも１電極式で、給電ノズルをオシレートして溶接する方法を用いているが、溶接条件は板厚ごとに変えている。ただし、開先幅（図２中のa）は鋼板板厚によらず２５ｍｍ一定とした。なお、実施例ではノズルをオシレートさせる１電極溶接を用いているが、２電極によるエレクトロスラグ溶接でも本発明の効果は変わらない。 The welding was performed by assembling the T-shaped joint shown in FIG. 2 and welding until a weld bead of 500 mm or more was made according to the welding conditions shown in Table 4 so that a steady portion could be sufficiently secured. As shown in Table 4, the welding conditions are a one-electrode type with both a steel plate thickness of 50 mm and a plate thickness of 60 mm, and a method of oscillating the power supply nozzle and welding is used, but the welding conditions are changed for each plate thickness. However, the groove width (a in FIG. 2) was fixed to 25 mm regardless of the steel plate thickness. In addition, although the 1-electrode welding which oscillates a nozzle is used in the Example, the effect of this invention does not change even in the electroslag welding by 2 electrodes.
図２に示すように、ボックス構造のスキンプレートにダイヤフラムを溶接するエレクトロスラグ溶接においては開先断面を閉断面とするために裏当金を用いる必要がある。溶接時に裏当金も一部溶融して溶接金属の一部を構成することになるが、その希釈率はせいぜい１０％であるため、本発明の溶接ワイヤを用いるに際しては、その組成は本発明の効果に影響を与えることはなく、特にその組成を限定する必要はないが、Ｃ、Ｎ量については溶接金属の靭性に対する影響がやや大きいため、Ｃ：０．２０％以下、Ｎ：０．０１５％以下の成分組成を用いる鋼を用いることがより好ましい。本実施例においては断面サイズが２８ｍｍ×５０ｍｍで、組成が、Ｃ：０．１１％、Ｓｉ：０．２９％、Ｍｎ：１．３４％、Ｐ：０．０１３％、Ｓ：０．０１３％、Ｃｕ：０．１０％、Ｎｉ：０．０５％、Ｎｂ：０．０１５％、Ａｌ：０．０３％、Ｎ：０．０９９％のフラットバーを使用した。 As shown in FIG. 2, in electroslag welding in which a diaphragm is welded to a skin plate having a box structure, it is necessary to use a backing metal in order to make the groove cross section a closed cross section. Although the backing metal partially melts during welding to form a part of the weld metal, the dilution rate is at most 10%. Therefore, when the welding wire of the present invention is used, the composition thereof is the present invention. However, the C and N contents have a somewhat large effect on the toughness of the weld metal, so that C: 0.20% or less, N: 0.00. It is more preferable to use steel using a component composition of 015% or less. In this example, the cross-sectional size is 28 mm × 50 mm, and the composition is C: 0.11%, Si: 0.29%, Mn: 1.34%, P: 0.013%, S: 0.013% , Cu: 0.10%, Ni: 0.05%, Nb: 0.015%, Al: 0.03%, N: 0.099% flat bars were used.
表５に溶接ワイヤと鋼板の組み合わせ条件、溶接金属の強度、靭性を示す。表５のうち、本発明の溶接ワイヤを用いて溶接した継手記号ＴＡ１〜ＴＡ３５の溶接金属は、いずれの強度レベルにおいても（引張強さで５２６〜６９２ＭＰａ）、０℃における２ｍｍＶノッチシャルピー吸収エネルギーは全て７０Ｊ以上を安定して達成しており、本発明によれば、メタル粉入り溶接ワイヤによるエレクトロスラグ溶接における溶接金属は極めて良好な靭性を達成できることが明らかである。また、表３−１および表３−２に示すように、一部の比較例とは異なり、溶接ワイヤの製造性に問題があったり、溶接作業性が劣るようなことも全くなかった。 Table 5 shows the combination conditions of the welding wire and steel plate, the strength and toughness of the weld metal. In Table 5, the weld metal of the joint symbols TA1 to TA35 welded using the welding wire of the present invention has a 2 mmV notch Charpy absorbed energy at 0 ° C. at any strength level (tensile strength of 526 to 692 MPa). All of 70 J or more were stably achieved, and according to the present invention, it is clear that the weld metal in electroslag welding with a metal powder-containing welding wire can achieve extremely good toughness. Further, as shown in Tables 3-1 and 3-2, unlike some comparative examples, there was no problem with the manufacturability of the welding wire and there was no inferior welding workability.
一方、比較例である、溶接ワイヤＷＢ１〜ＷＢ２９は、表２、表３−１、表３−２及び表５から、ワイヤ製造性、溶接作業性、溶接金属靭性の一つまたは二つあるいは全部が本発明のメタル粉入り溶接ワイヤに比べて劣っていることが明白である。 On the other hand, welding wires WB1 to WB29, which are comparative examples, are one or two or all of wire manufacturability, welding workability, and weld metal toughness from Table 2, Table 3-1, Table 3-2 and Table 5. Is clearly inferior to the metal powder-containing welding wire of the present invention.
すなわち、溶接ワイヤＷＢ１は、鋼製外皮のＣ含有量が過大であるため、鋼製外皮の延性特性が十分でなく、そのため、伸線加工中に破断が頻発し、溶接継手作製に供試できる溶接ワイヤとなすことができなかった。すなわち、ワイヤ製造性が極めて劣るため、好ましくない。 That is, since the welding wire WB1 has an excessive C content in the steel outer shell, the ductility characteristic of the steel outer shell is not sufficient, and therefore, breakage frequently occurs during wire drawing and can be used for making a welded joint. Could not be welded wire. That is, it is not preferable because wire manufacturability is extremely poor.
溶接ワイヤＷＢ２（継手ＴＢ１）は、鋼製外皮のＳｉ含有量が過小であるため、鋼製外皮中のＯ含有量が多く、粗大な酸化物も多いため、溶接ワイヤの伸線加工中に破断が生じた。溶接は実施できたが、溶接ワイヤ中のＳｉ含有量も過小であるため、その結果、溶接金属中のＯ含有量が過大となり、溶接金属の靭性が劣る。すなわち、溶接ワイヤＷＢ２は溶接ワイヤの製造性と溶接金属靭性とがともに劣るため、好ましくない。 Welding wire WB2 (joint TB1) breaks during wire drawing of the welding wire because the steel sheath has an excessively small Si content, so the steel sheath has a large O content and a large amount of coarse oxides. Occurred. Although welding could be carried out, the Si content in the welding wire is too small. As a result, the O content in the weld metal becomes excessive, and the toughness of the weld metal is inferior. That is, the welding wire WB2 is not preferable because both the productivity of the welding wire and the weld metal toughness are inferior.
溶接ワイヤＷＢ３は、鋼製外皮のＳｉ含有量が過大であることが原因で、鋼製外皮の延性特性が十分でないため、伸線加工中に破断が頻発し、溶接継手作製に供試できる溶接ワイヤとなすことができなかった。 Welding wire WB3 is a weld that can be used for making welded joints because the ductility characteristics of the steel sheath are not sufficient due to the excessive Si content in the steel sheath, and the fracture frequently occurs during wire drawing. I couldn't make it with wire.
溶接ワイヤＷＢ４（継手ＴＢ２）は、鋼製外皮のＭｎ含有量が過小であるため、鋼製外皮中のＯ含有量が多く、粗大な酸化物も多いため、溶接ワイヤの伸線加工中に破断が生じた。溶接は実施できたが、溶接ワイヤ中のＭｎ含有量が過小であるため、溶接金属中のＯ含有量が過大となり、また、溶接金属のミクロ組織も粗大となるため、溶接金属の靭性が劣る。すなわち、溶接ワイヤＷＢ４は溶接ワイヤの製造性と溶接金属靭性とがともに劣るため、好ましくない。 Welding wire WB4 (joint TB2) breaks during wire drawing of the welding wire because the Mn content in the steel outer skin is too small, so the O content in the steel outer shell is large and there are also many coarse oxides. Occurred. Although welding could be carried out, the Mn content in the welding wire is too small, so the O content in the weld metal becomes excessive, and the microstructure of the weld metal also becomes coarse, so the toughness of the weld metal is inferior. . That is, the welding wire WB4 is not preferable because both the productivity of the welding wire and the weld metal toughness are inferior.
溶接ワイヤＷＢ５は、鋼製外皮のＭｎ含有量が過大であるため、伸線加工中に外皮の強度が過大となり、伸線加工中に破断が頻発し、溶接継手作製に供試できる溶接ワイヤとなすことができなかった。 Since the welding wire WB5 has an excessively high Mn content in the steel outer sheath, the strength of the outer sheath becomes excessive during the wire drawing process, breakage frequently occurs during the wire drawing process, and a welding wire that can be used for making welded joints. I couldn't do it.
溶接ワイヤＷＢ６（継手ＴＢ３）は、溶接ワイヤのＰ含有量が過大なため、溶接金属中のＰ含有量も多く、そのため、溶接金属の靭性が劣る。 Since the welding wire WB6 (joint TB3) has an excessive P content in the welding wire, the welding wire WB6 (joint TB3) has a large P content in the weld metal, and therefore the toughness of the weld metal is inferior.
溶接ワイヤＷＢ７（継手ＴＢ４）は、溶接ワイヤのＳ含有量が過大なため、溶接金属中のＳ含有量も多く、そのため、溶接金属の靭性が劣る。 Since welding wire WB7 (joint TB4) has an excessive S content in the welding wire, it also has a large S content in the weld metal, and therefore the toughness of the weld metal is poor.
溶接ワイヤＷＢ８（継手ＴＢ５）は、鋼製外皮のＡｌ含有量が過大であることにより溶接ワイヤのＡｌ含有量も過大であるため、溶接中にスラグ量が増加してスパッタが発生して溶接作業性が劣化するとともに、溶接金属中のＯ含有量が過大であるために、溶接金属中の靭性も劣り、好ましくない。 Since welding wire WB8 (joint TB5) has an excessively high Al content in the steel sheath, the Al content in the welding wire is also excessive, so the amount of slag increases during welding and spatter is generated during welding. In addition to the deterioration of the properties, the O content in the weld metal is excessive, so the toughness in the weld metal is also inferior, which is not preferable.
溶接ワイヤＷＢ９（継手ＴＢ６）は、鋼製外皮のＮ含有量が過大であることにより溶接ワイヤのＮ含有量も過大であるため、溶接金属中のＯ含有量が過大となり、溶接金属中の靭性が劣り、好ましくない。 Welding wire WB9 (joint TB6) has an excessive N content in the weld metal due to an excessive N content in the steel outer sheath, so an excessive O content in the weld metal results in toughness in the weld metal. Is inferior and is not preferred.
溶接ワイヤＷＢ１０（継手ＴＢ７）は、鋼製外皮のＳｉ含有量とＭｎ含有量とがともに過大であるため、鋼製外皮の延性が十分でないため、溶接ワイヤの伸線加工中に破断が生じた。溶接は実施できたが、溶接ワイヤ中のＳｉとＭｎ含有量が過大であるため、溶接金属の靭性が劣る。すなわち、溶接ワイヤＷＢ１０は溶接ワイヤの製造性と溶接金属靭性とがともに劣るため、好ましくない。 Welding wire WB10 (joint TB7) has an excessive steel content and Mn content, so the ductility of the steel skin is not sufficient, and therefore breakage occurred during wire drawing of the welding wire. . Although welding could be performed, the toughness of the weld metal is inferior because the Si and Mn contents in the welding wire are excessive. That is, the welding wire WB10 is not preferable because both the productivity of the welding wire and the weld metal toughness are inferior.
溶接ワイヤＷＢ１１（継手ＴＢ８）は、鋼製外皮のＡｌ含有量が過大なため、溶接ワイヤ全体としてのＡｌ含有量も過大となり、溶接ワイヤＷＢ８と同様、溶接中にスラグ量が増加してスパッタが発生して溶接作業性が劣化するとともに、溶接金属中のＯ含有量が過大であるために、溶接金属中の靭性も劣り、好ましくない。 Since the welding wire WB11 (joint TB8) has an excessive aluminum content in the steel outer sheath, the Al content of the entire welding wire also becomes excessive, and as with the welding wire WB8, the amount of slag increases during welding and spattering occurs. It is generated and welding workability deteriorates, and since the O content in the weld metal is excessive, the toughness in the weld metal is also inferior, which is not preferable.
溶接ワイヤＷＢ１２（継手ＴＢ９）は、溶接ワイヤＷＢ１１と同様、鋼製外皮のＡｌ含有量が過大なため、溶接ワイヤ全体としてもＡｌ含有量が過大であるため、溶接中にスラグ量が増加してスパッタが発生して溶接作業性が劣化するとともに、溶接金属中のＯ含有量が過大であるために、溶接金属中の靭性も劣り、好ましくない。 As with the welding wire WB11, the welding wire WB12 (joint TB9) has an excessively high Al content in the steel outer sheath, and therefore the Al content of the entire welding wire is excessive, so the amount of slag increases during welding. Spatter is generated and welding workability deteriorates, and since the O content in the weld metal is excessive, the toughness in the weld metal is also inferior, which is not preferable.
溶接ワイヤＷＢ１３（継手ＴＢ１０）は、溶接ワイヤＷＢ１１、ＷＢ１２と同様、鋼製外皮のＡｌ含有量が過大なため、溶接ワイヤ全体としてもＡｌ含有量が過大であるため、溶接中にスラグ量が増加してスパッタが発生して溶接作業性が劣化するとともに、溶接金属中のＯ含有量が過大であるために、溶接金属中の靭性も劣る。 As with the welding wires WB11 and WB12, the welding wire WB13 (joint TB10) has an excessively high Al content in the steel outer sheath, and therefore the Al content of the entire welding wire is excessive, so the amount of slag increases during welding. As a result, spatter is generated and welding workability is deteriorated, and since the O content in the weld metal is excessive, the toughness in the weld metal is also inferior.
溶接ワイヤＷＢ１４（継手ＴＢ１１）は、鋼製外皮のＣ量が過大であるため、鋼製外皮の延性特性が劣り、そのため、溶接ワイヤの伸線加工中に破断が生じた。溶接は実施できたが、鋼製外皮のＣ含有量が過大であることに起因して溶接ワイヤ中のＣ含有量が過大であるため、溶接金属中のＣ含有量も過大となり、溶接金属の靭性が劣る。すなわち、溶接ワイヤＷＢ１４は溶接ワイヤの製造性と溶接金属靭性とがともに劣る。 Since the welding wire WB14 (joint TB11) has an excessive amount of C in the steel outer sheath, the ductility characteristic of the steel outer sheath is inferior, and therefore breakage occurred during the wire drawing of the welding wire. Although welding could be performed, the C content in the welding wire was excessive due to the excessive C content in the steel outer sheath, so the C content in the weld metal also became excessive. Toughness is inferior. That is, the welding wire WB14 is inferior in both the weld wire manufacturability and the weld metal toughness.
溶接ワイヤＷＢ１５（継手ＴＢ１２）は、鋼製外皮のＳｉ量が過大であるため、鋼製外皮の延性特性が劣り、そのため、溶接ワイヤの伸線加工中に破断が生じた。溶接は実施できたが、鋼製外皮のＳｉ含有量が過大であることに起因して溶接ワイヤ中のＳｉ含有量が過大であるため、溶接金属中のＳｉ含有量も過大となり、溶接金属の靭性が劣る。すなわち、溶接ワイヤＷＢ１５は溶接ワイヤの製造性と溶接金属靭性とがともに劣る。 Welding wire WB15 (joint TB12) has an excessive amount of Si in the steel outer sheath, so the ductility characteristics of the steel outer sheath are inferior, and therefore breakage occurred during wire drawing of the welding wire. Although welding could be carried out, the Si content in the weld metal was excessive because the Si content in the steel wire was excessive due to the excessive Si content in the steel sheath. Toughness is inferior. That is, the welding wire WB15 is inferior in both the weld wire manufacturability and the weld metal toughness.
溶接ワイヤＷＢ１６（継手ＴＢ１３）は、鋼製外皮のＭｎ量が過大であるため、鋼製外皮の強度が伸線中に過度に高くなったため、溶接ワイヤの伸線加工中に破断が生じた。溶接は実施できたが、鋼製外皮のＭｎ含有量が過大であることに起因して溶接ワイヤ中のＭｎ含有量が過大であるため、溶接金属中のＭｎ含有量も過大となり、溶接金属の靭性が劣る。すなわち、溶接ワイヤＷＢ１６は溶接ワイヤの製造性と溶接金属靭性とがともに劣る。 The welding wire WB16 (joint TB13) had an excessively high Mn content in the steel outer skin, so that the strength of the steel outer skin became excessively high during wire drawing, and therefore breakage occurred during wire drawing of the welding wire. Although welding could be performed, the Mn content in the weld metal was excessive due to the excessive Mn content in the steel outer sheath, so the Mn content in the weld metal also became excessive. Toughness is inferior. That is, the welding wire WB16 is inferior in both the weld wire manufacturability and the weld metal toughness.
溶接ワイヤＷＢ１７（継手ＴＢ１４）は、鋼製外皮のＯ量が過大であるため、鋼製外皮の延性特性が劣り、溶接ワイヤの伸線加工中に破断が生じた。溶接は実施できたが、鋼製外皮のＯ含有量が過大であることが主要因となって溶接ワイヤ中のＯ含有量が過大であるため、溶接金属中のＯ含有量も過大となり、溶接金属の靭性が劣る。すなわち、溶接ワイヤＷＢ１７は溶接ワイヤの製造性と溶接金属靭性とがともに劣る。 Since the welding wire WB17 (joint TB14) has an excessive amount of O in the steel outer sheath, the ductility characteristic of the steel outer sheath is inferior, and breakage occurred during wire drawing of the welding wire. Welding could be carried out, but the O content in the welding wire is excessive due to the excessive O content in the steel outer sheath, which is the main factor. Metal toughness is inferior. That is, the welding wire WB17 is inferior in both the weld wire manufacturability and the weld metal toughness.
溶接ワイヤＷＢ１８（継手ＴＢ１５）は、鋼製外皮は本発明を満足しているため、溶接ワイヤの製造性には問題はないが、溶接ワイヤ全体としてのＣ含有量が過大であるため、溶接金属中のＣ含有量も過大となり、靭性が劣る。 The welding wire WB18 (joint TB15) has no problem in manufacturability of the welding wire because the steel outer shell satisfies the present invention. However, since the C content of the entire welding wire is excessive, the weld metal The C content in the medium becomes excessive and the toughness is inferior.
溶接ワイヤＷＢ１９（継手ＴＢ１６）は、鋼製外皮は本発明を満足しているため、溶接ワイヤの製造性には問題はないが、溶接ワイヤ全体としてのＭｎ含有量が過大であるため、溶接金属中のＭｎ含有量も過大となり、靭性が劣る。 The welding wire WB19 (joint TB16) has no problem in manufacturability of the welding wire because the steel outer shell satisfies the present invention. However, since the Mn content of the entire welding wire is excessive, the weld metal The Mn content in the medium becomes excessive and the toughness is inferior.
溶接ワイヤＷＢ２０（継手ＴＢ１７）は、鋼製外皮は本発明を満足しているが、溶接ワイヤのＡｌ含有量としては過大であるため、Ａｌの悪影響が生じ、溶接作業性、溶接金属靭性が本発明に比べて劣る。 Welding wire WB20 (joint TB17) has a steel outer shell that satisfies the present invention. However, since the Al content of the welding wire is excessive, the adverse effect of Al occurs, and the welding workability and weld metal toughness are the same. It is inferior to the invention.
溶接ワイヤＷＢ２１（継手ＴＢ１８）は、溶接ワイヤ全体でＴｉを実質的に全く含有していないため、溶接金属中のＯ含有量もが過大となり、溶接金属の靭性が劣る。 Since welding wire WB21 (joint TB18) contains substantially no Ti in the entire welding wire, the O content in the weld metal is excessive and the toughness of the weld metal is poor.
溶接ワイヤＷＢ２２（継手ＴＢ１９）は、溶接ワイヤ中にＴｉは含有されているものの、その含有量が十分でないため、溶接ワイヤＷＢ２１と同様、溶接金属中のＯ含有量もが過大となり、溶接金属の靭性が劣る。 Although welding wire WB22 (joint TB19) contains Ti in the welding wire, but its content is not sufficient, as with welding wire WB21, the O content in the weld metal is excessive, and the weld metal Toughness is inferior.
溶接ワイヤＷＢ２３（継手ＴＢ２０）は、溶接ワイヤＷＢ２１、ＷＢ２２とは反対に、溶接ワイヤ中のＴｉ含有量が過大なため、また、Ｍｇ＋Ｔｉ／５の値も本発明を逸脱して過大であるため、溶接金属中に粗大な析出物を形成し、また、Ｔｉの析出脆化が生じて溶接金属の靭性を劣化させており、好ましくない。 The welding wire WB23 (joint TB20) is opposite to the welding wires WB21 and WB22, because the Ti content in the welding wire is excessive, and the value of Mg + Ti / 5 is also excessive from the present invention. Coarse precipitates are formed in the weld metal, and Ti embrittlement embrittles and deteriorates the toughness of the weld metal, which is not preferable.
溶接ワイヤＷＢ２４（継手ＴＢ２１）は、溶接ワイヤ中にＴｉとＭｇとがともに含有されておらず、従って、Ｍｇ＋Ｔｉ／５も過小であるため、溶接金属中のＯ含有量もが過大となり、溶接金属の靭性が劣る。 Since welding wire WB24 (joint TB21) does not contain both Ti and Mg in the welding wire, and therefore Mg + Ti / 5 is too small, the O content in the weld metal is too large, and the weld metal Inferior toughness.
溶接ワイヤＷＢ２５（継手ＴＢ２２）は、溶接ワイヤ中にＭｇが含有されておらず、Ｍｇ＋Ｔｉ／５も過小であるため、溶接金属中のＯ含有量もが過大となり、溶接金属の靭性が劣る。 Since welding wire WB25 (joint TB22) does not contain Mg in the welding wire and Mg + Ti / 5 is too small, the O content in the weld metal is too large and the toughness of the weld metal is poor.
溶接ワイヤＷＢ２６（継手ＴＢ２３）は、溶接ワイヤ中にＭｇは含有されているものの、その含有量が過小であり、また、Ｍｇ＋Ｔｉ／５も過小であるため、溶接金属中のＯ含有量もが過大となり、溶接金属の靭性が劣る。 Although welding wire WB26 (joint TB23) contains Mg in the welding wire, its content is too low, and Mg + Ti / 5 is too low, so the O content in the weld metal is too high. Thus, the toughness of the weld metal is inferior.
溶接ワイヤＷＢ２７（継手ＴＢ２４）は、溶接ワイヤ中のＭｇ含有量が過大なため、また、Ｍｇ＋Ｔｉ／５の値も本発明を逸脱して過大であるため、Ｍｇによる靭性劣化、Ｔｉの析出脆化により溶接金属の靭性が劣っており、好ましくない。 Since the welding wire WB27 (joint TB24) has an excessive Mg content in the welding wire, and the Mg + Ti / 5 value is also excessively deviating from the present invention, the toughness deterioration due to Mg, Ti precipitation embrittlement Therefore, the toughness of the weld metal is inferior, which is not preferable.
溶接ワイヤＷＢ２８は及び溶接ワイヤＷＢ２９は、メタル粉の充填率が過大であるため、溶接ワイヤの伸線加工中に破断を頻発した。そのため、溶接継手作製に供すべき溶接ワイヤを製造できなかった。 The welding wire WB28 and the welding wire WB29 frequently broke during the wire drawing of the welding wire because the filling rate of the metal powder was excessive. Therefore, the welding wire which should be used for welding joint preparation was not able to be manufactured.
以上の実施例からも、本発明によれば、非消耗ノズル式エレクトロスラグ溶接により形成された溶接金属の２ｍｍＶノッチシャルピー衝撃試験の０℃における吸収エネルギーが７０Ｊ以上となる、充填フラックスが金属粉あるいは／および合金粉からなるメタル粉入り溶接ワイヤを得られることが明らかである。 Also from the above examples, according to the present invention, the absorbed energy at 0 ° C. of the 2 mm V notch Charpy impact test of the weld metal formed by non-consumable nozzle type electroslag welding is 70 J or more, the filling flux is metal powder or It is clear that a welding wire containing metal powder made of / and alloy powder can be obtained.
１ 鋼板（スキンプレート）
２ 鋼板（ダイヤフラム）
３ 裏当金
ａ 開先幅
４ 溶接金属
５ 引張試験片
６ ２ｍｍＶノッチシャルピー衝撃試験片
1 Steel plate (skin plate)
2 Steel plate (diaphragm)
3 Back metal a
Claims (5)
Ｃ ：０．００５〜０．１０％、
Ｓｉ：０．０１〜１．０％、
Ｍｎ：０．１〜２．５％、
Ｐ ：０．０２％以下、
Ｓ ：０．００８％以下、
Ａｌ：０．０３０％以下、
Ｎ ：０．００１〜０．０１０％、
Ｏ ：０．０１０％以下、
を含有し、残部がＦｅおよび不可避不純物からなり、さらに、溶接ワイヤ全体の成分組成が、溶接ワイヤ全質量に対する質量％で、
Ｃ ：０．００５〜０．１０％、
Ｓｉ：０．１０〜１．５％、
Ｍｎ：０．１〜２．５％、
Ｐ ：０．０２％以下、
Ｓ ：０．００８％以下、
Ａｌ：０．０３０％以下、
Ｎ ：０．００１〜０．０１０％、
Ｔｉ：０．００５〜０．３０％、
Ｍｇ：０．０１５〜０．３０％、
Ｏ ：０．１５％以下、
を含有し、残部がＦｅおよび不可避不純物からなり、かつ、［Ｍｇ］＋［Ｔｉ］／５＝０．０２０〜０．３０％であり、合わせて、前記メタル粉の充填率が溶接ワイヤ全体に対する質量％で５〜２０％であることを特徴とする、メタル粉入りエレクトロスラグ溶接用溶接ワイヤ。
ただし、［Ｍｇ］、［Ｔｉ］は各々溶接ワイヤ全体の成分組成としてのＭｇとＴｉの質量％である。 In the welding wire for electroslag welding formed by filling metal powder in the steel outer shell, the steel outer shell is in mass% with respect to the total mass of the steel outer shell,
C: 0.005-0.10%,
Si: 0.01 to 1.0%,
Mn: 0.1 to 2.5%
P: 0.02% or less,
S: 0.008% or less,
Al: 0.030% or less,
N: 0.001 to 0.010%,
O: 0.010% or less,
The balance is composed of Fe and inevitable impurities, and the component composition of the entire welding wire is, in mass% with respect to the total mass of the welding wire,
C: 0.005-0.10%,
Si: 0.10 to 1.5%
Mn: 0.1 to 2.5%
P: 0.02% or less,
S: 0.008% or less,
Al: 0.030% or less,
N: 0.001 to 0.010%,
Ti: 0.005 to 0.30%,
Mg: 0.015-0.30%,
O: 0.15% or less,
And the balance consists of Fe and inevitable impurities, and [Mg] + [Ti] /5=0.020 to 0.30%, and the filling rate of the metal powder is based on the whole welding wire A welding wire for electroslag welding containing metal powder, characterized by being 5 to 20% by mass.
However, [Mg] and [Ti] are mass% of Mg and Ti as the component composition of the whole welding wire, respectively.
Ｃｕ：０．０１〜１．５０％、
Ｎｉ：０．０１〜６．０％、
Ｃｒ：０．０１〜２．０％、
Ｍｏ：０．０１〜２．０％、
Ｗ ：０．０１〜２．０％、
Ｎｂ：０．００２〜０．１０％、
Ｖ ：０．００５〜０．５０％、
Ｔａ：０．００５〜０．５０％、
Ｚｒ：０．００５〜０．５０％、
Ｂ ：０．０００２〜０．０１０％、
の１種または２種以上を含有することを特徴とする、請求項１に記載のメタル粉入りエレクトロスラグ溶接用溶接ワイヤ。 In the welding wire, the component composition of the entire welding wire is, in mass% with respect to the total mass of the welding wire,
Cu: 0.01 to 1.50%,
Ni: 0.01-6.0%,
Cr: 0.01 to 2.0%,
Mo: 0.01 to 2.0%,
W: 0.01 to 2.0%,
Nb: 0.002 to 0.10%,
V: 0.005-0.50%,
Ta: 0.005 to 0.50%,
Zr: 0.005 to 0.50%,
B: 0.0002 to 0.010%,
The welding wire for electroslag welding containing metal powder according to claim 1, comprising one or more of the following.
Ｃａ：０．０００２〜０．００５０％、
ＲＥＭ：０．０００２〜０．００５０％、
の１種または２種を含有することを特徴とする、請求項１または２に記載のメタル粉入りエレクトロスラグ溶接用溶接ワイヤ。 In the welding wire, the component composition of the entire welding wire is, in mass% with respect to the total mass of the welding wire,
Ca: 0.0002 to 0.0050%,
REM: 0.0002 to 0.0050%,
The welding wire for electroslag welding containing metal powder according to claim 1 or 2, characterized by containing one or two of the following.
Ｃｕ：０．０１〜１．５０％、
Ｎｉ：０．０１〜６．０％、
Ｃｒ：０．０１〜２．０％、
Ｍｏ：０．０１〜２．０％、
Ｗ ：０．０１〜２．０％、
Ｎｂ：０．００２〜０．１０％、
Ｖ：０．００５〜０．５０％、
Ｔａ：０．００５〜０．５０％、
Ｚｒ：０．００５〜０．５０％、
Ｂ ：０．０００２〜０．００５０％、
の１種または２種以上を含有することを特徴とする、請求項１〜３のいずれかに記載のメタル粉入りエレクトロスラグ溶接用溶接ワイヤ。 The steel outer shell is further in mass%,
Cu: 0.01 to 1.50%,
Ni: 0.01-6.0%,
Cr: 0.01 to 2.0%,
Mo: 0.01 to 2.0%,
W: 0.01 to 2.0%,
Nb: 0.002 to 0.10%,
V: 0.005 to 0.50%,
Ta: 0.005 to 0.50%,
Zr: 0.005 to 0.50%,
B: 0.0002 to 0.0050%,
The welding wire for electroslag welding containing metal powder according to any one of claims 1 to 3, characterized by containing one or more of the following.
Ｔｉ：０．００５〜０．０５０％、
Ｍｇ：０．００２〜０．０１０％、
Ｃａ：０．０００２〜０．００５０％、
ＲＥＭ：０．０００２〜０．００５０％、
の１種または２種以上を含有することを特徴とする、請求項１〜４のいずれかに記載のメタル粉入りエレクトロスラグ溶接用溶接ワイヤ。 The steel outer shell is further in mass%,
Ti: 0.005 to 0.050%,
Mg: 0.002 to 0.010%,
Ca: 0.0002 to 0.0050%,
REM: 0.0002 to 0.0050%,
The welding wire for electroslag welding containing metal powder according to any one of claims 1 to 4, characterized by containing one or more of the following.
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| JP2010016925A JP5375632B2 (en) | 2010-01-28 | 2010-01-28 | Welding wire for electroslag welding with metal powder |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2018030160A (en) * | 2016-08-25 | 2018-03-01 | 日鐵住金溶接工業株式会社 | Flux-cored wire for electroslag welding |
| KR20190070710A (en) * | 2017-12-13 | 2019-06-21 | 주식회사 포스코 | Flux cored arc weld material and welded joint using the same |
| KR20190078231A (en) * | 2017-12-26 | 2019-07-04 | 주식회사 포스코 | Cold-rolled steel sheet for flux cored wire and manufacturing the same |
| KR20190137300A (en) * | 2018-06-01 | 2019-12-11 | 주식회사 포스코 | Cold-rolled steel sheet for flux cored wire and manufacturing the same |
| WO2021125280A1 (en) * | 2019-12-20 | 2021-06-24 | Ｊｆｅスチール株式会社 | Steel wire for gas-shielded arc welding, gas-shielded arc welding method, and method for manufacturing gas-shielded arc welded joint |
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| JP2008093715A (en) * | 2006-10-13 | 2008-04-24 | Nippon Steel Corp | High yield strength and high toughness flux-cored wire for gas-shielded arc welding |
| JP2009045671A (en) * | 2007-07-23 | 2009-03-05 | Jfe Steel Kk | Wire for high-heat input electroslag welding |
| JP2009082947A (en) * | 2007-09-28 | 2009-04-23 | Jfe Steel Kk | Flux-cored wire for electrogas arc welding |
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| JP2018030160A (en) * | 2016-08-25 | 2018-03-01 | 日鐵住金溶接工業株式会社 | Flux-cored wire for electroslag welding |
| KR102045634B1 (en) | 2017-12-13 | 2019-11-15 | 주식회사 포스코 | Flux cored arc weld material and welded joint using the same |
| KR20190070710A (en) * | 2017-12-13 | 2019-06-21 | 주식회사 포스코 | Flux cored arc weld material and welded joint using the same |
| KR102134310B1 (en) * | 2017-12-26 | 2020-07-15 | 주식회사 포스코 | Cold-rolled steel sheet for flux cored wire and manufacturing the same |
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| KR102353730B1 (en) * | 2019-12-20 | 2022-01-19 | 주식회사 포스코 | Cold-rolled steel sheet for flux cored wire and manufacturing the same |
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