JPS62166098A - Flux-cored wire for gas shielded arc welding - Google Patents
Flux-cored wire for gas shielded arc weldingInfo
- Publication number
- JPS62166098A JPS62166098A JP519486A JP519486A JPS62166098A JP S62166098 A JPS62166098 A JP S62166098A JP 519486 A JP519486 A JP 519486A JP 519486 A JP519486 A JP 519486A JP S62166098 A JPS62166098 A JP S62166098A
- Authority
- JP
- Japan
- Prior art keywords
- flux
- welding
- weld metal
- wire
- low
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 238000003466 welding Methods 0.000 title claims description 48
- 229910052751 metal Inorganic materials 0.000 claims abstract description 50
- 239000002184 metal Substances 0.000 claims abstract description 50
- 230000004907 flux Effects 0.000 claims abstract description 17
- 229910044991 metal oxide Inorganic materials 0.000 claims abstract description 9
- BVKZGUZCCUSVTD-UHFFFAOYSA-L Carbonate Chemical compound [O-]C([O-])=O BVKZGUZCCUSVTD-UHFFFAOYSA-L 0.000 claims abstract description 8
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 6
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 6
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 5
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 5
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 5
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 5
- 150000004706 metal oxides Chemical class 0.000 claims description 7
- 229910000831 Steel Inorganic materials 0.000 claims description 5
- 239000010959 steel Substances 0.000 claims description 5
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 abstract description 19
- 229910052760 oxygen Inorganic materials 0.000 abstract description 19
- 239000001301 oxygen Substances 0.000 abstract description 19
- WUKWITHWXAAZEY-UHFFFAOYSA-L calcium difluoride Chemical compound [F-].[F-].[Ca+2] WUKWITHWXAAZEY-UHFFFAOYSA-L 0.000 abstract description 7
- 229910001632 barium fluoride Inorganic materials 0.000 abstract description 6
- 229910001634 calcium fluoride Inorganic materials 0.000 abstract description 6
- 239000000463 material Substances 0.000 abstract description 5
- 229910001209 Low-carbon steel Inorganic materials 0.000 abstract description 4
- 229910001635 magnesium fluoride Inorganic materials 0.000 abstract description 4
- KLZUFWVZNOTSEM-UHFFFAOYSA-K Aluminium flouride Chemical compound F[Al](F)F KLZUFWVZNOTSEM-UHFFFAOYSA-K 0.000 abstract 2
- -1 etc. Inorganic materials 0.000 abstract 2
- 230000003247 decreasing effect Effects 0.000 abstract 1
- PQXKHYXIUOZZFA-UHFFFAOYSA-M lithium fluoride Inorganic materials [Li+].[F-] PQXKHYXIUOZZFA-UHFFFAOYSA-M 0.000 abstract 1
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N Titan oxide Chemical compound O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 description 31
- 230000000694 effects Effects 0.000 description 14
- 239000002893 slag Substances 0.000 description 14
- 239000011324 bead Substances 0.000 description 9
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 9
- 239000010936 titanium Substances 0.000 description 5
- 239000003795 chemical substances by application Substances 0.000 description 4
- 229910001512 metal fluoride Inorganic materials 0.000 description 4
- 150000004649 carbonic acid derivatives Chemical class 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 239000007789 gas Substances 0.000 description 3
- 229910052739 hydrogen Inorganic materials 0.000 description 3
- 239000001257 hydrogen Substances 0.000 description 3
- 229910000851 Alloy steel Inorganic materials 0.000 description 2
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 description 2
- 239000010949 copper Substances 0.000 description 2
- 230000002542 deteriorative effect Effects 0.000 description 2
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 2
- 229910052737 gold Inorganic materials 0.000 description 2
- 239000010931 gold Substances 0.000 description 2
- 210000003786 sclera Anatomy 0.000 description 2
- 101100165035 Arabidopsis thaliana AZF3 gene Proteins 0.000 description 1
- 241001391944 Commicarpus scandens Species 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 230000002378 acidificating effect Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 229910052789 astatine Inorganic materials 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 239000003610 charcoal Substances 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000005553 drilling Methods 0.000 description 1
- 230000035553 feeding performance Effects 0.000 description 1
- 239000010436 fluorite Substances 0.000 description 1
- 239000004571 lime Substances 0.000 description 1
- 239000001095 magnesium carbonate Substances 0.000 description 1
- ZLNQQNXFFQJAID-UHFFFAOYSA-L magnesium carbonate Chemical compound [Mg+2].[O-]C([O-])=O ZLNQQNXFFQJAID-UHFFFAOYSA-L 0.000 description 1
- 229910000021 magnesium carbonate Inorganic materials 0.000 description 1
- 235000014380 magnesium carbonate Nutrition 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 239000007800 oxidant agent Substances 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 150000003839 salts Chemical class 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- LEDMRZGFZIAGGB-UHFFFAOYSA-L strontium carbonate Chemical compound [Sr+2].[O-]C([O-])=O LEDMRZGFZIAGGB-UHFFFAOYSA-L 0.000 description 1
- 229910000018 strontium carbonate Inorganic materials 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 239000004408 titanium dioxide Substances 0.000 description 1
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は、海洋構造物など低温靭性が要求される構造物
を製造する際のガスシールドアーク溶接に用いるフラッ
クス入シワイヤに関する。DETAILED DESCRIPTION OF THE INVENTION (Field of Industrial Application) The present invention relates to a flux-cored shear wire used in gas-shielded arc welding when manufacturing structures requiring low-temperature toughness such as offshore structures.
（従来の技術）
最近の石油開発は、より寒冷域で進められるようになり
、それに伴って石油掘削用の海洋構造物は大形化し、溶
接部の靭性はより低温で要求されるようになってきた。(Prior art) Recently, oil development has been proceeding in colder regions, and as a result, offshore structures for oil drilling have become larger and toughness of welds is required at lower temperatures. It's here.
このような要求に対しては、これまで被覆アーク溶接棒
あるいは潜弧浴接材料が適用されてきた。To meet such requirements, coated arc welding rods or submerged arc bath welding materials have so far been applied.
一方、自動、半自動溶接材料としてのガスシールドアー
ク溶接用ワイヤ、とりわけフラックス入シワイヤの最近
の伸長は著しく、鉄骨、橋梁、造船など様々な分野で用
いられている。それはフラックス入りワイヤがすみ肉溶
接、立向き溶接などあらゆる溶接姿勢で溶接作業性が良
好で、しかも高能率の得られる溶接材料だからである。On the other hand, gas-shielded arc welding wires as automatic and semi-automatic welding materials, especially flux-cored shear wires, have recently expanded significantly and are used in various fields such as steel frames, bridges, and shipbuilding. This is because flux-cored wire has good welding workability in all welding positions, including fillet welding and vertical welding, and is a welding material that provides high efficiency.
このガスシールドアーク溶接用フランクス入すワイヤは
、溶接作業性を特に重視しているため、チタニャ系フラ
ックスを充填している。このチタニャ系スラックス入り
ワイヤはアークが安定してスパッターが少なく、スラグ
のはぐり性が良く、ビード形状が良好である等あらゆる
溶接姿勢で良好な作業性が得られる。This wire for gas-shielded arc welding is filled with titania-based flux because welding workability is particularly important. This titania-based slack-cored wire has a stable arc, less spatter, good slag removal properties, and a good bead shape, providing good workability in all welding positions.
（発明が解決しようとする問題点）
しかしながら、チタニャ系フラックス入りワイヤは、溶
接作業性は良好であるが低温における靭性が充分ではな
い。チタニャ系フラックス人シワイヤの改良はこれまで
に種々なされてきておシ、特開昭５６−３９１９３号で
は、チタニャ系７ラツクスに金属弗化物、金属炭酸塩を
添加してフラックスを塩基性寄りにし、更に強膜酸剤も
添加して溶着金属の酸素量の低下を図っているが、溶着
金属の酸素量は依然高く、−２０℃以下の低温での靭性
は得られていなく、また特開昭５８−１６７９６号公報
に記載のワイヤではチタニャ系フラックスに強膜酸性元
素としてＭｇを添加しているが、低水素系被覆アーク溶
接棒で得られる低酸素量（２００〜４００ｐｐｍ程度）
の溶着金属は得られず、溶接入熱が高い場合、溶接金属
の靭性が低くなり易いという問題は解決されてない。(Problems to be Solved by the Invention) However, titania-based flux-cored wires have good welding workability, but do not have sufficient toughness at low temperatures. Various improvements have been made to the titania-based flux shear wire, and in JP-A-56-39193, metal fluorides and metal carbonates are added to the titania-based 7 lux to make the flux more basic. In addition, a sclera acid was added to reduce the amount of oxygen in the weld metal, but the amount of oxygen in the weld metal was still high, and toughness at low temperatures below -20°C was not achieved. In the wire described in Publication No. 58-16796, Mg is added to the titania-based flux as a sclera acidic element, but the amount of oxygen obtained with a low-hydrogen coated arc welding rod is low (about 200 to 400 ppm).
However, the problem that the toughness of the weld metal tends to decrease when the welding heat input is high has not been solved.
本発明は上記問題を解決し、全姿勢溶接が可能で、かつ
低温靭性の良好なガスシールドアーク溶接用フラックス
入りワイヤの提供を目的とする。The present invention aims to solve the above problems and provide a flux-cored wire for gas-shielded arc welding that is capable of welding in all positions and has good low-temperature toughness.
（問題点を解決するための手段）
本発明の要旨は、鋼を外皮鞘とする管状ワイヤに、ワイ
ヤ重量比で
ＢａＦ２ ： ４．５〜１０．３％Ｃ
ａＲ＊ Ｍｇ Ｆｚ ＋ ＡＺＦ３ ＊ ＬｉＦ の
１種又は２種以上：０．２〜３．０％
Ｍｎ ： ０．６〜３．０％Ｓｉ
：０．１〜２．５％Ｎｉ
：０．２〜３．０％Ｔ ｉ 、 Ａｌ、 Ｍ
ｇ 、 Ｚ ｒ の１種又は２種以上二０．３〜２．０
％
金属酸化物 二０．２〜３．０％金属炭酸塩
：０．２〜２．５％を含有するフラックスを充
填してなることを特徴とするガスシールドアーク溶接用
フラッフス人シワイヤにある。(Means for Solving the Problems) The gist of the present invention is to provide a tubular wire having an outer sheath made of steel, and a wire weight ratio of BaF2: 4.5 to 10.3%C.
one or more of aR* Mg Fz + AZF3 * LiF: 0.2 to 3.0% Mn: 0.6 to 3.0% Si
:0.1~2.5%Ni
:0.2-3.0% Ti, Al, M
One or more of g and Z r 20.3 to 2.0
% Metal oxide 20.2-3.0% Metal carbonate
: A fluff shear wire for gas shielded arc welding characterized by being filled with flux containing 0.2 to 2.5%.
チタニャ系フラックス入りワイヤは、全姿勢で溶接作業
性が良好であるが、低温靭性が十分でないことの１つの
理由は次のようなことであると考えられる。チタニャ系
フラックスはチタニャ（二酸化チタン、Ｔｉ０２）を多
く含み、かつ溶接作業性を調整するために、他の金属酸
化物が種々添加されている。従ってチタニャ系フラック
ス人シワイヤのアーク雰囲気中は酸素に富み、そのため
溶接金属中の酸素量が高ぐなる。溶接金属中の酸素量が
高いということは溶接金属中に色々な酸化物が多いとい
うことである。溶接金属の低温靭性を高めるためには
溶接金属の清浄度が高いことが必要だが、酸素量が多く
酸化物が多いということは清浄度が低いことであシ、十
分な借温靭性が得られない。チタニャ系フラックス入り
ワイヤの溶接金属中の酸素量は６００〜９００ ｐｐｍ
程度であり、低温靭性の良好な螢石（ＣａＦｚ）−炭酸
石灰（ＣａＣＯ３）系の低水素系、Ｖ覆アーク溶接棒の
溶接金属中の酸素量２００〜４００ ｐｐｍ程度と比べ
て格段に多い。Titania-based flux-cored wire has good welding workability in all positions, but one reason for its insufficient low-temperature toughness is thought to be as follows. Titania-based flux contains a large amount of titania (titanium dioxide, Ti02), and various other metal oxides are added to adjust welding workability. Therefore, the arc atmosphere of the titania-based flux shear wire is rich in oxygen, which increases the amount of oxygen in the weld metal. A high amount of oxygen in the weld metal means that there are many various oxides in the weld metal. To improve the low-temperature toughness of weld metal
It is necessary for the weld metal to be highly clean, but a high amount of oxygen and oxides means that the cleanliness is low, and sufficient borrowing temperature toughness cannot be obtained. The amount of oxygen in the weld metal of titania flux-cored wire is 600 to 900 ppm.
The amount of oxygen in the weld metal of a low-hydrogen V-covered arc welding rod such as fluorite (CaFz)-lime carbonate (CaCO3), which has good low-temperature toughness, is much higher than the 200 to 400 ppm.
本発明者らは、フラックス入りワイヤにおいてチタニャ
系フラックスで溶接金属の酸素量を下げることには限界
があること、低温靭性向上効果のあるニッケルを多量添
加することは充填率（全ワイヤ重量に対する７ラツクス
の重量％）と経済性の面から問題があることを考慮し、
チタニャ系以外のフラックス系を種々検討した。その結
果、全姿勢の溶接作業性と低温靭性が良好なりａＦｚ
を主体゛とする７ラツクス系を見い出した。The present inventors found that there is a limit to lowering the oxygen content of the weld metal using titania-based flux in flux-cored wires, and that adding a large amount of nickel, which has the effect of improving low-temperature toughness, is effective at filling ratio (7% relative to the total wire weight). Considering that there is a problem in terms of weight percent of Lux) and economic efficiency,
Various flux systems other than the titania system were investigated. As a result, welding workability in all positions and low-temperature toughness are good.aFz
We have discovered a 7-lux system consisting mainly of .
表１はこの間の実験結果を示すものである。外皮材とし
ては軟鋼（Ｃ：０．６５％、 Ｓｔ ： ０．０１％。Table 1 shows the experimental results during this period. Mild steel (C: 0.65%, St: 0.01%) was used as the outer skin material.
Ｍｎ ： ０．３２％、Ｐ ： ０．０１０％、Ｓ ：
０．００９％）を用い、ワイヤの共通成分として、脱
酸性元素はＭｎ ： １．７ ｚ％ 、 Ｓｔ ：
１．０％、Ｔｉ、Ａ／−およびＭｇ ：０．８％をワイ
ヤ重量あたり含有せしめ、各種金属弗化物と金属酸化物
、金属炭酸塩との組み合せを種々変えた１、６φのフラ
ックス人シワイヤを製造した。溶接は下記の条件で実施
し、溶接作業性と溶接金属のシャルピー衝撃靭性を調査
した。Mn: 0.32%, P: 0.010%, S:
0.009%), and the deoxidizing elements were Mn: 1.7 z% and St: as common components of the wire.
1.0%, Ti, A/-, and Mg: 0.8% per wire weight, and 1 and 6φ flux shear wires with various combinations of various metal fluorides, metal oxides, and metal carbonates. was manufactured. Welding was carried out under the following conditions, and the welding workability and Charpy impact toughness of the weld metal were investigated.
試験鋼板 ・・・・・・・・・・・・・・・ ５Ｍ−
５０Ｂ、２０ｍ’開先形状 ・・・・・・・・・・・・
・・・ ６０°、Ｖ開先溶接姿勢 ・・・・・・・・
・・・・・・・ 立向溶接電流 ・・・・・・・−・
・−・・−２３ＯＡ溶接電圧 ・・・・・・・・・・・
・・・・ ２５Ｖ溶接人熱 ・・・・・・・・・・
・・・・・ ３５ ＫＪ／ａｎシールドガス、流量
・・・・・ＣＯ，，２０１／分表１に示すように、溶接
作業性が良好であったのは、随４〜凰６のＢａＦｚ
を主フラックス成分とするワイヤのみで、ＣａＦｚ４る
いはＭｇＦ、を主フラックス成分とする随１〜１ｍ３．
Ｎ［Ｌ７，１ｍ８はいずれも溶接作業性が悪かった。Test steel plate ・・・・・・・・・・・・・・・ 5M-
50B, 20m' groove shape ・・・・・・・・・・・・
...60°, V groove welding posture...
・・・・・・ Vertical welding current ・・・・・・・−・
・−・・−23OA welding voltage ・・・・・・・・・・・・・
・・・・25V welding heat ・・・・・・・・・・
...35 KJ/an shielding gas, flow rate...CO,,201/min As shown in Table 1, the welding workability was good for BaFz No. 4 to No. 6.
A wire whose main flux component is CaFz4 or MgF is about 1 to 1 m3.
Both N[L7 and 1m8 had poor welding workability.
また、ＢａＦｚを主フラックス成分とするワイヤで溶接
した溶接金属の靭性はｖＥ−２０℃≧１０ｋｙｒｔｔｒ
ｔ が得られ良好であった。In addition, the toughness of weld metal welded with a wire whose main flux component is BaFz is vE-20℃≧10kyrttr
t was obtained, which was good.
次に本発明の各構成要件の作用と数値限定理由について
述べる。Next, the effects of each component of the present invention and the reasons for limiting the numerical values will be described.
（作 用）
ＢａＦ２は本発明ワイヤの主要なフシックス成分であり
、溶接金属を被包してビード形状を整え、立向溶接姿勢
でビードが垂れないように支える作用がある。ＢａＦ２
が４．５％未満ではこれらの効果が得られず、１０．３
％を超えるとスラグ過多となってビード形状が悪化しか
つスラグのはぐυ性が悪くなる。従って、ＢａＦｚは４
６５〜１０，３％の範囲がよい。(Function) BaF2 is the main fusic component of the wire of the present invention, and has the effect of enveloping the weld metal, adjusting the bead shape, and supporting the bead so that it does not sag in the vertical welding position. BaF2
If it is less than 4.5%, these effects cannot be obtained, and 10.3%
%, there will be too much slag, resulting in poor bead shape and poor slag repellency. Therefore, BaFz is 4
A range of 65 to 10.3% is preferable.
Ｃａ Ｆ２ 、 ＭｇＦ２ 、 ＡｌＦ２ 、 Ｌ Ｉ
Ｆ などの金属弗化物は溶融スラグの粘度や融点を
変えてその流動性を調整するだめのものであり、これら
金属弗化物の１種又は２種以上を添加することによりよ
り良いビード形状が得られる。ＣａＦ２ 、 ＭｇＦ２
、 ＡｌＦ２ 、 ＬＩ Ｆの１種又は２種以上が０
．２％未満ではそれらの効果がなく、３．０％を超えて
添加すると、アークが不安定となってスパッターが多く
なるので帆２〜３．０％が良い。CaF2, MgF2, AlF2, LI
Metal fluorides such as F are used to adjust the fluidity of molten slag by changing its viscosity and melting point, and by adding one or more of these metal fluorides, a better bead shape can be obtained. It will be done. CaF2, MgF2
, AlF2, LIF, one or more types are 0
．． If it is less than 2%, there is no effect, and if it exceeds 3.0%, the arc becomes unstable and spatter increases, so 2 to 3.0% is preferable.
Ｍｎは脱酸剤および合金剤としての役割があるが、Ｍｎ
が０．６％未満であると脱酸が不十分となってピット
が発生し易く、かつ溶接金属の焼入れ性が低下して溶接
金属の組織が粗くなって十分な低温靭性が得られない。Mn has a role as a deoxidizing agent and an alloying agent, but Mn
If it is less than 0.6%, deoxidation is insufficient and pits are likely to occur, and the hardenability of the weld metal decreases and the structure of the weld metal becomes coarse, making it impossible to obtain sufficient low-temperature toughness.
Ｍｎを３．０％を超えて添加すると、焼入れ性が高くな
り、溶接金属は硬くなって割れ易くなったり、低温靭性
が劣化する。従って、Ｍｎ の添加範囲は０．６〜３．
０％とする。When Mn is added in an amount exceeding 3.0%, the hardenability becomes high, the weld metal becomes hard and easily cracked, and the low-temperature toughness deteriorates. Therefore, the addition range of Mn is 0.6 to 3.
Set to 0%.
ＳｉはＭｎよりも強い脱酸剤であるが、ビード形状を整
えたり、アークを改善して溶接作業性を良くする作用が
ある。それらの効果は０．１％未満の添加では得られず
、２．５％を超えると溶接金属中にＳｉが過剰に歩留っ
て溶接金属が硬くなシ、低温靭性が劣化するので０．１
〜２．５％の添加が良い。Although Si is a stronger deoxidizing agent than Mn, it has the effect of adjusting the bead shape and improving arcing to improve welding workability. These effects cannot be obtained by adding less than 0.1%, and if it exceeds 2.5%, excessive Si remains in the weld metal, making the weld metal less hard and deteriorating low-temperature toughness. 1
It is best to add up to 2.5%.
Ｎｉ は低温靭性をよシ高めるために添加するが、０．
２％未満では低温靭性の向上効果がなく、３．０％を超
えると溶接金属が硬くなって引張強さが高くなりすぎた
り、割れ易くなるのでＮｉ の添加量は０，２〜３．０
％とする。Ni is added to improve low-temperature toughness, but 0.
If it is less than 2%, there is no effect of improving low-temperature toughness, and if it exceeds 3.0%, the weld metal becomes hard, the tensile strength becomes too high, and it becomes easy to break. Therefore, the amount of Ni added is 0.2 to 3.0%.
%.
Ｔ１ ＋ Ａ ４ Ｍｇ 、 Ｚ ｒ、などの強膜酸剤
は、アーク雰囲気あるいは溶融金属中の酸素と強力に化
合してスラグ化し、溶接金属中の酸素を低下させる。ま
た、Ｔｉ、 Ａｌ、 Ｚｒの一部は溶接金属中に歩留っ
て溶接金属の組織を微細化して低温靭性を高める作用が
ある。Ｔｉ、 Ａｔ、 Ｍｇ、 Ｚｒの１種又は２種以
上がＯ，ａＸ未満では脱酸が不十分と々ってピットが発
生し易くなったり、低温靭性が劣化したりする。A strong film oxidizing agent such as T1+A4Mg, Zr, etc. strongly combines with oxygen in the arc atmosphere or molten metal to form a slag, thereby reducing the oxygen content in the weld metal. In addition, some of Ti, Al, and Zr remain in the weld metal and have the effect of refining the structure of the weld metal and improving its low-temperature toughness. If the content of one or more of Ti, At, Mg, and Zr is less than O and aX, deoxidation is insufficient and pits are likely to occur and low-temperature toughness is deteriorated.
２．０％を昭え−ご添加するとアークが不安定となりス
パッターが多くなったり、スラグのはぐり性が劣化する
。従ってＴ ｉ、 ｋＡ、 Ｍｇ、 Ｚ ｒ、の１種又
は２種以上の添加範囲は０．３〜２．０％とする。If 2.0% is added, the arc becomes unstable, spatter increases, and slag removability deteriorates. Therefore, the addition range of one or more of Ti, kA, Mg, and Zr is 0.3 to 2.0%.
金、４酸化物としてはＳ ｉ ０２ 、 Ａｔ２０３
、 Ｔ ｉ ０２ 。Gold, 4 oxides include S i 02 , At203
, T i 02 .
ＺｒＯ２、ＭｇＯ，Ｆｅｄ、 Ｋ２０ などがあＩ）
スラグの粘性を調整してビードの形状を整えたり、アー
クを安定化させたり、アークの強さを調整したりするた
めに添加するものである。金シ【酸化物の添加量が０．
２％未満であるとそのような効果が得られず、３．０％
を超えると、アーク雰囲気中の酸素が多くなって溶接金
属中の酸素が増し、低温Ｗ性が劣化するので金属酸化物
は０．２〜３．０％の範囲が良い。ZrO2, MgO, Fed, K20 etc.)
It is added to adjust the viscosity of the slag to shape the bead, stabilize the arc, and adjust the strength of the arc. Gold [The amount of oxide added is 0.
If it is less than 2%, no such effect will be obtained, and if it is less than 3.0%
If it exceeds 0.2%, the amount of oxygen in the arc atmosphere increases and the oxygen in the weld metal increases, deteriorating the low-temperature W properties, so the metal oxide content is preferably in the range of 0.2 to 3.0%.
金属炭酸塩としては、、 Ｌ Ｔ２ ＣＯ３、Ｎａ２
ＣＯ３、ＭｇＣＯ３。As metal carbonates, L T2 CO3, Na2
CO3, MgCO3.
Ｃａ ＣＯ３、Ｓ ｒ ＣＯ３、ＢａＣＯ３ｆｋどがあ
るが、これらはアークを安定化し、ワイヤの先端で生成
した溶滴の溶融池への移行性を良好にする作用がある。These include CaCO3, SrCO3, BaCO3fk, etc., and these have the effect of stabilizing the arc and improving the transferability of droplets generated at the tip of the wire to the molten pool.
金属炭酸塩の添加量が０．２％未満ではそれらの効果は
得られず、２．５％を超えるとスパッターが多くなるの
で、金属炭酸塩の添加は０．２〜２．５％とする。If the amount of metal carbonate added is less than 0.2%, these effects will not be obtained, and if it exceeds 2.5%, spatter will increase, so the amount of metal carbonate added should be 0.2 to 2.5%. .
本発明ワイヤの主要構成は上記した通りであるが、更に
０．１〜２，５％程度のＭｏあるいは／およびＣｒ
を添加すれば強度、高温強度を向上させることができる
。また耐候性改善のために適量のＣｕ。The main composition of the wire of the present invention is as described above, but it also contains about 0.1 to 2.5% Mo or/and Cr.
By adding , strength and high temperature strength can be improved. Also, an appropriate amount of Cu is added to improve weather resistance.
Ｃｒ を添加することもできる。Cr can also be added.
ワイヤ外皮としては、通常軟鋼を用いるが用途に応じて
低合金鋼、高合金鋼をも用いることができる。Mild steel is usually used for the wire sheath, but low alloy steel or high alloy steel can also be used depending on the application.
まだ本発明ワイヤの断面形状は外皮円周部に合ずれでも
よいが、特にクローズドシームワイヤは充填フラックス
が吸湿することがないので、溶接金属の拡散性水素量が
少なく、低温割れの面で有利であり、又ワイヤ表面に銅
メッキが施せるため、通電性や送給性にすぐれる利点が
ある。Although the cross-sectional shape of the wire of the present invention may not match the circumference of the outer skin, the closed seam wire in particular does not absorb moisture from the filling flux, so the amount of diffusible hydrogen in the weld metal is small, which is advantageous in terms of low-temperature cracking. Moreover, since the surface of the wire can be plated with copper, it has the advantage of excellent current conductivity and feeding performance.
本発明を更に具体的に説明するために以下に実施例を述
べる。Examples will be described below to further specifically explain the present invention.
（実施例）
外皮材として軟鋼（Ｃ： ０．０ヰ５％、 Ｓｔ ：
０．０１％、 Ｍｎ ： ０．３２％、ｐ ： ｏ、ｏ
ｘｏＨ，Ｓ：０．００９％）を用い、表２に示すような
ワイヤ径１．６φのフラックス人シワイヤを製造した。(Example) Mild steel (C: 0.0ヰ5%, St:
0.01%, Mn: 0.32%, p: o, o
xoH, S: 0.009%), a flux wire with a wire diameter of 1.6φ as shown in Table 2 was manufactured.
溶接は下記の条件で実施し、溶接作業性と溶接金属の性
能を調査した。Welding was carried out under the following conditions, and the welding workability and performance of the weld metal were investigated.
試験鋼板 ５Ｍ−５０Ｂ、２０ｍ’開先形
状 ・・・・・・・・・・・・ ６０；Ｖ開先溶接
姿勢 ・・・・・・・・・・・・ 立向溶接電流
・・・・−・・・・・・・ ２３０Ａ溶接電圧
・・・・・・・・・・・・ ２５Ｖ溶接人熱
３５ＫＪ／ｃｍシールドガス、流量・・・・・・
ＣＯ２，２０ｔ／分表２に示すように、本発明ワイヤ鳩
１〜麹１０け、チタニャ系フラックス入りワイヤと較べ
て溶接金属中の酸素量が格段に低く、溶接金属の衝撃値
についてはＶＥ−２０℃≧１１．１ 吟ｆ、ｍ 、かつ
ｖＥ−４０℃≧７．ｌｋ７ｆ０ｍで良好である。また溶
接作業性についてもＮＩＩＬＩ〜曵１０の本発明ワイヤ
は良好であった。Test steel plate 5M-50B, 20m' groove shape ・・・・・・・・・・・・ 60; V groove welding posture ・・・・・・・・・ Vertical welding current
・・・・・・・・・・・・・・・ 230A welding voltage
・・・・・・・・・・・・ 25V welding heat
35KJ/cm shielding gas, flow rate...
CO2, 20t/min As shown in Table 2, the amount of oxygen in the weld metal for the wires of the present invention is much lower than that of titania-based flux-cored wires, and the impact value of the weld metal is VE- 20℃≧11.1 ginf, m, and vE-40℃≧7. lk7f0m is good. In addition, the wires of the present invention of NIILI to 10 had good welding workability.
次に比較ワイヤについて説明する。Next, the comparison wire will be explained.
Ｎａ１ｌけＢ ａ Ｆ２が少なく 、ＣａＦ２． Ｍｇ
Ｆ２． ＡｔＦ３＋ＬｉＦが過剰のため、立向溶接でス
ラグの流動性が過多で溶接金属が垂れ易く、溶接作業性
に難点がある。There is less Na1l, B a F2, and CaF2. Mg
F2. Due to the excess amount of AtF3+LiF, the fluidity of the slag is excessive during vertical welding, and the weld metal tends to sag, creating difficulties in welding workability.
随１２は、ＢａＦ２が過剰でＳｉが少ない場合であるが
、ビード形状が凸となり、まだスラグのはぐり性が悪化
してやはり溶接作業性の面に難点がある。Case 12 is a case where BaF2 is excessive and Si is small, but the bead shape becomes convex and the slag peeling property is still deteriorated, so there is still a problem in terms of welding workability.
随１３は、Ｍｎが過剰のために１溶接金属の焼入れ性が
高１って溶接金属が硬化し、衝撃値が低下した。In No. 13, the hardenability of the weld metal was high due to excess Mn, which caused the weld metal to harden and the impact value to decrease.
Ｎ［Ｌｉ２は、Ｓｌ が多いために、Ｓｉが溶接金属に
過剰に走留って溶接金属が硬化し、衝撃値が低下した。Since N[Li2 contains a large amount of Sl, Si excessively ran into the weld metal, hardening the weld metal and reducing the impact value.
又金属酸化物が少ないために、立向溶接でスラグが流れ
易くなシ、溶接金属が垂れ易い。Also, since there is little metal oxide, slag does not flow easily during vertical welding, and weld metal tends to drip.
階１５は、Ｍｎ が少ないために、溶接金属の焼入れ性
が不足して衝撃値が低く、かつ、Ｔｉ、Ａｚ。Floor 15 has a low impact value due to insufficient hardenability of the weld metal due to low Mn, and also contains Ti and Az.
Ｍｇ、Ｚｒが過剰のためＫそれらの酸化物がスラグ中に
多く生成され、スラグのはくシ性が悪化した。Due to the excess of Mg and Zr, a large amount of K and their oxides were produced in the slag, and the slag's deformability deteriorated.
またスパッターも多発した。Also, spatter occurred frequently.
随１６は、Ｔ ｉ 、 Ａ ４ Ｍ ｇ 、 Ｚ ｒ
カ少’ｌ イタａ６ Ｋ 溶接金属の酸素量が多くなっ
て、衝撃値が低い。又、ＣａＦ２． ＭｇＦ２． Ａｔ
Ｆ３． ＬｉＦが少ないだめに、スラグの流動性が悪く
、ビード形状が凸となった。Encyclopedia 16 is T i , A 4 M g , Z r
A6 K The amount of oxygen in the weld metal increases, resulting in a low impact value. Also, CaF2. MgF2. At
F3. Since the LiF content was low, the fluidity of the slag was poor and the bead shape became convex.
随１７は金属酸化物が多いために溶接金属中の酸素量が
増加して衝撃値が低い。又炭６ツ塩が少ないために安定
したアークと溶滴の移行が得られない。No. 17 has a large amount of metal oxide, so the amount of oxygen in the weld metal increases and the impact value is low. In addition, stable arc and droplet transfer cannot be obtained due to the small amount of charcoal salt.
随１８は、金属炭酸塩が過剰のために、スパッターが多
発し、寸たスラグの粘性が大きくなってピードが凸とな
り形状が悪化した。更に溶接金属の衝撃値はＮｉが少な
いために低い。In No. 18, due to excessive metal carbonate, spatter occurred frequently, the viscosity of the slag increased, the peads became convex, and the shape deteriorated. Furthermore, the impact value of the weld metal is low due to the low Ni content.
順１９はＮｉ が多いために溶接金属が硬くなって引
張強さが７０ ｋりｆ ／−を超え、Ｍ［の引張強さと
のバランスが悪い。またＮｉが多い割に衝撃値の向上効
果が少なく、Ｎｉ粉が高価であることを考えると不経済
である。In No. 19, the weld metal becomes hard due to the large Ni content, and the tensile strength exceeds 70 kf/-, which is poorly balanced with the tensile strength of M[. Furthermore, although the amount of Ni is large, the effect of improving the impact value is small, and considering that Ni powder is expensive, it is uneconomical.
（発明の効果）
以上説明したように、本発明フラックス入りワイヤによ
れば、溶接金属の酸素量が格段に低減して良好な低温靭
性が得られ、溶接部の信頼性向上に貢献するものである
。(Effects of the Invention) As explained above, according to the flux-cored wire of the present invention, the amount of oxygen in the weld metal is significantly reduced, good low-temperature toughness is obtained, and this contributes to improving the reliability of the welded joint. be.
代理人 弁理士 秋 沢 政 光 他２名Agent Patent Attorney Masaaki Akizawa 2 others
Claims (1)
、 ＢａＦ＿２：４．５〜１０．３％ ＣａＦ＿２、ＭｇＦ＿２、ＡｌＦ＿３、ＬｉＦの１種又
は２種以上：０．２〜３．０％ Ｍｎ：０．６〜３．０％ Ｓｉ：０．１〜２．５％ Ｎｉ：０．２〜３．０％ Ｔｉ、Ａｌ、Ｍｇ、Ｚｒの１種又は２種以上：０．３〜
２．０％ 金属酸化物：０．２〜３．０％ 金属炭酸塩：０．２〜２．５ を含有するフラックスを充填してなることを特徴とする
ガスシールドアーク溶接用フラックス入りワイヤ。(1) A tubular wire with a steel outer sheath, wire weight ratio: BaF_2: 4.5 to 10.3%, one or more of CaF_2, MgF_2, AlF_3, and LiF: 0.2 to 3.0 % Mn: 0.6-3.0% Si: 0.1-2.5% Ni: 0.2-3.0% One or more of Ti, Al, Mg, and Zr: 0.3-
A flux-cored wire for gas-shielded arc welding, characterized in that it is filled with a flux containing 2.0% metal oxide: 0.2-3.0% and metal carbonate: 0.2-2.5%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP519486A JPS62166098A (en) | 1986-01-14 | 1986-01-14 | Flux-cored wire for gas shielded arc welding |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP519486A JPS62166098A (en) | 1986-01-14 | 1986-01-14 | Flux-cored wire for gas shielded arc welding |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS62166098A true JPS62166098A (en) | 1987-07-22 |
Family
ID=11604402
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP519486A Pending JPS62166098A (en) | 1986-01-14 | 1986-01-14 | Flux-cored wire for gas shielded arc welding |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS62166098A (en) |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01271098A (en) * | 1988-04-21 | 1989-10-30 | Nippon Steel Corp | Flux cored wire for gas shielded arc welding |
| JP2006187805A (en) * | 2005-01-03 | 2006-07-20 | Lincoln Global Inc | Cored electrode for reducing diffusible hydrogen |
| CN100457372C (en) * | 2007-04-27 | 2009-02-04 | 北京工业大学 | Refractory steel alkaline flux-cored wire with excellent removability of slag |
| US8907248B2 (en) | 2007-05-03 | 2014-12-09 | Illinois Tool Works Inc. | Aluminum deoxidizing welding wire |
| US9517523B2 (en) | 2010-04-09 | 2016-12-13 | Illinois Tool Works Inc. | System and method of reducing diffusible hydrogen in weld metal |
| WO2017013965A1 (en) * | 2015-07-17 | 2017-01-26 | 株式会社神戸製鋼所 | Wire containing flux for gas shield arc welding |
| US9700955B2 (en) | 2011-04-04 | 2017-07-11 | Illinois Tool Works Inc. | Systems and methods for using fluorine-containing gas for submerged arc welding |
| US9700954B2 (en) | 2012-03-27 | 2017-07-11 | Illinois Tool Works Inc. | System and method for submerged arc welding |
-
1986
- 1986-01-14 JP JP519486A patent/JPS62166098A/en active Pending
Cited By (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01271098A (en) * | 1988-04-21 | 1989-10-30 | Nippon Steel Corp | Flux cored wire for gas shielded arc welding |
| JP2006187805A (en) * | 2005-01-03 | 2006-07-20 | Lincoln Global Inc | Cored electrode for reducing diffusible hydrogen |
| CN100457372C (en) * | 2007-04-27 | 2009-02-04 | 北京工业大学 | Refractory steel alkaline flux-cored wire with excellent removability of slag |
| US9604315B2 (en) | 2007-05-03 | 2017-03-28 | Illinois Tool Works Inc. | Aluminum deoxidizing welding wire |
| US9162323B2 (en) | 2007-05-03 | 2015-10-20 | Illinois Tool Works Inc. | Aluminum deoxidizing welding wire |
| US8907248B2 (en) | 2007-05-03 | 2014-12-09 | Illinois Tool Works Inc. | Aluminum deoxidizing welding wire |
| US9517523B2 (en) | 2010-04-09 | 2016-12-13 | Illinois Tool Works Inc. | System and method of reducing diffusible hydrogen in weld metal |
| US9700955B2 (en) | 2011-04-04 | 2017-07-11 | Illinois Tool Works Inc. | Systems and methods for using fluorine-containing gas for submerged arc welding |
| US9764409B2 (en) | 2011-04-04 | 2017-09-19 | Illinois Tool Works Inc. | Systems and methods for using fluorine-containing gas for submerged arc welding |
| US9700954B2 (en) | 2012-03-27 | 2017-07-11 | Illinois Tool Works Inc. | System and method for submerged arc welding |
| US9821402B2 (en) | 2012-03-27 | 2017-11-21 | Illinois Tool Works Inc. | System and method for submerged arc welding |
| WO2017013965A1 (en) * | 2015-07-17 | 2017-01-26 | 株式会社神戸製鋼所 | Wire containing flux for gas shield arc welding |
| JP2017024032A (en) * | 2015-07-17 | 2017-02-02 | 株式会社神戸製鋼所 | Flux-cored wire for gas shielded arc welding |
| KR20180016569A (en) | 2015-07-17 | 2018-02-14 | 가부시키가이샤 고베 세이코쇼 | Flux cored wire for gas shield arc welding |
| CN107848082A (en) * | 2015-07-17 | 2018-03-27 | 株式会社神户制钢所 | Flux-cored wire for gas-shielded arc welding |
| CN107848082B (en) * | 2015-07-17 | 2020-09-04 | 株式会社神户制钢所 | Flux-cored wire for gas-shielded arc welding |
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