JPS62183996A - Fused flux for horizontal fillet submerged arc welding - Google Patents
Fused flux for horizontal fillet submerged arc weldingInfo
- Publication number
- JPS62183996A JPS62183996A JP2724186A JP2724186A JPS62183996A JP S62183996 A JPS62183996 A JP S62183996A JP 2724186 A JP2724186 A JP 2724186A JP 2724186 A JP2724186 A JP 2724186A JP S62183996 A JPS62183996 A JP S62183996A
- Authority
- JP
- Japan
- Prior art keywords
- flux
- welding
- bead
- al2o3
- total
- 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 abstract description 42
- 230000004907 flux Effects 0.000 title claims abstract description 37
- 239000011324 bead Substances 0.000 abstract description 36
- 239000002184 metal Substances 0.000 abstract description 18
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N Titan oxide Chemical compound O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 abstract description 12
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 abstract description 11
- 229910052593 corundum Inorganic materials 0.000 abstract description 11
- 229910001845 yogo sapphire Inorganic materials 0.000 abstract description 11
- WUKWITHWXAAZEY-UHFFFAOYSA-L calcium difluoride Chemical compound [F-].[F-].[Ca+2] WUKWITHWXAAZEY-UHFFFAOYSA-L 0.000 abstract description 9
- 229910001634 calcium fluoride Inorganic materials 0.000 abstract description 9
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 abstract description 8
- 229910052681 coesite Inorganic materials 0.000 abstract description 4
- 229910052906 cristobalite Inorganic materials 0.000 abstract description 4
- 239000000377 silicon dioxide Substances 0.000 abstract description 4
- 235000012239 silicon dioxide Nutrition 0.000 abstract description 4
- 229910052682 stishovite Inorganic materials 0.000 abstract description 4
- 229910052905 tridymite Inorganic materials 0.000 abstract description 4
- NUJOXMJBOLGQSY-UHFFFAOYSA-N manganese dioxide Chemical compound O=[Mn]=O NUJOXMJBOLGQSY-UHFFFAOYSA-N 0.000 abstract 4
- 239000002893 slag Substances 0.000 description 15
- 229910000831 Steel Inorganic materials 0.000 description 11
- 230000000694 effects Effects 0.000 description 11
- 239000010959 steel Substances 0.000 description 11
- 238000002844 melting Methods 0.000 description 9
- 230000008018 melting Effects 0.000 description 8
- 239000002245 particle Substances 0.000 description 8
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 6
- 239000001257 hydrogen Substances 0.000 description 6
- 229910052739 hydrogen Inorganic materials 0.000 description 6
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 6
- 230000003449 preventive effect Effects 0.000 description 6
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 5
- 239000001301 oxygen Substances 0.000 description 5
- 229910052760 oxygen Inorganic materials 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 3
- 239000000470 constituent Substances 0.000 description 3
- 238000009863 impact test Methods 0.000 description 3
- 239000003915 liquefied petroleum gas Substances 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 238000005336 cracking Methods 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 239000006260 foam Substances 0.000 description 2
- 230000004927 fusion Effects 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 230000000087 stabilizing effect Effects 0.000 description 2
- -1 TiO20s Inorganic materials 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 238000004817 gas chromatography Methods 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 238000009413 insulation Methods 0.000 description 1
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N iron oxide Inorganic materials [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 235000013372 meat Nutrition 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000005070 sampling Methods 0.000 description 1
- 210000002966 serum Anatomy 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
- OGIDPMRJRNCKJF-UHFFFAOYSA-N titanium oxide Inorganic materials [Ti]=O OGIDPMRJRNCKJF-UHFFFAOYSA-N 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Landscapes
- Nonmetallic Welding Materials (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は、低温用鋼の潜弧溶接に用いるフラックスに係
わり、さらに詳しくは、高靭性な溶接金属を得、かつ高
速度の溶接をする際に用いられる水平すみ肉潜弧溶接用
溶融型フランクスに関するものである。Detailed Description of the Invention (Industrial Application Field) The present invention relates to a flux used for submerged arc welding of low-temperature steel, and more specifically, to obtain a high-toughness weld metal and perform high-speed welding. This relates to fusion type flanks for horizontal fillet submerged arc welding.
（従来の技術）
近年、液化石油ガス（ＬＰＧ”）の有用性が増すととも
に、多く建造されるようになったＬＰＧタンク、あるい
は寒冷地での油田開発用などの海洋構造物に、低温靭性
の優れた鋼材が使用されている。(Prior art) In recent years, as the usefulness of liquefied petroleum gas (LPG) has increased, low-temperature toughness has been applied to LPG tanks, which have been constructed in large numbers, and offshore structures for oil field development in cold regions. High quality steel is used.
これらの構造物では、低温条件下での溶接部に高い靭性
か求められ、潜弧溶接法も適宜使用されている。In these structures, high toughness is required for welded parts under low-temperature conditions, and submerged arc welding is also appropriately used.
最近はさらに、溶接の能率化も求められており、水平す
み肉溶接の高速化もそのひとつにあげられている。しか
し従来は、溶接部の要求靭性を確保するにとどまり、高
速性はもちろんビード外観やスラグ剥離にも、下記のよ
うな問題があり、これらを解決するフラックスの提供が
強く望まれていた。Recently, there has also been a demand for more efficient welding, and one example of this is increasing the speed of horizontal fillet welding. However, in the past, only the required toughness of the welded part was ensured, and there were the following problems not only in high speed but also in bead appearance and slag peeling, and there was a strong desire to provide a flux that would solve these problems.
すなわち、高いＯｆＩ撃靭性の溶接金属が得られる水平
すみ肉溶接用焼成型フラックスが、特開昭５８−１９６
１９５号公報に提案されている。このフラックスは、Ｍ
ｇＯ成分を多く含有させ、高塩基性とすることで、高靭
性を得ているが、母材とビードとの接触角が大きないわ
ゆる凸ビードとなったり、アンダカットが発生しやすい
。特に１ ｍ／ｍｉｎを超える溶接速度では、この傾向
が強く現われ、溶接の能率化は成し得す、このことは焼
成型フラックス全般にいえる大きな欠点でもある。That is, a firing type flux for horizontal fillet welding that can obtain weld metal with high OfI impact toughness was disclosed in Japanese Patent Application Laid-Open No. 58-196.
This is proposed in Publication No. 195. This flux is M
Although high toughness is obtained by containing a large amount of gO component and making the bead highly basic, the contact angle between the base material and the bead is large, resulting in a so-called convex bead, and undercutting is likely to occur. This tendency is particularly strong at welding speeds exceeding 1 m/min, and welding efficiency cannot be improved, which is a major drawback of sintered fluxes in general.
また、高靭性が得られる溶融型フラックスは。In addition, there is a melt-type flux that provides high toughness.
特開昭４９−５１３３６号公報や特公昭６０−５３９６
号公報などに提案されている。しかしこれらフラックス
は、下向突合せ溶接用に開発されたもので、塩基性成分
やＣａＦ２成分を多（含有するため、スラグが流れやす
（、水平すみ肉溶接に適用した場合、垂れやすいビード
形状、粗いビードの波目などのビード外観や、スラグ剥
離性などに問題がある。Japanese Patent Publication No. 49-51336 and Japanese Patent Publication No. 60-5396
It has been proposed in the Publication No. However, these fluxes were developed for downward butt welding, and because they contain a large amount of basic components and CaF2 components, slag tends to flow (and when applied to horizontal fillet welding, the bead shape tends to sag). There are problems with bead appearance such as rough bead wavy patterns and slag removability.
一方、本発明者らは、先に特願昭６０−１６８５５４号
において、すみ肉の高速溶接が可能な潜弧溶接用溶融型
フラックスを提案した。このフラックスは、Ｓ ｉｏ、
を低（したことおよびＡ４０３、ＴｉＯ２゜１ＶｆｎＯ
成分を比較的に多く含有したことで、高速溶接を可能と
したもので、溶接能率の著しい向上をもたらした。On the other hand, the present inventors previously proposed in Japanese Patent Application No. 60-168554 a melting type flux for submerged arc welding that is capable of high-speed welding of fillets. This flux is S io,
low (and A403, TiO2゜1VfnO
The relatively high content of these ingredients made it possible to perform high-speed welding, resulting in a significant improvement in welding efficiency.
しかし、防錆剤塗布鋼板での耐ピツト性が、Ｓｔｏｗの
特に低い場合およびＣａＯ、ＭｇＯ、ＢａＯの塩基性成
分含有量によっては、問題のあることが判明した。さら
には、高い衝繋靭性、たとえば−６０℃で３．５Ｋｇ−
ｍ以上を得られない場合のあることがわかり、低温用鋼
への適用には問題があった。However, it has been found that the pit resistance of the rust preventive-coated steel sheet is problematic depending on the case where the Stow is particularly low and the content of basic components such as CaO, MgO, and BaO. Furthermore, it has high impact toughness, e.g. 3.5Kg at -60℃.
It was found that there were cases where it was not possible to obtain more than m, and there was a problem in application to low-temperature steel.
このように、高靭性の溶接金属が得られ、かつ水平すみ
肉に適用でき、しかも高速溶接が可能な潜弧溶接用フラ
ックスが従来はなかった。As described above, there has been no flux for submerged arc welding that can produce high-toughness weld metal, can be applied to horizontal fillets, and can perform high-speed welding.
（発明が解決しようとする問題点）
本発明は、上記従来技術の問題点を解決するもので、そ
の目的は、高靭性な溶接金属が得られるとともに、従来
よりも高速度の溶接条件において、防錆剤塗布鋼板を使
用した場合でも、ピットやポックマークが発生せず、ア
ンダカットやオーバラップのないフラットなビード断面
形状と、均一で細かいビード波形を得ることができる水
平すみ肉清弧溶接用フラックスを提供することにある。(Problems to be Solved by the Invention) The present invention solves the above-mentioned problems of the prior art.The purpose of the present invention is to obtain a weld metal with high toughness, and to achieve a welding speed under higher speed welding conditions than before. Horizontal fillet clear arc welding allows you to obtain a flat bead cross-sectional shape without pits or pockmarks, no undercuts or overlaps, and a uniform, fine bead waveform even when using rust preventive-coated steel sheets. The aim is to provide flux for use.
（問題点を解決するだめの手段）
本発明者らは、先に特願昭６０−１６８５５４号で提案
した浦弧溶接用溶融型フラックスの特長、すなわちすみ
内継手の高速沼接性を維持しつつ、防錆剤塗布鋼板にお
いても良好な耐ピット性を有し、さらに高靭性なｄ接金
類が得られるフラックスの成分組成について、検討を続
けた。(Means for Solving the Problem) The present inventors have maintained the feature of the fusion type flux for arc welding previously proposed in Japanese Patent Application No. 168554/1983, that is, the high-speed weldability of corner joints. At the same time, we continued to study the composition of a flux that would provide good pit resistance even in rust preventive-coated steel sheets and provide highly tough d-welds.
その結果、ＳｉＯ□を単純に多く含有させた場合、耐ピ
ツト性は改善されるが、溶接金属の靭性は劣化し、また
ＣａＯ、ＭｇＯ１ＢａＯの塩基性成分やＣａＦ。As a result, if a large amount of SiO□ is simply added, the pit resistance is improved, but the toughness of the weld metal is degraded, and basic components such as CaO, MgO1BaO, and CaF.
を単純に多（含有させた場合は、溶接金属の高靭性化は
可能であったが、ビード外観やスラグ剥離性等が劣化し
、高速性を大きく阻害することがわかった。特にこれら
塩基性成分の含有量が特定量以上では、防錆剤塗布鋼板
におけるピットの発生が防止できなかった。Although it was possible to increase the toughness of the weld metal by simply adding a large amount of If the content of the component exceeds a certain amount, the occurrence of pits in the rust preventive coated steel plate could not be prevented.
よって、これら塩基性成分やＣａＦ、は、その悪影響が
出にくい比較的に少ない含有量で、高靭性の得られる成
分組成を求めるべ（詳しく検討した。Therefore, it is necessary to find a component composition that can provide high toughness with a relatively low content of these basic components and CaF, which is less likely to have an adverse effect (detailed study was conducted).
まず、第１表に示すフラックス組成Ａ、 Ｂ、 Ｃの３
種類をベースとして、ＣａＯ、ＭｇＯ１ＢａＯの合計は
、５％、１０％、１５％で一定とし、Ａ４０３含有量を
種々変化させ、それに応じＣ５ｉＯｚ 、 Ｍｎ０１Ｔ
ｉＯｚ 、ＣａＦ２その他の各成分は比例配分で増減さ
せたフラックスで、溶接金属の衝撃性能を調貸し、得ら
れた結果が第１図である。First, the three flux compositions A, B, and C shown in Table 1 are used.
Based on the type, the total of CaO, MgO1BaO is fixed at 5%, 10%, and 15%, and the A403 content is varied, and C5iOz, Mn01T is changed accordingly.
The impact performance of the weld metal was adjusted by adjusting the flux of iOz, CaF2, and other components in proportional proportions, and the results obtained are shown in Figure 1.
これより、Ａ４０ａを多く含有すれば、Ｓ ｉｏｚが多
く、塩基性成分が少量であっても、高靭性が得られるこ
とを見い出した。なお、試験方法は、第２表に示すワイ
ヤ、第３表に示すＰ２鋼板を用い、第２図（ａ）に示す
Ｖ溝の開先（ｄ＝１０１３１３１、θ７＝６０°）とし
て、第４表に示すＢ条件により２パス盛溶接し、第２図
（ｂ）に示すｈ＝２１３ＥＩＩ＋の位置から、ＪＩＳＡ
号シャルピー衝撃試験片を採取して調べた。From this, it has been found that if a large amount of A40a is contained, high toughness can be obtained even if Sioz is large and the basic component is small. The test method was to use the wire shown in Table 2 and the P2 steel plate shown in Table 3, with the V-groove groove (d=1013131, θ7=60°) shown in FIG. Two-pass welding was performed under the B conditions shown in the table, and JISA
No. Charpy impact test specimens were collected and examined.
第１表
第２表
第３表
第４表
次に、１４０３とＴｉｅ、の合計が特定量以上含有する
と、溶接中のアーク安定性を向上させることがわかった
。これにより、溶接金属中の酸素量低減に効果のあるＣ
ａＦｚを、Ａ４０ｓとＴｉＣｈ の合計に対し特定割合
とすることで、比較的に多く含有させた場合でも、ビー
ド外観上の問題を生じることな（高靭性な溶接金属が得
られることもわかった。Table 1 Table 2 Table 3 Table 4 Next, it has been found that when the total of 1403 and Tie is contained in a specific amount or more, arc stability during welding is improved. As a result, C is effective in reducing the amount of oxygen in weld metal.
It has also been found that by setting aFz at a specific ratio to the total of A40s and TiCh, a weld metal with high toughness can be obtained without causing problems in bead appearance even when it is contained in a relatively large amount.
なお、従来の軽石状フラックスは、内部気孔の少ない比
較的に緻密な粒子と、過度に発泡した粒子とが混在して
いるため、溶接時にフラックス粒子の溶融か均一ではな
く、特に高速度の溶接で、ビードの波目が粗くなったり
、赴端の不揃いが見られた。In addition, conventional pumice-like flux has a mixture of relatively dense particles with few internal pores and excessively foamed particles, so the flux particles do not melt uniformly during welding, especially during high-speed welding. However, the wavy texture of the beads became rough, and the edges of the beads were found to be uneven.
しかし、Ａ４０３とＴｉ１ｔの合計が特定量以上である
と、Ｓｔｏｗの含有を多（した場合でも、個々の７ラツ
クス粒子が均一に発泡し、これがビード外観の一層の向
上に寄与することもわかった。However, it was also found that when the sum of A403 and Ti1t exceeds a certain amount, even if the Stow content is high, the individual 7lux particles foam uniformly, which contributes to further improvement in the bead appearance. .
また、５ｉＯｚ、ＭｎＯの特定量を含有させることで、
Ａｌ２Ｏ３とＴｉＯ２０ｓとＴｉＯ２を多く含有するこ
とによる過度の融点上昇を抑え、ビード形成時のスラグ
粘性を調整でき、優れたビード外観を得られることがわ
かった。特にＳｔｏｗは、防錆剤塗布鋼板の場合の耐ピ
ツト性改善に重要であった。さらに、Ｂ２Ｏ３の含有に
よっても靭性の向上が可能で、溶接入熱の大きい場合は
特に有益であった。In addition, by containing a specific amount of 5iOz and MnO,
It was found that by containing a large amount of Al2O3, TiO20s, and TiO2, it was possible to suppress the excessive rise in melting point, adjust the slag viscosity during bead formation, and obtain an excellent bead appearance. In particular, Stow was important for improving pit resistance in the case of rust preventive coated steel sheets. Furthermore, the toughness can also be improved by including B2O3, which is particularly beneficial when the welding heat input is large.
本発明は、以上の知見をもとにして、従来フラックスの
問題点を解決したものである。即ち、本発明の要旨とす
るところは、成分が重量％で、Ａ４０ｇ ： ２５％超
４５％以下、Ｔｉ１ｔ ： １４％以上４０％以下、Ｍ
ｎＯ： ｌ Ｏ％超３５％以下、５ｉｆｔ ：８％超３
２％以下、ＣａＦ、 ： ３％以上１６％以下を必須成
分として含有し、ＣａＯ、ＩｖｌｇＯおよびＢａＯの合
計：１３％未満、Ａｌｘ ＯｓとＴｉ１ｔの合計：４２
％以上（Ａｌ２Ｏ３とＴｉＯｔＯｓとＴｉ１ｔの合計）
／ ＣａＦ、比＝４．Ｏ超であり、かさ密度が０．６
〜１．３ｆ／ｌｙｍ”、またはこれにさらに、Ｂ２Ｏ３
を０．１％以上１．２％以下含有することを特徴とする
水平すみ肉浦弧溶接用浴融型フラックスにある。The present invention solves the problems of conventional fluxes based on the above knowledge. That is, the gist of the present invention is that the components are expressed in weight percent, A40g: more than 25% and less than 45%, Ti1t: 14% and more and less than 40%, M
nO: l O% over 35%, 5ift: over 8% 3
Contains 2% or less, CaF: 3% or more and 16% or less as an essential component, total of CaO, IvlgO and BaO: less than 13%, total of Alx Os and Ti1t: 42
% or more (total of Al2O3, TiOtOs and Ti1t)
/CaF, ratio=4. O, and the bulk density is 0.6
~1.3f/lym”, or additionally B2O3
A bath-melting flux for horizontal fillet arc welding is characterized by containing 0.1% or more and 1.2% or less of.
以下、本発明の構成要件を、作用とともに詳述する。Hereinafter, the constituent elements of the present invention will be explained in detail along with their effects.
（作用）
まず、Ａ４０ａは溶接金属の酸素量を増大させることな
く、Ｓ ｉｏｚと同様のビード形成能を持つ成分として
多く含有させるもので、２５％を超え４５係以下の範囲
とする必要がある。Ａｌ２Ｏ３とＴｉＯｔ Ｏｘが２５
係以下では、ＳｉＯ２やＭｎＯを多（含有した場合、溶
接金属の酸素量が多くなるため高靭性は得られない。(Function) First, A40a is a component that has the same bead-forming ability as Sioz and should be contained in large amounts without increasing the amount of oxygen in the weld metal, and must be in the range of more than 25% and less than 45%. . Al2O3 and TiOtOx are 25
If the weld metal contains a large amount of SiO2 or MnO, the amount of oxygen in the weld metal increases and high toughness cannot be obtained.
また、Ａｌ２Ｏ３とＴｉＯ２０３が４５％を超えて含有
すると、融点が高くなり過ぎ、スラグの凝固が速くなる
ため、浴接アークにより母材、ワイヤ、フラックスとの
反応で、発生するＣＯｔガス等の放出を妨げて、ポック
マークが生ずる。In addition, if Al2O3 and TiO203 are contained in excess of 45%, the melting point will become too high and the slag will solidify quickly, resulting in the release of COt gas, etc. generated by the reaction with the base metal, wire, and flux due to the bath welding arc. This causes pockmarks.
次に、Ｔｉ０ｚはＡＬ２０ｓ同様に、融点を高める作用
があるとともに、安定したアークを発生させ、フラット
なビード断面形状が得られ、ビードの波形を均一にする
効果がある。しかし、Ｔｉ１ｔが１４％未満では、これ
らの効果は得られず、さらに、スラグの剥離性を悪化さ
せ、作業能率の低下を招（。Next, like AL20s, Ti0z has the effect of increasing the melting point, generates a stable arc, obtains a flat bead cross-sectional shape, and has the effect of making the bead waveform uniform. However, if Tilt is less than 14%, these effects cannot be obtained, and furthermore, the slag removability deteriorates, leading to a decrease in work efficiency.
また、４０％を超えて含有させた場合には、高融点とな
り過ぎること、およびスラグの導電性が増してアークが
細く絞られることにより、ア／ダカットが発生するとと
もに、ビード断面が凸形となるなど、ビード外観上の問
題を生ずる。In addition, if the content exceeds 40%, the melting point becomes too high, the conductivity of the slag increases, and the arc is narrowed, resulting in a/da cut and the bead cross section becoming convex. This may cause problems with the appearance of the bead.
また、Ａ４０３とＴ ｉ Ｏｘの合計を４２％以上とす
る必要がある。これにより、アークの安定性が非常に良
くなり、アーク安定性を悪化させるか、靭性向上に効果
のあるＣａＦ、を多く含有させることかり能となる。Further, the total content of A403 and T i Ox needs to be 42% or more. As a result, the stability of the arc becomes very good, and it becomes possible to contain a large amount of CaF, which is effective in deteriorating arc stability or improving toughness.
Ａｌ２Ｏ３とＴｉＯｔ ＯｘとＴｉＯ□の合計が４２％
未満の場合−アーク電圧の変動が大きくなりスラグ巻込
みが発生する。また、フラックス粒子が均一な軽石状と
ならずに１発泡の少ない淑密な粒子も含むようになるた
め、ビードの波目が粗（なったり、ピード赴端部の揃い
が悪くなる。Al2O3 and TiOt The total of Ox and TiO□ is 42%
If it is less than - fluctuations in arc voltage become large and slag entrainment occurs. In addition, the flux particles do not have a uniform pumice-like shape, but also include dense particles with few bubbles, resulting in rough undulations of the bead and poor alignment of the bead ends.
さらに、５ｉＯｚの含有は、Ａｌ２Ｏ３とＴｉＯｔ Ｏ
ｓとＴｉ１ｔを多く含有することによる過度の融点上昇
を抑え、ポックマークやア／ダカットが発生しにく（な
るほか、拡散性水素量を低減し、ピットや割れの欠陥を
防止する。しかし、３２％を超えて含有させると、溶接
金属の酸素量が多くなるため、高靭性は得られない。ま
た、Ｓ ｉｏ、が８％以下では、拡散性水素量が増大し
、防錆剤塗布鋼板の高速すみ肉溶接でピットを生ずる。Furthermore, the content of 5iOz is similar to that of Al2O3 and TiOtO
By containing a large amount of S and Ti1t, the excessive rise in melting point is suppressed, and pock marks and a/da cuts are less likely to occur (in addition, the amount of diffusible hydrogen is reduced and defects such as pits and cracks are prevented. However, If the content exceeds 32%, the amount of oxygen in the weld metal will increase, making it impossible to obtain high toughness.In addition, if Sio is less than 8%, the amount of diffusible hydrogen will increase, and the rust preventive coated steel sheet High-speed fillet welding causes pits.
ＭｎＯも、ＳｉＯ２と同様に融点の上昇を抑え、良好な
ビード外観を得るために必要な成分で、１０％を超え３
５％以下とする必要がある。１０％以下ではこれらの効
果が小さく、アンダカットが発生しビードの波目も粗く
なる。逆に多く含有し、３５係を超えると融点を下げ過
ぎ、ビード断面形状が凸形状となり、良好なフラット形
状は得られない。Like SiO2, MnO is also a necessary component to suppress the increase in melting point and obtain a good bead appearance, and if it exceeds 10%3
It needs to be 5% or less. If it is less than 10%, these effects will be small, undercutting will occur, and the bead will become rough. On the other hand, if it is contained in a large amount and exceeds a coefficient of 35, the melting point will be lowered too much and the cross-sectional shape of the bead will become convex, making it impossible to obtain a good flat shape.
ＣａＦ２は、溶接金属の酸素量を低減し、高靭性を得る
ために必要で、３％以上含有しないとこの効果が小さい
。またＣａＦ２は、発生するＦガスがアーク空洞を大気
から遮断し、ピット、プローホールの発生を防止するた
めにも、３％以上含有させる必要がある。しかし１６係
を超えると、アーク不安定となり、アンダカット、租い
ビードの波目が問題となる。CaF2 is necessary to reduce the amount of oxygen in the weld metal and obtain high toughness, and this effect will be small if it is not contained at 3% or more. Further, CaF2 must be contained in an amount of 3% or more in order to prevent the generated F gas from shielding the arc cavity from the atmosphere and preventing the formation of pits and plowholes. However, if it exceeds 16, the arc becomes unstable and problems arise such as undercuts and fine bead undulations.
また、ＣａＦ２が３％以上１６係以下の範囲であっても
、（ＡＬｘ’ｓとＴｉ１２の合計） ／ ＣａＦ２比が
４．０以下では、Ａ４０ｓとＴｉｅ、含有によるアーク
安定効果が得られず、スラグの流動性も大きくなり、ア
ンダカットを生じたりビードの波目が粗（なる。Furthermore, even if CaF2 is in the range of 3% to 16%, if the (total of ALx's and Ti12)/CaF2 ratio is 4.0 or less, the arc stabilizing effect due to the inclusion of A40s and Tie cannot be obtained. The fluidity of the slag also increases, causing undercuts and rough bead waves.
ＣａＯ、ＭｇＯおよびＢａＯの各塩基性成分の含有は、
靭性向上に有効ではあるが、これら３成分の合計を、１
３％未満とする必要がある。１３％以上含有した場合、
拡散性水素量の増大により、ピットが発生する。The content of each basic component of CaO, MgO and BaO is
Although it is effective in improving toughness, the sum of these three components is 1
It must be less than 3%. If it contains 13% or more,
Pit formation occurs due to an increase in the amount of diffusible hydrogen.
一方、かさ密度は、高速溶接で良好なビード外観を得る
ために、０．６〜１．３ｆ乃がとする必要がある。１．
３ ？ ７ｃｍ”を超えると、アーク空洞の圧力が不安
定となり、アンダカットを生じやすく、ビードの波目も
粗くなり、０．６ ｔ／ｒｓｓ未満では大気の遮断性が
悪くなるほか、吸湿しやすくなるため、ピットやブロー
ホールの発生することがあり好ましくない。なお、ここ
で言５かさ密度とは、自然落下によって測定するものを
さし、ＪＩＳ Ｋ ６７２１に準じて測定する。On the other hand, the bulk density needs to be 0.6 to 1.3 f in order to obtain a good bead appearance during high-speed welding. 1.
3? If it exceeds 7cm", the pressure in the arc cavity becomes unstable, undercuts are likely to occur, and the bead's undulations become coarse. If it is less than 0.6 t/rss, the atmospheric insulation becomes poor and moisture absorption is likely to occur. As a result, pits and blowholes may occur, which is undesirable.Note that the bulk density herein refers to the density measured by natural fall, and is measured in accordance with JIS K 6721.
またさらに、 ＢｚＯｓは溶接金属結晶粒の微細化作用
により、特に溶接入熱が大きい場合の靭性劣化を補うた
めに含有させることが有効である。その量は、０．１％
未満では大きな効果が得られず、１．２係を超えると高
温割れを起こしやすくなり、０．１〜１．２％の範囲と
することが必要である。Furthermore, it is effective to include BzOs to compensate for toughness deterioration, especially when the welding heat input is large, due to its effect of refining the weld metal crystal grains. The amount is 0.1%
If it is less than 1.2%, no great effect can be obtained, and if it exceeds 1.2%, hot cracking tends to occur, so it is necessary to keep it in the range of 0.1 to 1.2%.
なお、上記に規定した成分のほかに、Ｋｔ Ｏ、Ｎａｔ
Ｏノ含有は、アーク安定化作用によるアンダカットの
防止および靭性の向上に有効であるが、その合計か３％
を超えた場合は、拡散性水素量の増大や凸形のビード断
面形状が問題となる。ＦｅＯも、少量の含有であれば、
若干の靭性向上に有益であるが、３係を超えた場合には
、オーバラップとなりやすく好ましくない。ＺｒＯ，の
含有も、３係を超えた場合、スラグ粘性の低下が激しく
、オーバラップとなり、３％以下とすることが望ましい
。In addition to the components specified above, KtO, Nat
O content is effective in preventing undercut and improving toughness due to arc stabilizing effect, but the total content is 3%.
If it exceeds , problems arise such as an increase in the amount of diffusible hydrogen and a convex cross-sectional shape of the bead. If FeO is also contained in a small amount,
Although it is useful for improving toughness to some extent, if the ratio exceeds 3, it tends to cause overlap, which is not preferable. If the content of ZrO exceeds 3%, the slag viscosity decreases sharply and overlap occurs, so it is desirable to keep it at 3% or less.
次に、本発明フラックスの製造方法としては、従来フラ
ックスの製造と何ら変わることはなく、溶融した原料を
水中に投入することにより発泡させ、乾燥後粒度を揃え
ればよい。また、本発明フラックスは、すみ肉以外の鹸
接纒手にももちろん適用可能である。Next, the method for producing the flux of the present invention is no different from the production of conventional fluxes, and the molten raw material may be poured into water to foam, and the particle size may be made uniform after drying. Furthermore, the flux of the present invention can of course be applied to other types of seams other than fillets.
以下に、本発明の効果を実施例により、さらに具体的に
説明する。EXAMPLES Below, the effects of the present invention will be explained in more detail with reference to Examples.
（実施例）
第５表に示すフラックス（粒度：１２×４８メツシユ）
について、第２表に示すワイヤ、第３表に示すＰｌＩｉ
ＩＡ板を用い、第３図に示すごと（、鋼板とワイヤを組
み合わせて、水平すみ肉浴接した。(Example) Flux shown in Table 5 (particle size: 12 x 48 mesh)
For wires shown in Table 2, PlIi shown in Table 3
Using an IA plate, the steel plate and wire were combined and horizontally joined in a horizontal fillet as shown in Figure 3.
同図において、１はウェブ材、２はフランジ材。In the figure, 1 is a web material and 2 is a flange material.
Ｌ、Ｔは電極、Ｗは溶接進行方間を示す。L and T indicate electrodes, and W indicates welding progress.
浴接条件は、第４表に示すＡ条件、電極−一は第３図に
示ｊ通りの２電僅により、゛電流は先行８００Ａ、後行
７００Ａ、電圧はフラックスに応じた適正電圧（ピード
断面形状かフラットとなる電圧、ただし比較フラックス
にはフラットな形状とならないものもある。）を選び、
浴接速度２００ ａｎ／ｍｉｎで水平すみ肉溶接を行な
い、ピード外観およびスラグ剥離性を調べ、その結果を
第６表に示す。The bath contact conditions were A condition shown in Table 4, electrode 1 was 2 currents as shown in Figure 3; Select the voltage that will make the cross-sectional shape flat (however, some comparative fluxes may not have a flat shape),
Horizontal fillet welding was performed at a bath welding speed of 200 an/min, and the appearance of the pead and slag removability were examined, and the results are shown in Table 6.
また、溶接金属の靭性評価を、第２表に示すワイヤ、第
３表に示すＰｚＡ板を、第２図ｔａ）に示す開先形状（
ｄ＝１０閣、θ７＝６０°）として、第４表に示すＢ条
件により２パス盛溶接し、Ｘ線透過試駄により、高温割
れおよびスラグ巻込みの有無を調べた後、第２図（ｂ）
に示すｈ＝２１３の位置から、ＪＩＳ ４号シャルピー
衝撃試験片を採取し、−６０℃での蚊収エネルギー（２
ｖＥ−６０、ｈ−ｍ）を調べた。In addition, the toughness evaluation of the weld metal was performed using the wire shown in Table 2 and the PzA plate shown in Table 3, using the groove shape (ta) shown in Figure 2.
d = 10°, θ7 = 60°), two-pass welding was performed under the B conditions shown in Table 4, and the presence or absence of hot cracking and slag entrainment was examined using an X-ray transmission test, as shown in Figure 2 ( b)
A JIS No. 4 Charpy impact test piece was taken from the position h=213 shown in
vE-60, hm) was investigated.
なお、第５表に示す本発明フラックスＦ２． Ｆ３、Ｆ
４、Ｆ８および比較フラックスＦ９、Ｆ１４については
、第４表に示すＣ条件による入熱の大きい１ノξス苗接
も行ない、衝撃試版を実施した。さらに、拡散性水素量
を、ＷＥＳ１００３に準じたガスクロマトグラフ法によ
り測定した。これらの結果を第６表に併記する。In addition, the present invention flux F2. shown in Table 5. F3, F
4, F8 and comparative fluxes F9 and F14, seedlings were inoculated at 1 no. ξ with large heat input under the C conditions shown in Table 4, and impact trials were conducted. Furthermore, the amount of diffusible hydrogen was measured by gas chromatography according to WES1003. These results are also listed in Table 6.
この結果、本発明フラックスＦ１〜Ｆ８を用いた場合、
水平すみ肉溶接では、フラットなビード断面形状で、ア
ンダカット、ポックマーク、ピットの発生がなく、細か
いビードの波目を有し、スラグは自然剥離した。また、
低い拡散性水素量と優れた衝撃値も得られた。As a result, when using the fluxes F1 to F8 of the present invention,
Horizontal fillet welding had a flat bead cross-section, with no undercuts, pockmarks, or pits, fine bead undulations, and slag that peeled off naturally. Also,
Low diffusible hydrogen content and excellent impact values were also obtained.
一方、比較フラックスＦ９〜Ｆ１７（第５表中の各数値
にアンダーラインを引いたものは、本発明構成要件から
はずれることを示す。）は、ビード断面形状が凸のもの
、アンダカット、ポックマーク、ピットが発生したもの
、ビードの波目が粗いものなどピード外観、あるいはス
ラグの剥離性に問題があったり、低衝撃値であるなど、
満足できるものはなかった。On the other hand, comparative fluxes F9 to F17 (underlined values in Table 5 indicate that they deviate from the constituent requirements of the present invention) are those with a convex bead cross-sectional shape, undercuts, and pockmarks. , those with pits, rough bead undulations, etc., problems with the peelability of the slag, or low impact values, etc.
Nothing was satisfying.
ところで、比較フラックスＦ１７のように、かさ密度の
みが本発明の構成要件をはずれている場合は、水平すみ
肉以外の清液継手への適用は可能であることが確認され
た。By the way, it has been confirmed that when only the bulk density deviates from the constituent requirements of the present invention, such as the comparative flux F17, it is possible to apply it to fresh liquid joints other than horizontal fillet joints.
（発明の効果）
以上の実施例からも明らかなように、本発明フラックス
は、高靭性な溶接金属が得られ、しかも水平すみ内継手
の高速溶接においても、オーバラップ、アンダカットの
発生もな（、ビード外観とスラグ剥離性が優れることか
ら、高能率なひ接が可能となり、工業Ｅｒり価値は極め
て高い。(Effects of the Invention) As is clear from the above examples, the flux of the present invention can provide weld metal with high toughness, and even in high-speed welding of horizontal fillet joints, overlap and undercut do not occur. (Since the bead appearance and slag removability are excellent, highly efficient welding is possible, and the industrial value is extremely high.
第１図は、Ａｌ２Ｏ３とＴｉＯ２０．含有量と＠撃値の
関係を示す図表、第２図ｔａ）は、開先形状を示す断面
図、第２図ｔｂ＋は、シャルピー衝撃試妓片採取位置ン
示″″３−断ｍ１図、第３図は水平丁み肉清液の電ｍ配
置乞示す説明図であり、第３図（ａ）は側面図、第３図
（ｂ）は正面図である。
１・・・フランジ板、 ２・・・ウェブ板、Ｌ・
・・先行電蓮、 Ｔ・・・後行電極、Ｗ・・・俗
接辿行方向
代理人 弁理士 茶野木 立 夫
第１図
０Ｉ０２θ ３０ ４０ ５０ ６θＡｌ２Ｏ
３含廟量（％）
θヮ
第
（ａ）
（ｂ）
３図
（ｂ）Figure 1 shows Al2O3 and TiO20. A chart showing the relationship between content and impact value, Figure 2 (ta) is a cross-sectional view showing the groove shape, Figure 2 (tb+) is a Charpy impact test piece sampling position (3-section m1), FIG. 3 is an explanatory diagram showing the electrical arrangement of the horizontally cut meat serum, with FIG. 3(a) being a side view and FIG. 3(b) being a front view. 1...Flange plate, 2...Web plate, L.
... Leading electrode, T... Trailing electrode, W... General access direction agent Patent attorney Tatsuo Chanoki Figure 1 0I02θ 30 40 50 6θAl2O
3 Content (%) θヮth (a) (b) Figure 3 (b)
Claims (1)
以下、ＴｉＯ＿２：１４％以上４０％以下、ＭｎＯ：１
０％超３５％以下、ＳｉＯ＿２：８％超３２％以下、Ｃ
ａＦ＿２：３％以上１６％以下を必須成分として含有し
、ＣａＯ、ＭｇＯおよびＢａＯの合計：１３％未満、Ａ
ｌ＿２Ｏ＿３とＴｉＯ＿２の合計：４２％以上、（Ａｌ
＿２Ｏ＿３とＴｉＯ＿２の合計）／ＣａＦ＿２比：４．
０超であり、かさ密度が０．６〜１．３ｇ／ｃｍ＾３で
あることを特徴とする水平すみ肉潜弧溶接用溶融型フラ
ックス。 ２ 成分が重量％で、Ａｌ＿２Ｏ＿３：２５％超４５％
以下、ＴｉＯ＿２：１４％以上４０％以下、ＭｎＯ：１
０％超３５％以下、ＳｉＯ＿２：８％超３２％以下、Ｃ
ａＦ＿２：３％以上１６％以下、Ｂ＿２Ｏ＿３：０．１
％以上１．２％以下を必須成分として含有し、ＣａＯ、
ＭｇＯおよびＢａＯの合計：１３％未満、Ａｌ＿２Ｏ＿
３とＴｉＯ＿２の合計：４２％以上、（Ａｌ＿２Ｏ＿３
とＴｉＯ＿２の合計／ＣａＦ＿２比：４．０超であり、
かさ密度が０．６〜１．３ｇ／ｃｍ＾３であることを特
徴とする水平すみ肉潜弧溶接用溶融型フラックス。[Claims] 1 Components are in weight%, Al_2O_3: more than 25% and 45%
Below, TiO_2: 14% or more and 40% or less, MnO: 1
More than 0% and not more than 35%, SiO_2: More than 8% and not more than 32%, C
aF_2: Contains 3% to 16% as essential components, total of CaO, MgO and BaO: less than 13%, A
Total of l_2O_3 and TiO_2: 42% or more, (Al
_2O_3 and TiO_2)/CaF_2 ratio: 4.
0 and a bulk density of 0.6 to 1.3 g/cm^3. 2 Components are weight%, Al_2O_3: more than 25% 45%
Below, TiO_2: 14% or more and 40% or less, MnO: 1
More than 0% and not more than 35%, SiO_2: More than 8% and not more than 32%, C
aF_2: 3% or more and 16% or less, B_2O_3: 0.1
% or more and 1.2% or less as essential components, including CaO,
Total MgO and BaO: less than 13%, Al_2O_
3 and TiO_2: 42% or more, (Al_2O_3
and the sum of TiO_2/CaF_2 ratio: more than 4.0,
A molten type flux for horizontal fillet submerged arc welding, characterized by having a bulk density of 0.6 to 1.3 g/cm^3.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2724186A JPS62183996A (en) | 1986-02-10 | 1986-02-10 | Fused flux for horizontal fillet submerged arc welding |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2724186A JPS62183996A (en) | 1986-02-10 | 1986-02-10 | Fused flux for horizontal fillet submerged arc welding |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS62183996A true JPS62183996A (en) | 1987-08-12 |
Family
ID=12215580
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2724186A Pending JPS62183996A (en) | 1986-02-10 | 1986-02-10 | Fused flux for horizontal fillet submerged arc welding |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS62183996A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100505920B1 (en) * | 2000-12-15 | 2005-08-04 | 현대종합금속 주식회사 | Submerged arc welding Flux for Zinc primer plate |
| CN103962751A (en) * | 2014-05-21 | 2014-08-06 | 锦州公略焊接技术有限公司 | Sintered flux for efficient submerged arc welding and production technology thereof |
-
1986
- 1986-02-10 JP JP2724186A patent/JPS62183996A/en active Pending
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100505920B1 (en) * | 2000-12-15 | 2005-08-04 | 현대종합금속 주식회사 | Submerged arc welding Flux for Zinc primer plate |
| CN103962751A (en) * | 2014-05-21 | 2014-08-06 | 锦州公略焊接技术有限公司 | Sintered flux for efficient submerged arc welding and production technology thereof |
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