JPH04238695A - Bond flux used for low temperature service steel d.c. submerge arc welding - Google Patents
Bond flux used for low temperature service steel d.c. submerge arc weldingInfo
- Publication number
- JPH04238695A JPH04238695A JP5091A JP5091A JPH04238695A JP H04238695 A JPH04238695 A JP H04238695A JP 5091 A JP5091 A JP 5091A JP 5091 A JP5091 A JP 5091A JP H04238695 A JPH04238695 A JP H04238695A
- Authority
- JP
- Japan
- Prior art keywords
- welding
- slag
- flux
- low temperature
- metal
- 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.)
- Withdrawn
Links
- 238000003466 welding Methods 0.000 title claims abstract description 45
- 230000004907 flux Effects 0.000 title claims abstract description 30
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 14
- 239000010959 steel Substances 0.000 title claims abstract description 14
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 claims abstract description 26
- 229910052751 metal Inorganic materials 0.000 claims abstract description 25
- 239000002184 metal Substances 0.000 claims abstract description 25
- 239000000377 silicon dioxide Substances 0.000 claims abstract description 12
- 229910052681 coesite Inorganic materials 0.000 claims abstract description 11
- 229910052906 cristobalite Inorganic materials 0.000 claims abstract description 11
- 235000012239 silicon dioxide Nutrition 0.000 claims abstract description 11
- 229910052682 stishovite Inorganic materials 0.000 claims abstract description 11
- 229910052905 tridymite Inorganic materials 0.000 claims abstract description 11
- WUKWITHWXAAZEY-UHFFFAOYSA-L calcium difluoride Chemical compound [F-].[F-].[Ca+2] WUKWITHWXAAZEY-UHFFFAOYSA-L 0.000 claims abstract description 9
- 229910001634 calcium fluoride Inorganic materials 0.000 claims abstract description 9
- 229910017082 Fe-Si Inorganic materials 0.000 claims abstract description 7
- 229910017133 Fe—Si Inorganic materials 0.000 claims abstract description 7
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 claims abstract description 6
- 229910052593 corundum Inorganic materials 0.000 claims abstract description 6
- 229910001845 yogo sapphire Inorganic materials 0.000 claims abstract description 6
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 239000000203 mixture Substances 0.000 claims description 5
- 239000002893 slag Substances 0.000 abstract description 40
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 abstract description 12
- 239000001301 oxygen Substances 0.000 abstract description 12
- 229910052760 oxygen Inorganic materials 0.000 abstract description 12
- CPLXHLVBOLITMK-UHFFFAOYSA-N Magnesium oxide Chemical compound [Mg]=O CPLXHLVBOLITMK-UHFFFAOYSA-N 0.000 description 20
- 230000000694 effects Effects 0.000 description 16
- 239000011324 bead Substances 0.000 description 14
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N Titan oxide Chemical compound O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 description 10
- 239000000395 magnesium oxide Substances 0.000 description 10
- 239000003795 chemical substances by application Substances 0.000 description 9
- 239000000463 material Substances 0.000 description 6
- 238000009863 impact test Methods 0.000 description 4
- 239000002994 raw material Substances 0.000 description 4
- BVKZGUZCCUSVTD-UHFFFAOYSA-L Carbonate Chemical compound [O-]C([O-])=O BVKZGUZCCUSVTD-UHFFFAOYSA-L 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 239000010410 layer Substances 0.000 description 3
- 238000000034 method Methods 0.000 description 3
- 235000019353 potassium silicate Nutrition 0.000 description 3
- NTHWMYGWWRZVTN-UHFFFAOYSA-N sodium silicate Chemical compound [Na+].[Na+].[O-][Si]([O-])=O NTHWMYGWWRZVTN-UHFFFAOYSA-N 0.000 description 3
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- BYFGZMCJNACEKR-UHFFFAOYSA-N aluminium(i) oxide Chemical compound [Al]O[Al] BYFGZMCJNACEKR-UHFFFAOYSA-N 0.000 description 2
- 150000004649 carbonic acid derivatives Chemical class 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 238000005984 hydrogenation reaction Methods 0.000 description 2
- 239000004576 sand Substances 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Chemical compound O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 239000010456 wollastonite Substances 0.000 description 2
- 229910052882 wollastonite Inorganic materials 0.000 description 2
- 235000008733 Citrus aurantifolia Nutrition 0.000 description 1
- YCKRFDGAMUMZLT-UHFFFAOYSA-N Fluorine atom Chemical compound [F] YCKRFDGAMUMZLT-UHFFFAOYSA-N 0.000 description 1
- 239000004111 Potassium silicate Substances 0.000 description 1
- 239000004115 Sodium Silicate Substances 0.000 description 1
- 235000011941 Tilia x europaea Nutrition 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000005553 drilling Methods 0.000 description 1
- 229910052731 fluorine Inorganic materials 0.000 description 1
- 239000011737 fluorine Substances 0.000 description 1
- 150000002222 fluorine compounds Chemical class 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- 235000012204 lemonade/lime carbonate Nutrition 0.000 description 1
- 239000004571 lime Substances 0.000 description 1
- 229910001635 magnesium fluoride Inorganic materials 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000010450 olivine Substances 0.000 description 1
- 229910052609 olivine Inorganic materials 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 229910052913 potassium silicate Inorganic materials 0.000 description 1
- NNHHDJVEYQHLHG-UHFFFAOYSA-N potassium silicate Chemical compound [K+].[K+].[O-][Si]([O-])=O NNHHDJVEYQHLHG-UHFFFAOYSA-N 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 238000005070 sampling Methods 0.000 description 1
- 238000007493 shaping process Methods 0.000 description 1
- 239000002356 single layer Substances 0.000 description 1
- 229910052911 sodium silicate Inorganic materials 0.000 description 1
Landscapes
- Nonmetallic Welding Materials (AREA)
Abstract
Description
【０００１】0001
【産業上の利用分野】本発明は低温用鋼直流サブマージ
アーク（以下サブマージと略す）溶接用ボンドフラック
スに係わり、低温地域で用いる容器、工作機械に使用す
る低温用鋼の直流サブマージ溶接において、優れた溶接
作業性と安定した機械的性能が得られる低温用鋼直流サ
ブマージ溶接用ボンドフラックスの組成に関するもので
ある。[Industrial Application Field] The present invention relates to a bond flux for direct current submerged arc (hereinafter abbreviated as submerged) welding of low-temperature steel, which is excellent in direct current submerged welding of low-temperature steel used in containers and machine tools used in low-temperature regions. The present invention relates to the composition of a bond flux for direct current submerged welding of low-temperature steel that provides excellent welding workability and stable mechanical performance.
【０００２】0002
【従来の技術】サブマージ溶接法は、被覆アーク溶接法
、ガスシールド溶接法に比して電流を高くすることが出
来るため高能率溶接法として最も利点があり、広く適用
されている。近年、船舶、鉄骨、橋梁、貯槽タンクと共
に石油掘削のためのオイルリグ、人工島等の海洋構造物
が建造されるようになってきたが、石油資源は北海ある
いは北極海など寒冷地に求められており、上記構造物に
は厳しい低温靱性が要求されている。これらの低温用鋼
の溶接部には、少なくとも−４０℃以下での低温靱性が
必要とされる。以上のことにより高能率で低温靱性の良
好な溶接材料に対する要望が強くなっている。BACKGROUND OF THE INVENTION Submerged welding is the most advantageous high-efficiency welding method and is widely applied because it allows a higher current to be applied than covered arc welding or gas shield welding. In recent years, marine structures such as ships, steel frames, bridges, and storage tanks, as well as oil rigs for oil drilling and artificial islands, have been constructed, but oil resources are sought in cold regions such as the North Sea or the Arctic Ocean. Therefore, strict low-temperature toughness is required for the above structures. The welded parts of these low-temperature steels are required to have low-temperature toughness at least at -40°C or lower. Due to the above, there is an increasing demand for welding materials with high efficiency and good low-temperature toughness.
【０００３】高能率であるサブマージ溶接法の作業上の
大きな問題は、溶融したフラックスがスラグとして開先
内に残存し、除去するのに多大な労力を要することであ
る。即ち、被溶接材の板厚が比較的薄く両面１層溶接が
出来る場合は、スラグが開先の外側に生成するので簡単
に除去することが出来、問題にならないが、板厚が厚く
多層盛溶接の場合、特に初層又はその後の２〜３層では
スラグが堅く開先内に焼き付き、スラグを除去するのが
極めて困難となる。このような場合は、ジエットタガネ
のような特別なスラグ除去用工具を用いてスラグを機械
的に破砕しながら除去することが必要であり、溶接能率
を大きく低下せしめる結果となる。この傾向はスラグ剤
としてＴｉＯ２ を含有するフラックスの場合に顕著で
ある。[0003] A major operational problem with the highly efficient submerged welding method is that molten flux remains in the groove as slag, which requires a great deal of effort to remove. In other words, if the plate thickness of the material to be welded is relatively thin and single-layer welding can be performed on both sides, slag will form on the outside of the groove and can be easily removed, causing no problem, but if the plate thickness is thick and multilayer welding In the case of welding, especially in the first layer or the next two or three layers, the slag is hard and baked into the groove, making it extremely difficult to remove it. In such a case, it is necessary to remove the slag while mechanically crushing it using a special slag removal tool such as a jet chisel, which results in a significant reduction in welding efficiency. This tendency is remarkable in the case of a flux containing TiO2 as a slag agent.
【０００４】特開昭５８−１３４９３号公報記載の発明
はスラグ剥離性の改善と共にフラックスの消費量を少な
くすることを目的としたものであるが、フラックスの組
成が必ずしも適切でなく、ＴｉＯ２ の含有量が過剰で
あるため、開先内でのスラグは非常に堅く、そのためス
ラグ剥離が困難であるという問題点がある。又、特開昭
５５−９２２９２号公報記載のフラックスもＴｉＯ２の
含有量が過剰であるため、開先内でのスラグは非常に堅
く、そのためスラグ剥離が困難であるという問題点があ
る。このようなことからフラックス中にスラグ剤として
ＴｉＯ２ を含有することは好ましくない。[0004] The invention described in JP-A-58-13493 aims to improve the slag removability and reduce the amount of flux consumed, but the composition of the flux is not necessarily appropriate, and the composition of the flux is not necessarily appropriate. Due to the excessive amount, the slag within the groove is very hard, making it difficult to remove the slag. Furthermore, since the flux described in JP-A-55-92292 also has an excessive content of TiO2, the slag within the groove is very hard, which makes it difficult to remove the slag. For this reason, it is not preferable to include TiO2 as a slag agent in the flux.
【０００５】さらにはいづれも直流電源を用いて溶接を
行った場合の溶接金属中の酸素量の増加に対しての対応
が十分なされていないため、均一微細なミクロ組織が得
られず、必ずしも良好な低温靱性が得られないという欠
点がある。スラグの特性を改善してスラグ剥離性、低酸
素化を容易にすることが可能であれば、上記のような問
題がなく、サブマージ溶接による高能率溶接が可能とな
る。Furthermore, in both cases, adequate measures have not been taken to deal with the increase in the amount of oxygen in the weld metal when welding is performed using a DC power source, so a uniform and fine microstructure cannot be obtained, and it is not always possible to obtain a good microstructure. The disadvantage is that it does not have sufficient low-temperature toughness. If the characteristics of slag can be improved to facilitate slag removability and oxygen reduction, the above-mentioned problems will not occur and high-efficiency welding by submerged welding will become possible.
【０００６】[0006]
【発明が解決しようとする課題】本発明は、直流電源に
よる多層盛のサブマージ溶接において、特に初層又はそ
の近傍の溶接でスラグ剥離性が良好であり、溶接金属の
低酸素化を図ってあるため優れた溶接作業性と安定した
機械的性能が得られる低温用鋼直流サブマージ溶接用ボ
ンドフラックスを提供することを目的とするものである
。[Problems to be Solved by the Invention] The present invention aims at achieving good slag removability in submerged welding of multilayer welding using a DC power source, particularly in welding at or near the first layer, and reducing the oxygen content of the weld metal. Therefore, the object of the present invention is to provide a bond flux for direct current submerged welding of low-temperature steel that provides excellent welding workability and stable mechanical performance.
【０００７】[0007]
【課題を解決するための手段】即ち、本発明の要旨は重
量％で（以下、同じ）、ＳｉＯ２ ： ８〜１８％、
Ａｌ２ Ｏ３ ：２１〜３１％、ＭｇＯ ：２２〜３
２％、ＣａＦ２ ： １〜１１％、ＣａＯ：１０〜１
８％、Ｔ．ＣＯ２ ： ２〜１０％、金属成分として
Ｆｅ−Ｓｉ： １〜 ４％、金属Ｍｇ：０．１〜２
％、金属Ｍｎ：０．５〜４％、金属Ｔｉ：０．１〜２％
の組成と不可避不純物からなることを特徴とする低温用
鋼直流サブマージ溶接用ボンドフラックスにある。[Means for Solving the Problems] That is, the gist of the present invention is, in weight% (the same applies hereinafter), SiO2: 8 to 18%,
Al2O3: 21-31%, MgO: 22-3
2%, CaF2: 1-11%, CaO: 10-1
8%, T. CO2: 2-10%, Fe-Si as metal component: 1-4%, Metallic Mg: 0.1-2
%, metal Mn: 0.5-4%, metal Ti: 0.1-2%, and is characterized by consisting of inevitable impurities.
【０００８】[0008]
【作用】以下、本発明フラックスの成分限定理由を順を
追って説明する。
ＳｉＯ２ ：８〜１８％
ＳｉＯ２ はスラグの粘性を増加させ、ビードの整形に
対し極めて有効な効果を発揮し、欠陥の発生しない溶接
を行うために必要不可欠の成分である。ＳｉＯ２ はス
ラグをガラス質化する特性があり、これにより砕けやす
い剥離性の良好なスラグを生成することが出来る。この
ようなＳｉＯ２ の効果は８％以上の添加で得られるが
、１８％を超えて添加するとスラグの融点が下がり、ビ
ード形状が劣化し、スラグの焼付きを生じるので、Ｓｉ
Ｏ２の添加量は１８％以下にすることが必要である。Ｓ
ｉＯ２ を添加する原料は、ＳｉＯ２ を主成分とする
珪砂、珪灰石等とする。又、原料を造粒する際に用いる
水ガラス成分としてのＳｉＯ２ もＳｉＯ２ の添加量
として考慮する。[Function] The reasons for limiting the components of the flux of the present invention will be explained step by step below. SiO2: 8-18% SiO2 increases the viscosity of the slag, exhibits an extremely effective effect on bead shaping, and is an essential component for defect-free welding. SiO2 has the property of vitrifying the slag, thereby making it possible to produce a slag that is easily friable and has good releasability. Such effects of SiO2 can be obtained by adding 8% or more of SiO2, but adding more than 18% lowers the melting point of the slag, deteriorates the bead shape, and causes slag seizure.
The amount of O2 added must be 18% or less. S
The raw material to which iO2 is added is silica sand, wollastonite, etc. whose main component is SiO2. Further, SiO2 as a water glass component used when granulating the raw material is also considered as the amount of SiO2 added.
【０００９】Ａｌ２ Ｏ３ ：２１〜３１％Ａｌ２ Ｏ
３ はスラグ形成剤として作用し、溶接作業性の改善お
よび塩基度調整の目的で添加する必要がある。２１％以
上の添加によりスラグ剥離性が著しく改善される。しか
しながらＡｌ２ Ｏ３ を３１％を超えて添加するとビ
ード端部のなじみが劣化し、アンダーカットを生じやす
くなるため、かえってスラグ剥離性を劣化させる。
そのためにもＡｌ２Ｏ３ は２１〜３１％とする必要が
ある。[0009] Al2O3: 21-31% Al2O
3 acts as a slag forming agent and needs to be added for the purpose of improving welding workability and adjusting basicity. Addition of 21% or more significantly improves slag removability. However, if Al2O3 is added in excess of 31%, the conformability of the bead ends deteriorates and undercuts are more likely to occur, which actually deteriorates the slag removability. For this purpose, Al2O3 needs to be 21 to 31%.
【００１０】ＭｇＯ：２２〜３２％
ＭｇＯはスラグ塩基度を高める目的で添加する必要があ
る。高塩基度の溶融スラグは靱性の向上に有効である。
さらには溶融池内の溶解水素をスラグ内に吸収して溶接
金属中の低水素化に極めて有効であると共に溶接金属中
の酸素量を低減し、靱性を向上せしめる効果をも有する
。ＭｇＯ量が２２％未満では上記効果が認められず、３
２％を超えるとスラグ剥離性が著しく悪化する。又、ビ
ード外観が不均一となり開先へのなじみ性も悪くなり、
アンダーカットやスラグ巻き込み等の溶接欠陥が発生し
やすくなる。ＭｇＯを添加する材料としてはマグネシア
クリンカー、オリビンサンド等のＭｇＯを主成分とする
か、ＭｇＯを含有する酸化物、炭酸塩等を用いる。MgO: 22-32% MgO must be added for the purpose of increasing the basicity of the slag. Molten slag with high basicity is effective in improving toughness. Furthermore, dissolved hydrogen in the molten pool is absorbed into the slag, which is extremely effective in reducing hydrogen in the weld metal, and also has the effect of reducing the amount of oxygen in the weld metal and improving toughness. When the amount of MgO is less than 22%, the above effects are not observed, and 3
If it exceeds 2%, slag removability will deteriorate significantly. In addition, the bead appearance becomes uneven and its conformability to the groove becomes poor.
Welding defects such as undercuts and slag entrainment are more likely to occur. As the material to which MgO is added, a material containing MgO as a main component such as magnesia clinker or olivine sand, or an oxide or carbonate containing MgO is used.
【００１１】ＣａＦ２ ：１〜１１％
ＣａＦ２ の分解によって発生する弗素ガスはアーク雰
囲気中の水蒸気分圧を低下させ、炭酸塩と同様に低水素
化に有効である。又、比較的多量のＭｇＯ，ＣａＯを含
有させた高塩基度スラグにおいては、ＣａＦ２ 添加は
溶接金属中の酸素を低下させ、靱性の向上に極めて有効
に作用する。ＣａＦ２ 以外の弗化物としてはＮａＦ，
ＭｇＦ２ 等があるが、これらは溶接作業性を悪化させ
るため、本発明としてはＣａＦ２ として添加する必要
がある。ＣａＦ２ 量が１％未満では上記効果は認めら
れず、１１％を超えるとアークが極めて不安定となりビ
ード外観が悪くなり、溶接時悪臭を発生するためＣａＦ
２ 量は１〜１１％とする必要がある。CaF2: 1 to 11% Fluorine gas generated by decomposition of CaF2 lowers the partial pressure of water vapor in the arc atmosphere, and is effective in reducing hydrogenation similarly to carbonates. Furthermore, in high basicity slag containing relatively large amounts of MgO and CaO, addition of CaF2 lowers oxygen in the weld metal and is extremely effective in improving toughness. Fluorides other than CaF2 include NaF,
There are MgF2, etc., but since these deteriorate welding workability, it is necessary to add them as CaF2 in the present invention. If the amount of CaF2 is less than 1%, the above effect will not be observed, and if it exceeds 11%, the arc will become extremely unstable, the appearance of the bead will deteriorate, and a bad odor will occur during welding.
2 The amount should be between 1 and 11%.
【００１２】ＣａＯ：１０〜１８％
本発明フラックスにおいてはＣａＯは１０〜１８％であ
ることが必要である。ＣａＯは炭酸石灰、珪灰石等から
添加され、ＭｇＯと同様に塩基性成分として溶接金属靱
性の向上に有効な成分であるが、１０％未満ではその効
果は期待できず、１８％を超えるとスラグ剥離性が悪化
したり、ビード外観が不均一となったりするので、多量
の添加は有害となる。CaO: 10-18% In the flux of the present invention, CaO needs to be 10-18%. CaO is added from lime carbonate, wollastonite, etc., and like MgO, it is a basic component that is effective in improving the toughness of weld metal, but if it is less than 10%, no effect can be expected, and if it exceeds 18%, it will cause slag. Addition of a large amount is harmful because the peelability deteriorates and the bead appearance becomes non-uniform.
【００１３】Ｔ．ＣＯ２ ：２〜１０％ＣＯ２ は炭酸
塩が溶接熱で分解して発生するものであるが、アーク雰
囲気中の水蒸気分圧を下げるために必須の成分である。
そしてＣＯ２ 源の炭酸塩としては炭酸石灰の形で添加
とすることが最も好ましい。ＣＯ２に換算して２〜１０
％の範囲になる様に添加する必要がある。２％未満では
低水素化の効果が認められず、１０％を超えるとビード
表面にアバタが多発したり、溶接作業性が著しく低下す
る。[0013]T. CO2: 2 to 10% CO2 is generated when carbonates are decomposed by welding heat, and is an essential component for lowering the water vapor partial pressure in the arc atmosphere. The carbonate as a CO2 source is most preferably added in the form of carbonate lime. 2 to 10 in terms of CO2
% range. If it is less than 2%, no effect of low hydrogenation will be observed, and if it exceeds 10%, avatars will occur frequently on the bead surface and welding workability will be significantly reduced.
【００１４】上述の如く構成される本発明フラックスに
は、Ｆｅ−Ｓｉ、金属Ｍｇ、金属Ｍｎ、金属Ｔｉを添加
することが必要である。Ｆｅ−Ｓｉについては脱酸剤と
して添加する。特に直流溶接は交流溶接に比べ酸素量が
多くなる傾向にあるので低酸素化を図るために必要な成
分である。しかし１％未満では効果が認められず、４％
を超えるとＳｉが過剰となり靱性が著しく低下する。It is necessary to add Fe--Si, metal Mg, metal Mn, and metal Ti to the flux of the present invention constructed as described above. Fe-Si is added as a deoxidizing agent. In particular, direct current welding tends to have a higher amount of oxygen than alternating current welding, so this is a necessary component to achieve low oxygen levels. However, no effect was observed at less than 1%, and 4%
If it exceeds this amount, Si becomes excessive and the toughness decreases significantly.
【００１５】金属Ｍｇについては、Ｆｅ−Ｓｉと同様脱
酸剤として添加する。その効果はＦｅ−Ｓｉより強力で
あるため０．１〜２％の範囲とした。０．１％未満では
効果が認められず、２％を超えると靱性が著しく低下す
る。金属Ｍｎについては、強度を高めるために必要であ
り、溶接時のアーク熱による酸化消耗分を補うためにも
添加するものである。０．５％未満では効果が認められ
ず、４％を超えるとビード表面にスラグが焼付き溶接作
業性が著しく低下する。[0015] Metallic Mg is added as a deoxidizing agent like Fe-Si. Since its effect is stronger than that of Fe-Si, it is set in the range of 0.1 to 2%. If it is less than 0.1%, no effect will be observed, and if it exceeds 2%, the toughness will be significantly reduced. Metal Mn is necessary to increase strength and is also added to compensate for oxidation consumption due to arc heat during welding. If it is less than 0.5%, no effect will be observed, and if it exceeds 4%, slag will seize on the bead surface and welding workability will be significantly reduced.
【００１６】金属Ｔｉは、本発明では非常に重要な金属
成分である。なぜならば従来の低温用鋼フラックスはベ
ースをＴｉＯ２ としてあるため、先に述べたようにス
ラグ剥離性を著しく阻害していた。しかしフラックス中
のＴｉＯ２ は溶接過程において還元され、Ｔｉとして
溶接金属に移行し、靱性向上に大きく寄与していた。ス
ラグ剤からのＴｉでは入熱量の変動により溶接金属に移
行するＴｉ量は大きく左右されるため好ましくない。こ
れに対し金属Ｔｉは入熱量が変動しても溶接金属に移行
するＴｉ量は安定しているので靱性向上に大きく寄与す
る。
０．１％未満では効果が認められず、２％を超えるとビ
ード表面にスラグが焼付き溶接作業性が著しく低下する
。Metal Ti is a very important metal component in the present invention. This is because conventional low-temperature steel fluxes have a base of TiO2, which significantly impedes slag removability as described above. However, TiO2 in the flux was reduced during the welding process, transferred to the weld metal as Ti, and greatly contributed to improving toughness. Ti from a slag agent is not preferable because the amount of Ti transferred to the weld metal is greatly influenced by fluctuations in heat input. On the other hand, metal Ti greatly contributes to improving toughness because the amount of Ti transferred to the weld metal is stable even if the amount of heat input fluctuates. If it is less than 0.1%, no effect will be observed, and if it exceeds 2%, slag will seize on the bead surface and welding workability will be significantly reduced.
【００１７】以上本発明について詳述したが、さらに本
発明の効果を明確にするために以下に実施例について述
べる。The present invention has been described in detail above, and in order to further clarify the effects of the present invention, examples will be described below.
【００１８】[0018]
【実施例】まず、表１に示すようなＡ〜Ｊの１０種類の
ボンドフラックスを作製した。即ち、フラックス原料組
成欄に示すような原料粉を水ガラス（珪酸ソーダ＋珪酸
カリ）を固着剤として造粒した後、５００℃×１２０分
の条件で焼成し、１２×１００メッシュのフラックスと
した。表１のフラックスのうちＡ〜Ｆは本発明例であり
、Ｇ〜Ｊは本発明の効果を明確にするための比較例であ
る。[Example] First, ten types of bond fluxes A to J as shown in Table 1 were prepared. That is, the raw material powder as shown in the flux raw material composition column was granulated using water glass (sodium silicate + potassium silicate) as a fixing agent, and then fired at 500°C for 120 minutes to form a 12 x 100 mesh flux. . Among the fluxes in Table 1, A to F are examples of the present invention, and G to J are comparative examples for clarifying the effects of the present invention.
【００１９】表中のそれぞれのフラックスを用い、１０
種類の厚板の突合せ溶接を実施した。この場合の供試鋼
板、供試ワイヤ（Ｍｎ系鋼ワイヤ）を表２および表３に
、又開先形状を図１に示す。溶接条件を表４に、溶接結
果を表５に示す。スラグ剥離性についてはＢＰ、ＦＰ側
とも１〜２パス目の剥離しやすさについて調べた。衝撃
試験は、図２に示すような位置よりＶノッチシヤルピー
試験片２（ＪＩＳ Ｚ３１１２ ４号）を採取し、
−４０℃で試験を行った。さらに同位置より溶接金属中
の酸素量を調べた。尚、図２において、被溶接材１の表
面から試験片の中心迄の距離ｄは１／４ｔ（１２．５ｍ
ｍ）である。Using each flux in the table, 10
Performed butt welding of various types of thick plates. The test steel plate and test wire (Mn-based steel wire) in this case are shown in Tables 2 and 3, and the groove shape is shown in FIG. Table 4 shows the welding conditions, and Table 5 shows the welding results. Regarding slag removability, the ease of peeling in the first and second passes was investigated on both the BP and FP sides. For the impact test, a V-notch shear piece specimen 2 (JIS Z3112 No. 4) was taken from the position shown in Figure 2.
Tests were conducted at -40°C. Furthermore, the amount of oxygen in the weld metal was investigated from the same location. In Fig. 2, the distance d from the surface of the material to be welded 1 to the center of the test piece is 1/4t (12.5m).
m).
【００２０】本発明例のＡ〜Ｆは本発明の効果によりい
ずれも満足し得る結果が得られたが、比較例のＧ〜Ｊは
いずれもスラグ剥離性が悪く、又ビード形状も悪かった
。Ｇ，Ｊフラックスは脱酸剤として添加する金属−Ｍｇ
を含んでいないため、酸素量を下げることが出来なかっ
た。比較例のＧ〜Ｊフラックスについて述べると、Ｇフ
ラックスはＦｅ−Ｓｉ、金属−Ｔｉが多過ぎ、強脱酸剤
である金属−Ｍｇが添加されていないため、低温靱性が
劣っていた。またスラグ剥離性も悪く、ビード形状も悪
かった。Ｈフラックスはフラックス中にＣＯ２ 源が添
加されていないためスラグ巻き込みが発生し、またビー
ド形状も悪かった。Ｉフラックスは低温靱性の向上に最
も効果のある金属−Ｔｉが添加されていないため、衝撃
試験結果が劣っていた。ＪフラックスはＧフラックスと
同様、低酸素化への対応がなされていないため衝撃試験
結果が劣っていた。さらにビード形状も悪かった。Inventive Examples A to F all gave satisfactory results due to the effect of the present invention, but Comparative Examples G to J all had poor slag removability and poor bead shape. G, J flux is a metal added as a deoxidizing agent - Mg
Because it does not contain oxygen, it was not possible to lower the amount of oxygen. Regarding the G to J fluxes of Comparative Examples, G flux had too much Fe-Si and metal-Ti and no metal-Mg, which is a strong deoxidizing agent, was added, so the low-temperature toughness was poor. Furthermore, the slag removability was poor and the bead shape was also poor. Since no CO2 source was added to the H flux, slag entrainment occurred and the bead shape was also poor. I flux had poor impact test results because it did not contain the metal Ti, which is most effective in improving low-temperature toughness. Like G Flux, J Flux had poor impact test results because it was not designed to deal with low oxygen levels. Furthermore, the bead shape was also poor.
【００２１】[0021]
【表１】[Table 1]
【００２２】[0022]
【表２】[Table 2]
【００２３】[0023]
【表３】[Table 3]
【００２４】[0024]
【表４】[Table 4]
【００２５】[0025]
【表５】[Table 5]
【００２６】[0026]
【発明の効果】以上述べた如く、本発明フラックスによ
れば、低温用鋼の直流サブマージ溶接においてもスラグ
を容易に除去することが出来ると共に、優れたビード形
状および低温靱性を得ることが可能となる。[Effects of the Invention] As described above, according to the flux of the present invention, slag can be easily removed even in DC submerged welding of low-temperature steel, and excellent bead shape and low-temperature toughness can be obtained. Become.
【図１】図１は実施例に用いた開先形状を説明するため
の正面図である。FIG. 1 is a front view for explaining the groove shape used in the example.
【図２】図２は実施例で行った衝撃試験における試験片
の採取位置を説明するための正面図である。FIG. 2 is a front view for explaining the sampling positions of test pieces in the impact test conducted in the example.
１ 被溶接材 ２ シヤルピー試験片 1 Material to be welded 2 Shall pea test piece
Claims (1)
： ８〜１８％、Ａｌ２ Ｏ３ ：２１〜３１％、Ｍ
ｇＯ ：２２〜３２％、ＣａＦ２ ： １〜１１％
、ＣａＯ ：１０〜１８％、Ｔ．ＣＯ２ ： ２〜
１０％、金属成分としてＦｅ−Ｓｉ： １〜 ４％
、金属Ｍｇ：０．１〜２％、金属Ｍｎ：０．５〜４％、
金属Ｔｉ：０．１〜２％の組成と不可避不純物からなる
ことを特徴とする低温用鋼直流サブマージアーク溶接用
ボンドフラックス。[Claim 1] In weight% (hereinafter the same), SiO2
: 8-18%, Al2O3: 21-31%, M
gO: 22-32%, CaF2: 1-11%
, CaO: 10-18%, T. CO2: 2~
10%, Fe-Si as metal component: 1-4%
, metal Mg: 0.1-2%, metal Mn: 0.5-4%,
A bond flux for direct current submerged arc welding of low-temperature steel, characterized by having a composition of 0.1 to 2% metallic Ti and inevitable impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5091A JPH04238695A (en) | 1991-01-05 | 1991-01-05 | Bond flux used for low temperature service steel d.c. submerge arc welding |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5091A JPH04238695A (en) | 1991-01-05 | 1991-01-05 | Bond flux used for low temperature service steel d.c. submerge arc welding |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH04238695A true JPH04238695A (en) | 1992-08-26 |
Family
ID=11463431
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP5091A Withdrawn JPH04238695A (en) | 1991-01-05 | 1991-01-05 | Bond flux used for low temperature service steel d.c. submerge arc welding |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH04238695A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2009039761A (en) * | 2007-08-09 | 2009-02-26 | Nippon Steel & Sumikin Welding Co Ltd | Flux for submerged-arc welding for steel for low temperature use, and welding method thereof |
| JP2015120175A (en) * | 2013-12-20 | 2015-07-02 | 日鐵住金溶接工業株式会社 | SUBMERGED ARC WELDING METHOD OF 780 MPa GRADE HIGH TENSILE STEEL |
-
1991
- 1991-01-05 JP JP5091A patent/JPH04238695A/en not_active Withdrawn
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2009039761A (en) * | 2007-08-09 | 2009-02-26 | Nippon Steel & Sumikin Welding Co Ltd | Flux for submerged-arc welding for steel for low temperature use, and welding method thereof |
| JP2015120175A (en) * | 2013-12-20 | 2015-07-02 | 日鐵住金溶接工業株式会社 | SUBMERGED ARC WELDING METHOD OF 780 MPa GRADE HIGH TENSILE STEEL |
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| Date | Code | Title | Description |
|---|---|---|---|
| A300 | Application deemed to be withdrawn because no request for examination was validly filed |
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