JPH11170085A - Bond flux for submerged arc welding and submerged arc welding method using the same - Google Patents
Bond flux for submerged arc welding and submerged arc welding method using the sameInfo
- Publication number
- JPH11170085A JPH11170085A JP34338097A JP34338097A JPH11170085A JP H11170085 A JPH11170085 A JP H11170085A JP 34338097 A JP34338097 A JP 34338097A JP 34338097 A JP34338097 A JP 34338097A JP H11170085 A JPH11170085 A JP H11170085A
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- weight
- submerged arc
- arc welding
- toughness
- flux
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、４９０乃至５２０
Ｎ／ｍｍ2級のＴＭＣＰ鋼又はＮｂ及びＶの一方又は双
方が添加されていない４９０乃至５２０Ｎ／ｍｍ2級鋼
用として好適のサブマージアーク溶接用ボンドフラック
ス及びそれを使用したサブマージアーク溶接方法に関す
る。BACKGROUND OF THE INVENTION The present invention relates to 490 to 520
The present invention relates to a bond flux for submerged arc welding suitable for N / mm 2 grade TMCP steel or 490 to 520 N / mm 2 grade steel to which one or both of Nb and V are not added, and a submerged arc welding method using the same.
【０００２】[0002]
【従来の技術】阪神淡路大震災以降、溶接継手の品質向
上への要求はより厳しくなる傾向にある。一方、大空間
を有する建築構造物が増え、より肉厚が厚い板でボック
ス柱を製作するケースが増加している。このような状況
下で、厚板ボックス柱角継手の大入熱サブマージアーク
溶接の技術分野においては、強度及び靭性がいずれも従
来の溶接材料に比較して高いレベルで安定する材料の開
発が要望されている。2. Description of the Related Art Since the Great Hanshin-Awaji Earthquake, demands for improving the quality of welded joints have tended to become more severe. On the other hand, the number of architectural structures having a large space is increasing, and the number of cases in which box pillars are made of thicker plates is increasing. Under these circumstances, in the technical field of large heat input submerged arc welding of thick box box column joints, there is a demand for the development of a material whose strength and toughness are both at a higher level than conventional welding materials. Have been.
【０００３】特に最近、厚板のボックス柱に多く適用さ
れ始めているＴＭＣＰ鋼は、Ｍｏ、Ｎｂ及びＶ等の合金
成分の添加なしで従来鋼と同一強度の鋼板を製造するこ
とを可能にしたため、化学成分に着目すると、下記表１
に一例を示すように、ＴＭＣＰ鋼は従来鋼に比較して合
成成分の含有量が少なめになっている。また、ＴＭＣＰ
鋼以外の通常鋼の中にも、Ｎｂ及びＶを含まないものが
存在するようになっており、靭性が十分に得られないよ
うな場合も生じてきている。[0003] In particular, TMCP steel, which has recently begun to be widely applied to thick box columns, has made it possible to produce steel sheets having the same strength as conventional steel without the addition of alloying components such as Mo, Nb and V. Focusing on chemical components, Table 1 below
As shown in FIG. 1, TMCP steel has a lower content of synthetic components than conventional steel. Also, TMCP
Some ordinary steels other than steel do not contain Nb and V, and in some cases, sufficient toughness cannot be obtained.
【０００４】[0004]
【表１】 [Table 1]
【０００５】[0005]
【発明が解決しようとする課題】しかしながら、ボック
ス柱角継手の大入熱サブマージアーク溶接では一般に母
材希釈が多く、これらＴＭＣＰ鋼等を溶接した場合、溶
接金属の十分な強度及び靭性を確保するために必要な合
金成分が不足し、従来鋼を溶接した場合と比較して溶接
金属の引張強度及び靭性が低めになる場合があった。However, large heat input submerged arc welding of box column corner joints generally involves a large amount of base metal dilution, and when these TMCP steels and the like are welded, sufficient strength and toughness of the weld metal are ensured. As a result, the required alloying components are insufficient, and the tensile strength and toughness of the weld metal may be lower than in the case where conventional steel is welded.
【０００６】本発明はかかる問題点に鑑みてなされたも
のであって、４９０乃至５２０Ｎ／ｍｍ2級のＴＭＣＰ
鋼又はＮｂ及びＶの一方又は双方が添加されていない４
９０乃至５２０Ｎ／ｍｍ2級鋼という広い範囲にわたっ
て適用可能で、それらの鋼材の化学成分が多少異なる場
合でも、十分な強度を得ることができ、ＳＭ４９０Ｃ及
びＳＭ５２０Ｃ鋼の母材スペックである４７Ｊを上回る
靭性を得ることができるサブマージアーク溶接用ボンド
フラックスを提供することを目的とする。SUMMARY OF THE INVENTION The present invention has been made in view of the above problems, and has a TMCP of 490 to 520 N / mm 2 class.
Steel or one or both of Nb and V not added 4
Applicable over a wide range of 90 to 520 N / mm 2 grade steel, sufficient strength can be obtained even if the chemical composition of these steel materials is slightly different, exceeding the base metal specification of SM490C and SM520C steel of 47 J An object of the present invention is to provide a bond flux for submerged arc welding capable of obtaining toughness.
【０００７】[0007]
【課題を解決するための手段】本発明に係るサブマージ
アーク溶接用ボンドフラックスは、ＳｉＯ2：１０乃至
２５重量％、Ａｌ2Ｏ3：１０乃至２０重量％、Ｔｉ
Ｏ2：３乃至１２重量％、ＭｇＯ：１０乃至２０重量
％、ＣａＣＯ3：７乃至１５重量％、ｔｏｔａｌ Ｍ
ｎ：０．５乃至８重量％、鉄粉：１５乃至３５重量％、
ＣａＦ2：１．５乃至７．０重量％、Ｂ2Ｏ3：０．３乃
至０．８重量％、金属粉としてのＴｉ：０．４０乃至
１．５０重量％、Ｍｏ：０．４０乃至１．７５重量％を
含有することを特徴とする。The bond flux for submerged arc welding according to the present invention comprises: SiO 2 : 10 to 25% by weight; Al 2 O 3 : 10 to 20% by weight;
O 2 : 3 to 12% by weight, MgO: 10 to 20% by weight, CaCO 3 : 7 to 15% by weight, total M
n: 0.5 to 8% by weight, iron powder: 15 to 35% by weight,
CaF 2 : 1.5 to 7.0% by weight, B 2 O 3 : 0.3 to 0.8% by weight, Ti as metal powder: 0.40 to 1.50% by weight, Mo: 0.40 to 0.4% by weight It is characterized by containing 1.75% by weight.
【０００８】このサブマージアーク溶接用ボンドフラッ
クスは、４９０乃至５２０Ｎ／ｍｍ2級のＴＭＣＰ鋼並
びにＮｂ及びＶの一方又は双方が添加されていない４９
０乃至５２０Ｎ／ｍｍ2級鋼の溶接に使用されることが
好ましい。This bond flux for submerged arc welding does not contain 490 to 520 N / mm 2 class TMCP steel and one or both of Nb and V49.
It is preferably used for welding 0 to 520 N / mm 2 grade steel.
【０００９】また、本発明に係るサブマージアーク溶接
方法は、上記組成のボンドフラックスを使用し、Ｃ：
０．１２重量％以下、Ｓｉ：０．１０重量％以下、Ｍ
ｎ：１．５乃至２．４重量％のワイヤと組合せてサブマ
ージアーク溶接し、Ｔｉ：０．０１０乃至０．０２０重
量％、Ｂ：０．００４０乃至０．００８０重量％及びＭ
ｏ：０．１０乃至０．４５重量％を含有する組成の溶接
金属を得ることを特徴とする。Further, a submerged arc welding method according to the present invention uses a bond flux having the above composition,
0.12% by weight or less, Si: 0.10% by weight or less, M
Submerged arc welding in combination with a wire of n: 1.5 to 2.4% by weight, Ti: 0.010 to 0.020% by weight, B: 0.0040 to 0.0080% by weight and M
o: A weld metal having a composition containing 0.10 to 0.45% by weight is obtained.
【００１０】[0010]
【発明の実施の形態】本発明者等は、前述の課題を解決
すべく種々実験研究した結果、焼き入れ性改善のため良
く使われるＣ及びＭｎ等の成分系を調整しても、母材の
種類又は溶接条件の変動により歩留りが安定せず、その
結果、得られた溶接金属には安定して高いレベルの靱性
を得ることができないことが判明した。そこで、母材の
希釈の影響等を受けにくいＴｉ、Ｂ及びＭｏに着目し、
各元素を単独に添加してみたが、衝撃値：４７Ｊ以上の
値を安定して得るには至らなかった。そこで、本発明者
等は、Ｔｉ、Ｂ及びＭｏを複合添加していったところ、
それぞれの添加量がある一定の範囲でのみ所望の性能を
得ることができることを知見した。BEST MODE FOR CARRYING OUT THE INVENTION As a result of various experiments and researches to solve the above-mentioned problems, the present inventors have found that even if the components such as C and Mn which are often used for improving the hardenability are adjusted, the base material is not changed. It has been found that the yield is not stable due to the variation of the type of welding or the welding conditions, and as a result, the obtained weld metal cannot be stably provided with a high level of toughness. Therefore, paying attention to Ti, B and Mo, which are hardly affected by the dilution of the base material,
When each element was added alone, it was not possible to stably obtain an impact value of 47 J or more. Therefore, the present inventors have added Ti, B and Mo in a composite manner.
It has been found that the desired performance can be obtained only within a certain range of each addition amount.
【００１１】即ち、本発明にて規定したボンドフラック
スの組成範囲が上記所望の性能を得ることができるもの
である。以下、この本発明に係るボンドフラックスの成
分添加理由及び組成限定理由について説明する。That is, the composition range of the bond flux specified in the present invention can obtain the above-mentioned desired performance. Hereinafter, the reasons for adding the components of the bond flux according to the present invention and the reasons for limiting the composition will be described.
【００１２】ＳｉＯ2：１０乃至２５重量％ ＳｉＯ2はスラグの粘性を調整するのに必須の成分であ
るが、１０重量％未満ではスラグの粘性が不十分とな
り、ビード幅が不安定又は不均一となる。また、ＳｉＯ
2が少ないと、ビード形状が凸となると共に、スラグ生
成量も増すため、好ましくない。一方、ＳｉＯ2が２５
重量％を超えると、スラグの粘性が過剰となり、ビード
の広がりが悪くなる。このため、ＳｉＯ2は１０乃至２
５重量％とする。 SiO 2 : 10 to 25% by weight SiO 2 is an essential component for adjusting the viscosity of the slag, but if it is less than 10% by weight, the viscosity of the slag becomes insufficient and the bead width becomes unstable or uneven. Becomes In addition, SiO
If the number is small, the bead shape becomes convex and the amount of slag generated increases, which is not preferable. On the other hand, when SiO 2 is 25
If the amount exceeds the weight percentage, the viscosity of the slag becomes excessive, and the spread of the bead becomes poor. For this reason, SiO 2 is 10 to 2
5% by weight.
【００１３】Ａｌ2Ｏ3：１０乃至２０重量％ Ａｌ2Ｏ3はスラグの粘性及び凝固温度を調整するのに有
効な成分である。しかし、Ａｌ2Ｏ3が１０重量％未満で
はスラグの粘性及び凝固温度が低くなり、ビード幅が不
均一になったり、ビード形状が凸形になるため好ましく
ない。一方、Ａｌ2Ｏ3が２０重量％を超えると、スラグ
の凝固温度が高くなりすぎるため、ビードの広がりが不
十分となり、又はビードが蛇行しやすい。このため、Ａ
ｌ2Ｏ3は１０乃至２０重量％とする。 Al 2 O 3 : 10 to 20% by weight Al 2 O 3 is a component effective for adjusting the viscosity and solidification temperature of slag. However, when the content of Al 2 O 3 is less than 10% by weight, the viscosity and solidification temperature of the slag become low, and the bead width becomes uneven and the bead shape becomes unpreferable. On the other hand, when the content of Al 2 O 3 exceeds 20% by weight, the solidification temperature of the slag becomes too high, so that the spread of the bead becomes insufficient, or the bead tends to meander. Therefore, A
l 2 O 3 is 10 to 20% by weight.
【００１４】ＴｉＯ2：３乃至１２重量％ ＴｉＯ2はスラグの融点及び粘性調整材として有効な成
分である。しかし、ＴｉＯ2の総量が３重量％未満で
は、アンダーカットが発生しやすいため好ましくない。
一方、１２重量％を超えると、スラグ剥離性が急激に劣
化し、スラグ生成量も増大する。このため、ＴｉＯ2は
３乃至１２重量％とする。 TiO 2 : 3 to 12% by weight TiO 2 is a component effective as a material for adjusting the melting point and viscosity of slag. However, if the total amount of TiO 2 is less than 3% by weight, an undercut is likely to occur, which is not preferable.
On the other hand, when the content exceeds 12% by weight, the slag removability is rapidly deteriorated, and the amount of slag generated also increases. Therefore, the content of TiO 2 is set to 3 to 12% by weight.
【００１５】ＭｇＯ：１０乃至２０重量％ ＭｇＯは粘性調整剤としての作用を有している。しか
し、ＭｇＯが１０重量％未満ではビードが蛇行しやす
く、アンダーカットが発生する。一方、ＭｇＯが２０重
量％を超えると、スラグ焼き付きが増すと共に、ポック
マークが発生しやすい。更に、ＭｇＯが多いと、スラグ
生成量も増大するため好ましくない。このため、ＭｇＯ
は１０乃至２０重量％とする。 MgO: 10 to 20% by weight MgO has a function as a viscosity modifier. However, when the content of MgO is less than 10% by weight, the bead tends to meander, and undercut occurs. On the other hand, when the content of MgO exceeds 20% by weight, slag seizure increases and pock marks are easily generated. Further, a large amount of MgO is not preferable because the amount of slag generated increases. For this reason, MgO
Is 10 to 20% by weight.
【００１６】ＣａＣＯ3：７乃至１５重量％ ＣａＣＯ3は溶接中にＣａＯとＣＯ2とに分解され、ＣＯ
2ガスによって溶接部を外気からシールドするととも
に、不純物ガス（Ｈ2又はＮ2等）の分圧を低下させ、溶
接金属中への侵入を防止するのに有効な成分である。し
かし、ＣａＣＯ3が７重量％未満ではＣＯ2ガスによるシ
ールド効果が不十分であり、溶接金属中の水素及び窒素
量が増大し、低温割れ及び靱性の低下が生じやすい。一
方、ＣａＣＯ3が１５重量％を超えると、ＣＯ2ガスの発
生量が過剰になり、ガスが均一に抜けずに溶接中の吹上
減少がきわめて多くなり、ビード外観が劣化しやすい。
このため、ＣａＣＯ3は７乃至１５重量％とする。 CaCO 3 : 7 to 15% by weight CaCO 3 is decomposed into CaO and CO 2 during welding,
While shielding the weld from the outside air by 2 gas, lowering the partial pressure of the impurity gas (H 2 or N 2, etc.), it is an effective ingredient to prevent entry into the weld metal. However, if the content of CaCO 3 is less than 7% by weight, the shielding effect by the CO 2 gas is insufficient, the amounts of hydrogen and nitrogen in the weld metal increase, and low-temperature cracking and a decrease in toughness are likely to occur. On the other hand, when the content of CaCO 3 exceeds 15% by weight, the amount of generated CO 2 gas becomes excessive, the gas does not escape uniformly, and the blow-up during welding becomes extremely large, so that the bead appearance tends to deteriorate.
Therefore, the content of CaCO 3 is set to 7 to 15% by weight.
【００１７】ｔｏｔａｌ Ｍｎ：０．５乃至８重量％ Ｍｎはスラグの粘性及び凝固温度を調整するのに有効な
成分であるだけでなく、溶接金属中のＭｎ量を調整し、
引張性能、衝撃性能を確保するために必須の成分であ
る。しかし、Ｍｎが０．５重量％未満では、アンダーカ
ット及びスラグ焼き付きが発生しやすく好ましくない。
一方、Ｍｎが８重量％を超えると、ビードが蛇行しやす
く、かつフラックス消費量が増大するため好ましくな
い。 Total Mn: 0.5 to 8% by weight Mn is not only an effective component for adjusting the viscosity and solidification temperature of the slag, but also adjusts the Mn content in the weld metal.
It is an essential component for ensuring tensile performance and impact performance. However, when Mn is less than 0.5% by weight, undercut and slag seizure tend to occur, which is not preferable.
On the other hand, if Mn exceeds 8% by weight, the bead tends to meander and the amount of flux consumption increases, which is not preferable.
【００１８】なお、Ｍｎ成分は、金属Ｍｎ及びＦｅ−Ｍ
ｎなどの化合物並びにＭｎＯ、ＭｎＯ2などの酸化物の
形でフラックス中に添加されるが、上記本発明の範囲は
Ｍｎの総量としてｔｏｔａｌ Ｍｎで規定するものであ
る。従って、ｔｏｔａｌ Ｍｎ量が０．５乃至８重量％
の範囲とする。The Mn component includes metal Mn and Fe-M
The compound is added to the flux in the form of a compound such as n or an oxide such as MnO or MnO 2, and the scope of the present invention is defined as the total amount of Mn by total Mn. Therefore, the total Mn content is 0.5 to 8% by weight.
Range.
【００１９】鉄粉：１５乃至３５重量％ フラックス中に鉄粉を添加すると、鉄粉は溶接中に溶融
池へ移行し、消費量が増加する。これにより、溶接能率
の向上と溶接入熱の低下を図ることが可能である。しか
し、鉄粉が１５重量％未満ではこの効果が少なく、大入
熱溶接時の吹上も増加し、また溶込み深さも浅くなり、
溶込み不足が生じやすいので好ましくない。一方、鉄粉
が３５重量％を超えると、ビードの広がりが悪くなった
り、スラグ巻込みが発生しやすくなる。 Iron powder: When iron powder is added to the 15 to 35% by weight flux, the iron powder moves to the molten pool during welding and the consumption increases. Thereby, it is possible to improve welding efficiency and reduce welding heat input. However, when the iron powder is less than 15% by weight, this effect is small, the blow-up during large heat input welding increases, and the penetration depth becomes shallow,
It is not preferable because insufficient penetration easily occurs. On the other hand, if the iron powder exceeds 35% by weight, the spread of the beads becomes poor, and slag entrainment is likely to occur.
【００２０】ＣａＦ2：１．５乃至７．０重量％ ＣａＦ2は溶接金属中の［Ｏ］を低下させる効果がある
とともに、スラグの流動性を調整し、溶接中のスラグ−
メタル間の反応を促進させるために有効な成分である。
しかし、ＣａＦ2が１．５重量％未満では靱性向上に対
して効果が全くなく、粘性向上に対しても効果が少な
い。一方、ＣａＦ2が７．０重量％を超えると、スラグ
の流動性が増し、ビードの蛇行及びアンダーカットが発
生する。このため、ＣａＦ2は１．５乃至７．０重量％
とする。 CaF 2 : 1.5 to 7.0% by weight CaF 2 has the effect of lowering [O] in the weld metal, adjusts the fluidity of the slag, and reduces the slag during welding.
It is an effective component for promoting the reaction between metals.
However, if the content of CaF 2 is less than 1.5% by weight, there is no effect on the improvement of toughness, and there is little effect on the improvement of viscosity. On the other hand, if CaF 2 exceeds 7.0% by weight, the fluidity of the slag increases, and meandering of the bead and undercut occur. For this reason, CaF 2 is 1.5 to 7.0% by weight.
And
【００２１】Ｂ2Ｏ3：０．３乃至０．８重量％、金属粉
としてのＴｉ：０．４０乃至１．５０重量％、Ｍｏ：
０．４０乃至１．７５重量％ 従来これらの成分はいずれも靱性向上を図る場合に単独
で添加されている成分であるが、ＴＭＣＰ鋼並びにＮｂ
及びＶフリー鋼へ適用する場合には、各成分を単独で添
加しても４７Ｊ超で安定した靱性を得ることが困難であ
る。しかし、本発明においては、Ｔｉ、Ｂ及びＭｏの全
てを組み合わせて添加する。これにより、個々の成分の
添加量を最小限に抑えつつ、所望の靱性を安定して得る
ことができることを見出した。また、これらの成分は一
定量を超えると急激に靱性が劣化しはじめ、直ちに期待
する靱性値を下回ってしまう。このように、Ｂ２Ｏ３、
Ｔｉ及びＭｏの全てを添加し、その含有量を適切に設定
することにより、靱性を著しく高めることができる。 B 2 O 3 : 0.3 to 0.8% by weight, metal powder
Ti: 0.40 to 1.50% by weight, Mo:
0.40 to 1.75% by weight Conventionally, all of these components have been added alone in order to improve toughness.
And when applied to V-free steel, it is difficult to obtain stable toughness exceeding 47 J even if each component is added alone. However, in the present invention, Ti, B and Mo are all added in combination. As a result, it has been found that desired toughness can be stably obtained while minimizing the amount of each component added. When these components exceed a certain amount, the toughness starts to rapidly deteriorate, and immediately falls below the expected toughness value. Thus, B2O3,
By adding all of Ti and Mo and appropriately setting the contents thereof, the toughness can be significantly increased.
【００２２】図１乃至図５は、夫々Ｍｏ：０．３５重量
％、Ｍｏ：０．４５重量％、Ｍｏ：０．６０重量％、Ｍ
ｏ：１．６９重量％、Ｍｏ：１．８５重量％の場合のフ
ラックス中のＢ2Ｏ3添加量と衝撃値ｖＥ０℃（Ｊ）との
間系を、種々のＴｉ添加量０．３５乃至１．６０重量％
について測定した結果を示す。この図１乃至５に示すよ
うに、いずれの図においても、Ｂ2Ｏ3が０．３乃至０．
８重量％の場合に、衝撃値が高く、０℃における靱性が
高い溶接金属を得ることができた。また、Ｍｏが０．４
０乃至１．７５重量％の範囲に入る場合、即ち図２乃至
図４の場合に、その範囲から外れる図１及び図５の場合
よりも高い衝撃値が得られた。更に、これらの図２乃至
図４においても、Ｔｉ添加量が０．４０乃至１．５０重
量％の場合に、４７Ｊ以上の高い衝撃値が得られた。FIGS. 1 to 5 show Mo: 0.35% by weight, Mo: 0.45% by weight, Mo: 0.60% by weight, and M, respectively.
In the case of o: 1.69% by weight and Mo: 1.85% by weight, the system between the addition amount of B 2 O 3 in the flux and the impact value vE0 ° C. (J) was determined by changing the addition amount of Ti from 0.35 to 1.60% by weight
2 shows the results of measurement. As shown in FIGS. 1 to 5, in each of the figures, B 2 O 3 is 0.3 to 0.
When the content was 8% by weight, a weld metal having a high impact value and high toughness at 0 ° C. could be obtained. Mo is 0.4
In the range of 0 to 1.75% by weight, that is, in the case of FIGS. 2 to 4, higher impact values were obtained than in the case of FIGS. Further, in FIGS. 2 to 4, when the amount of Ti added was 0.40 to 1.50% by weight, a high impact value of 47 J or more was obtained.
【００２３】即ち、Ｂ2Ｏ3：０．３重量％以上、Ｔｉ：
０．４０重量％以上、Ｍｏ：０．４０重量％以上を全て
満足する場合にのみ靱性が著しく向上し、Ｂ2Ｏ3：０．
８重量％、Ｔｉ：１．５０重量％、Ｍｏ：１．７５重量
％をいずれか一つの成分でも上回った場合に、強度の上
がりすぎによって、靱性は著しく劣化する。このため、
本発明においては、Ｂ2Ｏ3：０．３乃至０．８重量％、
金属粉としてのＴｉ：０．４０乃至１．５０重量％、Ｍ
ｏ：０．４０乃至１．７５重量％の全てを満足するもの
とする。That is, B 2 O 3 : 0.3% by weight or more, Ti:
Only when all of 0.40% by weight or more and Mo: 0.40% by weight or more are satisfied, the toughness is remarkably improved, and B 2 O 3 : 0.
If any one component exceeds 8% by weight, Ti: 1.50% by weight, and Mo: 1.75% by weight, the toughness is remarkably deteriorated due to excessive increase in strength. For this reason,
In the present invention, B 2 O 3 : 0.3 to 0.8% by weight,
Ti as metal powder: 0.40 to 1.50% by weight, M
o: Satisfies all of 0.40 to 1.75% by weight.
【００２４】次に、溶接ワイヤの組成について説明す
る。Next, the composition of the welding wire will be described.
【００２５】Ｃ：０．１２重量％以下 厚板の溶接では、溶接金属は高温割れが発生しやすいこ
とが知られており、溶接金属中のＣ量を低くして高温割
れ防止を図る必要がある。また、溶接金属中のＣ量が多
い場合、焼き入れ性が上昇し、溶接金属の延性低下につ
ながる虞がある。以上の理由から、大入熱サブマージア
ーク溶接用ワイヤでは一般的にＣ：０．１２重量％以下
を使用している。 C: 0.12% by weight or less It is known that high-temperature cracking is liable to occur in a weld metal when welding a thick plate, and it is necessary to reduce the amount of C in the weld metal to prevent high-temperature cracking. is there. Also, when the C content in the weld metal is large, the hardenability increases, which may lead to a decrease in the ductility of the weld metal. For the above reasons, C: 0.12% by weight or less is generally used in the wire for large heat input submerged arc welding.
【００２６】Ｓｉ：０．１０重量％以下 Ｓｉは強力な脱酸剤であるが、溶接金属中のＳｉは靱性
を低下させるため、Ｓｉ：０．１０重量％以下とする。 Si: 0.10% by weight or less Si is a strong deoxidizing agent, but Si in the weld metal lowers toughness. Therefore, Si is made 0.10% by weight or less.
【００２７】Ｍｎ：１．５乃至２．４重量％ Ｍｎは焼き入れ性向上に不可欠な元素であるが、２．４
重量％を超えて添加した場合は、強度が上がりすぎ、低
温割れが発生する虞がある。また、Ｍｎが１．５重量％
未満では、焼き入れ性の効果が不足し、靱性が低下す
る。このため、溶接ワイヤ中のＭｎは１．５乃至２．４
重量％とする。 Mn: 1.5 to 2.4 wt% Mn is an element indispensable for improving hardenability, but is 2.4.
If it is added in excess of% by weight, the strength may be too high and low-temperature cracking may occur. Also, Mn is 1.5% by weight.
If it is less than the value, the effect of hardenability is insufficient, and the toughness is reduced. For this reason, Mn in the welding wire is 1.5 to 2.4.
% By weight.
【００２８】次に、溶接金属の組成について説明する。Next, the composition of the weld metal will be described.
【００２９】Ｔｉ：０．０１０乃至０．０２０重量％ Ｂ：０．００４０乃至０．００８０重量％ Ｍｏ：０．１０乃至０．４５重量％ ＴＭＣＰ鋼及びＮｂ、Ｖフリーの通常鋼については、そ
の成分系はミルメーカー、板厚により多少異なる。従っ
て従来のフラックスでは、それらの鋼種すべてで、安定
して高いレベルの靱性を得ることが困難であった。 Ti: 0.010 to 0.020 wt% B: 0.0040 to 0.0080 wt% Mo: 0.10 to 0.45 wt% For TMCP steel and Nb, V-free ordinary steel, Ingredients vary slightly depending on the mill maker and plate thickness. Therefore, it has been difficult to obtain a high level of toughness stably with all of these steel types using conventional fluxes.
【００３０】そこで、Ｔｉ、Ｂ、Ｍｏを複合添加したフ
ラックスを種々試作し、溶接金属の靱性と化学成分の関
係を検討した結果、ある化学成分範囲の場合に４７Ｊ以
上の靱性値を示すことを知見した。即ち、Ｔｉ：０．０
１０重量％以上、Ｂ：０．００４０重量％以上、Ｍｏ：
０．１０重量％以上のすべてを満足する場合に安定して
高いレベルの靱性を得ることができる。Therefore, various kinds of fluxes to which Ti, B, and Mo were added in a composite manner were manufactured, and the relationship between the toughness and the chemical composition of the weld metal was examined. As a result, it was found that a toughness of 47 J or more was exhibited in a certain chemical composition range. I learned. That is, Ti: 0.0
10% by weight or more, B: 0.0040% by weight or more, Mo:
When all of 0.10% by weight or more are satisfied, a high level of toughness can be stably obtained.
【００３１】しかしながら、Ｔｉ，Ｂ，Ｍｏのいずれか
の成分が、Ｔｉ：０．０２０重量％、Ｂ：０．００８０
重量％、Ｍｏ：０．４５重量％を超えた場合、強度の上
がりすぎによる靱性低下により安定して４７Ｊを得るこ
とができない。よって、溶接金属としては、Ｔｉ：０．
０１０乃至０．０２０重量％、Ｂ：０．００４０乃至
０．００８０重量％、Ｍｏ：０．１０乃至０．４５重量
％を満足するものとする。However, any one of the components Ti, B and Mo contains 0.020% by weight of Ti and 0.0080% of B.
If it exceeds 0.45% by weight, 47J cannot be obtained stably due to a decrease in toughness due to an excessive increase in strength. Therefore, Ti: 0.
010 to 0.020% by weight, B: 0.0040 to 0.0080% by weight, Mo: 0.10 to 0.45% by weight.
【００３２】[0032]
【実施例】次に、本発明の効果を実証するために、本発
明の範囲に入る実施例と本発明の範囲から外れる比較例
とについて、その特性を比較した結果について説明す
る。前記表１に示す板厚６０ｍｍのＴＭＣＰ鋼板を使用
し、開先形状をＹ形、開先角度３０゜、ルートフェース
２ｍｍとして溶接試験した。また、下記表２に示す組成
のワイヤ径６．４ｍｍの溶接用ワイヤを使用し、下記表
３に示すフラックスと組み合わせて溶接試験した。下記
表４は溶接条件を示し、溶接方法は２電極ワンランのサ
ブマージアーク溶接である。Ｔｉ、Ｂ、Ｍｏ以外のＳｉ
Ｏ2、Ａｌ2Ｏ3等の造滓成分は同じ成分にしたため、溶
接作業性、スラグ剥離及びビード外観等は特に差異が認
められなかった。EXAMPLES Next, in order to demonstrate the effects of the present invention, the results of comparing the characteristics of an example falling within the scope of the present invention and a comparative example out of the scope of the present invention will be described. A TMCP steel sheet having a thickness of 60 mm shown in Table 1 above was used, and a welding test was performed with a groove shape of Y shape, a groove angle of 30 °, and a root face of 2 mm. A welding test was performed using a welding wire having a composition shown in Table 2 below and having a wire diameter of 6.4 mm in combination with a flux shown in Table 3 below. Table 4 below shows the welding conditions, and the welding method is a two-electrode one-run submerged arc welding. Si other than Ti, B, Mo
Since the same slag-making components as O 2 and Al 2 O 3 were used, there was no particular difference in welding workability, slag peeling, bead appearance, and the like.
【００３３】溶接後、板厚中央部で機械試験片を採取
し、各種試験を行った。その結果を下記表５に示す。フ
ラックスＡ−４乃至Ａ−６は本発明の実施例であるが、
いずれも４７Ｊ以上の靱性値を得ることができた。これ
に対し、フラックスＡ−１乃至Ａ−３は、夫々Ｔｉ、
Ｂ、Ｍｏが本発明の範囲より少ない比較例であるが、い
ずれも焼き入れ不足により靱性は４７Ｊに達しなかっ
た。After welding, mechanical test pieces were taken at the center of the sheet thickness and subjected to various tests. The results are shown in Table 5 below. Fluxes A-4 to A-6 are examples of the present invention,
In each case, a toughness value of 47 J or more could be obtained. On the other hand, fluxes A-1 to A-3 are Ti,
B and Mo are comparative examples with less than the range of the present invention, but the toughness did not reach 47 J due to insufficient quenching.
【００３４】また、フラックスＡ−７乃至Ａ−９は、夫
々Ｔｉ、Ｂ、Ｍｏが本発明の範囲より多いものである
が、いずれも強度が６００Ｎ／ｍｍ2を超え、靱性は４
７Ｊ以下まで劣化している。The fluxes A-7 to A-9 have Ti, B and Mo, respectively, which are larger than the range of the present invention, but all have a strength exceeding 600 N / mm 2 and a toughness of 4%.
It has deteriorated to 7J or less.
【００３５】[0035]
【表２】 [Table 2]
【００３６】[0036]
【表３】 [Table 3]
【００３７】[0037]
【表４】 [Table 4]
【００３８】[0038]
【表５】 [Table 5]
【００３９】この表５において、Ａ−４、Ａ−５、Ａ−
６はフラックスが本発明の範囲に入る実施例であり、溶
接金属成分も本発明の請求項３を満足するため、溶接金
属の機械的性質（引張強度及び衝撃値）がいずれも優れ
ていた。これに対し、Ａ−２,Ａ−３はフラックス組成
が本発明の範囲から外れるものであり、また溶接金属組
成も本発明の請求項３から外れるため、引張強度及び靱
性がＡ−４，Ａ−５，Ａ−６より低いものであった。更
に、Ａ−７,Ａ−８，Ａ−９は、フラックス組成が本発
明の範囲から外れるため、Ａ−４、Ａ−５、Ａ−６より
引張強度が高いものの、靱性が劣るものであった。更に
また、Ａ−１はフラックス組成は本発明の範囲内である
が、溶接金属組成が本発明の範囲から外れるため、引張
強度及び靱性が従来のものよりは高いが、Ａ−４，Ａ−
５，Ａ−６よりは低いものであった。In Table 5, A-4, A-5, A-
No. 6 is an example in which the flux falls within the scope of the present invention. Since the weld metal component also satisfies claim 3 of the present invention, the mechanical properties (tensile strength and impact value) of the weld metal were all excellent. On the other hand, A-2 and A-3 have a flux composition outside the scope of the present invention and a weld metal composition outside the scope of claim 3 of the present invention. -5, lower than A-6. Further, A-7, A-8, and A-9 have higher tensile strengths than A-4, A-5, and A-6, but are inferior in toughness because the flux composition is out of the range of the present invention. Was. Furthermore, although the flux composition of A-1 is within the range of the present invention, the tensile strength and toughness are higher than those of the conventional one because the weld metal composition is out of the range of the present invention.
5, lower than A-6.
【００４０】[0040]
【発明の効果】以上説明したように、本発明に係るボン
ドフラックスは、Ｂ2Ｏ3：０．３乃至０．８重量％、金
属粉としてのＴｉ：０．４０乃至１．５０重量％、Ｍ
ｏ：０．４０乃至１．７５重量％の全てを満足するもの
であるから、引張強度及び衝撃値が高く、靱性が優れた
溶接金属を得ることができる。また、このボンドフラッ
クスを使用したサブマージアーク溶接方法は、所定の組
成の溶接ワイヤを使用し、所定の組成の溶接金属を得る
ものであるから、靱性が著しく高い溶接金属を得ること
ができる。As described above, the bond flux according to the present invention comprises B 2 O 3 : 0.3 to 0.8% by weight, Ti as metal powder: 0.40 to 1.50% by weight, M
o: Since 0.40 to 1.75% by weight is satisfied, a weld metal having high tensile strength and impact value and excellent toughness can be obtained. Further, in the submerged arc welding method using this bond flux, a welding metal having a predetermined composition is used to obtain a welding metal having a predetermined composition. Therefore, a welding metal having extremely high toughness can be obtained.
【図１】Ｍｏ、Ｔｉ及びＢ2Ｏ3量と、衝撃値との関係を
示すグラフ図である。FIG. 1 is a graph showing the relationship between the amount of Mo, Ti, and B 2 O 3 and the impact value.
【図２】Ｍｏ、Ｔｉ及びＢ2Ｏ3量と、衝撃値との関係を
示すグラフ図である。FIG. 2 is a graph showing the relationship between the amounts of Mo, Ti and B 2 O 3 and the impact value.
【図３】Ｍｏ、Ｔｉ及びＢ2Ｏ3量と、衝撃値との関係を
示すグラフ図である。FIG. 3 is a graph showing the relationship between the amount of Mo, Ti and B 2 O 3 and the impact value.
【図４】Ｍｏ、Ｔｉ及びＢ2Ｏ3量と、衝撃値との関係を
示すグラフ図である。FIG. 4 is a graph showing the relationship between the amount of Mo, Ti and B 2 O 3 and the impact value.
【図５】Ｍｏ、Ｔｉ及びＢ2Ｏ3量と、衝撃値との関係を
示すグラフ図である。FIG. 5 is a graph showing the relationship between the amounts of Mo, Ti and B 2 O 3 and the impact value.
Claims (3)
3：１０乃至２０重量％、ＴｉＯ2：３乃至１２重量％、
ＭｇＯ：１０乃至２０重量％、ＣａＣＯ3：７乃至１５
重量％、ｔｏｔａｌ Ｍｎ：０．５乃至８重量％、鉄
粉：１５乃至３５重量％、ＣａＦ2：１．５乃至７．０
重量％、Ｂ2Ｏ3：０．３乃至０．８重量％、金属粉とし
てのＴｉ：０．４０乃至１．５０重量％、Ｍｏ：０．４
０乃至１．７５重量％を含有することを特徴とするサブ
マージアーク溶接用ボンドフラックス。1. SiO 2 : 10 to 25% by weight, Al 2 O
3 : 10 to 20% by weight, TiO 2 : 3 to 12% by weight,
MgO: 10 to 20% by weight, CaCO 3 : 7 to 15
% By weight, total Mn: 0.5 to 8% by weight, iron powder: 15 to 35% by weight, CaF 2 : 1.5 to 7.0%
Wt%, B 2 O 3: 0.3 to 0.8 wt%, Ti as a metal powder: 0.40 to 1.50 wt%, Mo: 0.4
A bond flux for submerged arc welding, comprising 0 to 1.75% by weight.
Ｐ鋼並びにＮｂ及びＶの一方又は双方が添加されていな
い４９０乃至５２０Ｎ／ｍｍ2級鋼の溶接に使用される
溶接用フラックスであることを特徴とする請求項１に記
載のサブマージアーク溶接用ボンドフラックス。2. 490 to 520 N / mm 2 class TMC
Submerged arc welding bonding according to claim 1, characterized in that the P steels and welding flux one or both of Nb and V is used for welding of 490 to 520N / mm 2 class steel not added flux.
用し、Ｃ：０．１２重量％以下、Ｓｉ：０．１０重量％
以下、Ｍｎ：１．５乃至２．４重量％のワイヤと組合せ
てサブマージアーク溶接し、Ｔｉ：０．０１０乃至０．
０２０重量％、Ｂ：０．００４０乃至０．００８０重量
％及びＭｏ：０．１０乃至０．４５重量％を含有する組
成の溶接金属を得ることを特徴とするサブマージアーク
溶接方法。3. Using the bond flux according to claim 1, C: 0.12% by weight or less, Si: 0.10% by weight.
Hereinafter, submerged arc welding is performed in combination with a wire of Mn: 1.5 to 2.4% by weight, and Ti: 0.010 to 0.
A submerged arc welding method comprising obtaining a weld metal having a composition containing 020% by weight, B: 0.0040 to 0.0080% by weight, and Mo: 0.10 to 0.45% by weight.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP34338097A JPH11170085A (en) | 1997-12-12 | 1997-12-12 | Bond flux for submerged arc welding and submerged arc welding method using the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP34338097A JPH11170085A (en) | 1997-12-12 | 1997-12-12 | Bond flux for submerged arc welding and submerged arc welding method using the same |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH11170085A true JPH11170085A (en) | 1999-06-29 |
Family
ID=18361072
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP34338097A Pending JPH11170085A (en) | 1997-12-12 | 1997-12-12 | Bond flux for submerged arc welding and submerged arc welding method using the same |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH11170085A (en) |
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| JP2003230983A (en) * | 2002-02-08 | 2003-08-19 | Kobe Steel Ltd | Bonded flux for submerged arc welding |
| KR101464853B1 (en) * | 2012-01-10 | 2014-11-25 | 가부시키가이샤 고베 세이코쇼 | Bond flux, wire, welding metal and welding method for submerged arc welding |
| CN105397342A (en) * | 2015-12-18 | 2016-03-16 | 天津宝庆峰焊业有限公司 | Gas shielded flux-cored wire, preparation method thereof and gas shielded welding method |
| KR20160078771A (en) | 2014-12-24 | 2016-07-05 | 주식회사 포스코 | High strength heat input flux cored arc welded metal joint having excellent impact toughness |
| US9492894B2 (en) | 2010-12-27 | 2016-11-15 | Posco | Flux-cored arc welding wire for providing superior toughness and weldability to a welded joint at a low temperature, and welded joint using same |
| CN107685202A (en) * | 2017-10-10 | 2018-02-13 | 河南科技大学 | A kind of neutral sintered flux used for submerged arc welding and preparation method thereof |
| US10065272B2 (en) | 2012-12-27 | 2018-09-04 | Posco | Super high-strength flux cored arc welded joint having excellent impact toughness, and welding wire for manufacturing same |
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1997
- 1997-12-12 JP JP34338097A patent/JPH11170085A/en active Pending
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2003230983A (en) * | 2002-02-08 | 2003-08-19 | Kobe Steel Ltd | Bonded flux for submerged arc welding |
| US9492894B2 (en) | 2010-12-27 | 2016-11-15 | Posco | Flux-cored arc welding wire for providing superior toughness and weldability to a welded joint at a low temperature, and welded joint using same |
| KR101464853B1 (en) * | 2012-01-10 | 2014-11-25 | 가부시키가이샤 고베 세이코쇼 | Bond flux, wire, welding metal and welding method for submerged arc welding |
| US10065272B2 (en) | 2012-12-27 | 2018-09-04 | Posco | Super high-strength flux cored arc welded joint having excellent impact toughness, and welding wire for manufacturing same |
| US10266929B2 (en) | 2013-12-24 | 2019-04-23 | Posco | Ultrahigh-strength gas metal arc welded joint having excellent impact toughness, and solid wire for producing same |
| DE112013007707B4 (en) | 2013-12-24 | 2024-02-01 | Posco Co., Ltd | Ultra-high strength gas metal arc welding joint with excellent notched impact strength and solid wire to produce the same |
| KR20160078771A (en) | 2014-12-24 | 2016-07-05 | 주식회사 포스코 | High strength heat input flux cored arc welded metal joint having excellent impact toughness |
| CN105397342A (en) * | 2015-12-18 | 2016-03-16 | 天津宝庆峰焊业有限公司 | Gas shielded flux-cored wire, preparation method thereof and gas shielded welding method |
| CN107685202A (en) * | 2017-10-10 | 2018-02-13 | 河南科技大学 | A kind of neutral sintered flux used for submerged arc welding and preparation method thereof |
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