JP3152473B2 - Submerged arc welding method for high Mn non-magnetic steel - Google Patents
Submerged arc welding method for high Mn non-magnetic steelInfo
- Publication number
- JP3152473B2 JP3152473B2 JP00780692A JP780692A JP3152473B2 JP 3152473 B2 JP3152473 B2 JP 3152473B2 JP 00780692 A JP00780692 A JP 00780692A JP 780692 A JP780692 A JP 780692A JP 3152473 B2 JP3152473 B2 JP 3152473B2
- Authority
- JP
- Japan
- Prior art keywords
- welding
- flux
- wire
- weld metal
- arc welding
- 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.)
- Expired - Fee Related
Links
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
- B23K35/3053—Fe as the principal constituent
- B23K35/3073—Fe as the principal constituent with Mn as next major constituent
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Nonmetallic Welding Materials (AREA)
- Arc Welding In General (AREA)
Description
【０００１】[0001]
【産業上の利用分野】本発明は超電導マグネットを利用
した浮上式リニアモーターカーのガイドウェイ、橋梁、
分岐部の構造用鋼及び、核融合実験炉、ＭＨＤ発電等の
極低温強磁場構造用鋼として使用される高Ｍｎ非磁性鋼
の溶接に用いる潜弧溶接法に関し、更に詳しくは特定し
た成分のワイヤとフラックスとを組み合わせることによ
り透磁率、強度、靭性、耐割れ性等の溶接金属の特性は
当然のことながらビード形状、スラグ剥離性等の溶接作
業性が良好で溶接欠陥が無い優れた溶接金属が容易に効
率よく得られる潜弧溶接方法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a guideway, a bridge, and the like of a levitation type linear motor car using a superconducting magnet.
Regarding the structural steel of the branch part and the latent arc welding method used for welding of high Mn non-magnetic steel used as a cryogenic high magnetic field structural steel for fusion experimental reactors, MHD power generation, etc. By combining wire and flux, the welding properties such as magnetic permeability, strength, toughness, and cracking resistance are of course excellent, as well as good weldability such as bead shape and slag peelability, and excellent welding with no welding defects. The present invention relates to a latent arc welding method for easily and efficiently obtaining a metal.
【０００２】[0002]
【従来の技術】高Ｍｎオーステナイト鋼は強靭で耐摩耗
性が優れているため高Ｍｎ−高Ｃｒ鋼としてレールクロ
ッシング等の耐摩耗性の必要な部材に使用されている
が、最近では、透磁率が小さく、且つ、安定していると
いう非磁性鋼としての特徴を利用して強磁場構造材とし
て使用されるようになった。2. Description of the Related Art High Mn austenitic steels are tough and have excellent wear resistance and are used as high Mn-high Cr steels for members requiring abrasion resistance such as rail crossings. Utilizing the characteristics of nonmagnetic steel, which is small and stable, has come to be used as a strong magnetic field structural material.
【０００３】従来は高Ｍｎオーステナイト鋼の溶接材料
としてＪＩＳ Ｚ３２５１に規定されている高Ｍｎ−高
Ｃｒ系の硬化肉盛用被覆アーク溶接棒が使用されること
が殆どであったが、この種の溶接材料は継手溶接金属部
に溶接割れが発生したり、良好な性能が得られないこと
がある等の問題があった。そこで、継手溶接用に適した
溶接材料の開発がなされてきている。例えば、特開昭５
５−２４７０１号にＣ，Ｍｎ，Ｃｒ量を特定した基本成
分に、Ｎｉ，Ｍｏ，Ｖ，Ｎの中の少なくとも１種を特定
して含有させることにより、ＭＩＧ溶接、潜弧溶接で高
強度及び良好な曲げ延性を有し、透磁率が小さく且つ、
安定した溶接金属を得られる溶接材料が開示されてい
る。この材料はワイヤの成分のみを特定することにより
溶接金属性能を改善しているものであるが、この発明は
溶接作業性や溶接能率についてはまったく言及されてお
らず、本発明のように成分と特定したワイヤとフラック
スとを組み合わせることにより、溶接作業性が良好で健
全な溶接金属が効率良く得られる潜弧溶接方法とは根本
的に異なるものである。Conventionally, as a welding material for a high Mn austenitic steel, a high Mn-high Cr-based coated arc welding rod for hardfacing as specified in JIS Z3251 has been used in most cases. The welding material has problems such as the occurrence of weld cracks in the joint weld metal portion and the failure to obtain good performance. Thus, welding materials suitable for joint welding have been developed. For example, JP
By specifying and containing at least one of Ni, Mo, V, and N in the basic components whose amounts of C, Mn, and Cr are specified in Japanese Patent No. 5-24701, high strength and high strength can be obtained by MIG welding and latent arc welding. Has good bending ductility, low magnetic permeability,
A welding material capable of obtaining a stable welding metal is disclosed. Although this material improves the performance of the weld metal by specifying only the components of the wire, the present invention does not mention welding workability or welding efficiency at all, and as described in the present invention, The combination of the specified wire and flux is fundamentally different from a submerged arc welding method in which good welding workability and sound welding metal can be efficiently obtained.
【０００４】又、特開昭５６−５９５９７号に溶着鋼部
のＭｎ含有量を高めるように成分調整を行い、又、更に
その基本成分にＮｉ，Ｃｒ，Ｍｏ，Ｃｏ，Ｃｕ等を１種
以上含有させることにより溶接割れ感受性を低くする被
覆アーク溶接材料及びＭＩＧ溶接材料が開示されてい
る。これらの溶接材料も前述と同様に溶接金属性能のみ
を改善したもので、本発明とは全く異なるものである。
現状では溶接能率を重視する潜弧溶接方法の強磁場構造
鋼用としての溶接材料は殆ど市販されていない。高Ｍｎ
系のワイヤと市販されているオーステナイト系ステンレ
ス鋼用潜弧フラックスとを組み合わせて溶接するとスラ
グ剥離性が非常に悪く溶接作業性に問題がある。又、ス
ラグ剥離性改善のため特開昭５６−１４１９９３号に開
示されているようにフラックスにＰｂＯを添加すると溶
接作業性は改善されるものの溶接金属の耐高温割れ性や
機械的性質が劣化するという問題が発生した。In Japanese Patent Application Laid-Open No. 56-59597, the composition is adjusted so as to increase the Mn content of the welded steel part, and at least one of Ni, Cr, Mo, Co, Cu, etc. is used as the basic component. A coated arc welding material and a MIG welding material are disclosed which lower the weld cracking susceptibility by being contained. These welding materials also improve only the weld metal performance as described above, and are completely different from the present invention.
At present, there are few commercially available welding consumables for high magnetic field structural steel using a submerged arc welding method that emphasizes welding efficiency. High Mn
When welding in combination with a system wire and a commercially available latent arc flux for austenitic stainless steel, the slag peelability is very poor, and there is a problem in welding workability. Further, when PbO is added to the flux as disclosed in JP-A-56-141993 to improve slag peelability, welding workability is improved, but the hot crack resistance and mechanical properties of the weld metal deteriorate. The problem occurred.
【０００５】本発明は特定した成分のワイヤとフラック
スとを組み合わせて溶接することにより耐割れ性、強
度、靭性、延性等の性能が良好な溶接金属を能率良く得
ることのできる高Ｍｎ非磁性鋼の潜弧溶接方法の提供を
目的とするものである。[0005] The present invention provides a high Mn nonmagnetic steel capable of efficiently obtaining a weld metal having good crack resistance, strength, toughness, ductility, etc. by combining and welding a wire having a specified component and a flux. The purpose of the present invention is to provide a submerged arc welding method.
【０００６】[0006]
【発明が解決しようとする課題】本発明は成分を特定し
たワイヤとフラックスとを組み合わせることによりなさ
れるもので特にワイヤ中のＯの制限は本発明の重要な要
件であり、本発明者らは数々の実験の結果、高Ｍｎ系ワ
イヤとＰｂＯを含有するフラックスとの組み合わせで溶
接すると溶接金属の耐高温割れ性、延性及び靭性が劣化
するが、これはワイヤ中のＯが溶接金属中のＣｒ，Ｎ
ｉ，Ｓｉ等と酸化物を生成して粒界に析出し溶接金属を
劣化させることが原因となること、ワイヤ中のＯを減少
させることにより図１に示すように溶接金属の靭性が改
善され、図２に示すように曲げ試験において高温割れの
発生がなく、良好な曲げ延性が得られるという知見を得
た。DISCLOSURE OF THE INVENTION The present invention is achieved by combining a wire with a specified component and a flux. In particular, the restriction of O in a wire is an important requirement of the present invention. As a result of a number of experiments, welding with a combination of a high Mn-based wire and a flux containing PbO deteriorates the hot crack resistance, ductility, and toughness of the weld metal. , N
Oxide is generated with i, Si, etc., and precipitates at the grain boundaries to cause deterioration of the weld metal. By reducing O in the wire, the toughness of the weld metal is improved as shown in FIG. As shown in FIG. 2, it was found that a high-temperature crack did not occur in the bending test and good bending ductility was obtained.
【０００７】以上述べたような知見により、高Ｍｎ非磁
性鋼の継手溶接において、特定量のＣ，Ｓｉ，Ｍｎ，Ｃ
ｒ及びＮｉ又はＮの少なくとも１種を含有させたワイヤ
とＣａＯ，ＭｇＯの少なくとも１種、ＣａＦ2 ，Ａｌ2
Ｏ3 ，ＳｉＯ2 及びＰｂＯを含有させたフラックスとを
組み合わせて溶接することで、強磁場構造材用高Ｍｎ非
磁性鋼用の溶接金属として必要な基本特性の強度、靭
性、延性、耐割れ性及び透磁率が得られ、更に溶接欠陥
が無い健全な溶接金属が効率良く、容易に得られること
を見いだした。本発明はこれらの知見によりなされたも
のであり、高Ｍｎ非磁性鋼の継手溶接において良好な溶
接金属性能を効率良く簡単に得ることのできる潜弧溶接
方法の提供を目的とするものである。[0007] Based on the above findings, a specific amount of C, Si, Mn, C
r and a wire containing at least one of Ni or N and at least one of CaO and MgO, CaF 2 , Al 2
Welding in combination with a flux containing O 3 , SiO 2 and PbO provides strength, toughness, ductility, and crack resistance of the basic properties required as a weld metal for high magnetic field structural materials and high Mn non-magnetic steel. In addition, it has been found that a sound weld metal having high permeability and no welding defects can be obtained efficiently and easily. The present invention has been made based on these findings, and an object of the present invention is to provide a submerged arc welding method capable of efficiently and easily obtaining good weld metal performance in joint welding of high Mn nonmagnetic steel.
【０００８】[0008]
【課題を解決するための手段】本発明の要旨とするとこ
ろは、Ｃ；０．０１〜０．２０％、Ｓｉ；０．０５〜
０．５０％、Ｍｎ；１０〜２５％、Ｃｒ；５〜２０％を
基本成分とし、これにＮｉ；０．０５〜３％、Ｎ；０．
０２〜０．３０％の少なくとも１種を含み、更にＯ；
０．０３％以下に制限して残部Ｆｅ及び不可避不純物か
らなるワイヤと、ＣａＦ2 ；１０〜３０％、ＣａＯ，Ｍ
ｇＯの１種又は２種の合計で；１０〜４０％、Ａｌ2 Ｏ
3 ；１０〜４０％、ＳｉＯ2 ；５〜２５％、ＰｂＯ；
０．０１〜０．３０％に制限したボンドフラックスとを
組み合わせて行うことを特徴とする高Ｍｎ非磁性鋼の潜
弧溶接方法である。The gist of the present invention is that C: 0.01 to 0.20%, Si: 0.05 to 0.2%.
0.50%, Mn; 10 to 25%, Cr; 5 to 20% as basic components, and Ni; 0.05 to 3%, N;
From 0.2 to 0.30%, further comprising O;
A wire consisting of Fe and unavoidable impurities, limited to 0.03% or less, CaF 2 ; 10 to 30%, CaO, M
one or two of gO; 10-40%, Al 2 O
3 ; 10 to 40%, SiO 2 ; 5 to 25%, PbO;
A submerged arc welding method for high Mn nonmagnetic steel, characterized in that the method is performed in combination with a bond flux limited to 0.01 to 0.30%.
【０００９】[0009]
【作用】本発明は成分を特定したワイヤとフラックスと
を組み合わせることによりなされるものであり、ワイヤ
中のＣ，Ｓｉ，Ｍｎ，Ｃｒ及びＮｉ，Ｎの少なくとも１
種は高Ｍｎ鋼用ワイヤとして基本特性を得るための必須
成分であり、Ｏの制限は延性、靭性を改善し健全な溶接
金属を得るための重要な要件である。又、フラックス中
にＣａＦ2 ，ＣａＯ，ＭｇＯの一方又は両方、Ａｌ2 Ｏ
3 ，ＳｉＯ2 及びＰｂＯを含有させることが溶接作業効
率を高め、溶接欠陥が発生せず健全な溶接金属を得るた
めの重要な要件となるものである。According to the present invention, at least one of C, Si, Mn, Cr and Ni, N in a wire is combined by combining a wire with a specified component and a flux.
Species are an essential component for obtaining basic characteristics as a wire for high Mn steel, and the restriction of O is an important requirement for improving ductility and toughness and obtaining a sound weld metal. Further, one or both of CaF 2 , CaO, and MgO, Al 2 O
The inclusion of 3 , SiO 2 and PbO is an important requirement for improving welding work efficiency and obtaining a healthy weld metal without generating welding defects.
【００１０】まずワイヤの成分について以下に順次説明
する。 Ｃ；０．０１〜０．２０％ Ｃは溶接金属の強度を保持するために必要な成分であり
０．０１％未満ではその効果がなく、０．２０％を超え
ると溶接金属の耐割れ性を劣化させる。従ってＣの範囲
を０．０１〜０．２０％に制限する。First, the components of the wire will be sequentially described below. C: 0.01 to 0.20% C is a component necessary for maintaining the strength of the weld metal. If the content is less than 0.01%, there is no effect, and if it exceeds 0.20%, the crack resistance of the weld metal. Deteriorates. Therefore, the range of C is limited to 0.01 to 0.20%.
【００１１】Ｓｉ；０．０５〜０．５％ Ｓｉは脱酸元素として溶接金属の酸素量を減少させ、延
性を改善するのに効果があるほか、溶接作業性でビード
形状を改善するのに有効であるが、０．０１％未満では
効果がなく、０．５０％を超えると溶接金属の耐割れ性
を劣化させる。従ってＳｉの範囲を０．０５〜０．５％
に制限する。Si: 0.05 to 0.5% Si is effective as a deoxidizing element to reduce the amount of oxygen in the weld metal and improve ductility, and to improve the bead shape by welding workability. Although it is effective, if it is less than 0.01%, there is no effect, and if it exceeds 0.50%, the crack resistance of the weld metal deteriorates. Therefore, the range of Si is 0.05-0.5%
Restrict to
【００１２】Ｍｎ；１０〜２５％ Ｍｎは安定したオーステナイト組織を得るために必須な
成分であり１０％以上が必要であり、２５％を超えると
ワイヤの加工性が悪くなり、生産性が低下する。従って
Ｍｎの範囲を１０〜２５％に制限する。Mn: 10 to 25% Mn is an essential component in order to obtain a stable austenite structure, and 10% or more is required. If it exceeds 25%, the workability of the wire is deteriorated, and the productivity is reduced. . Therefore, the range of Mn is limited to 10 to 25%.
【００１３】Ｃｒ；５〜２０％ Ｃｒはオーステナイト組織を安定化するために有効な元
素であり、又、耐酸化性と強度を確保するために効果が
あるが５％未満では効果が少なく、２０％を超えると靭
性及び延性が劣化する。従ってＣｒの範囲を５〜２０％
に制限する。Cr: 5 to 20% Cr is an element effective for stabilizing the austenite structure, and is effective for securing oxidation resistance and strength, but is less effective when it is less than 5%. %, Toughness and ductility deteriorate. Therefore, the range of Cr is 5-20%.
Restrict to
【００１４】Ｎｉ；０．０５〜３％ Ｎｉはオーステナイト組織を安定化し、靭性の改善に有
効であるが０．０５％未満では効果が無く、３％を超え
ると強度が低下する。従ってＮｉの範囲を５〜２０％に
制限する。Ni: 0.05 to 3% Ni stabilizes the austenite structure and is effective for improving toughness. However, if it is less than 0.05%, there is no effect, and if it exceeds 3%, the strength decreases. Therefore, the range of Ni is limited to 5 to 20%.
【００１５】Ｎ；０．０２〜０．３０％ Ｎはオーステナイト組織を安定化し、強度を向上させる
のに効果があるが、０．０２％未満ではその効果がな
く、０．３０％を超えると溶接作業性を劣化させ、ブロ
ーホールが発生する。従ってＮの範囲を０．０２〜０．
３０％に制限する。なお、Ｎｉ，Ｎは少なくとも１種を
上記の範囲で含有する必要がある。N: 0.02 to 0.30% N is effective in stabilizing the austenite structure and improving the strength. However, if it is less than 0.02%, there is no effect, and if it exceeds 0.30%, it is not effective. The welding workability is deteriorated, and blow holes are generated. Therefore, the range of N is set to 0.02 to 0.
Limit to 30%. It is necessary that at least one of Ni and N is contained in the above range.
【００１６】Ｏ；０．０３％以下 ＰｂＯを含有するフラックスとの組み合わせで溶接して
も溶接金属に高温割れの発生が無く、溶接金属に粒界割
れが認められず、靭性、延性が改善されるためにはＯを
０．０３％以下に制限することが必要である。従ってＯ
を０．０３％以下に制限する。O: 0.03% or less Even when welding in combination with a flux containing PbO, no high-temperature cracking occurs in the weld metal, no grain boundary cracks are observed in the weld metal, and the toughness and ductility are improved. Therefore, it is necessary to limit O to 0.03% or less. Therefore O
To 0.03% or less.
【００１７】以上が本発明で特に定めるワイヤの成分と
その含有量であるが、その他にＰ，Ｓ等は不可避不純物
としての量が含まれる。次にフラックスの成分について
説明する。The components of the wire and the content thereof particularly defined in the present invention have been described above. In addition, P, S, and the like include the amounts as unavoidable impurities. Next, the components of the flux will be described.
【００１８】ＣａＦ2 ；１０〜３０％ ＣａＦ2 はスラグの塩基度を上げ、溶接金属中のＯを著
しく低減し靭性を良好にする効果があり、本発明のよう
に溶接金属中のＯを低減して粒界割れを防止するために
は不可欠の成分である。又、スラグの溶融点を低下させ
溶け込みを浅くしスラグの剥離性を良好にするとともに
ビード形状、外観を良好にする。１０％未満ではその効
果がなく、３０％を超えるとスラグの流動性が過大とな
りビード形状、外観が劣化する。従ってＣａＦ2 を１０
〜２０％に制限する。CaF 2 ; 10 to 30% CaF 2 has the effect of increasing the basicity of slag, significantly reducing O in the weld metal and improving the toughness, and reducing O in the weld metal as in the present invention. It is an essential component to prevent grain boundary cracking. In addition, the melting point of the slag is lowered, the penetration is made shallower, the removability of the slag is improved, and the bead shape and appearance are improved. If it is less than 10%, the effect is not obtained, and if it exceeds 30%, the fluidity of the slag becomes excessive and the bead shape and appearance deteriorate. Therefore, CaF 2 is reduced to 10
Limit to ~ 20%.
【００１９】 ＣａＯ及びＭｇＯの一方又は両方；１０〜４０％ ＣａＯ及びＭｇＯはいずれも強塩基性成分でＣａＦ2 と
ともに溶接金属中のＯ低減に有効である。又、ＣａＯ，
ＭｇＯは耐火性の大きい成分であり、融点の低いＣａＦ
2 を含有するフラックスの溶融特性を調整し、ビード形
状を整えるのに有効である。１０％未満ではその効果が
なく、４０％を超えるとフラックスが溶け難くビード表
面が平滑さを失い、又、アンダーカット等の溶接欠陥が
発生する。従ってＣａＯ及びＭｇＯの一方又は両方を１
０〜４０％に制限する。One or both of CaO and MgO: 10 to 40% Both CaO and MgO are strong basic components and are effective in reducing O in the weld metal together with CaF 2 . Also, CaO,
MgO is a component having high fire resistance, and CaF having a low melting point is used.
It is effective in adjusting the melting characteristics of the flux containing 2 and adjusting the bead shape. If it is less than 10%, the effect is not obtained. If it exceeds 40%, the flux is hardly melted, the bead surface loses smoothness, and welding defects such as undercut occur. Therefore, one or both of CaO and MgO are
Limit to 0-40%.
【００２０】Ａｌ2 Ｏ3 ；１０〜４０％ Ａｌ2 Ｏ3 は融点が高く、スラグの流動性を調整し、ビ
ード形状を整えるのに有効である。この効果は特に多層
盛溶接に用いる時に重要でありビードどうしのなじみが
良好となり、スラグ巻き込み、アンダーカット等の欠陥
の発生を防止する。１０％未満では効果がなく、４０％
を超えるとスラグ巻き込みや、アンダーカットが生じや
すくなる。従ってＡｌ2 Ｏ3 を１０〜４０％に制限す
る。Al 2 O 3 ; 10 to 40% Al 2 O 3 has a high melting point and is effective in adjusting the fluidity of the slag and adjusting the bead shape. This effect is particularly important when used in multi-pass welding, and the bead can be used well, and slag entrainment and undercuts can be prevented. Less than 10% has no effect, 40%
If it exceeds, slag entrainment and undercut tend to occur. Thus limiting the Al 2 O 3 10 to 40%.
【００２１】ＳｉＯ2 ；５％〜２５％ ＳｉＯ2 はスラグの粘性を調整し、ビード外観を改善す
るのに有効であるが、５％未満では効果がなく、２５％
を超えると粘性が大きくなりスラグ巻き込みが発生す
る。従ってＳｉＯ2 を５〜２５％に制限する。SiO 2 ; 5% to 25% SiO 2 is effective for adjusting the viscosity of the slag and improving the bead appearance.
If it exceeds, the viscosity increases and slag entrainment occurs. Thus limiting the SiO 2 5 to 25%.
【００２２】原料は単独物質とともに上記成分を含有す
る化合物、鉱石あるいは溶融形フラックス等で添加する
ことができる。例えば用いる原料として、ＣａＦ2 ；蛍
石、溶融形フラックス等、ＣａＯ；炭酸石灰、溶融形フ
ラックス等、ＭｇＯ；マグネシアクリンカー、溶融形フ
ラックス等、Ａｌ2 Ｏ3 ；アルミナ、溶融形フラックス
等である。必須成分のほかに成分を調整するために金属
粉、合金粉等を配合することができる。The raw material can be added together with the single substance in the form of a compound containing the above-mentioned components, ore or a molten flux. For example, the raw materials used include CaF 2 ; fluorite, melt flux, etc., CaO; carbonated lime, melt flux, etc., MgO; magnesia clinker, melt flux, etc., Al 2 O 3 ; alumina, melt flux, etc. In addition to the essential components, metal powders, alloy powders and the like can be blended to adjust the components.
【００２３】[0023]
【実施例】以下に本発明溶接方法の効果を実施例により
説明する。実験に供したワイヤは真空溶解炉にて溶解
し、鍛造、圧延及び線引きを行って４．０mmφに作製し
た。ワイヤの組成を表１に示すが、Ｗ１〜Ｗ５は本発明
に用いたワイヤ、Ｗ６〜Ｗ１１は比較例に用いたワイヤ
である。Ｗ９は生産性が悪く歩留りが他ワイヤの５０％
程度であった。EXAMPLES The effects of the welding method of the present invention will be described below with reference to examples. The wire used in the experiment was melted in a vacuum melting furnace, and forged, rolled and drawn to make a wire having a diameter of 4.0 mm. The composition of the wires is shown in Table 1, where W1 to W5 are the wires used in the present invention, and W6 to W11 are the wires used in the comparative examples. W9 has poor productivity and yield is 50% of other wires
It was about.
【００２４】実験に供したボンドフラックスは通常のフ
ラックス原料として用いられる鉱石粉、複合化合物等を
混合、撹拌後、水ガラスを用いて造粒し、４００℃で約
２時間焼成して作製した。フラックスの組成を表２に示
すが、Ｆ１〜Ｆ５は本発明用に用いたフラックス、Ｆ６
〜Ｆ１１は比較例に用いたものである。The bond flux used in the experiment was prepared by mixing ore powder, a composite compound, and the like used as ordinary flux raw materials, stirring, granulating using water glass, and firing at 400 ° C. for about 2 hours. The composition of the flux is shown in Table 2, where F1 to F5 are the flux used for the present invention, F6
F11 are used in Comparative Examples.
【００２５】表１のワイヤと表２のフラックスとを組み
合わせ、表３に示す鋼板を用い、表４に示す溶接条件及
び図３に示す開先形状及び積層要領により、１ｍの溶接
長で潜弧溶接を実施した。表５にワイヤとフラックスと
の組み合わせ及びその確性試験結果を示す。The wire shown in Table 1 was combined with the flux shown in Table 2, and a steel plate shown in Table 3 was used. Under the welding conditions shown in Table 4, the groove shape and the lamination procedure shown in FIG. Welding was performed. Table 5 shows the combinations of wires and fluxes and the results of their accuracy tests.
【００２６】溶接作業性試験については各パスの溶接後
に判定を行った。割れ試験は初層を溶接後カラーチェッ
クにて割れの有無を検査した。溶接終了後、Ｘ線透過試
験（ＪＩＳ Ｚ３１０４による）を行い、引張試験片
（ＪＩＳ Ｚ０５６７径；６mmφ）、衝撃試験片（ＪＩ
Ｓ Ｚ２２０２，４号）、側曲げ試験片（ＪＩＳ Ｚ３
１２２，３号）を採取して基本的な溶接金属性能を調査
した。衝撃試験は０℃、側曲げ試験はＲ＝２ｔで行っ
た。透磁率はＶＳＭ法（振動試料型磁化測定法）により
磁化曲線を測定し最大透磁率を求めた。The welding workability test was performed after each pass welding. In the cracking test, the first layer was inspected for any cracks by color check after welding. After welding, an X-ray transmission test (according to JIS Z3104) was performed, and a tensile test piece (JIS Z0567 diameter; 6 mmφ) and an impact test piece (JI
S Z2202, 4), side bending test piece (JIS Z3)
No. 122, No. 3), and the basic weld metal performance was investigated. The impact test was performed at 0 ° C., and the side bending test was performed at R = 2t. The magnetic permeability was determined by measuring the magnetization curve by the VSM method (vibration sample type magnetization measurement method) to determine the maximum magnetic permeability.
【００２７】本発明例のNo．１〜No．２０は優れた溶接
作業性、溶接金属が得られたがNo．２１はフラックス中
のＣａＦ2 が過多でＡｌ2 Ｏ3 が不足、No．２２はフラ
ックス中のＳｉＯ2 が不足、No．２３はフラックス中の
ＣａＦ2 が不足しＰｂＯが過多、No．２４はフラックス
中のＣａＯとＭｇＯとの和が不足しＡｌ2 Ｏ3 及びＰｂ
Ｏが過多、No．２５はフラックス中のＳｉＯ2 が過多、
No．２６はＣａＯとＭｇＯとの和が過多でＰｂＯが不
足、No．２７，No．２８はワイヤ中のＣ及びＣｒが過
多、No．２９，No．３０はワイヤ中のＣｒが不足しＮｉ
及びＯが過多、No．３１，No．３２はワイヤ中のＳｉ，
Ｎ及びＯ過多、No．３３はワイヤ中のＣ及びＮｉもしく
はＮが不足しＣｒが過多、No．３４はワイヤ中のＳｉ及
びＮｉもしくはＮが不足しＯが過多、No．３５はワイヤ
中のＣが過多でＭｎ及びＮｉもしくはＮの不足、No．３
６はフラックス中のＣａＦ2 が過多でＡｌ2 Ｏ3 が不足
しワイヤ中のＣが過多でＭｎ及びＮｉもしくはＮの不足
というその個々の理由により溶接作業性不良、機械的性
質の劣化、粒界割れの発生等の問題点が認められた。In Example No. of the present invention, 1 to No. In No. 20, excellent welding workability and weld metal were obtained. No. 21 had too much CaF 2 in the flux and lacked Al 2 O 3 ; No. 22 lacks SiO 2 in the flux. No. 23 lacked CaF 2 in the flux and excess PbO. No. 24 shows that the sum of CaO and MgO in the flux is insufficient and Al 2 O 3 and Pb
O is excessive, No. 25 is too much SiO 2 in the flux,
No. In No. 26, the sum of CaO and MgO was excessive and PbO was insufficient. 27, No. No. 28 was excessive in C and Cr in the wire. 29, No. No. 30 lacks Cr in the wire and Ni
And O are excessive, No. 31, No. 32 is Si in the wire,
N and O excess, No. No. 33 lacks C and Ni or N in the wire and has too much Cr. No. 34 is insufficient in Si and Ni or N in the wire and has excessive O. No. 35 has too much C in the wire and lacks Mn and Ni or N. 3
No. 6 shows poor welding workability, deterioration of mechanical properties, and grain boundaries due to individual reasons such as excessive CaF 2 in the flux, insufficient Al 2 O 3 , insufficient C in the wire, and insufficient Mn and Ni or N. Problems such as cracks were observed.
【００２８】[0028]
【表１】 [Table 1]
【００２９】[0029]
【表２】 [Table 2]
【００３０】[0030]
【表３】 [Table 3]
【００３１】[0031]
【表４】 [Table 4]
【００３２】[0032]
【表５】 [Table 5]
【００３３】[0033]
【表６】 [Table 6]
【００３４】[0034]
【発明の効果】以上述べたごとく、本発明は高Ｍｎ鋼の
潜弧溶接において強度、衝撃値、曲げ性能等の機械的性
能が優れ、透磁率が小さい溶接金属が得られるとともに
溶接欠陥が発生しない優れた溶接作業性を有する溶接方
法である。各種の強磁場構造材として使用される高Ｍｎ
鋼の潜弧溶接を本発明方法で行えば溶接継手部の信頼性
と溶接効率は大幅に向上できるものである。As described above, according to the present invention, in a submerged arc welding of high Mn steel, mechanical properties such as strength, impact value, bending performance, etc. are excellent, a weld metal with low magnetic permeability is obtained, and welding defects are generated. This is a welding method that has excellent welding workability. High Mn used as various high magnetic field structural materials
By performing the submerged arc welding of steel by the method of the present invention, the reliability and welding efficiency of the welded joint can be greatly improved.
【図１】ワイヤ中のＯ量と靭性の関係を示した図であ
る。FIG. 1 is a diagram showing the relationship between the amount of O in a wire and toughness.
【図２】ワイヤ中のＯ量、及びフラックス中のＰｂＯと
曲げ試験後の曲げ面の判定結果の関係を示した図であ
る。FIG. 2 is a diagram showing the relationship between the amount of O in a wire, PbO in a flux, and the result of determination of a bent surface after a bending test.
【図３】実施例において用いた開先形状及び積層要領を
示す図である。FIG. 3 is a diagram showing a groove shape and a lamination procedure used in an example.
フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ Ｃ２２Ｃ 38/00 ３０２ Ｃ２２Ｃ 38/00 ３０２Ｘ 38/38 38/38 (56)参考文献 特開 昭57−152448（ＪＰ，Ａ) 特開 昭61−242788（ＪＰ，Ａ) 特開 昭62−110894（ＪＰ，Ａ) 特公 昭46−39453（ＪＰ，Ｂ１) (58)調査した分野(Int.Cl.7，ＤＢ名) B23K 9/18,35/30,35/362 C22C 38/00,38/38 Continuation of the front page (51) Int.Cl. 7 Identification symbol FI C22C 38/00 302 C22C 38/00 302X 38/38 38/38 (56) References JP-A-57-152448 (JP, A) JP-A Sho 61-242788 (JP, A) JP-A-62-110894 (JP, A) JP-B-46-39453 (JP, B1) (58) Fields investigated (Int. Cl. 7 , DB name) B23K 9/18 , 35 / 30,35 / 362 C22C 38 / 00,38 / 38
Claims (1)
不純物からなるワイヤとＣａＦ 2 ；１０〜３０％ ＣａＯ，ＭｇＯの１種又は２種の合計で；１０〜４０％ Ａｌ2 Ｏ3 ；１０〜４０％ ＳｉＯ2 ；５〜２５％ ＰｂＯ；０．０１〜０．３０％ に制限したボンドフラックスとを組み合わせて行うこと
を特徴とする高Ｍｎ非磁性鋼の潜弧溶接方法。C. 0.01 to 0.20% Si; 0.05 to 0.50% Mn; 10 to 25% Cr; 5 to 20% by weight as a basic component, and Ni; 0.05 to 3% N; contains at least one of 0.02 to 0.30%, and O is limited to 0.03% or less, and a wire composed of the balance of Fe and unavoidable impurities and CaF 2. ; Limited to 0.01~0.30%; 10~30% CaO, 1 kind of MgO or two in total; 10~40% Al 2 O 3; 10~40% SiO 2; 5~25% PbO Submerged arc welding method for high Mn nonmagnetic steel, wherein the method is performed in combination with a bonded flux.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP00780692A JP3152473B2 (en) | 1992-01-20 | 1992-01-20 | Submerged arc welding method for high Mn non-magnetic steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP00780692A JP3152473B2 (en) | 1992-01-20 | 1992-01-20 | Submerged arc welding method for high Mn non-magnetic steel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH05192788A JPH05192788A (en) | 1993-08-03 |
| JP3152473B2 true JP3152473B2 (en) | 2001-04-03 |
Family
ID=11675864
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP00780692A Expired - Fee Related JP3152473B2 (en) | 1992-01-20 | 1992-01-20 | Submerged arc welding method for high Mn non-magnetic steel |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3152473B2 (en) |
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|---|---|---|---|---|
| KR20150066372A (en) * | 2013-12-06 | 2015-06-16 | 주식회사 포스코 | Material for submerged arc welding and gas metal arc welding having excellent impact resistance and abrasion resistance properties |
| CN109623198B (en) * | 2019-01-03 | 2020-12-18 | 南京钢铁股份有限公司 | Welding wire for submerged-arc welding of high-manganese low-temperature steel and welding method |
| CA3126854A1 (en) * | 2019-01-22 | 2020-07-30 | Aperam | Iron-manganese alloy having improved weldability |
| JP7276597B2 (en) * | 2020-12-17 | 2023-05-18 | Ｊｆｅスチール株式会社 | WIRE FOR SUBMERGED ARC WELDING AND METHOD FOR MANUFACTURING WELD JOINT USING THE SAME |
-
1992
- 1992-01-20 JP JP00780692A patent/JP3152473B2/en not_active Expired - Fee Related
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| Publication number | Publication date |
|---|---|
| JPH05192788A (en) | 1993-08-03 |
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