JP3120977B2 - Covered arc welding rod - Google Patents
Covered arc welding rodInfo
- Publication number
- JP3120977B2 JP3120977B2 JP11075801A JP7580199A JP3120977B2 JP 3120977 B2 JP3120977 B2 JP 3120977B2 JP 11075801 A JP11075801 A JP 11075801A JP 7580199 A JP7580199 A JP 7580199A JP 3120977 B2 JP3120977 B2 JP 3120977B2
- Authority
- JP
- Japan
- Prior art keywords
- present
- content
- steel core
- core wire
- cracking resistance
- 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 - Lifetime
Links
- 238000003466 welding Methods 0.000 title claims description 34
- 229910000831 Steel Inorganic materials 0.000 claims description 52
- 239000010959 steel Substances 0.000 claims description 52
- 229910052759 nickel Inorganic materials 0.000 claims description 42
- 229910052804 chromium Inorganic materials 0.000 claims description 38
- 229910052750 molybdenum Inorganic materials 0.000 claims description 37
- 239000011248 coating agent Substances 0.000 claims description 34
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 claims description 10
- 239000001257 hydrogen Substances 0.000 claims description 10
- 229910052739 hydrogen Inorganic materials 0.000 claims description 10
- 238000000576 coating method Methods 0.000 claims description 7
- 239000000126 substance Substances 0.000 claims description 5
- 238000006243 chemical reaction Methods 0.000 claims description 2
- 238000005336 cracking Methods 0.000 description 48
- 239000002893 slag Substances 0.000 description 45
- 229910052751 metal Inorganic materials 0.000 description 41
- 239000002184 metal Substances 0.000 description 41
- 230000000052 comparative effect Effects 0.000 description 19
- 238000011156 evaluation Methods 0.000 description 8
- 229910052760 oxygen Inorganic materials 0.000 description 8
- 229910052799 carbon Inorganic materials 0.000 description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 4
- 238000010521 absorption reaction Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N Titan oxide Chemical compound O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 description 3
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N Iron oxide Chemical compound [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 239000011324 bead Substances 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 235000008733 Citrus aurantifolia Nutrition 0.000 description 1
- 235000011941 Tilia x europaea Nutrition 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 230000008602 contraction Effects 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 230000003111 delayed effect Effects 0.000 description 1
- 239000004571 lime Substances 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
- 239000011135 tin Substances 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)
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、鋼心線等の外周に
被覆剤が塗布された被覆アーク溶接棒に関し、特に、ス
ラグの剥離性及び耐高温割れ性が優れた被覆アーク溶接
棒に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a coated arc welding rod in which a coating agent is applied to the outer periphery of a steel core wire or the like, and more particularly to a coated arc welding rod having excellent slag removability and hot cracking resistance.
【０００２】[0002]
【従来の技術】従来、イルミナイト系、ライムチタニア
系、高酸化チタン系及び鉄粉酸化鉄系等の非低水素系被
覆アーク溶接棒においては、被覆剤中のＭｇＯにより、
スラグの粘性を維持しつつ、結晶水から発生する水素ガ
スをこのスラグ中に拡散させて多孔質化させ、砕け易い
スラグにすることによりスラグの剥離性の向上させるこ
とを提案している（特公昭６１−３５９７号公報）。2. Description of the Related Art Conventionally, in non-low hydrogen type coated arc welding rods such as illuminite type, lime titania type, high titanium oxide type and iron powder iron oxide type, MgO in a coating agent is used.
It has been proposed that while maintaining the viscosity of the slag, the hydrogen gas generated from the water of crystallization is diffused into the slag to make it porous, and the slag is made easily breakable, thereby improving the slag removability. JP-B-61-3597).
【０００３】一方、低水素系被覆アーク溶接棒において
は、被覆剤中のＭｎ酸化物により、スラグの熱膨張と収
縮との差を大きくすることで形成スラグに多くの亀裂を
発生させ、かつそのＭｎ酸化物に含まれる酸素が溶接金
属中の炭素との反応によりＣＯガス又はＣＯ2ガスを発
生させることでスラグの緻密度が低下し、ビード接触面
のスラグに空隙を多発させると共に、更にスラグの粘性
を低下させてビード形状を平滑で良好にすることによ
り、スラグの剥離性を改善している（特開昭６３−２０
７４９６号公報）。[0003] On the other hand, in a low hydrogen-based coated arc welding rod, Mn oxide in a coating agent causes a large difference between thermal expansion and contraction of the slag to generate many cracks in the formed slag. Oxygen contained in the Mn oxide reacts with carbon in the weld metal to generate CO gas or CO 2 gas, thereby reducing the density of the slag, causing slag at the bead contact surface to generate many voids, and further increasing the slag. The slag removability is improved by lowering the viscosity of the slag to make the bead shape smooth and good.
No. 7496).
【０００４】[0004]
【発明が解決しようとする課題】しかし、上述の特公昭
６１−３５９７号公報及び特開昭６３−２０７４９６号
公報に記載された被覆アーク溶接棒では、狭開先を溶接
した場合に、スラグは自然剥離しない。このため、スラ
グを除去するためにチッピングハンマ等を使用して軽く
打撃しなければならず、スラグの剥離性が不十分である
という問題点がある。However, in the covered arc welding rod described in Japanese Patent Publication No. 61-3597 and Japanese Patent Laid-Open Publication No. 63-207496, when the narrow groove is welded, the slag is reduced. Does not spontaneously exfoliate. Therefore, the slag must be lightly hit with a chipping hammer or the like in order to remove the slag, and there is a problem that the slag is not sufficiently peeled.
【０００５】また、耐高温割れ性については何ら考慮さ
れていないため、耐高温割れ性が低いという問題点があ
る。Further, since no consideration is given to hot cracking resistance, there is a problem that hot cracking resistance is low.
【０００６】一方、近時、溶接作業を更に一層高能率化
すべく、アークタイム率を向上させるため、スラグ除去
時間の短縮を図ることが望まれている。また、溶接時間
の短縮のために狭開先化することも望まれている。On the other hand, recently, it has been desired to shorten the slag removal time in order to improve the arc time rate in order to further improve the efficiency of the welding operation. It is also desired to narrow the groove to shorten the welding time.
【０００７】本発明はかかる問題点に鑑みてなされたも
のであって、狭開先であってもスラグが自然剥離すると
共に、耐高温割れ性が優れた被覆アーク溶接棒を提供す
ることを目的とする。[0007] The present invention has been made in view of the above problems, and an object of the present invention is to provide a coated arc welding rod that exfoliates slag spontaneously even in a narrow groove and has excellent hot cracking resistance. And
【０００８】[0008]
【課題を解決するための手段】本発明に係る被覆アーク
溶接棒は、鋼心線と、この鋼心線の外周に塗布されたＳ
ｎの酸化物及び／又は単体をＳｎ換算で０．００２乃至
０．５質量％含有する被覆剤と、を有することを特徴と
する。According to the present invention, there is provided a covered arc welding rod comprising a steel core wire and a steel wire coated on the outer periphery of the steel core wire.
a coating containing 0.002 to 0.5% by mass of Sn oxide and / or simple substance in Sn conversion.
【０００９】本発明においては、前記鋼心線は、Ｏを
０．００１０乃至０．０２０質量％含有し、Ｎｉ、Ｃｒ
及びＭｏからなる群から選択された少なくとも１種を総
量で０．０１０乃至０．１０質量％含有することが好ま
しい。In the present invention, the steel core wire contains 0.0010 to 0.020% by mass of O, Ni, Cr
And Mo in a total amount of at least one selected from the group consisting of 0.010 to 0.10% by mass .
【００１０】また、本発明においては、前記被覆剤は、
例えば、非低水素系被覆剤又は低水素系被覆剤である。In the present invention, the coating agent is
For example, a non-low hydrogen coating or a low hydrogen coating.
【００１１】[0011]
【発明の実施の形態】以下、本発明の被覆アーク溶接棒
の実施例について説明する。本願発明者等は上記の問題
点を解決すべく鋭意研究した結果、被覆剤中にＳｎを添
加することにより、ＳｎとＦｅとの化合物であるＦｅ3
Ｓｎが低融点であることから、クレータが凝固する際に
このＦｅ3Ｓｎが最後までクレータ表面に存在し、凝固
が遅れる部分が散在し、その部分が収縮するとき、スラ
グの溶接金属に接する部分に微小な亀裂が多く生じ、こ
の微小な亀裂が起点になりスラグが破壊され、スラグが
自然剥離することを見出した。DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS An embodiment of a coated arc welding rod according to the present invention will be described below. The present inventors have conducted intensive studies to solve the above problems, and as a result, by adding Sn to the coating agent, a compound of Sn and Fe, Fe 3
Since Sn has a low melting point, when the crater solidifies, this Fe 3 Sn is present on the crater surface to the end, and a portion where solidification is delayed is scattered, and when the portion contracts, a portion of the slag that comes into contact with the weld metal is formed. It has been found that many small cracks are formed in the steel sheet, and the small cracks serve as a starting point to destroy the slag and spall naturally.
【００１２】以下、本発明の被覆アーク溶接棒の数値限
定理由について説明する。Hereinafter, the reasons for limiting the numerical values of the coated arc welding rod of the present invention will be described.
【００１３】Ｓｎ：０．００２乃至０．５質量％ Ｓｎの含有量が０．００２質量％未満であると、スラグ
の剥離性を向上させる効果が小さい。一方、Ｓｎの含有
量が０．５質量％を超えると、クレータが凝固する際
に、クレータ表面に存在するＳｎが濃化された部分が広
くなり大きな割れ、いわゆる高温割れが生じ易くなる。
従って、Ｓｎの含有量は０．００２乃至０．５質量％と
する。なお、被覆剤の中のＳｎは酸化物又は単体で含有
させることができる。 Sn: 0.002 to 0.5% by mass When the Sn content is less than 0.002% by mass , the effect of improving the slag removability is small. On the other hand, when the Sn content exceeds 0.5% by mass , when the crater is solidified, the Sn-enriched portion present on the crater surface is widened and large cracks, so-called hot cracks, are likely to occur.
Therefore, the content of Sn is set to 0.002 to 0.5% by mass . Note that Sn in the coating agent can be contained as an oxide or a simple substance.
【００１４】更に、本願発明者等は鋼心線にＯとＮｉ、
Ｃｒ及びＭｏの少なくとも１種を添加することにより、
被覆アーク溶接棒の耐高温割れ性をより一層改善するこ
とができることを見出した。Ｏは耐高温割れ性に最も影
響を及ぼすＳを無害な介在物にするため、耐高温割れ性
を改善することができる。また、Ｎｉ、Ｃｒ及びＭｏを
少量添加すると、Ｓｎの偏析を抑えることができるた
め、耐高温割れ性を改善することができる。Further, the inventors of the present application have added O and Ni to the steel core wire.
By adding at least one of Cr and Mo,
It has been found that the high temperature crack resistance of the coated arc welding rod can be further improved. O makes S the most harmful inclusion which has an effect on hot cracking resistance, so that hot cracking resistance can be improved. Further, when a small amount of Ni, Cr and Mo is added, the segregation of Sn can be suppressed, so that the hot cracking resistance can be improved.
【００１５】Ｏ：０．００１０乃至０．０２０質量％ 鋼心線中のＯの含有量が０．００１０質量％未満である
と、耐高温割れ性を向上させる効果が小さい。一方、Ｏ
の含有量が０．０２０質量％を超えると、溶接金属の中
の酸素量が多くなりすぎ、靭性が劣化する。従って、Ｏ
の含有量は０．００１０乃至０．０２０質量％とする。 O: 0.0010 to 0.020 mass% When the content of O in the steel core wire is less than 0.0010 mass %, the effect of improving the hot crack resistance is small. On the other hand, O
If the content exceeds 0.020% by mass , the amount of oxygen in the weld metal becomes too large, and the toughness deteriorates. Therefore, O
Is 0.0010 to 0.020% by mass .
【００１６】Ｎｉ、Ｃｒ及びＭｏからなる群から選択さ
れた少なくとも１種の総量：０．０１０乃至０．１０質
量％ Ｎｉ、Ｃｒ及びＭｏの含有量の合計が０．０１０質量％
未満であると、耐高温割れ性を向上させる効果が小さ
い。一方、Ｎｉ、Ｃｒ及びＭｏの含有量の合計が０．１
０質量％を超えると、溶接金属の強度が高くなりすぎ
て、延性が劣化する。従って、Ｎｉ、Ｃｒ及びＭｏから
なる群から選択された少なくとも１種を総量で０．０１
０乃至０．１０質量％含有する。 Selected from the group consisting of Ni, Cr and Mo
Total amount of at least one type: 0.010 to 0.10
Content% The total content of Ni, Cr and Mo is 0.010% by mass .
If it is less than the above, the effect of improving the hot crack resistance is small. On the other hand, the total content of Ni, Cr and Mo is 0.1
If it exceeds 0% by mass , the strength of the weld metal becomes too high, and the ductility deteriorates. Therefore, at least one selected from the group consisting of Ni, Cr and Mo is contained in a total amount of 0.01%.
0 to 0.10% by mass .
【００１７】[0017]
【実施例】以下、本発明の被覆アーク溶接棒の実施例に
ついて、本発明の範囲から外れる比較例と比較して具体
的に説明する。EXAMPLES Examples of the coated arc welding rod of the present invention will be specifically described below in comparison with comparative examples which are out of the scope of the present invention.
【００１８】第１実施例 表１に示す化学成分の鋼心線を使用して表２及び表３に
示す非低水素系被覆アーク溶接棒を試作した。なお、こ
の非低水素系被覆アーク溶接棒は鋼心線の直径が４．０
ｍｍで、被覆剤の直径が６．１０ｍｍである。なお、表
１中の鋼心線の種類ＡはＯの含有量並びにＮｉ、Ｃｒ及
びＭｏの含有量の合計が本発明の請求項２の範囲未満で
あるため、耐高温割れ性がやや劣った。種類ＢはＯの含
有量が本発明の請求項２の範囲未満であり、Ｎｉ、Ｃｒ
及びＭｏの含有量の合計が本発明の請求項２の範囲を超
えているため、耐高温割れ性がやや劣ると共に、溶接金
属の延性もやや劣った。種類ＣはＯの含有量が本発明の
請求項２の範囲未満であるため、耐高温割れ性がやや劣
った。種類Ｄ、種類Ｆ、種類Ｇ及び種類ＨはＯの含有量
並びにＮｉ、Ｃｒ及びＭｏの含有量の合計が本発明の請
求項２の範囲内にあるために耐高温割れ性及び溶接金属
の性能が良好であった。種類ＥはＮｉ、Ｃｒ及びＭｏの
含有量の合計が本発明の請求項２の範囲未満であるた
め、耐高温割れ性がやや劣った。種類ＩはＯの含有量が
本発明の請求項２の範囲を超え、Ｎｉ、Ｃｒ及びＭｏの
含有量の合計が本発明の請求項２の範囲未満であるた
め、溶接金属の靭性がやや劣ると共に、耐高温割れ性が
やや劣った。種類ＪはＯの含有量並びにＮｉ、Ｃｒ及び
Ｍｏの含有量の合計が本発明の請求項２の範囲を超えて
いるため、溶接金属の靭性がやや劣ると共に、延性もや
や劣った。種類ＫはＯの含有量が本発明の請求項２の範
囲を超えているため、溶接金属の靭性がやや劣った。種
類Ｌは、Ｎｉ、Ｃｒ及びＭｏの含有量の合計が本発明の
請求項２の範囲を超えているため、溶接金属の延性がや
や劣った。 First Example Non-low hydrogen coated arc welding rods shown in Tables 2 and 3 were experimentally produced using steel core wires having the chemical components shown in Table 1. The non-low hydrogen coated arc welding rod has a steel core diameter of 4.0.
mm, the diameter of the coating is 6.10 mm. In addition, since the total of the content of O and the content of Ni, Cr, and Mo was less than the range of Claim 2 of the present invention, the type A of the steel core wire in Table 1 was slightly inferior in hot cracking resistance. . Type B has an O content of less than the scope of claim 2 of the present invention, and Ni, Cr
Since the total content of Mo and Mo exceeds the scope of claim 2 of the present invention, the hot cracking resistance was slightly inferior and the ductility of the weld metal was also slightly inferior. Since the content of type C is less than the range of claim 2 of the present invention, the hot cracking resistance was slightly inferior. Type D, Type F, Type G and Type H have the content of O and the total content of Ni, Cr and Mo within the scope of claim 2 of the present invention, so that the hot crack resistance and the performance of the weld metal are obtained. Was good. Since the total content of Ni, Cr and Mo is less than the range of Claim 2 of the present invention, Type E has a slightly inferior hot cracking resistance. In Type I, the O content exceeds the scope of Claim 2 of the present invention, and the total content of Ni, Cr and Mo is less than the scope of Claim 2 of the present invention, so that the toughness of the weld metal is slightly inferior. In addition, the hot cracking resistance was slightly inferior. In the case of type J, the content of O and the total content of Ni, Cr and Mo exceeded the scope of claim 2 of the present invention, so that the toughness of the weld metal was slightly inferior and the ductility was also slightly inferior. Since the type K has a content of O exceeding the range of claim 2 of the present invention, the toughness of the weld metal is slightly inferior. Type L had a slightly inferior ductility of the weld metal because the total content of Ni, Cr and Mo exceeded the scope of claim 2 of the present invention.
【００１９】[0019]
【表１】 [Table 1]
【００２０】スラグ剥離性については、開先角度が４０
°のＶ字開先の継手を１８０Ａの溶接電流で表２及び３
に示す被覆アーク溶接棒を使用して下向溶接を行った。
評価は、スラグが自然剥離したものを◎とし、スラグが
自然剥離しなかったものを×とした。Regarding the slag removability, the groove angle is 40
° V-shaped groove joints with welding current of 180A Tables 2 and 3
The downward welding was performed using the covered arc welding rod shown in FIG.
The evaluation was evaluated as ◎ when the slag was spontaneously peeled off, and as × when the slag was not spontaneously peeled off.
【００２１】耐高温割れ性については、ＪＩＳ Ｚ３１
５５Ｃ形治具拘束突合わせ溶接割れ試験に従い、板厚が
１２ｍｍでギャップを３ｍｍに調整し１７０Ａの溶接電
流で表２及び３に示す被覆アーク溶接棒を使用して試験
を行った。評価は、割れ率が５％未満のものを◎とし、
割れ率が５乃至１０％のものを○とした。Regarding hot cracking resistance, JIS Z31
According to the 55C-type jig restraint butt welding crack test, the test was performed using a coated arc welding rod shown in Tables 2 and 3 at a welding current of 170 A with a plate thickness of 12 mm and a gap of 3 mm. In the evaluation, those with a crack rate of less than 5% were evaluated as ◎,
A sample having a cracking rate of 5 to 10% was rated as ○.
【００２２】溶接金属の延性はＪＩＳ Ｚ３２１１に従
い試験を行った。評価は、溶接金属の伸びが２５％以上
のものを◎とし、溶接金属の伸びが２２乃至２４％のも
のを○とした。The ductility of the weld metal was tested according to JIS Z3211. The evaluation was evaluated as ◎ when the elongation of the weld metal was 25% or more, and evaluated as ○ when the elongation of the weld metal was 22 to 24%.
【００２３】溶接金属の靭性はＪＩＳ Ｚ３２１１に従
い試験を行った。評価は、０℃における吸収エネルギが
８０Ｊ以上のものを◎とし、４７乃至７９Ｊのものを○
とした。これらの結果を表２及び３に示す。The toughness of the weld metal was tested according to JIS Z3211. The evaluation was ◎ when the absorption energy at 0 ° C. was 80 J or more, and ○ when the absorption energy was 47 to 79 J.
And The results are shown in Tables 2 and 3.
【００２４】[0024]
【表２】 [Table 2]
【００２５】[0025]
【表３】 [Table 3]
【００２６】上記表２に示すように、本発明の請求項１
を満足する実施例No.１乃至１８はいずれも狭開先の場
合であってもスラグ剥離性が良好であると共に、耐高温
割れ性について所期の目的を達成できた。また、本発明
の請求項２を満足している実施例No.２、６、８、９、
１０、１５及び１７はスラグ剥離性、耐高温割れ性、溶
接金属の延性及び靭性が更に一層良好であった。As shown in Table 2 above, claim 1 of the present invention
In Examples Nos. 1 to 18 satisfying the following conditions, the slag peeling property was good even in the case of a narrow groove, and the intended purpose of hot cracking resistance was achieved. Further, the embodiments No. 2, 6, 8, 9, satisfying claim 2 of the present invention,
Nos. 10, 15 and 17 had even better slag peelability, hot cracking resistance, ductility and toughness of the weld metal.
【００２７】なお、実施例No.１は本発明の請求項１は
満足しているものの、鋼心線中のＯの含有量並びにＮ
ｉ、Ｃｒ及びＭｏの含有量の合計が不足しているため、
本発明の請求項２を満足していない。このため、耐高温
割れ性がやや劣った。Although Example No. 1 satisfies claim 1 of the present invention, the content of O in the steel core wire and the content of N
Because the total content of i, Cr and Mo is insufficient,
Claim 2 of the present invention is not satisfied. Therefore, the hot cracking resistance was slightly inferior.
【００２８】実施例No.３は本発明の請求項１は満足し
ているものの、鋼心線中のＯの含有量並びにＮｉ、Ｃｒ
及びＭｏの含有量の合計が不足しているため、本発明の
請求項２を満足していない。このため、耐高温割れ性が
やや劣った。Although Example No. 3 satisfies claim 1 of the present invention, the content of O in the steel core wire and the contents of Ni, Cr
And the total content of Mo is insufficient, so that claim 2 of the present invention is not satisfied. Therefore, the hot cracking resistance was slightly inferior.
【００２９】実施例No.４は本発明の請求項１は満足し
ているものの、鋼心線中のＯの含有量が不足していると
共に、鋼心線中のＮｉ、Ｃｒ及びＭｏの含有量が過多で
あるため、本発明の請求項２を満足していない。このた
め、耐高温割れ性がやや劣り、溶接金属の延性がやや劣
った。Example No. 4 satisfies claim 1 of the present invention, but the content of O in the steel core wire is insufficient, and the content of Ni, Cr and Mo in the steel core wire is not sufficient. Since the amount is too large, claim 2 of the present invention is not satisfied. Therefore, the hot cracking resistance was slightly inferior, and the ductility of the weld metal was slightly inferior.
【００３０】実施例No.５は本発明の請求項１は満足し
ているものの、鋼心線中のＯの含有量が不足し、本発明
の請求項２を満足していない。このため、耐高温割れ性
がやや劣った。Although Example No. 5 satisfies claim 1 of the present invention, the content of O in the steel core wire is insufficient and does not satisfy claim 2 of the present invention. Therefore, the hot cracking resistance was slightly inferior.
【００３１】実施例No.７は本発明の請求項１は満足し
ているものの、鋼心線中のＮｉ、Ｃｒ及びＭｏの含有量
が不足し、本発明の請求項２は満足していない。このた
め、耐高温割れ性がやや劣った。Example No. 7 satisfies claim 1 of the present invention, but the content of Ni, Cr and Mo in the steel core wire is insufficient, and claim 2 of the present invention does not. . Therefore, the hot cracking resistance was slightly inferior.
【００３２】実施例No.１１は本発明の請求項１は満足
しているものの、鋼心線中のＯの含有量が過多であると
共に鋼心線中のＮｉ、Ｃｒ及びＭｏの含有量が不足して
いるため、本発明の請求項２を満足していない。このた
め、耐高温割れ性及び溶接金属の靭性がやや劣った。Although Example No. 11 satisfies claim 1 of the present invention, the steel core has an excessive O content and the steel core has Ni, Cr and Mo contents. Due to the shortage, claim 2 of the present invention is not satisfied. Therefore, the hot cracking resistance and the toughness of the weld metal were slightly inferior.
【００３３】実施例No.１２は本発明の請求項１は満足
しているものの、鋼心線中のＯの含有量が過多であると
共に鋼心線中のＮｉ、Ｃｒ及びＭｏの含有量が過多であ
るため、本発明の請求項２を満足していない。このた
め、溶接金属の延性及び靭性がやや劣った。Although Example No. 12 satisfies claim 1 of the present invention, the steel core wire has an excessive O content and the steel core wire has Ni, Cr and Mo contents. Since it is excessive, claim 2 of the present invention is not satisfied. For this reason, the ductility and toughness of the weld metal were slightly inferior.
【００３４】実施例No.１３は本発明の請求項１は満足
しているものの、鋼心線中のＯの含有量が過多であり、
本発明の請求項２を満足していない。このため、溶接金
属の靭性がやや劣った。Example No. 13 satisfies claim 1 of the present invention, but the content of O in the steel core wire is excessive,
Claim 2 of the present invention is not satisfied. For this reason, the toughness of the weld metal was slightly inferior.
【００３５】実施例No.１４は本発明の請求項１は満足
しているものの、鋼心線中のＯの含有量並びにＮｉ、Ｃ
ｒ及びＭｏの含有量が不足しているため、本発明の請求
項２を満足していない。このため、耐高温割れ性がやや
劣った。Example No. 14 satisfies claim 1 of the present invention, but the content of O in the steel core wire and Ni, C
Since the contents of r and Mo are insufficient, claim 2 of the present invention is not satisfied. Therefore, the hot cracking resistance was slightly inferior.
【００３６】実施例No.１６は本発明の請求項１は満足
しているものの、鋼心線中のＯの含有量並びにＮｉ、Ｃ
ｒ及びＭｏの含有量が不足しているため、本発明の請求
項２を満足していない。このため、耐高温割れ性がやや
劣った。Although Example No. 16 satisfies claim 1 of the present invention, the content of O in the steel core wire and Ni, C
Since the contents of r and Mo are insufficient, claim 2 of the present invention is not satisfied. Therefore, the hot cracking resistance was slightly inferior.
【００３７】実施例No.１８は本発明の請求項１は満足
しているものの、Ｎｉ、Ｃｒ及びＭｏの含有量が過多で
あるため、本発明の請求項２を満足していない。このた
め、溶接金属の延性がやや劣った。Example No. 18 satisfies claim 1 of the present invention, but does not satisfy claim 2 of the present invention because the contents of Ni, Cr and Mo are excessive. For this reason, the ductility of the weld metal was slightly inferior.
【００３８】一方、表３に示す本発明の範囲を外れる比
較例No.３７乃至４４においては、スラグ剥離性又は耐
高温割れ性について良好な結果を得ることができなかっ
た。On the other hand, in Comparative Examples Nos. 37 to 44 out of the range of the present invention shown in Table 3, good results could not be obtained with respect to slag peeling property or hot cracking resistance.
【００３９】比較例No.３７は被覆剤中のＳｎの含有量
が本発明の範囲未満であるためスラグ剥離性が劣り、鋼
心線中のＯの含有量並びにＮｉ、Ｃｒ及びＭｏの含有量
の合計が本発明の範囲未満であるため耐高温割れ性がや
や劣った。In Comparative Example No. 37, since the Sn content in the coating agent was less than the range of the present invention, the slag removability was poor, and the O content and the Ni, Cr and Mo contents in the steel core wire were reduced. Is less than the range of the present invention, the hot cracking resistance was slightly inferior.
【００４０】比較例No.３８は被覆剤中のＳｎの含有量
が本発明の範囲未満であるため、スラグ剥離性が劣っ
た。Comparative Example No. 38 was inferior in slag removability because the content of Sn in the coating agent was less than the range of the present invention.
【００４１】比較例No.３９は被覆剤中のＳｎの含有量
が本発明の範囲未満であるため、スラグ剥離性が劣っ
た。Comparative Example No. 39 was inferior in slag removability because the content of Sn in the coating agent was less than the range of the present invention.
【００４２】比較例No.４０は被覆剤中のＳｎの含有量
が本発明の範囲未満であるためスラグ剥離性が劣り、鋼
心線中のＯの含有量が本発明の範囲を超えているため溶
接金属の靭性がやや劣り、Ｎｉ、Ｃｒ及びＭｏの含有量
の合計が本発明の範囲を超えているため溶接金属の延性
がやや劣った。In Comparative Example No. 40, since the Sn content in the coating agent was less than the range of the present invention, the slag removability was poor, and the O content in the steel core wire exceeded the range of the present invention. Therefore, the toughness of the weld metal was slightly inferior, and the ductility of the weld metal was slightly inferior since the total content of Ni, Cr and Mo exceeded the range of the present invention.
【００４３】比較例No.４１は被覆剤中のＳｎの含有量
が本発明の範囲を超えていると共に、鋼心線中のＯの含
有量並びにＮｉ、Ｃｒ及びＭｏの含有量の合計が本発明
の範囲未満であるため、耐高温割れ性が劣った。In Comparative Example No. 41, the Sn content in the coating agent exceeded the range of the present invention, and the total content of O, Ni, Cr and Mo in the steel core wire was Since it is less than the range of the invention, the hot cracking resistance was inferior.
【００４４】比較例No.４２は被覆剤中のＳｎの含有量
が本発明の範囲を超えているため、耐高温割れ性が劣っ
た。Comparative Example No. 42 was inferior in hot cracking resistance because the content of Sn in the coating material exceeded the range of the present invention.
【００４５】比較例No.４３は被覆剤中のＳｎの含有量
が本発明の範囲を超えていると共に、鋼心線中のＯの含
有量並びにＮｉ、Ｃｒ及びＭｏの含有量の合計が本発明
の範囲未満であるため、耐高温割れ性が劣った。In Comparative Example No. 43, the Sn content in the coating material exceeded the range of the present invention, and the total content of O and Ni, Cr and Mo in the steel core wire was Since it is less than the range of the invention, the hot cracking resistance was inferior.
【００４６】比較例No.４４は被覆剤中のＳｎの含有量
が本発明の範囲を超えているため、耐高温割れ性が劣
り、鋼心線中のＯの含有量が本発明の範囲を超えている
ため、溶接金属の靭性がやや劣り、Ｎｉ、Ｃｒ及びＭｏ
の含有量の合計が本発明の範囲を超えているため、溶接
金属の延性がやや劣った。In Comparative Example No. 44, since the Sn content in the coating agent exceeded the range of the present invention, the hot cracking resistance was poor, and the O content in the steel core wire was within the range of the present invention. , The toughness of the weld metal is slightly inferior, Ni, Cr and Mo
, The total ductility of the weld metal was slightly inferior because the total content of the weld metal exceeded the range of the present invention.
【００４７】第２実施例 表１に示す化学成分の鋼心線を使用して表４及び５に示
す低水素系被覆アーク溶接棒を試作した。なお、この低
水素系被覆アーク溶接棒は鋼心線の直径が４．０ｍｍ
で、被覆剤の直径が６．２５ｍｍである。 Second Example Using a steel core wire having the chemical composition shown in Table 1, low-hydrogen-based coated arc welding rods shown in Tables 4 and 5 were prototyped. In addition, the diameter of the steel core wire of this low hydrogen system coated arc welding rod is 4.0 mm.
And the diameter of the coating agent is 6.25 mm.
【００４８】スラグ剥離性については、開先角度が４５
°のＶ字開先の継手を１７０Ａの溶接電流で表４及び５
に示す被覆アーク溶接棒を使用して下向溶接を行った。
評価は、スラグが自然剥離したものを◎とし、スラグが
自然剥離しなかったものを×とした。Regarding the slag removability, the groove angle was 45
° V-shaped groove joint at 170 A welding current Tables 4 and 5
The downward welding was performed using the covered arc welding rod shown in FIG.
The evaluation was evaluated as ◎ when the slag was spontaneously peeled off, and as × when the slag was not spontaneously peeled off.
【００４９】耐高温割れ性については、ＪＩＳ Ｚ３１
５５Ｃ形治具拘束突合わせ溶接割れ試験に従い、板厚が
１９ｍｍでギャップを３．０ｍｍに調整し、１７０Ａの
溶接電流で表４及び５に示す被覆アーク溶接棒を使用し
て試験を行った。評価は、割れ率が５％未満のものを◎
とし、割れ率が５乃至１０％のものを○とした。Regarding hot cracking resistance, JIS Z31
According to the 55C type jig restraint butt welding crack test, the thickness was adjusted to 19 mm and the gap was adjusted to 3.0 mm, and the test was performed using a coated arc welding rod shown in Tables 4 and 5 at a welding current of 170 A. In the evaluation, those having a crack rate of less than 5% were evaluated as ◎
, And those having a crack rate of 5 to 10% were evaluated as ○.
【００５０】溶接金属の延性はＪＩＳ Ｚ３２１１に従
い試験を行った。評価は、溶接金属の伸びが２８％以上
のものを◎とし、溶接金属の伸びが２５乃至２７％のも
のを○とした。The ductility of the weld metal was tested according to JIS Z3211. The evaluation was evaluated as ◎ when the elongation of the weld metal was 28% or more, and evaluated as ○ when the elongation of the weld metal was 25 to 27%.
【００５１】溶接金属の靭性はＪＩＳ Ｚ３２１１に従
い試験を行った。評価は、０℃における吸収エネルギが
１００Ｊ以上のものを◎とし、４７乃至９９Ｊのものを
○とした。これらの結果を表４及び５に示す。The toughness of the weld metal was tested according to JIS Z3211. The evaluation was ◎ when the absorption energy at 0 ° C. was 100 J or more, and ○ when the absorption energy was 47 to 99 J. The results are shown in Tables 4 and 5.
【００５２】[0052]
【表４】 [Table 4]
【００５３】[0053]
【表５】 [Table 5]
【００５４】上記表４に示すように、本発明の請求項１
を満足する実施例No.１９乃至３６はいずれも狭開先の
場合であってもスラグ剥離性が良好であると共に、耐高
温割れ性について所期の目的を達成できた。また、実施
例No.２０、２４、２６、２７、２８、３３及び３５は
スラグ剥離性、耐高温割れ性、溶接金属の延性及び靭性
が更に一層良好であった。As shown in Table 4 above, claim 1 of the present invention
In all of Examples Nos. 19 to 36 satisfying the following conditions, the slag peeling property was good even in the case of a narrow groove, and the intended purpose of hot cracking resistance was achieved. In Examples 20, 24, 26, 27, 28, 33 and 35, the slag peeling property, hot cracking resistance, ductility and toughness of the weld metal were even better.
【００５５】なお、実施例No.１９は本発明の請求項１
は満足しているものの、鋼心線中のＯの含有量並びにＮ
ｉ、Ｃｒ及びＭｏの含有量の合計が不足しているため、
本発明の請求項２を満足していない。このため、耐高温
割れ性がやや劣った。Incidentally, Embodiment No. 19 is the first embodiment of the present invention.
Is satisfied, but the content of O in the steel core wire and N
Because the total content of i, Cr and Mo is insufficient,
Claim 2 of the present invention is not satisfied. Therefore, the hot cracking resistance was slightly inferior.
【００５６】実施例No.２１は本発明の請求項１は満足
しているものの、鋼心線中のＯの含有量並びにＮｉ、Ｃ
ｒ及びＭｏの含有量の合計が不足しているため、本発明
の請求項２を満足していない。このため、耐高温割れ性
がやや劣った。Although Example No. 21 satisfies claim 1 of the present invention, the content of O in the steel core wire, Ni, C
Claim 2 of the present invention is not satisfied because the sum of the contents of r and Mo is insufficient. Therefore, the hot cracking resistance was slightly inferior.
【００５７】実施例No.２２は本発明の請求項１は満足
しているものの、鋼心線中のＯの含有量が不足すると共
に、鋼心線中のＮｉ、Ｃｒ及びＭｏの含有量の合計が過
多であるため、本発明の請求項２を満足していない。こ
のため、耐高温割れ性及び溶接金属の延性がやや劣っ
た。Example No. 22 satisfies claim 1 of the present invention, but the content of O in the steel core wire is insufficient, and the content of Ni, Cr and Mo in the steel core wire is low. Since the total is too large, claim 2 of the present invention is not satisfied. Therefore, the hot cracking resistance and the ductility of the weld metal were slightly inferior.
【００５８】実施例No.２３は本発明の請求項１は満足
しているものの、鋼心線中のＯの含有量が不足している
ため、本発明の請求項２を満足していない。このため、
耐高温割れ性がやや劣った。Example No. 23 satisfies claim 1 of the present invention, but does not satisfy claim 2 of the present invention because the O content in the steel core wire is insufficient. For this reason,
The hot cracking resistance was slightly inferior.
【００５９】実施例No.２５は本発明の請求項１は満足
しているものの、鋼心線中のＮｉ、Ｃｒ及びＭｏの含有
量の合計が不足しているため、本発明の請求項２を満足
していない。このため、耐高温割れ性がやや劣った。Although Example No. 25 satisfies Claim 1 of the present invention, the total content of Ni, Cr and Mo in the steel core wire is insufficient, and therefore Claim 2 of the present invention is satisfied. Not satisfied. Therefore, the hot cracking resistance was slightly inferior.
【００６０】実施例No.２９は本発明の請求項１は満足
しているものの、鋼心線中のＯの含有量が過多であり、
Ｎｉ、Ｃｒ及びＭｏの含有量が不足しているため、本発
明の請求項２を満足していない。このため、溶接金属の
靭性がやや劣ると共に、耐高温割れ性がやや劣った。Although Example No. 29 satisfies Claim 1 of the present invention, the content of O in the steel core wire is excessive,
Since the contents of Ni, Cr and Mo are insufficient, claim 2 of the present invention is not satisfied. For this reason, the toughness of the weld metal was slightly inferior and the hot cracking resistance was slightly inferior.
【００６１】実施例No.３０は本発明の請求項１は満足
しているものの、鋼心線中のＯの含有量が過多であると
共に、鋼心線中のＮｉ、Ｃｒ及びＭｏの含有量の合計が
過多であるため、本発明の請求項２を満足していない。
このため、溶接金属の靭性及び延性がやや劣った。Although Example No. 30 satisfies claim 1 of the present invention, the content of O in the steel core wire is excessive, and the content of Ni, Cr and Mo in the steel core wire is high. Does not satisfy claim 2 of the present invention.
For this reason, the toughness and ductility of the weld metal were slightly inferior.
【００６２】実施例No.３１は本発明の請求項１は満足
しているものの、鋼心線中のＯの含有量が過多であるた
め、本発明の請求項２を満足していない。このため、溶
接金属の靭性がやや劣った。Example No. 31 satisfies claim 1 of the present invention, but does not satisfy claim 2 of the present invention because the O content in the steel core wire is excessive. For this reason, the toughness of the weld metal was slightly inferior.
【００６３】実施例No.３２は本発明の請求項１は満足
しているものの、鋼心線中のＯの含有量並びにＮｉ、Ｃ
ｒ及びＭｏの含有量の合計が不足しているため、本発明
の請求項２を満足していない。このため、耐高温割れ性
がやや劣った。Although Example No. 32 satisfies claim 1 of the present invention, the content of O in the steel core wire, Ni, C
Claim 2 of the present invention is not satisfied because the sum of the contents of r and Mo is insufficient. Therefore, the hot cracking resistance was slightly inferior.
【００６４】実施例No.３４は本発明の請求項１は満足
しているものの、鋼心線中のＯの含有量並びにＮｉ、Ｃ
ｒ及びＭｏの含有量の合計が不足しているため、本発明
の請求項２を満足していない。このため、耐高温割れ性
がやや劣った。Although Example No. 34 satisfies claim 1 of the present invention, the content of O in the steel core wire, Ni, C
Claim 2 of the present invention is not satisfied because the sum of the contents of r and Mo is insufficient. Therefore, the hot cracking resistance was slightly inferior.
【００６５】実施例No.３６は本発明の請求項１は満足
しているものの、Ｎｉ、Ｃｒ及びＭｏの含有量の合計が
過多であるため、本発明の請求項２を満足していない。
このため、溶接金属の延性がやや劣った。Example No. 36 satisfies claim 1 of the present invention, but does not satisfy claim 2 of the present invention because the total content of Ni, Cr and Mo is excessive.
For this reason, the ductility of the weld metal was slightly inferior.
【００６６】一方、表５に示す本発明の範囲を外れる比
較例No.４５乃至５２においては、スラグ剥離性又は耐
高温割れ性について良好な結果を得ることができなかっ
た。On the other hand, in Comparative Examples Nos. 45 to 52 which are out of the range of the present invention shown in Table 5, good results could not be obtained with respect to the slag peeling property or the hot cracking resistance.
【００６７】比較例No.４５は被覆剤中のＳｎの含有量
が本発明の範囲未満であるためスラグ剥離性が劣り、鋼
心線中のＯの含有量並びにＮｉ、Ｃｒ及びＭｏの含有量
の合計が本発明の範囲未満であるため耐高温割れ性がや
や劣った。In Comparative Example No. 45, since the Sn content in the coating agent was less than the range of the present invention, the slag removability was poor, and the O content and the Ni, Cr and Mo contents in the steel core wire were reduced. Is less than the range of the present invention, the hot cracking resistance was slightly inferior.
【００６８】比較例No.４６は被覆剤中のＳｎの含有量
が本発明の範囲未満であるため、スラグ剥離性が劣っ
た。Comparative Example No. 46 was inferior in slag removability because the content of Sn in the coating agent was less than the range of the present invention.
【００６９】比較例No.４７は被覆剤中のＳｎの含有量
が本発明の範囲未満であるため、スラグ剥離性が劣っ
た。Comparative Example No. 47 was inferior in slag removability because the content of Sn in the coating agent was less than the range of the present invention.
【００７０】比較例No.４８は被覆剤中のＳｎの含有量
が本発明の範囲未満であるためスラグ剥離性が劣り、鋼
心線中のＯの含有量が本発明の範囲を超えているため溶
接金属の靭性がやや劣り、Ｎｉ、Ｃｒ及びＭｏの含有量
の合計が本発明の範囲を超えているため溶接金属の延性
がやや劣った。In Comparative Example No. 48, since the Sn content in the coating agent was less than the range of the present invention, the slag releasability was poor, and the O content in the steel core wire exceeded the range of the present invention. Therefore, the toughness of the weld metal was slightly inferior, and the ductility of the weld metal was slightly inferior since the total content of Ni, Cr and Mo exceeded the range of the present invention.
【００７１】比較例No.４９は被覆剤中のＳｎの含有量
が本発明の範囲を超えていると共に、鋼心線中のＯの含
有量並びにＮｉ、Ｃｒ及びＭｏの含有量の合計が本発明
の範囲未満であるため、耐高温割れ性が劣った。In Comparative Example No. 49, the Sn content in the coating agent exceeded the range of the present invention, and the total content of O and Ni, Cr and Mo in the steel core wire was Since it is less than the range of the invention, the hot cracking resistance was inferior.
【００７２】比較例No.５０は被覆剤中のＳｎの含有量
が本発明の範囲を超えているため、耐高温割れ性が劣っ
た。Comparative Example No. 50 was inferior in hot cracking resistance because the content of Sn in the coating agent exceeded the range of the present invention.
【００７３】比較例No.５１は被覆剤中のＳｎの含有量
が本発明の範囲を超えていると共に、鋼心線中のＯの含
有量並びにＮｉ、Ｃｒ及びＭｏの含有量の合計が本発明
の範囲未満であるため、耐高温割れ性が劣った。In Comparative Example No. 51, the Sn content in the coating agent exceeded the range of the present invention, and the total content of O and Ni, Cr and Mo in the steel core wire was Since it is less than the range of the invention, the hot cracking resistance was inferior.
【００７４】比較例No.５２は被覆剤中のＳｎの含有量
が本発明の範囲を超えているため、耐高温割れ性が劣
り、鋼心線中のＯの含有量が本発明の範囲を超えている
ため、溶接金属の靭性がやや劣り、Ｎｉ、Ｃｒ及びＭｏ
の含有量の合計が本発明の範囲を超えているため、溶接
金属の延性がやや劣った。In Comparative Example No. 52, since the Sn content in the coating agent exceeded the range of the present invention, the hot cracking resistance was poor, and the O content in the steel core wire was within the range of the present invention. , The toughness of the weld metal is slightly inferior, Ni, Cr and Mo
, The total ductility of the weld metal was slightly inferior because the total content of the weld metal exceeded the range of the present invention.
【００７５】[0075]
【発明の効果】以上詳述したように本発明においては、
被覆剤のＳｎの含有量を調整することにより、狭開先で
あってもスラグを自然剥離させることができると共に、
耐高温割れ性を向上させることができる。従って、開先
が狭開先であってもスラグが自然剥離するため、溶接時
間を短縮することができる。また、スラグが自然剥離す
るため、スラグ除去時間を短縮することができアークタ
イム率を向上させることができる。As described in detail above, in the present invention,
By adjusting the Sn content of the coating agent, the slag can be spontaneously peeled even with a narrow groove,
Hot cracking resistance can be improved. Therefore, even if the groove is a narrow groove, the slag is spontaneously separated, so that the welding time can be reduced. In addition, since the slag is spontaneously separated, the slag removal time can be shortened and the arc time ratio can be improved.
【００７６】また、鋼心線のＯの含有量並びにＮｉ、Ｃ
ｒ及びＭｏの含有量の合計を調整することにより耐高温
割れ性をより一層向上させることができると共に、溶接
金属の延性及び靭性をより一層向上させることができ
る。Further, the content of O in the steel core wire and Ni, C
By adjusting the total content of r and Mo, the hot crack resistance can be further improved, and the ductility and toughness of the weld metal can be further improved.
───────────────────────────────────────────────────── フロントページの続き (56)参考文献 特開 平10−272594（ＪＰ，Ａ) 特開 昭58−151991（ＪＰ，Ａ) 特開 平２−205293（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) B23K 35/30,35/365,35/368 ────────────────────────────────────────────────── ─── Continuation of front page (56) References JP-A-10-272594 (JP, A) JP-A-58-151991 (JP, A) JP-A-2-205293 (JP, A) (58) Field (Int.Cl. 7 , DB name) B23K 35 / 30,35 / 365,35 / 368
Claims (4)
たＳｎの酸化物及び／又は単体をＳｎ換算で０．００２
乃至０．５質量％含有する被覆剤と、を有することを特
徴とする被覆アーク溶接棒。1. A steel core wire and a Sn oxide and / or a simple substance applied to the outer periphery of the steel core wire are 0.002 in Sn conversion.
A coating agent containing from 0.5 to 0.5% by mass .
０．０２０質量％含有し、Ｎｉ、Ｃｒ及びＭｏからなる
群から選択された少なくとも１種を総量で０．０１０乃
至０．１０質量％含有することを特徴とする請求項１に
記載の被覆アーク溶接棒。2. The steel core wire contains O in an amount of 0.0010 to 0.020% by mass, and contains at least one selected from the group consisting of Ni, Cr and Mo in a total amount of 0.010 to 0.10. 2. The coated arc welding rod according to claim 1, wherein the coating arc is contained by mass %. 3.
ことを特徴とする請求項１又は２に記載の被覆アーク溶
接棒。3. The coated arc welding rod according to claim 1, wherein the coating agent is a non-low hydrogen coating agent.
とを特徴とする請求項１又は２に記載の被覆アーク溶接
棒。4. The coated arc welding rod according to claim 1, wherein the coating agent is a low hydrogen-based coating agent.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11075801A JP3120977B2 (en) | 1999-03-19 | 1999-03-19 | Covered arc welding rod |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11075801A JP3120977B2 (en) | 1999-03-19 | 1999-03-19 | Covered arc welding rod |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2000263286A JP2000263286A (en) | 2000-09-26 |
| JP3120977B2 true JP3120977B2 (en) | 2000-12-25 |
Family
ID=13586678
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP11075801A Expired - Lifetime JP3120977B2 (en) | 1999-03-19 | 1999-03-19 | Covered arc welding rod |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3120977B2 (en) |
-
1999
- 1999-03-19 JP JP11075801A patent/JP3120977B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JP2000263286A (en) | 2000-09-26 |
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