JPS61147990A - Submerged arc welding wire for high tension steel - Google Patents

Abstract

PURPOSE:To provide a titled wire which yields a weld metal having excellent strength and low-temp. characteristic under strict conditions by regulating the contents of C, Mn, Ni, Mo and Si which are essential components, determining the contents of Ni, C, Si and Mo in a manner as to satisfy the specific equations and consisting of the balance iron. CONSTITUTION:The wire for submerged arc welding contains, by wt%, 0.03-0.20% C, 1.60-3.00% Mn, 2.10-3.50% Ni, 0.30-1.50% Mo and <=0.25% Si as essential components, is limited to <=0.25% Cu, <=0.015% P and <=0.015% S, satisfies the conditions expressed by the equations and consists of the balance iron. The wire yields the weld metal having the outstanding strength, low-temp. toughness, crack resistance, etc. as the constituting elements and contents thereof are strictly controlled to the above-mentioned numerical values.

Description

【発明の詳細な説明】 ［産業上の利用分野］ 本発明は、例えば６０Ｋｇｆ／ｍｍ２級或はそれ以上の
張力を有する高張力鋼を対象として、優れた強臀及び低
温靭性を有する溶接金属を得ることのできる潜弧溶接用
ワイヤに関するものである。Detailed Description of the Invention [Industrial Application Field] The present invention is directed to a weld metal having excellent strength and low-temperature toughness, for example, for high-tensile steel having a tensile strength of 60 Kgf/mm2 class or higher. The present invention relates to a wire for submerged arc welding that can be obtained.

［従来の技術］ 上記の様な高張力鋼は圧力容器、鉄骨橋梁、”各種建設
機器或は揚水発電所の水圧鉄管等に広く用いられている
ダ、最近これら溶接構造物の大型化及び適用範囲の拡大
が進むにつれて鋼材に対す−る要求特性は一段と厳しく
なってきている０例えば石油危機以降の原油価格高騰に
対処する為北極圏の如き水海地域にまで海洋構造物の建
設が進められており、この様な厳しい自然環境に耐える
一度及び低温靭性を備えた鋼材の需要が急糟している。[Prior Art] High-strength steel as described above is widely used in pressure vessels, steel bridges, various construction equipment, penstock pipes for pumped storage power plants, etc. Recently, these welded structures have been enlarged and applied. As the range continues to expand, the required characteristics for steel materials are becoming more severe.For example, in order to cope with the soaring price of crude oil after the oil crisis, construction of offshore structures is proceeding even in aquatic regions such as the Arctic Circle. Demand for steel materials with high-temperature and low-temperature toughness that can withstand such harsh natural environments is rapidly increasing.

それにつれて溶接材料についても母材に匹敵する性能を
確保することが溶接分野における最近の重要な課題とな
っている。具体的には、従来のＨＴ６０系鋼材を対象と
する溶接部に要求される低温靭性値は一２０℃前後の価
を基準に設定されていたが、最近では一６０℃といった
低温域における安全性評価が必要になってきた。しかも
昨今の厳しい国際競争に鑑みれば低コスト化も不可欠の
要請であり、こうした意味では溶接能率の高い潜弧溶接
法が最も期待されるところであり、前述の如き苛酷な条
件下での安全性基準に適合し得る潜弧溶接用ワイヤの開
発が各社で積極的に進められている。Accordingly, it has recently become an important issue in the welding field to ensure the performance of welding materials comparable to that of the base metal. Specifically, the low-temperature toughness values required for welds of conventional HT60 series steel materials were set based on values around -20°C, but recently, safety in the low-temperature range of -60°C has been established. Evaluation has become necessary. Moreover, in view of the recent severe international competition, cost reduction is an essential requirement, and in this sense, the submerged arc welding method with high welding efficiency is the most promising, and it meets the safety standards under the harsh conditions mentioned above. Various companies are actively developing wires for submerged arc welding that are compatible with the above.

尚後述する本発明と比較的類似した先行技術としては特
開昭５８−１５７５９４号に記載された発明がある。し
かしながらこの公開発明は下記の点で本発明とは目的及
び構成が全く異なるものである。As a prior art relatively similar to the present invention which will be described later, there is an invention described in Japanese Patent Application Laid-Open No. 157594/1983. However, this disclosed invention is completely different in purpose and structure from the present invention in the following points.

■この公開発明では母材の成分も特定されており、母材
と溶接材料の組合せにより目的を達成しようとするもの
であるが、本願発明では母材成分との相互作用を問題に
していない。■ In this disclosed invention, the components of the base metal are also specified, and the objective is to be achieved by a combination of the base material and the welding material, but the present invention does not consider interaction with the base material components as an issue.

ｑ）公開発明では特に溶接後熱処理による焼戻し脆化特
性を改善したものであるのに対し、本発明では溶接のま
まの状態で高度の性能を確保しようとするものである。q) In contrast to the disclosed invention, in which the tempering embrittlement properties are particularly improved by post-weld heat treatment, the present invention aims to ensure high performance in the as-welded state.

として規定しているが、本発明ではＴｉをＡＩ、Ｚｒ、
Ｖ、Ｎｂと同様の脱酸成分として任意に含有させるもの
であり、しかもＴｉ量をＡＩ、Ｚｒ、Ｖ、Ｎｂ等と合わ
せたＭｏ量との相対的含有率で規定しており、Ｔ１添加
の目的及び含有率設定の趣旨が両発明は全く異なる。However, in the present invention, Ti is defined as AI, Zr,
It is optionally included as a deoxidizing component similar to V and Nb, and the amount of Ti is defined by the relative content of the amount of Mo combined with AI, Zr, V, Nb, etc. The two inventions are completely different in purpose and content rate setting.

［発明が解決しようとする問題点］ ところが潜弧溶接においては、「溶接能率が高い」とい
う特性を有効に発揮させるべく比較的高入熱の溶接施工
条件が採用され、１パス当たりの溶着金属量が多い為に
母材及び先行溶接金属に対する熱影響が大きく、前述の
様な高レベルの強度と低温靭性値を同時に満足する溶接
継手を得ることは非常に困難である。[Problems to be solved by the invention] However, in submerged arc welding, welding conditions with relatively high heat input are adopted in order to effectively exhibit the characteristic of "high welding efficiency", and the weld metal per pass is reduced. Since the amount is large, the thermal effect on the base metal and the preceding weld metal is large, and it is extremely difficult to obtain a welded joint that simultaneously satisfies the above-mentioned high level of strength and low-temperature toughness.

本発明はこうした状況のもとで、潜弧溶接法本来の溶接
能率を保持しつつ前述の様な厳しい要求特性を満足する
溶接金属を得ることのできる高張力鋼用の潜弧溶接用ワ
イヤを提供しようとするものである。Under these circumstances, the present invention has developed a wire for submerged arc welding for high-strength steel, which can obtain weld metal that satisfies the above-mentioned strict requirements while maintaining the welding efficiency inherent in submerged arc welding. This is what we are trying to provide.

［問題点を解決する為の手段］ 本発明に係る潜弧溶接用ワイヤの構成はＧ：　０．０３
〜０．２０２ Ｍｎ：　１．６０〜３．００２ Ｎｉ：　２．１０〜３．５０％ Ｍｏ：　０．３０〜０．２０２ Ｓｉ：　０．２５Ｘ以下 を必須成分として含み、且つ Ｃｕ≦０．２５ｍ Ｐ≦０．０１５％ Ｓ≦０．０１５％ に夫々制限され、残部が鉄及び不可避不純物からなり、
上記成分のうちＮｉ、Ｃ，Ｓｔ及びＭｏの各含有率が下
記式の関係を満たす様に成分調整してなるところにＩ旨
を有するものであり。[Means for solving the problem] The configuration of the submerged arc welding wire according to the present invention is G: 0.03
~0.202 Mn: 1.60~3.002 Ni: 2.10~3.50% Mo: 0.30~0.202 Si: Contains 0.25X or less as an essential component, and Cu≦0.25m P≦0.015% and S≦0.015%, respectively, with the remainder consisting of iron and inevitable impurities,
Among the above components, the composition is adjusted so that the contents of Ni, C, St, and Mo satisfy the relationship of the following formula.

［Ｎｉ　（＄）　＋　３０Ｘ　Ｃ（Ｘ）≦８（ｚ）３Ｓ
ｉ（駕）≦Ｍｏ（＄） 他の構成は上記の構成に加えてワイヤ中に０．２０％以
下のＣｒを必須成分として含有せしめると共に。[Ni ($) + 30X C(X)≦8(z)3S
i (paranse)≦Mo($) Another configuration is that in addition to the above configuration, the wire contains 0.20% or less of Cr as an essential component.

３１１１：ｒ（Ｘ）≦Ｍｏ（＄） 旨を有し、更に他の構成は、上記の構成に加えて、（Ｔ
ｉ、Ａ１．Ｚｒ及びＮｂよりなる群から選択される１種
類以上）をワイヤ中に合計量で０．１％以下含有させる
と共に １０Ｘ［Ｔｉ（＄）＋ＡＩ（＄）　＋Ｚｒ（＄）　＋Ｖ
（ｎ＋Ｎｂ（駕）１≦Ｍｏ（駕） の関係を満たす様に成分調整してなるところに要旨が存
在する。3111: r(X)≦Mo($), and other configurations include (T
i, A1. One or more types selected from the group consisting of Zr and Nb) are contained in the wire in a total amount of 0.1% or less, and 10X [Ti ($) + AI ($) + Zr ($) +V
The gist lies in the fact that the components are adjusted so as to satisfy the relationship (n+Nb (parallel) 1≦Mo (parallel)).

［作用］ 以下構成元素の種類及び含有率範囲を厳密に定めた理由
を明らかにする。[Effect] The reasons for strictly determining the types and content ranges of constituent elements will be explained below.

Ｃ：　０．０３〜０．２０２ 例えば６０Ｋｇｆ／■ｍ２　といった高強度の溶接金属
を得るうえで不可欠の元素であり、　０．０３％未満で
は目的にかなう強度を確保できなくなる。但し多過ぎる
と溶接金属が過度に硬質化し靭性が悪くなるので、　　
０．２０＄以下に抑えなければならない。C: 0.03 to 0.202 This is an essential element for obtaining a high-strength weld metal, such as 60 Kgf/m2, and if it is less than 0.03%, it will not be possible to secure the desired strength. However, if it is too much, the weld metal will become excessively hard and its toughness will deteriorate.
It must be kept below $0.20.

Ｍｎ：　１．６０〜３．００ｇ 比較的低Ｃ量のもとで目的にかなう溶接金属強度を確保
する為には、１．６０％以上のＭｎを含有させなければ
ならない、しかし多過ぎると金属組織が粗大化し靭性が
乏しくなるので３．００％以下に抑えなければならない
。Mn: 1.60-3.00g In order to ensure the desired weld metal strength with a relatively low C content, it is necessary to contain 1.60% or more of Mn, but if it is too large, the metal Since the structure becomes coarse and the toughness becomes poor, it must be kept below 3.00%.

Ｎｉ：　２．１０〜３．５０％ 一６０℃といった低温域における高靭性を確保する為に
は２．１０％以上含有させなければならない、しかし３
．５０％を超えて含有させてもそれ以上の低温靭性改善
効果は発揮されず、経済的に不利であるばかりでなく、
Ｃとの相互作用により高温割れが発生し易くなるので、
３．５０％に抑えるべきである。Ni: 2.10~3.50% In order to ensure high toughness in the low temperature range of -60°C, it must be contained at 2.10% or more, but 3.
．． Even if the content exceeds 50%, no further effect of improving low-temperature toughness will be exhibited, which is not only economically disadvantageous, but also
Because high-temperature cracking is likely to occur due to interaction with C,
It should be kept at 3.50%.

Ｍｏ：　０．３０２　Ｎ１．５０ｇ 強度増大に寄与する他、焼入れ性を向上して靭性を高め
る作用があり、０．３％未満ではこれらの効果が有効に
発揮されない、但し１．５０％を超えると炭化物の析出
等が著しくなって焼戻し脆化を起こし、かえって靭性が
低下する。Mo: 0.302 N1.50g In addition to contributing to strength increase, it has the effect of improving hardenability and increasing toughness, and if it is less than 0.3%, these effects will not be effectively exhibited, but if it exceeds 1.50% The precipitation of carbides and the like becomes significant, causing tempering embrittlement, which actually reduces toughness.

Ｓｉ：　０．２５Ｘ以下 に低融点酸化物となって析出し靭性を著しく阻害する。Si: 0.25X or less It precipitates as a low melting point oxide and significantly impairs toughness.

こうした問題を回避する為には最大量でも０．２５％以
下に抑えなければならず、より確実には０．１８％以下
に抑えることが望まれる。In order to avoid such problems, it is necessary to suppress the maximum amount to 0.25% or less, and more reliably, it is desirable to suppress it to 0.18% or less.

Ｃｕ：　０．２５％以下 ワイヤ防錆用のＣｕめっき材として混入してくる成分で
あり、多過ぎると低温靭性に悪影響が現われてくるので
０．２５％以下に抑えなければならない。Cu: 0.25% or less This is a component mixed as a Cu plating material for wire rust prevention. If it is too large, it will have an adverse effect on low temperature toughness, so it must be suppressed to 0.25% or less.

ｐ及びＳ：何れも０．０１５％以下 基本元素である鉄中の不純物として混入してくる有害元
素であり、靭性１曲げ性能、耐割れ性といったあらゆる
溶接性能に悪影響を及ぼすので、夫々０．０１５Ｘ以下
に抑えなければならない。p and S: Both 0.015% or less These are harmful elements that are mixed in as impurities in iron, which is a basic element, and have a negative effect on all welding performance such as toughness, bending performance, and cracking resistance, so each should be 0.015% or less. It must be kept below 0.015X.

［Ｎｉ（＄）＋３００（駕）］　６８８％　　　　　’
前述の如く潜弧溶接は比較的大入熱で行なわれるが、Ｎ
ｉ量が多過ぎると前述の如く溶接金属中の成長したデン
ドライトに沿って高温割れが発生し易くなり、こうした
高温割れは共存するＣの量こで高温割れに及ぼすＮｉ量
及びＣ量の相互作用を明確にすべく実験を行なったとこ
ろ、第１図に示ス如＜　［Ｎｉ（Ｘ）＋３０Ｘｅ（２）
］を８％以下に抑えることにより高温割れを確実に阻止
し得ることが明らかとなった。[Ni ($) + 300 (pallet)] 688%'
As mentioned above, submerged arc welding is performed with a relatively large heat input, but N
If the amount of i is too large, as mentioned above, hot cracking tends to occur along the dendrites that have grown in the weld metal, and these hot crackings are caused by the interaction between the amount of Ni and the amount of C that affects hot cracking due to the amount of coexisting C. We conducted an experiment to clarify this, and as shown in Figure 1, we found that
] It has become clear that hot cracking can be reliably prevented by suppressing the content to 8% or less.

ちなみに第１図は、下記の方法で高温割れに与えるＮｉ
及びＣの相互作用を調べた実験結果を示したものである
。即ち第２図（Ａ）　、　（Ｂ）に示す如く拘束板（Ｓ
Ｓ４１　・−９００ｍｍ”　Ｘ　１，３００ｍｍ’Ｘ　
７５ｍｍ”）　１の中央部に開先加工（Ｙ開先）を施し
た高張力鋼板（ＨＴ６０・・・８５０■ｔＪ’Ｘ３８脂
ＩＩｔ）２を拘束溶接Ｗし下記化学成分のワイヤ及びフ
ラックスを用いて潜弧溶接した後、拘束板を除去してＸ
線透過試験法により高温割れ発生状況を調べた。By the way, Figure 1 shows how Ni can be applied to hot cracking using the following method.
The results of an experiment investigating the interaction between C and C are shown. That is, as shown in Fig. 2 (A) and (B), the restraining plate (S
S41 ・-900mm"X 1,300mm'X
75mm") 1 with a beveling (Y beveling) in the center (HT60...850■tJ'X38 fat IIt) 2 was restraint welded using wire and flux with the following chemical composition. After submerged arc welding, remove the restraining plate and
The occurrence of hot cracking was investigated using the ray transmission test method.

くワイヤ成分〉 Ｃ：　０．０４〜０．００５ Ｍｎ：　１．６０〜１．９５％ Ｓｉ：　０．１２〜０．００５ Ｍｏ：　０．７５〜０．００５ Ｃｒ：　ｔｒ Ｎｉ：　　２．２　”３．３％ Ｃｕ：　０．１４〜０．００５（めっきＣｕ含む）Ｐ：
　　０．００４　〜ｏ、ｏｏｅ Ｓ：　　０．００２　〜０．００８駕 くフラックス〉 後記実施例で用いたものと同じ く溶接条件〉 ワイヤ経：４．０１層φ 電　　流：　７００　Ａ（ＡＣ） 電　　圧：３４ｖ 速　　度：　５０Ｃｍ／分 予熱温度＝１５０℃ 第１図からも明らかな様にＮｉ及びＣの含有率が夫々前
記規定範囲内に収まっている場合でも。Wire components> C: 0.04~0.005 Mn: 1.60~1.95% Si: 0.12~0.005 Mo: 0.75~0.005 Cr: tr Ni: 2.2'' 3.3% Cu: 0.14-0.005 (including plated Cu) P:
0.004 ~ o, ooe S: 0.002 ~ 0.008 high flux〉 Same welding conditions as those used in the examples below〉 Wire diameter: 4.01 layer φ Current: 700 A (AC) Voltage : 34v Speed: 50cm/min Preheating temperature = 150°C As is clear from FIG. 1, even when the Ni and C contents are within the specified ranges.

［Ｎｉ（Ｘ）＋３０×Ｃ（駕）】が８％を超えると高温
割れが発生しており、高温割れを無くす為には上記の値
を８％以下に抑えなければならない。Hot cracking occurs when [Ni(X)+30×C(k)] exceeds 8%, and in order to eliminate hot cracking, the above value must be suppressed to 8% or less.

３Ｓｉ（＄）≦Ｍｏ（＄） Ｓｉは脱酸成分として有効でありしかも溶接作業性の改
善にも有効な元素であるが、前述の如く低融点の酸化物
となって粒界に析出し靭性を著しく低下させる。ところ
が本発明者等が確認したところによると、上記Ｓｉの特
に靭性阻害作用はＭｏによって著しく抑制される現象が
見られ。3Si($)≦Mo($) Si is an element that is effective as a deoxidizing component and is also effective in improving welding workability, but as mentioned above, it becomes a low melting point oxide and precipitates at grain boundaries, reducing toughness. significantly decreases However, the present inventors have confirmed that the above-mentioned Si, particularly the toughness inhibiting effect, is significantly suppressed by Mo.

Ｓｉの含有率をＭｏ含有率の１／３以下に抑えてやれば
、ＳＬの靭性阻害作用がＭｏにより完全に消失すること
が明らかとなった。It has become clear that if the Si content is suppressed to 1/3 or less of the Mo content, the toughness inhibiting effect of SL is completely eliminated by Mo.

ちなみに第３図は、下記の方法で靭性に与えるＳｉ及び
Ｍｏの相互作用を調べた実験結果を示したものである。Incidentally, FIG. 3 shows the results of an experiment in which the interaction between Si and Mo on toughness was investigated using the method described below.

即ち第４図（Ａ）　、　（Ｂ）に示す２木ｃ７）ｅ＋束
材（ＳＳ４１・−５０ｍｍｔＸ１５０ｍｍ”　、　２本
）　１　。That is, 2 pieces of wood c7) e + bundle material (SS41・-50mmtX150mm'', 2 pieces) 1 shown in FIGS. 4(A) and 4(B).

ｌの上部に開先加工を施した高張力鋼板（ＨＴ８Ｇ・・
・４００　＋ｕ＋　ｗ、Ｘ　５００ｓａ＋”Ｘ　５０ｍ
ｍ　ｔ）　２　を拘束溶接１．、下記化学成分のワイヤ
及びフラックスを用いて潜弧溶接した後、溶接部の衝撃
試験を行なった。High tensile strength steel plate (HT8G...
・400 +u+w,X 500sa+"X 50m
m t) 2 restraint welding 1. After performing submerged arc welding using wire and flux having the chemical compositions shown below, an impact test was conducted on the welded parts.

くワイヤ成分〉 Ｃ：　０．０８〜０．００ Ｓｉ≦０．２３％ にａ：　０．３４”　１．４１％ ｃｒ：ｔｒ　　　　　　　　　　’ Ｎｉ：　　２．８２〜２．８８％ Ｃｕ：　０．１４〜０．１８！（めっきＣｕ含む）Ｐ：
　　０．００４　〜ｏ、ｏｏｅｘ Ｓ：　　０．００２　〜０．００５に くフラックス〉 後記実施例と同じ く溶接条件〉 ワイヤ径：４．０鳳膳φ 電　　流：　７００Ａ（ＡＣ） 電　　圧＝３４ｖ 速　　度：　３５ｃｍ／分 予熱φパス間温度＝１５０±２５℃ く衝撃試験〉 溶接部の板厚表面下７■■の位置よりＪＩＳ　　Ｚ３１
１２４号の試験片を採取し、−６０℃にて衝撃試験を行
なう。Wire components> C: 0.08~0.00 Si≦0.23% A: 0.34'' 1.41% cr:tr' Ni: 2.82~2.88% Cu: 0.14~ 0.18! (Including plating Cu) P:
0.004 ~ o, ooex S: 0.002 ~ 0.005 flux〉 Same welding conditions as in the example below〉 Wire diameter: 4.0 mm φ Current: 700 A (AC) Voltage = 34 V Speed : 35cm/min preheating φ interpass temperature = 150±25℃ Impact test> JIS Z31 from the position 7■■ below the plate thickness surface of the welded part
A No. 124 test piece is taken and subjected to an impact test at -60°C.

＠　：　ｖＥ−ｅｏ　＞８Ｋｇｆ＊　ｍＯ：　ｖＥ−ｓ
ｏ　＝　３．５〜８Ｋｇｆ　ｍ　ｍＸ　：　ｖＥ−ｓｏ
　＜３．５Ｋｇｆ　＊　ｔｓ第３図からも明らかな様に
、Ｓｔ含有率が前記規定範囲内に収まっている場合でも
３ｘＳｉ（Ｘ）がＭｏ（Ｘ）を上回っている場合は低温
靭性値が乏しく、目的にかなう低温靭性値を得る為には
３ＸＳｉ（駕）≦Ｍｏ（Ｘ）の嚢件を同時に満たす様に
両者の含有率を調整しなければならない。@: vE-eo >8Kgf* mO: vE-s
o = 3.5~8Kgf m mX: vE-so
<3.5Kgf * tsAs is clear from Figure 3, even if the St content is within the specified range, if 3xSi(X) exceeds Mo(X), the low temperature toughness value will be poor. In order to obtain a desired low-temperature toughness value, the content ratio of both must be adjusted so as to simultaneously satisfy the requirement of 3XSi(Si)≦Mo(X).

本発明における第１発明の構成は以上の通りであるが、
この構成に加えてワイヤ中に適量のＣｒを含有させるこ
とによって強度を更に高め、或は更にＴｉ、Ａ１．Ｚｒ
％Ｖ及びＮｂよりなる群から選択される脱酸性元素の１
種以上を含有させて溶接金属の健全性向上（ブローホー
ル等の溶接欠陥の防止）と強度向上を図ることも有効で
ある。The configuration of the first invention in the present invention is as described above,
In addition to this structure, the strength can be further increased by incorporating an appropriate amount of Cr into the wire, or by adding Ti, Al. Zr
%V and one of the deoxidizing elements selected from the group consisting of Nb
It is also effective to improve the soundness of the weld metal (prevent weld defects such as blowholes) and improve the strength by including more than 100% of the weld metal.

但しＣｒ量が多過ぎると低温靭性が悪くなるので０．２
％以下に抑えなければならず、また［Ｔｆ、Ａ１．Ｚｒ
、ｖ、Ｎｂｌの総和が多過ぎるとやはり低温靭性が劣悪
になるので０．１％以下に抑えなければならない。However, if the amount of Cr is too large, the low temperature toughness will deteriorate, so 0.2
% or less, and [Tf, A1. Zr
If the sum of , v, and Nbl is too large, the low-temperature toughness will deteriorate, so it must be suppressed to 0.1% or less.

またこれらＣｒや［Ｔｉ、Ａ１．Ｚｒ、Ｖ、Ｎｂ］によ
る靭性阻害作用もＳｉの場合と同様Ｍｏによって抑制さ
れる傾向があり、第３図に示したのと同様の実験により
Ｍｏ量との相互作用を調べたところによると、 ３　×Ｃｒ（り≦Ｍｏ（り ｌＯ×ｃＴｉ（Ｘ）＋ＡＩ（Ｘ）　＋Ｚｒ（％）　＋Ｖ
Ｃり＋Ｗｂ（％）］≦Ｎ。Moreover, these Cr, [Ti, A1. The toughness inhibiting effect of Zr, V, Nb] also tends to be suppressed by Mo, as in the case of Si, and according to an experiment similar to that shown in Fig. 3, which investigated the interaction with the amount of Mo, 3 ×Cr(ri≦Mo(rilO×cTi(X)+AI(X) +Zr(%) +V
C + Wb (%)]≦N.

の要件を満たす様に各元素の含有率を調整してやれば、
高レベルの低温靭性を確保し得ることが確認された。If the content of each element is adjusted to meet the requirements of
It was confirmed that a high level of low-temperature toughness could be ensured.

本発明は以上の様に構成されており、ワイヤの構成元素
及び含有率を厳密に規定することによって、強度、低温
靭性及び耐割れ性等の卓越した溶接金属を得ることがで
きる。尚本発明のワイヤと組合せて使用されるフラック
スは、溶融型及び焼成型の何れでもよいが、溶接金属中
の合金元素の偏析を防止してより良好な溶接継手を得る
為には合金元素を含まない高塩基性の低水素系焼成型フ
ラックスが最適である。The present invention is constructed as described above, and by strictly specifying the constituent elements and content of the wire, it is possible to obtain a weld metal with excellent strength, low-temperature toughness, and crack resistance. The flux used in combination with the wire of the present invention may be either a molten type or a fired type, but in order to prevent the segregation of alloy elements in the weld metal and obtain a better welded joint, alloy elements may be added. A highly basic, low hydrogen-based sintered flux that does not contain carbon dioxide is most suitable.

［実施例］ 第１表（１）　、　（２）に示す化学成分の潜弧溶接用
ワイヤ（但しＣｕはめっｇＣｕを含む、４．０ｍｍφ）
を作製した。一方第２表に示す配合組織の７ラツクス原
料を配合した後、珪酸ソーダー系水ガラスを加えて造粒
し５００℃でベーキング処理し、１０〜１００メツシユ
に粒度調整して散布フラックスを得た。この散布フラッ
クスと上記各ワイヤを用いて下記の条件で潜弧溶接を行
ない、溶接終了後各溶接部の板厚中央部から引張試験片
（ＪＩＳ　Ｚ　３１１１　Ａ１号）及び表面下７ｍ１１
ノ位置より衝撃試験片（ＪＩＳ　２３１１２４号）を採
取し、室温における引張試験及び−６０℃における衝撃
試験を行なった。尚試験片の採取に先立ってＵＴ検査に
より溶接割れの有無を確認した。また別途性なった供試
フラックスによる溶接金属の拡散性水素（ＪＩＳ　２３
１１Ｂに準拠）は、ワイヤ成分の如何を問わず何れも０
．５〜１．５ｍｌ　／１００ｇｒであることが確認され
た。結果を第４表（１）　、　（２）に示す。[Example] Wire for submerged arc welding having the chemical composition shown in Table 1 (1) and (2) (however, Cu includes plated Cu, 4.0 mmφ)
was created. On the other hand, after blending the 7 lux raw materials having the blend structure shown in Table 2, silicate soda water glass was added, granulated, baked at 500 DEG C., and the particle size was adjusted to 10 to 100 mesh to obtain a sprinkled flux. Submerged arc welding was performed under the following conditions using this sprinkled flux and each of the above wires, and after welding was completed, a tensile test piece (JIS Z 3111 A1) and 7 m11 below the surface were prepared from the center of the thickness of each welded part.
An impact test piece (JIS 231124) was taken from the position and subjected to a tensile test at room temperature and an impact test at -60°C. Before taking the test pieces, the presence or absence of weld cracks was confirmed by UT inspection. In addition, weld metal diffusible hydrogen (JIS 23
11B) is 0 regardless of the wire component.
．． It was confirmed that the amount was 5 to 1.5 ml/100 gr. The results are shown in Table 4 (1) and (2).

く溶接条件〉 母　　材：高張力鋼（ＨＴ６０）化学成分は第３表の通
り５０■１ 電　　圧：３０ｖ 速　　度：　４０　ｃｐｓ 予熱温度：　１５０℃ これらの実験より次の様に考えることができる。ワイヤ
Ｍｏ、２１〜３０は本発明の規定要件をすべて満たす実
施例であり、引張強度、低温靭性、耐割れ性の何れにお
いても良好な結果が得られている。これに対しワイヤＭ
ｏ、１〜２０は本発明で規定する何れかの要件を欠く比
較例であり、下記の如く何れかの性能に問題がある。Welding conditions> Base material: High tensile steel (HT60) Chemical composition is as shown in Table 3 50■1 Voltage: 30v Speed: 40 cps Preheating temperature: 150℃ Based on these experiments, the following can be considered. . Wires Mo, 21 to 30 are examples that satisfy all the specified requirements of the present invention, and good results were obtained in all of the tensile strength, low-temperature toughness, and cracking resistance. On the other hand, wire M
Samples o, 1 to 20 are comparative examples that lack any of the requirements defined in the present invention, and have some performance problems as described below.

Ｍｏ、１：Ｃ量が不足する為引張強度が低い。Mo, 1: Tensile strength is low due to insufficient C content.

Ｍｏ、２：ＣＪｉが多過ぎる為低温靭性が乏しく、また
（旧＋３０Ｇ）が８％を 超えている為溶接割れが発生し ている。Low temperature toughness is poor due to too much Mo, 2:CJi, and weld cracking occurs because (old +30G) exceeds 8%.

Ｍｏ、３ｒＳｉ量が多過ぎると共に３ＸＳｉ（％）がＭ
　ＯＣ％）を超えている為 ′　低温靭性が悪い。Mo, 3rSi amount is too large and 3XSi (%) is M
OC%), the low-temperature toughness is poor.

Ｍｏ、４：Ｍｎ量が不足する為強度が不足する。Mo, 4: Strength is insufficient due to insufficient amount of Mn.

Ｍｏ、５：Ｍｎ量が多過ぎる為低温靭性がＭｏ、６：Ｎ
ｉ量が不足する為低温靭性に欠ける。Mo, 5: Low temperature toughness due to too large amount of Mn, Mo, 6: N
Low temperature toughness is lacking due to insufficient i content.

Ｍｏ、７ｓＮｉ量が多過ぎる為低温靭性はむしろ低めと
なり、しかも高温 割れが発生している。Because the amounts of Mo and 7sNi are too large, the low-temperature toughness is rather low, and hot cracking occurs.

Ｍｏ、　８　：　３Ｘ！９ｉ（駕）がＭ　ｏ　（Ｘ）を
超えている為低温靭性が低く、しかも Ｍｏ量が不足する為強度も低い。Mo, 8: 3X! Since 9i (kiln) exceeds M o (X), the low temperature toughness is low, and the strength is also low because the amount of Mo is insufficient.

Ｍｏ、９ｓＭｏ量が多過ぎる為低温靭性がむしろ低くな
っている。Since the amounts of Mo and 9sMo are too large, the low temperature toughness is rather low.

Ｍｏ、１０：Ｃｕ量が多過ぎる為低温靭性が乏しい。Mo, 10: Low-temperature toughness is poor because the amount of Cu is too large.

Ｍｏ　、　１１　：　Ｎ　ｉ　（Ｘ）　＋３０Ｃ（Ｘ）
が８を超えている為高温側れが発生している。Mo, 11: N i (X) +30C(X)
Since the value exceeds 8, high-temperature side leakage occurs.

Ｍｏ　、　１２　：　３　Ｘ５ｉ（駕）　カＭ　ｏ　（
＄）　ｔｔ超エテイる為低温靭性が低い。Mo, 12: 3 X5i (palette) Mo (
$) Low temperature toughness due to tt super toughness.

Ｍｏ、１３：Ｃｒ量が多過ぎる為低温靭性が乏しい。Mo, 13: Low temperature toughness is poor because the amount of Cr is too large.

Ｍｏ　、　１４　：　３　Ｘ　０ｒ（Ｘ）　カＭ　ｏ　
（Ｘ）を上回ッテ１、Ｘ　　Ｌ　　うｋ　／ＩＧ　ｍ　
　５１５　Ｊ＋１・４ｔ　−ＣＩ　　＋、％Ｍｏ、１５
：ＴｉＪｌが多過ぎる為低温靭性が悪い。Mo, 14: 3 X 0r(X) Mo
(X) exceeds 1, X L Uk / IG m
515 J+1・4t-CI+, %Mo, 15
: Low temperature toughness is poor due to too much TiJl.

Ｍｏ、１６：Ａｌ量が多過ぎる為やはり低温靭性が不十
分である。Mo, 16: Since the amount of Al is too large, the low temperature toughness is still insufficient.

Ｍｏ、１７：（〒ｉ＋ＡＩ＋Ｖ　）の総和が０．１０％
を超えている為低温靭性が乏しい。Mo, 17: The sum of (〒i+AI+V) is 0.10%
It has poor low temperature toughness.

Ｍｏ、１８〜２０：何れもｌ０Ｘ（Ｔｉ　＋ＡＩ＋Ｖ　
＋Ｚｒ）がＭｏ量を超えている為 低温靭性が乏しい。Mo, 18-20: All 10X (Ti + AI + V
+Zr) exceeds the amount of Mo, resulting in poor low-temperature toughness.

［発明の効果］ 本発明は以上の様に構成されるが、要はワイヤの化学成
分を厳密に規定し、殊に［Ｎｉ（Ｘ）　＋　３０×Ｃ（
＄）］ノ値、３ＸＳｉ（り　トＭｏ（＄）　トｆ）相互
ｉ係、□更ニｌｔ　３　×Ｃｒ（＄）　ｅｌＯＸ　［〒
；Ｃり　＋　ＡＩ（Ｘ）　＋　Ｚｒ（％）　＋Ｎｂ（Ｘ
）　］　トＭｏ（Ｘ）　トノＪＩ互関係を厳密に規定す
ることによって、前述の如き苛酷な使用条件にも十分に
耐える強度及び低温靭性を有し且つ優れた高温割れ性を
発揮する高張力鋼用潜弧溶接用ワイヤを提供し得ること
になった。[Effects of the Invention] Although the present invention is configured as described above, the key point is to strictly define the chemical composition of the wire, and particularly to [Ni(X) + 30×C(
$)] value, 3XSi(ritoMo($)tof)mutual i relationship,
;Cri + AI(X) + Zr(%) +Nb(X
) ] ToMo(X) High tensile strength steel that has strength and low temperature toughness that can withstand the severe usage conditions mentioned above and exhibits excellent hot cracking resistance by strictly specifying the TonoJI correlation. We are now able to provide a wire for submerged arc welding.

【図面の簡単な説明】[Brief explanation of drawings]

第１図は高温割れ性に与えるＮ　ｉ　（Ｘ）と３０×Ｃ
（２）の相互作用を示す実験結果のグラフ、第２図は第
１図の実験で採用した溶接法の説明図、第３図は低温靭
性に与えるＭ　Ｏ（＄）と３ＸＳｉ（Ｘ）の相互作用を
示す実験結果のグラフ、第４図は第３図の実験で採用し
た溶接法の説明図である。 １・・・拘束板　　　　２・・・高張力鋼板Ｗ・・・拘
束溶接部Figure 1 shows the effects of N i (X) and 30×C on hot cracking.
(2) A graph of the experimental results showing the interaction. Figure 2 is an explanatory diagram of the welding method adopted in the experiment of Figure 1. Figure 3 shows the effects of M O ($) and 3XSi (X) on low-temperature toughness. The graph of the experimental results showing the interaction, FIG. 4, is an explanatory diagram of the welding method adopted in the experiment of FIG. 1...Restriction plate 2...High tensile strength steel plate W...Restriction welding part

Claims (3)

【特許請求の範囲】[Claims] （１）Ｃ：０．０３〜０．２０％（重量％：以下同じ） Ｍｎ：１．６０〜３．００％ Ｍｉ：２．１０〜３．５０％ Ｍｏ：０．３０〜１．５０％ Ｓｉ：０．２５％以下 を必須成分として含み、且つ Ｃｕ：≦０．２５％ Ｐ：≦０．０１５％ Ｓ：≦０．０１５％ に夫々制限され、残部が鉄及び不可避不純物からなり、
上記成分のうちＮｉ、Ｃ、Ｓｉ及びＭｏの各含有率が下
記式の関係を満たすことを特徴とする高張力鋼用の弧潜
溶接用ワイヤ。 ［Ｎｉ（％）＋３０×Ｃ（％）≦８（％） ３Ｓｉ（％）≦Ｍｏ（％）(1) C: 0.03-0.20% (weight%: same below) Mn: 1.60-3.00% Mi: 2.10-3.50% Mo: 0.30-1.50% Contains Si: 0.25% or less as an essential component, and is limited to Cu: ≦0.25%, P: ≦0.015%, and S: ≦0.015%, with the remainder consisting of iron and inevitable impurities,
A wire for arc latent welding for high-strength steel, characterized in that the content of Ni, C, Si, and Mo among the above components satisfies the relationship of the following formula. [Ni(%)+30×C(%)≦8(%) 3Si(%)≦Mo(%) （２）Ｃ：０．０３〜０．２０％ Ｍｎ：１．６０〜３．００％ Ｎｉ：２．１０〜３．５０％ Ｍｏ：０．３０〜１．５０％ Ｓｉ：０．２５％以下 Ｃｒ：０．２０％以下 を必須成分として含み、且つ Ｃｕ≦０．２５％ Ｐ≦０．０１５％ Ｓ≦０．０１５％ に夫々制限され、残部が鉄及び不可避不純物からなり、
上記成分のうちＮｉ、Ｃ、Ｓｉ、Ｍｏ及びＣｒの各含有
率が下記式の関係を満たすことを特徴とする高張力鋼用
の潜弧溶接用ワイヤ。 ［Ｎｉ（％）＋３０×Ｃ（％）］≦８（％） ３Ｓｉ（％）≦Ｍｏ（％） ３Ｃｒ（％）≦Ｍｏ（％）(2) C: 0.03-0.20% Mn: 1.60-3.00% Ni: 2.10-3.50% Mo: 0.30-1.50% Si: 0.25% or less Contains Cr: 0.20% or less as an essential component, and is limited to Cu≦0.25%, P≦0.015%, and S≦0.015%, with the remainder consisting of iron and inevitable impurities,
A wire for submerged arc welding for high-strength steel, characterized in that the content of Ni, C, Si, Mo, and Cr among the above components satisfies the relationship of the following formula. [Ni(%)+30×C(%)]≦8(%) 3Si(%)≦Mo(%) 3Cr(%)≦Mo(%) （３）Ｃ：０．０３〜０．２０％ Ｍｎ：１．６０〜３．００％ Ｎｉ：２．１０〜３．５０％ Ｍｏ：０．３０〜１．５０％ Ｓｉ：０．２５％以下 Ｃｒ：０．２０％以下 を含み、且つＴｉ、Ａｌ、Ｚｒ、Ｖ及びＮｂよりなる群
から選択される１種以上：合計で０．１％以下を必須成
分として含み、且つ Ｃｕ≦０．２５％ Ｐ≦０．０１５％ Ｓ≦０．０１５％ に夫々制限され、残部が鉄及び不可避不純物からなり、
上記成分のうちＮｉ、Ｃ、Ｓｉ、Ｍｏ、Ｃｒ、Ｔｉ、Ａ
ｌ、Ｚｒ、Ｖ及びＮｂの各含有率が下記式の関係を満た
すことを特徴とする高張力鋼用の弧潜溶接用ワイヤ。 ［Ｎｉ（％）＋３０×Ｃ（％）］≦８（％） ３Ｓｉ（％）≦Ｍｏ（％） ３Ｃｒ（％）≦Ｍｏ（％） １０×［Ｔｉ（％）＋Ａｌ（％）＋Ｚｒ（％）＋Ｖ（％
）＋Ｎｂ（％）］≦Ｍｏ（％）(3) C: 0.03-0.20% Mn: 1.60-3.00% Ni: 2.10-3.50% Mo: 0.30-1.50% Si: 0.25% or less Contains Cr: 0.20% or less, and one or more selected from the group consisting of Ti, Al, Zr, V, and Nb: 0.1% or less in total as essential components, and Cu≦0.25 % P≦0.015% and S≦0.015%, with the remainder consisting of iron and inevitable impurities,
Among the above components, Ni, C, Si, Mo, Cr, Ti, A
A wire for arc latent welding for high-strength steel, characterized in that the respective contents of L, Zr, V, and Nb satisfy the relationship of the following formula. [Ni (%) + 30 × C (%)] ≦ 8 (%) 3Si (%) ≦ Mo (%) 3 Cr (%) ≦ Mo (%) 10 × [Ti (%) + Al (%) + Zr (%) +V(%
)+Nb(%)]≦Mo(%)