JPS63132794A - Weld metal for high tensile steel products - Google Patents
Weld metal for high tensile steel productsInfo
- Publication number
- JPS63132794A JPS63132794A JP27914986A JP27914986A JPS63132794A JP S63132794 A JPS63132794 A JP S63132794A JP 27914986 A JP27914986 A JP 27914986A JP 27914986 A JP27914986 A JP 27914986A JP S63132794 A JPS63132794 A JP S63132794A
- Authority
- JP
- Japan
- Prior art keywords
- weld metal
- welding
- steel
- hardness
- less
- 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.)
- Pending
Links
- 229910052751 metal Inorganic materials 0.000 title claims abstract description 44
- 239000002184 metal Substances 0.000 title claims abstract description 44
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 31
- 239000010959 steel Substances 0.000 title claims abstract description 31
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 7
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 6
- 238000003466 welding Methods 0.000 claims description 41
- 239000000463 material Substances 0.000 claims description 16
- 230000007797 corrosion Effects 0.000 abstract description 4
- 238000005260 corrosion Methods 0.000 abstract description 4
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 4
- 229910052759 nickel Inorganic materials 0.000 abstract description 4
- 229910052804 chromium Inorganic materials 0.000 abstract description 3
- 229910052760 oxygen Inorganic materials 0.000 abstract description 3
- 239000013535 sea water Substances 0.000 abstract description 3
- 229910052799 carbon Inorganic materials 0.000 abstract description 2
- 229910052717 sulfur Inorganic materials 0.000 abstract description 2
- 230000006735 deficit Effects 0.000 abstract 1
- 239000000203 mixture Substances 0.000 description 18
- 238000000034 method Methods 0.000 description 5
- 150000002739 metals Chemical class 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 230000013011 mating Effects 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 229910001208 Crucible steel Inorganic materials 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 238000009863 impact test Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 238000007778 shielded metal arc welding Methods 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
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
- B23K35/001—Interlayers, transition pieces for metallurgical bonding of workpieces
- B23K35/004—Interlayers, transition pieces for metallurgical bonding of workpieces at least one of the workpieces being of a metal of the iron group
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Arc Welding In General (AREA)
Abstract
Description
【発明の詳細な説明】
〈発明の目的〉
産業上の利用分野
本発明は高張力鋼材の接合に供せられ、しかも、少なく
とも８０ｋｌｌ’ｍｍ２程度の引張り強さを持つ高張力
鋼材用溶接金属に係り、詳しくは、例えば、構造物のΦ
ｍ軽減のために使用される８０ｋＱｆ／ｌｌＩ２級の如
き高張力鋼材を溶接するときに形成され、引張り強度が
８０ｋｇｆ／ｓ’以上の溶接金属であって、溶接後に硬
度軽減のために応力除去焼鈍処理ｃ以下、単にＳＲ処理
という。）を行なったときにほとんどＳＲぜい化の生じ
ることのない靭性に優れる高張力鋼材用溶接金属に係る
。[Detailed Description of the Invention] <Object of the Invention> Industrial Field of Application The present invention is applicable to welding of high-tensile steel materials and has a tensile strength of at least about 80 kll'mm2. In detail, for example, the structure's Φ
It is a weld metal formed when welding high tensile strength steel materials such as 80kQf/llI2 class used for reducing the hardness, and has a tensile strength of 80kgf/s' or more, and is subjected to stress relief annealing to reduce the hardness after welding. Process c will hereinafter be simply referred to as SR processing. ) The present invention relates to a weld metal for high-strength steel that has excellent toughness and hardly causes SR embrittlement when subjected to the following steps.
なお、以下において、バタリング請を溶接金属で形成す
る場合を中心にして説明するが、本発明はこの例に限ら
れるものでなく、溶接接合一般に用いられるものを全て
含む。Note that although the following description will focus on the case where the buttering joint is formed of welded metal, the present invention is not limited to this example, and includes all welding joints that are generally used.
従来の技術
従来から、８０ｋｇｆ／ｓ２程度鍜鋼の如き高張力鋼材
を一部の構造部材として用いると、圧力容器や海洋構造
物等の重量が大巾に軽減されるため、高張力鋼材を溶接
し、てこれら構造物は構築されている。また、溶接部に
形成される溶接金属は８０ｋｌ／■２級鍛鋼の母材と同
等の性質を持つことが必要であり、換言すると、８０ｋ
ｇｆ／ｗ＋２級溶接金属になることが要求される。Conventional technology Conventionally, when high-tensile steel materials such as 80 kgf/s2 steel are used as some structural members, the weight of pressure vessels, offshore structures, etc. is greatly reduced, so high-tensile steel materials have been welded. However, these structures are being constructed. In addition, the weld metal formed in the welded part needs to have properties equivalent to the base metal of 80kl/■2 grade forged steel, in other words, 80kl/■
It is required to be gf/w+2 class weld metal.
また、例えば、サブマージアーク溶接（以下、ＳＪＶと
いう。）等のアーク溶接により形成される溶接金属のう
ちで、８０ｋｇＬ′ｍ１級の溶接金属の主組成は重量％
でＣ０，０５〜０．１２％、Ｓｉ ０１２０〜０．５０
％、Ｍｎ １，２〜１．９％、Ｐ ０００１５％以下、
Ｓｏ、ｏｉｏ％以下、Ｎｉ １．０〜３．０％、Ｃｒ
０．４〜１．０％、Ｍｏ ０．２〜０．８％ならびにＯ
０１２５〜０．０（３％を含んで、残余が実質的にＦｅ
から成っている。すなわち、溶接金属中に、Ｃ，ｃｒ、
ＭＯ等の強化元素を所定範囲含まれていると、例えば
８０ｋｇｆ／ｗ２程度の引張り強度が保持できる。For example, among weld metals formed by arc welding such as submerged arc welding (hereinafter referred to as SJV), the main composition of 80 kg L'm1 class weld metal is % by weight.
C0.05~0.12%, Si 0.120~0.50
%, Mn 1.2-1.9%, P 00015% or less,
So, oio% or less, Ni 1.0-3.0%, Cr
0.4-1.0%, Mo 0.2-0.8% and O
0125~0.0 (including 3%, the remainder is substantially Fe)
It consists of That is, in the weld metal, C, cr,
When a reinforcing element such as MO is contained in a predetermined range, a tensile strength of about 80 kgf/w2 can be maintained, for example.
しかし、この組成の溶接金属であると、溶接後にＳＲ処
理を行なうと、３８割れや、ＳＲぜい化が発生して好ま
しくない。このため、特開昭６０−６８１７６号公報に
示される如く、＾張力鋳鋼や鍛鋼等の鋼材の溶接には、
それに先立って、鋼材の先端に３８割れ感受性の低い材
料Ｃバタリング１を形成し、その侵、このバタリング層
に５Ｒｆｆｉ理を行なわずに、そのまま突合せて開先を
形成し、この開先を本溶接する方法や、高張力鋼材を上
記組成の溶接金属を形成して突合せ溶接し、溶接したま
まで使用することが行なわれている。However, when a weld metal with this composition is subjected to SR treatment after welding, 38 cracks and SR embrittlement occur, which is not preferable. For this reason, as shown in Japanese Patent Application Laid-Open No. 60-68176, when welding steel materials such as tension cast steel and forged steel,
Prior to that, a material C buttering 1 with low susceptibility to 38 cracking is formed on the tip of the steel material, and a groove is formed by butting the buttering layer as it is without performing 5Rffi processing, and this groove is welded for the main welding. Another method is to form a weld metal of the above-mentioned composition from high-strength steel, butt weld it, and then use the welded material as it is.
ところが、８０ｋｇｒ／ｎｌｃ級の高張力鋼、なかでも
、ｗ４鋼等のときは、溶接時に生成する熱影響部が顕著
に硬化し、海洋構造物では、耐海水腐食疲労性を高める
ためには溶接部の硬さを制限する必要があり、溶接後に
はどうしてもＳＲ処理が必要である。However, in the case of 80kgr/NLC class high-strength steel, especially W4 steel, the heat affected zone generated during welding becomes noticeably hardened, and in offshore structures, welding is required to improve seawater corrosion fatigue resistance. It is necessary to limit the hardness of the part, and SR treatment is absolutely necessary after welding.
ｔ ’ｌ ｆ） も、第３図は８０ｋ（ｉｌｚ’１ｌｔ
ｌ１２級のｗＩｔＪ４を溶接しｌ；ときに、この溶接に
より生成する熱影響部の最高硬さと溶接入熱量との関係
を示すグラフであり、Ｘ印は溶接したまま、Ｏ印は溶接
後にＳＲ処理したものを示す。この第３図から明らかな
如く、５０Ｘ１０３ ジュール／ｃｍ以下の入熱のとき
は、溶接のままでは硬さＩＩ Ｒｃ３７〜４０を示すが
、５９０℃×５時間程度のＳＲ処理によって硬さはＩＩ
、Ｃ≦３２に低下し、硬度を制限するためにはＳＲ処
理がどうしても必要になることがわかる。t'l f) is also 80k(ilz'1lt) in Figure 3.
This is a graph showing the relationship between the maximum hardness of the heat affected zone generated by this welding and the welding heat input when welding l12 class WItJ4. Show what you did. As is clear from Fig. 3, when the heat input is 50 x 103 Joules/cm or less, the hardness as welded is II Rc37-40, but the hardness increases to II after SR treatment at 590°C for about 5 hours.
, C≦32, indicating that SR treatment is absolutely necessary to limit the hardness.
しかしながら、このように溶接後にＳＲ処理すると、溶
接部の溶接金属が上記組成であるため、５ＲｔＦい化が
発生し、健全な継手が得られない。However, when SR treatment is performed after welding in this manner, since the weld metal in the welded portion has the above composition, 5RtF corrosion occurs and a sound joint cannot be obtained.
発明が解決しようとする問題点
本発明は上記欠点の解決を目的とし、具体的には、例え
ば％８０ｋｇｆｔ’ｒ１ｍ２級鍛鋼の如き高張力鋼材を
一部の構造部材として組込んで構造物等を溶接により構
築するときに、この溶接に先立って高張力鋼材側の開先
に８０ｋｌＪｌｚ’１ｌＤＩ２級溶接金属から成るバタ
リング層を形成してから５Ｒ９ａ理すると、このバタリ
ング■にＳＲぜい性が生じるＣと、これに対し、バタリ
ング調形成後にＳＲ処理を省略すると、このときに高強
度鋼材側に生成する熱影響部の硬度が８０ｋ（ｉｆ／■
２級鍜鋼であ鍛鋼、必要以上に高くなり、靭性も損なわ
れること等の問題点を解決することを目的とする。Problems to be Solved by the Invention The purpose of the present invention is to solve the above-mentioned drawbacks. Specifically, the present invention aims to solve the above-mentioned drawbacks. When constructing by welding, if a battering layer made of 80klJlz'1lDI 2nd grade weld metal is formed on the groove on the high-tensile steel side prior to welding and then treated with 5R9a, SR brittleness will occur in the battering. On the other hand, if the SR treatment is omitted after the battering-like formation, the hardness of the heat affected zone generated on the high-strength steel side will be 80k (if/■
The purpose is to solve the problems of second-grade cold steel and forged steel, which are unnecessarily expensive and suffer from loss of toughness.
〈発明の構成〉
問題点を解決するための
手段ならびにその作用
すなわち、本発明に係る溶接金属は、重量％でＣ０．０
１〜０．０５％、Ｓｉ ０．１５％以下、Ｍｎ １．２
〜１．９％、Ｐ ０．０１５％以下、Ｓ ０．０１０％
以下、Ｎｉ１．０〜３．０％、Ｏｒ ０．４〜１．０％
、Ｍｏ ０．２〜０．８％ムらびにＯ０．０１５％以下
を含んで、残部が実質的にＦｅから成ることを特徴とす
る。<Structure of the Invention> Means for solving the problem and its operation, that is, the weld metal according to the present invention has a C0.0 by weight%.
1 to 0.05%, Si 0.15% or less, Mn 1.2
~1.9%, P 0.015% or less, S 0.010%
Below, Ni 1.0-3.0%, Or 0.4-1.0%
, 0.2 to 0.8% of Mo, and 0.015% or less of O, with the remainder essentially consisting of Fe.
そこで、これら手段たる構成ならひにその作用につい−
Ｃ興体的に説明すると、次の通りである。Therefore, if we consider the configuration of these means, let us explain their effects.
To explain it in a simple way, it is as follows.
まず、本発明者等は、８０ｋｌＪｆｚ’ａｉ２程度の鍛
鋼を被溶接材として、この開先に種々の組成のワイヤを
用いてサブマージアーク溶接によって種々の組成の溶接
金属を形成し、その上で、８０ｋｌＪｆｚ’ｗ１２程度
の引張り強度を示す溶接金属について、その化学組成と
Ｓｌ′Ｉぜい化との関係を求めたところ、ケイ素（Ｓｉ
）ならびに酸素（０１がＳｉ ０．１５％以下、Ｏ０．
０１５％以下の関係にあると、他の１ヒ学組成が上記の
如＜ 、Ｇ ０．０５〜０．１２％、Ｍｎ１．２〜１．
９％、Ｐ ０．０１５％以下、Ｍｎ １．２〜１．９％
、Ｓｏ、ｏｉｏ％以下、Ｎｉ １．０〜３．０％、Ｃｒ
０．４〜１．０％、Ｍｏ０．２〜０．８％の範囲であ
っても、ＳＲぜい化しないことがわかった。更に、この
場合、溶接法は上記の如くサブマージアーク溶接法のほ
かにＳＭＡＷ％ＧＭＡＷの如く何れのアーク溶接であっ
ても溶接金属が上記範囲内にあると、ＳＲぜい化しない
ことがわかった。First, the present inventors used forged steel of about 80klJfz'ai2 as a material to be welded, and formed weld metals of various compositions by submerged arc welding using wires of various compositions on the groove, and then, When we investigated the relationship between the chemical composition and Sl'I embrittlement for weld metals exhibiting a tensile strength of approximately 80klJfz'w12, we found that silicon (Si)
) and oxygen (01 is Si 0.15% or less, O0.
0.015% or less, the other chemical compositions are as above, G 0.05-0.12%, Mn 1.2-1.
9%, P 0.015% or less, Mn 1.2-1.9%
, So, oio% or less, Ni 1.0-3.0%, Cr
It was found that SR embrittlement does not occur even in the ranges of 0.4 to 1.0% and Mo of 0.2 to 0.8%. Furthermore, in this case, it was found that SR embrittlement does not occur if the weld metal is within the above range, regardless of whether the welding method is submerged arc welding as described above or arc welding such as SMAW% GMAW. .
また、この組成の溶接金属によってバタリング層を形成
し、このバタリング層を介して例えば８０に’Ｊｆ／’
ｍ１程度の圧延材に溶接することもできる。このときに
溶接金属が上記組成から成っているとＣ頂が高いことも
あって、バタリング層に生じる熱影響部が硬化する。そ
こで、この点について本発明者等ｌｆ研究したところ、
上記組成の溶接金属中ＣＧのみを０．０１〜０．０５％
にすると、硬度Ｉ＋、。≦３９になることがわかった。In addition, a buttering layer is formed with the weld metal having this composition, and 'Jf/'
It is also possible to weld to a rolled material of about m1. At this time, if the weld metal has the above-mentioned composition, the heat-affected zone generated in the battering layer is hardened, partly because the C peak is high. Therefore, the inventors conducted research on this point and found that
Only 0.01 to 0.05% CG in the weld metal with the above composition
The hardness is I+. It was found that ≦39.
従って、溶接時には、この溶接に先立って上記組成の溶
接金属をバタリング層として形成し、例えば、８０ｋｇ
ｒ／ａ’程度の鍛鋼なその俊、例えば、８０ｋｑＬ’１
ｍ’級の圧延鋼に溶接するときには、溶接金属と略々同
じ組成のワイヤや、従来例のワイヤ等の溶接材料を使用
して本溶接すると、この溶接により組立てられた構造物
はＳＲ処理することなくそのままで実用に供することが
でき、溶接金属の高靭性は維持される。また、この本溶
接のときにバタリング雪に熱影響部が形成されるが、バ
タリング層の溶接金属ではＣが０．０１〜０．０５％の
範囲に調整されているために、上記の如く硬さはＩｌ、
ｃ≦３２に保持できる。Therefore, at the time of welding, a weld metal having the above composition is formed as a battering layer prior to welding, and for example, 80 kg of weld metal is formed as a buttering layer.
R/A' grade forged steel, for example, 80kqL'1
When welding to m' class rolled steel, if the actual welding is performed using a welding material such as a wire with approximately the same composition as the weld metal or conventional wire, the structure assembled by this welding will be subjected to SR treatment. The weld metal can be put to practical use as is, and the high toughness of the weld metal is maintained. Additionally, a heat-affected zone is formed in the buttering snow during this main welding, but since the C content in the weld metal of the buttering layer is adjusted to a range of 0.01 to 0.05%, it becomes hard as described above. Saha Il,
It can be maintained at c≦32.
すなわち、第１図ならびに第２図に示す如く、８０ｋｌ
ＪＬ’１ｌｌ１２程度の鍛鋼を使用する構造物を溶接に
よって組立てる場合には、第１図に示す如く、予め鍜！
１１の先端に、Ｇ ０．０１〜０．０５％、Ｓｉ ０．
１５％以下、Ｍｎ １．２〜１．９％、Ｐ ０００１５
％以下、Ｓｏ、ｏｉｏ％以下、Ｎｉ １．０〜３．０％
、Ｏｒ ０．４〜１．０％、Ｍｏ ０．２〜０．８％、
００．０１５％以下を含んで残余が実質的に［ｅから成
る組成の溶接金属をバタリング層２として形成してから
、所望形状に開先加工を行なって、その俊、ＳＲ処理を
する。その後、第２図に示す如く、他の部材３と突合せ
て開先を形成し、溶接を実施し、上記組成の溶接金属又
は先に示した従来例の８０ｋｌ／ｌｌｌｍ２程度の組成
の溶接金属を形成すると、溶接のままで使用ずれば、溶
接部の硬化層はなく、かつ高靭性の溶接金属が得られる
。That is, as shown in Figures 1 and 2, 80kl
When assembling a structure using forged steel of approximately JL'1ll12 by welding, as shown in Fig. 1, weld the forged steel in advance.
At the tip of No. 11, G 0.01-0.05%, Si 0.
15% or less, Mn 1.2-1.9%, P 00015
% or less, So, oio% or less, Ni 1.0-3.0%
, Or 0.4-1.0%, Mo 0.2-0.8%,
A weld metal having a composition of 0.015% or less and the remainder substantially consisting of [e] is formed as the buttering layer 2, and then a groove is formed into a desired shape and then subjected to SR treatment. Thereafter, as shown in FIG. 2, a groove is formed by butting with another member 3, and welding is carried out to produce a weld metal with the above composition or a weld metal with a composition of about 80 kl/llm2 in the conventional example shown earlier. Once formed, if used as welded, there is no hardened layer in the welded area and a highly tough weld metal can be obtained.
実 施 例 次に実施例について説明する。Example Next, an example will be described.
まず、８０ｋＱ ｒ／ＭＡ２級ｍ ｔＪ４ （７） ’
ｌｃ Ｇａ ニ第１ 表ニ示す組成のバッタリング層を
溶接入熱３０Ｘ１０３ ジュールｔ’ｃｒＡの条件で形
成し、その後、ＳＲ処理（５９０℃ｘ５時間）をした。First, 80kQ r/MA2 class m tJ4 (7)'
A battering layer having the composition shown in Table 1 was formed under conditions of welding heat input of 30 x 103 Joules t'crA, and then subjected to SR treatment (590°C x 5 hours).
その侵、相手材の８◇ｋｇＬ’ｍｌ１２級の圧延鋼との
間でサブマージ突合せ溶接を実施し、バタリング層の硬
さと衝撃試験を行なったとＣろ、第２表に示す通りであ
った。For this reason, submerged butt welding was carried out with the mating material, 8◇kgL'ml class 12 rolled steel, and the hardness and impact tests of the battering layer were conducted, as shown in Table 2.
第１表ならびに第２表において、＆１．２ならびに３は
本発明に係る溶接金属によってバッタリング層が形成さ
れたもので、この場合は、 ＳＲ処理を行なっても、吸
収エネルギーは高レベルを保持していた。これに対し、
Ｈａ ４１ｉらびに５で示すバッタリング層は比較例で
あって、これら比較例ではＳＲ処理によって吸収エネル
ギーは低下し、靭性が大ｒｌに低下していることがわか
る。In Tables 1 and 2, &1.2 and 3 have a battering layer formed by the weld metal according to the present invention, and in this case, even after SR treatment, the absorbed energy remains at a high level. Was. In contrast,
The battering layers designated by Ha 41i and 5 are comparative examples, and it can be seen that in these comparative examples, the absorbed energy is lowered by the SR treatment, and the toughness is significantly lowered.
また、本溶接時にはバタリング層に熱影響部が生じるが
この硬さは本発明の場合にはＣが低くなっていることし
あって）ＩＲｃ≦３１であった。Further, during main welding, a heat-affected zone occurs in the battering layer, but the hardness of this zone was IRc≦31 (due to the low C in the case of the present invention).
第１表バタリング層溶接金属組成（％）第２表 バタリ
ング１の硬さと
衝撃吸収エネルギー
バタリング溶接入熱３０にＪ ｔ’ ＣＩハタＩＪ ン
’ｊ ！１ｓＲ５９０℃ｘ５ｈ〈発明の効果〉
以上詳しく説明した通り、本発明に係る溶接金属によっ
てバタリング層を形成し、バタリング層を介して溶接す
ると、Ｓｉ含有量が０．１５％以下、Ｃ含有量が０．０
１５％以下の如く少量であるため、ＳＲ処理を行なって
もこの処理によってＳＲぜい化が生じない。また、バタ
リング１を介して溶接したのちに、ＳＲ処理することな
く、そのまま使用しても、溶接金属中のＣ含有量が０．
０１〜０．０５％の節回にあるため、溶接時にバタリン
グ層に生成する熱影響部の硬度が＾くならず、耐海水腐
食疲労性などが損なわれることがない。Table 1 Buttering layer weld metal composition (%) Table 2 Hardness and shock absorption energy of buttering 1 Buttering welding heat input 30 J t' CI Group IJ N'j! 1sR590°C x 5h <Effects of the Invention> As explained in detail above, when a buttering layer is formed using the weld metal according to the present invention and welding is performed through the buttering layer, the Si content is 0.15% or less and the C content is 0. .0
Since the amount is as small as 15% or less, SR embrittlement does not occur even if SR treatment is performed. Further, even if the weld metal is used as it is without SR treatment after welding through the buttering 1, the C content in the weld metal is 0.
01 to 0.05%, the hardness of the heat-affected zone generated in the battering layer during welding does not decrease, and seawater corrosion fatigue resistance is not impaired.
第１図ならびに第２図は本発明に係る溶接金属をバタリ
ング■として介在させて８０ｋａｆ／ｓ’級鍜鋼を溶接
する際のバタリング■形成工程と開先形成工程の各説明
図で、第３図は８０ｋｕｆ／Ｘｌ１ｍ’級鍜鋼を溶接し
たときの入熱量と溶接熱影響部の硬度との関係を示すグ
ラフである。
符号１・・・・・・８０ｋｌＪｆ／１１１１’鍜鋼の如
き母材２・・・・・・バタリング層
３・・・・・・相手材1 and 2 are explanatory diagrams of the battering ■ forming process and the groove forming process when welding 80 kaf/s' class steel by interposing the weld metal according to the present invention as the battering ■. The figure is a graph showing the relationship between the amount of heat input and the hardness of the weld heat affected zone when welding 80 kuf/Xl1 m' class steel. Code 1...80klJf/1111' Base material such as steel 2...Buttering layer 3...Mating material
Claims (1)
、Ｍｎ１．２〜１．９％、Ｐ０．０１５％以下、Ｓ０．
０１０％以下、Ｎｉ１．０〜３．０％、Ｃｒ０．４〜１
．０％、Ｍｏ０．２〜０．８％ならびにＯ０．０１５％
以下を含んで、残部が実質的にＦｅから成ることを特徴
とする高張力鋼材の接合に供せられ、しかも、少なくと
も８０ｋｇｆ／ｍｍ＾２程度の引張り強さを持つ高張力
鋼材用溶接金属。In weight%, C0.01 to 0.05%, Si 0.15% or less, Mn 1.2 to 1.9%, P 0.015% or less, S0.
010% or less, Ni1.0-3.0%, Cr0.4-1
．． 0%, Mo0.2-0.8% and O0.015%
A welding metal for high-strength steel materials, which is used for joining high-strength steel materials, and has a tensile strength of at least about 80 kgf/mm^2, comprising:
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP27914986A JPS63132794A (en) | 1986-11-21 | 1986-11-21 | Weld metal for high tensile steel products |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP27914986A JPS63132794A (en) | 1986-11-21 | 1986-11-21 | Weld metal for high tensile steel products |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS63132794A true JPS63132794A (en) | 1988-06-04 |
Family
ID=17607128
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP27914986A Pending JPS63132794A (en) | 1986-11-21 | 1986-11-21 | Weld metal for high tensile steel products |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS63132794A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008137042A (en) * | 2006-12-04 | 2008-06-19 | Hitachi Ltd | Turbine rotor |
-
1986
- 1986-11-21 JP JP27914986A patent/JPS63132794A/en active Pending
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008137042A (en) * | 2006-12-04 | 2008-06-19 | Hitachi Ltd | Turbine rotor |
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