JPH07214376A - Flux cored wire for hard facing by welding of cast iron and method for hard facing by welding - Google Patents

Flux cored wire for hard facing by welding of cast iron and method for hard facing by welding

Info

Publication number
JPH07214376A
JPH07214376A JP772694A JP772694A JPH07214376A JP H07214376 A JPH07214376 A JP H07214376A JP 772694 A JP772694 A JP 772694A JP 772694 A JP772694 A JP 772694A JP H07214376 A JPH07214376 A JP H07214376A
Authority
JP
Japan
Prior art keywords
welding
flux
cast iron
cored wire
metal
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
Application number
JP772694A
Other languages
Japanese (ja)
Inventor
Satoyuki Miyake
Hitoshi Nishimura
聰之 三宅
均 西村
Original Assignee
Nippon Steel Weld Prod & Eng Co Ltd
日鐵溶接工業株式会社
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Nippon Steel Weld Prod & Eng Co Ltd, 日鐵溶接工業株式会社 filed Critical Nippon Steel Weld Prod & Eng Co Ltd
Priority to JP772694A priority Critical patent/JPH07214376A/en
Publication of JPH07214376A publication Critical patent/JPH07214376A/en
Pending legal-status Critical Current

Links

Abstract

PURPOSE:To provide the deposited metal which is excellent in the weldability, free of cracks of deposited metal and heat affected zone of the base metal, stable in hardness, and excellent in wear resistance. CONSTITUTION:In a flux cared wire where the flux is filled in the steel sheath skin, the flux having the composition consisting of, by weight of flux cored wire, 0.12-0.80% C, 0.1-3.4% Si, 1.5-10.0% Mn, 1.0-6.0% Co, 0.05-0.83% one or more kinds of alkaline metal fluoride, 1.1-8.3% Cr, and 0.05-3.2% one or two kinds of Mo and V as necessary. The hard facing by welding of the cast iron is executed with the heat input of <=9600J by using this flux cored wire.

Description

【発明の詳細な説明】Detailed Description of the Invention
【0001】[0001]
【産業上の利用分野】本発明は、鋳鉄母材の硬化肉盛溶
接において、特に溶接作業性が良好で、溶着金属および
母材熱影響部の割れがなく、硬さも安定し、かつ耐摩耗
性に優れた溶着金属を得ることができる鋳鉄の硬化肉盛
溶接用フラックス入りワイヤおよび硬化肉盛溶接方法に
関するものである。
FIELD OF THE INVENTION The present invention has a particularly good workability in hardfacing welding of cast iron base metal, has no cracks in the weld metal and heat-affected zone of the base metal, has stable hardness, and is resistant to wear. TECHNICAL FIELD The present invention relates to a flux-cored wire for hardfacing welding of cast iron and a hardfacing welding method capable of obtaining a weld metal having excellent properties.
【0002】[0002]
【従来の技術】従来より鋳鉄の溶接は、母材への溶込み
を極力小さくし、熱影響部の硬化層(白銑化)の発生域
を少なくすることで耐割れ性の改善に努めてきた。その
結果、溶接電流、アーク電圧を可能な限り低く抑えるこ
とができる被覆アーク溶接法が一般的に多用されてい
る。しかし、最近では鋳鉄の溶接にも自動化、高級化の
ニーズが高まり、例えば特開昭56−47292号公報
「鋳鉄用溶接心線」では、40〜70%Niのソリット
ワイヤにSi、Mn、Nb等を適量添加することで溶着
金属の耐割れ性を改善した技術が開示されている。ま
た、特開昭59−179195号公報「球状黒鉛鋳鉄の
溶接に使用する自動溶接ワイヤ」では、40〜60%N
iのソリッドワイヤに希土類金属およびNb、Alを適
量添加することで溶着金属の高靱性化と高温割れの低減
を図ったワイヤが開示されている。
2. Description of the Related Art Conventionally, welding of cast iron has been made to improve crack resistance by minimizing the penetration into the base material and reducing the area where the hardened layer (white pig iron) in the heat affected zone is generated. It was As a result, the covered arc welding method, which can keep the welding current and the arc voltage as low as possible, is generally used. However, recently, there is a growing need for automation and high quality welding of cast iron. For example, in JP-A-56-47292, "Welding core wire for cast iron", Si, Mn, Nb is added to a solid wire of 40 to 70% Ni. A technique is disclosed in which the crack resistance of the deposited metal is improved by adding an appropriate amount of the above. Further, in JP-A-59-179195 "Automatic welding wire used for welding spheroidal graphite cast iron", 40-60% N
A wire is disclosed in which the toughness of the deposited metal and the reduction of hot cracking are achieved by adding an appropriate amount of a rare earth metal, Nb, and Al to the solid wire of i.
【0003】[0003]
【発明が解決しようとする課題】しかし、これらのワイ
ヤは、いずれもNi基のソリッドワイヤであり、用途と
してはいずれのワイヤも鋳鉄の継手溶接かあるいは鋳鉄
の補修溶接用で、耐摩耗性を要求される溶接には適用で
きない。また、ワイヤの形態がソリッドワイヤであるた
め十分な溶接作業性が確保できず、また母材への希釈が
大きいなど、鋳鉄の溶接における問題点を解決したもの
はいえない。
However, all of these wires are Ni-based solid wires, and are used for joint welding of cast iron or for repair welding of cast iron, and have a wear resistance. Not applicable to required welding. Moreover, since the form of the wire is a solid wire, sufficient welding workability cannot be ensured, and the dilution of the base metal is large.
【0004】本発明は、鋳鉄母材の硬化肉盛溶接におい
て、特に溶接作業性が良好で、溶着金属および母材熱影
響部の割れがなく、硬さも安定し、耐摩耗性に優れた溶
着金属を得ることができる鋳鉄の硬化肉盛溶接用フラッ
クス入りワイヤおよび硬化肉盛溶接方法を提供すること
を目的とする。
According to the present invention, in the hardfacing welding of cast iron base metal, the welding workability is particularly good, the weld metal and the base metal heat affected zone are not cracked, the hardness is stable, and the welding resistance is excellent. An object of the present invention is to provide a flux-cored wire for hardfacing hardfacing welding of cast iron capable of obtaining a metal, and a hardfacing hardfacing welding method.
【0005】[0005]
【課題を解決するための手段】本発明は、鋼製外皮にフ
ラックスを充填してなるフラックス入りワイヤにおい
て、フラックス入りワイヤ重量%でC:0.12〜0.
80%、Si:0.1〜3.4%、Mn:1.5〜1
0.0%、Co:1.0〜6.0%、アルカリ金属系フ
ッ化物の1種または2種以上:0.05〜0.83%、
またはさらにCr:1.1〜8.3%、必要に応じてさ
らにMo、Vの何れか1種または2種:0.05〜3.
2%を含有することを特徴とする鋳鉄の硬化肉盛溶接用
フラックス入りワイヤ、および溶接入熱量9600J以
下で前記フラックス入りワイヤを用いて肉盛溶接するこ
とを特徴とする鋳鉄の硬化肉盛溶接方法を要旨とするも
のである。
DISCLOSURE OF THE INVENTION The present invention relates to a flux-cored wire obtained by filling a steel shell with flux, in a flux-cored wire weight% of C: 0.12 to 0.
80%, Si: 0.1 to 3.4%, Mn: 1.5 to 1
0.0%, Co: 1.0 to 6.0%, one or more alkali metal fluorides: 0.05 to 0.83%,
Alternatively, Cr: 1.1 to 8.3%, and if necessary, any one or two of Mo and V: 0.05 to 3.
Flux-cored wire for hardfacing overlay welding of cast iron characterized by containing 2%, and hardfacing welding of cast iron characterized by performing overlay welding using the flux-cored wire with a welding heat input of 9600 J or less. The method is the gist.
【0006】[0006]
【作用】以下本発明を詳細に説明する。まずフラックス
入りワイヤの組成を限定した理由について述べる。C
は、低コストで容易に溶着金属の硬さを調整できる硬化
肉盛溶接材料として必須の元素であることは良く知られ
ている。本発明では、鋳鉄母材へ肉盛溶接を行うことか
ら、当然母材から溶着金属に移行する炭素は通常の肉盛
溶接に比べ多くなるが、溶着金属の硬さおよび耐割れ性
の観点から、溶着金属中のCが0.12%未満では硬さ
が十分でなく、耐摩耗性に劣る。また、Cが0.55%
超では耐割れ性に問題があるので、C量の歩留りを考慮
してフラックス入りワイヤ中のCを0.12〜0.80
%の範囲に限定した。
The present invention will be described in detail below. First, the reason for limiting the composition of the flux-cored wire will be described. C
It is well known that is an essential element as a hardfacing welding material that can easily adjust the hardness of the deposited metal at low cost. In the present invention, since the overlay welding is performed on the cast iron base material, the amount of carbon that is naturally transferred from the base material to the weld metal is larger than that in the normal overlay welding, but from the viewpoint of the hardness and crack resistance of the weld metal. If C in the weld metal is less than 0.12%, the hardness is insufficient and the wear resistance is poor. Also, C is 0.55%
If it exceeds the above value, there is a problem in crack resistance. Therefore, considering the yield of C, the C in the flux-cored wire is 0.12-0.80.
It was limited to the range of%.
【0007】Siは、脱酸剤として効果があり、また溶
着金属の流動性の調整に効果が大きいが、Siが0.1
0%未満では溶接ビードが凸ビードとなり、ビード重ね
部に未溶融部が生じてその部分から割れが発生し、また
脱酸不足からブローホールが発生して健全は溶着金属が
得られない。一方、Siが3.4%超では、過脱酸とな
って溶融池が沸騰するため、スパッタが増え、溶接作業
性が劣化する。
Si is effective as a deoxidizing agent and has a great effect on adjusting the fluidity of the deposited metal.
If it is less than 0%, the weld bead becomes a convex bead, an unmelted portion is generated in the bead overlapping portion, cracks occur at that portion, and blowholes are generated due to insufficient deoxidation, and a weld metal cannot be obtained soundly. On the other hand, if Si exceeds 3.4%, the molten pool boils due to over-deoxidization, so that spatter increases and welding workability deteriorates.
【0008】MnはSiと同様に脱酸剤としての効果と
溶着金属の耐割れ性の改善に効果がある。しかし、フラ
ックス入りワイヤ中のMnが1.5%未満では溶着金属
に微小割れが発生するなどその効果は十分でない。ま
た、Mnが10.0%超では溶着金属の硬さが低下し、
本来の目的とする硬さが得られない。Coは溶着金属の
再熱部の硬度低下抑制と硬さの安定化に効果があるが、
Coが1.0%未満ではその効果は十分でない。一方、
Coが6.0%超ではその効果も飽和し、それ以上の硬
さの上昇は認められず、また溶着金属に微小な高温割れ
が発生する。
Similar to Si, Mn has an effect as a deoxidizer and an effect of improving the crack resistance of the deposited metal. However, if Mn in the flux-cored wire is less than 1.5%, the effect is not sufficient, such as the occurrence of microcracks in the deposited metal. Further, if Mn exceeds 10.0%, the hardness of the deposited metal decreases,
The intended hardness cannot be obtained. Co is effective in suppressing the decrease in hardness of the reheated portion of the deposited metal and stabilizing the hardness,
If Co is less than 1.0%, the effect is not sufficient. on the other hand,
If the Co content exceeds 6.0%, the effect is saturated, no further increase in hardness is observed, and minute hot cracking occurs in the weld metal.
【0009】アルカリ金属系フッ化物は少量添加するこ
とでアークの安定性改善、溶融スラグの粘性調整に効果
がある。本発明のフラックス入りワイヤのように、高合
金組成を含む材料ではワイヤ設計上、充填フラックスに
全くスラグ剤を添加しない金属粉系またはスラグ剤の添
加を極力低く抑えた設計が必要となり、その面から溶接
作業性、スラグ流動性など少量添加で効果があるアルカ
リ金属系フッ化物は有効である。しかし、フラックス入
りワイヤ中のアルカリ金属系フッ化物の1種または2種
以上が0.05%未満ではその効果は認められず、アー
クの安定性に欠け、スパッタが多く発生する。一方、こ
の量が0.83%超ではスパッタが増加し、ビード表面
に微小なスラグが付着して未溶融欠陥の原因となる。な
お、ここでいうアルカリ金属系フッ化物とは、Na,
K,Liを含む金属フッ化物をいう。
Addition of a small amount of alkali metal fluoride is effective in improving arc stability and adjusting viscosity of molten slag. Like the flux-cored wire of the present invention, in a material containing a high alloy composition, the wire design requires a design in which the addition of a metal powder system or a slag agent in which the slag agent is not added to the filling flux is suppressed as low as possible. Therefore, it is effective to use an alkali metal fluoride, which is effective in adding a small amount such as welding workability and slag fluidity. However, if one or more of the alkali metal fluorides in the flux-cored wire is less than 0.05%, the effect is not recognized, the stability of the arc is insufficient, and spatter is often generated. On the other hand, if this amount exceeds 0.83%, spatter increases, and minute slag adheres to the bead surface, causing unmelted defects. The alkali metal fluorides referred to here are Na,
A metal fluoride containing K and Li.
【0010】またさらに、Crは溶着金属の耐食性、耐
摩耗性および耐熱性の改善に効果が大きい。しかし、C
rが1.1%未満では硬さが不安定となり、目的とする
硬さが得られない。一方、Crが8.3%超では、溶着
金属の硬さもほぼ飽和し、再熱部に微小な高温割れが発
生する。さらに、Mo、Vは溶着金属の再熱部の硬さ低
下を抑制し、硬さの安定化に効果がある。しかし、M
o、Vの1種または2種が0.05%未満ではその効果
は十分でなく、また3.2%超となるとその効果も飽和
し、溶着金属に割れが発生する。
Furthermore, Cr is highly effective in improving the corrosion resistance, wear resistance and heat resistance of the deposited metal. But C
If r is less than 1.1%, the hardness becomes unstable and the desired hardness cannot be obtained. On the other hand, if the Cr content exceeds 8.3%, the hardness of the deposited metal is almost saturated and minute hot cracking occurs in the reheated portion. Further, Mo and V suppress the decrease in hardness of the reheated portion of the deposited metal and are effective in stabilizing the hardness. But M
If 1 or 2 kinds of o and V are less than 0.05%, the effect is not sufficient, and if it exceeds 3.2%, the effect is saturated and cracks occur in the weld metal.
【0011】なお、鋼製外皮とは、JISG3131お
よびJISG3141に規定される圧延鋼板および鋼帯
を示す。
The steel outer shell means a rolled steel plate and a steel strip defined by JISG3131 and JISG3141.
【0012】次に溶接入熱量の限定理由について述べ
る。鋳鉄の溶接は一般的に、 溶接部の急冷により、白銑化して硬化し割れが発生
する、 鋳鉄中に多量に含有する炭素が溶接中に酸化して炭
酸ガスとなり、溶接性を阻害し、ブローホール、ピット
などの発生原因となる、 鋳鉄は母材自身の延性が低いので、溶接時の熱応力
によって割れが発生する、 鋳鉄中のセメンタイト(Fe3 C)は溶接熱によっ
て分解して体積膨張を起こし、急冷により白銑化して収
縮するので、その体積変化により割れが発生する、 などの理由により溶接性は極めて悪いとされている。こ
れらの軽減策として鋳鉄用被覆アーク溶接法では、冷間
溶接、低温予熱溶接および熱間溶接などが溶接材料の組
成、母材の寸法、形状により使い分けられている。
Next, the reasons for limiting the welding heat input will be described. Welding of cast iron generally causes white pig iron to harden and crack due to quenching of the weld.Carbon contained in cast iron in a large amount oxidizes during welding to become carbon dioxide gas, impairing weldability. Cast iron, which causes blow holes and pits, has low ductility in the base metal itself, so cracking occurs due to thermal stress during welding. Cementite (Fe 3 C) in cast iron decomposes due to welding heat It is said that the weldability is extremely poor due to the fact that it expands, shrinks into white pig iron by rapid cooling, and contracts, causing cracks due to its volume change. As a measure to reduce these, in the covered arc welding method for cast iron, cold welding, low-temperature preheating welding, hot welding, etc. are properly used depending on the composition of the welding material, the size and shape of the base material.
【0013】鋳鉄の溶接における溶接入熱量の管理は溶
接の良否を決定する上で重要な因子である。本発明者ら
は鋳鉄の溶接性を阻害しているこれらの原因を軽減する
ため、低温予熱溶接(予熱温度:100〜300℃)に
おける鋳鉄の硬化肉盛溶接用フラックス入りワイヤの開
発を進め、適正なフラックス入りワイヤ組成において、
溶接入熱量と母材を含む割れには図1に示す関係がある
ことを見出した。
Control of the welding heat input in the welding of cast iron is an important factor in determining the quality of welding. In order to reduce these causes that hinder the weldability of cast iron, the present inventors proceeded with the development of a flux-cored wire for hardfacing welding of cast iron in low-temperature preheating welding (preheating temperature: 100 to 300 ° C.), With an appropriate flux-cored wire composition,
It was found that the welding heat input and the crack containing the base material have the relationship shown in FIG.
【0014】即ち、図1は2種類の組成を有するワイヤ
を用い、溶接入熱量を変化させ、鋳鉄へ4パス2層の肉
盛溶接を行い、その後PT試験で溶着金属、母材熱影響
部の割れを測定した結果を整理したもので、この図から
わかるように、溶接熱量が9600Jを超えると母材へ
の溶込みが大きくなり、白銑域(硬化層)の増大、溶接
入熱量の増大により発生した熱応力も当然大きくなるこ
とから、鋳鉄母材と溶着金属の熱歪に対する許容差によ
り母材熱影響部に割れが発生する。従って、溶接入熱量
は鋳鉄溶接ではできるだけ低く抑えることが重要である
が、溶接の安定化などを考慮して、本発明のフラックス
入りワイヤを用いた場合、溶接入熱量を9600J以下
に管理すれば溶着金属、熱影響部の割れは防止できる。
That is, FIG. 1 shows that a wire having two kinds of composition is used, the welding heat input is changed, and a 4-pass two-layer overlay welding is performed on cast iron, and then a weld metal and a base metal heat-affected zone are subjected to a PT test. As can be seen from this figure, when the welding heat quantity exceeds 9600 J, the penetration into the base metal increases, the white pig area (hardened layer) increases, and the welding heat input quantity increases. Since the thermal stress generated by the increase naturally increases, cracks occur in the heat affected zone of the base material due to the tolerance of the cast iron base material and the weld metal with respect to the thermal strain. Therefore, it is important to keep the welding heat input as low as possible in cast iron welding, but if the flux-cored wire of the present invention is used in consideration of stabilization of welding, etc., if the welding heat input is controlled to 9600 J or less. It is possible to prevent cracks in the weld metal and heat affected zone.
【0015】[0015]
【実施例】以下実施例により本発明をさらに詳細に説明
する。表1、表2(表1のつづき−1)、表3(表1の
つづき−2)に製造したフラックス入りワイヤの組成を
示す。ワイヤ径は1.2mmφまたは1.6mmφとし
てフラックス充填率を10〜20%の範囲で組成を調整
し、スラグ剤を含むタイプとスラグ剤を含まない金属粉
系フラックス入りワイヤを製造した。いずれのフラック
ス入りワイヤも伸線性などの生産性は良好であった。
The present invention will be described in more detail with reference to the following examples. Tables 1 and 2 (continuation-1 of Table 1) and Table 3 (continuation-2 of Table 1) show the compositions of the produced flux-cored wires. The wire diameter was 1.2 mmφ or 1.6 mmφ and the composition was adjusted in the range of 10 to 20% of the flux filling rate to produce a type containing a slag agent and a metal powder type flux-cored wire containing no slag agent. All of the flux-cored wires had good productivity such as wire drawability.
【0016】[0016]
【表1】 [Table 1]
【0017】[0017]
【表2】 [Table 2]
【0018】[0018]
【表3】 [Table 3]
【0019】表4に使用した球状黒鉛鋳鉄の化学成分を
示す。
Table 4 shows the chemical composition of the spheroidal graphite cast iron used.
【0020】[0020]
【表4】 [Table 4]
【0021】溶接作業性の評価は、鋳鉄(寸法:20t
×100×200mm)に表5に示す溶接条件で溶接
し、150mm長さのビードを5パス2層溶接を行っ
た。溶着金属の性能試験は、この溶接後の試験片から採
取して断面マクロ試験、分析、硬さ試験を行って評価し
た。試験結果の各項目の評価は下記基準で行った。
Welding workability was evaluated by using cast iron (size: 20 t).
(× 100 × 200 mm) under the welding conditions shown in Table 5, and a bead having a length of 150 mm was subjected to 5-pass two-layer welding. The performance test of the deposited metal was evaluated by conducting a cross-section macro test, an analysis, and a hardness test by collecting the test piece after the welding. Evaluation of each item of the test result was performed according to the following criteria.
【0022】アーク安定性は中断することなく連続して
溶接できたものについて○評価、それ以外を×評価とし
た。スパッタは目視で観察し、溶接中および2層溶接終
了後、鋳鉄母材に付着したスパッタの多少で評価した。
ブローホール、ピートについては断面マクロ試験片でブ
ローホール、ピットの発生していないものについて○評
価、それ以外を×評価とした。
The arc stability was evaluated as ◯ for those that could be welded continuously without interruption, and evaluated as x for other cases. The spatter was visually observed, and the amount of spatter adhered to the cast iron base material was evaluated during welding and after the completion of the two-layer welding.
For blowholes and peat, macroscopic cross-section test pieces without blowholes and pits were evaluated as ◯, and other cases were evaluated as x.
【0023】ビードのなじみについては、断面マクロ試
験片においてビード重ね部にスラグ巻き込み、融合不良
が認められないものについて○評価、それ以外を×評価
とした。耐割れ性については、溶接終了後PT試験にお
いて母材熱影響部に割れが認められたものおよび溶着金
属に割れが認められたものについては×評価とし、全く
割れの認められないものについては○評価とした。
Regarding the familiarity of the bead, the cross-section macro test piece was evaluated as ◯ when the slag was caught in the bead overlapping portion and no defective fusion was observed, and the other was evaluated as x. Regarding cracking resistance, x was evaluated for cracks found in the heat-affected zone of the base metal and for cracks found in the weld metal in the PT test after welding was completed. It was evaluated.
【0024】溶着金属の硬さについては断面マクロ試験
片のビード表面から1mm下の硬さを20点測定した平
均値を示す。なお、溶着金属の硬さは耐割れ性と耐摩耗
性を考慮してHv350〜550を目標とした。これら
の結果を表6(表5のつづき−1)、表7(表5のつづ
き−2)にまとめて示す。
With respect to the hardness of the deposited metal, an average value obtained by measuring the hardness of 20 points at a point 1 mm below the bead surface of the macro-section test piece is shown. The hardness of the deposited metal was set to Hv 350 to 550 in consideration of crack resistance and wear resistance. These results are summarized in Table 6 (continued-1 in Table 5) and Table 7 (continued-2 in Table 5).
【0025】[0025]
【表5】 [Table 5]
【0026】[0026]
【表6】 [Table 6]
【0027】[0027]
【表7】 [Table 7]
【0028】表5、表6(表5のつづき−1)、表7
(表5のつづき−2)中の試験No.1〜9が本発明例
であり、溶接作業性および溶着金属の性能ともに良好で
あり、鋳鉄への硬化肉盛溶接用フラックス入りワイヤと
して極めて満足できるものであった。比較例中に示した
試験No.10は、ワイヤ記号C10のCが低いため、
溶着金属中の炭素量が少なく、目標とする硬さが得られ
ていない。
Tables 5 and 6 (continued from Table 5-1), Table 7
Test No. in (Continued-2 of Table 5). Nos. 1 to 9 are examples of the present invention, and the welding workability and the performance of the deposited metal were good, and they were extremely satisfactory as flux-cored wires for hardfacing welding on cast iron. The test No. shown in the comparative example. 10 has a low C of the wire symbol C10,
The amount of carbon in the deposited metal is too small to achieve the target hardness.
【0029】試験No.11は、ワイヤ記号C11のC
が高いため、溶着金属に割れが認められた。また、アル
カリ金属系フッ化物が少ないため、アークの安定性に欠
け、スパッタ、ビードなじみなどの溶接作業性も悪い。
試験No.12は、ワイヤ記号C12のSiが低いた
め、脱酸不足からピットが発生し、ビードも凸ビードと
なった。また、溶接入熱量が高いため、熱影響部の硬化
層が大きく、熱影響部に割れが認められた。
Test No. 11 is C of wire symbol C11
The cracks were observed in the deposited metal because of the high value. In addition, since the amount of alkali metal fluoride is small, arc stability is poor and welding workability such as spatter and bead familiarity is poor.
Test No. In No. 12, since the wire symbol C12 had low Si, pits were generated due to insufficient deoxidation, and the bead was also a convex bead. Further, since the welding heat input was high, the hardened layer in the heat-affected zone was large, and cracks were observed in the heat-affected zone.
【0030】試験No.13は、ワイヤ記号C13のS
iが高いため、溶接中にプールが沸騰し、アークが不安
定となり、またスパッタが多く、ブローホールも認めら
れ、溶接作業性が悪い。また、溶接入熱量が高いため、
試験No.12と同様に熱影響部に割れが認められた。
試験No.14は、ワイヤ記号C14のMnが低いた
め、溶着金属に微小な割れが認められた。
Test No. 13 is S of wire symbol C13
Since i is high, the pool boils during welding, the arc becomes unstable, there are many spatters, and blowholes are also recognized, and welding workability is poor. Also, because the welding heat input is high,
Test No. As in No. 12, cracks were observed in the heat affected zone.
Test No. In No. 14, since the Mn of wire symbol C14 is low, minute cracks were observed in the deposited metal.
【0031】No.15は、ワイヤ記号C15のMnが
高いため、スパッタが多く、ビードが凸ビードになり、
ブローホールも認められた。また、Crが低いため、溶
着金属の硬さのばらつきが大きく、安定した硬さが得ら
れていない。試験No.16は、ワイヤ記号C16のフ
ッ化物がアルカリ金属系フッ化物を含有していないた
め、溶接作業性のいずれの項目についても悪く、実用性
がなかった。
No. In No. 15, since the wire symbol C15 has a high Mn, spatter is large and the bead is a convex bead.
Blowholes were also recognized. Further, since Cr is low, the hardness of the deposited metal varies widely, and stable hardness is not obtained. Test No. In No. 16, since the fluoride of wire symbol C16 does not contain the alkali metal-based fluoride, the welding workability was poor and was not practical.
【0032】試験No.17は、ワイヤ記号C17のア
ルカリ金属系フッ化物が高いため、スパッタが多量に発
生し、Crが高いのと相まってビードのなじみも悪く、
溶着金属に割れが発生した。また、溶接入熱量も高いた
め、溶け込みが大きく、熱影響部に割れが認められら
た。試験No.18は、ワイヤ記号C18のCoが少な
いため、溶着金属の硬さのばらつきが大きく、割れも認
められた。また、Moを添加したが、硬さの上昇は図れ
なかった。
Test No. In No. 17, since the alkali metal fluoride of wire symbol C17 is high, a large amount of spatter is generated, and in addition to high Cr, the familiarity of beads is poor,
A crack occurred in the weld metal. In addition, since the welding heat input is also high, the penetration was large and cracks were observed in the heat-affected zone. Test No. In No. 18, since the wire symbol C18 had a small amount of Co, the variation in hardness of the deposited metal was large and cracks were also observed. Although Mo was added, the hardness could not be increased.
【0033】試験No.19は、本発明の成分範囲内の
ワイヤ記号C2を用いて溶接を行った例であるが、溶接
入熱量が大きいため、母材熱影響部に割れが認められ
た。試験No.20は、ワイヤ記号C19のMoとVの
合計量が高いため、溶着金属、熱影響部ともに割れが認
められた。試験No.21は、ワイヤ記号C20のCo
が多いため、溶着金属に微小な高温割れが認められた。
Test No. No. 19 is an example in which welding was performed using the wire symbol C2 within the composition range of the present invention, but cracks were observed in the base material heat affected zone because the welding heat input was large. Test No. In No. 20, since the total amount of Mo and V in the wire symbol C19 was high, cracks were observed in both the deposited metal and the heat-affected zone. Test No. 21 is Co of wire symbol C20
As a result, many high temperature cracks were observed in the deposited metal.
【0034】[0034]
【発明の効果】以上述べたように、本発明の鋳鉄の硬化
肉盛溶接用フラックス入りワイヤおよび硬化肉盛溶接方
法によれば、溶接作業性が良好で、溶着金属および母材
熱影響部の割れがなく、硬さも安定し、かつ耐摩耗性の
優れた溶着金属が得られ、その工業的価値は高い。
As described above, according to the flux-cored wire for hardfacing welding of cast iron and the hardfacing welding method of the present invention, the welding workability is good, and the weld metal and the base metal heat affected zone are not affected. A weld metal having no cracks, stable hardness, and excellent wear resistance can be obtained, and its industrial value is high.
【図面の簡単な説明】[Brief description of drawings]
【図1】溶接入熱量と割れ率の関係を示す図である。FIG. 1 is a diagram showing a relationship between a welding heat input amount and a cracking rate.

Claims (4)

    【特許請求の範囲】[Claims]
  1. 【請求項1】 鋼製外皮にフラックスを充填してなるフ
    ラックス入りワイヤにおいて、フラックス入りワイヤ重
    量%でC:0.12〜0.80%、Si:0.1〜3.
    4%、Mn:1.5〜10.0%、Co:1.0〜6.
    0%、アルカリ金属系フッ化物の1種または2種以上:
    0.05〜0.83%を含有することを特徴とする鋳鉄
    の硬化肉盛溶接用フラックス入りワイヤ。
    1. A flux-cored wire comprising a steel outer shell filled with flux, wherein C: 0.12 to 0.80% by weight of flux-cored wire and Si: 0.1 to 3.
    4%, Mn: 1.5 to 10.0%, Co: 1.0 to 6.
    0%, one or more alkali metal fluorides:
    A flux-cored wire for hardfacing hardfacing of cast iron, which contains 0.05 to 0.83%.
  2. 【請求項2】 鋼製外皮にフラックスを充填してなるフ
    ラックス入りワイヤにおいて、フラックス入りワイヤ重
    量%でC:0.12〜0.83%、Si:0.1〜3.
    4%、Mn:1.5〜10.0%、Co:1.0〜6.
    0%、Cr:1.1〜8.3%、アルカリ金属系フッ化
    物の1種または2種以上:0.05〜0.83%を含有
    することを特徴とする鋳鉄の硬化肉盛溶接用フラックス
    入りワイヤ。
    2. A flux-cored wire obtained by filling a steel shell with a flux, wherein C: 0.12 to 0.83% and Si: 0.1 to 3.
    4%, Mn: 1.5 to 10.0%, Co: 1.0 to 6.
    0%, Cr: 1.1 to 8.3%, and one or more alkali metal fluorides: 0.05 to 0.83% for hardfacing welding of hard cast iron. Flux-cored wire.
  3. 【請求項3】 鋼製外皮にフラックスを充填してなるフ
    ラックス入りワイヤにおいて、フラックス入りワイヤ重
    量%でC:0.12〜0.80%、Si:0.1〜3.
    4%、Mn:1.5〜10.0%、Co:1.0〜6.
    0%、Cr:1.1〜8.3%、MoおよびVの何れか
    1種または2種:0.05〜3.2%、アルカリ金属系
    フッ化物の1種または2種以上:0.05〜0.83%
    を含有することを特徴とする鋳鉄の硬化肉盛溶接用フラ
    ックス入りワイヤ。
    3. A flux-cored wire obtained by filling a steel shell with a flux, wherein C: 0.12 to 0.80% and Si: 0.1 to 3.
    4%, Mn: 1.5 to 10.0%, Co: 1.0 to 6.
    0%, Cr: 1.1 to 8.3%, any one or two kinds of Mo and V: 0.05 to 3.2%, one or more kinds of alkali metal fluorides: 0. 05-0.83%
    A flux-cored wire for hardfacing overlay welding of cast iron, characterized by containing.
  4. 【請求項4】 溶接入熱量9600J以下で請求項1、
    請求項2または請求項3記載の鋳鉄の硬化肉盛溶接用フ
    ラックス入りワイヤを用いて肉盛溶接することを特徴と
    する鋳鉄の硬化肉盛溶接方法。
    4. A welding heat input of 9600 J or less,
    A hardfacing welding method for hardfacing cast iron, which comprises overlay welding using the flux-cored wire for hardfacing overlay welding of cast iron according to claim 2 or 3.
JP772694A 1994-01-27 1994-01-27 Flux cored wire for hard facing by welding of cast iron and method for hard facing by welding Pending JPH07214376A (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
JP772694A JPH07214376A (en) 1994-01-27 1994-01-27 Flux cored wire for hard facing by welding of cast iron and method for hard facing by welding

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
JP772694A JPH07214376A (en) 1994-01-27 1994-01-27 Flux cored wire for hard facing by welding of cast iron and method for hard facing by welding

Publications (1)

Publication Number Publication Date
JPH07214376A true JPH07214376A (en) 1995-08-15

Family

ID=11673722

Family Applications (1)

Application Number Title Priority Date Filing Date
JP772694A Pending JPH07214376A (en) 1994-01-27 1994-01-27 Flux cored wire for hard facing by welding of cast iron and method for hard facing by welding

Country Status (1)

Country Link
JP (1) JPH07214376A (en)

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN1078512C (en) * 1998-07-14 2002-01-30 王玉彬 Special flux-cored wirecord for repairing continuous-casting roller
CN103182613A (en) * 2011-12-30 2013-07-03 北京赛亿科技股份有限公司 Impact-resistant thin-diameter self-protection bead weld flux-cored wire
CN103223559A (en) * 2013-05-21 2013-07-31 苏州威奥得焊材科技有限公司 High-manganese high-chromium self-shielded welding wire and production technique thereof
JP2015016497A (en) * 2013-07-12 2015-01-29 株式会社神戸製鋼所 Flux-cored wire for padding
CN105742583A (en) * 2014-12-31 2016-07-06 三星电子株式会社 Composite anode active material, anode including the composite anode active material, and lithium secondary battery including the anode

Cited By (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN1078512C (en) * 1998-07-14 2002-01-30 王玉彬 Special flux-cored wirecord for repairing continuous-casting roller
CN103182613A (en) * 2011-12-30 2013-07-03 北京赛亿科技股份有限公司 Impact-resistant thin-diameter self-protection bead weld flux-cored wire
CN103223559A (en) * 2013-05-21 2013-07-31 苏州威奥得焊材科技有限公司 High-manganese high-chromium self-shielded welding wire and production technique thereof
JP2015016497A (en) * 2013-07-12 2015-01-29 株式会社神戸製鋼所 Flux-cored wire for padding
CN105473277A (en) * 2013-07-12 2016-04-06 株式会社神户制钢所 Flux-cored wire for build-up welding
EP3020504A4 (en) * 2013-07-12 2017-02-22 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Flux-cored wire for build-up welding
CN105742583A (en) * 2014-12-31 2016-07-06 三星电子株式会社 Composite anode active material, anode including the composite anode active material, and lithium secondary battery including the anode
US10164240B2 (en) * 2014-12-31 2018-12-25 Samsung Electronics Co., Ltd. Composite anode active material, anode including the composite anode active material, and lithium secondary battery including the anode
CN105742583B (en) * 2014-12-31 2019-08-09 三星电子株式会社 Composite anode active material, cathode and lithium secondary battery including it

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