JPH0825056B2 - Welding material for hardfacing and submerged arc welding method for hardfacing - Google Patents
Welding material for hardfacing and submerged arc welding method for hardfacingInfo
- Publication number
- JPH0825056B2 JPH0825056B2 JP63307442A JP30744288A JPH0825056B2 JP H0825056 B2 JPH0825056 B2 JP H0825056B2 JP 63307442 A JP63307442 A JP 63307442A JP 30744288 A JP30744288 A JP 30744288A JP H0825056 B2 JPH0825056 B2 JP H0825056B2
- Authority
- JP
- Japan
- Prior art keywords
- flux
- hardfacing
- welding
- submerged arc
- hardness
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Fee Related
Links
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550°C
- B23K35/3053—Fe as the principal constituent
- B23K35/3093—Fe as the principal constituent with other elements as next major constituents
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Nonmetallic Welding Materials (AREA)
Description
【発明の詳細な説明】 （産業上の利用分野） 本発明は硬化肉盛溶接技術に係り、より詳しくは、耐
割れ性、耐摩耗性及び機械加工性が必要な製鉄機械の各
種ロール類、及び耐衝撃性、耐摩耗性及び機械加工性が
必要な破砕粉砕機械の各種部品類などの常温、高温での
金属間摩耗及び高応力、低応力の土砂摩耗を受ける部品
の肉盛溶接に適する高硬度肉盛溶接材料と肉盛溶接施工
法に関するものである。Description: TECHNICAL FIELD The present invention relates to a hardfacing welding technology, and more specifically, various rolls of an iron-making machine that require crack resistance, wear resistance, and machinability. It is also suitable for overlay welding of parts that undergo metal-to-metal wear at high temperature and high temperature and earth and sand stress with high stress and low stress, such as various parts of crushing and crushing machines that require impact resistance, wear resistance and machinability. The present invention relates to a high hardness overlay welding material and an overlay welding construction method.
（従来の技術及び解決しようとする課題） 製鉄機械の各種ロール類や、破砕粉砕機械の各種部品
類などで常温、高温での金属間摩耗及び高応力、低応力
の土砂摩耗を受ける部品等々には、少なくとも優れた耐
摩耗性能を有する材料が必要とされ、一般に硬化肉盛溶
接が採用されている。(Prior art and problems to be solved) For various rolls of iron making machines, various parts of crushing and crushing machines, etc., for parts that are subject to metal-to-metal wear at normal temperature and high temperature and high-stress, low-stress sand wear. Requires a material having at least excellent wear resistance, and hardfacing welding is generally used.
このような耐摩耗性能の優れた材料としては一般に低
合金鋼やマルテンサイト系鋼材料がしられており、各種
ロール等に用いられているが、これらはHv650〜700程度
の硬度を示すことが知られている。また更に、高硬度の
材料としてはＷ−Ｃ等の炭化物、Ｂ−Ｎ等の硼化物など
を多量に含むものが実用化されているが、これらは加工
性が劣り、また溶接割れも発生し易いなどの問題があ
る。Generally, low alloy steel and martensitic steel materials are known as materials having such excellent wear resistance, and they are used for various rolls, etc., but these may show hardness of about Hv650-700. Are known. Further, as a material having a high hardness, a material containing a large amount of a carbide such as WC or a boride such as BN has been put into practical use, but these are poor in workability and cause weld cracking. There are problems such as being easy.
一方、近年、２次硬化を利用して高硬度とすることが
可能な高速度鋼系溶接材料が開発され（特開昭60−1625
90号、特開昭61−7090号）、大幅に加工性及び耐摩耗性
が改善され実用化されつつある。しかし、これらの材料
では特に硬度のムラ、溶接割れを生じ易いなどの問題が
見られ、改善が求められていた。On the other hand, in recent years, high-speed steel-based welding materials capable of achieving high hardness by utilizing secondary hardening have been developed (Japanese Patent Laid-Open No. 60-1625).
No. 90, JP-A No. 61-7090), workability and wear resistance have been greatly improved, and they are being put to practical use. However, problems such as uneven hardness and easy occurrence of weld cracks have been observed with these materials, and improvements have been demanded.
本発明は、上記従来技術の問題点を解決するためにな
されたものであって、硬度ムラ、溶接割れ等がなく高硬
度の肉盛溶接が可能な材料並びに硬化肉盛溶接施工法を
提供することを目的とするものである。The present invention has been made in order to solve the above-mentioned problems of the prior art, and provides a material capable of overlay welding with high hardness without unevenness in hardness, welding cracks and the like, and a hard overlay welding method. That is the purpose.
（課題を解決するための手段） 上述の状況に鑑み、本発明者は、まず、硬度ムラに影
響する因子について検討した。その結果、硬度ムラは溶
接施工時の入熱量、冷却速度のバラツキによる炭化物析
出状態の差及び溶接ビードによる再熱領域が２次硬化を
起こすことによるものであることが判明した。(Means for Solving the Problem) In view of the above situation, the present inventor first examined factors that influence hardness unevenness. As a result, it was found that the uneven hardness was caused by the difference in the amount of heat input during welding, the difference in the carbide precipitation state due to the variation in the cooling rate, and the secondary rehardening in the reheat region due to the weld bead.
そこで、この硬度ムラを解消し得る溶着金属成分につ
いて検討を重ねた結果、ワイヤ成分のうち特にＷ量を制
限することにより、２次硬化現象を安定させ、溶接条件
のバラツキによる２次硬化及び再熱部の短時間での２次
硬化を抑える効果があることを見い出した。Therefore, as a result of repeated studies on the weld metal component that can eliminate this hardness unevenness, the secondary hardening phenomenon is stabilized by limiting the W content in the wire component in particular, and the secondary hardening and re-hardening due to variations in welding conditions are performed. It has been found that it has an effect of suppressing the secondary curing of the hot part in a short time.
また、Ｗ量の制限は溶着金属の伸びを付加し、溶着金
属の収縮割れの抑制にも効果が大なることが判明した。
すなわち、このＷは従来、Moと同じ２次硬化特性を付与
する元素として多量に添加されていたが、上記のように
炭化物析出の安定化及び収縮割れの防止の観点からはＷ
添加量を低くすべきである。It was also found that the limitation of the amount of W adds to the elongation of the deposited metal and has a great effect on the suppression of shrinkage cracking of the deposited metal.
That is, W was conventionally added in a large amount as an element that imparts the same secondary hardening characteristics as Mo, but from the viewpoint of stabilizing carbide precipitation and preventing shrinkage cracks as described above, W is added.
The added amount should be low.
また、Niは高温割れを助長しやすく、1.0以上の含有
は耐高温割れが極めて劣化する。望ましくは0.5以下に
抑制することにより、特に耐高温割れ性が向上すること
が判明した。Further, Ni easily promotes hot cracking, and a content of 1.0 or more causes extremely high resistance to hot cracking. It has been found that the hot crack resistance is particularly improved by suppressing the content to preferably 0.5 or less.
以上の知見に基づき、Cr、Mo、Ｖ、Co等の合金成分を
多量に含有させると共にＷ及びNi量を抑制した特定組成
の硬化肉盛用フラックス入りワイヤを開発したのであ
る。Based on the above findings, a flux-cored wire for hardfacing having a specific composition in which a large amount of alloy components such as Cr, Mo, V, and Co are contained and W and Ni contents are suppressed has been developed.
更に、このようなフラックス入りワイヤを使用する硬
化肉盛溶接はサブマージアーク溶接による行うが、その
組合せフラックスとしては特に限定されないものの、特
定組成、塩基度の焼結フラックスと組合せて使用する
と、より耐割れ性が向上することを見い出した。特に、
耐割れ性は、フラックスの塩基度及びビード形状にも影
響を受け易い欠陥、切欠などのない滑らかなビード形状
の得られる場合に、より向上することが判明した。Further, hardfacing welding using such a flux-cored wire is carried out by submerged arc welding, but the combination flux is not particularly limited, but when it is used in combination with a sintering flux of a specific composition and basicity, it is more resistant. It has been found that the crackability is improved. In particular,
It was found that the crack resistance is further improved when a smooth bead shape without defects, notches, etc., which are easily affected by the basicity of the flux and the bead shape is obtained.
すなわち、本発明に係る硬化肉盛用サブマージアーク
溶接材料は、鋼外皮中にフラックスを充填してなるフラ
ックス入りワイヤであって、ワイヤ全重量当たり、 C:1.0〜2.0％、 Cr:2.0〜8.0％、 Mo:8.5〜15.0％， V:0.5〜4.0％、 Co:2.0〜6.0％、 Mn:0.5〜2.0％、 Si:0.1〜2.0％、 を含有し、かつ、 W:0.8％以下、 Ni:1.0％未満、 に抑制したことを特徴とするものである。That is, the submerged arc welding material for hardfacing according to the present invention is a flux-cored wire obtained by filling a flux in the steel shell, and the total weight of the wire is C: 1.0 to 2.0%, Cr: 2.0 to 8.0. %, Mo: 8.5 to 15.0%, V: 0.5 to 4.0%, Co: 2.0 to 6.0%, Mn: 0.5 to 2.0%, Si: 0.1 to 2.0%, and W: 0.8% or less, Ni : Less than 1.0%.
また、該硬化肉盛用溶接材料を用いる本発明法は、要
するに、上記組成のフラックス入りワイヤと、 MgO:10〜40％、 Al2O3:10〜40％、 BaO:10〜40％、 SiO2:5〜30％、 CaO:3〜20％、 を含有し、且つ塩基度が１以上の焼結型フラックスとを
組合せて使用して硬化肉盛用サブマージアーク溶接し、
必要に応じて、更に525〜625℃×0.5〜10hrの熱処理を
行うことを特徴とするものである。Further, the present invention method using a hardening overlay welding material, in short, a flux-cored wire of the composition, MgO: 10~40%, Al 2 O 3: 10~40%, BaO: 10~40%, Submerged arc welding for hardfacing using SiO 2 : 5 to 30%, CaO: 3 to 20%, in combination with a sintering type flux having a basicity of 1 or more,
It is characterized by further performing heat treatment at 525 to 625 ° C. for 0.5 to 10 hours, if necessary.
以下に本発明を更に詳細に説明する。 The present invention will be described in more detail below.
（作用） （１）まず、本発明における硬化肉盛用溶接材料の成
分限定理由を説明する。(Operation) (1) First, the reasons for limiting the components of the welding material for hardfacing according to the present invention will be described.
硬化肉盛用溶接材料は鋼外皮中にフラックスを充填し
たフラックス入りワイヤとするが、フラックス成分の限
定理由は以下の通りである。The welding material for hardfacing is a flux-cored wire in which the steel shell is filled with flux. The reasons for limiting the flux components are as follows.
C: Ｃは鋼の焼入れ性を高めるために不可欠であり、且
つ、他の炭化物成形元素と結び付いて焼戻しによる２次
硬化現象を生じさせる作用がある。しかし、1.0％未満
ではその効果、特に２次硬化は殆ど得られない。また、
2.0％を超えると溶接時の高温割れが増加するので好ま
しくない。したがって、Ｃ量は1.0〜2.0％の範囲とす
る。C: C is indispensable for enhancing the hardenability of steel, and has the action of forming a secondary hardening phenomenon by tempering in combination with other carbide forming elements. However, if it is less than 1.0%, the effect, particularly the secondary curing, is hardly obtained. Also,
If it exceeds 2.0%, hot cracking during welding increases, which is not preferable. Therefore, the amount of C is made 1.0 to 2.0%.
Cr: Crは溶接のままで硬さを高め、安定化するのに必要で
あるが、２次硬化には寄与率が低い。しかし、耐酸化性
を与えるために必要であり、2.0％未満ではその効果が
ない。一方、多量に含有させると溶接時の高温割れを助
長するため、8.0％以内とする。したがって、Cr量は2.0
〜8.0％の範囲とする。Cr: Cr is necessary to increase hardness and stabilize the as-welded steel, but its contribution to secondary hardening is low. However, it is necessary to give oxidation resistance, and less than 2.0% is not effective. On the other hand, if contained in a large amount, it promotes high temperature cracking during welding, so the content should be within 8.0%. Therefore, the Cr content is 2.0
The range is ~ 8.0%.
Mo: Moは焼戻しによる２次硬化を生ずる主要元素である。
しかし、8.5％未満ではその効果が不充分で、且つ溶接
時の高温割れが生じる。また15.0％を超えるとその効果
は飽和し、且つ不経済である。したがって、Mo量は8.5
〜15.0％の範囲とする。Mo: Mo is the main element that causes secondary hardening by tempering.
However, if it is less than 8.5%, the effect is insufficient, and hot cracking occurs during welding. If it exceeds 15.0%, the effect is saturated and uneconomical. Therefore, the amount of Mo is 8.5
The range is up to 15.0%.
V: Ｖは溶接時の高温割れ防止に効果がある。0.5％以上
でその効果があるが、4.0％を超えるとスラグ剥離性が
劣化するので、Ｖ量は0.5〜4.0％の範囲とする。V: V is effective in preventing hot cracking during welding. If it is 0.5% or more, the effect is obtained, but if it exceeds 4.0%, the slag removability deteriorates, so the V amount is made 0.5 to 4.0%.
Co: Coは溶接時の収縮割れ防止及び２次硬化助長の働きを
有する成分である。しかし、2.0％未満ではその効果が
なく、また6.0％を超えるとその効果は飽和し、不経済
となる。したがって、Co量は2.0〜6.0％の範囲とする。Co: Co is a component that functions to prevent shrinkage cracking during welding and to promote secondary hardening. However, if it is less than 2.0%, it has no effect, and if it exceeds 6.0%, its effect is saturated and it becomes uneconomical. Therefore, the amount of Co is set to 2.0 to 6.0%.
Mn、Si: Mn、Siは脱酸作用を与え、鋼を清浄化する働きを有す
る成分である。しかし、Mnが0.5％未満、Siが0.1％未満
ではその効果がなく、またそれぞれ2.0％を超えると耐
割れ性が劣化する。したがって、Mn量は0.5〜2.0％、Si
量は0.1〜2.0％の範囲とする。Mn, Si: Mn, Si are components that exert a deoxidizing action and clean the steel. However, if Mn is less than 0.5% and Si is less than 0.1%, the effect is not obtained, and if it exceeds 2.0%, crack resistance deteriorates. Therefore, the Mn content is 0.5-2.0%, Si
The amount should be in the range of 0.1-2.0%.
W: Ｗは２次硬化元素ではあるが、0.8％を超えて有する
と、２次硬化現象が不安定になり、硬さムラが生じ、耐
割れ性が劣化する。しかし、0.8％以下に抑制すると、
２次硬化現象を安定化させ、溶接条件のバラツキによる
２次硬化及び再熱部の短時間での２次硬化を抑制する効
果が得られる。また、溶着金属に伸びを付与し、溶着金
属の収縮割れの抑制にも効果があり、耐割れ性が向上す
る。したがって、Ｗ量は0.8％以下に抑制する。勿論、
Ｗ量が０％の場合もあることは云うまでもない。W: W is a secondary hardening element, but if it exceeds 0.8%, the secondary hardening phenomenon becomes unstable, uneven hardness occurs, and crack resistance deteriorates. However, if it is suppressed below 0.8%,
The effect of stabilizing the secondary hardening phenomenon and suppressing the secondary hardening due to variations in welding conditions and the secondary hardening in the reheated part in a short time can be obtained. Further, it imparts elongation to the weld metal, has an effect of suppressing shrinkage cracking of the weld metal, and improves crack resistance. Therefore, the W content is suppressed to 0.8% or less. Of course,
It goes without saying that the W amount may be 0%.
Ni: Niは不純物成分であるが、1.0％以上含有すると耐高
温割れ性が急激に劣化するため、Ni量は1.0％未満に抑
制する。勿論、Ni量が０％の場合もあることは云うまで
もない。Ni: Ni is an impurity component, but if it is contained in an amount of 1.0% or more, the hot cracking resistance rapidly deteriorates, so the Ni content is suppressed to less than 1.0%. Of course, it goes without saying that the Ni content may be 0%.
なお、上記成分を必須成分とするが、Ti、Nb等々を適
宜添加することができる。また、外皮の鋼としては特に
制限されず、またフラックス充填率、ワイヤ形状寸法等
々も制限されないことは云うまでもない。Although the above components are essential components, Ti, Nb, etc. can be added as appropriate. Needless to say, the steel of the outer cover is not particularly limited, and the flux filling rate, the wire shape size, and the like are not limited.
（２）次に、上記フラックス入りワイヤと組合せてサ
ブマージアーク溶接による肉盛溶接を行う場合について
説明する。(2) Next, a case where overlay welding by submerged arc welding is performed in combination with the flux-cored wire will be described.
使用フラックスとしては特に限定されないが、更に耐
割れ性を向上させるためには、次の成分、塩基度を有す
る焼結型フラックスと組合せて使用することが推奨され
る。The flux to be used is not particularly limited, but in order to further improve crack resistance, it is recommended to use it in combination with the following component, a sinter type flux having a basicity.
MgO: MgOは塩基度を高め、溶着金属中の硫黄、酸素量を低
下させ、清浄度を高める効果を有し、及び良好なスラグ
剥離性を付与する働きを有し、耐割れ性の向上に寄与す
る。しかし、10％未満ではその効果が不充分であり、ま
た40％を超えるとビード形状が劣化し、逆にスラグ剥離
性が劣化する。したがって、MgO量は10〜40％の範囲と
する。MgO: MgO has the effect of increasing the basicity, reducing the amount of sulfur and oxygen in the deposited metal, and increasing the cleanliness, and also has the function of imparting good slag removability, improving crack resistance. Contribute. However, if it is less than 10%, the effect is insufficient, and if it exceeds 40%, the bead shape is deteriorated, and conversely the slag removability is deteriorated. Therefore, the amount of MgO should be in the range of 10-40%.
Al2O3： Al2O3は塩基度を低めることなく、スラグ粘性を高
め、溶け落ちを防ぎ、ビード形状を改善する。またスラ
グ剥離性を向上させる効果がある。しかし、10％未満で
はその効果が不充分であり、また40％を超えるとスラグ
の粘性が高くなりすぎるため、逆にビード形状の劣化を
生じる。したがって、Al2O3量は10〜40％の範囲とす
る。Al 2 O 3 : Al 2 O 3 enhances the slag viscosity, prevents burn through, and improves the bead shape without lowering the basicity. It also has the effect of improving the slag removability. However, if it is less than 10%, the effect is insufficient, and if it exceeds 40%, the viscosity of the slag becomes too high, and conversely the bead shape is deteriorated. Therefore, the amount of Al 2 O 3 is set in the range of 10 to 40%.
BaO: BaOは耐ポックマーク性及びビード止端部のなじみ改
善に寄与する。しかし、10％未満ではその効果が不充分
であり、また40％を超えるとビード形状が凸形になる。
したがって、BaO量は10〜40％の範囲とする。BaO: BaO contributes to the resistance to pockmarks and to improving the familiarity of the bead toe. However, if it is less than 10%, its effect is insufficient, and if it exceeds 40%, the bead shape becomes convex.
Therefore, the amount of BaO should be in the range of 10-40%.
なお、BaOの１部又は全部を炭酸塩（BaCO3）の形で添
加しても良い。その場合はBaOに換算した値が上記範囲
（10〜40％）になるように添加する。Incidentally, part or all of BaO may be added in the form of carbonate (BaCO 3 ). In that case, it is added so that the value converted to BaO falls within the above range (10 to 40%).
SiO2： SiO2はスラグに適度な粘性、流動性を与え、ビード外
観形状の改善に寄与する。しかし、５％未満では流動性
が大きく、ビード波目が粗く、不均一になる。また30％
を超えるとスラグ剥離性が低下する。したがって、SiO2
量は５〜30％の範囲とする。SiO 2 : SiO 2 imparts appropriate viscosity and fluidity to the slag and contributes to the improvement of the bead appearance shape. However, if it is less than 5%, the fluidity is large and the bead wave is rough, resulting in non-uniformity. 30% again
If it exceeds, the slag removability will be reduced. Therefore, SiO 2
The amount is in the range of 5 to 30%.
CaO: CaOは塩基度を高め、スラグの粘性を高くする効果が
ある。しかし、３％未満ではその効果が不充分であり、
また20％を超えるとフラックスの耐吸湿性劣化のため、
ピット、ブローホールの発生を招く。したがって、CaO
量は３〜20％の範囲とする。CaO: CaO has the effect of increasing the basicity and increasing the viscosity of the slag. However, if less than 3%, the effect is insufficient,
If it exceeds 20%, the moisture absorption resistance of the flux deteriorates,
This causes pits and blow holes. Therefore, CaO
The amount should be in the range of 3 to 20%.
なお、CaOの一部又は全部を炭酸塩（CaCO3）の形で添
加しても良い。その場合はCaOに換算した値が上記範囲
（３〜20％）となるように添加する。Incidentally, part or all of CaO may be added in the form of carbonate (CaCO 3 ). In that case, it is added so that the value converted to CaO falls within the above range (3 to 20%).
上記焼結型フラックスの塩基度は１以上とする必要が
ある。塩基度が１未満では耐割れ性の向上効果がそれほ
どに期待できない。なお、塩基度は次式の森式表示法に
よって表されるBLの値である。The basicity of the above-mentioned sintering type flux needs to be 1 or more. If the basicity is less than 1, the effect of improving crack resistance cannot be expected so much. The basicity is the value of B L expressed by the Mori-type notation method shown below.
BL＝ΣaiNi ここで、ai：第１表に示す数値 Ni：それぞれの酸化物のモル分率 なお、他の成分としては、Na2O、K2O、CaF2等々を適
宜添加することができる。B L = Σa i N i where a i : Numerical value shown in Table 1 N i : Molar fraction of each oxide In addition, Na 2 O, K 2 O, CaF 2 etc. are used as other components. It can be added as appropriate.
また、フラックス入りワイヤの寸法、断面形状等々に
ついても特に制限されない。Further, the size, cross-sectional shape, etc. of the flux-cored wire are not particularly limited.
上記フラックス入りワイヤ及び焼結型フラックスを使
用してサブマージアーク溶接により肉盛溶接するが、他
の溶接条件は特に制限されない。 Although overlay welding is performed by submerged arc welding using the above flux-cored wire and sintered type flux, other welding conditions are not particularly limited.
しかし、この肉盛溶接の後、525〜625℃×0.5〜10hr
の熱処理を施すことが好ましい。この溶接後熱処理を施
すことにより、更に高硬度にすることが可能である。熱
処理温度が525℃より低い温度或いは加熱時間が0.5hr未
満ではその効果が少なく、また625℃より高い温度或い
は10hrより長時間では過時効となるので好ましくない。However, after this overlay welding, 525-625 ℃ × 0.5-10hr
It is preferable to perform the heat treatment of. It is possible to further increase the hardness by performing the heat treatment after welding. If the heat treatment temperature is lower than 525 ° C. or the heating time is less than 0.5 hr, the effect is small, and if the temperature is higher than 625 ° C. or longer than 10 hr, overaging is not preferable.
次に本発明の実施例を示す。 Next, examples of the present invention will be described.
（実施例） 第２表に示す化学成分を有するフラックス入りワイヤ
と焼結型フラックスを使用し、第１図に示す形状の試験
板（板厚50mm、巾200mm、長さ250mm、溝深さ10mm、溝幅
50mm、溝長さ250mm）を用いて、この試験片を50mmの板
に全周溶接し拘束を付けた後、以下の溶接条件でサブマ
ージアーク溶接により硬化肉盛を行い、溶接後に575℃
×2hrの熱処理（時効硬化処理）を施した。なお、一部
については熱処理条件を変えて熱処理した。(Example) Using a flux-cored wire having a chemical composition shown in Table 2 and a sintering type flux, a test plate having a shape shown in FIG. 1 (plate thickness 50 mm, width 200 mm, length 250 mm, groove depth 10 mm) ,Groove width
(50 mm, groove length 250 mm), this test piece was welded all around the plate of 50 mm and constrained, and then hardfacing was performed by submerged arc welding under the following welding conditions, and 575 ° C after welding.
A heat treatment (age hardening treatment) for 2 hours was performed. Note that some of them were heat-treated under different heat-treatment conditions.
〈溶接条件〉 母材:SM50A 50t×200w×250l ワイヤ径:3.2mmφ 電流:400A（交流） アーク電圧:29〜30V 速度:40cpm 予熱パス間温度:350〜400℃ 塁層法:3層肉盛 溶接後、目視及び液体浸透探傷試験により、収縮割れ
及び高温割れの発生の有無を評価すると共に、溶接のま
までの硬さ及びそのバラツキ並びに熱処理後の硬さ及び
そのバラツキを測定した。それらの結果を第３表に示
す。<Welding conditions> Base material: SM50A 50t × 200w × 250l Wire diameter: 3.2mmφ Current: 400A (AC) Arc voltage: 29-30V Speed: 40cpm Preheating pass temperature: 350-400 ℃ Base layer method: 3 layer overlay After welding, the presence or absence of shrinkage cracks and high temperature cracks was evaluated by visual inspection and liquid penetrant flaw detection test, and the hardness as-welded and its variation and the hardness after heat treatment and its variation were measured. The results are shown in Table 3.
なお、硬さは第２図に示す位置（図中、Ｘ）で5mm間
隔で10点測定した。第３表中、硬さのバラツキは上記位
置を10点測定した値の中での最大値と最小値との差を示
している。最大値、最小値はそれぞれ溶接による再熱部
と原質部であることが多かった。The hardness was measured at 10 points at 5 mm intervals at the position shown in FIG. 2 (X in the figure). In Table 3, the variation in hardness indicates the difference between the maximum value and the minimum value among the values measured at 10 points at the above positions. The maximum and minimum values were often in the reheated part and the original part by welding.
第３表中、本発明例No.1〜No.6、No.7〜No.9、No.18
〜No.23はフラックス入りワイヤが本発明範囲内のもの
であるが、これらのうち、本発明例No.1〜No.6は焼結型
フラックスとして特に制限されないものを使用した例、
本発明例No.7〜No.9並びにNo.18〜No.23は焼結型フラッ
クスとして本発明法で推奨されるものを使用した例であ
る。一方、No.10〜No.17はフラックス入りワイヤが本発
明範囲外の比較例である。In Table 3, invention examples No. 1 to No. 6, No. 7 to No. 9, No. 18
~ No. 23 is a flux-cored wire within the scope of the present invention, among these, the present invention example No. 1 ~ No. 6 is an example of using those not particularly limited as a sintering type flux,
The invention examples No. 7 to No. 9 and No. 18 to No. 23 are examples using the sintering type flux recommended in the method of the present invention. On the other hand, No. 10 to No. 17 are comparative examples in which the flux-cored wire is outside the scope of the present invention.
第３表より以下の如く考察される。 The following is considered from Table 3.
本発明例はいずれも、本発明範囲内の硬化肉盛用溶接
材料を使用したため、硬さムラがなく高硬度が得られ、
耐割れ性（耐収縮割れ性、耐高温割れ性）が良好であ
る。Since all of the examples of the present invention used the welding material for hardfacing in the range of the present invention, high hardness without unevenness in hardness was obtained,
Good crack resistance (shrinkage crack resistance, high temperature crack resistance).
特に、本発明法で推奨される焼結型フラックスを使用
してサブマージアーク溶接により肉盛溶接した本発明例
No.7〜No.9、No.18〜No.20は耐割れ性が更に優れている
ことがわかる。しかし、この場合、熱処理条件が本発明
で推奨する条件でなくとも、硬さのバラツキは小さく、
比較的高硬度となる（本発明例No.21〜No.23）。In particular, the present invention example of overlay welding by submerged arc welding using the sintering type flux recommended in the present invention method
It can be seen that No.7 to No.9 and No.18 to No.20 have further excellent crack resistance. However, in this case, even if the heat treatment conditions are not those recommended in the present invention, the variation in hardness is small,
It has a relatively high hardness (Invention Examples No. 21 to No. 23).
一方、比較例No.10〜No.17は、フラックス入りワイヤ
が本発明範囲外であるため、使用するフラックス、熱処
理等の条件に拘らず、殆どが耐割れ性に劣り、或いは耐
割れ性が良好であっても溶接作業性が悪く、硬さムラの
あるものも認められる。On the other hand, in Comparative Examples No. 10 to No. 17, since the flux-cored wire is out of the scope of the present invention, most of the crack resistance is inferior, or the crack resistance is low, regardless of the conditions such as the flux used and the heat treatment. Even if it is good, welding workability is poor, and some with uneven hardness are also recognized.
（発明の効果） 以上詳述したように、本発明によれば、硬化肉盛用サ
ブマージアーク溶接材料としてのフラックス入りワイヤ
の成分を適切に調整したので、高硬度で硬度ムラがな
く、耐割れ性の良好な硬化肉盛が可能となる。更に、こ
のフラックス入りワイヤと特定組成の焼結型フラックス
とを使用してサブマージアーク溶接により肉盛溶接する
と、耐割れ性が更に優れたものとすることが可能であ
る。 (Effects of the Invention) As described in detail above, according to the present invention, since the components of the flux-cored wire as the submerged arc welding material for hardfacing are appropriately adjusted, the hardness is high, there is no unevenness in hardness, and crack resistance is high. Hardened surfacing with good properties is possible. Further, overlay welding by submerged arc welding using this flux-cored wire and a sintered flux of a specific composition can further improve the crack resistance.
第１図は実施例に用いた試験片の形状寸法を示す断面
図、 第２図は硬さの測定位置を説明する図である。FIG. 1 is a cross-sectional view showing the shape and dimensions of the test piece used in the examples, and FIG. 2 is a view for explaining the hardness measurement position.
Claims (3)
ックス入りワイヤであって、ワイヤ全重量当たり、 C:1.0〜2.0％、 Cr:2.0〜8.0％、 Mo:8.5〜15.0％、 V:0.5〜4.0％、 Co:2.0〜6.0％、 Mn:0.5〜2.0％、 Si:0.1〜2.0％、 を含有し、かつ、 W:0.8％以下、 Ni:1.0％未満、 に抑制したことを特徴とする硬度ムラが少なく耐収縮割
れ性、耐高温割れ性に優れる硬化肉盛用サブマージアー
ク溶接材料。1. A flux-cored wire comprising a steel outer shell filled with flux, wherein C: 1.0 to 2.0%, Cr: 2.0 to 8.0%, Mo: 8.5 to 15.0%, and V: 0.5 to 4.0%, Co: 2.0 to 6.0%, Mn: 0.5 to 2.0%, Si: 0.1 to 2.0%, and W: 0.8% or less, Ni: less than 1.0%. A submerged arc welding material for hardfacing that has little unevenness in hardness and excellent resistance to shrinkage cracking and high temperature cracking.
と、重量％で（以下、同じ） MgO:10〜40％、 Al2O3:10〜40％、 BaO:10〜40％、 SiO2:5〜30％、 CaO:3〜20％、 を含有し、且つ塩基度が１以上の焼結型フラックスとを
組合せて使用することを特徴とする硬化肉盛用サブマー
ジアーク溶接施工法。2. The flux-cored wire according to claim 1, and in weight% (hereinafter the same) MgO: 10-40%, Al 2 O 3 : 10-40%, BaO: 10-40%, SiO 2 : 5 to 30%, CaO: 3 to 20%, and a submerged arc welding method for hardfacing, which is used in combination with a sintering type flux having a basicity of 1 or more.
5〜625℃×0.5〜10hrの熱処理を行うことを特徴とする
硬化肉盛用サブマージアーク溶接施工法。3. After performing the overlay welding according to claim 2, 52
A submerged arc welding method for hardfacing, characterized by performing heat treatment at 5 to 625 ° C for 0.5 to 10 hours.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63307442A JPH0825056B2 (en) | 1988-12-05 | 1988-12-05 | Welding material for hardfacing and submerged arc welding method for hardfacing |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63307442A JPH0825056B2 (en) | 1988-12-05 | 1988-12-05 | Welding material for hardfacing and submerged arc welding method for hardfacing |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH02151392A JPH02151392A (en) | 1990-06-11 |
| JPH0825056B2 true JPH0825056B2 (en) | 1996-03-13 |
Family
ID=17969120
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP63307442A Expired - Fee Related JPH0825056B2 (en) | 1988-12-05 | 1988-12-05 | Welding material for hardfacing and submerged arc welding method for hardfacing |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0825056B2 (en) |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100343751B1 (en) * | 2000-03-16 | 2002-07-20 | 고려용접봉 주식회사 | Flux cored arc welding wire and welding method for surface build-up welding of various rolls |
| CN101450424B (en) | 2007-12-05 | 2011-02-16 | 中冶集团建筑研究总院 | Flux-cored wire for burred-arc build-up welding continuous-casting foot roll |
| CN101905396B (en) * | 2010-08-20 | 2012-09-05 | 河北翼辰实业集团有限公司 | Self-protecting flux-cored wire for hardfacing |
| CN110394830A (en) * | 2018-04-24 | 2019-11-01 | 武汉苏泊尔炊具有限公司 | Cutting tool and processing method of the cutting tool |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS617090A (en) * | 1984-06-21 | 1986-01-13 | Sumikin Yousetsubou Kk | Composite wire for hard facing welding |
-
1988
- 1988-12-05 JP JP63307442A patent/JPH0825056B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH02151392A (en) | 1990-06-11 |
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