KR20130073124A - Titania type flux cored wire having excellent crack resistance - Google Patents
Titania type flux cored wire having excellent crack resistance Download PDFInfo
- Publication number
- KR20130073124A KR20130073124A KR1020110140815A KR20110140815A KR20130073124A KR 20130073124 A KR20130073124 A KR 20130073124A KR 1020110140815 A KR1020110140815 A KR 1020110140815A KR 20110140815 A KR20110140815 A KR 20110140815A KR 20130073124 A KR20130073124 A KR 20130073124A
- Authority
- KR
- South Korea
- Prior art keywords
- welding
- wire
- crack resistance
- content
- comparative example
- Prior art date
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
- B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
- B23K35/0255—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in welding
- B23K35/0261—Rods, electrodes, wires
-
- 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
- B23K1/00—Soldering, e.g. brazing, or unsoldering
- B23K1/20—Preliminary treatment of work or areas to be soldered, e.g. in respect of a galvanic coating
- B23K1/203—Fluxing, i.e. applying flux onto surfaces
-
- 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
- B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
- B23K35/0255—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in welding
- B23K35/0261—Rods, electrodes, wires
- B23K35/0266—Rods, electrodes, wires flux-cored
-
- 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 degrees C
- B23K35/3053—Fe as the principal constituent
-
- 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
- B23K35/36—Selection of non-metallic compositions, e.g. coatings, fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest
- B23K35/362—Selection of compositions of fluxes
-
- 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
- B23K35/36—Selection of non-metallic compositions, e.g. coatings, fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest
- B23K35/365—Selection of non-metallic compositions of coating materials either alone or conjoint with selection of soldering or welding materials
-
- 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
- B23K35/40—Making wire or rods for soldering or welding
- B23K35/406—Filled tubular wire or rods
-
- 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
- B23K9/00—Arc welding or cutting
- B23K9/16—Arc welding or cutting making use of shielding gas
- B23K9/173—Arc welding or cutting making use of shielding gas and of a consumable electrode
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Chemical & Material Sciences (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Plasma & Fusion (AREA)
- Nonmetallic Welding Materials (AREA)
Abstract
Description
본 발명은 강재 외피내에 플럭스가 충전되어 있는 플럭스 충전 와이어에 관한 것으로, 보다 상세하게는 고온 균열을 억제하는 내균열성이 우수한 티타니아계 플럭스 충전 와이어에 관한 것이다.
The present invention relates to a flux filling wire in which flux is filled in a steel shell, and more particularly, to a titania-based flux filling wire having excellent crack resistance to suppress high temperature cracking.
티타니아계 플럭스 충전 와이어는 종래부터 그 탁월한 비드 외관과 용접성능 및 용접효율의 우수성으로 인하여 연강 및 50kgf/㎟급 고장력강과 60kgf/㎟급의 고장력강 등의 구조물을 용접하는데 널리 사용되어 오고 있다. 그러나, 티타니아계 플럭스 충전 와이어는 맞대기(Butt) 용접시 용접금속의 충격인성이 만족스럽지 못하기 때문에, 충격인성이 엄격히 제한되는 경우에는 그 사용에 많은 제한이 있었다.
Titania-based flux-filled wires have been widely used for welding structures such as mild steel, 50 kgf / mm 2 high tensile strength steel, and 60 kgf / mm 2 high tensile steel due to their excellent bead appearance, welding performance, and welding efficiency. However, since the titania-based flux-filled wire is not satisfactory in the impact toughness of the weld metal during butt welding, there are many restrictions on its use when the impact toughness is strictly limited.
나아가, 최근 사용되는 강재의 두께가 증가함으로써 용접부의 구속력이 증가하였고, 생산성 향상을 위해 고전류 용접을 실시하는 경우가 많아, 초층용접시 고온균열 발생에 대한 우려가 높아지고 있다. 용접시 용융 금속은 응고가 되어 고온에서 상온으로 냉각되면서 부피가 수축하는 성질이 있지만, 용접구조물은 고정되어 있어서, 용접금속의 수축현상을 방해한다.In addition, as the thickness of steel recently used increases, the binding force of the weld portion is increased, and high current welding is often performed to improve productivity, and there is a concern about the occurrence of high temperature cracking during the first layer welding. While welding, molten metal solidifies and cools at room temperature to room temperature, but the volume shrinks, but the welded structure is fixed, thus preventing the contraction of the weld metal.
특히, 초층 용접 비드의 형상은 두께는 얇고 폭은 넓어 폭방향으로 수축하려는 특성이 커셔 균열이 발생하기 쉽다.
In particular, the shape of the super-layer weld bead is thin and wide, so that the crack tends to occur due to the large shrinkage in the width direction.
본 발명의 일측면은 충격인성이 우수할 뿐만 아니라, 후판의 초층 용접에서도 용접부의 고온 균열을 효과적으로 방지할 수 있는 티타니아계 플럭스 충전 와이어를 제공하고자 하는 것이다.
One aspect of the present invention is to provide a titania-based flux-filled wire that can not only excellent impact toughness, but also effectively prevent high temperature cracking of the weld even in the first layer welding of the thick plate.
본 발명은 강재 외피 내에 플럭스가 충전된 플럭스 충전 와이어에 있어서, 와이어 전중량에 대한 중량%로, C: 0.035~0.050%, Ti2O: 5.5~8.5%, MgO: 0.2~0.7, SiO2: 0.3~0.8, Na2O: 0.1~0.7, K2O: 0.1~0.3%, Si: 0.4~0.6%, Mn: 1.5~2.5%, Mg:0.3~0.7%, 불화물의 F 환산량: 0.05~0.15%, 나머지는 외피중의 Fe, 철분 및 불가피한 불순물을 포함하고, The present invention provides a flux-filled wire in which a flux is filled in a steel shell, wherein the weight is based on the total weight of the wire, C: 0.035 to 0.050%, Ti 2 O: 5.5 to 8.5%, MgO: 0.2 to 0.7, and SiO 2 : 0.3 to 0.8, Na 2 O: 0.1 to 0.7, K 2 O: 0.1 to 0.3%, Si: 0.4 to 0.6%, Mn: 1.5 to 2.5%, Mg: 0.3 to 0.7%, F equivalent amount of fluoride: 0.05 to 0.15%, the remainder containing Fe, iron and inevitable impurities in the skin,
(Mn/Si)×C의 값이 0.15~0.20인 것을 포함하는 내균열성이 우수한 티타니아계 플럭스 충전 와이어를 제공한다.
Provided is a titania-based flux filled wire having excellent crack resistance, including a value of (Mn / Si) × C of 0.15 to 0.20.
본 발명 티타니아계 플럭스 충전 와이어를 이용하여 용접을 행하면, 충격인성이 우수한 용접금속을 얻을 수 있을 뿐만 아니라, 용접금속의 항복비(최대인장강도/하항복강도의 비)를 크게 함으로써 35mm 이상 후판의 초층 용접시에도 고온균열 발생을 효과적으로 방지할 수 있는 효과가 있다.
When welding is performed using the titania-based flux-filled wire of the present invention, not only can a weld metal excellent in impact toughness be obtained, but also the yield ratio (maximum tensile strength / lower yield strength ratio) of the weld metal is increased to increase the thickness of the thick plate to 35 mm or more. Even when the first layer welding, there is an effect that can effectively prevent the occurrence of high temperature cracks.
이하, 본 발명에 대하여 상세히 설명한다.Hereinafter, the present invention will be described in detail.
본 발명자들은 충격인성이 우수한 용접금속을 얻을 수 있고, 후판의 편면 초층 용접시 고온균열을 방지할 수 있는 플럭스 충전 와이어의 개발을 위해 수많은 연구와 실험을 거듭하였다.The present inventors have made numerous studies and experiments for the development of a flux-filled wire which can obtain a weld metal excellent in impact toughness and can prevent high temperature cracks during single-layered superlayer welding of thick plates.
그 결과, 종래 플럭스 충전 와이어의 조성 성분 중 B의 사용을 배재하여, 항복비(최대인장강도/하항복강도의 비)를 크게 하면, 용접부의 연성이 증가되어 효과적으로 고온균열을 방지할 수 있음을 발견하였다. 또한, B를 사용하지 않은데 따른 저온 충격인성 저하를 방지하기 위하여, 용접금속내 개재물 생성을 촉진하는 Al과 Si에 주목하여, Al은 그 사용을 배제하였고, Si 함량은 최소화하는 동시에, Mn, Si 및 C의 상관관계를 고려하여 적정범위와 비를 한정함으로서, 상기 효과를 확보할 수 있음을 인지하고 본 발명에 이르게 되었다.
As a result, if the yield ratio (ratio of maximum tensile strength / lower yield strength) is increased by excluding the use of B in the composition components of the conventional flux-filled wire, the ductility of the weld portion can be increased to effectively prevent high temperature cracking. Found. In addition, in order to prevent the low-temperature impact toughness caused by not using B, Al pays attention to Al and Si that promote the formation of inclusions in the weld metal, Al is excluded from the use, while Si content is minimized, while Mn, Si By limiting the appropriate range and ratio in consideration of the correlation of and C, it was recognized that the above effects can be ensured and led to the present invention.
이하, 본 발명 플럭스 충전 와이어의 조성에 대해 상세히 설명한다. 상기 플럭스 충전 와이어는 강재 외피 내에 플럭스가 충전되어 있는 것으로서, 플럭스 충전 와이어 전중량에 대한 중량%(이하, %)로, C: 0.035~0.050%, Ti2O: 5.5~8.5%, MgO: 0.2~0.7, SiO2: 0.3~0.8, Na2O: 0.1~0.7, K2O: 0.1~0.3%, Si: 0.4~0.6%, Mn: 1.5~2.5%, Mg:0.3~0.7%, 불화물의 F 환산량: 0.05~0.15%, 나머지는 외피중의 Fe, 철분 및 불가피한 불순물을 포함하고, (Mn/Si)×C의 값이 0.15~0.20인 것을 포함한다.
Hereinafter, the composition of the flux filling wire of the present invention will be described in detail. The flux filling wire is a flux filled in the steel shell, the weight% (hereinafter,%) to the total weight of the flux filling wire, C: 0.035 ~ 0.050%, Ti 2 O: 5.5 ~ 8.5%, MgO: 0.2 ~ 0.7, SiO 2 : 0.3 ~ 0.8, Na 2 O: 0.1 ~ 0.7, K 2 O: 0.1 ~ 0.3%, Si: 0.4 ~ 0.6%, Mn: 1.5 ~ 2.5%, Mg: 0.3 ~ 0.7%, of fluoride F conversion amount: 0.05-0.15%, the remainder contains Fe, iron, and an unavoidable impurity in an outer shell, and contains the thing whose value of (Mn / Si) * C is 0.15-0.20.
C: 0.035~0.050%C: 0.035-0.050%
C는 본 발명 와이어를 구성하는 강재 외피와 충전되는 플럭스에 함유되는 성분으로 용접금속의 기계적 성질에 영향을 주는 중요한 인자이며, 특히 B를 배제하면서 저온 충격인성을 확보하기 위하여 그 함유량을 엄격히 제한할 것이 요구된다.C is an important factor affecting the mechanical properties of the weld metal as a component contained in the steel shell and the flux to be constituting the wire of the present invention, and in particular, the content thereof may be strictly limited in order to secure low-temperature impact toughness while excluding B. Is required.
C함량이 0.035% 미만이면 용접금속의 인성이 열화되고, 0.050%를 초과하면 강도가 과도하게 높아지고 균열 감수성을 증가시켜 고온균열이 발생하기 쉽다.
If the C content is less than 0.035%, the toughness of the weld metal is deteriorated. If the C content is more than 0.050%, the strength is excessively high and the crack susceptibility is increased, thereby causing high temperature cracking.
TiO2: 5.5~8.5%TiO 2 : 5.5 ~ 8.5%
TiO2는 아크안정성을 향상시키고, 비드표면을 균일하게 하여 비드외관을 향상시키는 역할을 한다. 그 함량이 5.5% 미만으로 함유되면 슬래그량이 부족하게 되어 아크 안정성이 저하될 뿐만 아니라, 슬래그의 포피성이 열화되어 비드외관이 열악해진다. 또한, 그 함량이 8.5%를 초과하면 슬래그가 과다해져 입향하진 등의 용접자세에서 용융금속이 흘러내리고 비드외관이 열악해지므로, 그 함량을 5.5~8.5%로 하는 것이 바람직하다.
TiO 2 improves arc stability and serves to improve the appearance of beads by making the bead surface uniform. If the content is less than 5.5%, the amount of slag is insufficient, thereby deteriorating the arc stability, as well as deteriorating the foreskin property of the slag, resulting in poor bead appearance. In addition, when the content exceeds 8.5%, the slag becomes excessive, molten metal flows down in the weld posture such as zirconia, and the appearance of the bead becomes poor. Therefore, the content thereof is preferably 5.5 to 8.5%.
MgO: 0.2~0.7%MgO: 0.2-0.7%
MgO는 고융점 슬래그 형성제로서 하향 필렛용접이나 입향상진의 용접자세에서 슬래그의 응고속도를 향상시켜 비드의 처짐을 방지하고 비드외관을 안정화시키는 역할을 한다. 상기 MgO의 함량이 0.2% 미만이면 슬래그 응고속도가 지연되어 비드가 처지거나 외관이 나빠지는 반면에, 0.7%를 초과하게 되면 용융성이 저하되어 스패터 발생량이 증가하는 단점이 있으므로, 그 함량을 0.2~0.7%로 하는 것이 바람직하다.
MgO is a high melting point slag forming agent, which improves the solidification rate of slag in downward fillet welding or upstream welding posture, thereby preventing bead sag and stabilizing bead appearance. If the content of MgO is less than 0.2%, the slag solidification rate is delayed, causing the beads to sag or deteriorate in appearance, whereas if the content of MgO is more than 0.7%, there is a disadvantage in that the meltability decreases and the amount of spatter generated increases. It is preferable to set it as 0.2 to 0.7%.
SiO2: 0.3~0.8%SiO 2 : 0.3 ~ 0.8%
SiO2는 슬래그의 점성을 향상시키며 슬래그가 비드 표면에 고르게 응고하도록 하는 역할을 한다. 그러나, 그 함량이 0.3% 미만으로 너무 적으면 슬래그 점성이 작아져 포피성 저하 및 비드 불균일을 초래하며, 0.8%를 초과하여 과다하게 첨가되면 언더컷이 발생하고 스패터 발생량이 증가하므로, 그 함량을 0.3~0.8%로 하는 것이 바람직하다.
SiO 2 improves the viscosity of the slag and serves to allow the slag to solidify evenly on the bead surface. However, if the content is too small, less than 0.3%, the slag viscosity becomes small, resulting in deterioration of the foreskin and bead non-uniformity, and when excessively added in excess of 0.8%, undercut occurs and the amount of spatter generated increases. It is preferable to set it as 0.3 to 0.8%.
Na2O: 0.1~0.7%Na 2 O: 0.1-0.7%
Na2O는 아크 안정제로서 사용되고 용융성을 향상시키는 성분이다. 그 함량이 0.1% 미만이면 아크 안정제로서의 효과가 부족하고, 용융성 저하에 따라 스패터 발생량이 증가한다. 반면 그 함량이 0.7%를 초과하면 아크 집중이 과다하여 비드 외관을 해치게 되므로, 그 함량을 0.1~0.7%로 하는 것이 바람직하다.
Na 2 O is used as an arc stabilizer and is a component that improves meltability. If the content is less than 0.1%, the effect as an arc stabilizer is insufficient, and the amount of spatter generated increases as the meltability decreases. On the other hand, if the content exceeds 0.7%, the concentration of the arc is excessive, which damages the appearance of the beads. Therefore, the content is preferably 0.1 to 0.7%.
K2O: 0.1~0.3%K 2 O: 0.1-0.3%
K2O도 Na2O와 마찬가지로 아크 안정제로 사용되고 용융성을 향상시키는 역할을 한다. 그 함량이 0.1% 미만에서는 첨가에 따른 효과를 기대하기 어렵고, 0.3%를 초과하는 경우에는 용입이 부족하여 퓸(Fume)의 발생이 증가할 수 있기 때문에, 그 함량을 0.1~0.3%로 하는 것이 바람직하다.
K 2 O, like Na 2 O, is used as an arc stabilizer and serves to improve meltability. If the content is less than 0.1%, it is difficult to expect the effect of the addition. If the content is more than 0.3%, it is insufficient to infiltrate and the generation of fumes may increase, so the content is set at 0.1 to 0.3%. desirable.
Si: 0.4~0.6%Si: 0.4-0.6%
Si는 탈산제 및 슬래그 형성제로서, 비드퍼짐성을 향상시켜 비드외관을 양호하게 하고, 페라이트 안정화 원소로 고온균열을 억제하는 효과가 있다. 그 함량이 0.4% 미만이면 상기 효과를 기대하기 어렵고, 0.6%를 초과하게 되면 Si 개재물로 인하여 인성이 열화되고 고온균열을 초래하기 때문에, 그 함량을 0.4~0.6%로 하는 것이 바람직하다.
Si is a deoxidizer and a slag forming agent, which improves bead spreadability, improves the appearance of beads, and suppresses high temperature cracking with a ferrite stabilizing element. If the content is less than 0.4%, it is difficult to expect the above effect. If the content is more than 0.6%, the toughness is degraded due to Si inclusions and high temperature cracking is caused, so the content is preferably 0.4 to 0.6%.
Mn: 1.5~2.5%Mn: 1.5 ~ 2.5%
Mn은 탈황제로서 저융점 화합물의 형성을 방지하고 용접금속의 탈산효과와 Mn 개재물 형성으로 충격인성과 강도를 상승시킨다. 또한, 비드외관과 형상을 개선하고 양호한 작업성을 얻을 수 있도록 하는 성분이다. 그 함량이 1.5% 미만이면 상기 효과를 기대할 수 없으며, 2.5%를 초과하면 아크 안정성과 용융성이 저하되고 강도도 지나치게 증가하여 고온균열의 발생가능성이 높아지는 문제가 있으므로, 그 함량을 1.5~2.5%로 하는 것이 바람직하다.
Mn is a desulfurization agent that prevents the formation of low melting point compounds and increases the impact toughness and strength by the deoxidation effect of the weld metal and the formation of Mn inclusions. Moreover, it is a component which improves a bead appearance and a shape, and can obtain favorable workability. If the content is less than 1.5%, the above effect cannot be expected. If the content is more than 2.5%, there is a problem that the arc stability and meltability are lowered and the strength is excessively increased to increase the possibility of high temperature cracking, so the content is 1.5 to 2.5%. It is preferable to set it as.
Mg: 0.3~0.7%Mg: 0.3 ~ 0.7%
Mg는 강력한 탈산제로서 기능을 발휘하여 용접금속을 건전하게 한다. 그러나, 상기 함량이 0.3% 미만이면 탈산기능을 제대로 발휘하기 어렵고, 0.7%를 초과하면 용접금속의 건전성은 좋아질 수 있으나, 고온 산화물 형성으로 슬래그 응고속도가 빨라져 비드결이 거칠어지는 단점이 있으므로, 그 함량을 0.3~0.7%로 하는 것이 바람직하다.
Mg functions as a strong deoxidizer to make the weld metal sound. However, if the content is less than 0.3%, it is difficult to properly exhibit the deoxidation function, and if the content exceeds 0.7%, the integrity of the weld metal may be improved, but the slag solidification rate is increased due to the formation of high temperature oxide, resulting in a rough bead grain. It is preferable to make content into 0.3 to 0.7%.
불화물의 F 환산량: 0.05~0.15%F conversion amount of fluoride: 0.05 ~ 0.15%
불화물은 강력한 탈수소제로서 기능을 발휘하여 용접금속의 확산성 수소함량을 낮추어 저온균열 등의 용접결함을 방지하는 역할을 한다. 그 함량이 0.05% 미만이면 상기 역할을 기대하기 어렵고, 0.15%를 초과하는 경우에는 아크가 격렬해져 아크안정성과 비드형상이 저하되므로, 그 함량을 0.05~0.15%로 하는 것이 바람직하다.Fluoride acts as a powerful dehydrogenating agent to lower the diffusible hydrogen content of the weld metal to prevent welding defects such as low temperature cracking. If the content is less than 0.05%, it is difficult to expect the above-mentioned role. If the content is more than 0.15%, the arc becomes violent and the arc stability and the bead shape are lowered. Therefore, the content is preferably 0.05 to 0.15%.
상기 불화물로는 NaF, NaF, Na2SiF6, KF, K2SiF6, CaF, MgF2 등이 있다.
The fluoride includes NaF, NaF, Na 2 SiF 6 , KF, K 2 SiF 6 , CaF, MgF 2, and the like.
상기 성분 외 나머지로는 강재 외피중의 Fe, 철분 및 불가피한 불순물이 포함된다. 그러나, 상기 성분이외에 다른 성분의 첨가를 배제하는 것은 아니다.
Other than the above components, Fe, iron and inevitable impurities in the steel shell are included. However, the addition of other components in addition to the above components is not excluded.
또한, 본 발명은 상기한 바와 같이 종래 플럭스 충전 와이어의 조성 성분 중 B 의 사용을 배제하여 항복비(최대인장강도/하항복강도의 비)를 크게 함으로써 용접부의 연성을 증가시켜 효과적으로 고온균열을 방지한다. 그러나 B의 사용을 배제함에 따라 저온 충격인성이 저하되는 현상을 방지하기 위하여, Al의 사용을 배제하고 Si 함량을 줄여 용접금속내 Al 과 Si 개재물 생성을 억제하는 동시에, (Mn/Si)×C 값을 0.15~0.20 로 제한한다. In addition, the present invention by increasing the yield ratio (maximum tensile strength / lower yield strength ratio) by eliminating the use of B in the composition of the conventional flux-filled wire as described above to increase the ductility of the weld to effectively prevent high temperature cracking do. However, in order to prevent the low temperature impact toughness from being excluded by the use of B, the use of Al is reduced and the Si content is reduced to suppress the formation of Al and Si inclusions in the weld metal and at the same time (Mn / Si) × C Limit the value to 0.15 to 0.20.
상기 (Mn/Si)×C 값이 0.15 미만이면 충격인성이 부족하고, 0.20을 초과하면 충격인성은 향상되나 고온균열이 발생하는 문제가 있다.
If the (Mn / Si) × C value is less than 0.15, impact toughness is insufficient, and if it exceeds 0.20, impact toughness is improved but high temperature cracking occurs.
본 발명의 플럭스 충전 와이어는 플럭스의 충전율이 14~17%인 것이 바람직하다.
The flux filling wire of the present invention preferably has a filling rate of flux of 14 to 17%.
이하, 본 발명의 실시예에 대하여 상세히 설명한다. 하기 실시예는 본 발명의 이해를 위한 것일 뿐, 본 발명을 한정하는 것은 아니다.Hereinafter, embodiments of the present invention will be described in detail. The following examples are only for the understanding of the present invention, but not for limiting the present invention.
(실시예)(Example)
강재 외피에 플럭스를 충전하여, 하기 표 1의 조성을 갖는 직경 1.4㎜, 충전율 16%의 티티니아계 플럭스 충전 와이어를 마련하였다.Flux was filled in the steel shell to prepare a titania-based flux filling wire having a diameter of 1.4 mm and a filling rate of 16% having the composition shown in Table 1 below.
고온균열 저항성을 평가하기 위하여, 상기 표 1의 와이어를 이용하여 표 2의 용접조건으로 두께 35㎜ AH36 용접모재를 편면 용접(세라믹 백킹재 사용)하였으며, 용접 후 균열발생율(%)을 측정하여 그 결과를 표 4에 나타내었다. 이때 균열발생율(%)은 용접비드 표면에 발생한 균열의 길이를 전체 용접길이(500㎜)에 대한 백분율로 계산하였으며, 그 결과치가 2% 이하이면 고온균열 저항성이 우수한 것으로 판단하였다.
In order to evaluate the high temperature crack resistance, a one-sided welding (35 mm thick) of AH36 base metal with a thickness of 35 mm was used under the welding conditions of Table 2 using the wires of Table 1, and the crack incidence (%) was measured after welding. The results are shown in Table 4. At this time, the crack incidence (%) was calculated as a percentage of the total weld length (500 mm) of the crack generated on the surface of the weld bead, it was determined that the high temperature crack resistance is excellent when the result is 2% or less.
한편, 항복비와 충격인성 평가를 위해, 상기 표 1의 와이를 이용하여 두께 20㎜ AH36 용접모재를 표 3의 용접조건으로 용접한 후, 용접에 따른 용접금속의 기계적 성능을 평가하여 하기 표 4에 나타내었다.On the other hand, in order to evaluate the yield ratio and impact toughness, after welding the 20 mm thick AH36 welded base material under the welding conditions of Table 3 using the wires of Table 1, and evaluated the mechanical performance of the weld metal according to the welding Table 4 Shown in
용접금속의 기계적 성능 시험을 실시하여 항복비(최대 인장강도/하항복강도의 비)가 1.120 이상인 경우에는 우수한 것으로, 1.120미만인 경우에는 만족스럽지 못한 것으로 평가하였고, 충격인성은 -30℃에서 테스트하여 그 값이 60J 이상인 경우에는 우수한 것으로, 60J 미만인 경우에는 열위한 것으로 평가하였다.
The mechanical performance test of the weld metal was performed to evaluate the yield strength (ratio of maximum tensile strength / lower yield strength) to 1.120 or more and to be unsatisfactory if it was less than 1.120. The impact toughness was tested at -30 ° C. When the value was 60J or more, it was excellent, and when it was less than 60J, it was evaluated as being inferior.
또한, 용접사의 관능평가를 통해 아크안정성과 비드 형상을 평가하여 우수(◎), 양호(○), 미흡(△) 및 불량(×)으로 표 4에 나타내었다.In addition, the arc stability and the bead shape were evaluated through the sensory evaluation of the welder, and are shown in Table 4 as excellent (◎), good (○), poor (△) and poor (×).
충격인성 평가를 위해, 상기 표 1의 와이를 이용하여 두께 20㎜ AH36 용접모재를 표 3의 용접조건으로 용접한 후, 용접에 따른 용접금속의 기계적 성능을 평가하여 하기 표 4에 나타내었다. In order to evaluate the impact toughness, the 20 mm thick AH36 welded base metal was welded under the welding conditions of Table 3 using the wires of Table 1, and the mechanical performance of the weld metal according to the welding was evaluated and shown in Table 4 below.
용접금속의 기계적 성능 시험을 실시하여 항복비(최대 인장강도/하항복강도의 비)가 1.120 이상인 경우에는 우수한 것으로, 1.120미만인 경우에는 만족스럽지 못한 것으로 평가하였고, 충격인성은 -30℃에서 테스트하여 그 값이 60J 이상인 경우에는 우수한 것으로, 60J 미만인 경우에는 열위한 것으로 평가하였다.
The mechanical performance test of the weld metal was performed to evaluate the yield strength (ratio of maximum tensile strength / lower yield strength) to 1.120 or more and to be unsatisfactory if it was less than 1.120. The impact toughness was tested at -30 ° C. When the value was 60J or more, it was excellent, and when it was less than 60J, it was evaluated as being inferior.
또한, 용접사의 관능평가를 통해 아크안정성과 비드 형상을 평가하여 우수(◎), 양호(○), 미흡(△) 및 불량(×)으로 표 4에 나타내었다.
In addition, the arc stability and the bead shape were evaluated through the sensory evaluation of the welder, and are shown in Table 4 as excellent (◎), good (○), poor (△) and poor (×).
상기 표 1 내지 4로부터 알 수 있듯이, 와이어 조성이 본 발명범위를 만족하고, (Mn/Si)×C 값이 0.15~0.20로 제어된 발명예 1 내지 10은 모두 우수한 고온균열 저항성과 양호한 충격인성을 확보할 수 있었다.
As can be seen from Tables 1 to 4, the invention examples 1 to 10 in which the wire composition satisfies the present invention range and the (Mn / Si) × C value is controlled to 0.15 to 0.20 are all excellent high temperature cracking resistance and good impact toughness. Could secure.
이에 반하여, 비교예 1 내지 6은 (Mn/Si)×C의 값이 본 발명의 범위를 벗어난 것으로, 고온균열이 발생하거나 충격인성이 저하되는 문제가 있었다. 또한, 비교예 7 내지 10은 (Mn/Si)×C의 값은 본 발명의 범위를 만족하지만, Mn, Si, C의 함량이 본 발명의 범위를 벗어난 것으로서, 고온균열이 발생하거나, 충격인성이 저하되는 것을 알 수 있다.
On the contrary, in Comparative Examples 1 to 6, the value of (Mn / Si) × C was out of the range of the present invention, and there was a problem that high temperature cracking occurred or impact toughness was lowered. In addition, in Comparative Examples 7 to 10, the value of (Mn / Si) × C satisfies the scope of the present invention, but the contents of Mn, Si, and C are outside the scope of the present invention, whereby high temperature cracking or impact toughness occurs. It turns out that this falls.
한편, 비교예 11 내지 14는 (Mn/Si)×C의 값은 본 발명의 범위이나, TiO2, Na2O와 같은 다른 성분이 본 발명의 범위를 벗어난 것으로서, 용접작업성(아크 안정성, 비드 형상) 측면에서 바람직하지 않음을 알 수 있다.On the other hand, in Comparative Examples 11 to 14, the value of (Mn / Si) × C is in the range of the present invention, but other components such as TiO 2 and Na 2 O are out of the range of the present invention, and the welding workability (arc stability, It is understood that it is not preferable in terms of bead shape).
Claims (1)
(Mn/Si)×C의 값이 0.15~0.20인 것을 포함하는 내균열성이 우수한 티타니아계 플럭스 충전 와이어.Flux-filled wire in which the flux is filled in the steel shell, in weight% of the total weight of the wire, C: 0.035 to 0.050%, Ti 2 O: 5.5 to 8.5%, MgO: 0.2 to 0.7, SiO 2 : 0.3 to 0.8 , Na 2 O: 0.1-0.7, K 2 O: 0.1-0.3%, Si: 0.4-0.6%, Mn: 1.5-2.5%, Mg: 0.3-0.7%, F conversion amount of fluoride: 0.05-0.15%, The rest contains Fe, iron and inevitable impurities in the skin,
A titania-based flux-filled wire having excellent crack resistance, wherein the value of (Mn / Si) × C is 0.15 to 0.20.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
KR1020110140815A KR101286502B1 (en) | 2011-12-23 | 2011-12-23 | Titania type flux cored wire having excellent crack resistance |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
KR1020110140815A KR101286502B1 (en) | 2011-12-23 | 2011-12-23 | Titania type flux cored wire having excellent crack resistance |
Publications (2)
Publication Number | Publication Date |
---|---|
KR20130073124A true KR20130073124A (en) | 2013-07-03 |
KR101286502B1 KR101286502B1 (en) | 2013-07-16 |
Family
ID=48987639
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
KR1020110140815A KR101286502B1 (en) | 2011-12-23 | 2011-12-23 | Titania type flux cored wire having excellent crack resistance |
Country Status (1)
Country | Link |
---|---|
KR (1) | KR101286502B1 (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN111215788A (en) * | 2019-12-04 | 2020-06-02 | 天津市永昌焊丝有限公司 | Titanium type flux-cored wire for 62 kg-grade weathering steel |
Families Citing this family (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR102664069B1 (en) * | 2021-11-10 | 2024-05-09 | 현대종합금속 주식회사 | Flux cored wire for gas shielded arc welding |
Family Cites Families (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR100538756B1 (en) * | 2000-12-12 | 2005-12-26 | 현대종합금속 주식회사 | Titania type flux cored wire without Boron segregation |
JP4300153B2 (en) * | 2004-05-11 | 2009-07-22 | 日鐵住金溶接工業株式会社 | Flux-cored wire for gas shielded arc welding |
-
2011
- 2011-12-23 KR KR1020110140815A patent/KR101286502B1/en active IP Right Grant
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN111215788A (en) * | 2019-12-04 | 2020-06-02 | 天津市永昌焊丝有限公司 | Titanium type flux-cored wire for 62 kg-grade weathering steel |
Also Published As
Publication number | Publication date |
---|---|
KR101286502B1 (en) | 2013-07-16 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP4986562B2 (en) | Flux-cored wire for titania-based gas shielded arc welding | |
US10286499B2 (en) | Ni based alloy flux cored wire | |
JP5111028B2 (en) | Flux-cored wire for gas shielded arc welding | |
RU2638483C2 (en) | Wire with flux core | |
JP5179073B2 (en) | Flux-cored wire for gas shielded arc welding | |
JP5242665B2 (en) | Flux-cored wire for gas shielded arc welding | |
JP4209913B2 (en) | Flux-cored wire for gas shielded arc welding | |
KR101764008B1 (en) | Ni-based alloy coated arc welding rod | |
KR20030021397A (en) | Basic flux cored wire | |
KR20100006546A (en) | Titania-based flux cored wire for gas shielded arc welding | |
KR101311794B1 (en) | Covered electrode for nickel based high chromium alloy welding | |
JP5744816B2 (en) | Bond flux for submerged arc welding | |
JP2003019595A (en) | Flux cored wire for gas-shielded arc welding for low alloy heat resistant steel | |
KR101600174B1 (en) | Flux cored wire for gas shielded arc welding | |
JP4838100B2 (en) | Flux-cored wire for horizontal corner gas shielded arc welding for weathering steel | |
KR101286502B1 (en) | Titania type flux cored wire having excellent crack resistance | |
JP4949449B2 (en) | Flux-cored wire for welding | |
KR101157572B1 (en) | Titania type flux cored wire | |
KR101065222B1 (en) | Metal-based flux cored wire for gas shielded arc welding | |
JP2009018337A (en) | Flux cored wire for gas-shielded arc welding | |
JP2014065066A (en) | Flux cored wire for horizontal gas shielded arc welding | |
KR102114091B1 (en) | Titania Based Flux Cored Wire of Gas Shielded Arc Welding for excellent hot cracking resistance | |
KR101286501B1 (en) | Flux for submerged arc welding | |
KR101264606B1 (en) | Gas shielded arc welding titania based flux cored wire having excellent crack resistance | |
EP4265370A1 (en) | Flux cored wire |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
A201 | Request for examination | ||
E902 | Notification of reason for refusal | ||
E701 | Decision to grant or registration of patent right | ||
GRNT | Written decision to grant | ||
FPAY | Annual fee payment |
Payment date: 20160629 Year of fee payment: 4 |
|
FPAY | Annual fee payment |
Payment date: 20170628 Year of fee payment: 5 |
|
FPAY | Annual fee payment |
Payment date: 20190701 Year of fee payment: 7 |