KR20230068152A - Flux cored wire for gas shielded arc welding - Google Patents
Flux cored wire for gas shielded arc welding Download PDFInfo
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- KR20230068152A KR20230068152A KR1020210154188A KR20210154188A KR20230068152A KR 20230068152 A KR20230068152 A KR 20230068152A KR 1020210154188 A KR1020210154188 A KR 1020210154188A KR 20210154188 A KR20210154188 A KR 20210154188A KR 20230068152 A KR20230068152 A KR 20230068152A
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- 230000004907 flux Effects 0.000 title claims abstract description 21
- 238000003466 welding Methods 0.000 title abstract description 52
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 229910052751 metal Inorganic materials 0.000 claims description 17
- 239000002184 metal Substances 0.000 claims description 17
- 229910010413 TiO 2 Inorganic materials 0.000 claims description 10
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N Titan oxide Chemical compound O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 claims description 10
- 229910052799 carbon Inorganic materials 0.000 claims description 9
- 229910052748 manganese Inorganic materials 0.000 claims description 9
- 229910052710 silicon Inorganic materials 0.000 claims description 7
- 229910052749 magnesium Inorganic materials 0.000 claims description 6
- 230000000052 comparative effect Effects 0.000 description 45
- 239000011324 bead Substances 0.000 description 40
- 239000011572 manganese Substances 0.000 description 15
- 238000005336 cracking Methods 0.000 description 12
- 229910052760 oxygen Inorganic materials 0.000 description 12
- 239000011777 magnesium Substances 0.000 description 10
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 9
- 229910000831 Steel Inorganic materials 0.000 description 8
- 239000000463 material Substances 0.000 description 8
- 239000010959 steel Substances 0.000 description 8
- 239000000203 mixture Substances 0.000 description 7
- 230000006872 improvement Effects 0.000 description 6
- 230000009467 reduction Effects 0.000 description 6
- 230000015572 biosynthetic process Effects 0.000 description 5
- 239000002893 slag Substances 0.000 description 5
- 230000000694 effects Effects 0.000 description 4
- 239000007789 gas Substances 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 3
- 239000001301 oxygen Substances 0.000 description 3
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 2
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 2
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 2
- 239000003795 chemical substances by application Substances 0.000 description 2
- 238000010276 construction Methods 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 239000010703 silicon Substances 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- KKCBUQHMOMHUOY-UHFFFAOYSA-N Na2O Inorganic materials [O-2].[Na+].[Na+] KKCBUQHMOMHUOY-UHFFFAOYSA-N 0.000 description 1
- 229910004298 SiO 2 Inorganic materials 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 230000007812 deficiency Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000005538 encapsulation Methods 0.000 description 1
- 238000009863 impact test Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 239000010936 titanium Substances 0.000 description 1
- 239000003496 welding fume Substances 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Classifications
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- 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
- B23K35/02—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
- B23K9/00—Arc welding or cutting
- B23K9/16—Arc welding or cutting making use of shielding gas
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
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- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Physics & Mathematics (AREA)
- Plasma & Fusion (AREA)
- Nonmetallic Welding Materials (AREA)
Abstract
Description
본 발명은 가스쉴드 아크 용접용 플럭스 충전 와이어에 관한 것으로서, 보다 상세하게는, 우수한 저온충격인성 및 초층 고온균열 저항성을 가지면서 고전류 조건의 입향상진 용접자세 용접에서 우수한 비드퍼짐성 및 용접성을 갖는 티타니아계 용접용 플럭스 충전 와이어에 관한 것이다.The present invention relates to a flux-filled wire for gas shield arc welding, and more particularly, to a titania-based wire having excellent low-temperature impact toughness and first-layer high-temperature crack resistance, as well as excellent bead spreadability and weldability in vertical welding posture welding under high current conditions. It relates to a flux-filled wire for welding.
최근 조선소에서는 대형 컨테이너선 등에 후물강재 사용 개소가 증가함에 따라 용접에 따른 용접부의 고온균열 발생 빈도가 증가하고 있는 실정이다. 조선소에서는 이러한 균열을 방지하기 위하여 용접조건 등 시공방법의 변경 및 용접재료의 성능을 강화를 요구하고 있다. 또한 조선소에서는 경쟁력 확보를 위한 다양한 노력들을 하고 있다. 있다. 구체적으로는 용접효율성 향상을 통한 비용절감을, 그리고 시공방법 개선 및 용접재료 개발을 요구하고 있다.Recently, in shipyards, as the use of thick steel materials increases in large container ships, etc., the frequency of occurrence of high-temperature cracks in welding parts is increasing. In order to prevent such cracks, shipyards require changes in construction methods such as welding conditions and reinforcement of the performance of welding materials. In addition, shipyards are making various efforts to secure competitiveness. there is. Specifically, cost reduction through welding efficiency improvement, construction method improvement, and welding material development are required.
이와 관련된 종래 기술로는 특허문헌 1에 기재된 발명을 들 수 있다. 상기 특허문헌 1에서는 Mn, Mg, Ti성분과 SiO2, Al2O3 산화물의 비를 제어하여 양호한 고온균열성 및 저온충격인성을 얻고자 하였으나, 현재 조선소에서 요구하는 용접효율성 향상을 통한 비용절감 요구사항에는 부족한 부분이 있다. 이러한 부족한 부분은 조선소에서 주로 사용하는 고전류 조건의 입향상진 용접자세 용접에서 비드퍼짐성이 저하되면서 조선소 용접 현장에서는 비드 표면의 평탄화 작업인 사상 작업이 증가되고 있음을 보면 알 수 있다. 즉, 사상 작업 증가로 인해 용접작업 효율 감소 및 부가적인 비용 증가가 발생되고 있다. 현재 조선소에서는 기존의 고온균열성을 가지면서 비드 표면의 사상 작업의 감소를 통해 용접작업 효율 향상 및 부가적인 작업의 감소를 통한 비용절감을 얻을 수 있는 용접재료 개발을 요구하고 있으며, 이를 통해 선박 건조에 대한 경쟁력 확보를 원하고 있다.As a prior art related to this, the invention described in Patent Document 1 can be cited. In Patent Document 1, the ratio of Mn, Mg, Ti components and SiO 2 , Al 2 O3 oxides was controlled to obtain good high-temperature cracking properties and low-temperature impact toughness, but cost reduction is required by improving welding efficiency required by current shipyards There is a lack of details. This deficiency can be seen in the fact that the bead spreadability is reduced in the vertical welding posture welding under high current conditions mainly used in shipyards, and the deburring work, which is the flattening work of the bead surface, is increasing at the shipyard welding site. That is, due to the increase in finishing work, the efficiency of welding work is reduced and additional costs are increased. Currently, shipyards are demanding the development of a welding material that has the existing high-temperature cracking properties and can obtain cost reduction through improvement of welding work efficiency and reduction of additional work through the reduction of the deburring work on the bead surface, through which the ship is built. want to secure competitiveness.
따라서, 고전류 조건의 입향상진 용접자세 용접에서의 우수한 비드퍼짐성과 저온충격인성, 그리고 고온균열 저항성이 양호한 플럭스 충전 와이어에 대한 개발이 절실히 요구되고 있는 실정이다.Therefore, there is an urgent need to develop a flux-filled wire having excellent bead spreadability, low-temperature impact toughness, and high-temperature crack resistance in vertical welding posture welding under high current conditions.
따라서 본 발명은, 플럭스 충전 와이어의 성분을 적절히 제어함으로써 고전류 조건의 입향상진 용접자세 용접에서 우수한 비드퍼짐성을 가짐과 아울러, 저온충격인성 및 균열 저항성도 우수한 가스쉴드 아크 용접용 플럭스 충전 와이어를 제공함을 목적으로 한다. Therefore, the present invention, by appropriately controlling the components of the flux-filled wire, has excellent bead spreadability in vertical welding posture welding under high current conditions, as well as excellent low-temperature impact toughness and crack resistance. To provide a flux-filled wire for gas shield arc welding The purpose.
또한 본 발명에서 이루고자 하는 기술적 과제들은 이상에서 언급한 기술적 과제들에 한정되지 않으며, 언급하지 않은 또 다른 기술적 과제들은 아래의 기재로부터 본 발명이 속하는 기술분야에서 통상의 지식을 가진 자에게 명확하게 이해될 수 있을 것이다.In addition, the technical problems to be achieved in the present invention are not limited to the above-mentioned technical problems, and other technical problems not mentioned are clearly understood by those skilled in the art from the description below. It could be.
따라서 본 발명의 일 측면은, Therefore, one aspect of the present invention is,
금속 외피내 플럭스가 충전되어 있는 플럭스 코어드 와이어에 있어서,In a flux-cored wire filled with flux in a metal sheath,
자체 질량%로, TiO2 : 5.0~11.0%, C : 0.01~0.09%, Si : 0.6~1.5%, Mn : 2.0~4.0%, Mg : 0.1~1.5%, Na2O : 0.1~ 0.5%, K2O : 0.1~0.5%, 잔부 Fe 및 불가피한 불순물을 포함하고, 하기 관계식 1에 의해 정의되는 H 값이 1.70~3.65를 만족하는 티타니아계 플럭스 코어드 와이어에 관한 것이다.By mass %, TiO 2 : 5.0 to 11.0%, C: 0.01 to 0.09%, Si: 0.6 to 1.5%, Mn: 2.0 to 4.0%, Mg: 0.1 to 1.5%, Na 2 O: 0.1 to 0.5%, It relates to a titania-based flux-cored wire including K 2 O: 0.1 to 0.5%, the balance Fe and unavoidable impurities, and having an H value defined by the following relational expression 1 of 1.70 to 3.65.
[관계식 1][Relationship 1]
상술한 바와 같은 구성의 본 발명의 플럭스 충전 와이어를 사용하면, 고전류 조건의 입향상진 용접자세 용접에서 우수한 비드퍼짐성을 갖으면서 저온충격인성 및 균열 저항성이 우수한 용접금속을 확보할 수 있는 장점이 있다.If the flux-filled wire of the present invention having the configuration described above is used, there is an advantage in securing a weld metal having excellent low-temperature impact toughness and crack resistance while having excellent bead spreadability in welding in an upright welding position under high current conditions.
이하, 본 발명을 설명한다.Hereinafter, the present invention will be described.
본 발명자들은 우수한 저온충격인성 및 고온균열 저항성을 가지면서도 고전류 조건의 입향상진 용접에서 우수한 비드퍼짐성 및 용접성을 갖는 방안을 모색하였으며, 그 결과에 근거하여 본 발명의 제시하는 것이다. The present inventors have sought a method of having excellent low-temperature impact toughness and high-temperature crack resistance while having excellent bead spreadability and weldability in vertical upward welding under high current conditions, and based on the results, the present invention is proposed.
이러한 본 발명의 티타니아계 플럭스 충전 와이어는, 자체 질량%로, TiO2 : 5.0~11.0%, C : 0.01~0.09%, Si : 0.6~1.5%, Mn : 2.0~4.0%, Mg : 0.1~1.5%, Na2O : 0.1~ 0.5%, K2O : 0.1~0.5%, 잔부 Fe 및 불가피한 불순물을 포함하고, 관계식 1에 의해 정의되는 H 값이 1.70~3.65를 만족한다. In the titania-based flux-filled wire of the present invention, TiO 2 : 5.0 to 11.0%, C: 0.01 to 0.09%, Si: 0.6 to 1.5%, Mn: 2.0 to 4.0%, Mg: 0.1 to 1.5% by mass. %, Na 2 O: 0.1 to 0.5%, K 2 O: 0.1 to 0.5%, the balance including Fe and unavoidable impurities, and the H value defined by relational expression 1 satisfies 1.70 to 3.65.
이하, 본 발명의 플럭스 충전 와이어의 조성 성분 및 그 함량 제한사유를 상세히 설명하며, 조성 성분에서 "%"는 달리 규정한 바가 없다면 "질량%"를 의미한다. Hereinafter, the composition of the flux-filled wire of the present invention and the reason for limiting its content will be described in detail, and "%" in the composition means "% by mass" unless otherwise specified.
·탄소(C): 0.01~0.09%·Carbon (C): 0.01~0.09%
탄소(C)는 본 발명 와이어의 강재 외피 및 플럭스에 함유되는 것으로 용접금속의 강도를 확보하고 용접금속의 저온 충격인성을 확보 할 수 있는 오스테나이트 안정화 원소이다. 상기 C의 함량이 0.01% 미만에서는 오스테나이트가 안정화되지 않으므로 용접금속의 저온 충격인성이 저하되고, 0.09%를 초과해서는 강도 증가와 함께 균열감수성 증가로 고온균열이 발생하기 쉬우며, 스패터 발생이 증가하고 용접성이 저하된다. 따라서 본 발명에서는 탄소(C)의 함량은 0.01~0.09% 인 것이 바람직하다.Carbon (C) is contained in the steel sheath and flux of the wire of the present invention, and is an austenite stabilizing element capable of securing the strength of the weld metal and the low-temperature impact toughness of the weld metal. If the content of C is less than 0.01%, since austenite is not stabilized, the low-temperature impact toughness of the weld metal is lowered, and if it exceeds 0.09%, high-temperature cracking is likely to occur due to increased strength and increased crack susceptibility, and spatter generation increase and the weldability deteriorates. Therefore, in the present invention, the content of carbon (C) is preferably 0.01 to 0.09%.
·TiO2: 5.0~11.0%TiO 2 : 5.0~11.0%
TiO2(Ti 산화물)는 용접 시 주된 슬래그 형성제로서 비드 표면을 균일하게 하여 비드 외관을 향상시키는 역할을 한다. TiO2(Ti 산화물)의 함량이 5.0% 미만에서는 슬래그량이 부족하여 슬래그의 포피성 및 박리성이 저하되어 비드 외관이 열악해진다. 또한 TiO2(Ti 산화물)의 함량이 11.0%를 초과하면 슬래그 형성이 과다하고 유동성이 저하되는 문제가 있으며 비드 외관이 저하되므로, 그 함량을 5.0~11.0%로 하는 것이 바람직하다.TiO 2 (Ti oxide) is the main slag forming agent during welding, and serves to improve the appearance of the bead by making the bead surface uniform. If the content of TiO 2 (Ti oxide) is less than 5.0%, the amount of slag is insufficient and the encapsulation and peelability of the slag are deteriorated, resulting in poor bead appearance. In addition, when the content of TiO 2 (Ti oxide) exceeds 11.0%, slag formation is excessive, fluidity is deteriorated, and the appearance of the bead is deteriorated, so the content is preferably set to 5.0 to 11.0%.
·망간(Mn): 2.0~4.0%Manganese (Mn): 2.0 to 4.0%
망간(Mn)은 탈산제로서 용접금속내 산소량을 저감시키며, 용접금속의 강도를 유지시켜 준다. 또한 S와 반응하여 FeS보다 MnS를 먼저 형성하기 때문에 S의 편석에 의한 저융점 화합물의 형성을 방지하여 고온균열 예방에 효과적이다.Manganese (Mn), as a deoxidizer, reduces the amount of oxygen in the weld metal and maintains the strength of the weld metal. In addition, since MnS reacts with S to form MnS before FeS, it is effective in preventing high-temperature cracking by preventing the formation of low-melting compounds due to segregation of S.
그러나 Mn 함량이 2.0% 미만에서는 용접 금속부 내의 탈산 효과가 불충분하여 인성이 저하된다. 반면에 4.0%를 초과하면 저온 변태조직을 생성시켜 균열 저항성 및 인성이 급격하게 저하되고 강도가 증가되어 바람직하지 못하므로, 그 함량을 2.0~4.0%로 하는 것이 바람직하다.However, when the Mn content is less than 2.0%, the deoxidation effect in the weld metal part is insufficient and the toughness is lowered. On the other hand, if it exceeds 4.0%, a low-temperature transformation structure is generated, crack resistance and toughness are rapidly lowered, and strength is increased, which is undesirable. Therefore, it is preferable to set the content to 2.0 to 4.0%.
·실리콘(Si): 0.6~1.5%Silicon (Si): 0.6 to 1.5%
실리콘(Si)은 상기 Mn과 마찬가지로 탈산제로서 용접금속내 산소량을 저감시키며 적정량 첨가시 슬래그 유동성과 비드외관을 향상시키는 역할을 한다. 그러나 상기 Si의 함량이 0.6% 미만이면 용접금속 내의 탈산효과가 떨어지며 비드외관 향상 효과가 미흡하고, 1.5%를 초과하면 M-A상 생성을 촉진시켜 충격인성이 저하되므로, 그 함량을 0.6~1.5%로 하는 것이 바람직하다.Silicon (Si), like Mn, serves to reduce the amount of oxygen in the weld metal as a deoxidizer and improves slag fluidity and bead appearance when added in an appropriate amount. However, if the Si content is less than 0.6%, the deoxidation effect in the weld metal is reduced and the bead appearance improvement effect is insufficient, and if it exceeds 1.5%, the formation of the M-A phase is promoted and the impact toughness is lowered, so the Si content is reduced to 0.6 to 1.5%. It is desirable to do
·마그네슘(Mg): 0.1~1.5%Magnesium (Mg): 0.1 to 1.5%
마그네슘(Mg)은 강탈산제로서 용융금속 내의 산소와 반응하여 비금속 개재물의 생성을 억제하여 용접금속의 청정도 및 충격인성을 향상시킨다. 또한 조직 균일화 및 미세화에 따른 균열전파를 크게 방지할 수 있다. 그러나 그 함유량이 0.1% 미만에서는 탈산 역할이 미비하여 충격 인성 및 균열 저하를 가져올 수 있다. 반면에 1.5%를 초과하면 용접 흄 및 스패터 발생량이 증가하고 아크 집중이 증가하여 작업성이 저하된다. 따라서 Mg의 함량은 0.1~1.5%인 것이 바람직하다.Magnesium (Mg), as a strong deoxidizing agent, reacts with oxygen in molten metal to suppress generation of non-metallic inclusions to improve the cleanliness and impact toughness of weld metal. In addition, crack propagation due to tissue uniformity and refinement can be significantly prevented. However, if the content is less than 0.1%, the role of deoxidation is insufficient, and impact toughness and crack reduction may be brought about. On the other hand, if it exceeds 1.5%, the amount of welding fume and spatter increases and the concentration of arc increases, resulting in deterioration in workability. Therefore, the content of Mg is preferably 0.1 to 1.5%.
·Na2O 및 K2O : 0.1~0.5% ·Na 2 O and K 2 O : 0.1~0.5%
Na2O 및 K2O는 각각 용접 아크의 형성 및 안정성을 확보하는 역할을 하는 원소이다. 상기 효과를 얻기 위해서는 Na2O 및 K2O의 함량이 각각 0.1% 이상으로 첨가해야 하나, 0.5%를 초과해서는 아크 형성이 불안해져서 스패터 발생 및 아크 집중 증가로 용접성이 저해할 수 있기 때문에 Na2O 및 K2O의 함량은 각각 0.1~0.5%인 것이 바람직하다.Na 2 O and K 2 O are elements that play a role in securing the formation and stability of a welding arc, respectively. In order to obtain the above effect, the content of Na 2 O and K 2 O should be added at 0.1% or more, respectively, but if the content exceeds 0.5%, arc formation becomes unstable, and spatter generation and arc concentration increase, which can impair weldability. The content of 2 O and K 2 O is preferably 0.1 to 0.5%, respectively.
상기 조성 이외에 나머지는 강재 외피 중의 Fe, 플럭스 중의 철분 및 불가피하게 첨가되는 불순물을 포함하며, 이는 다른 성분이 첨가되는 것을 배제하는 것이 아니다.In addition to the above composition, the rest includes Fe in the steel shell, iron in the flux, and unavoidable impurities, which do not exclude the addition of other components.
한편, 본 발명자는 TiO2, Na2O, K2O, Si의 적정한 비율을 설정하여 고전류 조건의 입향상진 용접자세에서의 우수한 비드퍼짐성 및 용접성을 확보하였다. 또한 C 및 Mn 함량을 제어하여 저온충격인성 및 고온균열에 대한 저항성을 향상시키는 용접금속 미세조직을 확보하였다. 이에 근거하여, TiO2, Na2O, K2O, Si, C, Mn 함량비가 특정 범위내에 있을 때 가장 양호한 비드퍼짐성 및 우수한 고온균열 감수성을 가지며, 아울러 양호한 용접작업성 및 저온충격인성을 나타냄을 확인하였다. 구적으로, 본 발명은 하기 관계식 1에 의해 정의되는 H 값을 1.70~3.65 범위로 제어함을 특징으로 한다. On the other hand, the present inventors set an appropriate ratio of TiO 2 , Na 2 O, K 2 O, and Si to secure excellent bead spreadability and weldability in a vertical welding posture under high current conditions. In addition, by controlling the C and Mn contents, a weld metal microstructure that improves low-temperature impact toughness and resistance to high-temperature cracking was secured. Based on this, when the content ratio of TiO 2 , Na 2 O, K 2 O, Si, C, and Mn is within a specific range, it has the best bead spreadability and excellent high-temperature crack susceptibility, as well as good welding workability and low-temperature impact toughness. confirmed. Specifically, the present invention is characterized in that the H value defined by the following relational expression 1 is controlled in the range of 1.70 to 3.65.
[관계식 1][Relationship 1]
상기 관계식 1에 의해 저의되는 H 값이 1.70 미만에서는 C 및 Mn 함량의 증가로 용접금속 내 저온변태상 증가 및 용접부 강도가 증가하여 초층 고온균열성이 저하되고, 산화물 및 Si함량이 감소되어 용접성 및 비드퍼짐성이 저하될 수 있다. 반면 상기 H값이 3.65를 초과하는 경우에는 산화물 및 Si합량이 증가되어 용접작업성은 양호해지나 용접금속내에 미세한 침상형 페라이트 생성을 방행하여 저온충격인성이 저하되게 된다. 즉, 상기 관계식 1에 의해 정의되는 H값이 상술한 본 발명 범위를 벗어나는 경우, 초층 고온균열성, 저온충격인성, 용접성, 비드퍼짐성이 문제가 될 수 있다.When the H value determined by the relational expression 1 is less than 1.70, the increase in C and Mn content increases the low-temperature transformation phase in the weld metal and increases the strength of the weld, so that the first layer high-temperature cracking resistance decreases, and the oxide and Si content decreases, resulting in weldability and Bead spreadability may deteriorate. On the other hand, when the H value exceeds 3.65, the amount of oxide and Si increases, so welding workability becomes good, but fine acicular ferrite is formed in the weld metal, resulting in low-temperature impact toughness. That is, when the H value defined by the relational expression 1 is out of the range of the present invention described above, the first layer high-temperature cracking properties, low-temperature impact toughness, weldability, and bead spreadability may become problems.
한편 본 발명은 금속 외피 내에 플럭스가 충전된 플럭스 코어드 와이어에 관한 것으로, 상기 플럭스 코어드 와이어에서, 플럭스의 충전율을 10~20% 범위로 유지함이 바람직하다. On the other hand, the present invention relates to a flux-cored wire in which flux is filled in a metal sheath, and in the flux-cored wire, the flux filling rate is preferably maintained in the range of 10 to 20%.
이하, 본 발명의 실시예에 대하여 상세히 설명한다. Hereinafter, embodiments of the present invention will be described in detail.
(실시예)(Example)
하기 표 1의 조성을 갖는 직경 1.4㎜의 가스실드 아크 용접용 플럭스 충전 와이어를 마련하였다. 표 1의 와이어에서 미기재 성분은 강재 외피 중의 Fe, 플럭스 중 철분 및 불가피한 불순물이며, 성분단위는 질량%이다. 한편 이때 사용된 강재 외피의 조성을 하기 표 2에 나타내었다.A flux-filled wire for gas shielded arc welding having a diameter of 1.4 mm having the composition shown in Table 1 below was prepared. In the wires of Table 1, the unlisted components are Fe in the steel sheath, iron in the flux, and unavoidable impurities, and the component unit is mass%. Meanwhile, the composition of the steel outer shell used at this time is shown in Table 2 below.
*표 1에서 H는 관계식 1에서 정의하는 H 값임. *In Table 1, H is the H value defined in Relational Expression 1.
이어, 상기와 같이 마련된 각각의 와이어를 이용하여 두께 25mm의 AH36 강재에 입향상진 자세로 용접하여 용접부의 저온충격인성을 평가하였으며, 이때 모재 사양은 V형 개선 맞대기용접이며 그 구체적인 용접조건은 하기 표 3과 같다. 그리고 상기 용접 결과, 얻어진 용접부의 0℃ 충격인성 값을 측정하여 표 6에 나타내었다. 이때, 충격 시험편은 KS(KS B 0809) 3호 시험편에 준하여 제조하였으며, 샤르피 충격 시험기를 이용하여 해머로 0℃로 유지된 시편에 충격을 가하였을 때 파단 시 흡수된 에너지를 이용하여 충격인성값을 측정하였다. 구체적으로 상기 측정값이 47J 이상이 나왔을 경우 합격이라고 평가 하였다. Then, using each wire prepared as described above, the low-temperature impact toughness of the weld was evaluated by welding it to AH36 steel with a thickness of 25 mm in an upright posture. Same as 3. And as a result of the welding, the 0 ° C impact toughness values of the obtained weld were measured and shown in Table 6. At this time, the impact test piece was manufactured according to the KS (KS B 0809) No. 3 test piece, and when an impact was applied to the specimen maintained at 0 ° C with a hammer using a Charpy impact tester, the impact toughness value was measured using the energy absorbed at the time of fracture. was measured. Specifically, when the measured value was 47J or more, it was evaluated as passing.
또한 상기와 같이 마련된 각각의 와이어를 이용하여 EH36 35㎜t 강재에 아래보기 자세로 용접하여 용접부의 초층 고온균열시험을 진행하였으며, 그 구체적인 용접조건은 하기 표 4와 같다. 그리고 초층 용접부 비드 표면의 용접균열 길이를 전체 용접길이(600mm)에 대한 백분율로 계산하였으며(균열 발생율(%) = (균열길이)/(용접길이)X100%), 그 계산 결과를 하기 표 6에 나타내었다. 결과 값이 2% 이하이면 고온균열 저항성이 우수한 것으로 판단하였다. In addition, each wire prepared as described above was welded to EH36 35mmt steel in a downward posture to conduct a first layer high temperature crack test of the welded part, and the specific welding conditions are shown in Table 4 below. And the weld crack length of the bead surface of the first layer weld was calculated as a percentage of the total weld length (600 mm) (crack occurrence rate (%) = (crack length) / (weld length) X 100%), and the calculation results are shown in Table 6 below. showed up If the resultant value was 2% or less, it was determined that the high-temperature crack resistance was excellent.
나아가, 상기와 같이 마련된 각각의 와이어를 이용하여, 강재 AH36 25mmt를 이용하여 입향상진 용접자세에서의 비드퍼짐성을 평가하였다. 용접조건은 하기 표 5에 나타냈으며, 비드퍼짐성은 용접부 단면을 이용하여 비드폭(W)과 비드높이(H)를 측정하여 하기 표 6에 나타냈다. 비드폭(W)과 비드높이(H)의 비, 즉 W/H 값이 6.0 이상일 때 비드퍼짐성이 우수한 것으로 판단하였다.Furthermore, by using each of the wires prepared as described above, the bead spreadability was evaluated in an upright welding posture using a steel material AH36 25mmt. The welding conditions are shown in Table 5 below, and the bead spreadability is shown in Table 6 below by measuring the bead width (W) and bead height (H) using the cross section of the welded part. It was determined that the bead spreadability was excellent when the ratio of the bead width (W) and the bead height (H), that is, the W/H value was 6.0 or more.
본 발명의 용접작업성은 비드형상 등을 고려하여 육안으로 비교 판단한 것으로서 우수(○), 보통(△), 불량(Ⅹ)의 3단계로 구분하여 평가하였다.The welding workability of the present invention was visually compared and judged in consideration of the bead shape, etc., and was evaluated by dividing into three stages: excellent (○), normal (Δ), and poor (X).
또한 종합평가는 용접부의 저온충격인성, 초층 고온균열성, 용접작업성, 비드퍼짐성을 고려하여 비교 판단한 것으로서 우수(◎), 보통(○), 미흡(△), 불량(Ⅹ)의 4단계로 구분하여 평가하였다. 여기에서 우수 및 보통은 합격으로, 미흡 및 불량은 불합격으로 간주하였다.In addition, the comprehensive evaluation is a comparative judgment considering the low-temperature impact toughness of the welded part, high-temperature cracking resistance of the first layer, welding workability, and bead spreadability, and is divided into 4 stages: excellent (◎), average (○), poor (△), and poor (X). It was evaluated separately. Here, excellent and average were regarded as pass, and insufficient and poor were regarded as fail.
상기 표 1 및 표 6에 나타난 바와 같이, 본 발명의 조성성분 범위를 만족하는 발명예 1 내지 15의 가스실드 아크 용접용 플럭스 충전 와이어를 이용하여 용접할 경우, 각각 우수한 초층 고온균열 저항성 및 저온충격인성, 용접성, 비드퍼짐성을 나타내는 것을 확인할 수 있다.As shown in Table 1 and Table 6, when welding is performed using the flux-filled wires for gas shielded arc welding of Inventive Examples 1 to 15 satisfying the compositional ranges of the present invention, the first layer has excellent high-temperature crack resistance and low-temperature impact resistance, respectively. It can be confirmed that it exhibits toughness, weldability, and bead spreadability.
이에 반하여, 본 발명의 와이어 조성성분 중 TiO2 함량이 본 발명 범위를 벗어난 비교예 1의 경우 저온충격인성 및 용접성, 비드퍼짐성이 저하되었으며, 비교예 2는 용접성 및 비드퍼짐성이 저하되었다. In contrast, in the case of Comparative Example 1, in which the TiO 2 content of the wire composition of the present invention was outside the scope of the present invention, the low-temperature impact toughness, weldability, and bead spreadability were deteriorated, and in Comparative Example 2, weldability and bead spreadability were deteriorated.
그리고 Si 함량이 본 발명 범위를 벗어난 비교예 5의 경우 저온충격인성 및 용접성, 비드퍼짐성이 저하되었으며, 비교예 6은 용접성 및 비드퍼짐성이 저하되었다.In addition, in the case of Comparative Example 5, in which the Si content was outside the range of the present invention, low-temperature impact toughness, weldability, and bead spreadability were deteriorated, and in Comparative Example 6, weldability and bead spreadability were deteriorated.
또한 Na2O 또는 K2O 함량이 본 발명 범위를 벗어난 비교예 9-12의 경우 용접성 및 비드퍼짐성이 저하되었다.Also, in the case of Comparative Examples 9-12 in which the Na 2 O or K 2 O content was out of the range of the present invention, weldability and bead spreadability were deteriorated.
C 함량이 본 발명 범위를 벗어난 비교예 3의 경우에는 고온균열 및 용접성, 비드퍼짐성이 저하되었으며, 비교예 4의 경우에는 저온 충격인성이 저하되었다.In the case of Comparative Example 3, in which the C content was outside the range of the present invention, high-temperature cracking, weldability, and bead spreadability were deteriorated, and in the case of Comparative Example 4, low-temperature impact toughness was deteriorated.
Mn 함량이 본 발명 범위를 벗어난 비교예 7의 경우에는 고온균열 및 용접성, 비드퍼짐성이 저하되었으며, 비교예 8의 경우에는 저온 충격인성이 저하되었다.In the case of Comparative Example 7, in which the Mn content was outside the range of the present invention, high-temperature cracking, weldability, and bead spreadability were deteriorated, and in the case of Comparative Example 8, low-temperature impact toughness was deteriorated.
아울러, Mg 함량이 본 발명 범위를 벗어난 비교예 13의 경우에는 저온충격인성이 저하되었고, 비교예 14의 경우 용접성 및 비드퍼짐성이 저하되었다.In addition, in the case of Comparative Example 13, in which the Mg content was outside the range of the present invention, the low-temperature impact toughness was lowered, and in the case of Comparative Example 14, weldability and bead spreadability were lowered.
한편 비교예 15-16는 와이어 조성성분은 본 발명범위 이내이나, 관계식 1에 의해 정의되는 H 값이 본 발명의 범위를 벗어난 경우로서, 비교예 15는 저온충격인성이 저하되었으며, 비교예 16은 고온균열 및 용접성 및 비드퍼짐성이 저하되었다.On the other hand, in Comparative Examples 15 and 16, the wire composition is within the scope of the present invention, but the H value defined by relational expression 1 is outside the scope of the present invention. High-temperature cracking and weldability and bead spreadability were deteriorated.
이상에서 설명한 바와 같이, 본 발명의 상세한 설명에서는 본 발명의 바람직한 실시 예에 관하여 설명하였으나, 본 발명이 속하는 기술분야에서 통상의 지식을 가진 자라면 본 발명의 범주에서 벗어나지 않는 한도 내에서 여러 가지 변형이 가능함은 물론이다. 따라서 본 발명의 권리 범위는 설명된 실시 예에 국한되어 정해져서는 안 되며, 후술하는 청구범위뿐만 아니라, 이와 균등한 것들에 의해 정해져야 한다.As described above, the detailed description of the present invention has been described with respect to the preferred embodiments of the present invention, but those skilled in the art to which the present invention belongs can make various modifications without departing from the scope of the present invention. Of course this is possible. Therefore, the scope of the present invention should not be limited to the described embodiments and should not be defined, and should be defined by not only the claims described later, but also those equivalent thereto.
Claims (1)
자체 질량%로, TiO2 : 5.0~11.0%, C : 0.01~0.09%, Si : 0.6~1.5%, Mn : 2.0~4.0%, Mg : 0.1~1.5%, Na2O : 0.1~ 0.5%, K2O : 0.1~0.5%, 잔부 Fe 및 불가피한 불순물을 포함하고, 하기 관계식 1에 의해 정의되는 H 값이 1.70~3.65를 만족하는 티타니아계 플럭스 코어드 와이어.
[관계식 1]
In a flux-cored wire filled with flux in a metal sheath,
By mass %, TiO 2 : 5.0 to 11.0%, C: 0.01 to 0.09%, Si: 0.6 to 1.5%, Mn: 2.0 to 4.0%, Mg: 0.1 to 1.5%, Na 2 O: 0.1 to 0.5%, K 2 O: A titania-based flux-cored wire containing 0.1 to 0.5%, the balance Fe and unavoidable impurities, and having an H value defined by the following relational expression 1 of 1.70 to 3.65.
[Relationship 1]
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KR101286502B1 (en) * | 2011-12-23 | 2013-07-16 | 현대종합금속 주식회사 | Titania type flux cored wire having excellent crack resistance |
JP2016209901A (en) * | 2015-05-07 | 2016-12-15 | 日鐵住金溶接工業株式会社 | FLUX-CORED WIRE FOR Ar-CO2 MIXED GAS SHIELD ARC WELDING |
KR20190118898A (en) | 2018-04-11 | 2019-10-21 | 현대종합금속 주식회사 | Titania Based Flux Cored Wire of Gas Shielded Arc Welding for excellent hot cracking resistance |
KR102244428B1 (en) * | 2016-11-08 | 2021-04-26 | 닛폰세이테츠 가부시키가이샤 | Flux cored wire, manufacturing method of welded joint, and welded joint |
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KR101286502B1 (en) * | 2011-12-23 | 2013-07-16 | 현대종합금속 주식회사 | Titania type flux cored wire having excellent crack resistance |
JP2016209901A (en) * | 2015-05-07 | 2016-12-15 | 日鐵住金溶接工業株式会社 | FLUX-CORED WIRE FOR Ar-CO2 MIXED GAS SHIELD ARC WELDING |
KR102244428B1 (en) * | 2016-11-08 | 2021-04-26 | 닛폰세이테츠 가부시키가이샤 | Flux cored wire, manufacturing method of welded joint, and welded joint |
KR20190118898A (en) | 2018-04-11 | 2019-10-21 | 현대종합금속 주식회사 | Titania Based Flux Cored Wire of Gas Shielded Arc Welding for excellent hot cracking resistance |
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