KR100450613B1 - A method for manufacturing wire rod for thick plate welding with superior impact toughness - Google Patents
A method for manufacturing wire rod for thick plate welding with superior impact toughness Download PDFInfo
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- KR100450613B1 KR100450613B1 KR10-1999-0063200A KR19990063200A KR100450613B1 KR 100450613 B1 KR100450613 B1 KR 100450613B1 KR 19990063200 A KR19990063200 A KR 19990063200A KR 100450613 B1 KR100450613 B1 KR 100450613B1
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
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- 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
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- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- 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
Abstract
본 발명은 후판용접용 선재의 제조방법에 관한 것으로, 강성분을 조정하고 선재의 제조조건을 상기 강성분에 맞게 조절함으로써, 우수한 기계적 성질 및 충격흡수에너지를 갖고 용접효율이 높은 후판용접용 선재의 제조방법을 제공하고자 하는데, 그 목적이 있다.The present invention relates to a method for manufacturing a thick plate welding wire rod, by adjusting the steel component and adjusting the manufacturing conditions of the wire rod according to the steel component, it has a good mechanical properties, impact absorption energy and high welding efficiency To provide a manufacturing method, the purpose is.
본 발명은 중량%로 C: 0.10%이하, Mn: 1.30~1.50%, Si: 0.5~0.8%, P: 0.020이하, S: 0.010%~0.020%, Ti: 0.10~0.20%, Zr: 0.050~0.140%, Mo: 0.03%이하, 잔부 Fe 및 기타 불가피한 불순물로 이루어지는 강편을 1000~1050℃의 온도범위에서 가열하고, 800~850℃의 온도범위에서 고속압연한 후, 물과 공기의 혼합분사에 의해 750℃ 이하의 온도까지 급냉하여 이 온도에서 권취하고, 650℃ 이하의 온도까지 서냉한후 상온까지 공냉하는 것을 특징으로 하는 충격인성이 우수한 후판용접용 선재의 제조방법을, 그 기술적 요지로 한다.In the present invention, C: 0.10% or less, Mn: 1.30-1.50%, Si: 0.5-0.8%, P: 0.020 or less, S: 0.010%-0.020%, Ti: 0.10-0.20%, Zr: 0.050- 0.140%, Mo: 0.03% or less, steel sheet consisting of residual Fe and other unavoidable impurities is heated at a temperature range of 1000 to 1050 ° C., high-speed rolling at a temperature range of 800 to 850 ° C., and then mixed with water and air. The technical gist of the method for producing a thick-plate welded wire rod having excellent impact toughness is characterized by rapid cooling to a temperature of 750 ° C. or lower, winding up at this temperature, slow cooling to a temperature of 650 ° C. or lower, and air cooling to room temperature. .
Description
본 발명은 혼합가스를 이용한 두께 6mm이상의 건설 중장비용 중후판의 용접에 이용되는 선재의 제조방법에 관한 것으로, 보다 상세하게는 강성분을 조정하고 선재의 제조조건을 적절히 조절함으로써, 우수한 충격흡수에너지 및 높은 용접효율을 갖는 후판용접용 선재의 제조방법에 관한 것이다.The present invention relates to a method for manufacturing a wire rod used for welding a heavy plate for construction heavy equipment having a thickness of 6 mm or more using a mixed gas, and more particularly, by adjusting the steel components and appropriately adjusting the manufacturing conditions of the wire rod, excellent impact absorption energy And it relates to a method for producing a thick plate welding wire rod having a high welding efficiency.
일반적으로 중 후판 용접에 이용되는 특수 용접봉의 경우에는, 용접시 대전류 영역에서 아크가 불안정하고, 용착금속의 강도, 인성등에서 우수한 특성을 내기 어렵다.In general, in the case of a special electrode used for heavy plate welding, the arc is unstable in a large current region during welding, and it is difficult to produce excellent characteristics in the strength and toughness of the weld metal.
특히, 건설 중장비의 경우에는 용접부에서 충분한 충격인성, 중 후판의 용접에서 주어지는 높은 용입에너지(고전류)에 있어서 안정적인 아크유도 및 표면상태에 상관없이 우수한 용접성이 요구된다. 또한, 용접재의 특성상 전자세에서 이산화탄소(CO2) 뿐만 아니라, Ar+CO2등의 혼합가스에서도 적용할 수 있는 활용성을 필요로 한다.Particularly, in the case of construction heavy equipment, a sufficient impact toughness in the welded part, a high arcing energy (high current) given in the welding of the heavy plate, stable arc induction and excellent weldability regardless of the surface condition is required. In addition, due to the nature of the welding material, not only carbon dioxide (CO 2 ) in the electric field, but also needs to be applicable to a mixed gas such as Ar + CO 2 .
상기한 바와 같은 용접성의 향상을 위해서, 종래에는 주로 저탄소강에 망간(Mn), 티탄늄(Ti)등의 탈산재 성분을 첨가하였으나, Ti의 경우에는 용접성 및 용접부의 강도향상 등에 영향을 미치지만, Mn은 선재가공중 저온조직인 마르텐사이트등을 형성시켜 이후 공정인 신선가공을 어렵게 하는 문제가 있다.In order to improve the weldability as described above, in the past, deoxidizer components such as manganese (Mn) and titanium (Ti) are mainly added to low carbon steel, but Ti affects weldability and improved weld strength. , Mn forms a martensite, such as a low-temperature structure during wire processing, there is a problem that it is difficult to process the wire afterward.
한편, 중후판용접의 경우 용착부의 충분한 인성치가 요구되는데, 이를 얻기 위해서는 O, S, N 등과의 반응성을 고려하여 설파이드(Sulfide), 옥시설파이드 (Oxysulfide) 등의 비금속 개재물을 제어해야하기 때문에, 제조방법 및 성분계에 있어서 적절한 조건을 도출해야 한다.On the other hand, in the case of heavy plate welding, sufficient toughness of the weld is required, and in order to obtain this, it is necessary to control non-metallic inclusions such as sulfide and oxysulfide in consideration of reactivity with O, S, N, etc. Appropriate conditions should be derived for the method and composition.
이에 본 발명자들은 상기 목적을 달성하기 위하여 연구와 실험을 거듭하고 그 결과에 근거하여 본 발명을 제안하게 된 것으로, 본 발명은 강성분을 조정하고 선재의 제조조건을 상기 강성분에 맞게 조절함으로써, 우수한 기계적 성질 및 충격흡수에너지를 갖고 용접효율이 높은 후판용접용 선재의 제조방법을 제공하고자 하는데, 그 목적이 있다.In order to achieve the above object, the present inventors have repeatedly conducted research and experiment and propose the present invention based on the results. The present invention adjusts the steel component and adjusts the manufacturing conditions of the wire rod to the steel component. An object of the present invention is to provide a method for manufacturing a thick plate welding wire rod having excellent mechanical properties and impact absorption energy and high welding efficiency.
본 발명은 중량%로 C: 0.10%이하, Mn: 1.30~1.50%, Si: 0.5~0.8%, P: 0.020이하, S: 0.010%~0.020%, Ti: 0.10~0.20%, Zr: 0.050~0.140%, Mo: 0.03%이하, 잔부 Fe 및 기타 불가피한 불순물로 이루어지는 강편을 1000~1050℃의 온도범위에서 가열하고, 800~850℃의 온도범위에서 고속압연한 후, 물과 공기의 혼합분사에 의해 750℃ 이하의 온도까지 급냉하여 이 온도에서 권취하고, 650℃ 이하의 온도까지 서냉한후 상온까지 공냉하는 것을 특징으로 하는 용접부충격인성이 우수한 후판용접용 선재의 제조방법에 관한 것이다.In the present invention, C: 0.10% or less, Mn: 1.30-1.50%, Si: 0.5-0.8%, P: 0.020 or less, S: 0.010%-0.020%, Ti: 0.10-0.20%, Zr: 0.050- 0.140%, Mo: 0.03% or less, steel sheet consisting of residual Fe and other unavoidable impurities is heated at a temperature range of 1000 to 1050 ° C., high-speed rolling at a temperature range of 800 to 850 ° C., and then mixed with water and air. The present invention relates to a method for producing a thick plate welding wire rod having excellent weld impact toughness, which is rapidly cooled to a temperature of 750 ° C. or lower, wound up at this temperature, and slowly cooled to a temperature of 650 ° C. or lower.
이하, 본 발명을 보다 상세히 설명한다.Hereinafter, the present invention will be described in more detail.
상기 C는 강재의 강도를 향상시키는 필수성분이지만, 다량 함유된 경우에는 인성과 용접성을 저하시키고, 특히 0.10%보다 많이 첨가되면, 용접시 스패터량이 증가하여 용접작업성이 좋지 않을 뿐만 아니라, 용접와이어 신선시 경조직에 의해 신선성이 떨어지므로, 그 상한을 0.10%로 설정하는 것이 바람직하다. 이와 같이 하면, 용접금속 용접부의 균열이 발생하지 않아 우수한 내균열성을 확보할 수 있다.The C is an essential component for improving the strength of the steel, but when contained in a large amount, the toughness and weldability are lowered, and in particular, when more than 0.10% is added, the amount of spatter is increased during welding, resulting in poor weldability. Since the freshness is inferior by the hard structure at the time of wire drawing, it is preferable to set the upper limit to 0.10%. In this way, cracks in the weld metal weld portion do not occur and excellent cracking resistance can be ensured.
상기 Si은 용접시 중요한 탈산재이며 고용강화 원소이지만, 과도하게 함유되는 경우에는 용접부의 인성을 열화시키므로, 그 성분범위를 0.5~0.8%로 설정하는 것이 바람직하다.Si is an important deoxidizer during welding and is a solid solution strengthening element, but when excessively contained, it degrades the toughness of the welded part, and therefore it is preferable to set its component range to 0.5 to 0.8%.
상기 Si는 Mn와 함께 함량증가에 따라 용접시 스패터를 감소시키는데, Mn에 비해 Si의 경우가 스패터를 감소 시키는 효과가 크다.The Si reduces the spatter during welding as the content increases with Mn, and Si has a greater effect of reducing the spatter compared to Mn.
상기 Mn은 기본적으로 강도확보에 필요한 원소이지만, 다량 함유하면 용접성을 저하시키고 편석부의 인성을 저하시키므로, 그 성분범위를 1.30~1.50%로 설정하는 것이 바람직하다.The Mn is basically an element necessary for securing strength, but if it contains a large amount, the weldability is lowered and the toughness of the segregation portion is lowered. Therefore, the component range is preferably set to 1.30 to 1.50%.
한편, 용접금속의 인성은 일반적으로 잘 알려져 있는 산소함량에 의해서만 영향을 받는 것이 아니라, Si 및 Mn 함유량에 따라서도 크게 변화하는데, 특히, Si, Mn의 특정 함량범위내에서는 높은 인성치를 확보할 수 있다. 그 이유는, Si 및 Mn이 탈산원소로서의 역할뿐만 아니라 합금원소로서 용접금속의 조직변화에도 큰 역할을 수행하기 때문이다.On the other hand, the toughness of the weld metal is not only influenced by the well-known oxygen content, but also varies greatly depending on the content of Si and Mn. In particular, it is possible to secure high toughness within a specific content range of Si and Mn. have. The reason is that Si and Mn play a big role not only as the deoxidation element but also as the alloying element as the alloying element.
즉, 저Si-저Mn계에서는 소입성이 부족하여 조대한 페라이트(Ferrite)가 발달하고, 고Si-고Mn계에서는 래스상조직이 발달하여 파괴의 유효 결정립경을 크게하여 인성을 저하시키지만, 적정 Si-Mn계에서는 비교적 입내 페라이트를 미세화하여 인성을 향상시킨다.In other words, low Si-Low Mn system lacks hardenability, coarse ferrite develops, and high Si-High Mn system develops a lattice phase structure, thereby increasing the effective grain size of fracture and decreasing toughness. In an appropriate Si-Mn system, ferritic particles are relatively refined to improve toughness.
상기 P은 강의 제조상 불가피하게 함유되는 원소로서, 편석되기 쉽고 저온 변태조직을 형성하기 쉬우며, 산소와 친화력이 강하여 용접성을 해치기 때문에, 그 상한을 0.020%로 한정하는 것이 바람직하다.P is an element inevitably contained in the production of steel, and is easy to segregate, easily form a low temperature transformation structure, and has a high affinity with oxygen to impair weldability. Therefore, the upper limit thereof is preferably limited to 0.020%.
상기 S은 강의 제조상 불가피하게 함유되는 원소로서, 그 함량이 증가함에 따라 아크특성이 개선되는데, 그 이유는 용적이행을 억제하는 주된 힘인 용융금속의 표면장력이 감소하여 용적이행현상이 안정화되기 때문이다. 그러나, 그 함량이 0.020%를 초과하면 용융금속의 표면에너지가 과도하게 감소하여 용입이 깊어짐으로서 현저한 가스팽창 또는 순간단락 등과 같은 불안정한 아크현상에 의해 용융금속의 표면에 작용하는 강한 아크력 혹은 가스압력에 의하여 용적이나 용융지의 저항력이 감소함에 따라 스패터 발생이 촉진된다. 또한, 비금속개재물을 증가시켜 인성을 열화시키므로, 그 성분범위를 0.010~0.020%로 설정하는 것이 바람직하다. 즉, 그 함량이 0.010% 미만이거나 0.020%를 초과하면 스패터 발생량 및 대립의 스패터 발생비율이 증가하므로, 바람직하지 않다.S is an element that is inevitably contained in the production of steel, the arc properties are improved as its content increases, because the surface tension of the molten metal, which is the main force that inhibits the volume migration, decreases, thereby stabilizing the volume migration phenomenon. . However, if the content exceeds 0.020%, the surface energy of the molten metal is excessively reduced to deepen the penetration, and thus strong arc force or gas pressure acting on the surface of the molten metal by unstable arc phenomenon such as significant gas expansion or short circuit. As a result, the spatter generation is accelerated as the volume and the resistance of the molten pool decrease. In addition, since the toughness is deteriorated by increasing the non-metallic inclusion, it is preferable to set the component range to 0.010 to 0.020%. That is, when the content is less than 0.010% or more than 0.020%, the spatter generation amount and the spatter generation rate of the opposing increase, which is not preferable.
상기 Zr은 충격인성증가를 위해 첨가된 원소로, [O], [S], [N] 등과의 반응성이 좋기 때문에, 이러한 반응성을 고려하여 설퍼이드(Sulfide), 옥시설파이드 (Oxysulfide) 개재물을 제어하면 Z-방향의 충격치 및 취성치를 향상시킬 수 있는 효과를 얻을 수 있다. 특히, Zr/S≥1.41로 제어하면 MnS→ZrS2로 되어 열간열화를 억제함으로써, 취성 및 충격치를 향상시킬 수 있다. 본 발명에서는, 그 성분범위를 0.050~0.140%로 설정하는 것이 바람직한데, 이와 같이 하면, 결정립의 설파이드막 (Sulfide film)형성을 억제할 수 있고, 결정립성장을 억제하여 결정립을 미세화할 수 있으며, YP/TS비를 향상시키고 용접 비드(Bead) 직하의 다공성(porosity) 및 크랙을 저감하여 용접성을 향상시킬 수 있다.Zr is an element added to increase the impact toughness, and since the reactivity with [O], [S], [N], etc. is good, the sulfide and oxygensulfide inclusions are controlled in consideration of such reactivity. In this case, the effect of improving the impact value and brittleness value in the Z-direction can be obtained. In particular, when Zr / S? 1.41 is controlled, MnS? ZrS 2 is suppressed, so that brittleness and impact value can be improved. In the present invention, the component range is preferably set to 0.050 to 0.140%. In this case, the formation of a sulfide film of crystal grains can be suppressed, and grain growth can be suppressed to refine the grains. The weldability can be improved by improving the YP / TS ratio and reducing the porosity and cracks directly under the weld bead.
상기 Mo은 그 함량을 0.03%이하로 설정하는 것이 바람직한데, 그 이유는 그 함량이 0.03%를 초과하면 강도는 증가하나 인성이 저하하여, 용접금속이 래스상 페라이트로 이루어지고 페라이트와 페라이트 사이에 고경화 조직이 생성되고, 취성균열의 전파경로가 되는 문제가 있기 때문이다.The Mo is preferably set to less than 0.03%, because if the content exceeds 0.03%, the strength is increased but the toughness is reduced, the weld metal is made of las ferrite and between the ferrite and the ferrite This is because there is a problem that a hardened tissue is produced and becomes a propagation path of brittle cracks.
상기 Ti은 그 함량을 0.1~0.2%로 설정하는 것이 바람직한데, 그 이유는 그 함량이 0.1% 미만일 경우에는 산화력이 요구치에 도달하지 못하고, 0.2%를 초과하는 경우에는 제조중 TiC를 형성하여 취화를 유발할 수 있고, 이로인해 단선율이 높아지기 때문이다.The content of Ti is preferably set to 0.1 to 0.2%. The reason is that when the content is less than 0.1%, the oxidizing power does not reach the required value. This can lead to an increase in disconnection rate.
상기와 같이 조성된 빌렛을 가열한 후 열간압연하는데, 상기 가열온도는 1000~1050℃의 범위로 설정하고, 상기 열간압연온도는 800~850℃의 범위로 설정하는 것이 바람직하다. 이와 같이 하면, 오스테나이트 입자를 미세화시켜 재결정에 의한 변태가 빨리 일어나도록 유도함으로써, 저온조직의 생성을 억제할 수 있는 효과가 크기 때문에, 신선성을 높일 수 있다.After heating the billet formed as described above and hot rolling, the heating temperature is preferably set in the range of 1000 ~ 1050 ℃, the hot rolling temperature is preferably set in the range of 800 ~ 850 ℃. By doing so, the austenite particles can be made finer to induce the transformation due to recrystallization to occur quickly, so that the effect of suppressing the formation of low-temperature tissues is great, thus improving the freshness.
특히, 압연온도를 800~850℃로 한 것은 본 발명강이 저온조직형성 가능성이 높은 Mn을 다량 함유하므로, 제어압연을 통해 저온조직의 생성을 최대한 억제하기 위함이다. 이에 따라, 소재의 직진성이 우수하여 치수정밀도를 높이고 코블 (Cobble) 등을 억제할수 있으며, 표면흠 및 스케일발생을 억제할 수 있는 효과를 얻을 수 있다.In particular, the rolling temperature is 800 ~ 850 ° C is because the steel of the present invention contains a large amount of Mn, which is likely to form a low-temperature structure, to suppress the formation of low-temperature structure as possible through controlled rolling. As a result, the straightness of the material is excellent, the dimensional accuracy can be increased, the Cobble can be suppressed, and the effect of suppressing the surface scratches and scale generation can be obtained.
그 후, 제조된 선재를 오스테나이트 단상역인 750℃이하의 온도까지 급냉한 후 그 온도에서 코일로 권취하고, 다시 650℃ 이하의 온도까지 서냉한 후, 상온까지는 공냉하는 것이 바람직하다. 이 때, 750℃ 이하의 온도까지 급냉하는 이유는, 미세한 오스테나이트 결정립을 유지하고, 저온조직의 발생가능성을 억제하기 위함이다.Thereafter, the prepared wire rod is quenched to a temperature of 750 ° C. or less, which is an austenite single phase region, and then wound up with a coil at that temperature, cooled slowly to a temperature of 650 ° C. or less, and then air cooled to room temperature. At this time, the reason for rapid quenching to a temperature of 750 ° C. or lower is to maintain fine austenite grains and to suppress the possibility of low temperature structure.
한편, 상기한 바와 같은 본 발명의 제조조건에 따르면 고속신선시에도 신선성이 우수한 미세 페라이트+퍼얼라이트 조직과 2%이하의 저온조직을 확보할 수 있게 된다.On the other hand, according to the manufacturing conditions of the present invention as described above it is possible to secure a fine ferrite + pearlite structure and excellent low-temperature structure of less than 2% even in high-speed wire.
이하, 실시예를 통하여 본 발명을 보다 구체적으로 설명한다.Hereinafter, the present invention will be described in more detail with reference to Examples.
(실시예 1)(Example 1)
하기 표1의 화학성분을 갖는 용강을 통상의 방법을 이용해 블룸(BLOOM)으로 만든 후 빌렛으로 제조하고, 1000~1050℃에서 1시간30분까지 가열후 800~850℃의 온도범위에서 고속압연하고, 그 후 물과 공기의 혼합분사에 의해 750℃까지 급속냉각하여 권취하고, 650℃이하까지 서냉한 후 상온까지 공냉하였다. 이와 같이 하여 제조된 5.5mm압연선재를 최종 직경이 1.2mm인 용접와이어로 다시 신선한후 동도금하였다.The molten steel having the chemical composition of the following Table 1 was made into a BLOOM using a conventional method, and then manufactured as a billet, heated at 1000 to 1050 ° C. for 1 hour and 30 minutes, and then rapidly rolled at a temperature range of 800 to 850 ° C. Thereafter, the mixture was rapidly cooled to 750 ° C by winding of a mixture of water and air, wound up, cooled slowly to 650 ° C or less, and then cooled to room temperature. 5.5 mm manufactured in this way The final diameter of the rolled wire is 1.2mm The copper plated with phosphorus welded wire was fresh again.
그 후, 상기 용접 와이어와 베이스메탈로 SS400을 이용하여 용접을 행한후, 용착부의 강도 및 충격인성을 측정하여, 그 결과를 하기 표2에 나타내었다.Thereafter, after welding was performed using SS400 with the welding wire and the base metal, the strength and impact toughness of the welded portion were measured, and the results are shown in Table 2 below.
이 때, 시헙방법은 JIS-Z2202이고, 시험기준은 AWS기준을 따랐다.At this time, the test method was JIS-Z2202, and the test standard followed the AWS standard.
상기 표1에 나타난 바와 같이, 본 발명성분으로 제조된 발명재(1)~(3)은 강도 및 충격치가 비교재 대비 동등이상의 수준을 확보함을 알 수 있다. 반면에, 비교재(1)은 강도는 우수하나, 충격특성이 열화하였다.As shown in Table 1, it can be seen that the inventive materials (1) to (3) made of the present invention components ensure that the strength and the impact value are equal to or higher than those of the comparative materials. On the other hand, the comparative material 1 was excellent in strength but deteriorated in impact characteristics.
(실시예 2)(Example 2)
실시예 1의 발명재(3)에 있어서, Zr의 함량을 하기 표2와 같이 변화시킨 것을 제외하고는 실시예1과 같이하여, 충격인성을 측정하고, 그 결과를 하기 표2에 나타내었다.In the inventive material (3) of Example 1, the impact toughness was measured in the same manner as in Example 1 except that the Zr content was changed as shown in Table 2 below, and the results are shown in Table 2 below.
상기 표2에 나타난 바와 같이, 본 발명범위를 만족하는 발명예(1)~(3)은 우수한 충격특성이 우수한 것을 알 수 있다. 그 이유는, Zr성분이 본 발명의 범위내에서 증가함에 따라 [O], [S], [N]등을 포집하고, 결정립성장을 억제하여 결정립을 미세화하기 때문이다.As shown in Table 2, Inventive Examples (1) to (3) satisfying the present invention can be seen that the excellent impact characteristics are excellent. This is because as the Zr component increases within the scope of the present invention, [O], [S], [N], etc. are collected, grain growth is suppressed and the grains are refined.
그러나, 그 함량이 많은 비교예(2)는, 탈산능의 증가로 인한 용접부 표면장력이 증가하고, 내부 기공이 미세화되어 방출되지 못하고 잔존하기 때문에 인성치가 떨어지는 문제가 있었다.However, Comparative Example (2) having a high content has a problem in that the surface tension of the welded portion due to the increase in the deoxidation capacity increases, and the toughness decreases because the internal pores become fine and are not released.
상기한 바와 같이, 본 발명은 강성분과 이에 맞는 최적의 제조조건을 적용함으로써, 제조된 용접 와이어의 용착부강도가 480N/m2이상이고, 충격치에 있어서도 현격히 개선된 고능율 중후판 용접재료를 제공할 수 있는 효과가 있는 것이다.As described above, the present invention provides a high-performance heavy plate welding material, which has a welded part strength of the manufactured welding wire of 480 N / m 2 or more and is significantly improved even at an impact value by applying a steel component and an optimum manufacturing condition according thereto. There is an effect that can be done.
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Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS57134514A (en) * | 1981-02-12 | 1982-08-19 | Kawasaki Steel Corp | Production of high-tensile steel of superior low- temperature toughness and weldability |
| JPS61113717A (en) * | 1984-11-09 | 1986-05-31 | Kawasaki Steel Corp | Manufacture of nontemper high tensile steel plate superior in weldability and low temperature toughness |
| JPH02213416A (en) * | 1989-02-14 | 1990-08-24 | Toa Steel Co Ltd | Production of steel bar with high ductility |
| JPH02305925A (en) * | 1989-05-20 | 1990-12-19 | Kobe Steel Ltd | Production of high-strength hot rolled steel sheet having excellent ductility |
| JPH0317244A (en) * | 1989-06-14 | 1991-01-25 | Kobe Steel Ltd | High strength hot rolled steel plate high having excellent workability and weldability and its manufacture |
| JPH1171636A (en) * | 1997-06-23 | 1999-03-16 | Kawasaki Steel Corp | High strength and high workability hot rolled steel sheet excellent in impact resistance and material uniformity and its production |
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Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS57134514A (en) * | 1981-02-12 | 1982-08-19 | Kawasaki Steel Corp | Production of high-tensile steel of superior low- temperature toughness and weldability |
| JPS61113717A (en) * | 1984-11-09 | 1986-05-31 | Kawasaki Steel Corp | Manufacture of nontemper high tensile steel plate superior in weldability and low temperature toughness |
| JPH02213416A (en) * | 1989-02-14 | 1990-08-24 | Toa Steel Co Ltd | Production of steel bar with high ductility |
| JPH02305925A (en) * | 1989-05-20 | 1990-12-19 | Kobe Steel Ltd | Production of high-strength hot rolled steel sheet having excellent ductility |
| JPH0317244A (en) * | 1989-06-14 | 1991-01-25 | Kobe Steel Ltd | High strength hot rolled steel plate high having excellent workability and weldability and its manufacture |
| JPH1171636A (en) * | 1997-06-23 | 1999-03-16 | Kawasaki Steel Corp | High strength and high workability hot rolled steel sheet excellent in impact resistance and material uniformity and its production |
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