KR100851158B1 - High Manganese High Strength Steel Sheets With Excellent Crashworthiness, And Method For Manufacturing Of It - Google Patents

High Manganese High Strength Steel Sheets With Excellent Crashworthiness, And Method For Manufacturing Of It Download PDF

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KR100851158B1
KR100851158B1 KR1020060135658A KR20060135658A KR100851158B1 KR 100851158 B1 KR100851158 B1 KR 100851158B1 KR 1020060135658 A KR1020060135658 A KR 1020060135658A KR 20060135658 A KR20060135658 A KR 20060135658A KR 100851158 B1 KR100851158 B1 KR 100851158B1
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steel sheet
hot
steel
rolling
cold
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KR1020060135658A
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Korean (ko)
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KR20080060982A (en
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김성규
진광근
손일령
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주식회사 포스코
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Priority to KR1020060135658A priority Critical patent/KR100851158B1/en
Priority to PCT/KR2007/006780 priority patent/WO2008078940A1/en
Priority to CNA2007800156253A priority patent/CN101432456A/en
Priority to US12/298,959 priority patent/US20090074605A1/en
Priority to JP2009523729A priority patent/JP5393459B2/en
Priority to EP07851742A priority patent/EP2097548A4/en
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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
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium

Abstract

연신율이 높아 가공성이 우수하고, 항복강도가 높아 충돌특성이 우수한 고가공성 고강도 강판과 그 제조방법이 제공된다. A high workability high strength steel sheet having high elongation and excellent workability and high yield strength and excellent impact characteristics is provided.

고망간 강판은, 중량%로 탄소 0.2 ~ 1.5%, 망간 10 ~ 25%, 알루미늄 0.01 ~ 3.0%, 인0.03% 이하, 황 0.03%이하, 질소 0.040%이하를 포함하고, 여기에 실리콘 0.02 ~ 2.5%, 티타늄 0.01 ~ 0.10%, 니오븀 0.01 ~ 0.10%의 그룹에서 선택되는 적어도 1종, 나머지 Fe 및 기타 불가피하게 함유되는 불순물로 조성되는 것이다. High manganese steel sheet contains 0.2 to 1.5% carbon, 10 to 25% manganese, 0.01 to 3.0% aluminum, 0.03% or less phosphorus, 0.03% or less sulfur, 0.040% or less nitrogen, and silicon 0.02 to 2.5 %, 0.01 to 0.10% titanium, 0.01 to 0.10% niobium, at least one selected from the group consisting of the remaining Fe and other inevitable impurities.

본 발명의 강판은 열연강판, 냉연강판 또는 도금강판일 수 있으며, 연신율이 높고, 가공경화지수가 높아 프레스가공성이 우수하여 차체의 구조부재 뿐 만아니라, 형상이 복잡한 내판재로도 적합하다. 또한, 강판의 특성중 충격 흡수능이 우수하기 때문에 자동차의 프론트 사이드　멤버(front　side　member) 등의 부품에 사용할 수　있다.The steel sheet of the present invention may be a hot rolled steel sheet, a cold rolled steel sheet or a plated steel sheet, and has a high elongation rate, a high work hardening index, and thus is excellent in press workability, and is suitable as a structural member of a vehicle body, as well as a complicated inner plate material. In addition, because of its excellent shock absorption ability, the steel sheet can be used for parts such as front side members of automobiles.

고강도, 고연성, 용융도금, 전기도금, TWIP, TWIN High strength, high ductility, hot dip plating, electroplating, TWIP, TWIN

Description

충돌특성이 우수한 고망간형 고강도 강판 및 그 제조방법{ High Manganese High Strength Steel Sheets With Excellent Crashworthiness, And Method For Manufacturing Of It}High Manganese High Strength Steel Sheets With Excellent Crashworthiness, And Method For Manufacturing Of It}

도 1은 미세조직 사진이다.1 is a microstructure photograph.

도 2는 냉간압연 양에 따른 인장곡선변화와 강도-연신율의 변화를 나타내는 그래프이다. 2 is a graph showing changes in tensile curve and strength-elongation according to the cold rolling amount.

일본 공개특허공보1992-259325, Japanese Laid-Open Patent Publication 1992-259325,

국제공개공보WO02/101109International Publication WO02 / 101109

본　발명은 자동차용 강판에 사용되는 고망간강 및 그 제조법에 관한 것이다. 보다　상세하게는, 연신율이 높아 가공성이 우수하고, 항복강도가 높아 충돌특성이 우 수한 고가공성 고강도 강판과 그 제조방법에 관한 것이다. The present invention relates to high manganese steel used in automotive steel sheets and a method of manufacturing the same. More specifically, the present invention relates to a high workability high strength steel sheet having high elongation and excellent workability and high yield strength and excellent impact characteristics and a method of manufacturing the same.

자동차사는 환경오염, 연비향상, 안전성 향상을 목적으로 경량 소재, 고강도 소재의 적용을 확대하고 있으며 이는 자동차 부품 외의 많은 구조부재에 적용되는 재료가 가져야 할 특성이기도 하다. 그러나 소재의 강도가 증가하면 연신율이 감소하는 특성을 가지며, 이를 극복하고자 성형성이 우수한 이상조직강과 변태유기소성강 등을 사용하고 있다. Automobile companies are expanding the application of lightweight materials and high-strength materials for the purpose of environmental pollution, fuel efficiency improvement and safety improvement. This is also a characteristic that materials applied to many structural members other than automobile parts. However, as the strength of the material increases, the elongation decreases, and in order to overcome this problem, ideal tissue steel and metamorphic organic plastic steel are used.

그러나, 현재까지 개발된 자동차 구조부재 및 내판재로 적용되는 가공용 고강도강은 자동차부품이 요구하는 가공성을 만족하지 못하기 때문에 복잡한 형상을 갖고 있는 부품은 제조하기 어렵다. 이를 해소하기 위하여, 자동차사는 부품의 형상을 간소화 하거나, 여러 개의 부품으로 구분하여 성형하고 다시 용접하는 공정을 이용하고 있다. 용접을 하는 경우, 용접부의 강도가 모재 부분과 다르기 때문에 차체의 설계에 많은 제약을 받을 뿐만 아니라, 용접부의 열위에 의한 부품특성 저하는 물론 부품을 나누어 성형하면서 공정비용이 크게 증가한다. 따라서 자동차사에서는 복잡한 형상의 부품에 적용하고 차체설계시 설계자유도를 높이기 위해서 고강도이면서도 가공성이 높은 재료를 지속적으로 요구하고 있다.However, the high-strength steel for processing applied to automobile structural members and inner plates developed to date do not satisfy the processability required by automotive parts, it is difficult to manufacture parts having a complicated shape. In order to solve this problem, automobile companies use a process of simplifying the shape of parts or forming and re-welding them into several parts. In the case of welding, since the strength of the weld is different from that of the base material, not only the design of the vehicle body is restricted, but also the deterioration of the part characteristics due to the inferiority of the weld, as well as the process cost greatly increase while dividing the parts. Therefore, in order to apply to complex-shaped parts and increase design freedom when designing a vehicle body, automobile companies continuously demand high strength and high processability materials.

자동차용 강판분야에서는 최근들어 연비향상과 대기오염을 줄이기 위해서 자동차의 무게를 줄일수 있는 성형성이 우수한 고강도강 강판이 요구되고 있는 실정이다. 종래의 자동차용 강판으로는 성형성을 고려하여 기지조직이 페라이트인 저탄소강 계열의 고강도강이 사용되고 있다. 그러나 자동차용 강판으로 저탄소강 계열의 고강도강을 사용하는 경우에는 인장강도가 800MPa급 이상에서는 연신율이 상업적으로 최고 30% 이상 확보하기가 어렵다. 따라서 800MPa급 이상 고강도강을 복잡한 형상의 부품에 적용하는 것은 어렵기 때문에 부품의 형상을 간략하게 하는 등 자유로운 부품설계가 어려운 실정이다. 상기와 같은 문제를 해결하기 위해서 연성과 강도가 우수한 오스테나이트계 고망간강(일본 공개특허공보1992-259325, 국제공개공보WO02/101109)이 제안된 바 있다. 그러나, 상기 일본특허는 고망간 첨가에 의해 연성은 확보 되나, 변형부에 가공경화가 심하게 일어나서 가공 후 강판이 쉽게 파단되는 현상이 있다. 또한, 상기 국제특허 역시 연성은 확보 되나, 다량의 실리콘 첨가에 의해서 전기도금성 및 용융도금성이 불리한 단점이 있다. 또한 상기의 강판들은 가공성은 우수하나 항복강도가 낮아 충돌특성이 열위한 단점이 있다. In the field of automotive steel sheets, high strength steel sheet having excellent formability to reduce the weight of automobiles is required in recent years to improve fuel efficiency and reduce air pollution. As a conventional steel sheet for automobiles, a low-carbon steel-based high strength steel having a base structure of ferrite is used in consideration of formability. However, in the case of using low carbon steel-based high-strength steel as an automotive steel sheet, it is difficult to secure commercial elongation of more than 30% at a tensile strength of 800 MPa or more. Therefore, it is difficult to apply a high-strength steel of 800 MPa or more to a complicated shape part, so it is difficult to design a free part such as simplifying the shape of the part. In order to solve the above problems, an austenitic high manganese steel (Japanese Laid-Open Patent Publication No. 1992-259325, WO02 / 101109) having excellent ductility and strength has been proposed. However, the Japanese patent, but the ductility is secured by the addition of high manganese, there is a phenomenon that the work hardening occurs in the deformed portion so that the steel sheet is easily broken after processing. In addition, the international patent is also ductility is secured, there is a disadvantage that the electroplating and hot-meltability by the addition of a large amount of silicon. In addition, the steel sheet is excellent in workability, but the yield strength is low, there is a disadvantage in that the collision characteristics are poor.

자동차소재로 사용되는 소재는 충돌시 충돌에너지를 흡수하고, 변형을 방지하고자 항복강도가 높은 경우 유리하다. 그러나 고망간강의 경우 오스테나이트 조직을 가짐으로써 항복강도가 낮은 특성을 보이므로 이를 극복하는 것이 필요하다. Materials used as automotive materials are advantageous when the yield strength is high to absorb collision energy during collision and to prevent deformation. However, high manganese steel has a low yield strength by having austenite structure, so it is necessary to overcome this problem.

본 발명은 연신율이 우수하여 가공성이 높고, 항복강도가 높아 충돌특성이 우수한 고가공성 고강도 강판과 그 제조방법을 제공하고자 하는 것이다. The present invention is to provide a high workability high strength steel sheet excellent in elongation and workability, high yield strength and excellent impact characteristics and a method of manufacturing the same.

상기 목적을 달성하기 위한 본 발명의 강판은, 중량%로 탄소 0.2 ~ 1.5%, 망간 10 ~ 25%, 알루미늄 0.01 ~ 3.0%, 인0.03% 이하, 황 0.03%이하, 질소 0.040%이하를 포함하고, 여기에 실리콘 0.02 ~ 2.5%, 티타늄 0.01 ~ 0.10%, 니오븀 0.01 ~ 0.10%의 그룹에서 선택되는 적어도 1종, 나머지 Fe 및 기타 불가피하게 함유되는 불순물로 조성된다. 본 발명의 강판은 오스테나이트 단상조직으로 되는 것이다.Steel sheet of the present invention for achieving the above object, by weight% contains carbon 0.2-1.5%, manganese 10-25%, aluminum 0.01-3.0%, phosphorus 0.03% or less, sulfur 0.03% or less, nitrogen 0.040% or less Here, the composition is composed of at least one selected from the group of 0.02 to 2.5% silicon, 0.01 to 0.10% titanium, 0.01 to 0.10% niobium, the remaining Fe and other inevitable impurities. The steel sheet of the present invention is an austenite single phase structure.

본 발명의 강판은 400-600MPa이상의 항복강도와 900-1000MPa이상의 인장강도를 갖으며, 냉간에서의 압연에 의한 가공경화에 의해 750MPa이상의 항복강도와 1000MPa이상의 인장강도를 갖게 된다. The steel sheet of the present invention has a yield strength of 400-600MPa or more and a tensile strength of 900-1000MPa or more, and has a yield strength of 750MPa or more and a tensile strength of 1000MPa or more by work hardening by cold rolling.

본 발명에서는 상기한 본 발명의 성분계를 갖는 강판을 냉간에서 10-80%의 압하율로 압연하는 것이다. 여기서, 압연은 조질압연, 이중압연, 열연정정압연의 어느 하나의 압연일 수 있다. 또한, 상기 강판은 열연강판, 냉연강판, 도금강판의 어느 하나에서 선택될 수 있다. In the present invention, the steel sheet having the component system of the present invention described above is rolled at a reduction ratio of 10-80% in cold. Here, the rolling may be any one of temper rolling, double rolling and hot rolling. In addition, the steel sheet may be selected from any one of hot rolled steel sheet, cold rolled steel sheet, plated steel sheet.

본 발명에서는 냉연강판을 제조하는 경우에는, 상기한 성분계를 갖는 강을 1050 ~ 1300oC에서 균질화 처리 후 850 ~ 1000℃의 마무리압연온도조건으로 열간압연하고, 700℃이하의 온도범위에서 권취한 다음, 30~80%의 압하율로 냉간압연하고, 600℃이상의 온도에서 연속소둔하여 제조할 수 있다. In the present invention, in the case of manufacturing a cold rolled steel sheet, the steel having the above-described component system is hot-rolled at a finish rolling temperature condition of 850 ~ 1000 ℃ after homogenizing treatment at 1050 ~ 1300 o C, wound in a temperature range of 700 ℃ or less Next, it can be manufactured by cold rolling at a reduction ratio of 30 to 80% and continuous annealing at a temperature of 600 ° C. or higher.

이하, 본 발명을 상세히 설명한다.Hereinafter, the present invention will be described in detail.

본 발명에서는 적절한 양의 실리콘, 티타늄, 니오븀의 적어도 1종을 첨가함으로써 항복강도를 증가하고자 하는 것이다. 제조된 열간압연, 냉간압연, 도금 강판을 이용하여 냉간에서 압연함으로써 항복강도가 높아 충돌특성이 우수한 강을 제조할 수 있다. In the present invention, it is intended to increase the yield strength by adding at least one of silicon, titanium and niobium in an appropriate amount. Cold rolling is performed using the manufactured hot rolled, cold rolled, and plated steel sheets to produce steel having high yield strength and excellent impact characteristics.

본 발명에서는 오스테나이트 단상을 얻고 쌍정에 의해 가공성을 향상하고자 망간, 탄소, 알루미늄의 첨가 양을 적절히 조절하면서 미세조직을 제어하여 항복강도를 증가시키기 위하여 실리콘, 티타늄, 니오븀의 첨가량을 최적화하는데, 특징이 있다. 또한, 쌍정에 의해 가공경화되는 경우 연신율이 아주 우수하므로 냉간가공에 의해 연신율이 다소 감소하더라도 자동차 부품에 필요한 성형성을 확보할 수 있다는 실험결과에 의해 냉간가공을 통해 항복강도를 증가하도록 하는 것이다. The present invention optimizes the addition amount of silicon, titanium and niobium to increase the yield strength by controlling the microstructure while appropriately adjusting the addition amount of manganese, carbon and aluminum to obtain austenite single phase and improve processability by twinning. There is this. In addition, since the elongation is very excellent when the process is hardened by twins, even if the elongation is slightly reduced by cold working, it is possible to increase the yield strength through the cold working by the experimental result that the moldability required for automobile parts can be secured.

본 발명은 상온에서 완전 오스테나이트상을 확보하기 위해서 오스테나이트 안정화원소인 망간과 탄소의 양을 최적화하고, 이들 성분에 의해 변형시 쌍정을 형성하도록 한다. 또한 알루미늄의 양을 조절하여 쌍정이 형성되는 속도를 제어하여 인장성질을 개선하는 것이다. 제조원가를 줄이기 위해 첨가되는 망간(Mn)의 첨가량을 최소화 하는 것이 중요하며, 망간양을 줄이기 위해서는 탄소를 일부 첨가하는 것이 중요하다. 강의 가공시 쌍정(TWIN)변형을 조장하기 위해서 역시 탄소, 알루미늄의 첨가량을 적절히 조절한다. 한편 항복강도를 증가시키기 위해서는 결정입도를 줄이는 것이 바람직하며, 이를 위해 실리콘, 티타늄, 니오븀 등의 적어도 1종을 첨가하는 것이다. The present invention optimizes the amount of manganese and carbon, which are austenite stabilizing elements, in order to secure a full austenite phase at room temperature, and forms twins when modified by these components. In addition, by controlling the amount of aluminum to control the rate of twin formation is to improve the tensile properties. It is important to minimize the amount of manganese (Mn) added to reduce the manufacturing cost, and it is important to add some carbon to reduce the amount of manganese. In order to promote twin deformation in steel processing, the addition amount of carbon and aluminum is appropriately adjusted. On the other hand, in order to increase the yield strength it is desirable to reduce the grain size, for this purpose is to add at least one of silicon, titanium, niobium and the like.

본 발명에서 강판은 열연강판, 냉연강판, 도금강판에 해당되는 것이다. In the present invention, the steel sheet corresponds to a hot rolled steel sheet, a cold rolled steel sheet, a plated steel sheet.

이하, 상기한 강 성분의 선정 및 성분범위의 한정 이유 등에 대하여 설명한다. Hereinafter, the selection of the above steel components, the reason for limitation of the component range, and the like will be described.

탄소(C)의 함량은 0.2-1.5%가 바람직하다.The content of carbon (C) is preferably 0.2-1.5%.

탄소는 오스테나이트상의 안정화에 기여하기 때문에 그 첨가량이 증가할수록 유리하다. 탄소의 첨가량이 0.2%미만에서는 변형시 α'(알파다시)-마르테사이트상이 생성되기 때문에 가공시 크랙이 발생하고, 연성이 낮아지는 단점이 있다. 그리고 탄소의 첨가량이 1.5%초과인 경우에는 오스테나이트상의 안정도가 크게 증가하여 슬립변형에 의한 변형거동의 천이로 가공성이 낮아진다. Since carbon contributes to stabilization of the austenite phase, it is advantageous as the amount added increases. If the amount of carbon added is less than 0.2%, cracks are generated during processing and ductility is lowered because α '(alpha) -marte cite phase is generated during deformation. When the amount of carbon added is more than 1.5%, the stability of the austenite phase is greatly increased, and the workability is lowered due to the transition of the deformation behavior due to slip deformation.

망간(Mn)의 함량은 10-30%, 보다 바람직하게는 10-25%로 하는 것이다. The content of manganese (Mn) is 10-30%, more preferably 10-25%.

망간 역시 오스테나이트상을 안정화시키는데 필수적인 원소이지만, 10%미만에서는 성형성을 해치는 α'(알파다시)-마르테사이트상이 생성되기 되어 강도는 증가하지만 연성이 급격히 감소한다. 그리고 망간의 첨가량이 30% 이상에서는 쌍정발생이 억제되어 강도는 증가하지만 연성이 감소한다. 그리고 망간의 첨가량이 증가할수록 열간압연 크랙발생이 잘 일어나고, 원료원가가 비싼 망간의 다량 첨가로 강판제조원가가 증가하기 때문에 바람직하게는 망간의 함량을 25%이하로 하는 것이다. Manganese is also an essential element for stabilizing the austenite phase, but below 10%, an alpha '(alpha) -marthecite phase is formed which impairs the formability, increasing the strength but decreasing the ductility drastically. And when the amount of manganese is added more than 30% twinning is suppressed to increase the strength but decrease the ductility. And as the amount of manganese is increased, hot rolling cracking is more likely to occur, and the steel sheet manufacturing cost is increased by the addition of a large amount of manganese, which is a raw material cost. Preferably, the content of manganese is 25% or less.

알루미늄(Al)의 함량은 0.01-3.0%가 바람직하다.The content of aluminum (Al) is preferably 0.01-3.0%.

알루미늄은 통상 강의 탈산을 위하여 첨가되지만 본 발명에서는 알루미늄이 연성향상을 위해서 첨가한다. 즉 알루미늄은 페라이트상의 안정화 원소이지만 강의 슬립면에서 적층결함에너지(stacking fault energy)를 증가시켜 ε-마르테사이트상의 생성을 억제하여 연성을 향상시킨다. 뿐만 아니라 알루미늄은 낮은 망간첨가량의 경우에도 ε-마르테사이트상의 생성을 억제하기 때문에 망간의 첨가량을 최소화 하고 가공성을 향상시키는데 큰 기여을 한다. 따라서, 그 첨가량이 0.01%미만인 경우에는 ε-마르텐사이트가 생성되어 강도는 증가하지만 연성이 급격히 감소한다. 그리고 그 첨가량이 3.0%를 초과하는 경우에는 쌍정발생을 억제하여 연성을 감소시 키고, 연속조조시 주조성을 나쁘게하고, 열간압연시 표면산화가 심하여 제품의 표면품질을 저하시키게 된다. Aluminum is usually added for deoxidation of steel, but in the present invention aluminum is added for ductility improvement. That is, aluminum is a stabilizing element of the ferrite phase, but the stacking fault energy (stacking fault energy) is increased in the slip surface of the steel to suppress the formation of the ε-martesite phase to improve the ductility. In addition, aluminum suppresses the formation of ε-martesite phase even in the case of low manganese addition, thus minimizing the amount of manganese added and improving processability. Therefore, when the addition amount is less than 0.01%, epsilon-martensite is produced and the strength increases but the ductility decreases rapidly. If the amount exceeds 3.0%, the twinning is suppressed to reduce the ductility, the castability is poor during continuous bathing, and the surface oxidation is severe during hot rolling, which lowers the surface quality of the product.

인(P)과 황(S)의 함량은 각각 0.03%이하로 하는 것이 바람직하다.The content of phosphorus (P) and sulfur (S) is preferably 0.03% or less, respectively.

인과 황은 강의 제조시 불가피하게 함유되는 원소이므로 그 첨가범위를 0.03%이하로 제한한다. 특히 인은 편석이 일어나서 강의 가공성을 감소시키고, 황은 조대한 망간황화물(MnS)을 형성하여 플렌지크랙과 같은 결함을 발생시키고, 강판의 국멍확장성을 감소시키므로 그 첨가량을 최대한 억제 하는 것이 바람직하다. Phosphorus and sulfur are elements that are inevitably contained in the production of steel, so the addition range is limited to 0.03% or less. In particular, phosphorus is segregated to reduce the workability of the steel, sulfur forms coarse manganese sulfide (MnS) to generate defects such as flange cracks, and it is preferable to suppress the addition amount as much as possible to reduce the expansion of the steel sheet.

질소(N)의 함량은 0.04%이하가 바람직하다.The content of nitrogen (N) is preferably 0.04% or less.

질소는 응고과정에서 알루미늄과 작용하여 오스테나이트 결정립내에서 미세한 질화물을 석출시켜 쌍정발생을 촉진하므로 강판의 성형시 강도와 연성을 향상시킨다. 그러나, 질소의 첨가량이 0.04%를 초과할 경우에는 질화물이 과다하게 석출되어 열간가공성 및 연신율이 저하된다. Nitrogen acts with aluminum during the solidification process to precipitate fine nitride in the austenite grains to promote twin generation, thus improving strength and ductility during forming of steel sheet. However, when the addition amount of nitrogen exceeds 0.04%, nitrides are excessively precipitated, resulting in a decrease in hot workability and elongation.

상기와 같이 조성되는 강에 실리콘, 티타늄, 니오븀의 그룹에서 선택된 적어도 1종이 포함된다. At least one selected from the group consisting of silicon, titanium, and niobium is included in the steel formed as described above.

실리콘(Si)의 함량은 0.02-2.5%가 바람직하다. The content of silicon (Si) is preferably 0.02-2.5%.

실리콘은 고용강화되는 원소로 고용효과에 의해 결정립도를 줄임으로써 항복강도를 증가시키는 원소이다. 통상 과다하게 첨가될 경우 표면에 실리콘 산화층을 형성하여 용융도금성을 떨어뜨리는 것을 알려져 있다. 그러나 망간이 다량 첨가된 강에서는 적절한 양의 실리콘이 첨가될 경우 표면에 얇은 실리콘산화층이 형성되어 망간의 산화를 억제하기 때문에 냉연강판에서 압연 후 형성되는 두꺼운 망간 산화층이 형성되는 것을 방지할 수 있고, 소둔 후 냉연강판에서 진행되는 부식을 방지하여 표면품질을 향상시키고, 전기도금재의 소지강판으로써 우수한 표면품질을 유지할 수 있다. 그러나 실리콘의 첨가량이 증가하면 열간압연을 할 때 강판표면에 실리콘 산화물이 형성되어 산세성을 나쁘게 하여 열연강판의 표면품질을 나쁘게 하는 단점이 있다. 그리고 그리고 실리콘은 연속소둔공정과 연속용융도금공정에서 고온 소둔시 강판표면에 농화되어 용융도금을 할 때 강판표면에 용융아연의 젖음성을 감소시키기 때문에 도금성을 감소시키다. 뿐만 아니라 다량의 실리콘 첨가는 강의 용접성을 크게 저하시킨다. 따라서 실리콘의 상한 첨가량은 2.5%가 바람직하다. 충돌특성은 도금층의 부식성과 달리 내부 금속기지층의 기계적 특성과 관련되며, 도금위한 열처리 조건이 오스테나이트 단상조직을 가지는 고망간강의 기계적 특성에 영향을 미치지 않으므로 본 제품은 도금제품의 충돌특성을 포함한다. Silicon is an element that enhances the yield strength by reducing the grain size by the solid solution effect. In general, when excessively added, it is known to form a silicon oxide layer on the surface to lower the melt plating property. However, in the steel with a large amount of manganese, when a suitable amount of silicon is added, a thin silicon oxide layer is formed on the surface to suppress the oxidation of manganese, thereby preventing the formation of a thick manganese oxide layer formed after rolling on a cold rolled steel sheet. After annealing to prevent the corrosion of the cold rolled steel to improve the surface quality, it is possible to maintain the excellent surface quality as a steel plate of the electroplating material. However, when the amount of silicon is increased, silicon oxide is formed on the surface of the steel sheet during hot rolling, so that the pickling property is deteriorated, thereby deteriorating the surface quality of the hot rolled steel sheet. In addition, silicon is concentrated on the surface of the steel sheet during high temperature annealing in the continuous annealing process and the continuous hot dip plating process, thereby reducing the wettability of the molten zinc on the surface of the steel sheet. In addition, the addition of large amounts of silicon greatly reduces the weldability of the steel. Therefore, the upper limit of the amount of addition of silicon is preferably 2.5%. The impact properties are related to the mechanical properties of the inner metal base layer, unlike the corrosiveness of the plated layer, and this product includes the impact properties of the plated products because the heat treatment conditions for plating do not affect the mechanical properties of the high manganese steel with austenitic single-phase structure. .

티타늄(Ti)의 함량은 0.01-0.1%가 바람직하다.The content of titanium (Ti) is preferably 0.01-0.1%.

티타늄은 탄소와 결합하여 탄화물을 형성하는 강탄화물 형성 원소로, 이때 형성 된 탄화물은 결정입 성장을 막아 결정입도 미세화에 효과적인 원소이다. 그러나 티타늄의 함량이 0.005%미만으로 미량 첨가하는 경우 효과가 없고, 0.10%를 초과하면 과량의 티타늄이 결정입계에 편석하여 입계취화를 일으키거나, 석출상이 과도하게 조대화되어 결정입 성장 효과를 떨어뜨릴 수 있다. Titanium is a strong carbide-forming element that combines with carbon to form carbides, and the carbide formed is an effective element to reduce grain size by preventing grain growth. However, it is ineffective when the trace amount of titanium is added less than 0.005%, and when it exceeds 0.10%, the excess titanium segregates at the grain boundaries, causing grain embrittlement or excessively coarsening of the precipitate phase, thereby decreasing the grain growth effect. Can be dropped.

니오븀(Nb)의 함량은 0.005-0.1%, 보다 바람직하게는 0.01-0.1%로 하는 것이다. The content of niobium (Nb) is 0.005-0.1%, more preferably 0.01-0.1%.

니오븀은 티타늄과 같은 형태로 탄소와 결합하여 탄화물을 형성하는 강탄화물 형성원소이다. 역시 이때 형성된 탄화물은 결정입 성장을 막아 결정입도 미세화에 효과적인 원소이며 통상의 티타늄 보다 낮은 온도에서 석출상을 형성하므로 결정입도 미세화와 석출상 형성에 의한 석출강화효과가 큰 원소이다. 그러나, 0.005% 미만으로 미량 첨가하는 경우 효과가 없고, 0.10%를 초과하면 과량의 니오븀이 결정입계에 편석하여 입계취를 일으키거나, 석출상이 과도하게 조대화되어 결정입 성장 효과를 떨어뜨릴 수 있다. 바람직한 니오븀의 첨가량은 0.01-0.1%로 하는 것이다. Niobium is a strong carbide forming element that combines with carbon to form carbides in the same form as titanium. Also, the carbide formed at this time is an element effective in miniaturizing grain size by preventing grain growth and forming a precipitated phase at a temperature lower than that of ordinary titanium, and thus, an element having a large precipitation strengthening effect due to the refinement of grain size and formation of a precipitated phase. However, when the trace amount is added less than 0.005%, it is ineffective, and when it exceeds 0.10%, excess niobium may segregate at the grain boundary and cause grain boundary odor or excessively coarse precipitated phase may degrade the grain growth effect. . Preferable amount of niobium is 0.01-0.1%.

이하, 고망간강의 제조방법에 대해 설명한다.Hereinafter, the manufacturing method of high manganese steel is demonstrated.

일반적으로 고망간강 열연강판의 제조는 일반강의 제조공정과 마찬가지로 연속주조법을 이용할 수 있다. 상기 조성으로 가을 통상의 조건과 유사하게 균질화 처리를 실시한 다음에 마무리압연하고 권취하여 열연강판을 제조한다. In general, the production of high-manganese steel hot rolled steel sheet can be used in the continuous casting method as in the manufacturing process of ordinary steel. The composition is subjected to a homogenization treatment similar to the usual conditions for autumn, followed by finishing rolling and winding to produce a hot rolled steel sheet.

본 발명에서 열간압연시 고망간강의 연주슬라브 가열온도를 1050 ~ 1300 oC 하는 것이 바람직하다. 가열온도의 상한을 1300℃로 한정한 이유는 온도가 높을수록 결정입도가 증가하고, 표면산화가 발생하여 강도가 감소하거나, 표면이 열위되는 특성을 보이기 때문이다. 또한, 1300℃초과하여 가열하면 연주슬라브의 주상정입계에 액상막이 생기므로 열간압연시 균열이 발생하기도 한다. 한편 가열온도의 하한을 1050℃으로 한정한 이유는 가열온도가 낮게 되면 마무리 압연시 온도 확보가 어려워 온도감소에 의해 압연하중이 증가하여 소정의 두께까지 충분히 압연을 할 수 없기 때문이다. 즉 통상의 마무리 압연온도는 열연공정에서 최소 850oC이상, 바람직하게는 900oC 정도 이므로 마무리 압연온도를 낮추게 되면 압연하중이 높아져서 압연기에 무리가 갈 뿐만 아니라 강판내부의 품질에도 나쁜 영향을 미치게 된다. 그리고 압연 마무리 온도를 과도하게 높게 하는 경우 압연시 표면 산화가 발생하므로 압연마무리 온도는 1000℃로 제한한다.In the present invention, the hot slab heating slab heating temperature of hot manganese is preferably 1050 ~ 1300 ° C. The upper limit of the heating temperature is limited to 1300 ° C because the crystal grain size increases with higher temperature, surface oxidation occurs, the strength decreases, or the surface is inferior. In addition, when it is heated above 1300 ° C., a liquid film is formed at the columnar grain boundary of the slab, which may cause cracks during hot rolling. On the other hand, the lower limit of the heating temperature is limited to 1050 ° C., because when the heating temperature is low, it is difficult to secure the temperature during finish rolling, and the rolling load increases due to the temperature decrease, and thus the rolling cannot be sufficiently rolled to a predetermined thickness. That is, the normal finish rolling temperature is at least 850 o C, preferably 900 o C, in the hot rolling process, so lowering the finish rolling temperature increases the rolling load, which not only makes the rolling mill difficult but also adversely affects the quality of the steel sheet. do. And when the rolling finish temperature is excessively high, since surface oxidation occurs during rolling, the rolling finish temperature is limited to 1000 ℃.

열연권취온도는 700℃이하에서 행하는 것이다. 권취온도가 700℃ 초과되면 열연강판표면에 두꺼운 산화막과 내부산화가 일어나기 때문에 산세과정에서 산화층이 쉽게 제거되지 않는다. 따라서 열연강판의 권취온도는 낮게 하는 것이 바람직하다. Hot-rolled coiling temperature is performed at 700 degrees C or less. If the coiling temperature exceeds 700 ℃, the oxide layer is not easily removed during pickling because a thick oxide film and internal oxidation occur on the surface of the hot rolled steel sheet. Therefore, the coiling temperature of the hot rolled steel sheet is preferably lowered.

상기에서 얻어진 열연강판은 필요에 따라 냉연강판으로 제조한다.The hot rolled steel sheet obtained above is manufactured from a cold rolled steel sheet as needed.

냉연강판은 강판 형상과 두께를 맞추기 위해서 냉간압연하여 얻어지는데, 바람 직한 냉간압연은 30-80%의 압하율로 행하는 것이다.The cold rolled steel sheet is obtained by cold rolling in order to match the shape of the steel sheet and the thickness. Preferably, cold rolling is performed at a reduction ratio of 30-80%.

냉간압연강판은 600oC이상에서 연속소둔한다. 이때 소둔온도가 너무 낮으면 충분한 가공성을 확보하기 어렵고 저온에서 오스테나이트상을 유지할 수 있을 만큼 오스테나이트로의 변태가 충분히 일어나지 않기 때문에 소둔온도를 600oC 이상으로 하는 것이다. 본 발명에서는 상변태가 일어나지 않는 오스테나이트강이기 때문에 재결정온도 이상으로 가열하면 충분히 가공성을 확보할 수 있기 때문에 통상의 소둔조건으로 소둔을 실시하여 제조한다. Cold rolled steel sheets are continuously annealed at temperatures above 600 ° C. At this time, if the annealing temperature is too low, it is difficult to secure sufficient processability and the annealing temperature is set to 600 ° C. or more because transformation to austenite does not occur sufficiently to maintain the austenite phase at low temperatures. In the present invention, since it is an austenitic steel which does not cause phase transformation, when it is heated above the recrystallization temperature, the workability can be sufficiently secured.

상기에서 얻어진 소둔재를 필요에 따라 도금하는데, 도금은 용융도금, 전기도금, 증착도금등의 방법을 선택할 수 있으며, 바람직하게는 용융도금하는 것이다. 도금강판은 냉연강판을 이용하여 600℃이상에서 연속소둔을 실시하고 용융도금, 전기도금, 증착도금 강판을 제조하는 것으로 구성되어 있다. 통상 전기도금 공정이나 용융도금 공정시의 열처리조건은 일반 변태조직강의 경우에 영향을 미치나, 본 발명강은 오스테나이트 단상을 가지며 변태가 없어 기계적 특성에 큰 차이가 발생되지 않으므로 통상의 조건에서 도금을 실시한다.Although the annealing material obtained above is plated as needed, plating can be selected from a method such as hot-dip plating, electroplating, vapor deposition plating, and the like, and preferably hot-dip plating. The plated steel sheet is formed by performing continuous annealing at 600 ° C. or higher using a cold rolled steel sheet and manufacturing a hot-dip galvanized, electroplated, or deposited plated steel sheet. In general, the heat treatment conditions in the electroplating process or the hot dip process affect the general transformation tissue steel, but the steel of the present invention has austenite single phase and there is no transformation so that no big difference in the mechanical properties occurs. Conduct.

본 발명에서는 상기한 본 발명의 성분을 만족하는 고망간강 예를 들어 열연강 판, 냉연강판, 도금강판의 어느 하나를 냉간에서 10 ~ 80%의 압하율로 다시 압연하여 항복강도를 높게 할 수 있다. 여기서 압연은 제철소에서 사용하는 조질압연, 이중압연, 열연정정 공정의 어느 하나를 이용하여 행할 수 있다. In the present invention, high-manganese steel that satisfies the above-described components of the present invention, for example, hot rolled steel sheet, cold rolled steel sheet, or any one of the plated steel sheet can be rolled again in cold rolling at a reduction ratio of 10 to 80% to increase the yield strength. . The rolling can be performed using any one of temper rolling, double rolling, and hot rolling process used in steel mills.

이하의 실시 예를 통하여 본 발명을 상세히 설명한다.The present invention will be described in detail through the following examples.

[실시예]EXAMPLE

표 1은 본 발명강과 비교강의 화학성분을 나타낸 것으로 용해된 강의 강괴를 1200oC가열로에서 한시간 유지 후 열간압연을 실시하였다. 이때 열간압연 마무리 온도는 900oC, 권취온도는 650oC로 하였다. 열간압연강판 중 일부는 JIS5호 규격으로 인장시편을 가공한후 만능인장시험기를 이용하여 인장시험을 실시하였다. 그리고 열간압연을 한 강판을 이용하여 산세를 실시하고 냉간압하율을 50%로 하여 냉간압연을 실시 하였다. 냉간압연된 시편을 소둔온도를 800oC로 하고 과시효 온도를 400oC로 하여 연속소둔 모사 열처리를 실시하였다. 연속소둔 모사 열처리 후 만능인장시험기를 이용하여 인장시험을 실시하였다. 한편 냉간압연 시편을 소둔온도 800oC로 하고 용융아연욕을460oC로 하여 용융아연도금 모사 시험을 실시하였다.Table 1 shows the chemical composition of the present invention steel and comparative steel, and the hot-rolled after the steel ingot maintained for 1 hour in a 1200 ° C heating furnace. At this time, the hot rolling finish temperature was 900 ° C, the winding temperature was 650 ° C. Some of the hot rolled steel sheets were subjected to tensile tests using a universal tensile tester after processing tensile specimens according to JIS5 standard. Pickling was performed using a hot rolled steel sheet, followed by cold rolling with a cold reduction rate of 50%. Cold-rolled specimens were subjected to continuous annealing simulation heat treatment with an annealing temperature of 800 o C and an overaging temperature of 400 o C. Tensile tests were performed using a universal tensile tester after continuous annealing simulation heat treatment. On the other hand, hot-rolled specimens were subjected to a hot dip galvanizing simulation test with an annealing temperature of 800 o C and a hot dip zinc bath of 460 o C.

구분division CC MnMn PP SS AlAl SiSi NbNb TiTi NN 비고Remarks 1One 0.150.15 2.52.5 0.0100.010 0.0060.006 0.050.05 0.500.50 0.0260.026 0.0060.006 비교강Comparative steel 22 0.100.10 6.06.0 0.0100.010 0.0100.010 0.040.04 0.500.50 0.0060.006 비교강Comparative steel 33 0.450.45 12.012.0 0.0100.010 0.0110.011 1.481.48 0.010.01 0.0060.006 비교강Comparative steel 44 0.440.44 14.814.8 0.0120.012 0.0090.009 1.401.40 0.010.01 0.0060.006 비교강Comparative steel 55 0.430.43 15.015.0 0.0090.009 0.0050.005 0.050.05 0.010.01 0.0060.006 비교강Comparative steel 66 0.150.15 15.015.0 0.0100.010 0.0050.005 1.501.50 0.010.01 0.0060.006 비교강Comparative steel 77 0.600.60 15.115.1 0.0090.009 0.0080.008 1.361.36 2.502.50 0.0060.006 발명강Invention steel 88 0.600.60 15.215.2 0.0080.008 0.0050.005 1.501.50 0.010.01 0.0060.006 비교강Comparative steel 99 0.600.60 24.024.0 0.0050.005 0.0060.006 0.050.05 0.0060.006 비교강Comparative steel 1010 0.59 0.59 18.818.8 0.0100.010 0.0040.004 1.641.64 0.490.49 0.0060.006 발명강Invention steel 1111 0.62 0.62 17.917.9 0.0100.010 0.0090.009 1.601.60 0.0460.046 0.0060.006 발명강Invention steel 1212 0.62 0.62 18.218.2 0.0100.010 0.0080.008 1.601.60 0.0760.076 0.0060.006 발명강Invention steel 1313 0.62 0.62 18.218.2 0.0100.010 0.0090.009 1.571.57 0.0380.038 0.0060.006 발명강Invention steel 1414 0.62 0.62 18.618.6 0.0100.010 0.0090.009 1.611.61 0.0060.006 비교강Comparative steel 1515 0.63 0.63 18.2 18.2 0.012 0.012 0.010 0.010 0.0060.006 비교강Comparative steel 1616 0.66 0.66 19.219.2 0.0100.010 0.0080.008 1.661.66 0.0260.026 0.0060.006 발명강Invention steel 1717 0.61 0.61 18.118.1 0.0100.010 0.0090.009 1.511.51 0.50.5 0.030.03 1818 0.63 0.63 18.318.3 0.0100.010 0.0090.009 1.521.52 0.50.5 0.050.05 1919 0.60 0.60 17.517.5 0.0210.021 0.0020.002 1.421.42 0.0050.005 0.0060.006 비교강Comparative steel

구분division 열연강판Hot rolled steel 냉연/도금강판Cold Rolled / Plated Steel Sheets 구분division YSYS TSTS T-ElT-El YSYS TSTS T-ElT-El 1One 545545 646646 23.723.7 520520 800800 2323 비교강Comparative steel 22 818818 12481248 88 -- -- 　-- 비교강Comparative steel 33 403403 837837 40.540.5 339339 678678 40.340.3 비교강Comparative steel 44 435435 875875 66.766.7 341341 862862 63.263.2 비교강Comparative steel 55 374374 922922 32.832.8 373373 978978 3737 비교강Comparative steel 66 374374 991991 4949 377377 10191019 52.552.5 비교강Comparative steel 77 567567 979979 5454 514514 994994 66.966.9 발명강Invention steel 88 391391 893893 68.768.7 399399 894894 62.962.9 비교강Comparative steel 99 353353 772772 25.825.8 -- -- 　-- 비교강Comparative steel 1010 609609 899899 45.345.3 448448 873873 6363 발명강Invention steel 1111 587587 947947 55.555.5 521 521 974 974 66.9 66.9 발명강Invention steel 1212 557557 943943 59.459.4 531 531 969 969 55.3 55.3 발명강Invention steel 1313 452452 902902 70.170.1 482 482 952 952 63.6 63.6 발명강Invention steel 1414 418418 887887 68.368.3 445 445 932 932 66.5 66.5 비교강Comparative steel 1515 349.4 349.4 963.5 963.5 41.8 41.8 -- -- 　-- 비교강Comparative steel 1616 560560 947947 54.754.7 492 492 967 967 63.4 63.4 발명강Invention steel 1717 502502 924.1924.1 61.961.9 발명강Invention steel 1818 534534 965.7965.7 54.854.8 발명강Invention steel 1919 471.3471.3 939.9939.9 60.460.4 -- -- -　- 비교강Comparative steel

표 2는 본 발명강과 비교강의 제조조건에 따른 기계적성질의 변화를 나타낸 것이다. 비고에 발명강이라고 표시된 본 발명강은 열연강판 및 연속소둔열처리 모사시험을 한 후 인장시험결과 인장강도 700MPa이상, 연신율 40% 이상, 항복강도 500MPa이상의 재질을 나타내었으며, 자동차 멤버, 필라와 같은 구조부재용 재료로서 적절한 재질을 확보하였다.Table 2 shows the change in mechanical properties according to the manufacturing conditions of the inventive steel and comparative steel. Remarks Invention steel marked invention steel shows the material of tensile strength over 700MPa, elongation over 40%, yield strength over 500MPa after hot-rolled steel sheet and continuous annealing simulation test. An appropriate material was secured as a material for reuse.

시료번호 1,2번 강은 망간의 첨가량이 적어 충분한 강도와 연성을 확보할 수 없다.Steel No. 1 and 2 can not secure sufficient strength and ductility due to the small amount of manganese added.

시료번호 3~6, 8~9, 14~15, 19 강은 탄소, 망간, 실리콘, 알루미늄의 첨가 양이 접합하지 않아 연신율이 낮거나, 항복강도가 500MPa이하로 낮아 구조부재로 적당하지 않다. Sample Nos. 3 to 6, 8 to 9, 14 to 15, 19 The steel is not suitable for structural members because the added amount of carbon, manganese, silicon and aluminum is not bonded, so the elongation is low or the yield strength is lower than 500 MPa.

시료번호 7, 10~13, 16~18 강은 탄소, 망간, 알루미늄의 첨가 양이 적당하고, 실리콘, 티타늄, 니오븀의 첨가로 바람직한 항복강도를 가져 구조부재에 적합한 재질을 가진다. Sample Nos. 7, 10 to 13 and 16 to 18 steels are suitable for the structural member due to the appropriate amount of carbon, manganese, and aluminum added, and the desired yield strength by addition of silicon, titanium, and niobium.

[실시예 2]Example 2

실시예1로부터 얻어진 오스테나이트 단상조직을 가지는 고가공성 고망간형 고강도 강판을 다시 냉간압연하는 경우에 대한 기계적성질을 측정하고 그 결과를 표 3에 나타내었다. The mechanical properties of the case of cold rolling a high process high manganese high strength steel sheet having an austenitic single phase structure obtained in Example 1 were measured and the results are shown in Table 3.

구분division YSYS TSTS T-ElT-El 압연양Rolling amount 구분division 1919 471.3471.3 939.9939.9 60.460.4 00 비교강Comparative steel 19-119-1 750.5750.5 1047.21047.2 44.644.6 1010 발명강Invention steel 19-219-2 930.5930.5 1209.71209.7 22.222.2 2020 발명강Invention steel 19-319-3 1088.31088.3 1371.31371.3 12.512.5 3030 발명강Invention steel 19-419-4 1247.71247.7 1554.21554.2 8.68.6 4040 발명강Invention steel 19-519-5 1388.21388.2 1704.11704.1 6.86.8 5050 발명강Invention steel 19-619-6 1503.61503.6 1808.61808.6 4.64.6 6060 발명강Invention steel 19-719-7 1612.81612.8 1924.51924.5 2.82.8 7070 발명강Invention steel 19-819-8 1776.61776.6 2012.52012.5 1.81.8 8080 발명강Invention steel

표 3에 나타난 바와 같이, 항복강도가 증가하는 것을 보여준다. 통산 10%의 변형에서도 항복강도가 750MPa 이상으로 크게 증가하였으며, 연신율은 44%의 우수한 결과를 나타내어 구조부재로서의 성형성과 충돌특성을 가지는 것을 알 수 있다.As shown in Table 3, the yield strength is shown to increase. Yield strength was greatly increased to over 750MPa even in 10% of total deformation, and elongation was 44%, which shows excellent formability and impact characteristics as structural member.

본 발명에서 상기 실시형태는 하나의 예시로서, 본 발명이 여기에 한정되는 것은 아니다. 본 발명의 특허청구범위에 기재된 기술적 사상과 실질적으로 동일한 구성을 갖고 동일한 작용효과를 이루는 것은 어떠한 것이어도 본 발명의 기술적 범위에 포함된다. 따라서, 당해 기술분야의 통상의 지식을 가진 자가 본 발명의 특허청구범위에 기재된 본 발명의 기술사상을 벗어나지 않는 범위 내에서 다양한 형태의 치환, 변형, 변경이 가능할 것이며, 이러한 것들은 본 발명의 범위에 속한다고 할 것이다. In the present invention, the above embodiment is only one example, and the present invention is not limited thereto. Anything that has substantially the same configuration as the technical idea described in the claims of the present invention and achieves the same operation and effect is included in the technical scope of the present invention. Accordingly, various forms of substitution, modification, and alteration may be made within the scope of the present invention by those skilled in the art without departing from the technical spirit of the present invention described in the claims of the present invention. Will belong.

상술한 바와 같이, 본 발명에 따르면, 연신율이 높고, 고강도여서 차체의 구조부재 뿐 만아니라, 형상이 복잡한 내판재로도 적합한 강판이 제공된다. 이 강판은 강판의 특성 중 충격 흡수능이 우수하기 때문에 자동차의 프론트 사이드　멤버(front　side　member) 등의 부품에 사용할 수　있는 유용한 효과가 있다.As described above, according to the present invention, a steel sheet having a high elongation and high strength is suitable not only for the structural member of the vehicle body but also for a complicated inner plate member. Since the steel sheet has excellent impact absorption ability among the characteristics of the steel sheet, there is a useful effect that can be used for parts such as the front side member of the vehicle.

Claims (7)

중량%로 탄소 0.2 ~ 1.5%, 망간 10 ~ 25%, 알루미늄 0.01 ~ 3.0%, 인 0.03% 이하, 황 0.03%이하, 질소 0.040%이하를 포함하고, 여기에 실리콘 0.02 ~ 2.5%, 티타늄 0.01 ~ 0.10%, 니오븀 0.01 ~ 0.10%의 그룹에서 선택되는 적어도 1종, 나머지 Fe 및 기타 불가피하게 함유되는 불순물로 조성되며,% By weight, carbon 0.2-1.5%, manganese 10-25%, aluminum 0.01-3.0%, phosphorus 0.03% or less, sulfur 0.03% or less, nitrogen 0.040% or less, including silicon 0.02-2.5%, titanium 0.01- 0.10%, niobium 0.01 to 0.10% of at least one selected from the group, the remaining Fe and other inevitable impurities are contained, 미세조직은 오스테나이트 단상조직임을 특징으로 하는 충돌특성이 우수한 고망간형 고강도 강판.Microstructure is a high manganese high strength steel sheet with excellent collision characteristics, characterized in that the austenitic single-phase structure. 삭제delete 제 1항에 있어서, 상기 강판은 600~609MPa의 항복강도와 900~965.7MPa의 인장강도를 가지는 것을 특징으로 하는 충돌특성이 우수한 고망간형 고강도 강판.The high manganese high strength steel sheet having excellent collision characteristics according to claim 1, wherein the steel sheet has a yield strength of 600 to 609 MPa and a tensile strength of 900 to 965.7 MPa. 청구항 1의 조성을 가지며, 아래의 (a), (b), (c) 및 (d)의 공정, The process of (a), (b), (c) and (d) below having the composition of claim 1, (a) 강슬라브를 1050 ~ 1300℃에서 균질화처리 후 850 ~ 1000℃의 마무리압연온도조건으로 열간압연하고, 700℃이하의 온도범위에서 권취하여 열연강판을 얻는 공정; (a) hot-rolling the steel slab under homogenization treatment at 1050 to 1300 ° C. and hot rolling at a finish rolling temperature of 850 to 1000 ° C. and winding the steel slab at a temperature range of 700 ° C. or less to obtain a hot rolled steel sheet; (b) 강슬라브를 1050 ~ 1300℃에서 균질화처리 후 850 ~ 1000℃의 마무리압연온도조건으로 열간압연하고, 700℃이하의 온도범위에서 권취하여 얻어진 열연강판을 30~80%의 압하율로 냉간압연하고, 냉간강판은 600℃이상의 온도에서 연속소둔하여 냉연강판을 얻는 공정; (b) After homogenizing the steel slab at 1050 ~ 1300 ℃, hot rolled the steel slab at the finish rolling temperature condition of 850 ~ 1000 ℃, and winding the hot rolled steel sheet obtained by winding in the temperature range below 700 ℃ with cold reduction rate of 30 ~ 80%. Rolling and cold-rolled steel sheet continuously annealing at a temperature of 600 ° C. or higher to obtain a cold-rolled steel sheet; (c) 강슬라브를 1050 ~ 1300℃에서 균질화처리 후 850 ~ 1000℃의 마무리압연온도조건으로 열간압연하고, 700℃이하의 온도범위에서 권취하여 얻어진 열연강판을 용융도금, 전기도금, 증착도금에서 선택되는 방법으로 도금하여 도금강판을 얻는 공정; 및(c) The steel slab is homogenized at 1050 ~ 1300 ℃ and hot rolled under the finish rolling temperature condition of 850 ~ 1000 ℃, and the hot rolled steel sheet obtained by winding in the temperature range below 700 ℃ in hot dip galvanizing, electroplating, deposition plating Plating to obtain a plated steel sheet by a selected method; And (d) 강슬라브를 1050 ~ 1300℃에서 균질화처리 후 850 ~ 1000℃의 마무리압연온도조건으로 열간압연하고, 700℃이하의 온도범위에서 권취하여 얻어진 열연강판을 30~80%의 압하율로 냉간압연하고, 냉간강판은 600℃이상의 온도에서 연속소둔하여 냉연강판에 대하여 용융도금, 전기도금, 증착도금에서 선택되는 방법으로 도금하여 도금강판을 얻는 공정;(d) Hot-rolled steel sheet obtained by homogenizing the steel slab at 1050 ~ 1300 ℃ and hot rolling at the finish rolling temperature condition of 850 ~ 1000 ℃, and winding it in the temperature range of 700 ℃ or less at cold rate of 30 ~ 80% Rolling, cold-rolled steel sheet is continuously annealed at a temperature of 600 ° C. or higher to obtain a plated steel sheet by plating the cold-rolled steel sheet by a method selected from hot dip plating, electroplating, and deposition plating; 중 하나의 공정에 의해 얻어지는 강판에 대하여, About the steel plate obtained by one of the steps, 냉간에서 10-80%의 압하율로 압연하는 것을 특징으로 하는 충돌특성이 우수한 고망간형 고강도 강판의 제조방법.A method for producing a high manganese high strength steel sheet having excellent impact characteristics, characterized by rolling at a reduction ratio of 10-80% in cold. 삭제delete 삭제delete 삭제delete
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