WO2017111473A1 - High manganese steel sheet having excellent vibration-proof property, and manufacturing method therefor - Google Patents

High manganese steel sheet having excellent vibration-proof property, and manufacturing method therefor Download PDF

Info

Publication number
WO2017111473A1
WO2017111473A1 PCT/KR2016/015040 KR2016015040W WO2017111473A1 WO 2017111473 A1 WO2017111473 A1 WO 2017111473A1 KR 2016015040 W KR2016015040 W KR 2016015040W WO 2017111473 A1 WO2017111473 A1 WO 2017111473A1
Authority
WO
WIPO (PCT)
Prior art keywords
steel sheet
less
heat treatment
austenite
manufacturing
Prior art date
Application number
PCT/KR2016/015040
Other languages
French (fr)
Korean (ko)
Inventor
조원태
김태호
진광근
김영하
송태진
Original Assignee
주식회사 포스코
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by 주식회사 포스코 filed Critical 주식회사 포스코
Priority to JP2018532710A priority Critical patent/JP2019504208A/en
Priority to EP16879340.4A priority patent/EP3395978B1/en
Priority to CN201680075456.1A priority patent/CN108474082B/en
Priority to US16/061,134 priority patent/US20180371586A1/en
Publication of WO2017111473A1 publication Critical patent/WO2017111473A1/en

Links

Images

Classifications

    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • 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
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to a high Mn steel sheet having excellent dustproof characteristics that can be used where a dustproof characteristic for noise reduction is made by using steel sheets for automobiles or construction.
  • High Mn anti-vibration steel is a steel grade that has high dustproof and excellent mechanical properties by converting noise energy into thermal energy due to interfacial sliding of epsilon martensite during external impact and is suitable for this purpose.
  • An object of the present invention is to provide a high Mn steel sheet excellent in dustproof characteristics and a method of manufacturing the same.
  • One preferred aspect of the present invention is by weight, C: 0 ⁇ 0.1%, Mn: 8 ⁇ 30%, P: 0.1% or less, S: 0.02% or less, N: 0.1% or less, Ti 0 ⁇ 1.0% and
  • the present invention relates to a high Mn steel sheet having excellent anti-vibration characteristics including Fe and unavoidable impurities and consisting of epsilon martensite and austenite, and having an average particle diameter of martensite and austenite of 2 ⁇ m or less.
  • another preferred aspect of the present invention comprises the steps of heating a steel sheet satisfying the composition range to a heat treatment temperature of Ac1 ⁇ Ac3 + 50 °C at a temperature increase rate of 0.01 ⁇ 200 °C / s; Maintaining at the heat treatment temperature for 0.01 seconds to 24 hours; And it relates to a high Mn steel sheet manufacturing method having excellent dustproof characteristics including the step of cooling to room temperature at a cooling rate of 0.01 °C / s or more.
  • the present invention can provide a high Mn steel sheet having excellent dustproof characteristics, the present invention can be utilized in structural parts for automobiles and flooring materials for buildings that require noise reduction.
  • Example 1 is a view showing the microstructure of the Example heat-treated at 600 °C and Comparative Example heat-treated at 700 ⁇ 1000 °C.
  • FIG. 2 is a diagram illustrating a dilator cycle of the heat treatment shown in FIG. 1.
  • the present invention is by weight, C: 0 ⁇ 0.1% or less, Mn: 8 ⁇ 30%, P: 0.1% or less (including 0%), S: 0.02% or less (including 0%), N: 0.1% or less ( 0%), Ti: 1.0% or less (excluding 0) and Fe and inevitable impurities, and the microstructure is composed of epsilon martensite and austenite, and the average particle diameter of martensite and austenite is 2 ⁇ m or less
  • the excellent high Mn steel sheet and its manufacturing method are related.
  • Mn is an essential element to stably secure the austenite structure, and increases the lamination defect energy. At less than 8%, Mn forms martensite that impairs formability, thereby increasing strength but rapidly decreasing ductility. In addition, the partially formed austenite is easily converted into epsilon martensite due to a decrease in stacking defect energy, and the lower limit thereof is limited to 8%. On the other hand, when the amount of Mn added exceeds 30%, the slag cracks are caused by the increase in the manufacturing cost and the increase in the phosphorus content (P) due to the large amount of manganese.
  • the internal grain boundary oxidation occurs excessively when the slab is reheated to cause oxide defects on the surface of the steel sheet, and the surface properties are also inferior in hot dip galvanizing to limit the upper limit of the amount of Mn to 30%.
  • Phosphorus (P) and sulfur (S) are inevitably contained in the manufacture of steel, so the content of phosphorus (P) is 0.1% or less (including 0%) and sulfur (S) is 0.02% or less (including 0%). It is desirable to limit.
  • phosphorus segregates to reduce the machinability of steel, sulfur forms coarse manganese sulfide (MnS), which causes defects such as flange cracks, and reduces the expansion of steel sheet, so the amount of addition should be restrained as much as possible.
  • Nitrogen (N) is an element that is inevitably contained in the production, it is preferable to limit the addition range to 0.1% or less (including 0%).
  • Titanium (Ti) is a strong carbide forming element that combines with carbon to form carbide, and the carbide formed at this time is an element effective in miniaturizing grain size by preventing grain growth.
  • the carbide formed at this time is an element effective in miniaturizing grain size by preventing grain growth.
  • boron and the compound is added, high temperature compounds are formed at columnar grain boundaries to prevent grain boundary cracks.
  • it has a scavenging effect of forming a compound with C and N to reduce the fraction thereof, and thus is an essential element for improving dustproof performance.
  • excess titanium is segregated at grain boundaries to cause grain boundary odors, or precipitate phases are excessively coarsened to lower grain growth effects. Therefore, the amount of titanium added is limited to 1.0% or less.
  • High Mn steel according to another aspect of the present invention is additionally in weight percent Si: 0-3%, Cr: 0.005% -5.0%, Ni: 0.005-2.0%, Nb: 0.005-0.5%, B: 0.0001-0.01 %, V: 0.005 to 0.5%, and W: 0.005 to 1%.
  • Silicon (Si) is an element that enhances the yield strength by reducing the grain size due to the solid solution effect.
  • silicon oxide is formed on the surface of the steel sheet during hot rolling, which deteriorates pickling and deteriorates the surface quality of the steel sheet.
  • the addition of large amounts of silicon greatly reduces the weldability of the steel. Therefore, the upper limit of the silicon addition amount can be limited to 3%.
  • Cr reacts with external oxygen during hot rolling or annealing operation, whereby Cr-based oxide film (Cr 2 O 3 ) having a thickness of 20-50 ⁇ m is preferentially formed and Mn, Si, etc. contained in steel are eluted to the surface layer. It can contribute to the stabilization of the surface structure by preventing it can act as an element to improve the surface properties of the plating.
  • the upper limit of the content may be limited to 5.0% because chromium carbide is formed to lower the processability and delayed fracture resistance.
  • Ni is an element that contributes to stabilization of austenite and is advantageous not only for improving elongation but also for contributing to high temperature ductility above all.
  • Ni which is a strong high temperature toughness enhancing element, has a very small effect on high temperature toughness when its content is less than 0.005%, and it shows a great effect on preventing delayed fracture and slab cracking as the added content increases, but it increases the production cost due to high material cost.
  • the content can be limited to 0.005 ⁇ 2.0%.
  • Nb is a carbide-forming element which bonds with carbon in steel to form carbide, and can be added in the present invention for the purpose of increasing strength and minimizing particle size.
  • the precipitated phase is formed at a temperature lower than Ti, 0.005 to 0.5% may be added as an element having a large crystallization size and a precipitation strengthening effect due to the precipitated phase formation.
  • the effect of the addition amount of less than 0.005% is insignificant, whereas if it is added more than 0.5%, excessive Nb segregates in the grain boundary, causing grain boundary embrittlement, or excessively coarsening of the precipitate phase, thereby reducing the effect of grain growth.
  • the recrystallization is delayed to increase the rolling load, so the amount of Nb added may be limited to 0.005 to 0.5%.
  • V and W are elements that form carbonitrides by combining with C and N, such as Ti, and thus, form fine precipitated phases at low temperatures, and thus may have a precipitation strengthening effect and may be important elements for securing austenite.
  • C and N such as Ti
  • V and W are elements that form carbonitrides by combining with C and N, such as Ti, and thus, form fine precipitated phases at low temperatures, and thus may have a precipitation strengthening effect and may be important elements for securing austenite.
  • both components are added in a small amount of less than 0.005%, the effect is insignificant, whereas if V is more than 0.5% and W is more than 1.0%, the precipitated phase is excessively coarsened, which lowers the grain growth effect and causes hot brittleness.
  • the addition amount can be limited to V 0.005 to 0.5% and W 0.005 to 1%.
  • Boron (B) may be added together with Ti to form a high temperature compound of grain boundaries to prevent grain boundary cracks.
  • B Boron
  • the steel having the above components and component ranges and having a microstructure composed of austenite columnar phases is heated at a heating rate of 0.01 to 200 ° C / s to 0.01 at a heat treatment temperature of Ac1 to Ac3 + 50 ° C. After holding for 24 seconds to cool down to room temperature at a cooling rate of 0.01 °C / s or more.
  • the high Mn steel sheet may be a cold rolled steel sheet or a hot rolled steel sheet.
  • the microstructure of the high Mn steel sheet is composed of epsilon martensite and austenite.
  • the heating step exceeds 200 ° C / s Ac1 and Ac3 temperature is up, even if the heat treatment in the range of the present invention has a problem that the average particle diameter of the microstructure exceeds 2 ⁇ m, the upper limit of the temperature increase rate is limited to 200 ° C / s do.
  • coarse carbides may be formed due to phase instability and should be heat treated at a rate of 0.01 °C / s or more.
  • the heat treatment temperature is Ac1 ⁇ Ac3 + 50 It is limited to ° C.
  • the average particle diameter of the microstructure during cooling, as well as coarse carbides may occur due to phase instability, so the lower limit of the cooling rate is 0.01 °C / s It is limited. There is no upper limit to the cooling rate, and the faster it is, the more favorable it is to secure epsilon martensite and to secure a fine average particle size.
  • the embodiment heat-treated at 600 °C according to the present invention can be seen that the average particle diameter of the microstructure is 2 ⁇ m or less.
  • FIG. 2 is a diagram illustrating a dilator cycle of the heat treatment shown in FIG. 1.
  • FIG. 2 the embodiment shows the result of heat treatment at Ac3 + 30 ° C.
  • SDC is the damping ability (the property that the object absorbs vibration).
  • the room temperature SDC value of the anti-vibration steel having a microstructure according to the embodiment heat-treated at 600 ° C has a value 2.5 times higher than the anti-vibration steel according to Comparative Example (4). That is, the SDC value of the Example heat-treated at 600 ° C was 0.00025, and the SDC value of Comparative Example (4) heat-treated at 1000 ° C was measured as 0.0001.
  • the epsilon martensite area fraction of the embodiment heat-treated at 600 ° C. is relatively low, but the particle size is small, the structure is fine and uniformly distributed so that the residual dislocation and the interface are energized when an external impact is applied with the epsilon martensite.
  • the dustproof property is excellent because it contributes to the improvement of damping performance by increasing the ratio of converting to heat energy.
  • the room temperature SDC value is 0.00015 or more, it can be said that the dustproof property is excellent.
  • the epsilon martensite area fraction is higher than that of the example, but the dustproof performance is inferior because the average particle diameter of the microstructure is large.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

The present invention relates to a high Mn steel sheet and a manufacturing method therefor, the steel sheet comprising, by wt%: 0-0.1% or less of C; 8-30% of Mn; 0.1% or less of P; 0.02% or less of S; 0.1% or less of N; 0-1.0% of Ti; and Fe and inevitable impurities, wherein a microstructure has epsilon martensite and austenite, and the average particle diameter of the martensite and the austenite is 2 μm or less.

Description

방진특성이 우수한 고망간 강판 및 그 제조방법High manganese steel sheet with excellent dustproof properties and manufacturing method
본 발명은 자동차용 또는 건축용 강판으로 제조되어 소음 저감을 위한 방진 특성이 필요한 곳에 사용될 수 있는 방진특성이 우수한 고Mn강판에 관한 것이다.The present invention relates to a high Mn steel sheet having excellent dustproof characteristics that can be used where a dustproof characteristic for noise reduction is made by using steel sheets for automobiles or construction.
최근 자동차 제조 및 건축 자재에 있어서 소음 저감은 제조업체들이 반드시 해결해야 하는 이슈다. 자동차 제조업체의 경우, 크게 소음이 발생하는 엔진부, 오일펜등의 구성품에 우수한 기계적 특성과 함께 방진특성이 특히 요구된다. 건축자재의 경우 최근 층간 소음 규제의 강화로 인해 아파트를 포함한 복층건물의 바닥판으로서 방진강판의 개발이 요청된다. Recently, noise reduction in automobile manufacturing and building materials is an issue that manufacturers must solve. In the case of automobile manufacturers, particularly dustproof engine parts, oil pens and other components, such as excellent mechanical properties and dustproof characteristics are particularly required. In the case of building materials, due to the recent tightening of the noise regulation between floors, the development of anti-vibration steel plates is required as the floor plates of multi-story buildings including apartments.
고Mn 방진강은 외부 충격시 입실론 마르텐사이트의 계면 슬라이딩으로 인해 소음에너지를 열에너지로 전환되어 높은 방진특성 및 우수한 기계적 성질을 가지고 있는 강종으로 이와 같은 목적에 사용하기 적합하다. High Mn anti-vibration steel is a steel grade that has high dustproof and excellent mechanical properties by converting noise energy into thermal energy due to interfacial sliding of epsilon martensite during external impact and is suitable for this purpose.
본 발명은 방진특성이 우수한 고Mn강판 및 그 제조방법을 제공하는 것을 그 목적으로 한다.An object of the present invention is to provide a high Mn steel sheet excellent in dustproof characteristics and a method of manufacturing the same.
본 발명의 바람직한 일 측면은 중량%로, C : 0~0.1%이하, Mn : 8~30%, P : 0.1%이하, S : 0.02%이하, N : 0.1%이하, Ti 0~1.0% 및 Fe와 불가피한 불순물을 포함하고, 미세조직은 입실론 마르텐사이트와 오스테나이트로 이루어지고, 마르텐사이트와 오스테나이트의 평균 입경이 2μm이하인 방진특성이 우수한 고Mn강판에 관한 것이다.One preferred aspect of the present invention is by weight, C: 0 ~ 0.1%, Mn: 8 ~ 30%, P: 0.1% or less, S: 0.02% or less, N: 0.1% or less, Ti 0 ~ 1.0% and The present invention relates to a high Mn steel sheet having excellent anti-vibration characteristics including Fe and unavoidable impurities and consisting of epsilon martensite and austenite, and having an average particle diameter of martensite and austenite of 2 μm or less.
또한, 본 발명의 바람직한 다른 일 측면은 상기 조성범위를 만족하는 강판을 0.01~200℃/s의 승온속도로 Ac1~Ac3+50℃의 열처리 온도까지 가열하는 단계; 상기 열처리 온도에서 0.01초~24시간동안 유지하는 단계; 및 0.01℃/s 이상의 냉각속도로 상온까지 냉각하는 단계를 포함하는 방진특성이 우수한 고Mn강판의 제조방법에 관한 것이다.In addition, another preferred aspect of the present invention comprises the steps of heating a steel sheet satisfying the composition range to a heat treatment temperature of Ac1 ~ Ac3 + 50 ℃ at a temperature increase rate of 0.01 ~ 200 ℃ / s; Maintaining at the heat treatment temperature for 0.01 seconds to 24 hours; And it relates to a high Mn steel sheet manufacturing method having excellent dustproof characteristics including the step of cooling to room temperature at a cooling rate of 0.01 ℃ / s or more.
본 발명은 방진특성이 우수한 고Mn강판을 제공할 수 있으므로, 소음제거가 필요한 자동차용 구조부품 및 건축자재 바닥재 등에 활용될 수 있다. Since the present invention can provide a high Mn steel sheet having excellent dustproof characteristics, the present invention can be utilized in structural parts for automobiles and flooring materials for buildings that require noise reduction.
도 1은 600℃에서 열처리한 실시예와 700~1000℃에서 열처리한 비교예의 미세조직을 나타내는 도면이다. 1 is a view showing the microstructure of the Example heat-treated at 600 ℃ and Comparative Example heat-treated at 700 ~ 1000 ℃.
도 2는 도 1에 제시 된 열처리의 딜라토미터 사이클을 나타낸 도면이다.FIG. 2 is a diagram illustrating a dilator cycle of the heat treatment shown in FIG. 1.
도 3은 실시예 및 비교예(4) 대하여 내부 저항법으로 측정한 SDC(Specific Damping Capacity)결과를 나타내는 그래프이다.3 is a graph showing the results of the specific damping capacity (SDC) measured by the internal resistance method for the Example and Comparative Example (4).
이하, 본 발명에 대해 상세히 설명한다.Hereinafter, the present invention will be described in detail.
본 발명은 중량%로, C : 0~0.1%이하, Mn : 8~30%, P : 0.1%이하(0% 포함), S : 0.02%이하(0% 포함), N : 0.1%이하(0% 포함), Ti: 1.0%이하(0은 제외) 및 Fe와 불가피한 불순물을 포함하고, 미세조직은 입실론 마르텐사이트와 오스테나이트로 이루어지고, 마르텐사이트와 오스테나이트의 평균 입경이 2μm이하인 방진특성이 우수한 고Mn강판 및 그 제조방법에 관한 것이다.The present invention is by weight, C: 0 ~ 0.1% or less, Mn: 8 ~ 30%, P: 0.1% or less (including 0%), S: 0.02% or less (including 0%), N: 0.1% or less ( 0%), Ti: 1.0% or less (excluding 0) and Fe and inevitable impurities, and the microstructure is composed of epsilon martensite and austenite, and the average particle diameter of martensite and austenite is 2 μm or less The excellent high Mn steel sheet and its manufacturing method are related.
본원발명에 따른 강판의 구체적인 강 조성 및 그 성분 제한사유는 아래와 같다.Specific steel composition of the steel sheet according to the present invention and the reasons for the restriction thereof are as follows.
C은 그 첨가량이 0.1%를 초과할 경우에는 탄화물이 과다하게 석출되어 열간가공성 및 연신율을 저하시키고, 방진능이 크게 감소하여 첨가량을 0.1% 이하로 제한한다. When the amount of C exceeds 0.1%, carbides are excessively precipitated to lower the hot workability and elongation, and the anti-vibration ability is greatly reduced to limit the amount to 0.1% or less.
Mn은 오스테나이트 조직을 안정하게 확보하는데 필수적인 원소이며, 적층결함 에너지를 높이는 원소로, 8% 미만에서는 성형성을 해치는 마르테사이트가 형성되어 강도는 증가하지만 연성이 급격히 감소한다. 그리고 적층결함 에너지가 저하하여 일부 형성된 오스테나이트도 입실론 마르텐사이트로 변태하기 용이하여 하한은 8%로 제한한다. 반면, Mn의 첨가량이 30%를 초과하는 경우에는 다량 망간에 의한 제조비용 증가와 강중 인(P)함량 증가로 슬라브 균열의 원인이 된다. 또한 Mn의 첨가량이 증가할수록 슬라브 재가열시 내부 입계산화가 지나치게 일어나 강판 표면에 산화물 결함을 유발시키고 용융아연 도금시 표면 특성도 열위하여 Mn 첨가량의 상한을 30%로 한정한다.Mn is an essential element to stably secure the austenite structure, and increases the lamination defect energy. At less than 8%, Mn forms martensite that impairs formability, thereby increasing strength but rapidly decreasing ductility. In addition, the partially formed austenite is easily converted into epsilon martensite due to a decrease in stacking defect energy, and the lower limit thereof is limited to 8%. On the other hand, when the amount of Mn added exceeds 30%, the slag cracks are caused by the increase in the manufacturing cost and the increase in the phosphorus content (P) due to the large amount of manganese. In addition, as the amount of Mn is increased, the internal grain boundary oxidation occurs excessively when the slab is reheated to cause oxide defects on the surface of the steel sheet, and the surface properties are also inferior in hot dip galvanizing to limit the upper limit of the amount of Mn to 30%.
인(P)과 황(S)은 강의 제조 시 불가피하게 함유되는 원소이므로 그 함량은 인 (P)는 0.1% 이하(0% 포함), 황 (S)는 0.02% 이하(0% 포함)로 제한하는 것이 바람직하다. 특히 인은 편석이 일어나서 강의 가공성을 감소시키고, 황은 조대한 망간황화물(MnS)을 형성하여 플렌지크랙과 같은 결함을 발생시키고, 강판의 국멍확장성을 감소시키므로 그 첨가량을 최대한 억제 하여야 한다. Phosphorus (P) and sulfur (S) are inevitably contained in the manufacture of steel, so the content of phosphorus (P) is 0.1% or less (including 0%) and sulfur (S) is 0.02% or less (including 0%). It is desirable to limit. In particular, phosphorus segregates to reduce the machinability of steel, sulfur forms coarse manganese sulfide (MnS), which causes defects such as flange cracks, and reduces the expansion of steel sheet, so the amount of addition should be restrained as much as possible.
질소(N)는 제조 시 불가피하게 함유되는 원소이므로 그 첨가범위를 0.1% 이하(0% 포함)로 제한하는 것이 바람직하다.Nitrogen (N) is an element that is inevitably contained in the production, it is preferable to limit the addition range to 0.1% or less (including 0%).
티타늄(Ti)은 탄소와 결합하여 탄화물을 형성하는 강탄화물 형성원소로, 이때 형성된 탄화물은 결정입 성장을 막아 결정입도 미세화에 효과적인 원소이다. 그리고 보론과 복합첨가되는 경우 주상정 입계에서 고온 화합물을 형성하여 입계 크랙을 방지한다. 또한, C, N과 화합물을 형성하여 이들의 분율을 떨어뜨리는 스케빈징 (Scavenging) 효과를 가지고 있어 방진능 향상에 꼭 필요한 원소이다. 그러나 1.00%를 초과하면 과량의 티타늄이 결정입계에 편석하여 입계취를 일으키거나, 석출상이 과도하게 조대화되어 결정입 성장 효과를 떨어뜨리므로 티타늄의 첨가량은 1.0%이하로 한정한다.Titanium (Ti) is a strong carbide forming element that combines with carbon to form carbide, and the carbide formed at this time is an element effective in miniaturizing grain size by preventing grain growth. In addition, when boron and the compound is added, high temperature compounds are formed at columnar grain boundaries to prevent grain boundary cracks. In addition, it has a scavenging effect of forming a compound with C and N to reduce the fraction thereof, and thus is an essential element for improving dustproof performance. However, when 1.00% is exceeded, excess titanium is segregated at grain boundaries to cause grain boundary odors, or precipitate phases are excessively coarsened to lower grain growth effects. Therefore, the amount of titanium added is limited to 1.0% or less.
본 발명의 다른 일측면에 따른 고Mn강은 추가적으로 중량%로 Si: 0~3%, Cr: 0.005%~5.0%, Ni: 0.005~2.0%, Nb: 0.005~0.5%, B: 0.0001~0.01%, V: 0.005~0.5% 및 W: 0.005~1% 중의 1종 또는 2종 이상을 포함할 수 있다.High Mn steel according to another aspect of the present invention is additionally in weight percent Si: 0-3%, Cr: 0.005% -5.0%, Ni: 0.005-2.0%, Nb: 0.005-0.5%, B: 0.0001-0.01 %, V: 0.005 to 0.5%, and W: 0.005 to 1%.
실리콘(Si)은 고용강화되는 원소로 고용효과에 의해 결정립도를 줄임으로써 항복강도를 증가시키는 원소로 강도 확보를 위해 필요하다. 그러나 실리콘의 첨가량이 증가하면 열간압연을 할 때 강판표면에 실리콘 산화물이 형성되어 산세성을 악화하여 강판의 표면품질을 악화하는 단점이 있다. 뿐만 아니라 다량의 실리콘 첨가는 강의 용접성을 크게 저하시킨다. 따라서 실리콘 첨가량의 상한은 3%로 제한할 수 있다.Silicon (Si) is an element that enhances the yield strength by reducing the grain size due to the solid solution effect. However, when the amount of silicon is increased, silicon oxide is formed on the surface of the steel sheet during hot rolling, which deteriorates pickling and deteriorates the surface quality 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 silicon addition amount can be limited to 3%.
Cr은 열연 혹은 소둔 조업시 외부 산소와 반응하여 강판 표면에 20~50㎛의 두께의 Cr계 산화막(Cr2O3)이 우선적으로 형성하여 강중에 포함된 Mn, Si등이 표층으로 용출되는 것을 방지하여 표층 조직의 안정화에 기여할 수 있고 도금표면특성을 향상시키는 원소로 작용할 수 있다. Cr reacts with external oxygen during hot rolling or annealing operation, whereby Cr-based oxide film (Cr 2 O 3 ) having a thickness of 20-50 μm is preferentially formed and Mn, Si, etc. contained in steel are eluted to the surface layer. It can contribute to the stabilization of the surface structure by preventing it can act as an element to improve the surface properties of the plating.
그러나 0.005% 미만에서는 상기 효과가 미미하며 5.0% 초과시 크롬 탄화물을 형성하여 가공성과 내지연파괴 특성을 저하시키므로 그 함량의 상한은 5.0%로 제한할 수 있다.However, if the content is less than 0.005%, the effect is insignificant, and if it exceeds 5.0%, the upper limit of the content may be limited to 5.0% because chromium carbide is formed to lower the processability and delayed fracture resistance.
Ni은 오스테나이트 안정화에 기여하여 연신율의 향상에 유리할 뿐만 아니라, 무엇보다도 고온연성에 효과적으로 기여할 수 있는 원소이다. 강력한 고온인성 향상원소인 Ni은 그 함량이 0.005%미만의 경우 고온인성에 대한 효과가 매우 미미하며 첨가함량이 증가할수록 내지연파괴 및 슬라브크랙 방지에도 큰 효과가 나타나지만 재료원가가 높아 생산비를 높이므로 그 함량은 0.005~2.0%로 제한할 수 있다.Ni is an element that contributes to stabilization of austenite and is advantageous not only for improving elongation but also for contributing to high temperature ductility above all. Ni, which is a strong high temperature toughness enhancing element, has a very small effect on high temperature toughness when its content is less than 0.005%, and it shows a great effect on preventing delayed fracture and slab cracking as the added content increases, but it increases the production cost due to high material cost. The content can be limited to 0.005 ~ 2.0%.
Nb은 강중 탄소와 결합하여 탄화물을 형성하는 탄화물 형성 원소로서 본 발명에서는 강도 상승과 입도미세화를 목적으로 첨가할 수 있다. 통상적으로 Ti보다 낮은 온도에서 석출상을 형성하므로 결정립 크기의 미세화와 석출상 형성에 의한 석출 강화 효과가 큰 원소로서 0.005~0.5%를 첨가할 수 있다. 그러나 0.005% 미만의 첨가량에서는 그 효과가 미미하고, 반면 0.5%를 초과하여 첨가하면 과량의 Nb이 결정립계에 편석하여 입계 취화를 일으키거나, 석출상이 과도하게 조대화되어 결정립의 성장 효과를 떨어뜨리고, 열간압연 공정에서 재결정을 지연시켜 압연하중을 증가시키기 때문에 Nb의 첨가량은 0.005~0.5%로 한정할 수 있다.Nb is a carbide-forming element which bonds with carbon in steel to form carbide, and can be added in the present invention for the purpose of increasing strength and minimizing particle size. In general, since the precipitated phase is formed at a temperature lower than Ti, 0.005 to 0.5% may be added as an element having a large crystallization size and a precipitation strengthening effect due to the precipitated phase formation. However, the effect of the addition amount of less than 0.005% is insignificant, whereas if it is added more than 0.5%, excessive Nb segregates in the grain boundary, causing grain boundary embrittlement, or excessively coarsening of the precipitate phase, thereby reducing the effect of grain growth. In the hot rolling process, the recrystallization is delayed to increase the rolling load, so the amount of Nb added may be limited to 0.005 to 0.5%.
V과 W은 Ti과 같이 C,N와 결합하여 탄질화물을 형성하는 원소로서 본 발명에서는 저온에서 미세한 석출상을 형성하므로 석출강화 효과가 있을 수 있고, 오스테나이트 확보에 중요한 원소일 수 있다. 그러나, 두 성분 모두 0.005% 미만으로 미량 첨가하는 경우 효과가 미미하고, 반면 V은 0.5%, W은 1.0% 초과하면 석출상이 과도하게 조대화되어 결정립 성장 효과를 떨어뜨리고 열간취성의 원인이 되기 때문에 그 첨가량을 V 0.005~0.5%, W 0.005~1% 로 한정할 수 있다.V and W are elements that form carbonitrides by combining with C and N, such as Ti, and thus, form fine precipitated phases at low temperatures, and thus may have a precipitation strengthening effect and may be important elements for securing austenite. However, if both components are added in a small amount of less than 0.005%, the effect is insignificant, whereas if V is more than 0.5% and W is more than 1.0%, the precipitated phase is excessively coarsened, which lowers the grain growth effect and causes hot brittleness. The addition amount can be limited to V 0.005 to 0.5% and W 0.005 to 1%.
보론(B)은 Ti와 같이 첨가되어 입계의 고온 화합물을 형성하여 입계 크랙을 방지할 수 있다. 그러나 0.0001% 이하로 미량 첨가하는 경우 효과가 없고, 0. 01%를 초과하면 보론 화합물을 형성하여 표면특성을 악화 시키므로 그 범위를 0.0001~0.01%로 한정할 수 있다.Boron (B) may be added together with Ti to form a high temperature compound of grain boundaries to prevent grain boundary cracks. However, when added in a small amount of 0.0001% or less, it is ineffective, and if it exceeds 0.01%, the boron compound is formed to deteriorate the surface properties, so the range may be limited to 0.0001 to 0.01%.
이하, 본 발명의 방진특성이 우수한 고Mn강판의 제조방법에 대하여 설명한다.Hereinafter, the manufacturing method of the high Mn steel sheet excellent in the dustproof characteristic of this invention is demonstrated.
본 발명 고Mn강판의 제조방법에서는 상기 성분 및 성분범위를 갖고, 미세조직이 오스테나이트 주상으로 구성된 강을 0.01~200℃/s의 승온속도로 가열하여 Ac1~Ac3+50℃의 열처리 온도에서 0.01초~24시간 동안 유지한 후 0.01℃/s이상의 냉각속도로 상온까지 냉각한다.In the method for producing a high Mn steel sheet of the present invention, the steel having the above components and component ranges and having a microstructure composed of austenite columnar phases is heated at a heating rate of 0.01 to 200 ° C / s to 0.01 at a heat treatment temperature of Ac1 to Ac3 + 50 ° C. After holding for 24 seconds to cool down to room temperature at a cooling rate of 0.01 ℃ / s or more.
상기 고Mn강판은 냉간압연강판 또는 열간압연강판일 수 있다.The high Mn steel sheet may be a cold rolled steel sheet or a hot rolled steel sheet.
상기 고Mn강판의 미세조직은 입실론 마르텐사이트와 오스테나이트로 이루어진다.The microstructure of the high Mn steel sheet is composed of epsilon martensite and austenite.
상기 가열단계에서 200℃/s를 초과하면 Ac1 및 Ac3 온도가 상향되어 본 발명 조건 범위에서 열처리를 하여도 미세조직의 평균입경이 2μm 초과하는 문제점이 있으므로 승온속도의 상한은 200℃/s로 한정한다. 승온속도 0.01℃/s 이하 조업시 상 불안정에 의해 조대 탄화물이 생길 수 있어 0.01℃/s 이상의 속도로 열처리 되어야 한다 If the heating step exceeds 200 ° C / s Ac1 and Ac3 temperature is up, even if the heat treatment in the range of the present invention has a problem that the average particle diameter of the microstructure exceeds 2μm, the upper limit of the temperature increase rate is limited to 200 ° C / s do. When operating at temperature below 0.01 ℃ / s, coarse carbides may be formed due to phase instability and should be heat treated at a rate of 0.01 ℃ / s or more.
상기 열처리를 Ac1 미만으로 수행하면 변태가 진행되지 않아 열처리 효과가 나타나지 않는 문제점이 있고, Ac3+50℃를 초과하면, 미세조직의 평균입경이 2um 초과하는 문제점이 있으므로 열처리 온도를 Ac1~Ac3+50℃로 한정한다.If the heat treatment is less than Ac1, the transformation does not proceed, there is a problem that the heat treatment effect does not appear, and if it exceeds Ac3 + 50 ℃, the average particle diameter of the microstructure has a problem that exceeds 2um, so the heat treatment temperature is Ac1 ~ Ac3 + 50 It is limited to ° C.
상기 열처리 시간이 0.01초 미만으로 하면 재결정 및 회복 적용이 미미하게 적용되어 열처리의 효과가 나타나지 않으며, 24시간 초과하면 지나친 산화가 발생 되어 소지철이 삭아 없어지고 과도한 열처리 비용이 소모되는 공정적인 문제와, 평귱입경이 목표보다 성장하는 미세조직 상의 문제점이 있다.When the heat treatment time is less than 0.01 seconds, the recrystallization and recovery application is insignificantly applied, and the effect of heat treatment does not appear. When the heat treatment time exceeds 24 hours, excessive oxidation occurs, the iron is removed, and the excessive heat treatment cost is consumed. There is a problem in the microstructure that the average particle diameter is larger than the target.
상기 냉각단계에서 0.01℃/s 미만의 냉각속도로 냉각하면, 냉각 중에 미세조직의 평균입경이 커질 뿐 아니라 상 불안정에 의한 조대 탄화물이 생길 수 있는 문제점이 있으므로 냉각속도의 하한은 0.01℃/s로 한정한다. 냉각 속도의 상한은 없으며 빠를수록 입실론 마르텐사이트 확보 및 미세 평균입경의 확보에 유리하다.When cooling at a cooling rate of less than 0.01 ℃ / s in the cooling step, the average particle diameter of the microstructure during cooling, as well as coarse carbides may occur due to phase instability, so the lower limit of the cooling rate is 0.01 ℃ / s It is limited. There is no upper limit to the cooling rate, and the faster it is, the more favorable it is to secure epsilon martensite and to secure a fine average particle size.
이하, 본 발명의 실시예에 대해 상세히 설명한다. 하기 실시예는 본 발명의 이해를 위한 것일 뿐, 본 발명을 한정하고자 하는 것은 아니다.Hereinafter, embodiments of the present invention will be described in detail. The following examples are only for the understanding of the present invention and are not intended to limit the present invention.
중량%로 C: 0.02%, Mn: 17%, N: 0.01, P: 0.008, S: 0.008%, Ti: 0.03% 및 Fe와 불가피한 불순물을 포함하는 냉간압연 강판을 5℃/s의 승온속도로 가열하여 하기 표 1과 같은 열처리온도에서 열처리 시간 동안 유지한 후, 5℃/s의 냉각속도로 상온까지 냉각하였다.The cold rolled steel sheet containing C: 0.02%, Mn: 17%, N: 0.01, P: 0.008, S: 0.008%, Ti: 0.03%, and Fe and unavoidable impurities by weight percent at a temperature of 5 ° C./s After heating to maintain the heat treatment time at the heat treatment temperature shown in Table 1, it was cooled to room temperature at a cooling rate of 5 ℃ / s.
상기와 같이 열처리 및 냉각된 강판에 대하여 미세조직의 평균입경 및 입실론 마르텐사이트의 분율을 조사하고, 그 결과를 하기 표 1 및 도 1에 나타내었다.The average particle diameter of the microstructure and the fraction of epsilon martensite were investigated for the steel sheets heat-treated and cooled as described above, and the results are shown in Table 1 and FIG. 1.
구분division 열처리 온도 (℃)Heat treatment temperature (℃) 열처리 시간 (min)Heat treatment time (min) 입경 (μm)Particle size (μm) 입실론 마르텐사이트의 면적 분율 (%)Area fraction of epsilon martensite (%)
실시예Example 600600 3030 1.231.23 6.26.2
비교예 1Comparative Example 1 700700 3030 2.32.3 33
비교예 2Comparative Example 2 800800 3030 3.63.6 14.914.9
비교예 3Comparative Example 3 900900 1010 6.76.7 16.816.8
비교예 4Comparative Example 4 10001000 3030 6.76.7 34.634.6
상기 표 1 및 도 1에 개시한 바와 같이, 600℃에서 열처리한 실시예와 700~1000℃에서 열처리한 비교예(1-4)를 비교해보면, 열처리온도가 700℃인 비교예(1)은 600℃에서 열처리한 실시예 보다 입실론 마르텐사이트의 면적 분율이 적고, 입경도 크게 나타남을 알 수 있다.As shown in Table 1 and Figure 1, when comparing the Example heat-treated at 600 ℃ and Comparative Example (1-4) heat-treated at 700 ~ 1000 ℃, Comparative Example (1) having a heat treatment temperature of 700 ℃ It can be seen that the area fraction of epsilon martensite is smaller than that of the heat-treated example at 600 ° C., and the particle size is also large.
또한, 열처리온도가 각각 800, 900 및 1000℃인 비교예(2-4)의 입실론 마르텐사이트의 면적 분율은 600℃에서 열처리한 실시예보다 크게 나타났으나, 600℃에서 열처리한 실시예의 입경은 700~1000℃에서 열처리한 비교예(2-4)의 입경 보다 작게 나타났다.In addition, the area fraction of epsilon martensite of Comparative Example (2-4) having a heat treatment temperature of 800, 900, and 1000 ° C., respectively, was larger than that of the embodiment heat-treated at 600 ° C., but the particle diameter of the embodiment heat-treated at 600 ° C. It appeared smaller than the particle diameter of the comparative example (2-4) heat-processed at 700-1000 degreeC.
한편, 본 발명에 따라 600℃에서 열처리한 실시예는 미세조직의 평균입경이 2μm이하임을 알 수 있다. On the other hand, the embodiment heat-treated at 600 ℃ according to the present invention can be seen that the average particle diameter of the microstructure is 2μm or less.
도 2는 도 1에 제시 된 열처리의 딜라토미터 사이클을 나타낸 도면이다.FIG. 2 is a diagram illustrating a dilator cycle of the heat treatment shown in FIG. 1.
도2를 통해 Ac1과 Ac3를 확인할 수 있으며 실시예는 Ac3 + 30℃ 에서 열처리 한 결과이다.Ac1 and Ac3 can be confirmed through FIG. 2, and the embodiment shows the result of heat treatment at Ac3 + 30 ° C. FIG.
도 3은 600℃에서 열처리한 실시예와 1000℃에서 열처리한 비교예(4)에 대하여 마찰계수법으로 측정하였다. SDC(Specific Damping Capacity)를 측정한 결과를 나타낸다.3 is measured by the friction coefficient method for the Example heat-treated at 600 ℃ and Comparative Example (4) heat-treated at 1000 ℃. It shows the result of measuring the specific damping capacity (SDC).
여기서 SDC는 감쇠능(물체가 진동을 흡수하는 성질)을 의미한다.SDC is the damping ability (the property that the object absorbs vibration).
도 1 과 도 3을 참조하면, 600℃에서 열처리한 실시예에 의한 미세조직을 갖는 방진강의 상온 SDC 값이 비교예(4)에 의한 방진강에 비해 2.5배 높은 값을 가짐을 알 수 있다. 즉 600℃에서 열처리한 실시예의 SDC 값은 0.00025이고, 1000℃에서 열처리한 비교예(4)의 SDC 값은 0.0001로 측정되었다. 1 and 3, it can be seen that the room temperature SDC value of the anti-vibration steel having a microstructure according to the embodiment heat-treated at 600 ° C has a value 2.5 times higher than the anti-vibration steel according to Comparative Example (4). That is, the SDC value of the Example heat-treated at 600 ° C was 0.00025, and the SDC value of Comparative Example (4) heat-treated at 1000 ° C was measured as 0.0001.
600℃에서 열처리한 실시예의 입실론 마르텐사이트 면적 분율이 상대적으로 낮지만, 입경이 작으므로 조직이 미세하고 균일하게 분포되어 잔류 전위(dislocation)와 계면이 입실론 마르텐사이트와 함께 외부 충격이 가해졌을 때 에너지를 열에너지로 전환하는 비율을 높여 댐핑 성능 향상에 기여하기 때문에 방진특성이 우수하다.Although the epsilon martensite area fraction of the embodiment heat-treated at 600 ° C. is relatively low, but the particle size is small, the structure is fine and uniformly distributed so that the residual dislocation and the interface are energized when an external impact is applied with the epsilon martensite. The dustproof property is excellent because it contributes to the improvement of damping performance by increasing the ratio of converting to heat energy.
일반적으로 상온 SDC 값이 0.00015 이상이면 방진특성이 우수하다고 할 수 있다.Generally, when the room temperature SDC value is 0.00015 or more, it can be said that the dustproof property is excellent.
상기 결과를 종합해 보면, 본 발명에 따라 열처리를 하는 경우, 2μm이하의 평균입경을 확보함으로써 우수한 방진특성을 확보될 수 있음을 알 수 있다.In summary, when the heat treatment according to the present invention, it can be seen that by ensuring an average particle diameter of 2μm or less, excellent dustproof characteristics can be secured.
비교예의 경우 700℃에서 열처리한 비교예를 제외하고는 입실론 마르텐사이트 면적 분율이 실시예 대비 높으나 미세조직의 평균입경이 크므로 방진성능이 열위하다.In the comparative example, except for the comparative example heat-treated at 700 ° C., the epsilon martensite area fraction is higher than that of the example, but the dustproof performance is inferior because the average particle diameter of the microstructure is large.

Claims (6)

  1. 중량%로, C : 0.1%이하, Mn : 8~30%, P : 0.1%이하, S : 0.02%이하, N : 0.1%이하, Ti 0~1.0% 및 Fe와 불가피한 불순물을 포함하고, 미세조직은 입실론 마르텐사이트와 오스테나이트로 이루어지고, 마르텐사이트와 오스테나이트의 평균 입경이 2μm이하인 것을 특징으로 하는 고Mn강판.By weight%, C: 0.1% or less, Mn: 8-30%, P: 0.1% or less, S: 0.02% or less, N: 0.1% or less, Ti 0-1.0%, and Fe and unavoidable impurities The structure is made of epsilon martensite and austenite, and the high Mn steel sheet is characterized in that the average particle diameter of martensite and austenite is 2 μm or less.
  2. 제 1항에 있어서, The method of claim 1,
    상기 강판은 추가적으로 중량%로 Si: 0~3%, Cr: 0.005%~5.0%, Ni: 0.005~2.0%, Nb: 0.005~0.5%, B: 0.0001~0.01%, V: 0.005~0.5% 및 W: 0.005~1% 중의 1종 또는 2종 이상을 포함하는 것을 특징으로 하는 방진특성이 우수한 고Mn강판.The steel sheet additionally in weight% Si: 0-3%, Cr: 0.005% -5.0%, Ni: 0.005-2.0%, Nb: 0.005-0.5%, B: 0.0001-0.01%, V: 0.005-0.5% and W: High Mn steel sheet excellent in dustproof characteristics, characterized by containing one or two or more of 0.005 to 1%.
  3. 제 1항에 있어서, The method of claim 1,
    상기 강판의 상온 SDC 값이 0.00015 이상인 것을 특징으로 하는 방진특성이 우수한 고Mn강판.High Mn steel sheet excellent in dustproof characteristics, characterized in that the room temperature SDC value of the steel sheet is 0.00015 or more.
  4. 중량%로, C: 0~0.1%이하, Mn : 8~30%, P : 0.1%이하, S : 0.02%이하, N : 0.1%이하, Ti 0~1.0% 및 Fe와 불가피한 불순물을 포함하는 고Mn강판을By weight%, C: 0 to 0.1% or less, Mn: 8 to 30%, P: 0.1% or less, S: 0.02% or less, N: 0.1% or less, Ti 0 to 1.0% and containing Fe and unavoidable impurities High Mn steel sheet
    0.01~200℃/s 승온속도로 Ac1~Ac3+50℃의 열처리 온도까지 가열하는 단계;상기 열처리 온도에서 0.01초~24시간 동안 유지하는 단계; 및 Heating to a heat treatment temperature of Ac1 to Ac3 + 50 ° C. at a temperature increase rate of 0.01 to 200 ° C./s; maintaining at the heat treatment temperature for 0.01 seconds to 24 hours; And
    0.01℃/s 이상의 냉각속도로 상온까지 냉각하는 단계를 포함하는 방진특성이 우수한 고Mn강판의 제조방법.A method for producing a high Mn steel sheet having excellent dustproof characteristics, including cooling to room temperature at a cooling rate of 0.01 ° C./s or more.
  5. 제 4항에 있어서, The method of claim 4, wherein
    상기 고Mn강판의 미세조직은 입실론 마르텐사이트와 오스테나이트로 이루어지는 것을 특징으로 하는 방진특성이 우수한 고Mn강판의 제조방법.The microstructure of the high Mn steel sheet is a method of producing a high Mn steel sheet having excellent dustproof characteristics, characterized in that consisting of epsilon martensite and austenite.
  6. 제 4항에 있어서, The method of claim 4, wherein
    상기 강판은 추가적으로 중량%로 Si: 0~3%, Cr: 0.005%~5.0%, Ni: 0.005~2.0%, Nb: 0.005~0.5%, B: 0.0001~0.01%, V: 0.005~0.5% 및 W: 0.005~1% 중의 1종 또는 2종 이상을 포함하는 것을 특징으로 하는 방진특성이 우수한 고Mn강판의 제조방법.The steel sheet additionally in weight% Si: 0-3%, Cr: 0.005% -5.0%, Ni: 0.005-2.0%, Nb: 0.005-0.5%, B: 0.0001-0.01%, V: 0.005-0.5% and W: The manufacturing method of the high Mn steel plate excellent in the anti-vibration characteristic characterized by including 1 type (s) or 2 or more types in 0.005-1%.
PCT/KR2016/015040 2015-12-23 2016-12-21 High manganese steel sheet having excellent vibration-proof property, and manufacturing method therefor WO2017111473A1 (en)

Priority Applications (4)

Application Number Priority Date Filing Date Title
JP2018532710A JP2019504208A (en) 2015-12-23 2016-12-21 High manganese steel sheet with excellent anti-vibration properties and method for producing the same
EP16879340.4A EP3395978B1 (en) 2015-12-23 2016-12-21 High manganese steel sheet having excellent vibration-proof property, and manufacturing method therefor
CN201680075456.1A CN108474082B (en) 2015-12-23 2016-12-21 High manganese steel sheet having excellent vibration-proof properties and method for producing same
US16/061,134 US20180371586A1 (en) 2015-12-23 2016-12-21 High manganese steel sheet having excellent damping property, and manufacturing method therefor

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
KR10-2015-0185471 2015-12-23
KR1020150185471A KR101736636B1 (en) 2015-12-23 2015-12-23 HIHG-Mn STEEL PLATE HAVING EXCELLENT DAMPING PROPERTY AND METHOD FOR PRODUCING THE SAME

Publications (1)

Publication Number Publication Date
WO2017111473A1 true WO2017111473A1 (en) 2017-06-29

Family

ID=59048542

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/KR2016/015040 WO2017111473A1 (en) 2015-12-23 2016-12-21 High manganese steel sheet having excellent vibration-proof property, and manufacturing method therefor

Country Status (6)

Country Link
US (1) US20180371586A1 (en)
EP (1) EP3395978B1 (en)
JP (1) JP2019504208A (en)
KR (1) KR101736636B1 (en)
CN (1) CN108474082B (en)
WO (1) WO2017111473A1 (en)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2022505375A (en) * 2018-10-18 2022-01-14 ポスコ A method for manufacturing a high manganese steel material having excellent vibration isolation and formability, and a high manganese steel material manufactured by this manufacturing method.

Families Citing this family (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107794357B (en) * 2017-10-26 2018-09-14 北京科技大学 The method of super rapid heating technique productions superhigh intensity martensite cold-rolled steel sheet
CN112899577B (en) * 2021-01-18 2021-12-24 北京科技大学 Preparation method of Fe-Mn series high-strength high-damping alloy
CN114774800B (en) * 2022-04-19 2023-08-08 河南科技大学 Ultrahigh-strength high-plasticity and toughness martensitic steel and preparation method thereof

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2004137579A (en) * 2002-10-18 2004-05-13 Nisshin Steel Co Ltd HIGH Mn AUSTENITIC STEEL SHEET HAVING EXCELLENT BULLETPROOF PROPERTY
KR100840287B1 (en) * 2006-12-26 2008-06-20 주식회사 포스코 Composite steel of retained austenite and hcp martensite, and method for heat treatment thereof
JP2011230182A (en) * 2010-04-30 2011-11-17 Sumitomo Metal Ind Ltd Method for manufacturing high manganese-steel
KR20140085225A (en) * 2012-12-27 2014-07-07 주식회사 포스코 High manganese wear resistance steel having excellent weldability and method for manufacturing the same
KR20140119216A (en) * 2013-03-27 2014-10-10 주식회사 우진 High manganese alloy and the manufacturing method for high manganese alloy

Family Cites Families (19)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5445685A (en) * 1993-05-17 1995-08-29 The Regents Of The University Of California Transformation process for production of ultrahigh carbon steels and new alloys
JP2540283B2 (en) * 1993-07-28 1996-10-02 日本冶金工業株式会社 Superplastic duplex stainless steel
KR960006453B1 (en) * 1993-10-22 1996-05-16 최종술 Making method of vibration decrease alloy steel & the manufacturing process
US5891388A (en) * 1997-11-13 1999-04-06 Woojin Inc. Fe-Mn vibration damping alloy steel having superior tensile strength and good corrosion resistance
WO2004029313A1 (en) * 2002-09-30 2004-04-08 Nano Technology Institute, Inc Nano-crystal austenitic metal bulk material having high hardness, high strength and toughness , and method for production thereof
WO2006109919A1 (en) * 2005-04-11 2006-10-19 Korea Institute Of Science And Technology High-strength damping alloys and low-noise diamond saw using the same
JP4529872B2 (en) * 2005-11-04 2010-08-25 住友金属工業株式会社 High Mn steel material and manufacturing method thereof
CN100457952C (en) * 2007-06-26 2009-02-04 郑州航空工业管理学院 Casting high speed steel cutter and preparation method thereof
JP5500960B2 (en) * 2009-12-01 2014-05-21 新日鐵住金ステンレス株式会社 Fine grain austenitic stainless steel sheet with excellent stress corrosion cracking resistance and workability
KR20110075611A (en) * 2009-12-28 2011-07-06 주식회사 포스코 Wear resistant steel
CN102277539A (en) * 2011-08-01 2011-12-14 南京钢铁股份有限公司 High-strength steel with low yield ratio, high plasticity and ultrafine grain and preparation method thereof
KR101382981B1 (en) * 2011-11-07 2014-04-09 주식회사 포스코 Steel sheet for warm press forming, warm press formed parts and method for manufacturing thereof
CN103774052A (en) * 2012-10-25 2014-05-07 吴雪 Method for preparing high-strength steel plate with thickness of 20 mm
CN103774050A (en) * 2012-10-25 2014-05-07 吴雪 High-ductility steel with low yield ratio
CN103774051A (en) * 2012-10-25 2014-05-07 吴雪 High-strength steel
KR101518599B1 (en) * 2013-10-23 2015-05-07 주식회사 포스코 High manganess steel sheet with high strength and excellent vibration isolation property and mathod for manufacturing the same
KR101536469B1 (en) * 2013-12-24 2015-07-13 주식회사 포스코 High manganese steel having excellent vibration damping ability and machinability
CN103898401B (en) * 2014-04-11 2016-04-20 四川大学 A kind of method improving high strength ferrimanganic base damping alloy damping capacity
CN103966506B (en) * 2014-05-09 2016-04-13 曹帅 A kind of iron-based noiseless alloy with high damping characteristic and preparation method thereof

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2004137579A (en) * 2002-10-18 2004-05-13 Nisshin Steel Co Ltd HIGH Mn AUSTENITIC STEEL SHEET HAVING EXCELLENT BULLETPROOF PROPERTY
KR100840287B1 (en) * 2006-12-26 2008-06-20 주식회사 포스코 Composite steel of retained austenite and hcp martensite, and method for heat treatment thereof
JP2011230182A (en) * 2010-04-30 2011-11-17 Sumitomo Metal Ind Ltd Method for manufacturing high manganese-steel
KR20140085225A (en) * 2012-12-27 2014-07-07 주식회사 포스코 High manganese wear resistance steel having excellent weldability and method for manufacturing the same
KR20140119216A (en) * 2013-03-27 2014-10-10 주식회사 우진 High manganese alloy and the manufacturing method for high manganese alloy

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP3395978A4 *

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2022505375A (en) * 2018-10-18 2022-01-14 ポスコ A method for manufacturing a high manganese steel material having excellent vibration isolation and formability, and a high manganese steel material manufactured by this manufacturing method.
JP7304415B2 (en) 2018-10-18 2023-07-06 ポスコ カンパニー リミテッド Method for producing high-manganese steel with excellent vibration isolation and formability, and high-manganese steel produced by this method

Also Published As

Publication number Publication date
KR101736636B1 (en) 2017-05-17
JP2019504208A (en) 2019-02-14
EP3395978A1 (en) 2018-10-31
EP3395978B1 (en) 2020-12-16
CN108474082B (en) 2020-06-02
EP3395978A4 (en) 2019-01-02
US20180371586A1 (en) 2018-12-27
CN108474082A (en) 2018-08-31

Similar Documents

Publication Publication Date Title
WO2017111473A1 (en) High manganese steel sheet having excellent vibration-proof property, and manufacturing method therefor
WO2020130560A1 (en) Cold rolled steel sheet having excellent workability, hot-dip galvanized steel sheet, and manufacturing methods thereof
WO2012081871A2 (en) Austenitic, lightweight, high-strength steel sheet of which the yield ratio and flexibility are outstanding and a production method therefor
WO2014209064A1 (en) High-strength steel sheet and manufacturing method therefor
WO2017111290A1 (en) Steel sheet having excellent pwht resistance for low-temperature pressure vessel and method for manufacturing same
WO2021100995A1 (en) Steel sheet having high strength and high formability and method for manufacturing same
WO2017034216A1 (en) High-hardness steel sheet, and manufacturing method therefor
WO2019117430A1 (en) Ferritic stainless steel having excellent high-temperature oxidation resistance, and manufacturing method therefor
WO2009145562A2 (en) High-strength steel sheet with excellent ductility and crackless edge portion, hot-dip galvanized steel sheet, and manufacturing method thereof
WO2017052005A1 (en) Ferritic stainless steel and manufacturing method therefor
WO2019059660A1 (en) Low-alloy steel sheet having excellent strength and ductility and manufacturing method therefor
WO2016105092A1 (en) Ferrite-based stainless steel and method for manufacturing same
WO2011081236A1 (en) Quenched steel sheet having excellent hot press formability, and method for manufacturing same
WO2015030324A1 (en) High-strength hot-rolled plated steel sheet and method for manufacturing same
WO2020060051A1 (en) Hot rolled and unannealed ferritic stainless steel sheet having excellent impact toughness, and manufacturing method therefor
WO2016064226A1 (en) High strength and high ductility ferritic stainless steel sheet and method for producing same
WO2019125025A1 (en) High-strength austenite-based high-manganese steel material and manufacturing method for same
WO2015099214A1 (en) Quenched steel sheet having excellent strength and ductility and method for manufacturing same
WO2019117432A1 (en) Ferrite-based stainless steel having excellent impact toughness, and method for producing same
WO2021125793A1 (en) Wire rod for high strength cold head quality steel with excellent resistance to hydrogen embrittlement, and manufacturing method thereof
WO2021125564A1 (en) High-strength ferritic stainless steel for clamp, and manufacturing method therefor
KR102098501B1 (en) High-manganese steel having excellent vibration-proof properties and formability, and method for manufacturing thereof
WO2020085687A1 (en) High-strength ferritic stainless steel for clamp and method for manufacturing same
KR101736637B1 (en) HIHG-Mn STEEL PLATE HAVING EXCELLENT DAMPING PROPERTY AND METHOD FOR PRODUCING THE SAME
WO2020130257A1 (en) High strength steel sheet having excellent ductility and workability, and method for manufacturing same

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 16879340

Country of ref document: EP

Kind code of ref document: A1

ENP Entry into the national phase

Ref document number: 2018532710

Country of ref document: JP

Kind code of ref document: A

NENP Non-entry into the national phase

Ref country code: DE

WWE Wipo information: entry into national phase

Ref document number: 2016879340

Country of ref document: EP

ENP Entry into the national phase

Ref document number: 2016879340

Country of ref document: EP

Effective date: 20180723