EP3395978B1 - Tôle d'acier à haute teneur en manganèse ayant une excellente propriété d'amortissement des vibrations et procédé de fabrication s'y rapportant - Google Patents

Tôle d'acier à haute teneur en manganèse ayant une excellente propriété d'amortissement des vibrations et procédé de fabrication s'y rapportant Download PDF

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EP3395978B1
EP3395978B1 EP16879340.4A EP16879340A EP3395978B1 EP 3395978 B1 EP3395978 B1 EP 3395978B1 EP 16879340 A EP16879340 A EP 16879340A EP 3395978 B1 EP3395978 B1 EP 3395978B1
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steel sheet
less
heat treatment
manufacturing
austenite
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German (de)
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EP3395978A1 (fr
EP3395978A4 (fr
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Won-Tae Cho
Tai-Ho Kim
Kwang-Geun Chin
Young-Ha Kim
Tae-Jin Song
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Posco Holdings Inc
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Posco Co Ltd
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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
    • 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
    • C22C38/08—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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • 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
    • C22C38/12—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
    • C22C38/18—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

Definitions

  • the present disclosure relates to a high Mn steel sheet having excellent damping properties, provided as a steel sheet for a vehicle or construction equipment and used in a location requiring damping properties for noise reduction.
  • High Mn damping steel is steel having good damping properties and excellent mechanical properties, since noise energy may be converted to thermal energy due to interface sliding of epsilon martensite when an external impact is applied.
  • Patent Document EP 2 778 247 A1 relates to steel sheet for warm press forming, the steel sheet comprising, by weight%, C: 0.01% to 0.5%, Si: 3.0% or less (excluding 0%), Mn: 3% to 15%, P: 0.0001% to 0.1%, S: 0.0001% to 0.03%, A1 3.0% or less (excluding 0%), N: 0.03% or less (excluding 0%), and the balance of Fe and inevitable impurities.
  • Patent Document WO 2015/060499 A1 relates to a high-strength and high-manganese steel sheet suitable for an outer panel or a vehicle body of a transport vehicle and, more specifically, to a high-strength and high-manganese steel sheet having excellent vibration-proof properties and a method for producing the same.
  • An aspect of the present disclosure may provide a high Mn steel sheet having excellent damping properties and a method for manufacturing the same.
  • a high Mn steel sheet having excellent damping properties, includes: 0 wt% to 0.1 wt% of carbon (C), 8 wt% to 30 wt% of manganese (Mn), 0.1 wt% or less of phosphorus (P), 0.02 wt% or less of sulfur (S), 0.1 wt% or less of nitrogen (N), 0 wt% to 1.0 wt% of titanium (Ti), the balance of Fe and inevitable impurities, the high Mn steel sheet further optionally comprising one, two, or more among 0 wt% to 3 wt% of silicon (Si), 0.005 wt% to 5.0 wt% of chromium (Cr), 0.005 wt% to 2.0 wt% of nickel (Ni), 0.005 wt% to 0.5 wt% of niobium (Nb), 0.0001 wt% to 0.01 wt% of boron (B),
  • a high Mn steel sheet having excellent damping properties is provided, and is used for structural components for a vehicle and building materials such as a flooring material, in which a noise reduction is required.
  • the present disclosure relates to a high Mn steel sheet having excellent damping properties and a method for manufacturing the same.
  • the high Mn steel sheet includes 0 wt% to 0.1 wt% or less of carbon (C), 8 wt% to 30 wt% of manganese (Mn), 0.1 wt% or less (including 0%) of phosphorus (P), 0.02 wt% or less (including 0%) of sulfur (S), 0.1 wt% or less (including 0%) of nitrogen (N), 0 wt% to 1.0 wt% (excluding 0%) of titanium (Ti), and iron (Fe) and inevitable impurities.
  • a microstructure of the steel sheet consists of epsilon martensite and austenite, and an average particle diameter of each of the epsilon martensite and the austenite is 2 ⁇ m or less.
  • a specific steel composition of the steel sheet according to the present disclosure and the reasons for restricting the steel composition thereof are as follows.
  • addition amount of carbon (C) exceeds 0.1%, carbides may be excessively precipitated, and the hot workability and elongation are lowered, and the damping capability may be significantly reduced. Thus, the addition amount of C is limited to 0.1% or less.
  • Manganese (Mn) is an element essential for stably securing an austenite structure and is an element for increasing the stacking fault energy. If an addition amount of Mn is less than 8%, martensite, degrading formability, is formed. Thus, strength increases but ductility significantly decreases. Moreover, the stacking fault energy is lowered, so austenite, partially formed, may be easily transformed into epsilon martensite. Thus, a lower limit of Mn is limited to 8%. On the other hand, if the addition amount of Mn exceeds 30%, manufacturing costs may be increased due to a large amount of Mn, and slab cracking may be caused by an increase in an amount of phosphorus (P) in steel.
  • P phosphorus
  • an upper limit of the addition amount of Mn is limited to 30%.
  • Phosphorus (P) and sulfur (S) are inevitably included when steel is produced.
  • the content of P is limited to 0.1% or less (including 0%), and the content of S is limited to 0.02% or less (including 0%).
  • P segregation occurs, so the workability of steel may be reduced.
  • S coarse manganese sulfide (MnS) is formed, so a defect such as flange cracking may be generated, and the hole expansion of a steel sheet may be reduced.
  • an addition amount thereof should be significantly suppressed as much as possible.
  • N Nitrogen
  • Titanium (Ti) is a strong carbide forming element, combined with carbon to form a carbide.
  • the carbide formed at this time is an element effective in refining a grain size by inhibiting crystal grain growth.
  • Ti when Ti is added in combination with boron, a high temperature compound is formed in a columnar-grained boundary to prevent grain boundary cracking from occurring.
  • Ti has a scavenging effect in which a fraction of each of C and N is lowered by forming a compound with C and N.
  • Ti is an essential element for improving damping capabilities.
  • an addition amount of Ti exceeds 1.00%, an excessive amount of Ti may be segregated in a crystal grain boundary and grain boundary embrittlement may be caused, or a precipitation phase may be excessively coarse. Thus, a grain growth effect may be lowered. Therefore, the addition amount of Ti is limited to being 1.0% or less.
  • the high Mn steel sheet according to another aspect to the present disclosure additionally includes one, two, or more among 0 wt% to 3 wt% of silicon (Si), 0.005 wt% to 5.0 wt% of chromium (Cr), 0.005 wt% to 2.0 wt% of nickel (Ni), 0.005 wt% to 0.5 wt% of niobium (Nb), 0.0001 wt% to 0.01 wt% of boron (B), 0.005 wt% to 0.5 wt% of vanadium (V), and 0.005 wt% to 1 wt% of tungsten (W).
  • Si silicon
  • Cr chromium
  • Ni nickel
  • Nb niobium
  • B boron
  • B 0.005 wt% to 0.5 wt% of vanadium
  • W 0.005 wt% to 1 wt% of tungsten
  • Silicon (Si) is a solid solution strengthening element, and is an element for increasing yield strength by reducing a grain size by a solid solution effect. Thus, Si is necessary to secure strength.
  • Si is necessary to secure strength.
  • an addition amount of Si is increased, during hot rolling, silicon oxide is formed on a surface of a steel sheet. Thus, pickling properties are deteriorated, so surface qualities of a steel sheet may be deteriorated, as a disadvantage.
  • due to addition of a large amount of Si the weldability of steel may be significantly lowered.
  • an upper limit of the addition amount of Si is limited to 3%.
  • Chromium (Cr) reacts with external oxygen during a hot rolling or annealing operation, and a Cr-based oxide film (Cr 2 O 3 ) having a thickness of 20 ⁇ m to 50 ⁇ m is preferentially formed on a surface of a steel sheet, so Mn and Si, contained in the steel, are prevented from being eluted into a surface layer.
  • Cr may act as an element for contributing to stabilization of a structure of a surface layer and improving plating surface properties.
  • Nickel (Ni) contributes to the stabilization of the austenite, which is not only advantageous for improving the elongation but also contributing effectively to the high temperature ductility. If the content of Ni, a strong high temperature toughness improving element, is less than 0.005%, an effect on high temperature toughness is insignificant. If an added content of Ni increases, Ni has a significant effect on prevention of delayed fracture and slab cracking. However, material costs may be high, so production costs may be increased. Thus, the content of Ni is Limited to 0.005% to 2.0%.
  • Niobium is a carbide forming element for forming carbide by being combined with carbon in the steel.
  • Nb may be added for the purpose of increasing the strength and refining the grain size.
  • Nb forms a precipitate at a lower temperature as compared to Ti, so Nb is an element having significant effects of refining a crystal grain size and strengthening precipitation by formation of a precipitate.
  • Nb may be added in an amount of 0.005% to 0.5%. However, if an addition amount of Nb is less than 0.005%, the effect described above is insignificant.
  • Nb is added in an amount exceeding 0.5%, an excessive amount of Nb is segregated in a grain boundary, thereby causing grain boundary embrittlement, or a precipitate may be excessively coarse, thereby lowering a growth effect of a crystal grain. Moreover, in a hot rolling process, recrystallization is delayed, so rolling load may be increased. Thus, the addition amount of Nb is Limited to 0.005% to 0.5%.
  • Vanadium (V) and tungsten (W) are elements for forming carbonitride by being combined with C and N together with Ti.
  • V and W may be important elements for securing austenite.
  • V is added in small amounts, less than 0.005%, the effect described above is insignificant.
  • V is added in an amount exceeding 0.5% and W is added in an amount exceeding 1.0%, a precipitate is excessively coarse, so a grain growth effect may be lowered, which may cause hot brittleness.
  • the addition amount of V is Limited to 0.005% to 0.5%
  • the addition amount of W is limited to 0.005% to 1%.
  • B Boron
  • steel which has the composition and composition range, and in which a microstructure is comprised of a austenite as main phase, is heated at a heating rate of 0.01°C/s to 200°C/s, and maintained at a heat treatment temperature of Ac1°C to Ac3+50°C for 0.01 second to 24 hours, and is then cooled 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 consists of epsilon martensite and austenite.
  • the heat treatment is performed at a temperature less than Ac1, transformation does not proceed, so there may be a problem in which a heat treatment effect can not be obtained. If a heat treatment temperature exceeds Ac3+50°C, there may be a problem in which an average particle diameter of a microstructure exceeds 2 ⁇ m. Thus, the heat treatment temperature is limited to Ac1°C to Ac3+50°C.
  • the heat treatment time is less than 0.01 second, the application of recrystallization and recovery is insignificant, so an effect of heat treatment may be not obtained. If the heat treatment time exceeds 24 hours, there may be a problem in a process in which excessive oxidation occurs, so base iron is removed, and excessive heat treatment costs are consumed, as well as a problem in a microstructure in which a microstructure significantly grows, so an average particle diameter thereof is greater than a target particle diameter.
  • cooling is performed at a cooling rate less than 0.01°C/s, there may be problems in which an average particle diameter of a microstructure is increased during the cooling, and coarse carbides are generated due to phase instability.
  • a lower limit of a cooling rate is limited to 0.01°C/s.
  • a cold rolled steel sheet including 0.02 wt% of C, 17 wt% of Mn, 0.01 wt% of N, 0.008 wt% of P, 0.008 wt% of S, 0.03 wt% of Ti, and Fe and inevitable impurities, was heated at a heating rate of 5°C/s, and was then maintained for the heat treatment time at a heat treatment temperature illustrated in Table 1. Then, the heat treated steel sheet was cooled to room temperature at a cooling rate of 5°C/s.
  • the Example, heat treated at 600°C is compared with the Comparative Examples (2 to 4), heat treated at 800°C to 1000°C.
  • the area fraction of epsilon martensite was greater, as compared to the Example, heat treated at 600°C.
  • a particle diameter of the Example, heat treated at 600°C was smaller than a particle diameter of the Comparative Examples (2 to 4), heat treated at 800°C to 1000°C.
  • an average particle diameter of a microstructure was 2 ⁇ m or less.
  • FIG. 2 is a drawing illustrating a dilatometer cycle of heat treatment illustrated in FIG. 1 .
  • SDC indicates the damping capacity (a property in which an object absorbs vibrations).
  • a room temperature SDC value of damping steel having a microstructure according to the Example, heat treated at 600°C is a value 2.5 times that of damping steel according to Comparative Example (4).
  • a SDC value of Example, heat treated at 600°C is 0.00025
  • a SDC value of Comparative Example (4), heat treated at 1000°C was measured as 0.0001.

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

Claims (4)

  1. Tôle d'acier à haut Mn ayant d'excellentes propriétés d'amortissement, comprenant
    0,1 % en poids ou moins de carbone (C), 8 % en poids à 30 % en poids de manganèse (Mn), 0,1 % en poids ou moins de phosphore (P), 0,02 % en poids ou moins de soufre (S), 0,1 % en poids ou moins d'azote (N), 0 % en poids à 1,0 % en poids de titane (Ti), le solde de Fe et d'impuretés inévitables, la tôle d'acier à haut Mn comprenant en outre facultativement un, deux, ou plus de deux éléments parmi 0 % en poids à 3 % en poids de silicium (Si), 0,005 % en poids à 5,0 % en poids de chrome (Cr), 0,005 % en poids à 2,0 % en poids de nickel (Ni), 0,005 % en poids à 0,5 % en poids de niobium (Nb), 0,0001 % en poids à 0,1 % en poids de bore (B), 0,005 % en poids à 0,5 % en poids de vanadium (V), et 0,005 % en poids à 1 % en poids de tungstène (W),
    une microstructure de la tôle d'acier étant composée de martensite epsilon et d'austénite, et un diamètre de particule moyen de chacune de la martensite epsilon et de l'austénite est de 2 µm ou moins.
  2. La tôle d'acier à haut Mn ayant d'excellentes propriétés d'amortissement de la revendication 1, sachant qu'une valeur de capacité d'amortissement spécifique à température ambiante de la tôle d'acier est de 0,00015 ou plus.
  3. Procédé de fabrication d'une tôle d'acier à haut Mn de la revendication 1, comprenant :
    le chauffage d'une tôle d'acier à haut Mn, incluant 0,1 % en poids ou moins de carbone (C), 8 % en poids à 30 % en poids de manganèse (Mn), 0,1 % en poids ou moins de phosphore (P), 0,02 % en poids ou moins de soufre (S), 0,1 % en poids ou moins d'azote (N), 0 % en poids à 1,0 % en poids de titane (Ti), le solde de Fe et d'impuretés inévitables, la tôle d'acier à haut Mn comprenant en outre facultativement un, deux, ou plus de deux éléments parmi 0 % en poids à 3 % en poids de silicium (Si), 0,005 % en poids à 5,0 % en poids de chrome (Cr), 0,005 % en poids à 2,0 % en poids de nickel (Ni), 0,005 % en poids à 0,5 % en poids de niobium (Nb), 0,0001 % en poids à 0,1 % en poids de bore (B), 0,005 % en poids à 0,5 % en poids de vanadium (V), et 0,005 % en poids à 1 % en poids de tungstène (W), à une température de traitement thermique de Ac1 °C à Ac3+50 °C à une cadence de chauffage de 0,01 °C/s à 200 °C/s ;
    le maintien de la tôle d'acier à haut Mn pendant 0,01 seconde à 24 heures à la température de traitement thermique ; et
    le refroidissement de la tôle d'acier à haut Mn à température ambiante à une cadence de refroidissement de 0,01 °C/s ou plus.
  4. Le procédé de fabrication d'une tôle d'acier à haut Mn ayant d'excellentes propriétés d'amortissement de la revendication 3, sachant qu'une microstructure de la tôle d'acier à haut Mn est composée de martensite epsilon et d'austénite.
EP16879340.4A 2015-12-23 2016-12-21 Tôle d'acier à haute teneur en manganèse ayant une excellente propriété d'amortissement des vibrations et procédé de fabrication s'y rapportant Active EP3395978B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
KR1020150185471A KR101736636B1 (ko) 2015-12-23 2015-12-23 방진특성이 우수한 고Mn강판 및 그 제조방법
PCT/KR2016/015040 WO2017111473A1 (fr) 2015-12-23 2016-12-21 Tôle d'acier à haute teneur en manganèse ayant une excellente propriété d'amortissement des vibrations et procédé de fabrication s'y rapportant

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EP3395978A1 EP3395978A1 (fr) 2018-10-31
EP3395978A4 EP3395978A4 (fr) 2019-01-02
EP3395978B1 true EP3395978B1 (fr) 2020-12-16

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US (1) US20180371586A1 (fr)
EP (1) EP3395978B1 (fr)
JP (1) JP2019504208A (fr)
KR (1) KR101736636B1 (fr)
CN (1) CN108474082B (fr)
WO (1) WO2017111473A1 (fr)

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CN107794357B (zh) * 2017-10-26 2018-09-14 北京科技大学 超快速加热工艺生产超高强度马氏体冷轧钢板的方法
KR102098501B1 (ko) * 2018-10-18 2020-04-07 주식회사 포스코 방진성 및 성형성이 우수한 고망간 강재의 제조방법 및 이에 의해 제조된 고망간 강재
CN112899577B (zh) * 2021-01-18 2021-12-24 北京科技大学 一种Fe-Mn系高强度高阻尼合金的制备方法
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WO2017111473A1 (fr) 2017-06-29
US20180371586A1 (en) 2018-12-27
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CN108474082A (zh) 2018-08-31
EP3395978A1 (fr) 2018-10-31
CN108474082B (zh) 2020-06-02
EP3395978A4 (fr) 2019-01-02

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