EP2431492B1 - Tôle d'acier contenant de l'azote à haute teneur en manganèse présentant une résistance et une ductilité élevées, et son procédé de fabrication - Google Patents

Tôle d'acier contenant de l'azote à haute teneur en manganèse présentant une résistance et une ductilité élevées, et son procédé de fabrication Download PDF

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Publication number
EP2431492B1
EP2431492B1 EP10769913.4A EP10769913A EP2431492B1 EP 2431492 B1 EP2431492 B1 EP 2431492B1 EP 10769913 A EP10769913 A EP 10769913A EP 2431492 B1 EP2431492 B1 EP 2431492B1
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Prior art keywords
steel sheet
nitrogen
manganese
steel
less
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German (de)
English (en)
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EP2431492A2 (fr
EP2431492A4 (fr
Inventor
Young Kook Lee
Yeon Seung Jung
Sin Gon Kang
Dong Joon Min
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Hyundai Steel Co
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Hyundai Steel Co
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Priority claimed from KR1020090036963A external-priority patent/KR101140931B1/ko
Priority claimed from KR1020100026584A external-priority patent/KR101193718B1/ko
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips 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
    • 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
    • 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
    • C22C38/02—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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—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
    • C21D2211/004—Dispersions; Precipitations

Definitions

  • the present invention relates to high manganese-nitrogen containing TWIP steel sheets having high strength and high ductility, and a method of manufacturing the same, which may be used as steel sheets for automobiles requiring high workability and impact absorbing materials such as bumper reinforcing materials for automobiles.
  • US 4 855 105 A refers to a wear-resistant steel containing carbon, manganese, silicon, sulphur, phosphorus, nitrogen, titanium and iron in the following ratio of the components in % by weight: carbon: 0.4-1.3; manganese: 3-11.5; sulphur: up to 0.05; phosphorus: up to 0.1; titanium: 0.01-0.15; nitrogen: 0.02-0.9; iron: the balance, and a method for making it which provides for saturation of the melted alloying addition with the nitrogen by treating said addition with the low-temperature plasma produced from a nitrogen-containing gas mixture at a partial pressure of the nitrogen in the latter of approximately from 0.08 to 0.3 MPa. While mixing the melts, first the melted non-alloyed steel base representing up to 0.7 of the total weight of the melt is taken and the whole of the melted alloying addition saturated with the nitrogen is added to it, after which the rest of the melted non-alloyed steel base is introduced.
  • GB 2 024 862 A refers to a high-manganese, non-magnetic steel having excellent weldability and machinability and suitable for use in the structural parts of electrical equipment or nuclear fusion equipment consisting essentially of (% by weight): -carbon 0.55-0.80 -silicon 0.1-1.2 -manganese 10.0-14.5 -nickel 0.3-3.0 - chromium 0.5-3.6 -nitrogen 0.01-0.2 - balance iron and inevitable impurities.
  • the steel may further contain at least one element of 0.01 to 1.0% of molybdenum, 0.01 to 0.5% of vanadium, 0.01 to 0.5% of niobium, 0.005 to 0.5% of titanium, 0.01 to 1.0% of zirconium, 0.0007 to 0.005% of calcium, 0.01 to 0.15% of sulfur, 0.03 to 0.2% of selenium, 0.03 to 0.2% of lead, and 0.01 to 0.8% of tin.
  • JP H03 13544 A refers to the preparation of a slab of a steel having a composition consisting of, by weight, 0.55-0.80% C, ⁇ +0.5% Si, 11-17% Mn, 0.02-0.06% Al, 0.02-0.06% N, ⁇ +0.02% P, and the balance iron with inevitable impurities.
  • high strength steel for automobiles examples include dual phase (DP) steel, transformation induced plasticity (TRIP) steel, twin induced plasticity (TWIP) steel, and the like.
  • DP dual phase
  • TRIP transformation induced plasticity
  • TWIP twin induced plasticity
  • DP steel has a dual phase of ferrite and martensite transformed from austenite at room temperature and is manufactured by setting a cooling finish temperature below a martensite start temperature (Ms) to transform part of the austenite into martensite when cooling a hot rolled steel sheet to room temperature.
  • Ms martensite start temperature
  • Such DP steel may have various mechanical properties through regulation of mole fraction of martensite and ferrite.
  • TRIP steel exhibits good workability and is obtained by partially forming retained austenite, followed by transformation of the austenite into martensite during component machining.
  • TRIP steel has high strength resulting from significant work hardening based on martensite transformation, but has a drawback of excessively low elongation.
  • both DP steel and TRIP steel have a work hardening mechanism mainly based on a martensite structure, which is a hard phase and exhibits a highly increasing rate in the degree of work hardening during plastic deformation, thereby enabling manufacture of high strength hot-rolled steel sheets.
  • the steel sheets have significantly low ductility, thereby making it difficult to guarantee an elongation of 30% or more.
  • TWIP steel contains a large amount of manganese and has a single austenite phase, which is stable at room temperature and allows formation of mechanical twins in the austenite structure during component machining, thereby increasing the degree of work hardening.
  • TWIP steel has an austenite structure instead of a ferrite structure as a matrix structure and has improved elongation through additional work hardening by continuously generating mechanical twins in austenite grains to obstruct movement of dislocations during plastic deformation.
  • TWIP steel may have high elongation and high tensile strength due to the mechanical twins causing a high degree of work hardening.
  • TWIP steel has elongation 50% higher than that of conventional DP steel or TRIP steel and is thus preferably applied to steel sheets for automobiles.
  • TWIP steel has a high manganese content in the range of about 18 to 30% in order to guarantee austenite stability and adjust stacking fault energy, and requires addition of large amounts of aluminum or silicon together with manganese, causing a significant increase in material and manufacturing costs.
  • TWIP steel which has a low Mn content in order to avoid additional increase in manufacturing costs caused by volatilization of Mn or temperature decrease during a steel manufacturing process or continuous casting process.
  • mechanical properties since currently developed TWIP steel has a low yield strength of about 300 MPa and a tensile strength of 1 GPa or less, there is a need for steel sheets which have higher strength without deteriorating elongation.
  • the present invention provides a steel sheet capable of solving problems of DP steel, TRIP steel and TWIP steel in the related art.
  • the present invention provides a steel sheet which has both high strength and high ductility with reduced amounts of manganese.
  • the present invention provides a steel sheet which contains inexpensive elements instead of manganese while guaranteeing higher strength and ductility and easier working than steel sheets having a high manganese content.
  • the present invention provides a method of manufacturing a high manganese-nitrogen containing steel sheet, which allows an increase in nitrogen content of the steel sheet.
  • a high manganese-nitrogen containing TWIP steel sheet consisting of:
  • a high manganese-nitrogen containing steel sheet includes: 0.5 to 1.0 wt% of carbon, 10 to 20 wt% of manganese, 4.0 wt% or less of chromium, 0.02 to 0.3 wt% of nitrogen, and the balance of Fe and unavoidable impurities.
  • a high manganese-nitrogen containing steel sheet includes: 0.5 to 1.0 wt% of carbon, 10 to 20 wt% of manganese, 4.0 wt% or less of chromium, 0.02 to 0.3 wt% of nitrogen, at least one of less than 4 wt% of silicon, less than 3 wt% of aluminum, less than 0.30 wt% of niobium, less than 0.30 wt% of titanium and less than 0.30 wt% of vanadium, and the balance of Fe and unavoidable impurities.
  • At least part of the nitrogen is contained in the steel sheet through arc-melting.
  • the steel sheet has a tensile strength and total elongation (TS ⁇ El) of 50,000 MPa% or more.
  • Manganese may be present in an amount of 15 to 18 wt%.
  • Nitrogen may be present in an amount of 0.10 to 0.3 wt%.
  • the steel sheet may be a hot-rolled steel sheet.
  • the steel sheet may be a cold-rolled annealed steel sheet.
  • a method of manufacturing a high manganese-nitrogen containing steel sheet according to claim 6 includes: placing electrolytic iron, electrolytic manganese and carbon powder in a chamber; filling the chamber with an argon-nitrogen atmosphere; and arc-melting the electrolytic iron, electrolytic manganese and carbon powder.
  • the arc-melting may be repeated plural times.
  • the nitrogen-argon atmosphere may have a nitrogen fraction of 0.2 to 0.8.
  • the method may further include: hot rolling the high nitrogen-containing steel sheet at 900 °C or more; and air cooling or forced air cooling the hot rolled steel sheet.
  • the method may further include: cold rolling the cooled steel sheet at a reduction rate of 50% or more at room temperature; annealing the cold rolled steel sheet at 800 °C or more; and air cooling or forced air cooling the annealed steel sheet.
  • the manufactured steel sheet may consist of: 0.5 to 1.0 wt% of carbon, 10 to 20 wt% of manganese, 0.02 to 0.2 wt% of nitrogen, and the balance of Fe and unavoidable impurities.
  • a raw material for chromium may be further placed in the chamber.
  • the manufactured steel sheet may consist of 0.5 to 1.0 wt% of carbon, 10 to 20 wt% of manganese, 4.0 wt% or less of chromium, 0.02 to 0.2 wt% of nitrogen, and the balance of Fe and unavoidable impurities.
  • raw materials for chromium and at least one of silicon, aluminum, niobium, titanium and vanadium may be placed in the chamber.
  • the manufactured steel sheet may consist of: 0.5 to 1.0 wt% of carbon, 10 to 20 wt% of manganese, 4.0 wt% or less of chrome, 0.02 to 0.3 wt% of nitrogen, at least one of less than 4 wt% of silicon, less than 3 wt% of aluminum, less than 0.30 wt% of niobium, less than 0.30 wt% of titanium and less than 0.30 wt% of vanadium, and the balance of Fe and unavoidable impurities.
  • high manganese-nitrogen containing TWIP steel sheets have an austenite structure formed at room temperature and allow effective regulation of stacking fault energy through addition of chrome and nitrogen.
  • the steel sheets allow a high degree of work hardening, and have high tensile strength and excellent workability by mechanical twins formed during plastic deformation of the steel sheets.
  • the high manganese-nitrogen containing steel sheets according to the exemplary embodiments have a very high product of tensile strength to total elongation (TS ⁇ El) of 50,000 MPa% or more, which is much higher than that of conventional TWIP steel, thereby guaranteeing a significantly high product of tensile strength to total elongation while reducing manufacturing costs.
  • high manganese-nitrogen containing steel sheets may be used in various ways such as hot rolled steel sheets, cold-rolled annealed steel sheets, and the like.
  • carbon and nitrogen are added while lowering the manganese content to be in the range of 10 ⁇ 20 wt% to have a single austenite phase structure at room temperature, as compared with conventional twin induced plasticity (TWIP) steel containing 20 wt% of manganese.
  • TWIP twin induced plasticity
  • nitrogen induces not only solid solution strengthening effects, but also mechanical twins by affecting the stacking fault energy.
  • the high manganese-nitrogen containing steel sheets according to the exemplary embodiments include the aforementioned alloy elements, thereby achieving an elongation of 50% or more and higher yield strength and tensile strength than conventional TWIP steel while reducing the amounts of expensive alloy elements such as manganese or aluminum below those of the conventional TWIP steel.
  • a high manganese-nitrogen containing steel sheet consists of 0.5 to 1.0 wt% of carbon, 10 to 20 wt% of manganese, 0.02 to 0.3 wt% of nitrogen, and the balance of Fe and unavoidable impurities.
  • the high manganese-nitrogen containing steel sheet according to the first exemplary embodiment includes 10 to 20 wt% of manganese. Namely, since TWIP steel has mechanical twins formed in an austenite matrix at room temperature during plastic deformation, it is important to expand an austenite region of high temperature to an austenite region at room temperature on a Fe-carbon phase diagram. In this embodiment, manganese is used as an austenite stabilizing element.
  • manganese is present in an amount of 15 to 18 wt% in the steel sheet. If the Mn content reaches 15 wt%, austenite stability can be secured and stacking fault energy can be effectively lowered to promote formation of mechanical twins during plastic deformation, thereby providing a very high product of tensile strength to elongation.
  • the Mn content is less than 10 wt%, austenite stability is significantly deteriorated, causing formation of ferrite or martensite in the austenite region during cooling after hot rolling. Further, if the Mn content is less than 10 wt%, stacking fault energy of the austenite phase excessively increases, thereby making it difficult to form mechanical twins.
  • the stacking fault energy excessively increases, so that the twins are not formed and plastic deformation of austenite occurs, thereby causing deterioration of mechanical properties.
  • the high manganese-nitrogen containing steel sheet according to this embodiment includes 0.5 to 1.0 wt% of carbon.
  • Fe-Mn binary alloys containing 20 wt% or less of Mn have ⁇ -martensite or ⁇ -martensite partially formed therein instead of a single austenite phase microstructure at room temperature.
  • carbon is added as an austenite stabilizing element which is inexpensive and highly effective.
  • the carbon content is less than 0.5 wt%, it is difficult to obtain a single austenite phase during cooling after hot rolling due to insufficient austenite stability, or, even in the case where the single austenite phase is obtained at room temperature, phase transformation occurs from austenite to martensite during plastic deformation to form TRIP steel, and thus desired TWIP steel cannot be obtained.
  • the carbon content exceeds 1.0 wt%, stable austenite can be obtained at room temperature, but cementite precipitation occurs, causing deterioration in elongation or weldability. Further, if the carbon content exceeds 1.0 wt%, the stacking fault energy excessively increases thereby making it difficult to form the mechanical twins during deformation.
  • the high manganese-nitrogen containing steel sheet according to the first exemplary embodiment contains 0.02 to 0.3 wt% of nitrogen.
  • nitrogen acts as an interstitial element which stabilizes the austenite structure, and as in carbon, austenite stability increases and strength resulting from solid solution strengthening increases with increasing amount of nitrogen.
  • the stacking fault energy does not increase, thereby facilitating formation of the mechanical twins.
  • the degree of solid solution hardening increases, thereby providing advantageous effects of significantly increased yield strength of the steel sheet.
  • the nitrogen content less than 0.02 wt% is an amount of nitrogen added as an impurity in manufacture of typical steel sheets and makes it difficult to obtain austenite stability. Thus, ferrite or martensite is not formed at room temperature after hot rolling, and it is difficult to obtain a function of regulating the stacking fault energy.
  • the present invention enables an increase of the nitrogen content to 0.1 wt% or more, more preferably 0.2 wt% or more, through an arc-melting process described below.
  • a high manganese-nitrogen containing steel sheet consists of 0.5 to 1.0 wt% of carbon, 10 to 20 wt% of manganese, 0.02 to 0.3 wt% of nitrogen, 4 wt% or less of chromium, and the balance of Fe and unavoidable impurities.
  • chromium improves not only corrosion resistance but also nitrogen solubility of steel. Further, chromium reduces the stacking fault energy, which increases due to addition of carbon, thereby promoting formation of the mechanical twins.
  • chromium is a ferrite stabilizing element, the chromium content exceeding 4.0 wt% can cause partial formation of ferrite during hot rolling. Further, since chromium is expensive, use of large amounts of chromium increases manufacturing costs. Thus, the content of chromium is set to 4 wt% or less.
  • the nitrogen content exceeds 0.3 wt%, it is necessary to increase the Cr content added in order to allow nitrogen to be dissolved in a large amount in the steel sheet, which results in an undesirable increase of manufacturing costs.
  • a high manganese-nitrogen containing steel sheet consists of 0.5 to 1.0 wt% of carbon, 10 to 20 wt% of manganese, 4.0 wt% or less of chromium, 0.02 to 0.3 wt% of nitrogen, at least one of less than 4 wt% of silicon, less than 3 wt% of aluminum, less than 0.30 wt% of niobium, less than 0.30 wt% of titanium and less than 0.30 wt% of vanadium, and the balance of Fe and unavoidable impurities.
  • the silicon content is 4 wt% or less, solid solution hardening obtained by silicon results in reduction of grain size, thereby improving strength through increase of yield strength. Further, addition of silicon reduces the stacking fault energy of steel, thereby facilitating formation of mechanical twins during plastic deformation.
  • the silicon content of silicon is set to 4 wt% or less.
  • aluminum content is 3 wt% or less, deoxidation effects cannot be obtained. Further, aluminum suppresses formation of ⁇ -martensite through increase in stacking fault energy at a slip plane, thereby improving ductility. In addition, aluminum may suppress formation of ⁇ -martensite even with a low amount of manganese, thereby enabling minimization of manganese content in manufacture of steel while improving workability.
  • niobium, titanium and vanadium are strong carbide forming elements coupling with carbon to form carbide, which effectively prevents grain growth to form fine grains while providing precipitation hardening effects by formation of precipitate phases.
  • the amount of niobium, titanium or vanadium exceeds 0.30 wt%, segregation of niobium, titanium or vanadium can occur in grain boundaries causing grain boundary brittlement, or the precipitate phases can become excessively coarse, thereby deteriorating grain growth effects.
  • niobium, titanium or vanadium may be added in an amount of 0.30 wt% or less.
  • the amounts of other elements added to the steel sheet according to the third embodiment are the same as those of the steel sheets according to the first and second embodiments, and a detailed description thereof will thus be omitted herein.
  • the method of manufacturing a high manganese-nitrogen containing steel sheet according to the exemplary embodiment is as follows. First, electrolytic iron, electrolytic manganese, and carbon powder are placed in a chamber. Here, the composition of a final steel sheet may be controlled by controlling the amounts of such raw materials supplied to the chamber. Then, the chamber is evacuated and is filled with argon and nitrogen to create an argon-nitrogen atmosphere therein.
  • the argon-nitrogen atmosphere has a total pressure of 1 atm., and nitrogen has a partial pressure in the range of 0.2 to 0.8 atm. If the ratio of nitrogen is less than 20 wt%, the amount of nitrogen added becomes too low in the steel during arc-melting, thereby deteriorating arc-melting efficiency.
  • the ratio of nitrogen exceeds 80 wt%, the pressure of inert gas, that is, the pressure of argon, is excessively reduced, causing severe generation of manganese fumes, by which the interior of the chamber is severely contaminated. Further, if the ratio of nitrogen is too high, scattering of the raw materials severely occurs due to melting of a tungsten electrode rod, causing a very rough surface of the steel sheet after arc-melting.
  • the raw materials are subjected to arc-melting using an electrode rod within the chamber, followed by cooling for an appropriate period of time, thereby providing desired steel.
  • arc-melting and cooling may be performed once, arc-melting and cooling are desirably repeated plural times.
  • the nitrogen content increases with increasing the number of times of repeating the processes of arc-melting and cooling.
  • the nitrogen content is limited to 0.02 to 0.1 wt% in a typical method of manufacturing TWIP steel, it is very difficult to form a high manganese-nitrogen containing steel sheet having the composition according to the first exemplary embodiment without adding an element for promoting dissolution of nitrogen in the steel sheet, such as chrome.
  • the steel is formed by arc-melting in the argon-nitrogen atmosphere as described above, it is possible to add a larger amount of nitrogen without adding an expensive element such as chromium than in the case of forming the steel sheet using a typical method, and, particularly, the high manganese-nitrogen containing steel sheet having the composition according to the first embodiment may be obtained.
  • the method of manufacturing a steel sheet using arc-melting may be applied not only to the steel sheet having the composition according to the first embodiment but also to steel sheets having various compositions.
  • the steel sheet After manufacturing the high manganese-nitrogen containing steel sheet using the arc-melting, the steel sheet is subjected to hot rolling at 900°C or more, followed by air cooling or forced air cooling.
  • the hot rolled and cooled steel sheet is subjected to cold rolling at a reduction rate of 50% at room temperature, followed by annealing at 800°C or more and air cooling or forced air cooling.
  • the high manganese-nitrogen containing steel sheets according to the embodiments of the invention may be manufactured by a typical method.
  • the typical method of manufacturing the steel sheet includes heating a steel slab having a desired composition to 1100°C or more, hot rolling the heated steel slab at 900°C or more to provide a steel sheet, and air cooling or forced air cooling the hot rolled steel sheet. Then, the method may further include cold rolling the cooled steel sheet at a reduction rate of 50% or more, annealing the cold rolled steel sheet at 800°C or more, and air cooling or forced air cooling the annealed steel sheet.
  • Samples of Examples 1 to 6 and Comparative Examples 1 to 6 were each produced in accordance with the method of the invention by heating steel slabs having compositions listed in Table 1 to 1100°C or more, hot rolling at 900°C or more to provide steel sheets with a thickness of 3mm, and air cooling the hot rolled steel sheet.
  • the sample of Example 4 is a cold rolled steel sheet sample which was produced by cold rolling the hot rolled steel sheet sample of Example 3 from a thickness of 3mm to a thickness of 1.5 mm, followed by annealing at 800°C for 10 minutes.
  • Example 5 70820 cold-rolled annealed steel sheet
  • Example 5 343.2 803.2 68.2 53413 hot-rolled steel sheet
  • Example 6 358.4 818.3 66.5 54417 hot-rolled steel sheet
  • Comparative Example 1 650.1 928.7 15.5 14395 hot-rolled steel sheet Comparative Example 2 339.0 666.0 67.0 44622 hot-rolled steel sheet Comparative Example 3 313.3 711.4 61.4 43680 hot-rolled steel sheet Comparative Example 4 387.0 1021.2 33.9 34619 hot-rolled steel sheet Comparative Example 5 461.2 908.8 7.61 6916 hot-rolled steel sheet Comparative Example 6 470.5 937.3 5.04 4724 hot-rolled steel sheet
  • each of the steel sheets according to Examples 1 to 4 has a yield strength (YS) exceeding 300 MPa and a tensile strength (TS) exceeding 880Mpa. Further, each of the steel sheets according to Examples 1 to 4 has a total elongation (EL) of about 60%, and a very high product of tensile strength to elongation (TS ⁇ EL) of 50,000 MPa%. In other words, it can be seen that each of the steel sheets according to the examples has higher yield strength and higher tensile strength than conventional TWIP steel (Comparative Examples 2 and 3), and similar elongation to the conventional TWIP steel.
  • Example 3 when the nitrogen content exceeds 0.2 wt%, the steel sheet sample have very high yield strength and tensile strength provided by solid solution hardening effects of nitrogen. Namely, the steel sheet according to Example 3 has a tensile strength exceeding 1 GPa and an elongation approaching 60%, thereby providing a product of tensile strength and elongation (TS ⁇ EL) exceeding 60,000 MPa%. Further, Example 4 is a steel sheet produced by cold rolling and annealing the hot rolled steel sheet of Example 3, and it was confirmed that Example 4 had improved tensile strength and elongation.
  • Fig. 1 is an electron micrograph of a high manganese-nitrogen containing steel sheet according to one example of the present invention, and as seen from Fig.1 , the steel sheet according to Example 3 has mechanical twins.
  • the steel sheet of Example 5 further including aluminum and silicon and the steel sheet of Example 6 further including aluminum have large amounts of nitrogen despite a significant decrease in Cr content, thereby exhibiting excellent yield strength and tensile strength.
  • the steel sheets of the comparative examples were produced by a conventional method and had lower tensile strength or elongation than those of the examples.
  • the steel sheet according to Comparative Example 1 was a TRIP steel sheet and had a high tensile strength of 928.7 MPa and a low total elongation of 15.5%.
  • Other TWIP steel sheets (Comparative Examples 2 and 3), which did not contain nitrogen and were produced by a conventional method, have high total elongation of 60% or more, but have a relatively low tensile strength of about 700 MPa, thereby providing a product of tensile strength to elongation (TS ⁇ EL) of about 40,000 MPa%.
  • TS ⁇ EL product of tensile strength to elongation
  • the steel sheets according to Examples 8 to 9 were produced using arc-melting.
  • electrolytic iron, electrolytic manganese, and carbon powder were placed in a predetermined ratio in a chamber, which in turn was evacuated and filled with argon and nitrogen to create an argon-nitrogen atmosphere in the chamber.
  • the argon-nitrogen atmosphere had a total pressure of 1 atm.
  • nitrogen had a partial pressure in the range of 0.2 to 0.8 atm.
  • the raw materials were subjected to arc-melting using an arc electrode rod at an electric current of 400A for 30 minutes while advancing the arc electrode rod in a state of being separated a distance of 2 to 5 cm from each of the samples, followed by cooling for 30 minutes. The process of arc-melting and cooling was repeated three times.
  • the steel sheet according to Comparative Example 7 was produced by melting the raw materials in a nitrogen atmosphere without arc-melting.
  • Example 8 is a reference example only.
  • Table 3 Sample No. Composition (wt%) Note C Mn Cr N Example 8 0.760 14.27 - 0.109 Arc-melting Example 9 0.570 16.47 - 0.090 Arc-melting Comparative Example 7 0.618 15.03 1.82 0.086 Melting in nitrogen atmosphere
  • Example 8 it was possible to produce a high-Mn steel sheet by arc-melting Cr-free steel in an argon-nitrogen atmosphere. Further, as in Example 4, it was possible to form higher-nitrogen steel by arc-melting Cr-containing steel in an argon-nitrogen atmosphere.
  • the steel according to the comparative example included chromium and was produced by a typical steel manufacturing method in a nitrogen atmosphere. It could be confirmed that, even in the case where Cr-containing steel was subjected to melting in a nitrogen atmosphere as in the comparative example, the nitrogen content of the steel was less than that of the steel sheets according to the examples 8, 9. Namely, as in the comparative example, when steel containing 1.73 wt% of Cr is produced by melting, the steel contained 0.086 wt% of nitrogen.
  • Fig. 2 is a tensile strength curve of steel according to Example 9.
  • the steel according to Example 9 has excellent strength and elongation, that is, 985 MPa and 56%, and has a product of tensile strength to elongation of about 55,000 MPa%, which is much higher than high Mn steel containing 20 wt% or less of Mn without containing Cr, and which is similar to high Mn steel containing more than 20% Mn and an expensive metal element such as Cr or the like.

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Claims (8)

  1. Tôle d'acier TWIP à plasticité induite par maclage contenant de l'azote à haute teneur en manganèse, contenant de 0,5 % en poids à 1,0 % en poids de carbone; de 10 % en poids à 20 % en poids de manganèse; de 0,02 % en poids à 0,3 % en poids d'azote, optionnellement 4,0 % en poids ou moins de chrome, optionnellement d'au moins parmi moins de 4 % en poids de silicium, moins de 3 % en poids d'aluminium, moins de 0,30 % en poids de niobium, moins de 0,30% en poids de titane et moins de 0,30 % en poids de vanadium; le reste étant du fer et des impuretés inévitables,
    dans laquelle au moins une partie de l'azote est contenue dans la tôle d'acier par l'entremise d'une fusion à l'arc, et
    dans laquelle la tôle d'acier présente un produit de la résistance à la traction avec l'allongement total (TS x El) de 50000 MPa%, ou plus.
  2. Tôle d'acier contenant de l'azote à haute teneur en manganèse selon la revendication 1, dans laquelle le manganèse est présent en une quantité de 15 % en poids à 18 % en poids.
  3. Tôle d'acier contenant de l'azote à haute teneur en manganèse selon l'une quelconque des revendications 1 ou 2, dans laquelle l'azote est présent en une quantité de 0,10 % en poids à 0,3 % en poids.
  4. Tôle d'acier contenant de l'azote à haute teneur en manganèse selon l'une quelconque des revendications 1 à 3, dans laquelle la tôle d'acier est une tôle d'acier laminée à chaud.
  5. Tôle d'acier contenant de l'azote à haute teneur en manganèse selon l'une quelconque des revendications 1 à 4, dans laquelle la tôle d'acier est une tôle d'acier recuite laminée à froid.
  6. Procédé de fabrication d'une tôle d'acier contenant de l'azote à haute teneur en manganèse selon les revendications 1 à. 5, comprenant les étapes suivantes:
    placer les composants des revendications 1 à 3, dans lesquels le fer se présente sous la forme de fer électrolytique, le manganèse se présente sous la forme de manganèse électrolytique et le carbone se présente sous la forme poudre de carbone, dans une chambre;
    évacuer la chambre et remplir la chambre avec une atmosphère d'azote-argon qui présente une pression totale de 1 atm, où l'azote présente une pression partielle comprise dans la gamme de 0,2 atm à 0,8 atm; et
    faire fondre à l'arc lesdits composants, ensuite les refroidir, chauffer la brame d'acier à 1100°C; laminer à chaud la brame d'acier chauffée à 900°C ou plus pour former une tôle d'acier, et refroidir à l'air ou refroidir à l'air forcé la tôle d'acier laminée à chaud;
    soumettre optionnellement la tôle d'acier laminée à chaud et refroidie à un laminage à froid à une vitesse de réduction de 50 % à la température ambiante, et ensuite recuire à 800°C ou plus et refroidir à l'air ou refroidir à l'air forcé.
  7. Procédé selon la revendication 6, dans lequel la fusion à l'arc est répétée plusieurs fois.
  8. Procédé selon l'une quelconque des revendications 6 ou 7, dans lequel l'atmosphère d'azote-argon présente une fraction d'azote comprise entre 0,2 et 0,8.
EP10769913.4A 2009-04-28 2010-04-27 Tôle d'acier contenant de l'azote à haute teneur en manganèse présentant une résistance et une ductilité élevées, et son procédé de fabrication Revoked EP2431492B1 (fr)

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KR1020090036963A KR101140931B1 (ko) 2009-04-28 2009-04-28 고강도 및 고연성을 갖는 고망간 질소 함유 강판 및 그 제조방법
KR1020100026584A KR101193718B1 (ko) 2010-03-25 2010-03-25 고강도 및 고연성을 갖는 고망간 질소 함유 강판 및 그 제조방법
PCT/KR2010/002625 WO2010126268A2 (fr) 2009-04-28 2010-04-27 Tôle d'acier contenant de l'azote à haute teneur en manganèse présentant une résistance et une ductilité élevées, et son procédé de fabrication

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN110724874A (zh) * 2018-07-17 2020-01-24 宝钢特钢有限公司 具有抗腐蚀磨损性能的高锰奥氏体钢及热轧板制备方法

Families Citing this family (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2402472B2 (fr) † 2010-07-02 2017-11-15 ThyssenKrupp Steel Europe AG Acier à résistance élevée pouvant être déformé à froid et produit plat en acier constitué d'un tel acier
KR101510505B1 (ko) * 2012-12-21 2015-04-08 주식회사 포스코 우수한 도금성과 초고강도를 갖는 고망간 용융아연도금강판의 제조방법 및 이에 의해 제조된 고망간 용융아연도금강판
KR101490567B1 (ko) * 2012-12-27 2015-02-05 주식회사 포스코 용접성이 우수한 고망간 내마모강 및 그 제조방법
US10041139B2 (en) * 2013-06-27 2018-08-07 Hyundai Steel Company High-strength steel sheet and manufacturing method therefor
KR101747034B1 (ko) 2016-04-28 2017-06-14 주식회사 포스코 항복비가 우수한 초고강도 고연성 강판 및 이의 제조방법
CN109154050B (zh) * 2016-05-24 2021-04-06 安赛乐米塔尔公司 用于制造具有奥氏体基体的twip钢板的方法
CN107537860A (zh) * 2016-06-25 2018-01-05 天津大学 采用冷轧调整tp347h奥氏体耐热钢组织的方法
EP3617337A4 (fr) * 2017-04-26 2020-03-25 JFE Steel Corporation ACIER RICHE EN Mn ET SON PROCÉDÉ DE PRODUCTION
CN109536815A (zh) * 2018-11-24 2019-03-29 冯良荣 一种制备氮化锰合金的方法
CN111850422B (zh) * 2020-04-30 2022-01-11 中科益安医疗科技（北京）股份有限公司 高氮无镍奥氏体不锈钢无缝薄壁管材及其制备方法
CN112708823A (zh) * 2020-11-24 2021-04-27 河钢股份有限公司 高热塑性的高锰高铝twip钢及其生产方法

Family Cites Families (27)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS558474A (en) * 1978-07-04 1980-01-22 Kobe Steel Ltd Non-magnetic high manganese steel excellent in weldability and machinability
US4256516A (en) * 1978-12-26 1981-03-17 Nippon Kokan Kabushiki Kaisha Method of manufacturing non-magnetic Fe-Mn steels having low thermal expansion coefficients and high yield points
JPS58126956A (ja) * 1982-01-22 1983-07-28 Nippon Steel Corp プレス加工性の優れた高強度薄鋼板
JPS6036647A (ja) * 1983-08-06 1985-02-25 Kawasaki Steel Corp 局部腐食抵抗性に優れる高マンガン鋼
JPS60141823A (ja) * 1983-12-27 1985-07-26 Kobe Steel Ltd 非磁性エンドリングの製造方法
IN165225B (fr) * 1986-03-26 1989-09-02 Bruss Ti Kirova
JPS63235428A (ja) * 1987-03-24 1988-09-30 Nippon Mining Co Ltd 非磁性材料の製造方法
JPH0762172B2 (ja) * 1989-06-09 1995-07-05 新日本製鐵株式会社 高Ｍｎ非磁性鉄筋棒鋼の製造方法
JPH07107187B2 (ja) * 1990-10-15 1995-11-15 新日本製鐵株式会社 応力腐食割れ感受性の小さい高Ｍｎ非磁性鋼
KR940007374B1 (ko) * 1992-07-24 1994-08-16 포항종합제철 주식회사 성형성, 강도 및 용접성이 우수한 오스테나이트계 고 망간강과 그 제조방법
BR9205689A (pt) * 1991-12-30 1994-05-24 Po Hang Iron & Steel Aço austenitico de elevado manganês com uma melhor conformabilidade, resistência e soldabilidade, e o correspondente processo de fabricaçao
JPH0657379A (ja) * 1992-08-12 1994-03-01 Nippon Steel Corp 熱間加工性および耐食性に優れた非磁性鋼材
JP3182995B2 (ja) * 1993-10-15 2001-07-03 株式会社神戸製鋼所 耐応力腐食割れ性および機械的性質の優れた高Ｍｎ非磁性鋼
KR100241016B1 (ko) * 1995-12-26 2000-03-02 이구택 인성이 우수한 고망간강 및 이의 열간압연방법
FR2796083B1 (fr) * 1999-07-07 2001-08-31 Usinor Procede de fabrication de bandes en alliage fer-carbone-manganese, et bandes ainsi produites
DE10128544C2 (de) * 2001-06-13 2003-06-05 Thyssenkrupp Stahl Ag Höherfestes, kaltumformbares Stahlblech, Verfahren zu seiner Herstellung und Verwendung eines solchen Blechs
FR2829775B1 (fr) * 2001-09-20 2003-12-26 Usinor Procede de fabrication de tubes roules et soudes comportant une etape finale d'etirage ou d'hydroformage et tube soude ainsi obtenu
FR2857980B1 (fr) * 2003-07-22 2006-01-13 Usinor Procede de fabrication de toles d'acier austenitique fer-carbone-manganese, a haute resistance, excellente tenacite et aptitude a la mise en forme a froid, et toles ainsi produites
KR101178775B1 (ko) * 2003-12-23 2012-09-07 막스-플랑크-인스티투트 퓌어 아이젠포르슝 게엠베하 경량 구조강의 핫 스트립의 제조 방법
JP2005325387A (ja) * 2004-05-13 2005-11-24 Kiyohito Ishida 低比重鉄合金
JP2008519160A (ja) * 2004-11-03 2008-06-05 ティッセンクルップ スチール アクチェンゲゼルシャフト Ｔｗｉｐ特性をもつ高強度の鋼ストリップ又はシートの製造方法、コンポーネント及び高強度鋼ストリップ又はシートの製造方法
FR2878257B1 (fr) * 2004-11-24 2007-01-12 Usinor Sa Procede de fabrication de toles d'acier austenitique, fer-carbone-manganese a tres hautes caracteristiques de resistance et d'allongement, et excellente homogeneite
FR2881144B1 (fr) * 2005-01-21 2007-04-06 Usinor Sa Procede de fabrication de toles d'acier austenitique fer-carbone-manganese a haute resistance a la fissuration differee, et toles ainsi produites
KR100742823B1 (ko) * 2005-12-26 2007-07-25 주식회사 포스코 표면품질 및 도금성이 우수한 고망간 강판 및 이를 이용한도금강판 및 그 제조방법
JP4627069B2 (ja) * 2006-05-09 2011-02-09 株式会社日本製鋼所 高窒素鋼の製造方法
KR100851158B1 (ko) * 2006-12-27 2008-08-08 주식회사 포스코 충돌특성이 우수한 고망간형 고강도 강판 및 그 제조방법
KR20070085757A (ko) * 2007-06-04 2007-08-27 티센크루프 스틸 악티엔게젤샤프트 Ｔｗｉｐ 특성을 갖는 고강도 강 스트립 또는 박판 및 직접스트립 주조에 의한 상기 스트립 제조 방법

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN110724874A (zh) * 2018-07-17 2020-01-24 宝钢特钢有限公司 具有抗腐蚀磨损性能的高锰奥氏体钢及热轧板制备方法

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WO2010126268A2 (fr) 2010-11-04
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