WO2006048034A1 - Bande ou tole d'acier extremement resistante a proprietes twip et procede de fabrication de ladite bande a l'aide de la 'coulee directe de bandes' - Google Patents

Bande ou tole d'acier extremement resistante a proprietes twip et procede de fabrication de ladite bande a l'aide de la 'coulee directe de bandes' Download PDF

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Publication number
WO2006048034A1
WO2006048034A1 PCT/EP2004/012407 EP2004012407W WO2006048034A1 WO 2006048034 A1 WO2006048034 A1 WO 2006048034A1 EP 2004012407 W EP2004012407 W EP 2004012407W WO 2006048034 A1 WO2006048034 A1 WO 2006048034A1
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WO
WIPO (PCT)
Prior art keywords
strip
hot
contents
cold
mass
Prior art date
Application number
PCT/EP2004/012407
Other languages
German (de)
English (en)
Inventor
Jens-Ulrik Becker
Harald Hofmann
Manfred Menne
Jochen Wans
Original Assignee
Thyssenkrupp Steel Ag
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 Thyssenkrupp Steel Ag filed Critical Thyssenkrupp Steel Ag
Priority to PCT/EP2004/012407 priority Critical patent/WO2006048034A1/fr
Priority to BRPI0419185-4A priority patent/BRPI0419185A/pt
Priority to EP04797547A priority patent/EP1807542A1/fr
Priority to US11/718,498 priority patent/US20090010793A1/en
Priority to CN200480044461.3A priority patent/CN101065503A/zh
Priority to JP2007539465A priority patent/JP2008519160A/ja
Publication of WO2006048034A1 publication Critical patent/WO2006048034A1/fr

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Classifications

    • 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
    • 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
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • C21D8/0215—Rapid solidification; Thin strip casting
    • 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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T29/00—Metal working
    • Y10T29/49—Method of mechanical manufacture
    • Y10T29/4998—Combined manufacture including applying or shaping of fluent material
    • Y10T29/49988—Metal casting
    • Y10T29/49991—Combined with rolling

Definitions

  • the invention relates to a method for producing high-strength, good cold-workable and TWIP properties steel strip or sheet of a Fe-C-Mn lightweight steel, a method for producing components and a high-strength steel strip or sheet having TWIP properties ,
  • Hadfield steels containing 11 to 14 wt .-% Mn and 1.1 to 1.4 wt .-% C in addition to iron as essential alloying elements.
  • Steels with such a high manganese content are characterized by a very high tensile strength and solidification when subjected to repeated impacts or friction.
  • TWIP "Twinning Induced jPlasticity”
  • the steels in question have a low ductility and good strength, a high ductility under mechanical stress as a result of a twinning of the grains of the microstructure occurring in the course of the mechanical stress.
  • This twin formation facilitates the deformation of the steel immediate.
  • the twins also contribute to increasing the yield stress of the steel in the case of mechanical stress by restricting the mobility of dislocations.
  • the ductility of TWIP steels is additionally supported by a martensitic ⁇ / oc transformation associated with the formation of twins.
  • a process for producing steel strips of Fe-C-Mn alloys of the type described above is known from EP 1 067 203 B1.
  • a molten steel containing 0.001-1.6 wt% C, 6-30 wt% Mn, up to 10 wt% Ni, the sum of the contents of Mn and Ni being 16 wt.
  • cast strip can also be produced by so-called “direct strip casting” method, for which usually the Short name “DSC method” is used.
  • DSC method Short name
  • the melt to be poured from the ladle is placed in a distribution vessel, from which it is placed on a continuously rotating conveyor belt.
  • the melt is intensively cooled, so that it solidifies upon reaching the end of the conveyor line of the conveyor belt to a solid pre-band.
  • the pre-band usually passes through a second cooling section, before it is also hot-rolled without interruption to this cooling section. Hot rolling can be done in one or more stands. After hot rolling, another controlled cooling then takes place before the finished hot rolled strip is wound into a coil.
  • TRIP Transformation ⁇ nduced Plasticity
  • TWIP Transformation ⁇ nduced Plasticity
  • steels with high Mn contents can only be hot-rolled and cold-rolled due to their inherently high strength. This is particularly critical in the case of high-strength TWIP steels of the type in question. In such steels, instabilities or cracks often appear at the strip edges, which is the reason for the large-scale production and processing of. Making strips or sheets of such steels difficult in practice. Also, due to the great hardness, the Steels with Mn contents of 18 wt .-% and more already in the as-cast condition prior to hot rolling own, a great manufacturing effort required to produce from such steels thin hot strip, from which subsequently at low cost, a cold strip of small thickness are produced can. On such thin cold-rolled sheets, which have a low weight with high strength and good deformation and Festiglceits in the event of an accident, however, there is an increased demand, especially in the field of automobile body construction.
  • the object of the invention was, on the basis of the above-described prior art, to provide a method for the production of TWAN steel strip and sheets with high manganese content, which makes it possible, with reduced effort, to produce products of optimized combination of properties and also optimum utility value To make available.
  • a process for the production of high-strength components of a steel of the type specified should be specified.
  • a steel strip or sheet should be created, which has a particularly good deformation behavior.
  • the remainder contains iron and impurities caused by melting, the contents of Sn, Sb, Zr, Ta and As, the sum of which does not exceed 0.30%, being attributed to these impurities, being applied to a conveyor belt and cooled there until it solidifies to a pre-band .
  • the stripped stock is, if necessary, subjected to a heat treatment, the hot strip is hot rolled at a temperature of at least 700 ° C. to a hot strip having a completely recrystallized structure,
  • the hot strip is reeled at a coiler temperature of up to 750 0 C.
  • the invention achieves the above-mentioned object by producing a hot or cold strip by applying the method according to the invention, from which then optionally a precursor is produced, which subsequently to the component finished cold forming.
  • the present invention produced steel strip or is -Sheet metal characterized in that its brittle / Duktil_ticiansübergangs- temperature T ue at below -40 0 C. D ⁇ e relevant transition temperature T ue is usually determined in the bucket impact test or in the impact test.
  • the invention is based on the finding that steels with Mn contents of 18% by weight and more can be processed in a particularly advantageous manner by using the DSC process known per se, if the hot rolling and coiling temperatures are set in accordance with the invention become. Since the hot rolling end temperature is at least 700 ° C., typically at least 850 ° C., after hot rolling there is a completely recrystallized hot strip, which is outstandingly suitable for a subsequent cold deformation. In addition, since the coiling temperature of at most 750 ° C., typically at most 550 ° C., is selected so that grain boundary oxidation of the hot strip obtained is largely avoided, surface defects occur only to a minimal extent in the hot strip obtained after coiling. Therefore, hot rolled strip produced according to the invention or cold strip produced therefrom can be coated particularly well with metallic coatings in order, for example, to improve its corrosion resistance.
  • a further advantage of the procedure according to the invention is that it is possible to cast pre-tapes with a thickness which is far higher than that which can be achieved in conventional strip casting.
  • pre-bands whose thickness is typically more than 10 mm, in particular more than 12 mm.
  • more than 15 mm or more than 20 mm thick pre-strip is deformed during subsequent hot rolling using high degrees of deformation to a thin hot strip whose thickness is typically less than 3 mm, in particular less than 2 mm.
  • the hot deformation of the cast pre-strip in the procedure according to the invention is preferably carried out so that high degrees of deformation of preferably more than 60%, in particular up to 95%, are achieved.
  • Another essential advantage of the method according to the invention is that it is significantly more tolerant of the presence of alloying elements in the processed melt which disturb the conventional process. Thus, even those melts shed with good success, in addition to noteworthy levels of phosphorus, sulfur and copper impurities in the form of relatively high levels of Sn, Sb, Zr, Ta and As of a total of up to 0.30 wt .-% can have. This makes it possible to tolerate higher levels of accompanying elements, without affecting the manufacturability of a correspondingly alloyed steel strip according to the invention.
  • the invention thus enables the cost-effective production of the melt via the electric arc furnace route with the use of inexpensive inferior scrap.
  • a replacement of a high C0 2 emissions causing blast furnaces is so feasible.
  • the possible processing of Metallschmel zen by the invention whose composition can be varied to high tolerances, allows the use of non-optimal alloying agent with corresponding impurities and thus additionally reduces the expenditure for alloying agent.
  • the high cost of blast furnace coke can be eliminated.
  • the method according to the invention can be carried out on production lines which require significantly less expenditure on equipment than conventional continuous casting systems.
  • the investment costs are correspondingly lower than those of a conventional continuous hot-rolled strip machine.
  • the method according to the invention also allows a width adjustment in coils.
  • the throughput achievable with a production line operating according to the invention is comparable to conventional continuous casting plants.
  • the C content of the alloy processed according to the invention can be 0.0000 wt. -% to 1, 6 wt. -%. Preferably it is in the range of from 0.2% to 0.8% by weight. At C contents of at least 0.2% by weight, the risk of decarburization of the melt is minimized. Carbon contents of more than 0.8% by weight may make it difficult to optimize the content of other alloying elements with a view to attaining favorable mechanical properties.
  • the preferably selected carbon content of 0.2 to 0.8% ensures improved manufacturability of steel sheets and strips produced according to the invention. Cracks and instabilities in the band edge area are significantly reduced, with increasing carbon content, the instabilities decrease in particular.
  • inventively provided carbon contents open up a wide range of
  • the manganese content of the alloy processed according to the invention is at least 18% by weight, in particular at least 20% by weight.
  • Such high Mn-containing steels of the erfind ⁇ ngswash processed type certainly have TWIP Eigenticiane ⁇ on. Since the sum of the contents of Mn and Ni in steels of the type in question should not exceed 30% by weight, the nickel content is limited to up to 10% by weight.
  • the silicon content of a melt processed according to the invention can be up to 8% by weight, which element is then added if steels of very low weight are to be produced.
  • higher levels of Si may be provided to substitute correspondingly reduced levels of C and Mn while retaining the TWIP properties.
  • the molten aluminum alloyed according to the invention may optionally be added in amounts of up to 10% by weight.
  • Chromium may be added to the steel alloy processed according to the present invention to improve the corrosion resistance.
  • a limitation of the Cr content to max. LO wt .-% is useful from a cost point of view, since above this limit, only slight property improvements are observed.
  • an advantageous embodiment of the invention that the sum of the melt at Te and Se at least 0.01 wt ⁇ ⁇ .-% by weight.
  • melt cast to the preliminary strip contains in total at least 0.01% by weight of V, Ti, Nb and / or REM.
  • the property-improving effect of B already sets in when B is present in contents of at least 0.001% by weight.
  • the total content of molybdenum, tungsten and cobalt can be up to 1.5% by weight to take advantage of the known property-improving effects of these elements. It is also possible to provide contents of Ca and Mg of up to 0.5% by weight in total, if the effects of these elements, which are also known per se, are to be utilized in steels of the type processed according to the invention.
  • Nitrogen levels up to 0.6% by weight can be added to utilize the strength-increasing and corrosion-inhibiting effect of nitrogen in steels of the type in question.
  • the steel sheet according to the invention for the production of wheels for vehicles, in particular power tools, for the production hydroformed or extruded parts, for use in the manufacture of high-strength engine parts, such as camshafts or piston rods, for the production of impulse-resistant loads, such as shelling, certain components, such as armor plating, and protective elements designed to protect persons, especially against shelling.
  • steel sheets according to the invention are particularly suitable for the production of non-magnetic components in the case of a purely austenitic microstructure.
  • steel strips or sheets produced according to the invention maintain their toughness even at particularly low temperatures.
  • steel products produced according to the invention are particularly suitable for the production of components used in cryotechnology, such as containers or pipes for refrigeration.
  • Deformation behavior according to the invention produced steel strips and sheets.
  • steel strips and sheets can be made available without problems whose mean r value r m is 1.0 +/- 0.15 and whose ⁇ r value is -0.2 to 0.2.
  • the hot strip according to the invention is hot rolled at a hot rolling end temperature amounting to at least 700 0 C, in addition to the already mentioned avoiding grain boundary oxidation, the positive effect of the carbon is fully utilized.
  • carbon causes higher tensile strength and yield strength values, while the elongation values which are still acceptable are still acceptable.
  • the hot rolling end temperature increases, the tensile strength and yield strength decrease while the elongation values increase.
  • Hot rolling temperatures in the frame given by the invention can be so targeted and easily influence the desired properties of the resulting steel strip.
  • the heat treatment performed between the solidification of the sliver on the conveyor belt and the hot rolling serves to raise the temperature of the sliver to a level from which optimum hot rolling results are achieved.
  • the heat treatment in a conventional manner include a supplementary targeted cooling, with which the pre-strip is brought to an optimal for hot rolling hot rolling start temperature.
  • it is also conceivable to carry out the heat treatment as heating of the pre-strip if the structure of the pre-strip is to be influenced by such a heat treatment or an increase in the temperature of the pre-strip to the optimum hot-rolling start temperature is required.
  • hot strip is characterized by good performance characteristics. If thinner sheets or strips are to be produced, then the hot strip can be cold rolled after being rolled into cold strip, wherein the cold rolling is advantageously carried out with a degree of cold rolling of 10% to 90%, preferably 30% to 75%.
  • the hot strip may be pickled prior to cold rolling.
  • the cold strip obtained after the one or more stages of cold rolling annealing-subjected, wherein the annealing temperatures between 600 0 C to 1IL00 0 C should be.
  • the annealing may be performed in the hood 0 C in the temperature range of 600 0 C to 750 0 C or in the pass at "temperatures" by TOO "C bi ⁇ f HOO" - are.
  • a first advantageous use of steel strips or sheets produced according to the invention consists in the production of cold-formed components by spin forming. For this purpose, blanks are made from the steel, which are then formed by the Drückwal zen finished. Due to its special property profile, steel strip or strip produced according to the invention is suitable. Sheet metal or sheet metal blanks produced therefrom in a special way for this purpose.
  • Good deformable steels with higher strengths of the inventively produced type can be used for the manufacture of components that are seen ver with gears or similar form elements. These components are typically gear units provided with internal or external gears. These can be produced inexpensively and with high dimensional accuracy by spin forming.
  • a method for producing gear parts by spin forming is known from DE 197 24 661. According to this known method, a blank is formed from a microalloyed high strength structural steel having a lower yield strength of at least 500 N / mm 2 from a sheet. This blank is then cold worked by spin forming to the gearbox. In the course of the Forming the toothing, the sheet material is transformed to the limit of its formability. Finally, a surface of the workpiece provided with the toothing is hardened substantially free of heat distortion while maintaining the temperature.
  • a purely austenitic or a microstructure consisting of a mixture of ferrite and austenite with proportions of martensite can be set in steel strip or sheet produced according to the invention.
  • the steels according to the invention can therefore be shaped much better. In the course of cold working, they solidify much more strongly than the high-strength microalloyed or multiphase steels known for the manufacture by spin forming.
  • component strengths in the range from 1400 N / mm 2 to 2200 N / mm 2 can be achieved. An additional hardening of the components produced after the cold deformation can therefore be omitted.
  • the procedure according to the invention enables the cost-effective production of lightweight, heavy-duty steel strips and sheets, which form the starting material for the production of dimensionally stable components by cold forming, which is possible with little production outlay.
  • all variants of steel sheets according to the invention are particularly suitable for the production of body components, especially for the outer panels of an automobile body or load-bearing components for bodies, of wheels for vehicles, especially motor vehicles, of non-magnetic components, of containers used in cryotechnology, of internal high-pressure or extruded parts, of pipes intended in particular for the manufacture of high-strength engine parts, such as camshafts or piston rods, for impulse-type protection, such as bombardment, certain components or protective elements, such as armor plating, or body armor for the human or animal body.
  • Table 1 shows the compositions of steels A, B, C, D, E and VI, of which the steels AE belong to the steels processed in accordance with the invention, while the steel VI is indicated for comparative purposes only.
  • the steels are each melted and cast in the DSC process to Vorb skilledn.
  • the melt has been passed through a distribution channel on a circulating, strongly cooled conveyor on which it has been additionally intensively cooled by an acting from above liquid cooling.
  • the thus solidifying on the conveyor belt to the pre-band melt is then removed from the conveyor belt and have been subjected in the immediately subsequent passage still a second cooling.
  • the steel strips emerging from the second cooling and still having a sufficiently high temperature are in turn immediately thereafter, taking advantage of the inherent heat with a thickness of 2 mm hot rolled, the hot rolling end temperature was 900 0 C.
  • the hot strips thus obtained were then coiled at a reel temperature of 500 0 C to form a coil.
  • cold rolling was carried out, in which the hot strips with a degree of deformation of about 62.5% were formed into a cold strip whose thickness was 0.75 mm.
  • the cold strips were then recrystallized annealed at temperatures of 950 0 C.
  • the steel strips A - E produced from the steels A - E in the manner according to the invention have an excellent cold workability coupled with a high degree of cold workability Have strength and high elongation at break. At the same time they each have a pronounced isotropic behavior. As such, they are particularly suitable for being cold-forged into components that are subjected to high forces in practical use.
  • the property profile of KC given in Tab. 2 is worse than that of KVl, which is due to the weakly formed TWIP effect.
  • the advantage of KC over KVl lies in the high density reduction due to the high Al content.
  • the comparable steel Vl with TRIP properties has high strengths with comparatively low A80 and Ag values, which represent a significantly lower formability. This significantly poorer deformation behavior is also reflected in the significantly lower r and ⁇ r values compared to steels A - E.

Abstract

Procédé de fabrication de bandes ou tôles d'acier déformables à froid et extrêmement résistantes possédant des propriétés de déformation plastique par maclage (TWIP), selon lequel les étapes de travail successives se suivent sans interruption. Selon ledit procédé, une masse fondue possède la composition suivante (en % en poids): C: 0,003 - 1,50 %, Mn: 18,00 - 30,00 %, Ni: = 10,00 %, Si: = 8,00 %, Al: = 10,00 %, Cr: = 10,00 %, N: = 0,60 %, Cu: = 3,00 %, P: = 0,40 %, S: = 0,15 %, sélectivement un ou plusieurs éléments du groupe Se, Te, V, Ti, Nb, B, REM, Mo, W, Co, Ca et Mg, à condition que la somme des teneurs en Se, Te soit = à 0,25 %, que la somme des teneurs en V, Ti, Nb, B, REM soit = à 4,00 %, que la somme des teneurs en Mo, W, Co soit = à 1,50 % et que la somme des teneurs en Ca, Mg soit = à 0,50 %, le reste étant du fer et les impuretés dues à la production d'acier, les teneurs en Sn, Sb, Zr, Ta et As dont la somme ne dépasse pas 0,30 % étant comprises dans lesdites impuretés. Ladite composition est appliquée sur une bande transporteuse et refroidie sur ladite bande jusqu'à se solidifier en une bande préalable, la bande est retirée de la bande transporteuse, la bande préalable retirée est soumise au besoin à un traitement thermique, ladite bande préalable est laminée à chaud à une température de laminage à chaud d'au moins 700 °C, ce qui permet d'obtenir un feuillard à chaud à structure totalement recristallisée, et le feuillard à chaud est dévidé à une température de dévidage allant jusqu'à 750 °C.
PCT/EP2004/012407 2004-11-03 2004-11-03 Bande ou tole d'acier extremement resistante a proprietes twip et procede de fabrication de ladite bande a l'aide de la 'coulee directe de bandes' WO2006048034A1 (fr)

Priority Applications (6)

Application Number Priority Date Filing Date Title
PCT/EP2004/012407 WO2006048034A1 (fr) 2004-11-03 2004-11-03 Bande ou tole d'acier extremement resistante a proprietes twip et procede de fabrication de ladite bande a l'aide de la 'coulee directe de bandes'
BRPI0419185-4A BRPI0419185A (pt) 2004-11-03 2004-11-03 chapa ou fita de aço de resistência superior, apresentando propriedades twip, e processo para sua fabricação por meio de "direct strip casting"
EP04797547A EP1807542A1 (fr) 2004-11-03 2004-11-03 Bande ou tole d'acier extremement resistante a proprietes twip et procede de fabrication de ladite bande a l'aide de la "coulee directe de bandes"
US11/718,498 US20090010793A1 (en) 2004-11-03 2004-11-03 Method For Producing High Strength Steel Strips or Sheets With Twip Properties, Method For Producing a Component and High-Strength Steel Strip or Sheet
CN200480044461.3A CN101065503A (zh) 2004-11-03 2004-11-03 具有twip性能的高强度钢带或薄钢板以及通过钢带连铸制备它的方法
JP2007539465A JP2008519160A (ja) 2004-11-03 2004-11-03 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

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/EP2004/012407 WO2006048034A1 (fr) 2004-11-03 2004-11-03 Bande ou tole d'acier extremement resistante a proprietes twip et procede de fabrication de ladite bande a l'aide de la 'coulee directe de bandes'

Publications (1)

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WO2006048034A1 true WO2006048034A1 (fr) 2006-05-11

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Country Status (6)

Country Link
US (1) US20090010793A1 (fr)
EP (1) EP1807542A1 (fr)
JP (1) JP2008519160A (fr)
CN (1) CN101065503A (fr)
BR (1) BRPI0419185A (fr)
WO (1) WO2006048034A1 (fr)

Cited By (19)

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WO2009090228A1 (fr) * 2008-01-17 2009-07-23 Technische Universität Bergakademie Freiberg Composants en acier moulé solide et ductile, à forte teneur en manganèse, procédé de production et utilisation de ceux-ci
WO2011068328A2 (fr) * 2009-12-04 2011-06-09 주식회사 포스코 Tôle d'acier laminée à froid à traiter présentant une excellente résistance à la chaleur, et procédé de production de celle-ci
US20110308673A1 (en) * 2008-11-12 2011-12-22 Voestalpine Stahl Gmbh Manganese steel strip having an increased phosphorous content and process for producing the same
CN102418032A (zh) * 2011-12-09 2012-04-18 北京科技大学 一种增强孪晶诱导塑性高锰钢板强塑积的退火制备工艺
EP2757164A1 (fr) * 2013-01-16 2014-07-23 Volkswagen Aktiengesellschaft Dispositif de réglage à forte capacité de charge, notamment dispositif de réglage de siège à base de FeMn
CN104148900A (zh) * 2014-08-13 2014-11-19 权明勇 一种环形钢带的加工工艺
CN104254632A (zh) * 2012-04-24 2014-12-31 杰富意钢铁株式会社 高强度薄钢板及其制造方法
DE102013108163A1 (de) * 2013-07-30 2015-02-05 Benteler Defense Gmbh & Co. Kg Verfahren zur Herstellung eines Panzerungsbauteils für ein Kraftfahrzeug
US8999085B2 (en) * 2005-12-26 2015-04-07 Posco High manganese steel strips with excellent coatability and superior surface property, coated steel strips using steel strips and method for manufacturing the steel strips
CN104846269A (zh) * 2015-05-05 2015-08-19 柳州金特新型耐磨材料股份有限公司 一种挖掘机用耐磨钢主刀板
WO2015158328A1 (fr) * 2014-04-17 2015-10-22 Salzgitter Flachstahl Gmbh Procédé de calcul de la combinaison de propriétés qui s'établit pour un acier de construction légère déformable
CN106191404A (zh) * 2016-08-03 2016-12-07 中国科学院力学研究所 一种高强度高塑性twip钢的制备方法
WO2017068008A1 (fr) * 2015-10-21 2017-04-27 Salzgitter Flachstahl Gmbh Tube composite constitué d'un tube de support et d'au moins un tube de protection et procédé de fabrication associé
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DE102017119076A1 (de) * 2017-08-21 2019-02-21 Benteler Steel/Tube Gmbh Hydraulik- oder Pneumatikleitungsrohrelement und Verwendung einer Stahllegierung zur Herstellung
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CN114606430A (zh) * 2022-03-01 2022-06-10 兴机电器有限公司 一种低碳Fe-Mn-Al-Si系TWIP钢及其制备方法

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