EP1319091B1 - Verfahren zum herstellen eines überwiegend aus mn-austenit bestehenden stahlbands oder -blechs - Google Patents

Verfahren zum herstellen eines überwiegend aus mn-austenit bestehenden stahlbands oder -blechs Download PDF

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Publication number
EP1319091B1
EP1319091B1 EP01978372A EP01978372A EP1319091B1 EP 1319091 B1 EP1319091 B1 EP 1319091B1 EP 01978372 A EP01978372 A EP 01978372A EP 01978372 A EP01978372 A EP 01978372A EP 1319091 B1 EP1319091 B1 EP 1319091B1
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EP
European Patent Office
Prior art keywords
max
steel
strip
casting
thin strip
Prior art date
Legal status (The legal status 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 status listed.)
Expired - Lifetime
Application number
EP01978372A
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German (de)
English (en)
French (fr)
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EP1319091A1 (de
Inventor
Gabriele BRÜCKNER
Wolfgang Schlump
Hans-Joachim Krautschick
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Outokumpu Nirosta GmbH
Original Assignee
ThyssenKrupp Nirosta GmbH
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Publication date
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Publication of EP1319091A1 publication Critical patent/EP1319091A1/de
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Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
    • B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
    • 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
    • C22C38/001—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
    • C22C38/06—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
    • C22C38/38—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
    • 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

Definitions

  • the invention relates to a method for producing a steel strip or sheet consisting predominantly of Mn austenite.
  • Steels that are suitable for the production of such products are assigned to the AISI 200 and have there designation S20100 to S24000.
  • Steel materials of this type are characterized by a high strength, which is maintained after welding in the weld area.
  • interstitial and substitutional solid solution hardening are carbon and nitrogen.
  • carbon and nitrogen are preferably used for interstitial solid solution hardening in steels of the type in question.
  • the production of steels with an increased nitrogen content is complicated in relation to the alloy constituents or the equipment required for the production.
  • a further increase in the strength of steels of the above-mentioned, conventionally castable steels can be achieved by alloying aluminum and / or silicon. These two elements promote solid-solution hardening, leading to a further increase in strength.
  • the addition of aluminum and silicon can influence the stacking fault energy, which in turn has an influence on the deformation processes.
  • the addition of aluminum results in an increase in stacking fault energy and favors twinning formation.
  • Silicon lowers the stacking fault energy but favors deformation about martensite formation.
  • the combined addition of silicon and aluminum can thus be used to influence the solidification of the material during deformation. The formation of martensite leads to a high degree of solidification, while twinning reduces the solidification.
  • US Pat. No. 4,946,644 discloses a possibility of likewise producing a conventional slab-based production of a high-manganese-containing steel which at the same time has high nitrogen concentrations.
  • the known steel contains 13 - 17% Cr, 8 - 12% Mn, 0.05 - 0.2% C, 0.15 - 0.23% N, ⁇ 1.5% Ni, ⁇ 1% Si, ⁇ 1 % Cu, balance Fe and unavoidable impurities.
  • the problem of potting such a composite steel has not been dealt with. Instead, it has only been found in US 4,946,644 that a steel containing 14% Cr, 10% Mn and 0.11% C at a nitrogen content of 0.23% showed undesirable porosities. Therefore, in this prior art, the nitrogen content has been limited to 0.16-0.22%.
  • the object of the invention is to provide a method for producing a predominantly Mn austenite steel, which can be produced inexpensively and at the same time has an increased strength compared to the prior art,
  • This object is achieved by a method for producing a steel strip (W) or sheet consisting predominantly of Mn austenite, in which a steel is melted containing (in% by weight) the following alloying constituents: 15.00 - 24.00% Cr, 5.00 - 12.00% Mn, 0.10 - 0.60% N, 0.01 - 0.2% C, Max. 0.07% P, Max. 0.05% S, Max. 0.5% Nb, Max. 0.5% V, Max. 3.0% Ni, Max. 5.0% Mo, Max.
  • the thickness of the thin strip is between 1 and 5 mm.
  • the specification of the steel composition used according to the invention also includes in principle those alloys in which the content of those alloying elements is equal to zero, to which only a maximum permissible upper limit of the content is specified.
  • the chromium content of the steel may be 17.00-21.00% by weight Cr, the manganese content may be 8.00-12.00% by weight Mn and / or the nitrogen content limited to 0.40-0.60 wt% N be.
  • levels of Ni, Mo and / or Cu can be present in the steel.
  • the contents of the alloying elements contained in the steel composition used according to the invention are each optimized with regard to the effect of these elements.
  • Cr, Mn, Mo, V, Nb and Al increase the nitrogen solubility in the melt, while Ni, Cu as the austenite former and Si lower the nitrogen solubility.
  • Si simultaneously acts as a mixed-crystal hardener.
  • Al increases the stacking fault energy.
  • Mo also acts as a mixed crystal hardener and improves the corrosion behavior.
  • V also has a grain-refining effect and increases strength.
  • the addition of Nb leads to an increase in strength through precipitation hardening.
  • the invention makes use of the generally known technique of a strip casting plant by casting the steel in the casting gap formed between the rolls or rolls of, for example, a double-roller casting apparatus, thereby cooling it to such an extent that it causes a displacement of primary ferritic to toward primary austenitic solidification comes.
  • This makes it possible to transfer the nitrogen dissolved in the melt into the steel, because the austenite has a high solubility for nitrogen.
  • the possibility of such intensive cooling is only opened by the casting of a thin strip in a casting gap, whose walls, which are formed by the casting rolls or rollers, move at substantially the same speed as the cast strip, so that a constant, intensive heat exchange between the walls (casting rolls / roller) and the cast steel in the casting gap is ensured.
  • the intensive, with high cooling rate cooling ensures that possibly formed in the solidifying melt nitrogen gas bubbles remain small and the pressure directed against them is large. This prevents outgassing of the nitrogen in the course of solidification.
  • such leakage of nitrogen is suppressed by the high ferrostatic pressure that occurs due to the high height of the melt pool in the casting gap. In this way, it is ensured that the pressure P N in the possibly formed nitrogen gas bubbles is always smaller than the sum of the ambient pressure P A , the ferrostatic pressure P F and twice the surface tension ⁇ of the gas bubbles relative to the bubble radius r (ie P N ⁇ P A + P F + 2 ⁇ / r).
  • the rapid solidification of the cast strip during strip casting thus opens up great freedom, particularly in connection with steels of the type used according to the invention, with regard to the choice of the steel composition.
  • the rapid solidification of larger amounts of nitrogen can be solved. Alloying elements that improve the material properties can therefore be added in larger quantities, regardless of their possibly negative influence on the nitrogen solubility, than in conventional production methods. If, for example, the steel contains higher amounts of Si, then this is the case in conventional production due to the slow solidification and the associated increased Ferritoul existing danger of outgassing of nitrogen prevented according to the inventive approach.
  • the rapid cooling provided according to the invention avoids the formation of AlN, which sets in with slower cooling.
  • the invention makes it possible, by suitable choice of the Al and Si contents, to adjust the deformation mechanism of the respectively used alloy in a targeted manner in such a way that an end product with optimized properties is obtained.
  • the cost advantage achieved by the invention in the processing of steels of the type used according to the invention that are difficult to form is considerable. This applies both to those up to 7.5 wt .-% Mn-containing steels that can be cast in conventional continuous casting, as well as for such more than 7.5 wt .-% Mn-containing steels that are conventionally cast only in the block casting and can then be rolled in several rolling passes with any necessary reheating to the desired final thickness.
  • Hot strip made of extrudable alloy can currently only be produced on a conventional hot strip mill with a minimum thickness of 3.5 mm.
  • the production of cold strip in the typical target thickness of 0.8 - 1.2 mm can only be achieved by intermediate annealing.
  • an intermediate annealing is no longer necessary due to the smaller thickness of the hot strip obtained.
  • the procedure according to the invention makes it possible to produce steel strips and sheets which have particularly high nitrogen contents of 0.4 to 0.6% by weight and which are simultaneously alloyed with up to 3% aluminum and / or silicon, without the need for steel production must be carried out under pressure or particularly high levels of manganese are required.
  • the steel products produced in this way have a fine-grained, isotropic microstructure with a low macrosegregation or a small number of coarse inclusions. Due to its Al and / or Si content, they also have an increased strength and ductility compared with the prior art.
  • the solidification and thus the energy absorption during deformation can be set in a targeted manner by the choice of alloy.
  • the casting of the thin strip takes place under a protective gas atmosphere.
  • inert gas By casting under inert gas can be easily produce a thin strip with a modified surface, the degree of oxidation can be influenced in a targeted manner. Thus, a scale formation can be avoided.
  • the strip thus obtained can then be hot rolled in-line without the risk of sticking of the rolls in a roll stand. It is particularly advantageous in this context if the thin strip is heated to a rolling start temperature before hot rolling. Due to this temperature increase, higher degrees of deformation can be achieved during hot rolling.
  • the hot strip By subjecting the hot strip to a heat treatment after hot rolling, its microstructure can be optimized in a targeted manner.
  • the heat treatment may include annealing and subsequent controlled cooling.
  • steel sheets produced in accordance with the invention are particularly suitable for the production of body panel parts, in particular in general vehicle construction and stiffening structural components used especially in automobile construction, of chassis parts, of vehicle wheels and of fuel tanks.
  • the particularly good strength properties of steel sheets produced by the process according to the invention have an advantageous effect.
  • the good corrosion resistance of steel sheets and strips according to the invention proves to be advantageous in those uses where they come in contact with aggressive media such as fuels.
  • the single FIGURE schematically shows a strip casting plant 1.
  • a steel is processed, which in addition to the usual unavoidable impurities (in wt .-%) 0.08% C, 0.5% Si, 10% Mn, 19% Cr, 0.5% N , 0.3% Al and the balance iron.
  • the strip casting plant 1 comprises a two-roller casting apparatus, referred to as a "double roller", of which the rolls 2, 3, which are rotating in opposite directions about an axis of rotation, are shown in the figure. Between the rollers 2, 3 a casting gap 4 is formed, which is continuously filled with melt, so that above the casting gap 4 a melt pool S is formed.
  • the rollers 2,3 are intensively cooled during the casting process, so that the entering into the casting gap 4 melt with cooling rates of more than 200 K / s primary austenitic solidifies and the casting gap 4 as a thin strip D with a thickness of 1 to 5 mm leaves.
  • the thin strip D thus produced then passes through an oven 5 in which it is heated to a rolling start temperature.
  • Both the two-roll casting device with the rollers 2, 3 as well as the furnace 5 are accommodated in an enclosure 6, in which a protective gas atmosphere is contained.
  • a protective gas atmosphere is contained.
  • the thin strip D heated to initial rolling temperature enters a rolling mill 7 in which it is hot-rolled to a final size. Due to the high rolling start temperature, large degrees of deformation are possible.
  • the hot strip W rolled from the thin strip D which essentially reaches the rolling mill without any scale, has a particularly high-quality surface after hot rolling.
  • the hot strip W is annealed in a continuous annealing furnace 8 and then controlled cooled under a cooling device 9 in order to improve its structure targeted.
  • the thus heat-treated hot strip W is finally wound into a reel 10.
  • Steel strip produced in the above-described manner has particularly high strength with respect to conventionally assembled and produced steel strips due to its high nitrogen content achieved by the rapid cooling between the rollers 2, 3 of the two-roll casting apparatus and at the same time good formability and energy absorption capacity.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Continuous Casting (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Metal Rolling (AREA)
  • Heat Treatment Of Articles (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
EP01978372A 2000-09-19 2001-09-14 Verfahren zum herstellen eines überwiegend aus mn-austenit bestehenden stahlbands oder -blechs Expired - Lifetime EP1319091B1 (de)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
DE10046181 2000-09-19
DE10046181A DE10046181C2 (de) 2000-09-19 2000-09-19 Verfahren zum Herstellen eines überwiegend aus Mn-Austenit bestehenden Stahlbands oder -blechs
PCT/EP2001/010645 WO2002024969A1 (de) 2000-09-19 2001-09-14 Verfahren zum herstellen eines überwiegend aus mn-austenit bestehenden stahlbands oder -blechs

Publications (2)

Publication Number Publication Date
EP1319091A1 EP1319091A1 (de) 2003-06-18
EP1319091B1 true EP1319091B1 (de) 2007-01-03

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EP01978372A Expired - Lifetime EP1319091B1 (de) 2000-09-19 2001-09-14 Verfahren zum herstellen eines überwiegend aus mn-austenit bestehenden stahlbands oder -blechs

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Country Link
US (1) US20040025979A1 (enrdf_load_stackoverflow)
EP (1) EP1319091B1 (enrdf_load_stackoverflow)
JP (1) JP2004509762A (enrdf_load_stackoverflow)
KR (1) KR100748256B1 (enrdf_load_stackoverflow)
CN (1) CN100357478C (enrdf_load_stackoverflow)
AT (1) ATE350504T1 (enrdf_load_stackoverflow)
AU (1) AU2002210506A1 (enrdf_load_stackoverflow)
BR (1) BR0113950A (enrdf_load_stackoverflow)
DE (2) DE10046181C2 (enrdf_load_stackoverflow)
ES (1) ES2279831T3 (enrdf_load_stackoverflow)
TW (1) TW522060B (enrdf_load_stackoverflow)
WO (1) WO2002024969A1 (enrdf_load_stackoverflow)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2163659A1 (de) 2008-09-11 2010-03-17 ThyssenKrupp Nirosta GmbH Nichtrostender Stahl, aus diesem Stahl hergestelltes Kaltband und Verfahren zur Herstellung eines Stahlflachprodukts aus diesem Stahl
DE102015005742A1 (de) 2015-05-05 2016-11-10 Dbi Gas- Und Umwelttechnik Gmbh Verfahren zur Herstellung von Feinblech aus einem nichtrostenden, austenitischen CrMnNi-Stahl

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US7485196B2 (en) * 2001-09-14 2009-02-03 Nucor Corporation Steel product with a high austenite grain coarsening temperature
AT501044B8 (de) 2004-10-29 2007-02-15 Voest Alpine Ind Anlagen Verfahren zum herstellen eines gegossenen stahlbandes
AT504782B1 (de) * 2005-11-09 2008-08-15 Siemens Vai Metals Tech Gmbh Verfahren zur herstellung eines warmgewalzten stahlbandes und kombinierte giess- und walzanlage zur durchführung des verfahrens
US8182963B2 (en) * 2009-07-10 2012-05-22 GM Global Technology Operations LLC Low-cost manganese-stabilized austenitic stainless steel alloys, bipolar plates comprising the alloys, and fuel cell systems comprising the bipolar plates
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CN101812646B (zh) * 2010-04-22 2011-09-07 河北工业大学 轧辊用高速钢合金的铸造工艺
CN103614659A (zh) * 2013-10-22 2014-03-05 芜湖市鸿坤汽车零部件有限公司 一种内燃机用奥氏体合金钢材料及其制备方法
KR101622705B1 (ko) * 2014-08-06 2016-05-23 한국기계연구원 내공식성이 우수한 오스테나이트계 스테인리스 강
US9975170B2 (en) * 2014-12-11 2018-05-22 Posco Method for manufacturing duplex stainless steel sheet having high nitrogen content and good surface quality
DE102016211411A1 (de) * 2016-06-24 2017-12-28 Thyssenkrupp Ag Fahrzeugrad und Verwendung
US10960487B2 (en) * 2017-09-21 2021-03-30 United States Steel Corporation Weldability improvements in advanced high strength steel
CN108179364B (zh) * 2017-12-28 2019-05-31 钢铁研究总院 一种具有高碰撞吸收能的合金结构钢及其制备方法
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CN110484833A (zh) * 2019-08-21 2019-11-22 首钢集团有限公司 一种高铬低锰奥氏体钢及其制备方法
CN111876670B (zh) * 2020-06-30 2021-11-09 九牧厨卫股份有限公司 一种高硬度耐刮不锈钢、不锈钢水槽及其制备方法
CN112974532B (zh) * 2021-02-05 2023-01-31 山西太钢不锈钢股份有限公司 一种超高氮奥氏体不锈钢热连轧卷板的轧制方法
CN115368760A (zh) * 2022-07-20 2022-11-22 江苏甬金金属科技有限公司 一种抗菌奥氏体不锈钢带的加工工艺
EP4316727A1 (en) 2022-08-05 2024-02-07 Outokumpu Oyj Filler metal for welding of dissimilar welds
CN117845127A (zh) * 2023-05-12 2024-04-09 江苏工程职业技术学院 一种高氮低镍的奥氏体合金材料及合金盘条
CN119663138B (zh) * 2024-12-13 2025-08-29 中南大学 一种高Cu含量的200系不锈钢及其薄带的连铸制备方法

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Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2163659A1 (de) 2008-09-11 2010-03-17 ThyssenKrupp Nirosta GmbH Nichtrostender Stahl, aus diesem Stahl hergestelltes Kaltband und Verfahren zur Herstellung eines Stahlflachprodukts aus diesem Stahl
US8608873B2 (en) 2008-09-11 2013-12-17 Outokumpu Nirosta Gmbh Stainless steel, cold strip produced from this steel, and method for producing a flat steel product from this steel
DE102015005742A1 (de) 2015-05-05 2016-11-10 Dbi Gas- Und Umwelttechnik Gmbh Verfahren zur Herstellung von Feinblech aus einem nichtrostenden, austenitischen CrMnNi-Stahl

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ES2279831T3 (es) 2007-09-01
CN1659300A (zh) 2005-08-24
DE50111818D1 (de) 2007-02-15
JP2004509762A (ja) 2004-04-02
ATE350504T1 (de) 2007-01-15
CN100357478C (zh) 2007-12-26
KR100748256B1 (ko) 2007-08-10
US20040025979A1 (en) 2004-02-12
KR20030051660A (ko) 2003-06-25
BR0113950A (pt) 2003-07-22
TW522060B (en) 2003-03-01
EP1319091A1 (de) 2003-06-18
DE10046181A1 (de) 2002-04-04
DE10046181C2 (de) 2002-08-01
WO2002024969A1 (de) 2002-03-28
AU2002210506A1 (en) 2002-04-02

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