EP1469954B2 - Verfahren zur herstellung von warmband aus austenitischen nichtrostenden stählen - Google Patents

Verfahren zur herstellung von warmband aus austenitischen nichtrostenden stählen Download PDF

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Publication number
EP1469954B2
EP1469954B2 EP03702404A EP03702404A EP1469954B2 EP 1469954 B2 EP1469954 B2 EP 1469954B2 EP 03702404 A EP03702404 A EP 03702404A EP 03702404 A EP03702404 A EP 03702404A EP 1469954 B2 EP1469954 B2 EP 1469954B2
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EP
European Patent Office
Prior art keywords
rolling
temperature
stage
carried out
heat
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
EP03702404A
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German (de)
English (en)
French (fr)
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EP1469954A1 (de
EP1469954B1 (de
Inventor
Ingo Schuster
Manfred Albedyhl
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.)
SMS Siemag AG
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SMS Demag AG
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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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B1/24—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process
    • B21B1/26—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process by hot-rolling, e.g. Steckel hot mill
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/46—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting
    • B21B1/466—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting in a non-continuous process, i.e. the cast being cut before rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/16—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling wire rods, bars, merchant bars, rounds wire or material of like small cross-section
    • B21B1/18—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling wire rods, bars, merchant bars, rounds wire or material of like small cross-section in a continuous process
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B3/02—Rolling special iron alloys, e.g. stainless steel
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
    • B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B45/00—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
    • B21B45/004—Heating the product
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling

Definitions

  • the invention relates to a method for producing hot strip of austenitic stainless steels, wherein in a first step, a cast product is subjected to a rolling operation in a rolling mill with a finishing train and in a second step, a heat treatment to prevent corrosion susceptibility, in particular with respect to an intercrystalline corrosion due to Chromium carbide precipitates, is performed.
  • austenitic stainless steels among which steel grades of at least 10.5% chromium and nickel are generally found, are particularly susceptible to intergranular corrosion due to chromium depletion of the near-comer regions of the structure during formation chromium-rich precipitates on the grain boundaries and the associated reduction in the corrosion resistance of these areas against microstructure areas with high content of dissolved chromium based. This happens in particular if they pass through critical Temperaur Schemee during cooling too slowly. Therefore, such austenitic Cr-Ni steels are adjusted in the solution-annealed and quenched state.
  • solution annealing with subsequent quenching is a heat treatment in which at solution annealing temperatures between about 1,000 and 1,100 ° C, the chromium of the precipitated Cr carbides goes back into solution and is prevented by the subsequent quenching that form again chromium carbides by keeping the C atoms in forced solution in the matrix.
  • solution annealing followed by quenching is carried out in a separate from the rolling heat treatment process.
  • the rolled products are transported to separate heat treatment plants and subjected there for the heat treatment of annealing and rapid cooling.
  • solution heat treatment also improves the cold formability of austenitic Cr-Ni steels.
  • From the EP 0 415 987 B2 is a process for the continuous production of strip steel or steel sheet from thin strip of about 50 mm thickness produced by sheet casting with horizontal discharge direction with the process steps rolling the thin slab after solidification of the strand in the arcuate guide shaft at temperatures of more than 1100 ° C, temperature drop of Slabs by radiation or Entzundem, inductive reheating to a temperature of about 1,100 ° C and rolling the thin slab in at least one rolling mill known.
  • a temperature is set in the slabs, so that adjusts a temperature gradient at the deformation means of the rolling train in such a way that when tapping into the last roll stand, the temperature is within a sufficient deformation for a good order.
  • the rolling stock temperature has dropped, for example, to 988 ° C and sufficient as a tapping temperature for the last rolling.
  • the rolling stock leaves the last stand with a temperature of 953 ° C or less and is then separated at further lowered temperature in desired lengths and stacked or reeled.
  • the outlet temperature from the roller hearth furnace is about 1,100 ° C.
  • the heat energy required for the rolling process is thus almost completely covered by the amount of heat contained in the cast strand.
  • the heat losses are controlled by cooling in the rolling train and from the roller contact, so that sets a desired final rolling temperature, for example, 880 ° C. This is followed by a slow cooling in the cooling section and a subsequent coiling.
  • Both known methods have in common that a slab temperature is set as the inlet temperature in the finishing stand, which is just sufficient to ensure rolling in the last frame of the finishing train.
  • the invention has for its object to propose a method by which austenitic stainless steels can be produced while saving energy and time.
  • the heat treatment to prevent susceptibility to corrosion is carried out directly from the rolling heat, ie immediately after the rolling process by utilizing the The fact that the temperatures in the belt are so high that no Cr carbides are eliminated or that, starting from the rolling temperatures, only very small temperature differences have to be overcome in order to set temperatures for dissolution of the chromium.
  • the rolled product is no longer solution heat treated in a separate heat treatment step, which includes annealing from room temperature to solution annealing temperature, but using the rolling heat and thus saving the high energy annealing process.
  • the steels can therefore be produced without subsequent separately performed heat treatment, consisting of solution annealing and quenching treatment, while saving energy and time.
  • this desired relatively high final rolling temperature at the end of the finishing train is achieved by setting a higher inlet temperature of the cast product in the finishing mill of the rolling mill, which is above 1,150 ° C., preferably above 1,200 ° C. Then, the temperature level of the rolling stock despite the temperature gradient during the rolling process is always above the temperature at which Cr carbides could excrete.
  • the cast product is subjected to a multi-stage, in particular two-stage, heating, which comprises a preheating stage and an intensive heating stage.
  • the final rolling temperature of the rolling stock is set at temperatures above 1000 ° C, preferably above 1050 ° C, i.e., at temperatures above 1000 ° C. at temperatures at which the carbide precipitate chromium of the chromium-containing stainless steels is in solution.
  • the final rolling temperature should be at a level at which no precipitate Cr carbides, but in which the structure still recrystallized.
  • the term final rolling temperature refers to the temperature of the rolling stock in the last or last stands of the finishing train.
  • the rolling stock is quenched to temperatures below 600 ° C, preferably below 450 ° C, with a precipitation of particular Cr carbides is suppressed.
  • the temperature of the cast product is set to values between 1000 and 1150 ° C., wherein the temperature is raised to values of above 1200 ° C. only in the subsequent intensive heating zone.
  • the pre-heat stage is preferably carried out in a gas- or oil-heated oven and the subsequent intensive heating stage in an induction oven or in an induction heating zone.
  • the slab temperature is increased to temperatures between 1,000 and 1,150 ° C without exceeding the load capacity of the furnace elements.
  • the casting product surface in particular the slab surface
  • a Entzu minimums device is provided between the Vorümlab and the Intensivffymark.
  • the inlet temperature is then set in the inductive intensive heating zone. It is also proposed, in addition or alone, to carry out a descaling even before the roller hearth of the preheating to protect the roles of the furnace from scale and thus the surfaces of the slabs against unwanted scale marks and to improve the heat transfer into the slab.
  • the rolling stock with the defined final rolling temperature is passed through a - preferably inductive heating section adjoining the finishing line for further holding at temperatures at which accelerated recrystallization processes take place and only then is quenched.
  • This heating section can be used when it is determined that the desired Endwalztemperatur despite high inlet temperatures could not be achieved, for example by an unwanted unfavorable rolling process.
  • Fig. 1 shows a plant for the production of sheets or strips of chromium and nickel alloyed steel grades, which are rolled without cooling to room temperature and heat treated, so that the final product is already solution-annealed and quenched available.
  • Such a plant 1 comprises a continuous casting plant 2, which is shown here schematically with the aid of a ladle 3 for the molten steel, a distributor 4 and a mold 5.
  • the near-final cast strand or cast product 6 is cut into slabs in front of the roller hearth furnace or preheating furnace 7 with the aid of scissors 8, and these then enter the furnace 7 in order to be heated to temperatures of between 1,000 and 1,150 ° C. to experience a temperature compensation.
  • the heated slabs pass through a descaling device 9, in order then to run into an inductive intensive heating zone 10.
  • the slabs are raised to temperatures in an interval of 1,000-1,300 ° C, preferably above 1,200 ° C, in a short, rapid heating process.
  • the temperature set in the intensive heating zone 10 must be sufficient to set the desired final rolling temperatures above 1000 ° C. Possibly. It may also be sufficient to heat to temperatures around 1000 ° C., provided that only a very small temperature loss occurs during the rolling process.
  • the preheating furnace 7 and the intensive heating zone 10 form the temperature adjusting system 11.
  • the means for performing the heat treatment are the preheating furnace 7 and the intensive heating zone 10 and the cooling section for rapid cooling.
  • the hot slabs are again descaled (second descaling device 12) and introduced into the finishing train 13, which here consists of six stands 13a-f.
  • the inlet temperatures are in the temperature range of 1,050-1,250 ° C, preferably at temperatures above 1,200 °. Temperatures of 1050 ° C are also adjustable, provided that the temperature loss in the rolling mill is low and the desired Endwalztemperaturen be achieved.
  • an emergency shear 14 is provided for incidents.
  • the temperatures of the slabs decrease by radiation and cooling, but do not sink to the end of the rolling train 13 to temperatures below 1000 to 1100 ° C, so that the chromium always remains in solution and no Cr carbides on the grain boundaries can excrete the structure and a complete recrystallization takes place.
  • the rolling stock 15 enters the means for cooling 16 or in a cooling section, the cooling parameters are set so that the rolling stock is cooled rapidly to temperatures in an interval of 400-650 ° C, preferably below 600 ° C, to keep the dissolved Cr atoms in forced solution.
  • the cooling section shown here is cooling bar 17 with water cooling, other types of cooling are also conceivable.
  • the thus rolled and already heat-treated and thus corrosion-resistant tape is reeled in a coiler 18.
  • Fig. 2 For comparison, the prior art casting-heat rolling apparatus is to be solution-annealed in a separate process.
  • Fig. 1 corresponding system parts are provided with corresponding reference numerals.
  • slab or strip temperatures which prevail or are set in the individual system parts are mentioned.
  • the cast product 106 is cut and then fed into an equalizing furnace 107 to be subsequently rolled. The held in a separate part of the plant with annealing solution annealing with subsequent quenching process is not shown.
  • the invention relates to austenitic stainless steels, ie steels having a mass fraction of at least 10.5% Cr and at most 1.2% C.
  • the invention is particularly directed to stainless steels in which intercrystalline corrosion by Cr depletion upon precipitation of Cr carbides is to be prevented.

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  • Engineering & Computer Science (AREA)
  • Chemical & Material Sciences (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Metal Rolling (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Pressure Welding/Diffusion-Bonding (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
EP03702404A 2002-01-31 2003-01-09 Verfahren zur herstellung von warmband aus austenitischen nichtrostenden stählen Expired - Lifetime EP1469954B2 (de)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
DE10203711A DE10203711A1 (de) 2002-01-31 2002-01-31 Verfahren und Anlage zur Herstellung von Warmband aus austenitischen nichtrostenden Stählen
DE10203711 2002-01-31
PCT/EP2003/000119 WO2003064069A1 (de) 2002-01-31 2003-01-09 Verfahren und anlage zur herstellung von warmband aus austenitischen nichtrostenden stählen

Publications (3)

Publication Number Publication Date
EP1469954A1 EP1469954A1 (de) 2004-10-27
EP1469954B1 EP1469954B1 (de) 2006-03-22
EP1469954B2 true EP1469954B2 (de) 2009-03-11

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ID=27588155

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EP03702404A Expired - Lifetime EP1469954B2 (de) 2002-01-31 2003-01-09 Verfahren zur herstellung von warmband aus austenitischen nichtrostenden stählen

Country Status (14)

Country Link
US (3) US7854884B2 (ja)
EP (1) EP1469954B2 (ja)
JP (1) JP4860110B2 (ja)
KR (1) KR100971902B1 (ja)
CN (1) CN1292847C (ja)
AT (1) ATE320866T1 (ja)
CA (1) CA2471481C (ja)
DE (2) DE10203711A1 (ja)
ES (1) ES2261914T5 (ja)
RU (1) RU2302304C2 (ja)
TW (1) TWI283613B (ja)
UA (1) UA78281C2 (ja)
WO (1) WO2003064069A1 (ja)
ZA (1) ZA200404829B (ja)

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DE102006054932A1 (de) 2005-12-16 2007-09-13 Sms Demag Ag Verfahren und Vorrichtung zum Herstellen eines Metallbandes durch Gießwalzen
JP5167145B2 (ja) * 2005-12-22 2013-03-21 アルヴェディ，ジョヴァンニ 鋼帯を非連続的に製造するための方法及びプラント
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DE102007005015A1 (de) * 2006-06-26 2008-01-03 Sms Demag Ag Verfahren und Anlage zur Herstellung von Warmband-Walzgut aus Siliziumstahl auf der Basis von Dünnbrammen
CN100435987C (zh) * 2006-11-10 2008-11-26 广州珠江钢铁有限责任公司 一种基于薄板坯连铸连轧流程采用Ti微合金化工艺生产700MPa级高强耐候钢的方法
CN101230413B (zh) * 2007-01-26 2012-07-04 宝山钢铁股份有限公司 含碳量较高的奥氏体不锈钢热轧卷板的热加工工艺
DE102008020412A1 (de) * 2007-08-24 2009-02-26 Sms Demag Ag Verfahren und Vorrichtung zum Herstellen eines Metallbandes durch Gießwalzen
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DE102009036378A1 (de) * 2009-08-06 2011-02-17 Sms Siemag Ag Verfahren und Vorrichtung zum Herstellen eines mikrolegierten Stahls, insbesondere eines Röhrenstahls
EP2441540A1 (de) 2010-10-12 2012-04-18 Siemens VAI Metals Technologies GmbH Verfahren und Anlage zur energieeffizienten Erzeugung von Stahlwarmband
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KR101417230B1 (ko) * 2011-12-28 2014-08-06 주식회사 포스코 배치 및 연연속 압연 겸용 시스템 및 압연 방법
TWI552812B (zh) * 2012-01-25 2016-10-11 Sms Group Gmbh 製造金屬帶的方法與設備
RU2482197C1 (ru) * 2012-03-07 2013-05-20 Федеральное государственное автономное образовательное учреждение высшего профессионального образования "Белгородский государственный национальный исследовательский университет" Способ деформационно-термической обработки аустенитных нержавеющих сталей
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DE50302735D1 (de) 2006-05-11
US7922840B2 (en) 2011-04-12
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CA2471481C (en) 2010-08-17
ATE320866T1 (de) 2006-04-15
JP4860110B2 (ja) 2012-01-25
ES2261914T3 (es) 2006-11-16
EP1469954A1 (de) 2004-10-27
DE10203711A1 (de) 2003-08-14
KR20040073597A (ko) 2004-08-19
WO2003064069A1 (de) 2003-08-07
CN1625447A (zh) 2005-06-08
UA78281C2 (en) 2007-03-15
RU2302304C2 (ru) 2007-07-10
ZA200404829B (en) 2005-02-23
US20090260728A1 (en) 2009-10-22
EP1469954B1 (de) 2006-03-22
ES2261914T5 (es) 2009-05-25
CA2471481A1 (en) 2003-08-07
RU2004126316A (ru) 2005-06-10
US20080000559A1 (en) 2008-01-03
US7854884B2 (en) 2010-12-21
TWI283613B (en) 2007-07-11
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CN1292847C (zh) 2007-01-03
US20050072499A1 (en) 2005-04-07

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