EP1228255A1 - Procede pour produire un feuillard a chaud - Google Patents

Procede pour produire un feuillard a chaud

Info

Publication number
EP1228255A1
EP1228255A1 EP00966035A EP00966035A EP1228255A1 EP 1228255 A1 EP1228255 A1 EP 1228255A1 EP 00966035 A EP00966035 A EP 00966035A EP 00966035 A EP00966035 A EP 00966035A EP 1228255 A1 EP1228255 A1 EP 1228255A1
Authority
EP
European Patent Office
Prior art keywords
temperature
strip
strand
hot
cold
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.)
Granted
Application number
EP00966035A
Other languages
German (de)
English (en)
Other versions
EP1228255B1 (fr
Inventor
Rudolf Kawalla
Bernhard Engl
Thomas Heller
Wolfgang Rasim
Eberhard Sowka
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.)
ThyssenKrupp Steel Europe AG
Original Assignee
ThyssenKrupp Stahl 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 Stahl AG filed Critical ThyssenKrupp Stahl AG
Publication of EP1228255A1 publication Critical patent/EP1228255A1/fr
Application granted granted Critical
Publication of EP1228255B1 publication Critical patent/EP1228255B1/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/041—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing involving a particular fabrication or treatment of ingot or slab
    • 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
    • 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
    • B22D11/04—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds
    • B22D11/041—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds for vertical casting
    • 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
    • B22D11/12—Accessories for subsequent treating or working cast stock in situ
    • B22D11/1213—Accessories for subsequent treating or working cast stock in situ for heating or insulating strands
    • 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
    • B22D11/16—Controlling or regulating processes or operations
    • B22D11/22—Controlling or regulating processes or operations for cooling cast stock or mould
    • B22D11/225—Controlling or regulating processes or operations for cooling cast stock or mould for secondary cooling
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—Hot rolling
    • 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
    • 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
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0436—Cold rolling

Definitions

  • the invention relates to a method for producing a hot strip, in particular for producing a hot strip intended for producing a good deep-drawing cold strip, from a low-carbon, low-alloy steel, in which thin slabs are produced by continuous casting, in which the strand emerging from a casting mold during continuous casting passes through a cooling section and in which the cast strand itself or thin slabs separated from the strand are reheated in a compensating furnace before they are hot-rolled into hot strip.
  • thin slabs are separated from a steel strand produced in a continuous casting plant and, after temperature compensation in a tunnel kiln, continuously rolled into hot strip in a multi-stand rolling mill.
  • the thin slabs generally enter the compensating furnace at a temperature between 950 ° C. and 1100 ° C. and are reheated therein to temperatures which are between 1100 ° C. and 1200 ° C.
  • the known method makes use of the heat present in the strand after casting Production of hot strip with an energy expenditure which is reduced compared to other conventional processes of this type.
  • the compensating furnace must be operated at very high temperatures. These high temperatures lead to premature wear of the furnace, which maintenance therefore consumes the energy savings achieved.
  • the high temperatures of the compensating furnace are required in the prior art in order to bring or keep the alloy components of the steel strand in solution, which cause the formation of precipitates in the course of the further process steps in the production of the hot strip or the cold strip produced therefrom, which decisively influence the formation of a certain structural structure of the finished hot strip or the cold strip produced therefrom.
  • EP 0 686 702 A1 discloses a modification of the above-described method, in which the surface temperature of the slab between the casting mold and the compensating furnace is reduced to such an extent that a structural transformation of austenite into ferrite / pearlite occurs in the slab , It is also stated that the temperatures reached at a depth of 2 mm below the slab surface are preferably less than 600 ° C.
  • the aim of the measures described in EP 0 686 702 AI is that slabs containing copper in the course of the addition of larger amounts of secondary scrap to the melt in significant amount a state in the equalization furnace, through which an excessive accumulation of copper in the region of the grain boundaries of the primary austenite is prevented. Otherwise, these accumulations cause severe scale formation and can lead to a so-called "solder break" in the further course of hot strip production.
  • the slabs By cooling the slabs to temperatures below the A r3 temperature (the temperature below which the austenite converts to ferrite), a structural change is forced with a reorientation of the austenite grain boundaries in the course of reheating in the compensating furnace.
  • the slabs cooled in this way are heated in the compensating furnace to the high temperatures usually set in the compensating furnace.
  • the depth of the cooling and the time provided for this are reduced to a minimum in the process known from EP 0 686 702 A1, so that the temperature inside the slab when it enters the compensating furnace is as high as possible.
  • the object of the invention is to reduce the required temperatures in the compensating furnace in a process of the type mentioned in the course of processing low-alloy, low-carbon steels so that the load on the furnace is reduced without sacrificing the quality of the hot strip produced or a cold strip made from it comes.
  • a method for producing a hot strip in particular for producing a hot strip intended for producing a cold strip which is capable of good deep drawing, in which a steel melt which (in mass%) C: ⁇ 0.07%, Si: ⁇ 0.5%, Mn: ⁇ 2.5%, AI: ⁇ 0.1%, N: ⁇ 0.01%, P: ⁇ 0.025, B: ⁇ 0.05, possibly up to a total of 0.35% Nb, Ti and V, and the balance contains iron and usual impurities, in which the molten steel is continuously discharged from a casting mold in one strand, in which the cast strand is passed through a cooling section immediately after emerging from the casting mold, in which the Strand is cooled intensively at a cooling rate of at least 3 K / s to a temperature of A r ⁇ i 25 K, in which the strand is cooled in air for at least 30 seconds following its intensive cooling, and in the strand itself or by thin slabs divided into a strand in a meadow be
  • the strand emerging from the casting mold of intensive cooling Cooling rates of at least 3 K s is exposed /, (is finished the temperature at which the transformation of austenite to ferrite) in which the strand below the A r ⁇ temperature is cooled, the the hot strip for the formation of the desired material properties are required
  • Excretions are specifically induced in the area that is to be upstream of the compensating furnace. There is so much time available during the subsequent cooling in air after the intensive cooling that the excretion processes have essentially expired when entering the compensating furnace. At the same time, the temperature in the strand is homogenized during this time, so that there is a uniform temperature distribution when entering the furnace.
  • the furnace temperature can be limited to temperatures which are lower than those required in the conventional procedure
  • the equalization furnace temperature to be maintained according to the invention is in a range whose lower limit is determined by the A r3 temperature and whose upper limit is 1150 ° C.
  • Reheating temperatures of a maximum of 1050 ° C. are sufficient if a cold strip is produced from the hot strip produced according to the invention, which is annealed in a continuous furnace after the cold rolling. In this case, preferably all during the Production of the hot and cold strip associated with the rewarming subsequent work steps no more precipitation processes take place, so that it is no longer necessary to dissolve alloy components involved in the formation of excretions.
  • the temperature when the strand or thin slabs are heated in the compensating furnace should be in the range from 1100 ° C. to 1150 ° C.
  • Al nitride dissolves to an extent which is sufficient to produce a desired “pancake” structure in the course of the hood annealing.
  • a strip produced in accordance with the invention has a fine-grained structure which has a favorable effect on the deep-drawing ability of a cold strip produced from the hot strip.
  • the invention thus provides a method which makes it possible to reduce the temperature in the compensating furnace, so that its service life is increased and the economy of the method is improved compared to the conventional procedure.
  • a method according to the invention provides a product which is outstandingly suitable for processing by deep drawing.
  • a plurality of pass passes are preferably carried out during hot rolling, the finished rolled hot strip having a thickness of 2 to 5 mm. It should a thickness decrease S> 15% can be achieved in the last pass of the rolling.
  • the hot-rolled strip rolled in this way has a particularly fine-grained structure, which further improves its deep-drawing ability.
  • the “change in shape ⁇ ” is understood to mean the ratio of the decrease in thickness during the last pass to the thickness of the strip as it enters the last rolling stand of the hot rolling mill.
  • the final rolling temperature at the end of hot rolling is preferably at least 20 ° C. above the A r3 temperature. If, however, after hot rolling a substantially ferritic microstructure of the hot strip are present, so the final rolling temperature is preferably at the completion of the hot rolling less than the A r ⁇ temperature + 50 ° C.
  • a further improvement in the microstructure of a cold strip produced from the hot strip produced according to the invention with regard to the deep-drawing properties can be achieved in that it was achieved during the cold rolling of the hot strip
  • Total shape change ⁇ total is at least 60%.
  • the "overall change in shape ⁇ tot" is understood here to mean the ratio of the decrease in thickness during cold rolling to the thickness of the unwrought strip as it enters the cold rolling stand.
  • a hot strip produced according to the invention has a thickness h 0, for example after hot rolling. After cold rolling, the thickness of the strip is reduced to hi.
  • the finished rolled hot strip produced from the hot strip is annealed in a continuous furnace after cold rolling, the finished rolled hot strip should be coiled at a coiling temperature of at least 650 ° C. By adhering to this minimum temperature, the formation of precipitates in the coiled hot strip is promoted, so that the recrystallization of the cold strip can proceed unhindered during the continuous annealing of the precipitates.
  • the finished rolled hot strip should first be coiled at a coiling temperature of at most 625 ° C. In this way, the rest of the alloy constituents still present in the dissolved state and involved in the formation of precipitates are kept in solution.
  • the precipitates are formed in the cold strip, which are required for the formation of the desired pancake structure of the cold strip.
  • Figure 1 shows the beginning of a production line for producing a hot strip from a cast steel strand in a side view.
  • Diag. 1 shows the course of the Arl and Ar3 temperatures as a function of the carbon content of a low-carbon steel
  • Diag. 2 shows the course of the temperature of the strand in the region of the start of a production line shown in FIG. 1.
  • a melt of a low-carbon, low-alloy steel is cast via a casting mold 1 to form a steel strand S between 20 and 70 mm thick.
  • the steel strand S is intensively cooled by cooling water, which is directed onto the steel strand S from cooling devices 2 arranged on both sides of the steel strand S, in the course of a “metallurgical length” LM.
  • the cooling rate a LM reached during the intensive cooling of the steel strand S within the metallurgical length LM is at least 3 K / s, the cooling rate a LM actually set being dependent on the respective thermal conductivity of the steel strand S and the required temperature T LM at the end of the metallurgical length LM.
  • the extent of the intensive cooling is in any case such that the steel strand S at the end of the metallurgical length LM has a temperature T LM of A r ⁇ ⁇ 25 ° C, for example 710 ° C.
  • T LM temperature of A r ⁇ ⁇ 25 ° C, for example 710 ° C.
  • the position of the A r ⁇ Temperature is given in function of the carbon content of the composition of the steel strand S.
  • the steel strand S runs on a roller table 3 through a cooling section LT, in which the steel strand S is cooled in air.
  • the steel strand S requires at least 30 seconds, so that at the end of the cooling section LT the formation of precipitates in the steel strand S is essentially complete and there is a homogeneous temperature distribution.
  • the steel strand S itself or thin slabs D divided by it by means of a dividing device 4 enter an equalizing furnace 5.
  • the steel strand S or the thin slabs D are heated to a reheating temperature T w which is above the A r3 temperature but below 1100 ° C.
  • the position of the A r3 temperature is also in Diag. 1 in Depends on the carbon content of the steel composition.
  • the temperature T w reached during the reheating in the compensating furnace 5 depends on the annealing treatment which is carried out during the further processing of the hot strip produced from the steel strand S or the thin slabs D into cold strip. If the cold-rolled cold-rolled strip is subjected to a hood anneal, the reheating temperature T w is in the range of 1100 ° C. If, on the other hand, the cold strip passes through a continuous anneal, the reheating temperature T w is approx. 1000 ° C.

Landscapes

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

Abstract

L'invention concerne un procédé pour produire un feuillard à chaud destiné à produire un feuillard à froid présentant une bonne aptitude à l'emboutissage. Ce procédé consiste à faire fondre un acier qui contient les composants suivants (en % en poids) : C: </= 0,07 %, Si: </= 0,5 %, Mn: </= 2,5 %, Al: </= 0,1 %, N: </= 0,01 %, P: </= 0,025, B: </= 0,05, et qui présente éventuellement une teneur en Nb, Ti et V pouvant atteindre jusqu'à 0,35 % en poids, le reste étant constitué de fer et d'impuretés habituelles. Ce procédé consiste également à retirer l'acier liquide présent dans la coquille, sous la forme d'une barre de coulée continue (S) et à faire passer cette dernière (S) immédiatement après sa sortie de la coquille, par une section de refroidissement (2) dans laquelle elle est refroidie de manière intensive à une température Ar1 +/- 25 K, à une vitesse de refroidissement (aLM) d'au moins 3 K/s. Ce procédé consiste ensuite à refroidir la barre de coulée (S) à l'air libre pendant au moins 30 secondes, puis à réchauffer la barre de coulée (S) elle-même ou les brames minces (D) séparées de cette dernière, dans un four de compensation (5), avant le laminage à chaud de la barre de coulée (S) ou des brames minces (D) pour former un feuillard à chaud. Ce procédé permet, lors de la transformation d'aciers à faible teneur en carbone et faiblement alliés, de faire baisser les températures requises dans le four de compensation de façon à réduire la sollicitation de ce dernier, sans pour autant affecter la qualité du feuillard à chaud obtenu ou du feuillard à froid produit à partir de ce dernier.
EP00966035A 1999-10-20 2000-09-16 Procede pour produire un feuillard a chaud Expired - Lifetime EP1228255B1 (fr)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
DE19950502A DE19950502C1 (de) 1999-10-20 1999-10-20 Verfahren zum Herstellen eines Warmbandes
DE19950502 1999-10-20
PCT/EP2000/009063 WO2001029273A1 (fr) 1999-10-20 2000-09-16 Procede pour produire un feuillard a chaud

Publications (2)

Publication Number Publication Date
EP1228255A1 true EP1228255A1 (fr) 2002-08-07
EP1228255B1 EP1228255B1 (fr) 2004-08-25

Family

ID=7926268

Family Applications (1)

Application Number Title Priority Date Filing Date
EP00966035A Expired - Lifetime EP1228255B1 (fr) 1999-10-20 2000-09-16 Procede pour produire un feuillard a chaud

Country Status (6)

Country Link
US (1) US6835253B1 (fr)
EP (1) EP1228255B1 (fr)
AU (1) AU7657400A (fr)
DE (2) DE19950502C1 (fr)
ES (1) ES2223585T3 (fr)
WO (1) WO2001029273A1 (fr)

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US8333923B2 (en) * 2007-02-28 2012-12-18 Caterpillar Inc. High strength gray cast iron
US20090084517A1 (en) 2007-05-07 2009-04-02 Thomas Brian G Cooling control system for continuous casting of metal
JP4678448B2 (ja) * 2009-07-15 2011-04-27 住友金属工業株式会社 熱延鋼板の製造装置、及び鋼板の製造方法
DE102014214374A1 (de) * 2014-07-23 2016-01-28 Sms Group Gmbh Verfahren zur Herstellung eines metallischen Produkts
KR102361377B1 (ko) 2017-06-27 2022-02-10 캐논 아네르바 가부시키가이샤 플라스마 처리 장치
CN110743911A (zh) * 2019-10-24 2020-02-04 中铝瑞闽股份有限公司 一种钎焊板用铝合金卷的热轧复合方法
CN115478221A (zh) * 2022-09-20 2022-12-16 武汉钢铁有限公司 一种基于CSP工艺的450MPa级磁极钢及其制造方法

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5168422A (en) 1974-12-11 1976-06-14 Nippon Steel Corp Kyojinkono seizoho
JPS6045689B2 (ja) 1982-02-19 1985-10-11 川崎製鉄株式会社 プレス成形性にすぐれた冷延鋼板の製造方法
FR2544333B1 (fr) 1983-04-18 1988-05-20 Siderurgie Fse Inst Rech Procede pour l'obtention de toles laminees a froid et recuites
DE3818879C1 (fr) 1988-06-01 1989-11-16 Mannesmann Ag, 4000 Duesseldorf, De
DE4416752A1 (de) * 1994-05-13 1995-11-16 Schloemann Siemag Ag Verfahren und Produktionsanlage zur Erzeugung von Warmbreitband

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See references of WO0129273A1 *

Also Published As

Publication number Publication date
DE50007566D1 (de) 2004-09-30
AU7657400A (en) 2001-04-30
US6835253B1 (en) 2004-12-28
DE19950502C1 (de) 2000-11-16
ES2223585T3 (es) 2005-03-01
EP1228255B1 (fr) 2004-08-25
WO2001029273A1 (fr) 2001-04-26

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