EP2066466B2 - Procédé de fabrication d'un feuillard d'acier - Google Patents

Procédé de fabrication d'un feuillard d'acier Download PDF

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Publication number
EP2066466B2
EP2066466B2 EP07801685.4A EP07801685A EP2066466B2 EP 2066466 B2 EP2066466 B2 EP 2066466B2 EP 07801685 A EP07801685 A EP 07801685A EP 2066466 B2 EP2066466 B2 EP 2066466B2
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EP
European Patent Office
Prior art keywords
steel
strip
metallic inclusions
steel strip
mns
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.)
Active
Application number
EP07801685.4A
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German (de)
English (en)
Other versions
EP2066466A1 (fr
EP2066466B1 (fr
Inventor
Christian Bernhard
Gerald Eckerstorfer
Gerald Hohenbichler
Bernd Linzer
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.)
SIEMENS VAI METALS Technologies GmbH
Original Assignee
Siemens VAI Metals Technologies GmbH Austria
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Application filed by Siemens VAI Metals Technologies GmbH Austria filed Critical Siemens VAI Metals Technologies GmbH Austria
Priority to SI200730701T priority Critical patent/SI2066466T1/sl
Priority to PL07801685T priority patent/PL2066466T3/pl
Publication of EP2066466A1 publication Critical patent/EP2066466A1/fr
Application granted granted Critical
Publication of EP2066466B1 publication Critical patent/EP2066466B1/fr
Publication of EP2066466B2 publication Critical patent/EP2066466B2/fr
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    • 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
    • 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

Definitions

  • the melting temperature of the non-metallic inclusions of Mn / Si partially annealed steel melts is very sensitive to changes in the steel composition and associated changes in the MnO / SiO 2 ratio of its own composition.
  • each treated ladle has a composition which comprises the Ensures the presence of liquid non-metallic inclusions during the casting process. This can lead to cracks and surface defects.
  • the tolerance of non-metallic inclusion melting temperature to deviations from a setpoint of the steel composition should be sufficient to ensure the presence of liquid non-metallic inclusions in the casting process in each melted melt in the industrial smelting operation.
  • the object of the invention is achieved by a method in which a molten steel with a Mn and Si content in a certain ratio and with a certain sulfur content in normal operation using a certain band forming force (roll separating force, RSF) is processed.
  • a molten steel with a Mn and Si content in a certain ratio and with a certain sulfur content in normal operation using a certain band forming force (roll separating force, RSF) is processed.
  • the invention therefore relates to a method for producing a strip-cast low carbon, Mn / Si partially annealed steel strip, wherein a molten steel is fed from a melt reservoir between at least two, with a steel belt moving and cooled casting rolls and solidifies at the casting rolls at least partially to the steel strip, characterized in that the molten steel has a ratio Mn / Si ⁇ 3.5 and in normal operation, the band forming force between 2 and 50 kN / m, wherein the molten steel has a sulfur content between 70 and 200 ppm.
  • a steel strip made in this way is largely free of cracks and surface defects and has a homogeneous surface.
  • low-carbon steel strip a steel strip in which the carbon content is less than 0.1% by weight.
  • the inventive composition of the molten steel ensures a low melting temperature of the non-metallic inclusions.
  • the low melting temperature causes the non-metallic inclusions in the casting process during the solidification of the steel shell on the casting rolls in the liquid state.
  • the tolerance of the melting temperature of non-metallic inclusions to deviations from a target value of the steel composition increases. This broadened composition range ensures that the molten steel has a composition that guarantees liquid non-metallic inclusions in the casting process, even if the setpoint for a particular steel composition is not exactly met in industrial smelting operations.
  • nonmetallic inclusions of an oxidic or sulfidic nature are formed in a molten steel.
  • the main components of non-metallic inclusions in Mn / Si partially annealed steel melts are MnO and SiO 2 .
  • the adjustment according to the invention of the sulfur content to values between 70 and 200 ppm and the Mn / Si ratio to values ⁇ 3.5 ensures that the non-metallic inclusions mainly consist of a multiphase system with the main components MnO-SiO 2 -MnS. If the proportion of MnS in this multi-phase system is less than 37% by weight MnS, the melting temperature of the multiphase system is lower than the melting temperature of a multiphase system composed of the main components MnO and SiO 2 .
  • the 3-phase system MnO-SiO 2 -MnS has a ternary eutectic at approx. 1130 ° C.
  • the modeling of the 3-phase system MnO-SiO 2 -MnS in FIG. 1 shows that the liquidus region touches the binary boundary system MnO-SiO 2 at its eutectic temperature of 1251 ° C in the eutectic point and widens with increasing MnS content in the transition to a 3-phase system. At lower temperatures, the liquidus area has lifted off the edge system and exists only at minimum levels of MnS.
  • FIG. 2 shows the influence of the sulfur content of a low-carbon, Mn / sitillated molten steel (0.05 wt% C, 0.7 wt% Mn, 0.2 wt% Si) with a Mn / Si ratio of ⁇ 3.5 on the crack tendency, expressed in terms of the crack frequency or the width of the melt interval of the molten steel, on the composition of non-metallic inclusions, and on the melting temperatures (liquidus temperatures) of the non-metallic inclusions.
  • the measured data in FIG. 2 were won from the diving experiments mentioned above.
  • FIG. 2 shows the opposite behavior of increasing hot cracking tendency and decreasing melting temperature of non-metallic inclusions.
  • inventively recommended sulfur content in which sufficiently low melting temperatures of the non-metallic inclusions and at the same time tolerable hot cracking tendency can be achieved, can be derived.
  • the presence of sulfur in a steel alloy results in the expansion of the 2-phase solid / liquid zone, ie the melt interval, of the steel alloy while reducing its solidus temperature, thereby expanding the temperature range of the hot cracking formation between Liquid Impenetration Temperature LIT and zero ductility temperature ZDT.
  • the width of the 2-phase region increases approximately linearly up to about 45 ° C. From this sulfur content, the width of the 2-phase region remains approximately constant as a result of MnS precipitation in the course of solidification with increasing sulfur content. These MnS precipitates deposit in solid form on the casting roll surfaces and thereby hinder a homogeneous heat flow or a homogeneous cooling effect, which favors the formation of surface defects and cracks. Rising sulfur content of the molten steel leads to increasing amounts of MnS precipitates and thus to the increase of surface defects and cracks. Therefore, the maximum sulfur content according to the invention is limited to 200 ppm.
  • the lowering of the melting temperature of the liquid non-metallic inclusions relative to multiphase systems of the major components MnO and SiO 2 is not large enough to ensure the presence of liquid non-metallic inclusions in the casting process during the solidification of the steel shell on the casting rolls.
  • the width of the compositional range in which liquid nonmetallic inclusions are present in the multiphase system is not large enough to ensure sufficient tolerance to deviations from a setpoint of the steel composition in industrial smelting operation.
  • the sulfur content is at least 70 ppm.
  • the upper limit of the sulfur content is 200 ppm.
  • the sulfur content of the molten steel can be brought to the desired level by desulphurisation or controlled addition of sulfur or sulfur compounds.
  • the Mn / Si ratio according to the invention must be greater than or equal to 3.5.
  • a low band forming force avoids such problems and additionally offers the advantage that the mechanical stress of the casting apparatus is lower.
  • the choice of a low band forming force can adversely affect the stability of the casting process, because with a low band forming force there is a risk that the metal shells solidified on the casting rolls will be insufficiently compressed due to inhomogeneities in the solidification and the steel strip tears under its own weight that the Steel shells stick to the casting roll partially or over the entire width and that the steel shell tears.
  • the size of the roller separation force during normal operation is between 5 and 250 kN / m.
  • the strip forming force is less than 50 kN / m. Since the inventive composition of the molten steel due to ensuring the occurrence of liquid non-metallic inclusions minimizes the formation of inhomogeneities during the solidification of the steel shells, such a low strip forming force can be used without risk to the stability of the casting process.
  • the crack frequency increases with increasing band forming force.
  • strip forming forces above 50 kN / m, the production of a homogeneous, free of cracks and surface defects free surface of the steel strip can not be ensured.
  • the lower limit for the strip forming force is 2 kN / m. Below this value, sufficient stability of the casting process is not guaranteed.
  • the band forming force is at least 5 kN / m. Its upper limit is preferably 30 kN / m.
  • the given values for the strip forming force refer to the steady-state normal operation of a casting plant, but not to the conditions when starting up the plant or for temporary extraordinary load effects.
  • the non-metallic inclusions of the molten steel have a mass fraction of Al 2 O 3 which is less than 45% by weight.
  • the forming multiphase system with the main components MnO-SiO 2 -MnS-Al 2 O 3 has a melting temperature which is lower than the melting temperature of a multiphase system of the main components MnO and SiO 2 .
  • the composition range in which liquid non-metallic inclusions are present is wider in the multiphase system with the main components MnO-SiO 2 -MnS-Al 2 O 3 than in the multiphase system consisting of the main components MnO and SiO 2 .
  • the Al 2 O 3 content is adjusted by the choice of the starting materials for the preparation of the molten steel or optionally by the specific addition of Al or Al compounds.

Landscapes

  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Continuous Casting (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Coating With Molten Metal (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Claims (3)

  1. Procédé de fabrication d'un feuillard d'acier à bas carbone partiellement calmé au Mn-Si coulé en forme de bande, selon lequel de l'acier liquide est versé depuis un réservoir d'acier liquide entre au moins deux cylindres de coulée refroidis se déplaçant avec un feuillard d'acier et se solidifie au moins partiellement sur lesdits cylindres de coulée pour former le feuillard d'acier, caractérisé en ce que l'acier liquide présente un rapport Mn/Si ≥ 3,5 et la force de formation de feuillard est comprise entre 2 et 50 kN/m en fonctionnement normal,
    l'acier liquide présentant une teneur en soufre comprise entre 70 et 200 ppm.
  2. Procédé selon la revendication 1, caractérisé en ce que la force de formation de feuillard est comprise entre 5 et 30 kN/m.
  3. Procédé selon l'une des revendications 1 à 2, caractérisé en ce que l'acier liquide contient des inclusions non métalliques ayant une teneur massique en Al2O3 inférieure à 45% en poids.
EP07801685.4A 2006-09-22 2007-08-16 Procédé de fabrication d'un feuillard d'acier Active EP2066466B2 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
SI200730701T SI2066466T1 (sl) 2006-09-22 2007-08-16 Postopek za izdelavo jeklenega traku
PL07801685T PL2066466T3 (pl) 2006-09-22 2007-08-16 Sposób wytwarzania taśmy stalowej

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
AT0159306A AT504225B1 (de) 2006-09-22 2006-09-22 Verfahren zur herstellung eines stahlbandes
PCT/EP2007/007228 WO2008034502A1 (fr) 2006-09-22 2007-08-16 Procédé de fabrication d'un feuillard d'acier

Publications (3)

Publication Number Publication Date
EP2066466A1 EP2066466A1 (fr) 2009-06-10
EP2066466B1 EP2066466B1 (fr) 2011-06-29
EP2066466B2 true EP2066466B2 (fr) 2014-08-27

Family

ID=38541914

Family Applications (1)

Application Number Title Priority Date Filing Date
EP07801685.4A Active EP2066466B2 (fr) 2006-09-22 2007-08-16 Procédé de fabrication d'un feuillard d'acier

Country Status (16)

Country Link
US (1) US20100018665A1 (fr)
EP (1) EP2066466B2 (fr)
JP (1) JP5129253B2 (fr)
KR (1) KR101442724B1 (fr)
CN (1) CN101516544B (fr)
AT (2) AT504225B1 (fr)
AU (1) AU2007299343B2 (fr)
BR (1) BRPI0717489B1 (fr)
DK (1) DK2066466T3 (fr)
ES (1) ES2366139T5 (fr)
MX (1) MX2009002629A (fr)
PL (1) PL2066466T3 (fr)
RU (1) RU2418650C2 (fr)
SI (1) SI2066466T1 (fr)
UA (1) UA93097C2 (fr)
WO (1) WO2008034502A1 (fr)

Families Citing this family (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7975754B2 (en) * 2007-08-13 2011-07-12 Nucor Corporation Thin cast steel strip with reduced microcracking
CN113198995A (zh) * 2021-04-25 2021-08-03 芜湖新兴铸管有限责任公司 一种包晶钢连铸坯凹陷改善控制方法

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH05115946A (ja) † 1991-07-09 1993-05-14 Nisshin Steel Co Ltd 双ロール式連鋳機の運転制御法
US6491089B1 (en) † 1999-03-26 2002-12-10 Sollac Process for manufacturing carbon-steel strip by twin-roll continuous casting, product produced and apparatus
WO2003024644A1 (fr) † 2001-09-14 2003-03-27 Nucor Corporation Feuillard d'acier de coulage
US6818073B2 (en) † 2000-09-29 2004-11-16 Nucor Corporation Method of producing steel strip
US20050205233A1 (en) † 2002-10-15 2005-09-22 Gerald Hohenbichler Process for the continuous production of a thin steel strip
EP2049287A1 (fr) † 2006-08-09 2009-04-22 Nucor Corporation Procédé de coulée d'une bande coulée mince

Family Cites Families (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3308102B2 (ja) * 1994-05-26 2002-07-29 キャストリップ・リミテッド・ライアビリティ・カンパニー 金属ストリップ連続鋳造方法
AUPN281195A0 (en) * 1995-05-05 1995-06-01 Bhp Steel (Jla) Pty Limited Casting steel strip
JPH09168844A (ja) * 1995-12-19 1997-06-30 Mitsubishi Heavy Ind Ltd 双ドラム式連続鋳造方法
JP3117638B2 (ja) * 1996-03-28 2000-12-18 新日本製鐵株式会社 薄帯鋳片連続鋳造方法
IT1291931B1 (it) * 1997-06-19 1999-01-21 Voest Alpine Ind Anlagen Procedimento per la produzione di nastri grezzi di colaggio in acciaio a basso contenuto di carbonio e nastri cosi' ottenibili
JP4518645B2 (ja) * 2000-01-21 2010-08-04 日新製鋼株式会社 高強度高靱性マルテンサイト系ステンレス鋼板並びに冷延耳切れ抑止方法および鋼板製造法
UA76140C2 (en) * 2001-04-02 2006-07-17 Nucor Corp A method for ladle refining of steel
DE10125669B4 (de) * 2001-05-25 2006-04-27 Hammelmann Maschinenfabrik Gmbh Pumpe, insbesondere Plungerpumpe
FR2834722B1 (fr) * 2002-01-14 2004-12-24 Usinor Procede de fabrication d'un produit siderurgique en acier au carbone riche en cuivre, et produit siderurgique ainsi obtenu
KR100489018B1 (ko) * 2002-08-30 2005-05-11 주식회사 포스코 쌍롤형 박판 주조기를 이용한 고망간강의 박판 제조 방법
MXPA05007704A (es) * 2003-01-24 2005-09-30 Nucor Corp Tira de acero colado.
KR101286890B1 (ko) * 2003-10-10 2013-07-23 누코 코포레이션 캐스팅 강 스트립
WO2007079545A1 (fr) * 2006-01-16 2007-07-19 Nucor Corporation Bande d'acier coulé mince à microfissuration réduite

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH05115946A (ja) † 1991-07-09 1993-05-14 Nisshin Steel Co Ltd 双ロール式連鋳機の運転制御法
US6491089B1 (en) † 1999-03-26 2002-12-10 Sollac Process for manufacturing carbon-steel strip by twin-roll continuous casting, product produced and apparatus
US6818073B2 (en) † 2000-09-29 2004-11-16 Nucor Corporation Method of producing steel strip
WO2003024644A1 (fr) † 2001-09-14 2003-03-27 Nucor Corporation Feuillard d'acier de coulage
US20050205233A1 (en) † 2002-10-15 2005-09-22 Gerald Hohenbichler Process for the continuous production of a thin steel strip
US20050211412A1 (en) † 2002-10-15 2005-09-29 Gerald Hohenbichler Installation for continuously producing a thin steel strip
EP2049287A1 (fr) † 2006-08-09 2009-04-22 Nucor Corporation Procédé de coulée d'une bande coulée mince

Also Published As

Publication number Publication date
KR20090064462A (ko) 2009-06-18
BRPI0717489A2 (pt) 2013-10-15
AU2007299343A1 (en) 2008-03-27
MX2009002629A (es) 2009-03-24
UA93097C2 (uk) 2011-01-10
AT504225A1 (de) 2008-04-15
RU2418650C2 (ru) 2011-05-20
BRPI0717489B1 (pt) 2016-02-10
DK2066466T3 (da) 2011-10-24
US20100018665A1 (en) 2010-01-28
AT504225B1 (de) 2008-10-15
AU2007299343B2 (en) 2011-09-08
RU2009115180A (ru) 2010-10-27
JP5129253B2 (ja) 2013-01-30
EP2066466A1 (fr) 2009-06-10
SI2066466T1 (sl) 2011-10-28
EP2066466B1 (fr) 2011-06-29
ATE514502T1 (de) 2011-07-15
KR101442724B1 (ko) 2014-09-23
ES2366139T3 (es) 2011-10-17
WO2008034502A1 (fr) 2008-03-27
CN101516544A (zh) 2009-08-26
CN101516544B (zh) 2011-06-08
ES2366139T5 (es) 2014-10-06
PL2066466T3 (pl) 2011-11-30
JP2010504214A (ja) 2010-02-12

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