EP2460596B1 - Procédé de fabrication d'acier très résistant et faiblement allié avec la cuivre. - Google Patents

Procédé de fabrication d'acier très résistant et faiblement allié avec la cuivre. Download PDF

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Publication number
EP2460596B1
EP2460596B1 EP20100193403 EP10193403A EP2460596B1 EP 2460596 B1 EP2460596 B1 EP 2460596B1 EP 20100193403 EP20100193403 EP 20100193403 EP 10193403 A EP10193403 A EP 10193403A EP 2460596 B1 EP2460596 B1 EP 2460596B1
Authority
EP
European Patent Office
Prior art keywords
rolling
process according
strip
steel
strand
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
EP20100193403
Other languages
German (de)
English (en)
Other versions
EP2460596A1 (fr
Inventor
Gregor Arth
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.)
Primetals Technologies Austria GmbH
Original Assignee
Siemens VAI Metals Technologies GmbH Austria
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 Siemens VAI Metals Technologies GmbH Austria filed Critical Siemens VAI Metals Technologies GmbH Austria
Priority to EP20100193403 priority Critical patent/EP2460596B1/fr
Priority to ES10193403T priority patent/ES2433425T3/es
Priority to UAA201114236A priority patent/UA112150C2/uk
Priority to RU2011149098/02A priority patent/RU2589961C2/ru
Priority to MX2011012920A priority patent/MX2011012920A/es
Priority to CN201110395086.9A priority patent/CN102485362B/zh
Publication of EP2460596A1 publication Critical patent/EP2460596A1/fr
Application granted granted Critical
Publication of EP2460596B1 publication Critical patent/EP2460596B1/fr
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Anticipated expiration legal-status Critical

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Classifications

    • 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
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B2201/00—Special rolling modes
    • B21B2201/10—Endless rolling

Definitions

  • the invention relates to a process for the production of high strength, low alloy steel with the addition of copper.
  • High-strength, low alloy steel is also referred to as HSLA steel due to its English name "high-strength low-alloy steel”.
  • HSLA steel offers better mechanical and processing properties than C-alloyed steel of equal strength.
  • HSLA steel has a carbon content of 0.05 to 0.25% by weight and contains up to 2% by weight of manganese and small amounts of other alloying elements such as copper, nickel, niobium, nitrogen, vanadium, chromium, molybdenum, titanium, calcium, rare earths or zircon.
  • the yield strength is between 250-590 MPa and can even go up to 700 MPa.
  • the alloying elements niobium, titanium and vanadium are necessary for a specific strength of the steel, but account for a large proportion of the cost of steel despite their low (and depending on the steel grade) share. Therefore, there have been and are attempts to reduce the use of these alloying elements.
  • the WO 2004/026497 A1 shows a process for the production of steel strip, with which a strand is produced and is then further processed by endless rolling in a roughing train and a finishing train, wherein after the finishing rolling takes place unspecified cooling.
  • niobium is in the range of 0.01-0.05%
  • vanadium is 0.01 to 0.1%
  • titanium is 0.01-0.03%.
  • Copper in these amounts has the property to produce a precipitation of particles which are stable in the temperature range of forming and heating and have a particle size distribution, which prevents grain growth and thereby at the same time
  • Copper is often already contained in steel in certain steel production processes, for example when low-value scrap with a high copper content is used in the electric arc furnace.
  • copper has the disadvantage that, especially in combination with sulfur, it can lead to the formation of a second ductility minimum of the steel, which occurs as a result of cracking during forming in the rolling train, for example in the form of edge cracks.
  • This phenomenon is associated with enrichment mechanisms, which are enhanced mainly by slow solidification rates and long residence times of the steel in reheating furnaces.
  • This object is achieved by a method according to claim 1, wherein the steel to a copper content of 0.15% to 0.35% is brought and then cast in a strand or strip casting machine in a strand or a belt with a maximum thickness of 130 mm and solidified, the casting speed of at least 4.5 m / min, preferably at least 5 m / min , is and the strand or the strip is then rolled by endless or semi-endless rollers in less than 5.8 minutes, in particular less than 4.5 minutes, to the desired final thickness, and wherein after rolling to the desired final thickness cooling of 15-90 K / s, preferably 25-60 K / s, to a temperature below 650 ° C, preferably below 600 ° C takes place.
  • the duration of the rolling process is measured from the end of the strand or strip casting, so if the cast strand or the cast strip has left the last guide means (usually a pair of guide rollers) of the strand or strip casting.
  • the duration of 5.8 minutes corresponds to a casting speed of about 3-3.5 m / min, the duration of 4.5 minutes to a casting speed of about 4.8-5.4 m / min.
  • the continuous rolling or semi-endless rolling according to the invention preferably takes place in a two-stage rolling mill, consisting of roughing train and finishing train.
  • Under a rolling mill is the immediate juxtaposition of rolling stands each less than 7 m, preferably less than 6 m, understood stand spacing. Further spaced rolling stands already belong to the next rolling mill or are single stands.
  • the casting process takes place in a casting plant, wherein a liquid steel strand emerging from a mold of a casting installation is passed through a strand guiding device directly following the casting mold.
  • This comprises a plurality (usually three to fifteen) guide segments, each guide segment comprising one or more (usually three to ten) pairs of guide elements, preferably designed as strand support rollers.
  • the support rollers are rotatable about an axis orthogonal to the transport direction of the strand.
  • individual To perform guide elements as static, eg runner-shaped components. Regardless of the specific embodiment of the guide elements, these are arranged on both sides of the strand broad sides, so that the strand is guided by upper and lower guide element series.
  • the strand emerges substantially vertically downwards from the mold and is deflected into the horizontal.
  • the strand guiding device therefore has a course substantially curved over an angular range of 90 °.
  • the beginning of the strand or of the strip can therefore already be finished rolled to a steel strip to the final thickness, while the casting plant continues to pour on the same strand or on the same band, so there is no end of the strand or the band.
  • the cast strand is divided into slabs after casting or the strips are split after casting and the divided slabs or strips are fed without intermediate storage and cooling to ambient temperature of the rolling mill.
  • This separation can take place in such a way that the slab head of the preceding slab is or will already be rolled in the subsequent rolling train, or has not yet been covered by larger distances from the first rolling mill.
  • the emerging from the casting line strand is usually descaled, pre-rolled in the roughing, the resulting intermediate band is reheated in an oven conventional manner to temperatures of about 1200 ° C and rolled finished in the finishing train.
  • hot rolling takes place in the finishing train, which means that the rolling stock remains in the austenite area during rolling.
  • the final rolling temperatures are in the range of 780-850 ° C, preferably in the range of 800-830 ° C.
  • the continuous rolling or semi-endless rolling prevents the cooling of the steel after the casting process by the immediate further processing in the roughing mill.
  • the slabs are often stored after their production and must be reheated already before the roughing mill. But this sets in motion the unwanted enrichment mechanisms.
  • the thicknesses of the cast strands or slabs or slabs of at most 130 mm which occur during continuous or semi-continuous rolling, also have a positive effect on undesired precipitates, because the copper particles are deposited more rapidly and are thus limited to a specific, small mean diameter , which mainly depends on the solidification rate.
  • the size range of the 20-40 nm precipitates also corresponds to the size range of the precipitates targeted by micro-alloying elements (titanium, niobium) in order to have a microstructure-influencing and also strength-increasing effect.
  • a tensile strength of up to 925 MPa or a yield strength of up to 700 MPa can be achieved, the higher values preferably by rapid cooling (50-90 K / s) immediately after the last forming step and by cooling to less be achieved as 500 ° C.
  • the resulting room temperature structure consists primarily of ferrite or perlite and bainite.
  • Comparable HSLA steels conventionally produced contain about 0.07% vanadium, 0.15% titanium and 0.07% niobium.
  • the added proportion of vanadium (V) in the steel below 0.03%, in particular less than 0.01% and / or that the added amount of niobium (Nb) in the steel below 0.055%, preferably below 0.045%, more preferably below 0.03%.
  • the cast slab has a preferred thickness of 40-130 mm, particularly preferably from 40-105 mm, in particular about 80 mm.
  • the cast and solidified strip has a preferred thickness of 1-4.5 mm, in particular about 3 mm. Unless rolled after strip casting, a subdivision into a pre-rolling and a finishing train will naturally not take place.
  • the thickness of the intermediate strip is in the process of the invention preferably 5-25 mm, preferably 10-18 mm.
  • the roughing mill should comprise at least two, preferably three, rolling mills, the finishing mill at least four, preferably five mills.
  • the final thickness of the finished rolled product is in the range of 0.6-12 mm, preferably 1-6 mm.
  • the method according to the invention has the advantage that it is also possible to use inferior scrap and thus copper-containing scrap in the steelmaking and, in addition, to reduce the addition of alloying elements, in particular micro-alloying elements (niobium, titanium, vanadium).
  • alloying elements in particular micro-alloying elements (niobium, titanium, vanadium).
  • the inventive method can be used for uncoated sheets for the automotive industry, for electrolytically galvanized sheets and for hot-dip galvanized sheets in the automotive sector.
  • a strand is poured in a casting machine, which is about 70 - 100mm thick.
  • a casting machine which is about 70 - 100mm thick.
  • the roughing line in which a large decrease in the strip thickness of the intermediate strip is achieved, to about 15 mm.
  • a plant for descaling is provided and thereafter, the material passes through an inductive heater and a five-stand finishing train, in which the thickness can be reduced to 0.6 mm.
  • a cooling of the strip in the cooling section as by water application, for adjusting the material properties and after this there is a reel on which the tape is wound into coils, whereby the production process is completed.
  • the mill By installing several shears (after the roughing line, before the finish rolling mill and before the reel), the mill could be operated in single-piece mode, with the intermediate belts being cut after the roughing mill and individually rolled in the finish rolling mill. In endless rolling, the strips rolled to final thickness are not cut before the reel, the rolling operation is continuous.
  • the big advantage of this system is the low energy requirement for producing the steel strip. While in conventional hot rolling mills approx. 2 GJ of energy are required to produce one ton of hot strip, this value falls in a continuous or semi-continuous rolling mill to up to 0.4 GJ per ton of hot strip.
  • cooling section for the finished rolled strip is a cooling of 15-90 K / s, preferably from 25-60 K / s, to a temperature below 650 ° C, preferably below 600 ° C, within a maximum of 35 seconds, preferably within from maximum 15 seconds, after rolling to the desired final thickness.

Landscapes

  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Metal Rolling (AREA)
  • Continuous Casting (AREA)

Claims (11)

  1. Procédé de fabrication d'acier haute résistance faiblement allié avec adjonction de cuivre, caractérisé en ce que l'acier est amené à une teneur en cuivre de 0,15% à 0,35% et est ensuite coulé et solidifié en barre resp. feuillard d'une épaisseur maximale de 130 mm dans une installation de coulée continue ou de coulée en bande, la vitesse de coulée étant d'au moins 4,5 m/min, de préférence d'au moins 5 m/min, et la barre resp. le feuillard étant ensuite laminé(e) à l'épaisseur finale voulue par laminage continu ou laminage semi-continu en moins de 5,8 min, notamment moins de 4,5 min, et en ce qu'un refroidissement de 15-90 K/s, de préférence 25-60 K/s, à une température inférieure à 650°C, de préférence inférieure à 600°C, a lieu après le laminage à l'épaisseur finale voulue.
  2. Procédé selon la revendication 1, caractérisé en ce que le laminage continu ou laminage semi-continu est réalisé dans un laminoir à deux étages formé d'un train dégrossisseur et d'un train finisseur.
  3. Procédé selon la revendication 1, caractérisé en ce que le refroidissement a lieu dans les 35 secondes au maximum, de préférence dans les 15 secondes au maximum, qui suivent le laminage à l'épaisseur finale voulue.
  4. Procédé selon l'une des revendications 1 à 3, caractérisé en ce que la proportion ajoutée de vanadium (V) dans l'acier est inférieure à 0,03%, notamment inférieure à 0,01%.
  5. Procédé selon l'une des revendications 1 à 4, caractérisé en ce que la proportion ajoutée de niobium (Nb) dans l'acier est inférieure à 0,055%, de préférence inférieure à 0,045%, plus préférablement inférieure à 0,03% .
  6. Procédé selon l'une des revendications 1 à 5, caractérisé en ce que la barre coulée et solidifiée a une épaisseur préférentielle de 40-130 mm, plus préférablement de 40-105 mm, notamment d'environ 80 mm.
  7. Procédé selon l'une des revendications 1 à 5, caractérisé en ce que le feuillard coulé et solidifié a une épaisseur préférentielle de 1-4,5 mm, notamment d'environ 3 mm.
  8. Procédé selon l'une des revendications 1 à 6, caractérisé en ce que l'épaisseur du feuillard intermédiaire est de 5-25 mm, de préférence 10-18 mm.
  9. Procédé selon l'une des revendications 2 à 6 et 8, caractérisé en ce que le train dégrossisseur comprend au moins deux, de préférence trois, cages de laminoir.
  10. Procédé selon l'une des revendications 2 à 6, 8 et 10, caractérisé en ce que le train finisseur comprend au moins quatre, de préférence cinq, cages de laminoir.
  11. Procédé selon l'une des revendications 1 à 10, caractérisé en ce que l'épaisseur finale est comprise entre 0,6 mm et 12 mm, de préférence entre 1 mm et 6 mm.
EP20100193403 2010-12-02 2010-12-02 Procédé de fabrication d'acier très résistant et faiblement allié avec la cuivre. Active EP2460596B1 (fr)

Priority Applications (6)

Application Number Priority Date Filing Date Title
EP20100193403 EP2460596B1 (fr) 2010-12-02 2010-12-02 Procédé de fabrication d'acier très résistant et faiblement allié avec la cuivre.
ES10193403T ES2433425T3 (es) 2010-12-02 2010-12-02 Procedimiento para producir acero de resistencia elevada, de baja aleación, con cobre
UAA201114236A UA112150C2 (uk) 2010-12-02 2011-12-01 Спосіб одержання виробу з високоміцної, низьколегованої сталі
RU2011149098/02A RU2589961C2 (ru) 2010-12-02 2011-12-01 Способ получения высокопрочной низколегированной стали
MX2011012920A MX2011012920A (es) 2010-12-02 2011-12-02 Proceso para producir acero de baja aleacion de alta resistencia.
CN201110395086.9A CN102485362B (zh) 2010-12-02 2011-12-02 用于生产高强度低合金钢的方法

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP20100193403 EP2460596B1 (fr) 2010-12-02 2010-12-02 Procédé de fabrication d'acier très résistant et faiblement allié avec la cuivre.

Publications (2)

Publication Number Publication Date
EP2460596A1 EP2460596A1 (fr) 2012-06-06
EP2460596B1 true EP2460596B1 (fr) 2013-08-28

Family

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Family Applications (1)

Application Number Title Priority Date Filing Date
EP20100193403 Active EP2460596B1 (fr) 2010-12-02 2010-12-02 Procédé de fabrication d'acier très résistant et faiblement allié avec la cuivre.

Country Status (6)

Country Link
EP (1) EP2460596B1 (fr)
CN (1) CN102485362B (fr)
ES (1) ES2433425T3 (fr)
MX (1) MX2011012920A (fr)
RU (1) RU2589961C2 (fr)
UA (1) UA112150C2 (fr)

Families Citing this family (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN104946981A (zh) * 2015-06-23 2015-09-30 宁波吉威熔模铸造有限公司 一种低合金钢制造方法
CN106086596A (zh) * 2016-08-15 2016-11-09 宁波吉威熔模铸造有限公司 一种机械性能好的低合金钢制备工艺

Family Cites Families (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2843665B2 (ja) * 1990-10-25 1999-01-06 新日本製鐵株式会社 連続鋳造鋳片の熱間加工割れ防止方法
NL1003293C2 (nl) * 1996-06-07 1997-12-10 Hoogovens Staal Bv Werkwijze en inrichting voor het vervaardigen van een stalen band.
DE10025080A1 (de) * 1999-06-08 2001-05-17 Sms Demag Ag Verfahren zum Herstellen von Metallband
EP1326725B1 (fr) * 2000-09-29 2009-08-05 Nucor Corporation Production de bandes d'acier fines
ITMI20021996A1 (it) * 2002-09-19 2004-03-20 Giovanni Arvedi Procedimento e linea di produzione per la fabbricazione di nastro a caldo ultrasottile sulla base della tecnologia della bramma sottile
KR100961334B1 (ko) * 2002-12-26 2010-06-04 주식회사 포스코 박슬래브를 이용한 Ｃｕ첨가 열연강판의 제조방법
CA2460399A1 (fr) * 2004-03-10 2005-09-10 Algoma Steel Inc. Produit en acier a haute resistance a formabilite amelioree et processus de fabrication d'acier
EP1807542A1 (fr) * 2004-11-03 2007-07-18 ThyssenKrupp Steel AG 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"
KR100627475B1 (ko) * 2004-12-24 2006-09-25 주식회사 포스코 미니밀공정을 이용한 표면특성이 우수한 저항복비형고장력 열연강판 제조방법
CN101353766B (zh) * 2007-07-23 2011-07-20 宝山钢铁股份有限公司 抗沟槽腐蚀高强度erw焊接套管用钢、套管及生产方法
CN101135030B (zh) * 2007-10-12 2010-09-08 莱芜钢铁集团有限公司 一种耐候热轧窄钢带及其制造方法
CN101481778B (zh) * 2008-01-07 2010-12-01 宝山钢铁股份有限公司 一种奥氏体不锈钢带及其制造方法
CN101225498B (zh) * 2008-01-28 2010-06-02 广州珠江钢铁有限责任公司 一种600MPa级高强耐候钢及其制备方法
KR101318227B1 (ko) 2008-05-23 2013-10-15 한국기계연구원 구리를 함유한 복합 베이나이트계 강재 및 그 제조방법
CN101768704A (zh) * 2010-01-21 2010-07-07 山西太钢不锈钢股份有限公司 一种高强度耐大气腐蚀热轧钢带及其制造方法

Also Published As

Publication number Publication date
ES2433425T3 (es) 2013-12-11
UA112150C2 (uk) 2016-08-10
MX2011012920A (es) 2012-06-11
RU2589961C2 (ru) 2016-07-10
RU2011149098A (ru) 2013-06-10
CN102485362A (zh) 2012-06-06
CN102485362B (zh) 2015-06-03
EP2460596A1 (fr) 2012-06-06

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