JP4688890B2 - Method and equipment for producing lightweight steel with high manganese content - Google Patents

Method and equipment for producing lightweight steel with high manganese content Download PDF

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JP4688890B2
JP4688890B2 JP2007557433A JP2007557433A JP4688890B2 JP 4688890 B2 JP4688890 B2 JP 4688890B2 JP 2007557433 A JP2007557433 A JP 2007557433A JP 2007557433 A JP2007557433 A JP 2007557433A JP 4688890 B2 JP4688890 B2 JP 4688890B2
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bloom
casting powder
casting
sio
steel
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JP2008531292A (en
JP2008531292A5 (en
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ギルゲンゾーン・アルブレヒト
ケンプケン・イェンス
ライフェルシャイト・マルクス
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エス・エム・エス・ジーマーク・アクチエンゲゼルシャフト
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Priority to DE102005010243.3 priority
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Priority to PCT/EP2006/001954 priority patent/WO2006094718A1/en
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    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/02Ferrous alloys, e.g. steel alloys containing silicon
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B21MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21BROLLING OF METAL
    • B21B1/00Metal-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
    • B21B1/46Metal-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
    • B21B1/466Metal-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
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B21MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21BROLLING OF METAL
    • B21B3/00Rolling 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
    • B21B3/02Rolling special iron alloys, e.g. stainless steel
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B22CASTING; POWDER METALLURGY
    • B22DCASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/10Supplying or treating molten metal
    • B22D11/11Treating the molten metal
    • B22D11/111Treating the molten metal by using protecting powders
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B22CASTING; POWDER METALLURGY
    • B22DCASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/12Accessories for subsequent treating or working cast stock in situ
    • B22D11/1213Accessories for subsequent treating or working cast stock in situ for heating or insulating strands
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B22CASTING; POWDER METALLURGY
    • B22DCASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/14Plants for continuous casting
    • B22D11/142Plants for continuous casting for curved casting
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE BY DECARBURISATION, TEMPERING OR OTHER TREATMENTS
    • C21D6/00Heat treatment of ferrous alloys
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE BY DECARBURISATION, TEMPERING OR OTHER TREATMENTS
    • C21D6/00Heat treatment of ferrous alloys
    • C21D6/005Heat treatment of ferrous alloys containing Mn
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE BY DECARBURISATION, TEMPERING OR OTHER TREATMENTS
    • C21D8/00Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/021Modifying 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
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/04Ferrous alloys, e.g. steel alloys containing manganese
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/06Ferrous alloys, e.g. steel alloys containing aluminium
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE BY DECARBURISATION, TEMPERING OR OTHER TREATMENTS
    • C21D8/00Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/021Modifying 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
    • C21D8/0215Rapid solidification; Thin strip casting

Description

  The present invention relates to manganese (Mn), aluminum (Al) and silicon in which steel is first cast as continuous strands in a continuous casting facility, divided into blooms and then rolled to final thickness. The present invention relates to a method and equipment for producing a hot-rolled strip of high strength austenitic lightweight steel with high (Si) content and good cold formability with TWIP (twinning induced plasticity) properties.

  For example, according to Patent Document 1, for example, austenitic lightweight steel having TWIP characteristics used for a vehicle body sheet rope, a vehicle body reinforcing member, a low temperature container and a pipe is 10-30% Mn, 1-6% Si. 1-8% Al (however, Si + Al ≦ 12%) and the remaining Fe.

  Patent Document 2 includes 7-30% Mn, 1-10% Al, 0.7-4% Si, which has good resistance to corrosion and stress corrosion cracking in addition to good mechanical properties. High strength lightweight steel further comprising 10% or less of Cr, 10% or less of Ni, 3% or less of Cu and 0.5% or less of C, and optionally further alloying elements N, Va, Nb, Ti, P Has been. This steel is cast by a continuous casting method, hot-rolled, or cast to a shape close to the final size by a thin plate casting method.

  In the prior art, it is considered difficult or impossible to produce steel with a high manganese content by continuous casting for various reasons. The reason for this is that the strength of the strand solidification shell at the time of solidification is small against strong microsegregation of Mn (there is a possibility of breaking through when Mn> 15%), and high strength at low temperature (overload due to equipment) , Cracking problems), reaction of aluminum in steel with casting powder (restriction of function), macrosegregation, absorption of hydrogen and / or oxygen by sprinkling cooling, increased incorporation of non-metallic inclusions, alloys in the peripheral region This is a decrease in element density and oxidation of grain boundaries when bloom is reheated in a boost furnace.

  In that regard, Non-Patent Document 1 shows that steel becomes more difficult to cast as the manganese content increases. On the other hand, when the manganese content is large, the manganese is greatly concentrated in the residual melt and lowers the melting point in the interdendritic region, so that the strength of the steel decreases when the temperature after solidification is high. This increases the tendency of the shell to break through, and according to current estimates, continuous casting is not possible when the manganese content is 15% or more. On the other hand, when the temperature is low, the steel has great strength, so that when the strand is bent, the equipment is overloaded and must be prepared to crack. Furthermore, in the case of such steel, when the aluminum content reaches several percent, the reaction with the casting powder occurs so that the aluminum is mixed in to reduce the density and the like, and this greatly affects the function. Will give.

  In that regard, Non-Patent Document 2 summarizes that, for the method using casting powder, it is confirmed that it is not advantageous to cast with the assumed alloy configuration to make a TWIP rope.

A major problem in casting steel with high Al content (greater than 1%) is that the aluminum in the steel reacts with the oxide component of the casting powder. The reaction between SiO 2 in the slag and aluminum in the steel produces Al 2 O 3 and is incorporated into the slag, thereby increasing the basicity of the slag (CaO / SiO 2 ratio). As a result, the viscosity and lubricity in the mold change greatly.

  Because of this difficulty, various methods for manufacturing TWIP ropes have been described in the past.

  According to Patent Document 3, an increase in possible carbon content (C ≦ 1%) and addition of further elements (here in particular B, but Ni, Cu, N, Nb, Ti, V, P are also possible) Thus, it is well known how to achieve an apparent reduction in the elastic limit and thereby an improvement in plasticity during hot and cold rolling. In order to produce this steel, the input material (bloom, thin bloom or strip) is heated, hot rolled and wound while paying attention to predetermined temperature limits.

  In Patent Document 4, a steel containing 12 to 30% manganese is cast as a thin intermediate strip having a thickness of 1 mm to less than 6 mm using a two-roll caster, and the steel roll exits vertically from the gap between the rolling rolls. A method is described in which the incoming intermediate strip is cooled by a coolant applied to its surface and then rolled to a final thickness in one hot rolling pass. The overall time interval between the output from the mill roll gap and the input to the mill is about 8 seconds.

According to US Pat. No. 6,057,049, a method for producing a strip made of Fe—C—Mn alloy is known, in which first, 6-30% Mn, 0.001-1.6% C, 2. A thin steel sheet having a thickness of 1.5 to 10 mm having a composition of 5% or less of Si, 6% or less of Al, 10% or less of Cr and further elements is produced by a two-roll casting machine, and then Hot rolling is performed by one or more processes having a reduction degree of 10 to 60%.
EP 0 899 144 German Patent Publication No. 19900199 International Patent Publication No. 02/101109 Specification EP 1341937 European Patent No. 10672203 Spitzer et al.:"Innovative Stahlprodukte-Herausforderung fuer die Prozessentwicklung "; Konferenz-Einzelbericht: Barbara 2001, S.71-84 Gigacher et al.:"Eigenschaften hochmanganhaltiger Staehle unter stranggiessaehnlichen Bedingungen "; BHM149 (2004), Heft 3, S.112-117

  The object of the present invention is to provide a method and equipment that can be realized as simply as possible, making it possible to produce a manganese-rich steel having a predetermined chemical composition with a predetermined chemical composition by a continuous casting method. Is to present.

This set task is based on the features listed in claim 1 with respect to the method, including 15-27% Mn, 1-6% Al, 1-6% Si, 0.8% carbon or less and the rest. Based on a process in which lightweight steel with a predetermined chemical composition of iron and trace elements is placed in order,
Casting in a thin bloom (d ≦ 120 mm) caster (1) with a suitable casting powder that achieves equilibrium at very high speed and then no longer changes its lubricity; Divided into
-Immediately after solidification and division, the temperature of the bloom (3) is equalized in the intermediate furnace (4) in the work process, and then
-Hot-roll the bloom (3) immediately without cooling after that,
It is solved by.

  An installation for carrying out this method is characterized by the features of claim 7.

  For example, when producing thin blooms on a CSP caster (CSP: compact strip manufacture), the strands are drawn vertically, bent horizontally following solidification, and then divided into blooms. Therefore, in this case, there is no problem with internal cracks. The production of high strength austenitic steel can be carried out without overloading by equipment, and as far as this is the prior art.

  Most of the microsegregation existing in the strands immediately after solidification disappears again by diffusion in the course of work in an intermediate furnace, for example, a roller hearth furnace, before subsequent rolling. In that case, the macrosegregation at the center of the bloom is sufficiently equalized by the large forming in the hot rolling equipment, as in the case of the austenitic special steel.

  By using a roller hearth furnace in a CSP facility according to the invention, it is advantageous because of its short transit time, for example, in the booster furnace of a traditional wide strand hot rolling line according to the prior art. A large decrease in density or oxidation of the grain boundaries of the alloying elements that can be an obstacle due to the heating phase is prevented.

  In order to be able to utilize the technique of casting TWIP lightweight steel with high manganese and aluminum contents in a thin bloom caster based on this invention, it is necessary to use a suitable casting powder. Such a suitable casting powder has, according to the invention, the property of achieving an equilibrium state very fast and subsequently no longer changing its lubricity.

In this invention, for example, the casting powder contains more than 10% Al 2 O 3 component to slow down the reaction rate of lowering SiO 2 by aluminum in the steel. In order to make more SiO 2 available in equilibrium, instead or in addition, the SiO 2 component of the casting powder is increased, in which case the increase is between 0.5 and 0.7. Up to basicity (CaO / SiO 2 ratio).

MnO 2 is easily reduced as SiO 2 by Al in the steel, because it by a reduction in SiO 2 (combustion) is prevented, as an additional method of the present invention, the addition of MnO 2 to the casting powder It is possible.

In this invention, it works in the form of gas like SiO 2 , but it is also possible to replace a part of SiO 2 with TiO 2 that is not eroded (reduced) by aluminum in the steel and to mix it with the casting powder. It is.

Finally, there is a technique for reducing the viscosity of the casting powder in the mold. By doing so, the amount of casting powder used is increased, and a larger amount of Al 2 O 3 is removed, and as a result, an equilibrium state is set with a lower content of Al 2 O 3 . This reduction in viscosity is achieved by adding B 2 O 3 (borate), Na 2 O and / or LiO 2 to the casting powder.

  In the following, the equipment for producing a hot-rolled strip according to the present invention is illustrated in a schematic diagram, and the configuration of the method will be described in detail.

  Basically, the equipment used is a well-known CSP equipment. In the present invention, the interval between the individual equipment components is changed, and immediately after solidification, the temperature is equalized in the intermediate furnace in the work process. It is possible to carry out the method according to the invention in such a way that it fulfills the requirement that it is carried out and then immediately hot-rolled without subsequent cooling.

  Correspondingly, the equipment shown in the drawing consists of a thin bloom casting machine 1 and an intermediate furnace 4 arranged thereafter, in which the bloom is divided from the continuous strand 2 after solidification. 3 is brought in. This intermediate furnace 4 is further provided with a rolling facility 5 in which the bloom 3 after the temperature equalization in the intermediate furnace 4 is heated immediately, i.e. without cooling thereafter. It is rolled as an intermediate rolled strip 6.

Schematic diagram of equipment for producing hot rolled strips according to this invention

Claims (6)

  1. Lightweight steel is first cast as a continuous strand (2) in a continuous casting facility (1), divided into blooms (3), then rolled to final thickness, manganese (Mn), methods for containing aluminum (Al) and silicon (Si), for producing a TWIP hot-rolled strip of (twinning induced plasticity) good cold formable high-strength austenitic lightweight steel having a characteristic (6) In
    Predetermined chemical composition with 15 to 27% Mn, 1 to 6% Al, 1 to 6% Si, less than or equal to 0.8% carbon and the balance iron and impurities with respect to the weight percentage of the total weight Based on the process of arranging lightweight steel with
    Casting with casting powder (1) in a thin bloom (d ≦ 120 mm) casting powder and dividing into bloom (3), in which case the reduction reaction rate of SiO 2 by the aluminum in the steel is slowed Or by reducing the Al 2 O 3 content by reducing the viscosity in the mold, or by adding ingredients suitable for realizing both to the casting powder,
    -Immediately following solidification of the continuous strand (2) and division into bloom (3), the temperature is equalized in the intermediate furnace (4) in the working process, then
    -Hot-roll the bloom (3) immediately without cooling after that,
    And
    The casting powder, and having a SiO 2 with increased content before having viscosity (CaO / SiO 2 ratio) of 0.5 to 0.7,
    A method characterized by.
  2. The process according to claim 1, characterized in that the casting powder has Al 2 O 3 with an increased content by more than 10% in terms of weight percentage with respect to the total weight.
  3. Casting powder in question, the method according to claim 1 or 2, characterized in that it contains MnO 2 and / or TiO 2.
  4. To reduce the viscosity of the casting powder in the mold, according to claim casting powder in question, B 2 O 3 to (borate), characterized in that it contains Na 2 O and / or Li 2 O component The method according to any one of 1 to 3 .
  5. Intermediate furnace (4) The method according to any one of claims 1 to 4, characterized in that the roller hearth furnace.
  6. A CSP (Compact Strip Manufacturing) facility, followed by a thin-bloom caster (1), an intermediate component, for carrying out the method according to any one of claims 1-5 , intermediate Composed of a furnace (4) and rolling equipment (5), with respect to the weight percentage of the total weight, 15 to 27% manganese (Mn), 1 to 6% aluminum (Al) and 1 to 6% silicon In a production facility for hot-rolled strips made of high-strength austenitic lightweight steel containing (Si) and well cold-formable with TWIP (twinning induced plasticity) properties,
    Cast in thin bloom casting machine (1) with casting powder, split into bloom (3), and immediately after solidification of continuous strand (2), split in intermediate furnace in process Changing the spacing between these equipment components so that the temperature of the bloom (3) is equalized and then immediately hot rolled without subsequent cooling ;
    The casting powder, and having a SiO 2 with increased content before having viscosity (CaO / SiO 2 ratio) of 0.5 to 0.7,
    Equipment characterized by.
JP2007557433A 2005-03-05 2006-03-03 Method and equipment for producing lightweight steel with high manganese content Expired - Fee Related JP4688890B2 (en)

Priority Applications (3)

Application Number Priority Date Filing Date Title
DE200510010243 DE102005010243A1 (en) 2005-03-05 2005-03-05 Method and plant for producing a lightweight steel with a high manganese content
DE102005010243.3 2005-03-05
PCT/EP2006/001954 WO2006094718A1 (en) 2005-03-05 2006-03-03 Process and installation for producing a lightweight structural steel with a high manganese content

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JP2008531292A JP2008531292A (en) 2008-08-14
JP2008531292A5 JP2008531292A5 (en) 2008-08-14
JP4688890B2 true JP4688890B2 (en) 2011-05-25

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US (1) US20080164003A1 (en)
EP (1) EP1725347B1 (en)
JP (1) JP4688890B2 (en)
CN (1) CN101160183B (en)
CA (1) CA2560681A1 (en)
DE (1) DE102005010243A1 (en)
RU (1) RU2335358C2 (en)
TW (1) TW200700566A (en)
UA (1) UA80237C2 (en)
WO (1) WO2006094718A1 (en)
ZA (1) ZA200607920B (en)

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TR201900039T4 (en) * 2008-01-30 2019-01-21 Tata Steel Ijmuiden Bv Hot-rolled steel to be produced and TWIP-method whereby a TWIP steel product produced.
CN101543837B (en) * 2008-03-24 2012-02-29 宝山钢铁股份有限公司 Method for manufacturing Fe-Mn-C series high-manganese steel thin strip by continuous casting and tandem rolling
DE102009030324A1 (en) * 2009-06-24 2011-01-05 Voestalpine Stahl Gmbh Manganese steel and process for producing the same
DE102010034161B4 (en) * 2010-03-16 2014-01-02 Salzgitter Flachstahl Gmbh Method for producing workpieces made of lightweight steel with material properties that can be adjusted via the wall thickness
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CN106624603A (en) * 2015-10-28 2017-05-10 丹阳市龙鑫合金有限公司 ACP1000 anti-vibration strip assembly and production method thereof
CN106271449A (en) * 2016-08-31 2017-01-04 云南德胜钢铁有限公司 A kind of technique using bloom production fine grain valve snail reinforcing bar
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EP1725347B1 (en) 2012-12-26
KR20070108440A (en) 2007-11-12
WO2006094718A1 (en) 2006-09-14
US20080164003A1 (en) 2008-07-10
UA80237C2 (en) 2007-08-27
JP2008531292A (en) 2008-08-14
RU2006136036A (en) 2008-05-10
ZA200607920B (en) 2008-04-30
TW200700566A (en) 2007-01-01
CA2560681A1 (en) 2006-09-14
CN101160183A (en) 2008-04-09
CN101160183B (en) 2011-07-06
RU2335358C2 (en) 2008-10-10
EP1725347A1 (en) 2006-11-29
DE102005010243A1 (en) 2006-09-07

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