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US20080164003A1 - Method and Installation for Producing Light Gauge Steel with a High Manganese Content - Google Patents

Method and Installation for Producing Light Gauge Steel with a High Manganese Content Download PDF

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US20080164003A1
US20080164003A1 US11/666,535 US66653506A US2008164003A1 US 20080164003 A1 US20080164003 A1 US 20080164003A1 US 66653506 A US66653506 A US 66653506A US 2008164003 A1 US2008164003 A1 US 2008164003A1
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slab
accordance
installation
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light gauge
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US11/666,535
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Jens Kempken
Markus Reifferscheid
Albrecht Girgensohn
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SMS Siemag AG
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    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • 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
    • 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
    • B22D11/10—Supplying or treating molten metal
    • B22D11/11—Treating the molten metal
    • B22D11/111—Treating the molten metal by using protecting powders
    • 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
    • B22D11/14—Plants for continuous casting
    • B22D11/142—Plants for continuous casting for curved casting
    • 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
    • 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
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • 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
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C21D8/0215—Rapid solidification; Thin strip casting

Definitions

  • the invention concerns a method and an installation for producing hot-rolled strip from a highly cold-workable, high-strength, austenitic light gauge steel with increased contents of manganese (Mn), aluminum (Al), and silicon (Si) with TWIP properties (Twinning-Induced Plasticity), wherein the steel is first cast into an endless strand in a continuous casting installation, cut into slabs, and then rolled to the final thickness.
  • Mn manganese
  • Al aluminum
  • Si silicon
  • Austenitic light gauge steels with TWIP properties for use, e.g., in automobile body parts, reinforcing automobile body members, and cryogenic tanks and pipelines have, for example, according to EP 0 889 144 B1, a chemical composition of 10-30% Mn, 1-6% Si, 1-8% Al (with Si+Al ⁇ 12%), with the remainder consisting of Fe.
  • DE 199 00 199 A1 discloses a high-strength light gauge steel with 7-30% Mn, 1-10% Al, 0.7-4% Si, ⁇ 10% Cr, ⁇ 10% Ni, ⁇ 3% Cu, ⁇ 0.5% C, and optionally with the additional alloying elements N, Va, Nb, Ti, and P, which has not only good mechanical properties but also good resistance to corrosion and stress-corrosion cracking.
  • This steel is intended to be cast by continuous casting and hot rolled or to be cast by thin-strip casting with near-net shape.
  • WO 02/101109 A1 discloses a method in which a significant reduction of the offset yield stress and thus an improvement of the formability by hot rolling and cold rolling are achieved by increasing the possible carbon content (C ⁇ 1%) and by adding additional elements, here especially B as well as Ni, Cu, N, Nb, Ti, V, and P.
  • a feedstock (slab, thin slab, or strip) is heated and hot rolled and coiled within specific temperature limits.
  • EP 1 341 937 B1 describes a method in which a steel containing 12-30% Mn is cast in a twin-roll casting machine into a near-net shape thin strip with a thickness of less than 1 mm to 6 mm.
  • the near-net shape strip emerging vertically from the casting gap is cooled by coolants applied to its surface and is then rolled to the final thickness in a single hot rolling pass.
  • the total time interval between the exit from the casting gap and the entry into the rolling stand is about 8 seconds.
  • EP 1 067 203 B1 discloses a method for producing strip made of an Fe—C—Mn alloy in which a thin steel strip with a thickness of 1.5-10 mm and a composition of 6-30% Mn, 0.001 to 1.6% C, ⁇ 2.5 Si, ⁇ 6% Al, ⁇ 10% Cr and other elements is first cast on a twin-roll casting machine and then hot rolled in one or more stages with 10-60% reduction.
  • the objective of the invention is to specify a method and an installation which can be realized as simply as possible and with which high-manganese steels with a given chemical composition can be produced by continuous casting.
  • An installation for carrying out the method is characterized by the features of Claim 7 .
  • Microsegregations that are still present in the strand after solidification are largely removed again by diffusion during passage through the intermediate furnace, for example, through a roller hearth furnace, before the subsequent rolling deformation.
  • the macrosegregations in the slab center are sufficiently equalized during the intense deformation in the hot rolling mill, much like high-grade austenitic steels.
  • the use of the roller hearth furnace of a CSP installation advantageously avoids any relatively great depletion of the alloying elements and oxidation of the grain boundaries due to the short passage time. Depletion of the alloying elements and oxidation of the grain boundaries can cause problems, for example, during the relatively long heating times in the pusher furnace of a conventional hot-rolled wide strip mill in accordance with the prior art.
  • a suitable flux powder is one which has the property of achieving equilibrium very quickly and then undergoing no further change in its lubrication behavior.
  • the flux powder used in accordance with the invention has a high content of Al 2 O 3 of >10%.
  • the SiO 2 content of the flux powder is increased sufficiently to obtain a basicity (CaO/SiO 2 ratio) of 0.5-0.7.
  • MnO 2 is more readily reduced than SiO 2 by the Al in the steel, and thus the SiO 2 is protected from this reduction (protected from loss), an additional measure that can be taken in accordance with the invention is the addition of MnO 2 to the flux powder.
  • TiO 2 it is also possible to add TiO 2 to the flux powder as a partial replacement of the SiO 2 , since TiO 2 also has a vitrifying effect but is not attacked (reduced) by the Al in the steel.
  • the installation is basically a well-known CSP installation, in which, in accordance with the invention, the distances between the individual installation units were changed in such a way that the method of the invention can be carried out with the requirements that temperature equalization is brought about in a continuous-type intermediate furnace immediately after the solidification and that the slab is then immediately hot rolled without intermediate cooling.
  • the installation illustrated in the drawing consists of a thin-slab casting machine 1 and a downstream intermediate furnace 4 , into which the slab 3 is fed after it has solidified and has been cut from the endless strand 2 .
  • the intermediate furnace 4 is followed by a rolling mill 5 , in which the slab 3 , after it has been subjected to temperature equalization in the intermediate furnace 4 , is immediately (i.e., without intermediate cooling) rolled out into hot-rolled strip 6 .

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Metal Rolling (AREA)
  • Continuous Casting (AREA)
  • Heat Treatment Of Steel (AREA)
  • Treatment Of Steel In Its Molten State (AREA)

Abstract

The production of steels with high contents of manganese (Mn), aluminum (Al), and silicon (Si) with TWIP properties (Twinning-Induced Plasticity) by continuous casting is considered difficult or impossible in the present state of the art for various reasons. These reasons include low strength of the strand shell during solidification due to intense microsegregation of Mn, high strength at relatively low temperatures, reactions of the aluminum in the steel with the flux powder, macrosegregation, depletion of the alloying elements near the surface, and oxidation of the grain boundaries during the reheating of slabs in the pusher furnace. Therefore, in accordance with the invention, successively arranged process steps are used to cast light gauge steel with a given chemical composition of 15-27% Mn, 1-6% Al, 1-6% Si, ≦0.8% C, with the remainder consisting of Fe and accompanying impurity elements on a thin-slab casting machine (1) (d≦120 mm) with the use of suitable flux powders, to cut slabs (3) from the endless strand (2) immediately after solidification, to bring about temperature equalization in a continuous-type intermediate furnace (4), and then to hot roll the slab (3) immediately without intermediate cooling.

Description

  • The invention concerns a method and an installation for producing hot-rolled strip from a highly cold-workable, high-strength, austenitic light gauge steel with increased contents of manganese (Mn), aluminum (Al), and silicon (Si) with TWIP properties (Twinning-Induced Plasticity), wherein the steel is first cast into an endless strand in a continuous casting installation, cut into slabs, and then rolled to the final thickness.
  • Austenitic light gauge steels with TWIP properties for use, e.g., in automobile body parts, reinforcing automobile body members, and cryogenic tanks and pipelines have, for example, according to EP 0 889 144 B1, a chemical composition of 10-30% Mn, 1-6% Si, 1-8% Al (with Si+Al≦12%), with the remainder consisting of Fe.
  • DE 199 00 199 A1 discloses a high-strength light gauge steel with 7-30% Mn, 1-10% Al, 0.7-4% Si, ≦10% Cr, ≦10% Ni, ≦3% Cu, ≦0.5% C, and optionally with the additional alloying elements N, Va, Nb, Ti, and P, which has not only good mechanical properties but also good resistance to corrosion and stress-corrosion cracking. This steel is intended to be cast by continuous casting and hot rolled or to be cast by thin-strip casting with near-net shape.
  • The production of high-manganese steels by continuous casting is considered difficult or impossible in the present state of the art for various reasons, namely, low strength of the strand shell during solidification due to intense microsegregation of Mn (danger of breakout at Mn>15%), high strength at relatively low temperatures (installation overloading, cracking problems), reactions of the aluminum in the steel with the flux powder (limitation of function), macrosegregation, hydrogen and/or oxygen absorption by spray water cooling, increased occurrence of nonmetallic inclusions, depletion of the alloying elements near the surface, and oxidation of the grain boundaries during the reheating of slabs in the pusher furnace.
  • In a publication by Spitzer et al.: “Innovative Steel Products—Challenge for Process Development”; Conference Report: Barbara 2001, pp. 71-84, it is stated in this regard that steels with increasing manganese contents are increasingly difficult to cast. For one thing, they have low strength at high temperatures after solidification, since at high manganese contents, manganese becomes highly concentrated in the residual melt and lowers the melting point in the interdendritic regions. This increases the tendency towards sticking-type breakouts, which make continuous casting impossible at Mn contents of 15% or more according to present estimates. On the other hand, the steels have high strength at low temperatures, so that installation overloading occurs during the bending of the steel, and cracking must be expected. In addition, at aluminum contents of several percent, which are used in these steels for the purpose, among others, of reducing the density, reactions occur with the flux powder, which have serious adverse effects on the function of the flux powder.
  • In another publication by Gigacher et al.: “Properties of High-Manganese Steels under Conditions Similar to Continuous Casting”; BHM 149 (2004), No. 3, pp. 112-117, it is stated in summary that the casting of the alloying concepts presented there for the production of TWIP steels is not advantageous for methods with flux powders.
  • The principal problem with the casting of steels with a high Al content (>1%) is the reaction of the Al from the steel with the oxide constituents of the flux powder. The reduction of the SiO2 in the slag by the Al from the steel gives rise to Al2O3, which is absorbed by the slag and causes the basicity of the slag (the CaO/SiO2 ratio) to increase. This leads to very sharp changes in viscosity and in the lubrication conditions in the mold.
  • Due to these difficulties, various approaches for the production of TWIP steels have been taken:
  • WO 02/101109 A1 discloses a method in which a significant reduction of the offset yield stress and thus an improvement of the formability by hot rolling and cold rolling are achieved by increasing the possible carbon content (C≦1%) and by adding additional elements, here especially B as well as Ni, Cu, N, Nb, Ti, V, and P. To produce this steel, a feedstock (slab, thin slab, or strip) is heated and hot rolled and coiled within specific temperature limits.
  • EP 1 341 937 B1 describes a method in which a steel containing 12-30% Mn is cast in a twin-roll casting machine into a near-net shape thin strip with a thickness of less than 1 mm to 6 mm. The near-net shape strip emerging vertically from the casting gap is cooled by coolants applied to its surface and is then rolled to the final thickness in a single hot rolling pass. The total time interval between the exit from the casting gap and the entry into the rolling stand is about 8 seconds.
  • EP 1 067 203 B1 discloses a method for producing strip made of an Fe—C—Mn alloy in which a thin steel strip with a thickness of 1.5-10 mm and a composition of 6-30% Mn, 0.001 to 1.6% C, ≦2.5 Si, ≦6% Al, ≦10% Cr and other elements is first cast on a twin-roll casting machine and then hot rolled in one or more stages with 10-60% reduction.
  • Based on this prior art, the objective of the invention is to specify a method and an installation which can be realized as simply as possible and with which high-manganese steels with a given chemical composition can be produced by continuous casting.
  • The objective with respect to the method is achieved by the characterizing features of Claim 1, which involve the use of successive process steps, in which a light gauge steel with the given chemical composition of 15-27% Mn, 1-6% Al, 1-6% Si, ≦0.8% C with the remainder consisting of Fe and accompanying impurity elements
      • is cast on a thin-slab casting machine (d≦120 mm) with the use of suitable flux powders, which very quickly reach equilibrium and then undergo no further change in their lubrication behavior, and is then cut into slabs,
      • immediately after the solidification and cutting of a slab, temperature equalization is brought about in a continuous-type intermediate furnace, and then
      • the slab is immediately hot rolled without intermediate cooling.
  • An installation for carrying out the method is characterized by the features of Claim 7.
  • In the production of thin slabs, for example, on CSP casting machines (CSP=Compact Strip Production), the strand is withdrawn vertically, bent horizontally after solidification, and then cut into slabs. Therefore, no problems can arise with internal cracks. The production of high-strength austenitic steels without installation overloading is possible and in the meantime has become the state of the art.
  • Microsegregations that are still present in the strand after solidification are largely removed again by diffusion during passage through the intermediate furnace, for example, through a roller hearth furnace, before the subsequent rolling deformation. In the process, the macrosegregations in the slab center are sufficiently equalized during the intense deformation in the hot rolling mill, much like high-grade austenitic steels.
  • In accordance with the invention, the use of the roller hearth furnace of a CSP installation advantageously avoids any relatively great depletion of the alloying elements and oxidation of the grain boundaries due to the short passage time. Depletion of the alloying elements and oxidation of the grain boundaries can cause problems, for example, during the relatively long heating times in the pusher furnace of a conventional hot-rolled wide strip mill in accordance with the prior art.
  • In accordance with the invention, to be able to use the technology of casting TWIP light gauge steels with high Mn and Al contents on a thin-slab casting machine, it is necessary to use a suitable flux powder. In accordance with the invention, a suitable flux powder is one which has the property of achieving equilibrium very quickly and then undergoing no further change in its lubrication behavior.
  • In order, for example, to reduce the reaction rate of the SiO2 reduction by the Al in the steel, the flux powder used in accordance with the invention has a high content of Al2O3 of >10%. Alternatively or additionally, to have more SiO2 available in the equilibrium state, the SiO2 content of the flux powder is increased sufficiently to obtain a basicity (CaO/SiO2 ratio) of 0.5-0.7.
  • Since MnO2 is more readily reduced than SiO2 by the Al in the steel, and thus the SiO2 is protected from this reduction (protected from loss), an additional measure that can be taken in accordance with the invention is the addition of MnO2 to the flux powder.
  • In accordance with the invention, it is also possible to add TiO2 to the flux powder as a partial replacement of the SiO2, since TiO2 also has a vitrifying effect but is not attacked (reduced) by the Al in the steel.
  • Finally, it is also possible to lower the viscosity of the flux powder in the mold. This increases the consumption of flux powder, and more of the Al2O3 that is formed is removed, so that an equilibrium with lower Al2O3 concentrations is established. This reduction in viscosity is achieved by the addition of B2O3 (borate), Na2O, and/or LiO2 to the flux powder.
  • The process diagram of an installation of the invention for producing hot-rolled strip is shown in the schematic drawing and is explained in detail below.
  • The installation is basically a well-known CSP installation, in which, in accordance with the invention, the distances between the individual installation units were changed in such a way that the method of the invention can be carried out with the requirements that temperature equalization is brought about in a continuous-type intermediate furnace immediately after the solidification and that the slab is then immediately hot rolled without intermediate cooling.
  • Accordingly, the installation illustrated in the drawing consists of a thin-slab casting machine 1 and a downstream intermediate furnace 4, into which the slab 3 is fed after it has solidified and has been cut from the endless strand 2. The intermediate furnace 4 is followed by a rolling mill 5, in which the slab 3, after it has been subjected to temperature equalization in the intermediate furnace 4, is immediately (i.e., without intermediate cooling) rolled out into hot-rolled strip 6.

Claims (7)

1. Method for producing hot-rolled strip (6) from a highly cold-workable, high-strength, austenitic light gauge steel with increased contents of manganese (Mn), aluminum (Al), and silicon (Si) with TWIP properties (Twinning-Induced Plasticity), wherein the light gauge steel is first cast into an endless strand (2) in a continuous casting installation (1), cut into slabs (3), and then rolled to the final thickness, wherein successive process steps are used, in which a light gauge steel with the given chemical composition of 15-27% Mn, 1-6% Al, 1-6% Si, ≦0.8% C, with the remainder consisting of Fe and impurities
is cast on a thin-slab casting machine (1) (d≦120 mm) with the use of flux powders and cut into slabs (3), such that suitable mineral substances are added to the flux powders to reduce the reaction rate of the SiO2 reduction by the Al in the steel and/or to reduce the amount of Al2O3 that is formed by lowering the viscosity in the mold,
immediately after the solidification of the endless strand (2) and cutting of a slab (3), temperature equalization is brought about in a continuous-type intermediate furnace (4), and then
the slab (3) is immediately hot rolled without intermediate cooling.
2. Method in accordance with claim 1, wherein the flux powder has an increased Al2O3 content of >10%.
3. Method in accordance with claim 1, wherein the flux powder has an increased SiO2 content with a basicity (CaO/SiO2 ratio) of 0.5-0.7.
4. Method in accordance with claim 1, wherein the flux powder contains MnO2 and/or TiO2.
5. Method in accordance with claim 1, wherein, to lower the viscosity of the flux powder in the mold, the flux powder contains B2O3 (borate), Na2O, and/or LiO2.
6. Method in accordance with claim 1, wherein the intermediate furnace (4) is a roller hearth furnace.
7. Installation for producing hot-rolled strip from a highly cold-workable, high-strength, austenitic light gauge steel with increased contents of manganese (Mn), aluminum (Al), and silicon (Si) with TWIP properties (Twinning-Induced Plasticity) for carrying out the method in accordance with claim 1, which consists of a CSP installation (Compact Strip Production) with the successively arranged installation units thin-slab casting machine (1), intermediate furnace (4), and hot rolling mill (5), wherein the distances between the individual installation units are changed in such a way that immediately after the solidification of the endless strand (2), temperature equalization of a cut slab (3) is brought about in a continuous-type intermediate furnace (4), and then the slab (3) is immediately hot rolled without intermediate cooling.
US11/666,535 2005-03-05 2006-03-03 Method and Installation for Producing Light Gauge Steel with a High Manganese Content Abandoned US20080164003A1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
DE102005010243A 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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US (1) US20080164003A1 (en)
EP (1) EP1725347B1 (en)
JP (1) JP4688890B2 (en)
KR (1) KR101153735B1 (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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CN106653128A (en) * 2015-10-28 2017-05-10 丹阳市龙鑫合金有限公司 Anti-vibration bar assembly for ACP1000 nuclear power plant and method for producing same
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
CN106624601A (en) * 2015-10-28 2017-05-10 丹阳市龙鑫合金有限公司 Anti-vibration strip assembly for nuclear power station and production method thereof
CN106624602A (en) * 2015-10-28 2017-05-10 丹阳市龙鑫合金有限公司 Vibration-resistant bar component for water reactor nuclear power plant ACP1000 and production method of component
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