EP1378577A1 - Verfahren zum Wärmebehandeln eines verformbaren kaltgewalzten Stahlbandes und so erhaltenes Stahlband - Google Patents

Verfahren zum Wärmebehandeln eines verformbaren kaltgewalzten Stahlbandes und so erhaltenes Stahlband Download PDF

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Publication number
EP1378577A1
EP1378577A1 EP03447154A EP03447154A EP1378577A1 EP 1378577 A1 EP1378577 A1 EP 1378577A1 EP 03447154 A EP03447154 A EP 03447154A EP 03447154 A EP03447154 A EP 03447154A EP 1378577 A1 EP1378577 A1 EP 1378577A1
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EP
European Patent Office
Prior art keywords
temperature
steel strip
steel
process according
annealing temperature
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EP03447154A
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English (en)
French (fr)
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EP1378577B1 (de
Inventor
Annick De Paepe
Jean-Claude Herman
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Centre de Recherches Metallurgiques CRM ASBL
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Centre de Recherches Metallurgiques CRM ASBL
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    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/185—Hardening; Quenching with or without subsequent tempering from an intercritical temperature
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/0447—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing characterised by the heat treatment
    • C21D8/0473—Final recrystallisation annealing
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/0421—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing characterised by the working steps
    • C21D8/0426—Hot rolling

Definitions

  • the present invention relates to the manufacture of steel strips by cold rolling, particularly steel belts for forming treatments, for example stamping deep.
  • the invention relates more particularly to a process for the heat treatment of a steel strip cold rolled, in order to give it a high resistance and great formability.
  • steel strips intended for forming operations are cold-rolled strips.
  • the band has favorable properties, and particular good ductility, for the operations considered. In general, these properties are the result of heat treatments for annealing and well known cooling.
  • the annealing is operated by heating the strip of steel up to an annealing temperature in the intercritical domain of the equilibrium diagram of steel, between transformation points A1 (temperature of the eutectoid) and A3 (minimum temperature at which the austenitic phase ⁇ is the only stable phase of steel).
  • the steel strip is then maintained at this temperature annealing for a time sufficient to convert the initial ferritic structure of steel into a structure mixed ferrite and austenite.
  • We then execute the quenching by suddenly cooling the steel strip up to a temperature below the Ms temperature of transformation of austenite into martensite.
  • the annealing temperature located in the field intercritical between equilibrium points A1 and A3 of steel, is selected to provide training maximum of 20% (preferably 10 to 15%) by volume of austenite in the mixed structure of ferrite and of austenite, in order to give steel high without significantly affecting its ductility.
  • temperatures from 725 to 825 ° C.
  • the temperatures below 350 ° C for example temperatures from 120 to 340 ° C or room temperature.
  • Heat treatment of steel strips according to the method described above is preferably performed in a continuous process, in an installation online.
  • Reasons for investment and congestion at soil impose to limit the duration of the various stages of the process.
  • the heating of the steel strip up to the annealing temperature is carried out at a speed at least 150 ° C / s, advantageously from 150 to 350 ° C / s, the maintaining the steel strip at this temperature does not exceed not 20s and the cooling rate up to the critical quenching temperature Ms is at least 300 ° C / sec (for example 300 to 1000 ° C / s).
  • the invention aims to remedy this disadvantage of the known method described above, in providing a new process for heat treatment a cold-rolled steel strip, which gives it reproducible mechanical strength properties, especially a high ductility and a high resistance, in online industrial installations reduced size.
  • the invention relates to a method for heat treatment of a cold rolled steel strip, comprising heating to an annealing temperature above the temperature A3, a stabilization at said annealing temperature and quenching up to a temperature below the critical temperature Ms of martensitic transformation, the method being characterized in that an annealing temperature is selected greater than the processing temperature A3 austenitic and in that between stabilization at the annealing temperature and quenching, we submit the tape from steel to cooling down to a temperature intermediate located in the intercritical domain between transformation points A1 and A3, and stabilize it at said intermediate temperature.
  • temperatures A1 and A3 are well known in the middle steel.
  • the temperature A1 corresponds to the temperature of the eutectoid of the equilibrium diagram of the iron-carbon alloy. It is around 725 ° C but can vary in function of alloy elements of steel and speed heating the steel strip up to the temperature of annealing.
  • the temperature A3 is the minimum temperature at which phase ⁇ is the only stable phase of steel. It depends on the composition of the steel, particularly its carbon content, and the heating rate up to the annealing temperature.
  • the critical transformation temperature Ms martensitic is also well known in the middle steel. It is the temperature limit under which, during a rapid cooling of the steel since the annealing temperature, the austenite is transformed into martensite without perlite formation. This temperature critical and the cooling rate required for the transformation into martensite depend on the composition of steel and annealing temperature.
  • the annealing temperature is greater than the temperature A3 of the steel, so that the treated steel is then in the austenitic field of the phase equilibrium diagram of steel.
  • the choice of the optimum temperature of the annealing will depend on the composition of steel, especially its carbon content. In the case of a low-alloy steel, including 0.08 at 0.15% by weight of carbon, the annealing temperature is generally above 830 ° C and advantageously between 850 and 880 ° C.
  • Heating the steel strip to the annealing temperature is advantageously carried out at large speed, so as to reduce the bulk of the annealing installation and optimize the structure crystalline steel. Speeds above 100 ° C / sec are recommended, speeds of 100 to 300 ° C / s being preferred.
  • Heating the steel to the temperature annealing can be done in an oven heated by any conventional heating means. This one can for example include natural gas heating, fuel oil or electric induction heating. Such ovens are well known in technique.
  • the steel strip After heating up to the temperature annealing, the steel strip is subjected to a step of stabilization. During this period, the steel strip is kept at the annealing temperature for a while enough to turn the steel into austenite and form a homogeneous austenite. .
  • the duration of this stage of stabilization depends on the temperature at which one the performs and the composition of the steel. This stage of stabilization being carried out in a thermostatically controlled oven, interest in making it as short as possible, for congestion and investment considerations. In practice, it is usually maintained under 1 minute, durations of 1 to 20 s generally suitable.
  • the stabilization at Annealing temperature is followed by cooling up to an intermediate temperature located in the intercritical domain.
  • the domain intercritical is the equilibrium domain of steel, located between the temperature A1 and the temperature A3. It corresponds the field of coexistence of a ferritic phase ⁇ and a austenitic phase ⁇ .
  • the choice of the optimum value for the intermediate temperature will depend on the properties sought for the steel strip subjected to the treatment thermal. In general, it is chosen so that the equilibrium there corresponds to the maximum 20% (for example of 5 to 20% by weight of austenite, the values of 10 to 15% by weight austenite weight generally suitable.
  • This optimum temperature depends on the steel temperature A3 concerned and, consequently, of the composition of the and can easily be determined from the diagram steel balance. In practice, temperatures of 600 to 750 ° C are suitable in most cases.
  • Cooling to temperature intermediary is usually carried out using a gas cooling ("gas jet cooling"). We do it advantageously at a speed greater than 50 ° C./s, example of 100 to 150 ° C / s.
  • Stabilization at intermediate temperature is to maintain the band of steel at the selected intermediate temperature during enough time to transform a fraction of ferrite austenite and achieve equilibrium thermodynamics of the two phases in the presence (ferritic and austenitic).
  • the duration of stabilization at intermediate temperature is usually greater than 2 s. In practice, it is usually at least 5 s. We has no interest in exceeding 25s. The durations of 5 at 15s are generally well suited.
  • the phase of stabilization at the intermediate temperature is performed preferably in a low inertia oven, also called a tunnel oven.
  • the steel strip is subject to a quench. This is to cool the steel strip to a temperature below the temperature critical Ms, with sufficient cooling speed to turn the austenitic phase into martensite without perlite formation.
  • the choice of optimum values for the quenching temperature and the cooling rate is going depend in particular on the composition of the steel and the intermediate temperature. These optimum values can be easily determined by laboratory tests. In practical, we choose a quenching start temperature between 600 and 750 ° C and a cooling rate greater than 100 ° C / s. Quenching can for example be performed by spraying a mist of water and air compressed or by immersion in a hot water bath (for example at a temperature of 70 to 90 ° C). For the cooling down to the quenching temperature, speeds of 300 to 1000 ° C / s are especially recommended.
  • quenching is carried out in immersing the steel strip in a galvanizing bath, ideally a bath of molten zinc at a temperature of 460 to 500 ° C.
  • the steel strip is subjected to an operation of overaging, intended to precipitate soluble carbon formed during the transformation of austenite into martensite.
  • the method according to the invention makes it possible to confer to cold-rolled steel strips of properties optimum mechanical properties, which are reproducible in online industrial facilities, not requiring a Excessive congestion and investment.
  • This result advantage of the process according to the invention in particular the reproducibility of the properties sought, is imputable, on the one hand, at the choice of an annealing temperature which places the point of thermodynamic equilibrium of steel in the austenitic zone and, on the other hand, to precede quenching a cooling down to a temperature intermediate that places the representative point of steel in the intercritical domain.
  • the inventors found that this advantageous result of the process according to the invention originates in the speed of transformation and carbon diffusion in the steel during annealing and during the intermediate cooling that follows this one.
  • the method according to the invention applies to all low carbon steel bands of the type biphasic (or "dual phase") defined above. It suits especially good to LC ('Low Carbon') steel strips cold rolled products of 0.3 to 2 mm thickness, intended for forming as applied in the manufacture of components used in the automotive industry. More particularly, the heat treatment process according to the invention applies especially well to steel strips low carbon and manganese contents, particularly steel strips containing from 0.06 to 0.2% by weight of carbon and from 0.6 to 2.0% by weight of manganese. Examples of LC steels for which the process according to the invention be well understood to include from 0.08 to 0.15% by weight of carbon and 0.6 to 1.5% by weight of manganese. Content silicon is preferably less than 0.5% by weight, for example, between 0.01 and 0.4% by weight.
  • Cold-rolled steel strip in the heat treatment process according to the invention generally comes from a manufactured slab in a hot rolling mill.
  • the invention also a method of manufacturing a steel strip adapted to forming, according to which a steel slab is subjected hot rolling at a temperature in the area austenitic steel, the sheet collected from the hot rolling at a winding at a temperature of 680 to 750 ° C, then to a cold rolling with a reduction rate from 50 to 80% and the sheet collected from the cold rolling to a heat treatment in accordance with the invention.
  • the invention also relates to bands of steel suitable for forming, obtained by means of the manufacture according to the invention, described above, particularly steel belts for the industry automobile.
  • Figure 1 is a diagram schematizing the different operating stages of two distinct processes for the heat treatment of a mild steel strip two-phase structure for forming.
  • Figure 2 is a diagram showing the mechanism of formation of austenite with ordinate the volume fraction indicated by P, from a structure homogeneous ferritic (curve 11) or from a structure homogeneous austenitic (curve 12).
  • the abscissa scale represents the time and the ordinate scale represents the temperatures.
  • the line designated as a whole by the reference notation 1 represents the process of heat treatment of the state of the art.
  • Line referred to as a whole by the reference notation 5 represents a heat treatment process according to the invention.
  • the abscissa scale designates the time and the ordinate scale designates the content in austenite steel.
  • Line 11 corresponds to the treatment according to the state of the art (shown schematically by line 1 in Figure 1) and line 12 corresponds to heat treatment according to the invention (schematized by line 5 in Figure 1).
  • the steel initially in the equilibrium zone of the ferrite is heated to the annealing temperature T 1 located in the intercritical zone of the equilibrium diagram (between the temperatures A1 and A3) .
  • T 1 located in the intercritical zone of the equilibrium diagram (between the temperatures A1 and A3) .
  • a fraction of the ferrite turns into austenite and a substantial time t 1 is required to reach equilibrium.
  • the steel is first heated to the annealing temperature T 2 located in the equilibrium zone of the austenite (higher than the temperature A3 of the equilibrium diagram). The time required to obtain a transformation of all the ferrite into austenite is very short and represented by t 2 . Then, the steel is cooled to the intermediate temperature T 3 located in the intercritical zone of the equilibrium diagram and maintained at this temperature the time required to obtain a transformation of a fraction of austenite to ferrite.
  • each of the examples we implemented a low alloy steel strip (0.1% by weight of carbon and 1.25% by weight of manganese) 0.7 mm thick, from a cold rolling mill.
  • the steel band was subjected to heat treatment, for the purpose of to confer a two-phase structure (or "dual phase") comprising martensite grains dispersed in a ferrite matrix.
  • the steel strip has been subjected to a treatment according to the state of the art, shown schematically by line 1 in Figure 1.
  • This treatment thermal featured a rapid heating 2 of some seconds up to an annealing temperature of 800 ° C, a stabilization 3 at this temperature for 3 minutes and quenching 4 to room temperature.
  • the steel strip has been subjected to a treatment according to the state of the art, shown schematically by line 1 in Figure 1.
  • This treatment thermal featured a quick heating of some seconds up to an annealing temperature of 800 ° C, a stabilization at this temperature for 3 minutes followed cooling in boiling water (2 seconds) up to a temperature of 641 ° C and quenching up to ambient temperature.
  • the steel strip has been subjected to a treatment according to the state of the art, shown schematically by line 1 in Figure 1.
  • This treatment thermal featured a quick heating of some seconds up to an annealing temperature of 800 ° C, a stabilization at this temperature for 3 minutes followed from an air cooling (14 seconds) to a temperature of 516 ° C and quenching to temperature room.
  • the steel strip has been subjected to a treatment thermal device according to the invention, shown schematically by line 5 in Figure 1.
  • This treatment thermal featured a rapid heating 6 of some seconds to an annealing temperature of 865 ° C, a stabilization 7 at this temperature for 40 seconds a rapid intermediate cooling 8 speed greater than 100 ° C / s up to a temperature of 650 ° C, a stabilization 9 at the temperature of 650 ° C for 10 seconds and quench to room temperature.
  • a comparison of the results of Examples 1 to 3 shows that in the method of the prior art a structure stable biphasic ferrite and martensite requires a long-term stabilization at annealing temperature (3 minutes), followed by a slow preliminary cooling (14 seconds) before quenching. In the absence of this slow preliminary cooling, the resulting structure is not stable or reproducible or contains a phase of perlite untimely, detrimental to properties mechanical steel strip.
  • the method of the invention allows to obtain the desired characteristics in term stability of the microstructure and mechanical properties, without requiring a long annealing period, nor a slow cooling before quenching.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
EP03447154A 2002-07-02 2003-06-17 Verfahren zum Wärmebehandeln eines verformbaren kaltgewalzten Stahlbandes und so erhaltenes Stahlband Expired - Lifetime EP1378577B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
BE2002/0421A BE1015018A3 (fr) 2002-07-02 2002-07-02 Procede pour le traitement thermique d'une bande d'acier laminee a froid, procede de fabrication d'une bande d'acier adaptee au fromage et bande d'acier ainsi obtenue.
BE200200421 2002-07-02

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EP1378577A1 true EP1378577A1 (de) 2004-01-07
EP1378577B1 EP1378577B1 (de) 2008-12-03

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EP03447154A Expired - Lifetime EP1378577B1 (de) 2002-07-02 2003-06-17 Verfahren zum Wärmebehandeln eines verformbaren kaltgewalzten Stahlbandes und so erhaltenes Stahlband

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EP (1) EP1378577B1 (de)
AT (1) ATE416265T1 (de)
BE (1) BE1015018A3 (de)
DE (1) DE60324989D1 (de)
ES (1) ES2316713T3 (de)

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2477664A (en) * 2009-03-31 2011-08-10 Kobe Steel Ltd Cold rolled steel sheet with relationship between inclusion separation distance and yield strength
US8460800B2 (en) 2009-03-31 2013-06-11 Kobe Steel, Ltd. High-strength cold-rolled steel sheet excellent in bending workability
EP2794936B1 (de) 2011-12-22 2016-12-28 ThyssenKrupp Rasselstein GmbH Stahlblech zur verwendung als verpackungsstahl sowie verfahren zur herstellung eines verpackungsstahls
EP2794935B1 (de) 2011-12-22 2017-01-11 ThyssenKrupp Rasselstein GmbH Aufreissdeckel für dosen sowie verfahren zur herstellung eines aufreissdeckels

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113373388B (zh) * 2021-04-29 2022-08-05 宝鸡文理学院 一种利用双组织结构提升含硼共晶合金塑韧性的方法

Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2472021A1 (fr) * 1979-12-14 1981-06-26 Nippon Kokan Kk Procede pour fabriquer une bande d'acier a haute resistance laminee a froid ayant une excellente aptitude au formage a la presse
EP0053913A1 (de) * 1980-12-04 1982-06-16 Uss Engineers And Consultants, Inc. Verfahren zur Herstellung von hochfesten tiefziehfähigen Stahlblechen mit Dualphasen-Gefüge
JPS60100630A (ja) 1983-11-07 1985-06-04 Kawasaki Steel Corp 延性と曲げ加工性の良好な高強度薄鋼板の製造方法
US5405463A (en) * 1980-10-24 1995-04-11 Nippon Kokan Kabushiki Kaisha Continuous annealing process of producing cold rolled mild steel sheet excellent in deep drawability and aging resistibility
US5900082A (en) * 1996-04-19 1999-05-04 Naco, Inc. Method of making a heat treated steel casting and a heat treated steel casting
US20010017172A1 (en) * 1999-12-17 2001-08-30 Maruta Kei-Ichi Method for controlling structure of two-phase steel
WO2002000947A1 (fr) * 2000-06-29 2002-01-03 Centre De Recherches Metallurgiques, Association Sans But Lucratif Procede pour la fabrication d'une bande d'acier laminee a froid a haute resistance et haute formabilite

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2472021A1 (fr) * 1979-12-14 1981-06-26 Nippon Kokan Kk Procede pour fabriquer une bande d'acier a haute resistance laminee a froid ayant une excellente aptitude au formage a la presse
US5405463A (en) * 1980-10-24 1995-04-11 Nippon Kokan Kabushiki Kaisha Continuous annealing process of producing cold rolled mild steel sheet excellent in deep drawability and aging resistibility
EP0053913A1 (de) * 1980-12-04 1982-06-16 Uss Engineers And Consultants, Inc. Verfahren zur Herstellung von hochfesten tiefziehfähigen Stahlblechen mit Dualphasen-Gefüge
JPS60100630A (ja) 1983-11-07 1985-06-04 Kawasaki Steel Corp 延性と曲げ加工性の良好な高強度薄鋼板の製造方法
US5900082A (en) * 1996-04-19 1999-05-04 Naco, Inc. Method of making a heat treated steel casting and a heat treated steel casting
US20010017172A1 (en) * 1999-12-17 2001-08-30 Maruta Kei-Ichi Method for controlling structure of two-phase steel
WO2002000947A1 (fr) * 2000-06-29 2002-01-03 Centre De Recherches Metallurgiques, Association Sans But Lucratif Procede pour la fabrication d'une bande d'acier laminee a froid a haute resistance et haute formabilite

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
PATENT ABSTRACTS OF JAPAN vol. 009, no. 241 (C - 306) 27 September 1985 (1985-09-27) *

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2477664A (en) * 2009-03-31 2011-08-10 Kobe Steel Ltd Cold rolled steel sheet with relationship between inclusion separation distance and yield strength
GB2477664B (en) * 2009-03-31 2012-01-18 Kobe Steel Ltd High-strength cold-rolled steel sheet excellent in bending workability
US8460800B2 (en) 2009-03-31 2013-06-11 Kobe Steel, Ltd. High-strength cold-rolled steel sheet excellent in bending workability
EP2794936B1 (de) 2011-12-22 2016-12-28 ThyssenKrupp Rasselstein GmbH Stahlblech zur verwendung als verpackungsstahl sowie verfahren zur herstellung eines verpackungsstahls
EP2794935B1 (de) 2011-12-22 2017-01-11 ThyssenKrupp Rasselstein GmbH Aufreissdeckel für dosen sowie verfahren zur herstellung eines aufreissdeckels
EP2794936B2 (de) † 2011-12-22 2019-10-02 ThyssenKrupp Rasselstein GmbH Stahlblech zur verwendung als verpackungsstahl sowie verfahren zur herstellung eines verpackungsstahls

Also Published As

Publication number Publication date
ATE416265T1 (de) 2008-12-15
DE60324989D1 (de) 2009-01-15
EP1378577B1 (de) 2008-12-03
ES2316713T3 (es) 2009-04-16
BE1015018A3 (fr) 2004-08-03

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