EP1929055B1 - Procede de traitement d'un feuillard en acier - Google Patents

Procede de traitement d'un feuillard en acier Download PDF

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Publication number
EP1929055B1
EP1929055B1 EP06754580A EP06754580A EP1929055B1 EP 1929055 B1 EP1929055 B1 EP 1929055B1 EP 06754580 A EP06754580 A EP 06754580A EP 06754580 A EP06754580 A EP 06754580A EP 1929055 B1 EP1929055 B1 EP 1929055B1
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EP
European Patent Office
Prior art keywords
heat treatment
annealing
process according
recrystallization
steel strip
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.)
Not-in-force
Application number
EP06754580A
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German (de)
English (en)
Other versions
EP1929055A1 (fr
Inventor
Uwe Paar
Kurt Dr. Prof. Steinhoff
Klaudia Bergmann
Manuel Maikranz-Valentin
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.)
Universitaet Kassel
Volkswagen AG
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Universitaet Kassel
Volkswagen AG
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Publication date
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Publication of EP1929055A1 publication Critical patent/EP1929055A1/fr
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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
    • 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
    • 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
    • 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
    • C21D1/62—Quenching devices
    • C21D1/673—Quenching devices for die quenching
    • 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
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips 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
    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing 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
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment

Definitions

  • the present invention relates to a method of treating steel strip after cold rolling with at least a first heat treatment comprising recrystallization annealing and at least one further subsequent heat treatment comprising hardening.
  • the present invention further provides a sheet metal semifinished product intended for further processing, which was produced by this process, and motor vehicle components, in particular bodywork components of motor vehicles, which were produced from such a semifinished sheet metal product.
  • a heat treatment is usually required after reducing cold rolling. Due to the reducing cold rolling, the steel sheet undergoes considerable strain hardening, which necessitates thermally induced structure formation, since otherwise further processing by means of conventional cold forming technology would not be sufficiently possible. After the cold rolling, therefore, a final heat treatment called recrystallization annealing is required.
  • This recrystallization annealing can be done in a hood or in a continuous furnace.
  • a complete recrystallization is sought and achieved.
  • the steel strip is usually present as a coil during recrystallization annealing. This step of the heat treatment is generally carried out at the steel manufacturer prior to delivery of the semi-finished sheet metal to the processor. As antioxidant protection, the steel strip is usually coated, wherein the coating can take place in combination with the annealing process or as a decoupled process step. The user himself then takes the desired board cut.
  • the DE 34 06 792 A1 describes a process for recrystallization annealing of cold rolled steel strip in a hood furnace under inert gas.
  • the DE 698 15 943 T2 describes a continuous process for continuous annealing of steel sheet under reduced pressure whereby a cold plasma is generated in a gas atmosphere and annealed at about 700 ° C.
  • the JP 62 093 341 A discloses a method of producing a steel strip after cold rolling in which only partial recrystallization occurs in the subsequent heat treatment.
  • high-strength heat-treated steels are used, which are characterized in particular by a very high strength.
  • the user is again subjected to a heat treatment with heating of the blanks to the austenitizing temperature.
  • accelerated cooling (equivalent to quenching) follows to set a hardened microstructure state.
  • This measure can be done for example as a combined forming and quenching in a press tool, which corresponds to the so-called form hardening.
  • the final component geometry and the material strength or toughness of the metallic structure are set by the form hardening.
  • the accelerated heat dissipation within the forming tool leads by the initiation of a phase transformation to the hardening of the component and thus to an increase in the strength.
  • the object of the invention is to provide a method for the treatment of steel strip after the cold rolling of the aforementioned type available, which under principle retention of the previous Sawroute semi-finished sheet supplies, which allows the production of components with improved properties.
  • Core of the present invention is a modified heat treatment after the reducing cold rolling, are controlled by the thermally induced microstructural changes so that the occurred in the previously desired complete recrystallization complete degradation of the very fine grain in the longitudinal direction elongated microstructure is deliberately avoided.
  • a recrystallization annealing is carried out in such a way that a recrystallized fraction in the microstructure of from about 15% to about 45%, preferably from about 20% to about 40%, is achieved.
  • the remnants of the finely grained deformation structure still present due to the partial recrystallization according to the invention also have a positive effect on the subsequent processing step of hardening by the user. For example, it comes through the preheating of the boards for the mold hardening to another structural change that is to ensure a sufficient hot forming capacity in the balance between the interaction of temperature and structure dependence of the yield stress.
  • the preheating during mold hardening can additionally be optimized by reducing the previously very high temperatures (above A C3 in the pure austenite range).
  • the goal is in the foreground, remains of the remaining fine-grained elongated deformation structure of the to obtain reducing cold rolling.
  • These structural components may lead to increased strength due to the fine grain for the form-hardened component, but also due to the remaining deformation structure shares also increased ductility with an immediate positive effect z. B. on the crash behavior when manufactured from the semi-finished sheet metal body according to the invention body parts.
  • the further subsequent heat treatment used in the process of the invention may be a final heat treatment, i. final heat treatment of the component to the user.
  • This final heat treatment may include forming to provide a desired component geometry, e.g. B. a form hardening as mentioned above.
  • the further heat treatment does not necessarily have to be accompanied by a forming.
  • the further, usually final heat treatment comprises shaping in a mold-forming tool.
  • this also includes the case in which the component has already received the final shape and the mold-forming tool serves to ensure that the component retains this shape during the heat treatment (avoidance of distortion, etc.) Cooling provided via a cooling medium or via a mold-forming tool.
  • the method according to the invention is preferably used for the heat treatment of steel strip made of heat-treatable steel, in particular steel strip made of ultra-high-strength steels is heat-treated.
  • steel strip made of ultra-high-strength steels is heat-treated.
  • tempering steels which contain manganese and / or boron as alloying element.
  • the steel grade 22MnB5 is called.
  • the alloying elements manganese and boron promote a rapid structural change, which is advantageous in particular for mold hardening.
  • a further advantage of the method according to the invention lies in the fact that the flow behavior of the material can be controlled during a subsequent transformation by way of direction-dependent structural components which have been retained during the first heat treatment.
  • the recrystallization annealing at a temperature below the recrystallization temperature preferably about 1% to about 10%, more preferably about 2% to about 6% below the Recrystallization takes place.
  • recrystallization is clearly the fastest.
  • a shortening of the annealing time is also possible.
  • the forming process can be more flexibly controlled. Since the annealing cycles can thus be shortened in both annealing treatments, this leads to a significant shortening of the overall process chain.
  • the austenitizing conditions can be changed also in comparison with the conventional methods, in particular, the austenitizing time can be shortened. With such a modified further heat treatment, a better strength / elongation ratio is still obtained than after the conventional process route.
  • the technological progress is clear, which brings the inventive method with it.
  • Table 1 Table 1: ⁇ / b> Melt Analysis of a 22MnB5 (1.5528) C Si Mn P S al Cr tl B 0.19 to 0.25 from 0.15 to 0.40 1.10-1.30 max.0,025 max.0,015 from 0.020 to 0.060 0.15-0.35 0.020 to 0.050 0.0008 to 0.0050
  • the industrial cold rolled on a tandem rolling mill and supplied in the form of panels test material was cut into 600 mm long and 20 mm wide strips.
  • the second strip after the recrystallization samples, was first austenitized.
  • a heating to 900 ° C took place with a holding time of 300 s.
  • the strip was transported via a chain transport to the form hardening tool. Until manual insertion of the strip in the tool passed about 5 s.
  • the tool was closed by lowering a top plate and held in that position for 20 seconds.
  • the sample material cooled down to approx. 70 ° C could be removed. Between each experiment, the tool repeatedly cooled, so that it had a maximum temperature of 40 ° C.
  • the thermoset samples were also split into three tensile specimens and one metallographic specimen.
  • the variation of the austenitizing conditions was limited to an annealing time shortening to 200 s at 900 ° C (conventionally the annealing time is 300 s) and two temperature reductions to 850 ° C and 800 ° C at 300 s annealing time (the conventional annealing temperature is 900 ° C).
  • these three altered austenitizing conditions were performed with subsequent quenching in the tool. Tensile tests and metallographic investigations were also carried out on these conditions.
  • the recrystallized fraction RX in% is plotted against the annealing time in minutes.
  • the greater the difference between annealing temperature and recrystallization temperature (see curve at T 700 ° C), the larger the parameter window, that is, the desired recrystallized portion RX of the structure can be best influenced by varying the annealing time.
  • the graph shows that at this temperature after an annealing time of 20 minutes the recrystallized fraction RX is about 25%, while after an annealing time of about 30 minutes RX is already at about 80%.
  • Fig. 2 The tensile strength (left) and the elongation at break (right) after recrystallization annealing are plotted as important mechanical properties as a function of the recrystallized fraction RX.
  • the values result from experimentally determined data which were obtained after the first heat treatment according to the invention, that is to say after the recrystallization annealing. It can be seen that the tensile strength decreases as the recrystallized fraction RX increases, but at RX between about 20% and about 40%, sufficiently low values in the range of about 620 N / mm 2 and 740 N / mm 2 are still achieved.
  • the elongation at break increases with increasing recrystallized portion RX, where it can be seen that even with RX 20% to 40% good values are achieved and then increase only slightly with further increasing RX.
  • the elongation at break A 50 in% is shown.
  • Fig. 3 shows the mechanical properties after the form hardening as a function of the recrystallized fraction RX before austenitizing.
  • the tensile strength in N / mm 2 is again indicated on the y-axis, and the elongation at break A 50 in% on the right-hand y-axis.
  • the recrystallized fraction RX in% given from left to right increasingly. It can be seen that for an optimum combination of high strengths and high elongation values, an optimum range for RX is about 20% to about 40%.
  • an improvement in the elongation of at least 20% can be achieved.
  • Fig. 4a and 4b illustrate the influence of austenitizing time, ie the duration of the second heat treatment on the mechanical properties after the form hardening.
  • Fig. 4a is the tensile strength in N / mm 2 plotted against the recrystallized fraction RX in%, where two curves for each different annealing times are shown.
  • the annealing time was 200 s or 300 s with the same annealing temperature of 900 ° C. It can be seen that the tensile strength values for the annealing time of 200 s are higher over the entire curve than for the longer annealing time of 300 s.
  • the difference in the tensile strength values increases only slightly with increasing recrystallized fraction RX.
  • Fig. 4a is the tensile strength in N / mm 2 plotted against the recrystallized fraction RX in%, where two curves for each different annealing times are shown.
  • the annealing time was 200 s or 300 s
  • a shortening of the annealing time is also possible in recrystallization annealing itself in that the annealing process can be terminated earlier, namely when the desired degree of recrystallization of, for example, about 20% or about 40% is reached.

Claims (15)

  1. Procédé de traitement d'un feuillard d'acier après le laminage à froid avec au moins un premier traitement thermique, comprenant un recuit de recristallisation, ainsi qu'avec au moins un traitement thermique supplémentaire consécutif, comprenant une trempe, caractérisé en ce que lors du premier traitement thermique, la courbe temps/température est choisie de façon à ce que lors du premier traitement thermique, un recuit de recristallisation s'effectue de telle sorte qu'une part recristallisée d'environ 15 % à environ 45 % soit obtenue dans la structure et que la structure allongée créée par la solidification à froid précédente reste partiellement conservée.
  2. Procédé selon la revendication 1, caractérisé en ce que le traitement thermique supplémentaire consécutif est un traitement thermique final, qui comprend une trempe par refroidissement.
  3. Procédé selon la revendication 2, caractérisé en ce que le traitement thermique supplémentaire consécutif comprend une déformation.
  4. Procédé selon la revendication 1 ou 2, caractérisé en ce que le traitement thermique supplémentaire consécutif comprend un façonnage par l'intermédiaire d'un outil reproduisant la forme.
  5. Procédé selon l'une quelconque des revendications 1 à 4, caractérisé en ce qu'un refroidissement par l'intermédiaire d'un fluide de refroidissement ou par l'intermédiaire d'un outil reproduisant la forme fait suite au traitement thermique supplémentaire consécutif.
  6. Procédé selon l'une quelconque des revendications 1 à 5, caractérisé en ce que le traitement thermique supplémentaire consécutif inclut un échauffement à une température d'austénitisation.
  7. Procédé selon l'une quelconque des revendications 1 à 6, caractérisé en ce qu'on soumet à un traitement thermique un feuillard d'acier en un acier trempable.
  8. Procédé selon l'une quelconque des revendications 1 à 7, caractérisé en ce qu'on soumet à un traitement thermique un feuillard d'acier en un acier à résistance extrême.
  9. Procédé selon l'une quelconque des revendications 1 à 8, caractérisé en ce qu'on traite un feuillard d'acier en un acier contenant du manganèse et/ou du bore en tant qu'élément d'alliage.
  10. Procédé selon la revendication 9, caractérisé en ce qu'on soumet à un traitement thermique un feuillard d'acier en 22MnB5.
  11. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce qu'on contrôle l'aptitude à l'écoulement de la matière ouvrable lors d'une déformation consécutive par l'intermédiaire des parties de structures directionnelles obtenues lors du premier traitement thermique.
  12. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que lors du premier traitement thermique, un recuit de recristallisation s'effectue de telle sorte qu'une part recristallisée d'environ 20 % à environ 40 % soit obtenue dans la structure.
  13. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que le recuit de recristallisation s'effectue à une température inférieure à la température de recristallisation, de préférence inférieure d'environ 1 % à environ 10 %, de façon particulièrement préférée d'environ 2 % à environ 6 % à la température de recristallisation.
  14. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que le temps de recuit lors du recuit de recristallisation est raccourci en comparaison de procédés conventionnels et que de ce fait, il n'est obtenu qu'une recristallisation partielle.
  15. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que lors du traitement thermique supplémentaire consécutif, le temps de recuit est raccourci par rapport à des procédés conventionnels comparables.
EP06754580A 2005-09-22 2006-06-27 Procede de traitement d'un feuillard en acier Not-in-force EP1929055B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102005045466.6A DE102005045466B4 (de) 2005-09-22 2005-09-22 Verfahren zur Behandlung von Stahlband
PCT/EP2006/006184 WO2007033711A1 (fr) 2005-09-22 2006-06-27 Procede de traitement d'un feuillard en acier

Publications (2)

Publication Number Publication Date
EP1929055A1 EP1929055A1 (fr) 2008-06-11
EP1929055B1 true EP1929055B1 (fr) 2010-09-01

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EP06754580A Not-in-force EP1929055B1 (fr) 2005-09-22 2006-06-27 Procede de traitement d'un feuillard en acier

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EP (1) EP1929055B1 (fr)
AT (1) ATE479781T1 (fr)
DE (2) DE102005045466B4 (fr)
WO (1) WO2007033711A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102021203239A1 (de) 2021-03-30 2022-10-06 Volkswagen Aktiengesellschaft Verfahren zur Herstellung einer presshärtegeeigneten Blechplatine mit unterschiedlichen Blechdicken und Verfahren zur Herstellung eines pressgehärteten Blechformteils

Families Citing this family (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102006032617B4 (de) * 2006-07-12 2008-04-03 Universität Kassel Verfahren zur Herstellung eines zum Formhärten geeigneten Blechhalbzeugs
DE102006049146B4 (de) * 2006-10-17 2012-12-27 Braun CarTec GmbH Verfahren zur Herstellung einer aus mindestens zwei miteinander verbundenen Blechteilen bestehenden Baugruppe
DE102009016027A1 (de) * 2009-04-02 2010-10-07 Volkswagen Ag Verfahren zur Herstellung eines Bauteils, insbesondere eines Karosserieteiles, sowie Fertigungsstraße zur Durchführung des Verfahrens

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE1168462B (de) * 1957-06-12 1964-04-23 Cornigliano Societa Per Azioni Verfahren zum Rekristallisationsgluehen von kalt verformtem Stahl
DE3406792A1 (de) * 1984-02-24 1985-08-29 Linde Ag, 6200 Wiesbaden Verfahren und vorrichtung zum gluehen von metallteilen
JPS6293341A (ja) * 1985-10-21 1987-04-28 Kawasaki Steel Corp 加工用冷延鋼板およびその製造方法
BE1010913A3 (fr) * 1997-02-11 1999-03-02 Cockerill Rech & Dev Procede de recuit d'un substrat metallique au defile.
KR100536828B1 (ko) * 1997-09-22 2006-02-28 카가쿠기쥬쯔죠 킨조쿠자이료 기쥬쯔켄큐죠 미세페라이트주체조직강과그제조방법
US20030015263A1 (en) * 2000-05-26 2003-01-23 Chikara Kami Cold rolled steel sheet and galvanized steel sheet having strain aging hardening property and method for producing the same
DE10149220C1 (de) * 2001-10-05 2002-08-08 Benteler Automobiltechnik Gmbh Verfahren zur Herstellung eines gehärteten Blechprofils
DE10149221C1 (de) * 2001-10-05 2002-08-08 Benteler Automobiltechnik Gmbh Verfahren zur Herstellung eines gehärteten Blechprofils
JP4220871B2 (ja) * 2003-03-19 2009-02-04 株式会社神戸製鋼所 高張力鋼板およびその製造方法

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102021203239A1 (de) 2021-03-30 2022-10-06 Volkswagen Aktiengesellschaft Verfahren zur Herstellung einer presshärtegeeigneten Blechplatine mit unterschiedlichen Blechdicken und Verfahren zur Herstellung eines pressgehärteten Blechformteils

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Publication number Publication date
EP1929055A1 (fr) 2008-06-11
WO2007033711A1 (fr) 2007-03-29
DE102005045466A1 (de) 2007-03-29
DE102005045466B4 (de) 2015-10-29
DE502006007789D1 (de) 2010-10-14
ATE479781T1 (de) 2010-09-15

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