EP2125263B1 - Verfahren und vorrichtung zum temperierten umformen von warmgewalztem stahlmaterial - Google Patents

Verfahren und vorrichtung zum temperierten umformen von warmgewalztem stahlmaterial Download PDF

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Publication number
EP2125263B1
EP2125263B1 EP08701117A EP08701117A EP2125263B1 EP 2125263 B1 EP2125263 B1 EP 2125263B1 EP 08701117 A EP08701117 A EP 08701117A EP 08701117 A EP08701117 A EP 08701117A EP 2125263 B1 EP2125263 B1 EP 2125263B1
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EP
European Patent Office
Prior art keywords
steel
die
shaping
temperature
plate
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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
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EP08701117A
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German (de)
English (en)
French (fr)
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EP2125263A1 (de
Inventor
Hans-Jörg KIRCHWEGER
Karl-Heinz Krenn
Wolfgang Kriegner
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Voestalpine Anarbeitung GmbH
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Voestalpine Anarbeitung GmbH
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Publication of EP2125263A1 publication Critical patent/EP2125263A1/de
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Classifications

    • BPERFORMING OPERATIONS; TRANSPORTING
    • B21MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21DWORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D37/00Tools as parts of machines covered by this subclass
    • B21D37/16Heating or cooling
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B21MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21DWORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/02Stamping using rigid devices or tools
    • 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, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/04Modifying 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
    • 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, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C21D9/48Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets

Definitions

  • the invention relates to a method and a device for tempered forming of hot-rolled steel material.
  • Such forming processes can be carried out both as a hot forming process and as a cold forming process.
  • Fig. 18 The procedure of this procedure is in Fig. 18 shown.
  • the board 101 is arched on the ground.
  • the board 101 can be fixed only in the rest position before deformation in the tool 103.
  • the circuit board 101 is manipulated into the second tool 105 (FIG. Fig. 18 below). In this step, the edges 106, or radii 107 of the workpiece are compressed.
  • embossing of the welding edge can take place.
  • embossing since the indentation is free, a dimensionally pronounced embossing of the edge is difficult to carry out.
  • embossing there is an opposite curvature 108 of the component. This material is pushed into the ground and not used for the expression. However, this causes large upsetting paths to meet the dimensional accuracy of the edge and radii. That is, due to the high compression paths, the tool is subject to a high degree of wear.
  • Typical components that are manufactured in this way are axle bridges of trucks.
  • hot forming is used to reduce the forming force and the bending radii.
  • the bending edges can be compressed, whereby the component undergoes a higher rigidity.
  • Such a method is z. B. from the US 2,674,783 known.
  • this method in the first step, a form and then finally pronounced this preform in a second operation.
  • the component temperature decreases increasingly. This has the consequence that the forming forces increase and just when calibrating, i. the process step with the highest forming force, the forming resistance is very high and reduces the advantage of hot forming. Furthermore, care must be taken that the second transformation must be completed above 750 ° C or 700 ° C.
  • thermocouples were inserted into elongated holes with a diameter of 2 mm and formed with.
  • a detailed view of the forming process shows Fig. 20 , Here it can be seen that the first forming stage at about 790 ° C and the second forming stage at about 680 ° C are completed. However, this means below the minimum forming temperature of 750 ° C, or 700 ° C.
  • Fig. 19 It can also be seen that the conversion of ferrite into austenite either between or during the forming takes place. The exact transformation temperature depends on the alloy composition. The final temperature also indicates that the benefits of hot forming, ie low forming forces, can no longer be asserted in the second forming stage.
  • Normalized annealed or rolled steels achieve their mechanical properties both in the initial state (normalized rolling) and in the annealed condition, provided that this is a normalized annealing.
  • the heat treatment takes place above the A3 temperature. That is, annealing occurs in the single-phase austenitic region. If these steels are cold-formed, a heat treatment should be carried out if the degree of deformation exceeds 5%.
  • the mechanical characteristics are achieved mainly by the formation of a ferritic-pearlitic matrix.
  • the cooling rate must be maintained exactly to ensure the formation of a fine-lamellar perlite. Cooling must be slow, either in still air or in the oven. It is important to ensure that the ferrite and perlite phases are eliminated and that martensite formation is prevented. From 600 ° C, the cooling rate is not critical.
  • the strength of the material is linearly dependent on the Perlitanteil and this in turn of the carbon content. An increase in strength can be achieved for the most part only by a higher carbon content. This means, however, in a further consequence that the weldability decreases. This is recognizable by the increase of the carbon equivalent (see Fig. 15 ).
  • normalized annealed steels For normalized annealed steels, a distinction can be made between normalized rolled products and normalized annealed products, and in the case of normalized rolled products, care must be taken that the last hot rolling is above the austenite recrystallization temperature. This is typically around 950 ° C.
  • the steel recrystallizes completely and the rolling direction is recognizable only due to segregation effects.
  • the recrystallized austenite then converts into ferrite and perlite at a defined cooling rate.
  • boards or components are heated above the A3 temperature and then cooled in a controlled manner. After this heat treatment, the steel recovers the initial properties.
  • the board or component can be formed from the heat. However, it must be ensured that the forming must be completed above 750 ° C. At a degree of deformation of not more than 5%, a temperature of 700 ° C applies.
  • the boards or components are to be cooled in still air.
  • Thermomechanically rolled steels obtain their strength from targeted production during hot rolling.
  • the final strain is carried out below the recrystallization temperature of austenite.
  • the temperature control of the recrystallization is carried out by additional alloying elements. These elements, and here predominantly niobium, increase the re-crystallization temperature of the austenite, so that a sufficient process window arises between the A3 temperature and the recrystallization temperature.
  • the microstructure can no longer recrystallise after the last pass, it has a large number of germs for the transformation of austenite to ferrite due to the stretched rolling structure.
  • the result is a very fine-grained microstructure consisting mainly of ferrite and too little bainite.
  • Bainite is a very fine lamellar pearlite that can only solidify in imbalance. This is done by a controlled rapid cooling after the last pass. An additional effect is an increase in the toughness of the material.
  • Solidification in equilibrium requires slow cooling rates, this applies more to normalizing rolled steels.
  • alloying elements in precipitated form as carbides, nitrides or carbonitrides prevent grain growth above 1100 ° C. This also has an advantageous effect in the coarse grain zone of the heat-affected zone during welding.
  • Normalized annealed steels exhibit critical behavior in the manufacture of hot strip at high strengths due to alloy composition. Due to the lower alloy content of TM steels, they can be produced with significantly higher strengths.
  • Acid gas resistant steels are made in the same process as thermomechanical steels. Due to their field of application, however, they are shown in the standard API spec 51 or DIN EN 10208-2. These sheets are characterized by extremely low levels of impurities such as sulfur. This causes recombination of the hydrogen to H 2 , that is, cracking in the vicinity of manganese sulfides, to be prevented. On the other hand, the toughness is greatly improved even at very low temperatures. Furthermore, the low carbon content reduces the formation of center segregation. This prevents the formation of hard phases in the matrix. To increase the strength, the cooling end temperature must be reduced. The result is a steel with a very fine ferritic microstructure.
  • Fig. 16 A comparison of the manufacturing paths in the hot rolling mill is the Fig. 16 refer to. Here is the difference in the final deformation clearly visible. With the cooling conditions from the rolling heat, the microstructure formation during thermomechanical rolling can still be influenced.
  • the different structures of normalized rolled, or annealed and thermomechanically rolled are the Fig. 17 refer to.
  • T temperature
  • TRS austenite recrystallization temperature
  • TM thermomechanical
  • ACC accelerated cooled
  • the chemical compositions of normalized rolled steel can be found in the standards DIN EN 10149-3 and DIN EN 10025-3.
  • the chemical composition of thermomechanically rolled steel is shown in the standard DIN EN 10149-2. If one compares steel grades with the same minimum yield strength, then the higher carbon contents can be seen in normalized rolled steels.
  • thermomechanical steels show better formability at the same yield strengths.
  • An embossing of the edges, or a weld preparation is not possible in the cold forming, since the forces would be too large. For this reason, an economic design of a press for components with complex geometry is no longer present.
  • the object of the invention is to provide a method which is simple and quick to carry out, with respect to the tool wear is improved and a better controllable Process with lower costs results.
  • the material is indeed heated, but subjected to no phase transformation, that is, the transformation takes place in the ferritic, pearlitic or bainitic region. Neither the eutectoid nor the recrystallization temperature should be exceeded.
  • steels can be used, which at temperatures up to max. 700 ° C stable structure possess.
  • thermomechanically rolled steels since they have a stable structure. These steels are also released for stress relief annealing, which occurs approximately in the same temperature range. When using these steels, care must be taken that no recrystallization occurs during the heating and subsequent forming.
  • Multiphase steels also have martensitic phases in the matrix. However, this martensite is annealed at such high temperatures and thereby changes the mechanical characteristics of the steel grade.
  • the method according to the invention advantageously makes it possible to reshape without scale. While in known forming processes with temperatures of 900 ° C and higher thick scale layers occur in this case, only thin O-xidphase formed on the surface of the workpiece. comparing unhardened hot strip with inventively formed components, no difference in surface formation is apparent.
  • Fig. 1 and 2 show the structure of the tool. Depending on the type of applications, the tool parts can be carried out cooled.
  • the stamp 2 which generates the shape of the component and the Regeleisten to the expression of small radii and, if necessary, the welding preparation.
  • This spring package may consist of steel springs and hydraulic spring / damper systems or gas springs.
  • the die insert 3 In the lower part 11 are the die insert 3 and the die 6 itself.
  • the spring assembly 5 for controlling the die insert 3 may also consist of steel springs and hydraulic spring / damper systems or gas springs.
  • a processing of the welding edge allows the further use of components for component production without a machining intermediate machining of the edge.
  • Fig. 3 shows the necessary forming forces as a function of the temperature on an identical component. From this diagram it can be seen that hot forming at 900 ° C halves the pressing forces compared to tempered forming. However, since the final temperature drops to 700 ° C in the two-stage hot forming process, the forming forces increase to 1.5 times (-..- line). Considering further that two components are in the press, it can be assumed that the press must be designed similarly to the tempered forming. In addition, the increased friction at 900 ° C is clearly visible. While at lower temperatures, the force decreases after the first forming, the Umformwiderstand at 900 ° C remains approximately constant, which suggests increased friction due to the present Zunders in Zargen Symposium. This phenomenon occurs in step 2 in Fig. 18 during the forming.
  • the temperature profile of the tempered forming according to the invention is the example of a transformation of 700 ° C in Fig. 4 seen.
  • the second occurs while a maximum temperature loss of only about 120 ° C.
  • a reduction of the initial temperature of approx. 240 ° C results in a reduction of the final temperature of only 100 ° C.
  • Fig. 5 Another example is in Fig. 5 seen.
  • the board temperature at the beginning of the forming was 500 ° C.
  • the evaluation shows that in the region of the bottom and the frame, the temperature loss is less than 100 ° C, while in the region of the edge, ie at the point where the Regeleisten attack, a reduction in the forming temperature of more than 150 ° C occurs. Due to the heat conduction in the component, however, an immediate increase in the temperature is still the opening of the press.
  • Fig. 6 shows the dependence of the oxidation rate of iron on air as a function of the temperature. If one selects the oxidation rate at 600 ° C as a reference, the rate increases sevenfold at 700 ° C and 230 times at 950 ° C. This makes the advantage of tempered deformation according to the invention clearly.
  • the drastic reduction of oxide formation on the component surface reduces the wear of the tool.
  • the second cost effect is the increase in the cycle time, since the intermediate cleaning of the tool can be many times less, or
  • the cooling rate has only a small influence on the mechanical properties of the material after forming, while with the use of normalizing rolled steels, the cooling rate is an essential function for achieving the mechanical properties.
  • the yield strength increases due to accelerated aging effects. Furthermore, precipitations can still form.
  • Short term temperatures e.g. occur during flame straightening, if they are carried out according to the delivery condition of the starting material, can be carried out analogously to the starting material.
  • thermomechanical steels since the already good formability at room temperature is improved by the tempered forming and the process can be supplemented by upsetting processes.
  • the tempered forming according to the invention does not limit the further processing with respect to welding or surface coatings. This method makes it possible to produce complex components with high strengths without restriction to subsequent processes. Due to the hot forming, for example, only normalizing rolled steels can be used. As already described, these are much more critical to welding due to their alloy composition. In addition, due to the high temperature, the surface needs to be cleaned considerably more expensively.
  • AC1 eutectoid temperature
  • the softening zone With tempered steel (V), the softening zone is designed to be much wider, since it also undergoes transformations below the ACl. In this case, tempering effects occur and thus change the mechanical properties of the material. In addition, due to the higher carbon content, there is an increased carburization in the transition region from the melt to the heat-affected zone. This is particularly critical under dynamic loading as it acts like a metallurgical notch.
  • the method allows, so to speak, the use of standardized steels, provided that the annealing conditions are maintained analogous to stress relief annealing. During production, however, a recrystallization must be avoided during the forming, as this is accompanied by a reduction in strength. Steels are used which have a strong tendency to start, e.g. due to martensitic phases, a loss of strength is to be expected.
  • thermomechanically rolled steel for tempered forming is shown in FIG Fig. 9 shown.
  • the samples were heated to the respective temperature within 15 minutes. In all cases, a complete warming could be ensured. Subsequently, the samples were cooled in air, in water or between two cooled copper plates.
  • the Evaluation shows that up to a temperature of 700 ° C the mechanical properties are at least equal to the initial values. An increase in the yield strength is due to accelerated aging. Above 700 ° C, a change in the structure occurs, the formation of austenite begins. A softening of the thermomechanically rolled steel is the result.
  • the method described above for the production of components by means of tempered forming can be carried out by different tool designs. Furthermore, the functions of springs, hydraulic dampers and gas pressure dampers can also be taken over by the press itself. Depending on the number of pieces and the accuracy of the components, water cooling can be carried out in the tools. In contrast to curing in water-cooled tools, in this case, no such cooling rates must be achieved. The cooling is intended to protect the tool and its functions from thermal stress.
  • the board 1 between the punch 2 and die insert 3 is clamped. This can prevent slippage of the board.
  • the forming is done due to the omission of a die insert, i. the board is not guided.
  • chipping scale can affect the operation of the die insert.
  • Spring 4 and spring 5 are on bias.
  • step 4 can be skipped.
  • Spring 1 is displaced to preload, spring 2 by stamp and the die insert 3 is based on die 6 from.
  • the die insert 3 also serves to eject the component and can accommodate the next board in this position.
  • Board 1 is clamped between die 6 and 2 stamp.
  • a die insert may support the clamping (not shown).
  • F1, F2 and F3 see note in Fig. 11 ,
  • the components are freely deformed when leaving the Matrizen injuredes. F1, F2 and F3 without change.
  • stamp 2 is retracted, this is done by the control of F1. Stamping strips 8 come into contact with the frame 9. F2 and F3 remain unchanged.
  • Top 7 moves down, F3 is completely displaced.
  • F2 is proportionately displaced by this amount. This causes a displacement of the material in the corners, without a high friction occurs in the frame area.
  • Board 1 is clamped between die 6 and 2 stamp.
  • a die insert may support the clamping (not shown).
  • F1 and F2 see note in Fig. 12 ,
  • the components are freely deformed when leaving the Matrizen injuredes. F1 and F2 without change.
  • the bottom area is clamped between punch 2 and 9 Vorwölber. F1 and F2 without change.
  • F1 is displaced by the downward movement of the upper part 7, so that the stamping strips 8 press the component into the die 6 in the corner area.
  • F2 remains unchanged.
  • Stamp 2 and recuperative 8 simultaneously go down and emboss the component. This F2 is displaced.
  • Board 1 is clamped between die 6 and 2 stamp.
  • a die insert may support the clamping (not shown).
  • F1 and F2 see note in Fig. 12 ,
  • the components are freely deformed when leaving the Matrizen injuredes. F1 and F2 without change.
  • the bottom area is clamped between punch 2 and 9 Vorwölber. F1 and F2 without change.
  • the stamp 2 holds its position by controlled displacement of F1.
  • the upper part 7 moves downwards, so that the stamping strips 8 press the component in the corner area into the die.
  • F2 remains unchanged.
  • Stamping bars move to the final dimension of the component and the punch remains in a constant position
  • F1 controls the relative movement to the stamping bar so that the punch position remains constant.
  • F2 remains unchanged.
  • a method and a device are provided, with which a guided deformation, including the upsetting of material, embossing of welding edges and the component ejection within a tool can be performed reliably, quickly and safely, wherein due to the process control, in particular the low temperatures, less wear occurs, the cycle time is increased and more compact furnace systems are available.
  • the scale formation is reduced, which reduces post-processing and gives the opportunity to produce complex components from higher-strength TM steels.
  • bare sheet metal but also coated sheet metal can be used.
  • Suitable coatings are electrolytic or the most diverse hot dip galvanizing, optionally with an alloying step, zinc-aluminum or aluminum-zinc layers, aluminum layers but also nano-layers, etc.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Articles (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Shaping Metal By Deep-Drawing, Or The Like (AREA)
EP08701117A 2007-02-19 2008-01-15 Verfahren und vorrichtung zum temperierten umformen von warmgewalztem stahlmaterial Not-in-force EP2125263B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102007008117A DE102007008117B8 (de) 2007-02-19 2007-02-19 Verfahren und Vorrichtung zum temperierten Umformen von warmgewalztem Stahlmaterial
PCT/EP2008/000261 WO2008101567A1 (de) 2007-02-19 2008-01-15 Verfahren und vorrichtung zum temperierten umformen von warmgewalztem stahlmaterial

Publications (2)

Publication Number Publication Date
EP2125263A1 EP2125263A1 (de) 2009-12-02
EP2125263B1 true EP2125263B1 (de) 2010-06-23

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EP08701117A Not-in-force EP2125263B1 (de) 2007-02-19 2008-01-15 Verfahren und vorrichtung zum temperierten umformen von warmgewalztem stahlmaterial

Country Status (9)

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US (1) US20100187291A1 (ru)
EP (1) EP2125263B1 (ru)
JP (1) JP5226013B2 (ru)
AT (1) ATE471775T1 (ru)
BR (1) BRPI0806212A2 (ru)
DE (2) DE102007008117B8 (ru)
EA (1) EA016031B1 (ru)
ES (1) ES2345741T3 (ru)
WO (1) WO2008101567A1 (ru)

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CN109290744A (zh) * 2018-10-30 2019-02-01 安徽东升达精密机件有限公司 一种转轴及转轴加工方法

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DE102005024627A1 (de) * 2005-05-30 2006-12-07 Mt Aerospace Ag Vakuumgestütztes Verfahren und Vorrichtung zum Umformen eines im Wesentlichen flächigen Rohlings aus Metall zu einem dünnwandigen Schalenkörper sowie deren Verwendung
DE102005055494B3 (de) * 2005-11-18 2007-05-24 Thyssenkrupp Steel Ag Verfahren zum Herstellen von einem Bauteil aus einem metallischen Flachprodukt durch Pressumformen

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102013103751A1 (de) * 2013-04-15 2014-10-16 Thyssenkrupp Steel Europe Ag Verfahren zur Herstellung von hochmaßhaltigen Halbschalen und Vorrichtung zur Herstellung einer Halbschale
US10065229B2 (en) 2013-04-15 2018-09-04 Thyssenkrupp Steel Europe Ag Method for producing highly dimensionally accurate half-shells and apparatus for producing a half-shell
CN109290744A (zh) * 2018-10-30 2019-02-01 安徽东升达精密机件有限公司 一种转轴及转轴加工方法
CN109290744B (zh) * 2018-10-30 2020-01-24 安徽东升达精密机件有限公司 一种转轴及转轴加工方法

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EA200901086A1 (ru) 2010-04-30
ATE471775T1 (de) 2010-07-15
JP5226013B2 (ja) 2013-07-03
JP2010519048A (ja) 2010-06-03
EA016031B1 (ru) 2012-01-30
BRPI0806212A2 (pt) 2011-08-30
EP2125263A1 (de) 2009-12-02
DE102007008117B8 (de) 2009-04-23
WO2008101567A1 (de) 2008-08-28
US20100187291A1 (en) 2010-07-29
ES2345741T3 (es) 2010-09-30
DE102007008117B3 (de) 2008-08-21

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