EP1320110A1 - Verfahren zur Herstellung nanokristalliner Ringbandkerne - Google Patents
Verfahren zur Herstellung nanokristalliner Ringbandkerne Download PDFInfo
- Publication number
- EP1320110A1 EP1320110A1 EP02027302A EP02027302A EP1320110A1 EP 1320110 A1 EP1320110 A1 EP 1320110A1 EP 02027302 A EP02027302 A EP 02027302A EP 02027302 A EP02027302 A EP 02027302A EP 1320110 A1 EP1320110 A1 EP 1320110A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- amorphous
- magnetic core
- anisotropy
- band
- incubator
- 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.)
- Granted
Links
Classifications
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/147—Alloys characterised by their composition
- H01F1/153—Amorphous metallic alloys, e.g. glassy metals
- H01F1/15341—Preparation processes therefor
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/147—Alloys characterised by their composition
- H01F1/153—Amorphous metallic alloys, e.g. glassy metals
- H01F1/15333—Amorphous metallic alloys, e.g. glassy metals containing nanocrystallites, e.g. obtained by annealing
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
- H01F41/02—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets
- H01F41/0206—Manufacturing of magnetic cores by mechanical means
- H01F41/0213—Manufacturing of magnetic circuits made from strip(s) or ribbon(s)
- H01F41/0226—Manufacturing of magnetic circuits made from strip(s) or ribbon(s) from amorphous ribbons
Definitions
- Nanocrystalline alloys are common described for example in EP 0 271 657 B1. In as a rule, these are iron-based alloys. It however, other alloys are also conceivable.
- the magnetic properties are essentially determined by the size of the so-called anisotropy energy K, which is composed of several contributions, but typically only the magnetically inducible anisotropy energy K u is used to set the magnetic properties in magnetic cores.
- the size of the magnetically inducible anisotropy energy K u is limited to values less than 100 J / m 3 . Since it is additionally required for most applications that the magnetostriction ⁇ s is as low as possible, the attractive alloy ranges are limited to inducible anisotropy energies in the range of less than 25 J / m 3 .
- the minimum permeability of the magnetic cores is therefore about 5000 or 18,000. It is usually achieved by a so-called heat treatment in a magnetic transverse field. This heat treatment is called cross-field annealing and the resulting BH loop has a so-called "F shape".
- Magnetic cores known from the prior art are each after activation for continuous operation in a temperature range from a maximum of 120 ° C to 150 ° C. Some uses require higher permanent temperature loads and / or lower Permeabilities that are only cut by so-called Magnetic cores or other materials with otherwise disadvantageous Properties can be realized.
- Another way to induce magnetic anisotropy is to induce them via mechanical stresses.
- the so-called voltage-induced magnetic anisotropies can compared to the magnetically induced anisotropies achieve higher anisotropy energies. These higher anisotropy energies in turn improve aging stability.
- the anisotropy incubator is understood in general terms to mean means which cooperate with the first amorphous band in such a way that a mechanical tension is generated in the first amorphous band during the heat treatment, which leads to a permanent directional stress-induced anisotropy K u .
- This can be a body or a material with different Crystallization temperature, a metallic band or be a coating or a support body. Be exploited the different coefficients of thermal expansion of the first amorphous band and the anisotropy incubator and / or the volume shrinkage of an amorphous band nanocrystallization or conventional crystallization.
- either F- or Z-shaped BH loops can be generated.
- the magnetic cores are considerably more resistant to aging than the magnetic cores from the prior art, which in particular allows continuous operating temperatures above 150 ° C.
- the achievable voltage-induced anisotropy K u in the magnetic core is distributed homogeneously or inhomogeneously. This allows magnetic cores to be manufactured with a linear bra loop or with a so-called "soft" junction with saturation.
- the first amorphous ribbons are made of iron-based alloys manufactured as e.g. from the aforementioned EP 0 271 657 B1 are known. However, they are in principle other nanocrystalline alloy systems possible.
- a support body is used as an anisotropy incubator which the first amorphous ribbon is wound.
- a metallic sleeve is provided as a support body.
- the first amorphous band then becomes as tight as possible on it Support body wrapped.
- this tape shrinks during the Nanocrystallization on the support body. This will make it The tape is pulled in the tape direction and perpendicular to the tape surface pressed onto the support body.
- transverse anisotropy is formed in the alloys known from EP 0 299 498 B1.
- This transverse anisotropy in turn results in an F-shaped bra loop.
- the preferred magnetic orientation with this procedure lies not only in the band plane but also perpendicular to it. The anisotropy induced in this way is amplified perpendicular to the strip surface as a result of the pressure on the strip layers of the wound magnetic core.
- the support body Due to the temperature increase necessary for nanocrystallization both the support body and the nanocrystallizing one stretch first amorphous band. typically, the support body has a higher coefficient of thermal expansion as the first amorphous band. This will the inducible tension increases.
- the support body is the present invention, a body made of metal, for example a sleeve made of a non-magnetic material.
- This metallic sleeve can also be part of the fixation of the material can be used.
- the tensile stress and thus the strength of the induced anisotropy K u generated decreases continuously from the inside to the outside, which manifests itself in a "rounded" BH loop. This can be mitigated by giving the first amorphous ribbon the opportunity to distribute the tension more evenly by sliding the ribbon layers through a smooth surface and / or a "lubricating film", at least in the first phase of the shrinkage.
- a coating made of magnesium methylate or other known insulation coatings can be considered as a "lubricating film”.
- Magnetic cores with F-shaped B-H loops according to the invention Processes have been established strikingly low permeability, typically permeabilities less than 5000. They are extremely resistant to aging and almost magnetostriction-free, i.e. (
- a second embodiment of the present invention is an anisotropy incubator with a thin layer second thermal expansion coefficient provided that onto the first amorphous ribbon before winding into a magnetic core is applied.
- the coating can either be irregular or isotropic or anisotropic. With a surface isotropic coating However, tensions also arise across the board as well as along the belt direction, so that with larger widths an isotropic distribution of the first amorphous band slight preferred directions in the band plane is generated. there can undefined B-H loop shapes with high magnetization losses arise.
- anisotropic surface coatings have been preferred proved.
- Anisotropic coatings can, for example done in line shapes.
- the thin layer acting as an anisotropy incubator is typical a metallic layer, preferably on the first amorphous band is electroplated.
- coatings via CVD or PVD processes there are also other coating methods conceivable, in particular coatings via CVD or PVD processes.
- a third embodiment of the present invention is used as an anisotropy incubator with a second band of metal uses a second coefficient of thermal expansion, the first amorphous band and the second band made of metal bifilar be wound into a magnetic core. The so wound The magnetic core is then used to generate the nanocrystalline Alloy structure serving heat treatment subjected.
- a crystalline band is provided as the second band of metal.
- this third embodiment becomes a second amorphous band instead of a crystalline one Tape used.
- This second amorphous band faces a different (second) crystallization temperature for the first amorphous band on.
- the first amorphous band and the second amorphous Bifilar tapes are wound into a magnetic core. Due to the different crystallization temperatures of the two amorphous bands and the associated different Mechanical tension becomes "shrinkage" created between the two originally amorphous bands.
- the result of the heat treatment initially depends on what volume fraction of the first crystallizing amorphous Band is already crystallized when the second amorphous Band begins to crystallize. This will reduce the tension, which the two amorphous bands during the setting the mutually induced anisotropy, controlled.
- the setting parameters for this are the differences in the two Crystallization temperatures, which in turn over the respective alloy compositions of the amorphous bands can be adjusted.
- Another setting parameter is the local heating rate during the heat treatment.
- the magnetostriction ⁇ s and thus the composition of the two amorphous bands also have a significant influence on the size of the induced anisotropy K u .
- the second amorphous band is made of an alloy that during the Heat treatment converted into a nanocrystalline alloy can be.
- the second amorphous band made of an alloy exists, which crystallizes out "normally", i.e. while the heat treatment completely crystallized. Examples for this are those well known from the prior art amorphous cobalt based alloys.
- the nanocrystalline alloys usually so brittle that the winding of nanocrystalline Alloy tapes to magnetic cores very difficult to impossible is.
- the alloys on which the exemplary embodiments are based were selected from the Fe a CO b CU c Si d B e M f K g alloy system, M being at least one of the elements V, Nb, Ta, Ti, Mo, W, Zr and / or Hf and K is at least one of the elements C, P, Ge, As, Sb, In, O, N and the indices a, b, c, d, e, f, g are expressed in atomic percent and the following relationships apply:
- Such an alloy melt became rapid solidification technology amorphous tapes with thicknesses of 12-40 ⁇ m and widths from 1 to 200 mm. To reduce the Eddy current losses between the belt layers in the to be manufactured Magnetic cores among themselves became this first amorphous Apply layers of magnesium methylate to the tape.
- An alloy with a composition of Fe BAL- Cu 1 Nb 3 Si 15.5 B 7 was cast into a first amorphous band.
- the tape had a width of 25mm and was coated with a magnesium methylate.
- This first amorphous tape was wound on a metal sleeve serving as a support body.
- the metal sleeve had a diameter of 26mm and a winding height of 1mm was made.
- the metal sleeve wound in this way was then field-annealed at a temperature of approximately 550 ° C. for one hour.
- the resulting magnetic core had an F-shaped BH loop with a remanence ratio B r / B m of approximately 5%.
- the anisotropy field strength reached was 1200 A / m, which corresponded to a permeability of 800.
- Comparative magnetic cores without the voltage induction according to the invention were annealed in the magnetic field only anisotropy field strengths of 50 A / m on what permeabilities of approximately 20,000.
- the magnetic properties at room temperature and temperatures of approximately 150 ° C were almost identical. amendments the magnetic characteristics after field-free outsourcing of 14 days at 150 ° C, then 2 days at 200 ° C and another 2 hours at 220 ° C were not detectable. To another 10 days at 205 ° C and DC magnetization no changes of 200A / m were also detectable. The comparison magnetic cores, however, were at temperatures above 140 ° changes in magnetic properties clearly detectable after just 10 days.
- the first amorphous strip coated in this way was wound into a magnetic core and then annealed at 550 ° C. for one hour without a field.
- the quasi-static BH loop then showed a coercive field strength H c of 50 mA / cm, a high remanence ratio and an atypically wide BH loop even with high modulation. This could be explained by a superposition of Z and F components in the BH loop due to relatively large induced anisotropy energies K u , the preferred direction of which had an isotropic distribution in the band plane.
- a first amorphous tape with the alloy composition FC Bal Cu 1 Nb 3 Si 12.5 B 8 and a second amorphous tape with the alloy composition Fe BAL Cu 1 Nb 3 Si 16 B 7 were bifilarly wound into a magnetic core with the dimensions 60mm x 40mm x 25mm , The difference in crystallization temperatures between the two alloys was approximately 20 K.
- the bifilar wound magnetic core became field-free at 550 ° C annealed for 1 hour.
- the heating rate was 1 K / min.
- To the heat treatment showed the magnetic core an F-shaped B-H loop with an anisotropy field strength of 120 A / m, which is a Permeability corresponded to 8000.
- the remanence ratio was 5% for the magnetic core thus obtained.
- the first crystallized band showed in the "wrapped" and thus relaxed state a Z-shaped B-H loop.
- the F-shaped B-H loop of the bifilar wound created Magnetic core resulted from the stable existing Tension in connection with the not disappearing Magnetostriction ⁇ s of the first originally amorphous band.
- the influence of the magnetostriction ⁇ s could also be an audible noise when the excitation in the audible Frequency range are verified.
- the magnetic parameters changed after a field-free Aging for 14 days at 150 ° C, 2 days at 200 ° C and 2 hours at 220 ° C not in the detectable range.
- saturated 10 days at 205 ° C with a DC magnetization of 200A / m, (saturation) had the permeability by building up a magnetic field-induced longitudinal anisotropy increased by 15%.
- the magnetic core thus wound was then annealed at a temperature of 550 ° C for 1 hour.
- the resulting magnetic core had a relatively round BH loop with an anisotropy field strength increased compared to reference cores without aluminum tape.
- magnetic cores with Z-shaped bra loops were achieved, for example, which had coercive field strengths H c of 35 mA / cm and remanence ratios of B r / B m of almost 99% at frequencies of 1 Hertz.
- fill factors can be found in the magnetic cores are present, which are in the range between 40% and 95%.
- the magnetic reversal losses of the process according to the invention achievable magnetic cores are in bipolar operation depending on the embodiment and operating conditions at 2-20 times losses according to the classic eddy current theory.
- the magnetic reversal losses are due to operation 1.3-10 times the losses according to the classic eddy current theory. For example, if the anisotropy incubator "Wrapping" removed are magnetic cores with an F-loop Magnetic reversal losses according to the classic eddy current theory
- the magnetic cores produced according to the invention depend on Embodiment very low magnetostrictions, typically Magnetostrictions
- the magnetic cores produced according to the invention have a low dependence of the magnetic parameters on the temperature, are very resistant to aging and have a high permanent temperature resistance.
- permanent temperature load capacities are possible, which are well above 150 ° C.
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- Engineering & Computer Science (AREA)
- Power Engineering (AREA)
- Chemical & Material Sciences (AREA)
- Physics & Mathematics (AREA)
- Electromagnetism (AREA)
- Dispersion Chemistry (AREA)
- Crystallography & Structural Chemistry (AREA)
- Inorganic Chemistry (AREA)
- Materials Engineering (AREA)
- Manufacturing & Machinery (AREA)
- Soft Magnetic Materials (AREA)
- Manufacturing Cores, Coils, And Magnets (AREA)
Abstract
Description
Claims (13)
- Verfahren zum Herstellen eines Magnetkerns aus einer weichmagnetischen Basislegierung, der mindestens 50% Legierungsstruktur von feinkristallinen Teilchen mit einer mittleren Teilchengröße von 100 Nanometer oder weniger eingenommen werden, mit folgenden Schritten:a) Bereitstellen eines ersten amorphen Bandes aus einer Eisenbasislegierungsschmelze mittels Rascherstarrungstechnologie, wobei das amorphe Band einen ersten thermischen Ausdehnungskoeffizienten und eine erste Kristallisationtemperatur aufweist;b) Bereitstellen eines Anisotropieinkubators;c) Wickeln des ersten amorphen Bandes zu einem Magnetkern unter Beteiligung des Anisotropieinkubators;d) Wärmebehandeln des gewickelten Magnetkerns, wobei die amorphe Legierungsstruktur in eine Legierungsstruktur überführt wird, bei der mindestens 50% der Legierungsstruktur von feinkristallinen Teilchen mit einer mittleren Teilchengröße von 100 Nanometer oder weniger eingenommen werden (nanokristalline Legierungsstruktur) und wobei mittels des Anisotropieinkubators eine zeitweise oder permanente mechanische Verspannung im Magnetkern erzeugt wird, die zu einer permanenten, gerichteten, induzierten magnetischen Anisotropie Ku führt.
- Verfahren nach Anspruch 1, wobei als Anisotropieinkubator ein Stützkörper verwendet wird, auf welchen das erste amorphe Band gewickelt wird.
- Verfahren nach Anspruch 2, wobei ein Stützkörper aus Metall oder Keramik verwendet wird.
- Verfahren nach Anspruch 1, wobei als Anisotropieinkubator eine dünne Schicht mit einem zweiten thermischen Ausdehnungskoeffizienten vorgesehen ist, die auf das erste amorphe Band vor dem Wickeln des ersten amorphen Bandes zu einem Magnetkern aufgebracht wird.
- Verfahren nach Anspruch 4, wobei die dünne Schicht anisotrop auf dem ersten amorphen Band aufgebracht wird.
- Verfahren nach Anspruch 4 oder 5, wobei als dünne Schicht eine metallische Schicht vorgesehen ist.
- Verfahren nach einem der Ansprüche 4-6, wobei als metallische Schicht eine Schicht aus Gold, Silber, Kupfer oder Aluminium vorgesehen ist.
- Verfahren nach Anspruch 6, wobei die metallische Schicht auf das erste amorphe Band aufgalvanisiert wird.
- Verfahren nach Anspruch 1, wobei als Anisotropieinkubator ein zweites Band aus Metall mit einem zweiten thermischen Ausdehnungskoeffizienten verwendet wird und wobei das erste amorphe Band und das zweite Band aus Metall bifilar zu einem Magnetkern gewickelt werden.
- Verfahren nach Anspruch 9, wobei als zweites Band ein kristallines Band vorgesehen ist.
- Verfahren nach Anspruch 9, wobei als zweites Band ein amorphes Band mit einer zweiten Kristallisationstemperatur vorgesehen ist.
- Verfahren nach Anspruch 11, wobei die Legierungsstruktur des zweiten amorphen Bandes während der Wärmebehandlung in einer Legierungsstruktur überführt wird, bei der mindestens 50% der Legierungsstruktur von feinkristallinen Teilchen mit einer mittleren Teilchengröße von 100 Nanometer oder weniger eingenommen werden.
- Verfahren nach einem der Ansprüche 9-12 mit folgenden zusätzlichen Schritten:e) Umwickeln des bifilar gewickelten Magnetkerns;f) Entfernen des zweiten Bandes aus Metall undg) erneutes Wickeln des nanokristallinen ersten Bandes zu einem Magnetkern.
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE10161907 | 2001-12-17 | ||
DE2001161907 DE10161907A1 (de) | 2001-12-17 | 2001-12-17 | Verfahren zur Herstellung nanokristalliner Ringbandkerne |
Publications (2)
Publication Number | Publication Date |
---|---|
EP1320110A1 true EP1320110A1 (de) | 2003-06-18 |
EP1320110B1 EP1320110B1 (de) | 2008-11-12 |
Family
ID=7709504
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP20020027302 Expired - Lifetime EP1320110B1 (de) | 2001-12-17 | 2002-12-06 | Verfahren zur Herstellung nanokristalliner Ringbandkerne |
Country Status (2)
Country | Link |
---|---|
EP (1) | EP1320110B1 (de) |
DE (2) | DE10161907A1 (de) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE102015211487B4 (de) | 2015-06-22 | 2018-09-20 | Vacuumschmelze Gmbh & Co. Kg | Verfahren zur herstellung eines nanokristallinen magnetkerns |
CN114959213A (zh) * | 2022-04-13 | 2022-08-30 | 宁波中科毕普拉斯新材料科技有限公司 | 一种高频低损耗铁基纳米晶磁芯的热处理方法 |
Families Citing this family (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE102015107294A1 (de) | 2015-05-11 | 2016-11-17 | Technische Hochschule Köln | Spulenanordnung für Spannungsregler |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS57186306A (en) * | 1981-05-11 | 1982-11-16 | Hitachi Ltd | Magnetic core and manufacture thereof |
JPS58131724A (ja) * | 1982-01-30 | 1983-08-05 | Matsushita Electric Works Ltd | 磁心の製法 |
JP2000277357A (ja) * | 1999-03-23 | 2000-10-06 | Hitachi Metals Ltd | 可飽和磁心ならびにそれを用いた電源装置 |
Family Cites Families (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4413406A (en) * | 1981-03-19 | 1983-11-08 | General Electric Company | Processing amorphous metal into packets by bonding with low melting point material |
JP2975142B2 (ja) * | 1991-03-29 | 1999-11-10 | 株式会社日立製作所 | アモルファス鉄心製造方法及びその装置 |
-
2001
- 2001-12-17 DE DE2001161907 patent/DE10161907A1/de not_active Ceased
-
2002
- 2002-12-06 EP EP20020027302 patent/EP1320110B1/de not_active Expired - Lifetime
- 2002-12-06 DE DE50213003T patent/DE50213003D1/de not_active Expired - Lifetime
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS57186306A (en) * | 1981-05-11 | 1982-11-16 | Hitachi Ltd | Magnetic core and manufacture thereof |
JPS58131724A (ja) * | 1982-01-30 | 1983-08-05 | Matsushita Electric Works Ltd | 磁心の製法 |
JP2000277357A (ja) * | 1999-03-23 | 2000-10-06 | Hitachi Metals Ltd | 可飽和磁心ならびにそれを用いた電源装置 |
Non-Patent Citations (3)
Title |
---|
PATENT ABSTRACTS OF JAPAN vol. 007, no. 033 (E - 157) 9 February 1983 (1983-02-09) * |
PATENT ABSTRACTS OF JAPAN vol. 007, no. 243 (E - 207) 28 October 1983 (1983-10-28) * |
PATENT ABSTRACTS OF JAPAN vol. 2000, no. 13 5 February 2001 (2001-02-05) * |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE102015211487B4 (de) | 2015-06-22 | 2018-09-20 | Vacuumschmelze Gmbh & Co. Kg | Verfahren zur herstellung eines nanokristallinen magnetkerns |
US10538825B2 (en) | 2015-06-22 | 2020-01-21 | Vacuumschmelze Gmbh & Co. Kg | Method for the manufacture of a nanocrystalline magnetic core |
CN114959213A (zh) * | 2022-04-13 | 2022-08-30 | 宁波中科毕普拉斯新材料科技有限公司 | 一种高频低损耗铁基纳米晶磁芯的热处理方法 |
Also Published As
Publication number | Publication date |
---|---|
DE10161907A1 (de) | 2003-06-26 |
EP1320110B1 (de) | 2008-11-12 |
DE50213003D1 (de) | 2008-12-24 |
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