JP2011061210A - Distributed gap electrical choke - Google Patents
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- 230000035699 permeability Effects 0.000 claims abstract description 30
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 25
- 230000005291 magnetic effect Effects 0.000 claims abstract description 22
- 229910052742 iron Inorganic materials 0.000 claims abstract description 8
- 229910000808 amorphous metal alloy Inorganic materials 0.000 claims abstract description 7
- 238000009826 distribution Methods 0.000 claims description 4
- 230000004907 flux Effects 0.000 claims description 4
- 239000000203 mixture Substances 0.000 claims description 4
- 238000000137 annealing Methods 0.000 abstract description 27
- 238000002425 crystallisation Methods 0.000 abstract description 14
- 230000008025 crystallization Effects 0.000 abstract description 14
- 238000000034 method Methods 0.000 abstract description 9
- 229910001092 metal group alloy Inorganic materials 0.000 abstract 1
- 239000011162 core material Substances 0.000 description 25
- 229910045601 alloy Inorganic materials 0.000 description 4
- 239000000956 alloy Substances 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 230000008569 process Effects 0.000 description 4
- 230000005294 ferromagnetic effect Effects 0.000 description 3
- 238000004626 scanning electron microscopy Methods 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 238000002441 X-ray diffraction Methods 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000004146 energy storage Methods 0.000 description 2
- 239000011261 inert gas Substances 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 239000011230 binding agent Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 230000005684 electric field Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000005284 excitation Effects 0.000 description 1
- 239000003302 ferromagnetic material Substances 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 230000001939 inductive effect Effects 0.000 description 1
- 229910001004 magnetic alloy Inorganic materials 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 239000005300 metallic glass Substances 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 238000001878 scanning electron micrograph Methods 0.000 description 1
- 238000004804 winding Methods 0.000 description 1
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F17/00—Fixed inductances of the signal type
- H01F17/04—Fixed inductances of the signal type with magnetic core
- H01F17/06—Fixed inductances of the signal type with magnetic core with core substantially closed in itself, e.g. toroid
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F27/00—Details of transformers or inductances, in general
- H01F27/24—Magnetic cores
-
- 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
- H01F1/15308—Amorphous metallic alloys, e.g. glassy metals based on Fe/Ni
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F27/00—Details of transformers or inductances, in general
- H01F27/24—Magnetic cores
- H01F27/25—Magnetic cores made from strips or ribbons
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- Engineering & Computer Science (AREA)
- Power Engineering (AREA)
- Microelectronics & Electronic Packaging (AREA)
- Physics & Mathematics (AREA)
- Electromagnetism (AREA)
- Chemical & Material Sciences (AREA)
- Dispersion Chemistry (AREA)
- Soft Magnetic Materials (AREA)
- Cable Accessories (AREA)
- Suspension Of Electric Lines Or Cables (AREA)
- Manufacturing Cores, Coils, And Magnets (AREA)
- Insulation, Fastening Of Motor, Generator Windings (AREA)
Abstract
Description
本発明は、分布ギャップを有する電気チョーク用アモルファス金属磁気コアに関し、より詳細に言えばアモルファスコアを焼鈍して該アモルファスコアに分布ギャップを形成する方法に関する。 The present invention relates to an amorphous metal magnetic core for electric chokes having a distributed gap, and more particularly to a method for annealing a amorphous core to form a distributed gap in the amorphous core.
電気チョークは、エネルギ蓄積インダクタである。トロイダル状のインダクタに関して、蓄積されたエネルギWは、W=1/2[(B2Aclm)/(2μ0μr)]で表され、Bは磁束密度であり、Acはコアの有効磁気面積であり、lmは平均磁束路長であり、μ0は自由空間の透磁率であり、μrは材料の比透磁率である。 The electric choke is an energy storage inductor. For a toroidal inductor, the stored energy W is expressed as W = 1/2 [(B 2 A c l m ) / (2 μ 0 μ r )], B is the magnetic flux density, and A c is the core an effective magnetic area, l m is the mean magnetic flux path length, mu 0 is the permeability of the free space, the mu r is the relative permeability of the material.
小さなエアギャップをトロイドに導入すると、そのようなエアギャップの磁束は強磁性コア材料の磁束と同じ磁束のままである。しかしながら、空気の透磁率(μ〜1)は、代表的な強磁性体材料の透磁率(μ〜数千)よりも著しく小さいので、ギャップの磁界強度(H)は、コアの残りの部分の磁界強度よりも極めて大きくなる(H=B/μ)。磁界に蓄積される単位体積当たりのエネルギWは、W=1/2(B/H)で表され、そのようなエネルギは、主としてエアギャップに集中されることを表している。換言すれば、コアのエネルギ蓄積能力は、ギャップの導入により高められる。上記ギャップは、離散させる(discrete)かあるいは分布させる(distribute)ことができる。分布されたギャップすなわち分布ギャップは、非磁性結合剤で結合した強磁性体粉末を用いることによって、あるいは、アモルファス合金を部分的に結晶化させることによって、導入することができる。アモルファス合金を部分的に結晶化させることによってギャップを導入する場合には、強磁性結晶相が分離して、非磁性マトリックスに包まれる。この部分的な結晶化のメカニズムは、本発明のチョークに関して利用される。 When a small air gap is introduced into the toroid, the magnetic flux in such air gap remains the same as that of the ferromagnetic core material. However, since the permeability of air (μ-1) is significantly smaller than that of typical ferromagnetic materials (μ-thousands), the magnetic field strength (H) of the gap is It becomes extremely larger than the magnetic field strength (H = B / μ). The energy W per unit volume accumulated in the magnetic field is represented by W = 1/2 (B / H), which indicates that such energy is mainly concentrated in the air gap. In other words, the energy storage capacity of the core is enhanced by introducing a gap. The gap can be discrete or distributed. A distributed gap or distribution gap can be introduced by using a ferromagnetic powder bonded with a non-magnetic binder or by partially crystallizing an amorphous alloy. When the gap is introduced by partially crystallizing the amorphous alloy, the ferromagnetic crystal phase separates and is encased in a nonmagnetic matrix. This partial crystallization mechanism is utilized with the chalk of the present invention.
Fe基材のアモルファスコアを焼鈍する原理に基づく電気チョークは、英国特許第2,117,979号A及び、米国特許第4,812,181号に記載されている。上記米国特許第4,812,181号には、Fe基材のアモルファスコアに410℃よりも高い温度で長時問(10時間以上)の焼鈍を行うことによって、平坦な磁化巻線(Flat magnetization loop)を得るための方法が開示されている。上記米国特許に開示されているこの方法は、アモルファスリボンの表面を結晶化し、これにより、該リボンのアモルファスバルクに応力を与える工程を備えている。 Electrical chokes based on the principle of annealing an Fe-based amorphous core are described in British Patent 2,117,979A and US Pat. No. 4,812,181. In the above U.S. Pat. No. 4,812,181, a flat magnetized winding is obtained by annealing an amorphous core of Fe base material at a temperature higher than 410 ° C. for a long time (10 hours or more). A method for obtaining a loop) is disclosed. The method disclosed in the above U.S. patent comprises the step of crystallizing the surface of the amorphous ribbon, thereby stressing the amorphous bulk of the ribbon.
上記英国特許第2,117,979号においては、電気チョークは、Fe基材のアモルファスコアの熱処理作業に基づいて形成されている。最大透磁率は、その初期値の1/50乃至1/30まで減少し(40,000の最大透磁率に関して、上記処理によって、約800から1,300の範囲の値が生ずる)、アモルファスコアは、その体積の10%を超えない一定程度の結晶化を示す。 In the above-mentioned British Patent No. 2,117,979, the electric choke is formed on the basis of a heat treatment operation of the Fe-based amorphous core. The maximum permeability is reduced to 1/50 to 1/30 of its initial value (for a maximum permeability of 40,000, the above process results in a value in the range of about 800 to 1,300) Shows a certain degree of crystallization not exceeding 10% of its volume.
IEEE Transactions on Magnetics(MAG−20(1984) Sep.,No.5,Part2,NY,USA)は、その1415−1416ページにおいて、チョーク及びインダクタ用のFe−B基材のアモルファス合金の開発を議論している。この論文は、高い周波数損失特性を犠牲にする200の透磁率を注記している。
IEEE Transactions on Magnetics (MAG-20 (1984) Sep., No. 5,
欧州特許出願第513385号(EP−A−513−385)は、Fe−B結晶の生成を阻止するためにアルミニウムを必要とする、鉄基材の軟らかい磁気合金を開示している。 European Patent Application No. 513385 (EP-A-513-385) discloses an iron-based soft magnetic alloy that requires aluminum to prevent the formation of Fe-B crystals.
ノートブック型コンピュータ及び他の小型装置用の電源に応用する場合には、小さな透磁率(100−300)、非常に低い鉄損及び飽和磁化性を有すると共に、高いDCバイアス磁界に耐えることのできる、極めて小型の電気チョークが必要とされる。 When applied to power supplies for notebook computers and other small devices, it has low magnetic permeability (100-300), very low iron loss and saturation magnetizability, and can withstand high DC bias fields. A very small electric choke is required.
本発明は、100から400の範囲の透磁率及び低い鉄損(100kHz及び0.1Tで70W/kg未満)を有する、8mmから45mm(OD)の範囲の寸法の電気チョークを提供する。その磁気特性は、DCバイアスの下で維持される(初期透磁率の少なくとも40%が、3980A/m又は50OeのDCバイアス電界の下で維持される)ので効果的である。 The present invention provides an electric choke with dimensions in the range of 8 mm to 45 mm (OD), with permeability in the range of 100 to 400 and low iron loss (less than 70 W / kg at 100 kHz and 0.1 T). Its magnetic properties are effective because it is maintained under DC bias (at least 40% of the initial permeability is maintained under a DC bias field of 3980 A / m or 50 Oe).
また、Fe基材のアモルファス合金を制御した状態で熱処理してアモルファスリボン本体を部分的に結晶化させて、コアに微小ギャップを生じさせるための方法が、本発明によって提供される。分布ギャップが生ずる結果、上述の特性が得られる。 Also, the present invention provides a method for producing a micro gap in the core by heat-treating the Fe-based amorphous alloy in a controlled state to partially crystallize the amorphous ribbon body. As a result of the distribution gap, the characteristics described above are obtained.
より詳細に言えば、本発明によれば、結晶化の度合いと透磁率との間の独特な関係がもたらされる。100から400の範囲の透磁率を得るために、アモルファスコア本体の結晶化が必要とされ、コアの体積の10乃至25%程度を結晶化させるのが好ましい。 More specifically, the present invention provides a unique relationship between the degree of crystallization and the magnetic permeability. In order to obtain a permeability in the range of 100 to 400, crystallization of the amorphous core body is required, and it is preferable to crystallize about 10 to 25% of the core volume.
更に、本発明は、所望のチョーク特性を得るために、ある種の温度及び時間の焼き鈍し処理パラメータ、並びに、これらパラメータの制御度合いを必要とする。 Furthermore, the present invention requires certain temperature and time annealing process parameters and the degree of control of these parameters in order to obtain the desired choke characteristics.
図1は、焼き鈍し処理されたFe基材の磁気コアの透磁率を焼き鈍し処理温度の関数として示している。透磁率は、10kHzの周波数、8回転のジグ及び100mVのAC励磁電圧において、誘導ブリッジで測定した。焼き鈍し処理時間は、6時間で一定とした。総てのコアは、不活性ガス雰囲気中で焼き鈍し処理を受けた。種々の曲線は、化学組成が少し変動し従って結晶化温度が少し変化するFe基材合金を表している。結晶化温度は、示差走査熱量計(DSC)によって測定した。一定の焼き鈍し処理時間に関して焼き鈍し処理温度を増加させると、透磁率の減少が観察された。与えられた焼き鈍し処理温度に関して、結晶化温度に従う透磁率の目盛、すなわち、透磁率は、最も高い結晶化温度を有する合金について最も大きい。 FIG. 1 shows the magnetic permeability of the annealed Fe base magnetic core as a function of the annealing temperature. The permeability was measured with an inductive bridge at a frequency of 10 kHz, an 8 revolution jig and an AC excitation voltage of 100 mV. The annealing treatment time was fixed at 6 hours. All cores were annealed in an inert gas atmosphere. The various curves represent Fe-based alloys with a slight variation in chemical composition and thus a slight change in crystallization temperature. The crystallization temperature was measured by a differential scanning calorimeter (DSC). As the annealing temperature was increased for a certain annealing time, a decrease in permeability was observed. For a given annealing temperature, the permeability scale according to the crystallization temperature, ie the permeability, is the highest for the alloy with the highest crystallization temperature.
図2は、焼き鈍し処理を受けた同じ化学組成を有するコアの透磁率を焼き鈍し処理温度の関数として示している。種々の曲線は、異なる焼き鈍し処理時間を表している。そのプロットは、450℃よりも高い温度に関して、焼き鈍し処理温度の効果は、焼き鈍し処理時間の効果よりも支配的であることを示している。 FIG. 2 shows the permeability of a core having the same chemical composition that has been annealed as a function of the annealing temperature. Various curves represent different annealing treatment times. The plot shows that for temperatures higher than 450 ° C., the effect of annealing treatment temperature is more dominant than the effect of annealing treatment time.
適宜な焼き鈍し処理温度及び焼き鈍し処理時間の条件が、図1及び図2の情報に基づいて、Fe−B−Si基材のアモルファス合金について選択される。この選択は、その合金の結晶化温度(Tx)及び/又は化学組成が既知である場合に行うことができる。例えば、Fe80B11Si9(Tx=507℃)に関して100乃至400の範囲の透磁率を達成するためには、420乃至425℃の範囲の焼き鈍し処理温度で6時間の焼き鈍し処理を行うのが適当である。 Appropriate annealing treatment temperature and annealing treatment time conditions are selected for the Fe-B-Si based amorphous alloy based on the information in FIGS. This selection can be made when the crystallization temperature (T x ) and / or chemical composition of the alloy is known. For example, in order to achieve a magnetic permeability in the range of 100 to 400 with respect to Fe 80 B 11 Si 9 (T x = 507 ° C.), an annealing treatment is performed for 6 hours at an annealing temperature in the range of 420 to 425 ° C. Is appropriate.
図1を再度参照すると、1〜2℃未満の温度変動を維持した場合に、与えられた透磁率の値について再現性及び均一性が得られる。炉の中の温度の均一性及び再現性が確立されるように焼鈍プロセスを行うために、特殊な装填形態が開発された。箱型の不活性ガス炉に関して、ワイヤメッシュのAlプレート(アルミニウム板)2を図3に示すように積み重ね、この構造体を炉の中央に置く。上記Alプレートは、焼き鈍し処理の間にコア1を保持する基材である。 Referring again to FIG. 1, reproducibility and uniformity are obtained for a given permeability value when temperature fluctuations of less than 1-2 ° C. are maintained. Special loading configurations have been developed to perform the annealing process so that temperature uniformity and repeatability in the furnace are established. With respect to the box-type inert gas furnace, wire mesh Al plates (aluminum plates) 2 are stacked as shown in FIG. 3, and this structure is placed in the center of the furnace. The Al plate is a base material that holds the core 1 during the annealing process.
鉄損及びDCバイアスの如き、チョークに関する代表的な磁気特性データが、図4及び図5に示されている。鉄損のデータは、DCバイアス電界の関数としてプロットされており、種々の曲線は、異なる測定周波数を示している。図示のデータは、25mmのOD(外径)を有するコアに関するものである。チョークの性能に関する重要なパラメータは、コアをDCバイアス電界で駆動した時に残る初期透磁率のパーセントすなわち割合である。図5は、35mmのODを有するコアに関する代表的なDCバイアス曲線を示している。 Representative magnetic property data for the choke, such as iron loss and DC bias, is shown in FIGS. Iron loss data is plotted as a function of DC bias field, and various curves show different measurement frequencies. The data shown relates to a core having an OD (outer diameter) of 25 mm. An important parameter for choke performance is the percent or percentage of the initial permeability that remains when the core is driven with a DC bias field. FIG. 5 shows a typical DC bias curve for a core with an OD of 35 mm.
断面走査電子顕微鏡法(SEM)、及び、X線回折法(XRD)を行って、焼き鈍し処理を受けたコアの分布及び結晶化パーセントを測定した。図6は、代表的な断面走査電子顕微鏡写真を示しており、これら写真は、合金の本体及び表面が共に結晶化していることを示している。このことは、表面だけが結晶化される上述の米国特許第4,812,181号に記載されている方法とは容易に区別される。 Cross-sectional scanning electron microscopy (SEM) and X-ray diffraction (XRD) were performed to determine the distribution and percent crystallization of the annealed core. FIG. 6 shows representative cross-sectional scanning electron micrographs, which show that the body and surface of the alloy are both crystallized. This is easily distinguished from the method described in the above-mentioned US Pat. No. 4,812,181 where only the surface is crystallized.
結晶化の体積パーセントをSEM及びXRDの両方のデータから決定し、その結果を透磁率の関数として図7にプロットした。100乃至400の範囲の透磁率に関して、5乃至30%の範囲の本体の結晶化が必要とされる。 The volume percent of crystallization was determined from both SEM and XRD data and the results plotted in FIG. 7 as a function of permeability. For permeability in the range of 100 to 400, crystallization of the body in the range of 5 to 30% is required.
以上本発明をかなり詳細に説明したが、そのような細部に厳密にこだわる必要はなく、当業者には他の変形例及び変更例が自明であり、そのような変形例及び変更例は総て、請求の範囲に示す本発明の範囲に入るものであることを理解する必要がある。 Although the present invention has been described in considerable detail above, it is not necessary to strictly stick to such details, and other variations and modifications will be apparent to those skilled in the art, and all such variations and modifications are obvious. It should be understood that it is within the scope of the present invention as set forth in the appended claims.
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US6144279A (en) * | 1997-03-18 | 2000-11-07 | Alliedsignal Inc. | Electrical choke for power factor correction |
AU746454B2 (en) | 1998-03-02 | 2002-05-02 | Massachusetts Institute Of Technology | Poly zinc finger proteins with improved linkers |
CA2326328A1 (en) * | 1998-03-27 | 1999-09-30 | D. Christian Pruess | Dry-type transformer having a generally rectangular, resin encapsulated coil |
US6534261B1 (en) | 1999-01-12 | 2003-03-18 | Sangamo Biosciences, Inc. | Regulation of endogenous gene expression in cells using zinc finger proteins |
AU776576B2 (en) | 1999-12-06 | 2004-09-16 | Sangamo Biosciences, Inc. | Methods of using randomized libraries of zinc finger proteins for the identification of gene function |
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JPS6324016A (en) * | 1986-04-05 | 1988-02-01 | バク−ムシユメルツエ、ゲゼルシヤフト、ミツト、ベシユレンクテル、ハフツング | Achievement of flat magnetization curve in manetic core of amorphous material |
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US4300950A (en) * | 1978-04-20 | 1981-11-17 | General Electric Company | Amorphous metal alloys and ribbons thereof |
GB2117979B (en) * | 1982-04-01 | 1985-06-26 | Telcon Metals Ltd | Electrical chokes |
JPS62186506A (en) * | 1986-02-12 | 1987-08-14 | Meidensha Electric Mfg Co Ltd | Annealing method of amorphous iron core |
JP2868121B2 (en) * | 1987-07-28 | 1999-03-10 | 日立金属株式会社 | Method for producing Fe-based magnetic alloy core |
JP3322407B2 (en) * | 1990-11-30 | 2002-09-09 | 三井化学株式会社 | Fe-based soft magnetic alloy |
KR950014314B1 (en) * | 1990-11-30 | 1995-11-24 | 미쓰이세끼유 가가꾸고오교오 가부시끼가이샤 | Iron-base soft magnetic alloy |
JPH04341544A (en) * | 1991-05-17 | 1992-11-27 | Mitsui Petrochem Ind Ltd | Fe base soft magnetic alloy |
US5252144A (en) * | 1991-11-04 | 1993-10-12 | Allied Signal Inc. | Heat treatment process and soft magnetic alloys produced thereby |
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JPS6324016A (en) * | 1986-04-05 | 1988-02-01 | バク−ムシユメルツエ、ゲゼルシヤフト、ミツト、ベシユレンクテル、ハフツング | Achievement of flat magnetization curve in manetic core of amorphous material |
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CN1114217C (en) | 2003-07-09 |
KR100452535B1 (en) | 2004-12-17 |
TW351816B (en) | 1999-02-01 |
KR19990076747A (en) | 1999-10-15 |
CN1208497A (en) | 1999-02-17 |
EP0873567A1 (en) | 1998-10-28 |
JP4629165B2 (en) | 2011-02-09 |
ATE215727T1 (en) | 2002-04-15 |
WO1997025727A1 (en) | 1997-07-17 |
DE69711599D1 (en) | 2002-05-08 |
JP4990389B2 (en) | 2012-08-01 |
JP2000503169A (en) | 2000-03-14 |
DE69711599T2 (en) | 2002-10-31 |
EP0873567B1 (en) | 2002-04-03 |
DK0873567T3 (en) | 2002-07-01 |
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