WO2001027946A1 - Modules d'interface pour reseaux de donnees locaux - Google Patents

Modules d'interface pour reseaux de donnees locaux Download PDF

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Publication number
WO2001027946A1
WO2001027946A1 PCT/EP2000/009882 EP0009882W WO0127946A1 WO 2001027946 A1 WO2001027946 A1 WO 2001027946A1 EP 0009882 W EP0009882 W EP 0009882W WO 0127946 A1 WO0127946 A1 WO 0127946A1
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WO
WIPO (PCT)
Prior art keywords
alloy
interface module
permeability
module according
magnetic
Prior art date
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PCT/EP2000/009882
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German (de)
English (en)
Inventor
Johannes Beichler
Johannes Binkofski
Ralf Heindel
Dirk Heumann
Harald Hundt
Jörg PETZOLD
Norbert Preusse
Ulrich PÜTZ
Original Assignee
Vacuumschmelze Gmbh
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Publication date
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Priority to EP00972702A priority Critical patent/EP1221169A1/fr
Publication of WO2001027946A1 publication Critical patent/WO2001027946A1/fr

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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
    • H01F1/15316—Amorphous metallic alloys, e.g. glassy metals based on Co
    • 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
    • H01F19/00—Fixed transformers or mutual inductances of the signal type
    • H01F19/04—Transformers or mutual inductances suitable for handling frequencies considerably beyond the audio range
    • H01F19/08—Transformers having magnetic bias, e.g. for handling pulses
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F3/00—Cores, Yokes, or armatures
    • H01F3/04—Cores, Yokes, or armatures made from strips or ribbons
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F38/00—Adaptations of transformers or inductances for specific applications or functions
    • H01F38/14—Inductive couplings

Definitions

  • the invention relates to an interface module for local data networks with at least one inductive component for coupling interface circuits to a data line used to connect computers.
  • Such modules are also referred to as A modules.
  • I DC 8mA
  • the number of turns for ferrites must be high, typically 20 to 40 turns for 100 Mbit / s Ethernet transmitters.
  • the high number of turns leads to manufacturing disadvantages, for example when designing the transformers using planar technology.
  • LAN interface modules with ferrite cores take up a lot of space.
  • the main inductance maintains its value even with a maximum direct current preload of 8 mA in a temperature range from -40 ° C to 85 ° C, but preferably up to 120 ° C.
  • the permeability of the ferrites mentioned at the outset, in particular the MnZn ferrites fluctuates in the temperature range from -40 ° C. to 120 ° C. in some cases by more than +/- 40%. These fluctuations are undesirable.
  • the task is solved by an inductive component with a magnetic core made of an amorphous cobalt-based alloy or a nanocrystalline iron-based alloy, which have permeabilities ⁇ > 30000.
  • the main frequency range extends from local data networks to 10 MHz (10 Mbit / s Ethernet) or up to 125 MHz (100 Mbit / s Ethernet) or even higher in the case of Gigabit Ethernet.
  • 10 Mbit / s Ethernet 10 Mbit / s Ethernet
  • 125 MHz 100 Mbit / s Ethernet
  • ferrite cores helps to achieve the required level of indication
  • I DC up to 8mA high number of turns necessary. These lead to high coupling and winding capacities as well as a large leakage inductance. These influences have a negative impact on the pulse shape, due to overshoots and long rise and fall times.
  • amorphous and nanocrystalline alloys can also be adjusted to average permeability values in the range from 12,000 to 80,000 and generally have a high degree of saturation.
  • nanocrystalline and amorphous alloys it is therefore possible to coordinate the geometric dimensions of a magnetic core, its permeability and the number of turns so that small designs are possible. It should be particularly emphasized that the number of turns can be set to optimal values, so that there is at the same time a low leakage inductance and winding capacity.
  • amorphous and nanocrystalline magnetic cores can be used to create interface modules that meet the requirements for the signal form in accordance with standards and are also characterized by a particularly small construction volume and the possibility of cost-effective production using planar technology.
  • Figure 1 shows an overview of part of a local data network
  • Figure 2 shows an embodiment of a circuit of inductive components in an interface module
  • Figure 3 is a diagram showing the dependency of the real part of the permeability in the serial equivalent circuit diagram for a nanocrystalline alloy and a ferrite;
  • Figure 4 is a diagram showing the dependence of the inductance in the parallel equivalent circuit diagram of a coil with a nanocrystalline magnetic core and a coil with a ferrite core on the direct current load;
  • FIG. 5 shows the temperature dependency of the permeability of amorphous and nanocrystalline alloys in comparison to the temperature dependence of the permeability of ferrites
  • FIG. 6 shows the frequency response of the real part of the permeability of a nanocrystalline alloy compared to a ferrite
  • FIG. 7 shows the frequency response of the inductance in the parallel replacement circuit diagram for a coil with a magnetic core made of a nanocrystalline alloy and for coils of ferrite cores;
  • FIG. 8 shows the frequency response of the ohmic resistance in the parallel equivalent circuit diagram for a magnetic core made of a nanocrystalline alloy
  • FIG. 9 shows the frequency response of the insertion loss that can be achieved with the nanocrystalline magnetic core from FIGS. 7 and 8; and
  • Figure 10 shows an example of a flat hysteresis loop of a magnetic core made of a nanocrystalline alloy.
  • Local data networks or LANs are used to connect computers (PCs, workstations, mainframes) for data transmission over short distances.
  • LANs Local Area Networks
  • transmission standards IEEE 802.3, Ethernet, IEEE 802.4 (Token Bus), IEEE 802.5 (Token Ring), transmission rates (e.g. 10 MBit / s, 100 MBit / s for Ethernet) and physical transmission medium (RG58 coaxial cable, twisted pair , Fiber optic, etc.)
  • Computers can be interconnected via different topologies (star, bus, ring), thereby, as shown in FIG.
  • the interface module 5 in FIG. 2 comprises a transformer 7, as well as current-compensated chokes 8, which each have magnetic cores 9.
  • the magnetic cores 9 can be made of the same or different material.
  • the interface module can have further inductive components such as transformer, throttle and filter components.
  • Ethernet as systems representative of all these LAN technologies.
  • the main frequency range of the signals is ⁇ 10 MHz for 10 Mbit / s Ethernet and ⁇ 125 MHz for 100 Mbit / s Ethernet.
  • Interface modules 5 however, higher transmission rates (e.g. for Gigabit Ethernet) are also conceivable.
  • the inductive components presented here are inductive components for the LAN interface module 5, which contain the magnetic core 9 in the form of a small metal band core made of an amorphous or nanocrystalline alloy instead of a ferrite core.
  • This receives its standard-compliant properties through an optimized combination of strip thickness, alloy and heat treatment in the magnetic field as well as core technological manufacturing steps.
  • a first basic requirement is that the inductance of the LAN transmitter 7 is greater than 350 ⁇ H at 100 kHz. This must be ensured in the entire temperature range from 0 to 70 ° C or even from -40 ° C to + 85 ° C, possibly even from -40 ° C to + 120 ° C, with a direct current of up to 8 mA. 3, 4 and 5 show, this requirement was met with a correctly coordinated alloy, core dimension and winding, for example with nanocrystalline, but also with amorphous alloys.
  • FIG. 3 is a diagram in which the real part of the permeability is plotted in the serial equivalent circuit diagram against the strength of the constant field.
  • the solid curve shows the dependence of the real part of the permeability of the nanocrystalline alloy (FeCuNb) 77.5 (SiB) 22/5
  • the dashed curve shows the dependence of the real part of the permeability of a MnZn ferrite with the trade name (“Ferronics B ”) implies.
  • Figure 4 shows the ideal inductance of the transformer 7 as a function of the DC bias.
  • the dashed line is the ideal inductance of a transmitter with an MnZn ferrite core (“Ferronics B”) with an initial permeability of] x x - 5000 and 20 turns. From FIG. 4 it can be seen that the transmitter 5 with the magnetic core 9 made of the nanocrystalline alloy meets the requirements despite the small number of turns fulfilled much better than the transformer with the ferrite core.
  • FIG. 5 shows the relative change in permeability based on the permeability at room temperature in percent for different materials.
  • a first steeply rising curve represents the temperature change of a MnZn ferrite with the trade name "Siferrit N27".
  • the permeability of a further MnZn ferrite (“Ferronics B”) fluctuates in the temperature range from -40 to 120 ° C by more than +/- 40%.
  • the relative change in permeability for the nanocrystalline Fe7 3.5 Cu ⁇ Nb 3 Si ⁇ s, 5 B 7 and the amorphous (CuFi) 72 (MuMnSiB) 2B is in the range of +/- 20%.
  • a second basic requirement is that the insertion loss a E of the transmitter 7 is as low as possible over the entire frequency range.
  • a E values of well below 1 dB can be achieved at f> 100 kHz.
  • the insertion loss decreases with increasing value for R p .
  • R p is the ohmic resistance in the parallel equivalent circuit diagram for the transformer 7, which represents the remagnetization losses in the magnetic core 9 and the ohmic copper losses of the winding.
  • the relationship p mec h can be related
  • R p (f) 2 * ⁇ r N ⁇ * 1 / Pmech J (A Fe / l Fe ⁇ * B 7P Fe ( f
  • Pre (f) represents the frequency response of the specific total losses, which in turn depend on the hysteresis and the band properties. At the frequencies considered here of more than 100 kHz and extremely linear hysteresis loops, however, only play 8th
  • R p values can also be achieved with the low number of turns sought here.
  • particularly high R p values can be achieved with the lowest possible strip thicknesses of ⁇ 20 ⁇ m, better ⁇ 17 ⁇ m or, if possible, even ⁇ 14 ⁇ m.
  • the R p value can be further improved by coating at least one strip surface with an electrically insulating medium, which must have a small dielectric number of ⁇ r ⁇ 10.
  • a third basic requirement is that the leakage inductance L s of both the transformer 7 and the current-compensated chokes 8 is as small as possible. This is based on the requirements of ANSI X3.263 1995 points 9.1.3. (Flooding of the signal), 9.1.6. (Rise times of the signal) and 9.1.5. (Reflection loss requirements). A large leakage inductance causes an overshoot and a long rise time of the signal. At higher signal frequencies, the reflection attenuation is reduced by a large scattering ductility. Because of the core geometry used
  • the magnetic cores 9 have a high saturation induction of B s > 0.55 T, preferably> 0.9 T, better> 1 T and a linear hysteresis loop with a saturation to remanence ratio B r / B s ⁇ 0.2, preferably
  • the magnetostriction-free nanocrystalline materials based on Fe are characterized by a particularly high saturation induction of 1.1 T or more.
  • a list of all considered and suitable alloy systems can be found below.
  • a typical loop shape can be seen in FIG. 10. Such a hysteresis loop can be achieved, for example, by the production steps described below:
  • Mg which is applied to the strip surface as a liquid magnesium-containing preliminary product and, during a special heat treatment that does not affect the alloy, is converted into a layer of MgO, the thickness of which can be between 50 n and 1 ⁇ m ,
  • the magnetic core 9 consists of an alloy which is suitable for setting a nanocrystalline structure or not.
  • Magnetic cores 9 made of alloys which are suitable for nanocrystallization are subjected to a precisely coordinated crystallization heat treatment for adjusting the nanocrystalline structure, which is between 450 ° C. and 690 ° C. depending on the alloy composition. Typical holding times are between 4 minutes and 8 hours. Depending on the alloy, this heat treatment can be carried out in a vacuum or in a passive or reducing protective gas. In all cases, material-specific cleanliness conditions must be taken into account, which can be brought about by appropriate aids such as element-specific absorber or getter materials.
  • annealing is carried out either in a field-free manner or in a magnetic field along the direction of the wound strip (“longitudinal field”) or transversely thereto (“transverse field”) in order to achieve high permeability values.
  • longitudinal field the direction of the wound strip
  • transverse field transversely thereto
  • a combination of two or even three of these magnetic field constellations may be necessary in succession or in parallel.
  • the magnetic properties ie the linearity and the slope of the hysteresis loop
  • temperatures between 350 ° C and 690 ° C are required. Due to the kinetics of the atomic reorientation processes, the lower the cross-field temperature, the higher the resulting permeability values.
  • This magnetic field heat treatment is either combined directly with the crystallization heat treatment or carried out separately.
  • the magnetic properties ie the shape and gradient of the linear flat hysteresis loop
  • the magnetic properties are created by a heat treatment in a magnetic field that runs parallel to the axis of symmetry of the magnetic core 9 - that is, perpendicular to the band direction.
  • Favorable management of the heat treatment takes advantage of the fact that the value of the saturation agnostriction changes during the heat treatment in a positive direction, depending on the alloy composition, until it reaches the range ⁇ s
  • a reducing for example NH 3 , H 2 , CO
  • passive or even weakly oxidizing protective gas for example He, Ne, Ar, N 2 , C0 2
  • Oxidation or other reactions can occur. Nor can solid-state physical reactions due to diffusing protective gas be allowed to take place inside the material.
  • Particularly small magnetic cores 9 for LAN transmitters 7 can be achieved if the amorphous alloys used on the one hand have low Curie temperatures of, for example, less than 250 ° C., but on the other hand still have a sufficiently high saturation induction of, for example, 0.65 Tesla or more.
  • contradictory combinations can be achieved by gradually increasing the metalloid content (eg Si, B etc.) of the alloy and / or at the same time adding an antiferromagnetic element such as Mn in the range of less at% of the alloy.
  • the wound magnetic core 9 in the form of a metal strip core must be relaxed by means of a relaxation anneal even at the smallest magnetostriction values.
  • the temperature required for this is to be set so high that the relaxation kinetics on the one hand proceed sufficiently quickly, but on the other hand no crystallization occurs yet. This procedure is particularly effective when the crystallization and Curie temperatures are far more than 100 ° C apart, which is the case with the amorphous alloys with high metalloid content used here. 14
  • the magnetic cores 9 are electrically insulated (for example surface passivated, coated, whirl sintered or encapsulated in a plastic housing), provided with the primary and secondary windings and, if appropriate, glued or cast in the component housing. It is also possible to use a structure in so-called planar technology. This method is independent of whether the magnetic core 9 consists of amorphous or nano-crystalline material. Due to the brittleness, however, the mechanical handling of the tempered nanocrystalline magnetic cores 9 must be carried out with particular care. 15
  • the main inductance of the magnetic core 9 in the form of a wound metal strip core must meet the following condition:
  • the main inductance fulfills this value even with a maximum direct current preload of 8 mA in a temperature range from -40 ° to 85 ° C, when using nanocrystalline alloys also up to 120 ° C.
  • the error in the hysteresis loop of the magnetic core 9 is so small that the ratio of permeability ⁇ to the mean permeability ⁇ is in the range
  • Bs / 100 to 0.8 B s applies: 1.2> ⁇ (B) / ⁇ > 0.8, preferably 1.1> ⁇ (B) / ⁇ > 0.9, B likewise in the interval B s / 100 to 0.8 B 3 .
  • the cross-section tempering for predetermined values of the main inductance results for example, in the typical dimensions of the magnetic core 9 shown in Table 1, the dimensions being in the order of the outside diameter, inside diameter and height of the ring ring core present magnetic core 9 are specified.
  • the LAN interface modules 5 realized with these magnetic cores 9 have a large volume advantage over the ferrite cores due to their design, the high permeability and the high saturation induction of the metal strip cores used.
  • equation (1) is decisive for the dimensioning of inductive components with nanocrystalline or amorphous metal cores.
  • the number of turns N must not be chosen too small, since otherwise the insertion loss will be too great due to the too low R p resistance of the transformer 7.
  • small numbers of turns result in high leakage inductances, which cause overshoot and a long rise time for the signal.
  • An increase in the number of turns also leads to a smaller signal modulation B ac and thus to a lower distortion factor.
  • the transformer 7 therefore preferably has average turns between 5 and 25 turns. 18
  • alloy systems are described below. It has been found that the alloy systems described below can be used to produce inductive components for the interface modules 5 with particularly linear hysteresis loops and small designs, all of which have properties that conform to the standards, while complying with the conditions mentioned above.
  • Co a 40 - 82 at% preferably 55 ⁇ a ⁇ 72 at%
  • Ni d 0 - 30 at% preferably d ⁇ 20 at%
  • M e 0-5 at% preferably e ⁇ 3 at%
  • Si x 0 - 18 at% preferably x> 1 at%
  • the value of the saturation magnetostriction with a heat treatment matched to the alloy composition certainly reaches particularly small values of
  • the occurrence of harmful magnetoelastic resonances of the ring-shaped magnetic core 9 is thereby avoided. At certain frequencies of the induction curve, these led to drops in the permeability and / or to increased magnetic reversal losses.
  • a second alloy system has the composition Fe x Cu y M z SivBw, where M is an element from the group Nb, W,
  • M z 1 - 6 at% preferably 2 - 4 at%
  • Si v 6.5 - 18 at% preferably 14 - 17 at%
  • Alloys of this system have proven to be very suitable for the transformer 7 because of their linear loop shape and their very good frequency behavior. Particularly good properties are achieved in the alloy compositions highlighted as “preferred”, since here, just as in the alloy system 1, a zero crossing of the saturation magnetostriction can be set. It was also found here that the combination of a high specific electrical resistance from 1.1 to
  • high values for the gyromagnetic cutoff frequency, which ultimately depends on B s / ⁇ , are achieved. The latter is an important prerequisite for high permeabilities in the MHz range.
  • the temperature characteristic of the magnetic cores 9 can be specifically adjusted via the heat treatment to adjust the permeability. This can give rise to application-specific advantages that cannot be realized otherwise, particularly in harsh environmental conditions, such as can occur in telecommunications equipment.
  • Nb z 2 - 5 at% preferably 3 - 4 at%
  • Cu w 0.5 - 1.5 at%, preferably 1 at%, where y + z> 5 at%, preferably 7 at%, and y + z + v> 11, preferably 12 - 16 at%.
  • interface modules 5 can again be realized with particularly small designs.
  • alloy systems 2 to 5 are given a fine crystalline structure with grain diameters below 100 nm. These grains are surrounded by an amorphous phase, which however takes up less than 50% of the material volume.
  • All alloy systems 1 to 5 are characterized by the following properties:
  • the size of the fine-crystalline grain can be achieved through a targeted coordination of the heat treatment, the metalloid content and the content of refractory metals.
  • the saturation reduction can be fine-tuned by choosing the content of Ni, Co, M, Si, B and C.
  • the thickness of which can be less than 17 ⁇ m
  • the amorphous, distant or nanocrystalline alloys in Table 2 are characterized by particularly high saturation modulation values of up to 1.7 Tesla. These allow comparatively high permeability values, which gives advantages in terms of size and wrapping compared to remote transmitters.

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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)
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Abstract

Module d'interface pour réseaux de données locaux qui comporte une rangée de composants (7,8) inductifs servant à relier un circuit (3, 4) d'interface avec une ligne (6) de données. Les composants inductifs, en particulier le dispositif de transmission (8), possèdent des noyaux magnétiques (9) constitués d'un alliage amorphe ou nanocristallin et se caractérisent par un volume de construction particulièrement faible.
PCT/EP2000/009882 1999-10-11 2000-10-09 Modules d'interface pour reseaux de donnees locaux WO2001027946A1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
EP00972702A EP1221169A1 (fr) 1999-10-11 2000-10-09 Modules d'interface pour reseaux de donnees locaux

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE1999148897 DE19948897A1 (de) 1999-10-11 1999-10-11 Schnittstellenmodule für lokale Datennetzwerke
DE19948897.5 1999-10-11

Publications (1)

Publication Number Publication Date
WO2001027946A1 true WO2001027946A1 (fr) 2001-04-19

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EP (1) EP1221169A1 (fr)
DE (1) DE19948897A1 (fr)
WO (1) WO2001027946A1 (fr)

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2388715A (en) * 2002-05-13 2003-11-19 Splashpower Ltd Separable inductive coupler with an amorphous or non-annealed core component
WO2005034341A1 (fr) * 2003-10-09 2005-04-14 Audio Products International Corp Amplificateur de puissance et procede pour transducteur ou haut-parleur a bobine mobile partagee
US6906495B2 (en) 2002-05-13 2005-06-14 Splashpower Limited Contact-less power transfer
WO2005114682A1 (fr) * 2004-05-17 2005-12-01 Vacuumschmelze Gmbh & Co. Kg Noyau de transformateur de courant et procede de production d'un noyau de transformateur de courant

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Cited By (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2388715A (en) * 2002-05-13 2003-11-19 Splashpower Ltd Separable inductive coupler with an amorphous or non-annealed core component
US6906495B2 (en) 2002-05-13 2005-06-14 Splashpower Limited Contact-less power transfer
GB2388715B (en) * 2002-05-13 2005-08-03 Splashpower Ltd Improvements relating to the transfer of electromagnetic power
US7863861B2 (en) 2002-05-13 2011-01-04 Access Business Group International Llc Contact-less power transfer
US7952324B2 (en) 2002-05-13 2011-05-31 Access Business Group International Llc Contact-less power transfer
WO2005034341A1 (fr) * 2003-10-09 2005-04-14 Audio Products International Corp Amplificateur de puissance et procede pour transducteur ou haut-parleur a bobine mobile partagee
WO2005114682A1 (fr) * 2004-05-17 2005-12-01 Vacuumschmelze Gmbh & Co. Kg Noyau de transformateur de courant et procede de production d'un noyau de transformateur de courant
US7358844B2 (en) 2004-05-17 2008-04-15 Vacuumschmelze Gmbh & Co. Kg Current transformer core and method for producing a current transformer core
US7861403B2 (en) 2004-05-17 2011-01-04 Vacuumschmelze Gmbh & Co. Kg Current transformer cores formed from magnetic iron-based alloy including final crystalline particles and method for producing same

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EP1221169A1 (fr) 2002-07-10

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