EP1918407A1 - Alliage légèrement magnétique à base de fer et de cobalt ainsi que son procédé de fabrication - Google Patents

Alliage légèrement magnétique à base de fer et de cobalt ainsi que son procédé de fabrication Download PDF

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EP1918407A1
EP1918407A1 EP07113372A EP07113372A EP1918407A1 EP 1918407 A1 EP1918407 A1 EP 1918407A1 EP 07113372 A EP07113372 A EP 07113372A EP 07113372 A EP07113372 A EP 07113372A EP 1918407 A1 EP1918407 A1 EP 1918407A1
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Prior art keywords
soft magnetic
alloy
marked
magnetic alloy
alloy according
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EP07113372A
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German (de)
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EP1918407B1 (fr
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Joachim Dr. Gerster
Witold Dr. Pieper
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Vacuumschmelze GmbH and Co KG
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Vacuumschmelze GmbH and Co KG
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    • 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
    • H01F1/14708—Fe-Ni based alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F02—COMBUSTION ENGINES; HOT-GAS OR COMBUSTION-PRODUCT ENGINE PLANTS
    • F02M—SUPPLYING COMBUSTION ENGINES IN GENERAL WITH COMBUSTIBLE MIXTURES OR CONSTITUENTS THEREOF
    • F02M51/00—Fuel-injection apparatus characterised by being operated electrically
    • F02M51/06—Injectors peculiar thereto with means directly operating the valve needle
    • F02M51/061—Injectors peculiar thereto with means directly operating the valve needle using electromagnetic operating means
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F02—COMBUSTION ENGINES; HOT-GAS OR COMBUSTION-PRODUCT ENGINE PLANTS
    • F02M—SUPPLYING COMBUSTION ENGINES IN GENERAL WITH COMBUSTIBLE MIXTURES OR CONSTITUENTS THEREOF
    • F02M61/00—Fuel-injectors not provided for in groups F02M39/00 - F02M57/00 or F02M67/00
    • F02M61/16—Details not provided for in, or of interest apart from, the apparatus of groups F02M61/02 - F02M61/14
    • F02M61/166—Selection of particular materials
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment
    • C21D8/1272—Final recrystallisation annealing
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F02—COMBUSTION ENGINES; HOT-GAS OR COMBUSTION-PRODUCT ENGINE PLANTS
    • F02M—SUPPLYING COMBUSTION ENGINES IN GENERAL WITH COMBUSTIBLE MIXTURES OR CONSTITUENTS THEREOF
    • F02M2200/00—Details of fuel-injection apparatus, not otherwise provided for
    • F02M2200/90—Selection of particular materials
    • F02M2200/9053—Metals
    • F02M2200/9061—Special treatments for modifying the properties of metals used for fuel injection apparatus, e.g. modifying mechanical or electromagnetic properties

Definitions

  • the invention relates to a soft magnetic iron-cobalt-based alloy having a cobalt content of 10% by weight (wt .-%) to 22 wt .-%, and a method for producing the alloy and a method for producing semi-finished from this alloy , in particular of magnetic components for actuator systems.
  • Soft magnetic alloys based on iron-cobalt have a high saturation magnetization and can therefore be used to form high-force and / or small-volume electromagnetic actuator systems.
  • a typical application of these alloys are solenoid valves, such as solenoid valves for fuel injection in internal combustion engines.
  • Soft magnetic alloys based on iron-cobalt with a cobalt content of 10 wt .-% to 22 wt .-% are for example from US 7,128,790 known.
  • the switching frequency can be limited due to the resulting eddy currents. Further, improvements in the strength of the magnetic cores in continuous operation in high frequency actuator systems are desired.
  • the object of the invention is therefore to provide an alloy which is better suited for use as a magnetic core in fast-switching actuators.
  • a soft magnetic alloy consists essentially of 10% by weight ⁇ Co ⁇ 22% by weight, 0% by weight ⁇ V ⁇ 4% by weight, 1.5% by weight ⁇ Cr ⁇ 5% by weight. %, 1 wt% ⁇ Mn ⁇ 2 wt%, 0 wt% ⁇ Mo ⁇ 1 wt%, 0.5 wt% ⁇ Si ⁇ 1.5 wt%, 0, 1 wt .-% ⁇ Al ⁇ 1.0 wt .-%, balance iron.
  • the alloy preferably has a maximum of 200 ppm of nitrogen, a maximum of 400 ppm of carbon and a maximum of 100 ppm of oxygen.
  • the alloy according to the invention has a higher specific resistance compared with the binary Co-Fe alloy, which leads to a suppression of the eddy currents, with the lowest possible lowering of the saturation polarization. This is achieved by the alloying of the non-magnetic elements. Further, the alloy has higher strength due to the content of Al and Si. This alloy is suitable for use as a magnetic core of a fast-switching actuator system, such as a fuel injection valve of an internal combustion engine.
  • Al, V and Si also increase the electrical resistance while raising the annealing temperature.
  • an alloy with high resistance, high saturation and high annealing temperature and thus good soft magnetic properties can be specified.
  • the alloy has higher strength due to the content of Al and Si.
  • the alloy is cold-workable and ductile in the final annealed condition.
  • the alloy can have an elongation A L of> 2%, preferably A L > 20%.
  • the elongation A L is measured during tensile tests.
  • This alloy is suitable for use as a magnetic core of a fast-switching actuator system, such as a fuel injection valve of an internal combustion engine.
  • the alloy should also have high electrical resistivity and good soft magnetic properties.
  • This alloy thus has a cobalt content of 10% by weight ⁇ Co ⁇ 22% by weight.
  • a low cobalt content reduces the raw material cost of the alloy, making it suitable for high cost pressure applications, such as in the automotive industry.
  • the maximum permeability is high within this range, which leads to cheaper lower drive currents when used as an actuator.
  • the alloy has a cobalt content of 14 wt% ⁇ Co ⁇ 22 wt% and 14 wt% ⁇ Co ⁇ 20 wt%.
  • the soft magnetic alloy of the magnetic core has a content of chromium and manganese, which leads to a higher electrical resistivity p in the annealed state with little decrease in saturation. This higher resistivity allows smaller switching times for an actuator as eddy currents are reduced. At the same time, the alloy has a high saturation and a high permeability ⁇ max , so that good soft magnetic properties are maintained.
  • the elements Si and Al of the alloy provide improved strength of the alloy without significantly degrading the soft magnetic properties.
  • the strength of the alloy can be significantly increased by solid solution hardening, without a significant deterioration of the soft magnetic properties.
  • the aluminum content and vanadium content according to the invention enables a higher annealing temperature, which leads to good soft magnetic properties of the coercive force H c and the maximum permeability ⁇ max leads.
  • High permeability is desired, as this leads to lower drive currents when using the alloy as a magnetic core or flux guide of an actuator.
  • the alloy has a silicon content of 0.5% by weight ⁇ Si ⁇ 1.0% by weight.
  • the content of Mo has been kept low to prevent the formation of carbides, which may lead to deterioration of the magnetic properties.
  • the content of aluminum and silicon is from 0.6% by weight ⁇ Al + Si ⁇ 1.5% by weight, so that brittleness and processing problems that may occur with higher total contents of aluminum and silicon are avoided ,
  • the content of the elements is chromium and manganese and molybdenum and aluminum and silicon and vanadium 4.0 wt% ⁇ (Cr + Mn + Mo + Al + Si + V) ⁇ 9.0 wt%.
  • This alloy has an even higher resistivity compared to the binary CoFe alloy, which leads to a suppression of the eddy currents, at the same time the saturation polarization is lowered as little as possible and the coercive field strength H c is even less increased.
  • the content of chromium and manganese and molybdenum and aluminum and silicon and vanadium in one embodiment is 6.0% by weight ⁇ Cr + Mn + Mo + Al + Si + V ⁇ 9.0% by weight.
  • the soft magnetic alloy consists essentially of 10 wt% ⁇ Co ⁇ 22 wt%, 0 wt% ⁇ V ⁇ 1 wt%, 1.5 wt% ⁇ Cr ⁇ 3 wt.%, 1 wt.% ⁇ Mn ⁇ 2 wt.%, 0 wt.% ⁇ Mo ⁇ 1 wt.%, 0.5 wt.% ⁇ Si ⁇ 1.5 wt. %, 0.1% by weight ⁇ Al ⁇ 1.0% by weight, balance iron.
  • It can have a content of aluminum and silicon of 0.6% by weight ⁇ Al + Si ⁇ 1.5% by weight and / or a content of chromium and manganese and molybdenum and aluminum and silicon of 4.5% by weight.
  • the alloy consists essentially of 0 wt% ⁇ V ⁇ 2.0 wt%, 1.6 wt% ⁇ Cr ⁇ 2.5 wt%, 1.25 wt% ⁇ Mn ⁇ 1.5 wt%, 0 wt% ⁇ Mo ⁇ 0.02 wt%, 0.6 wt% ⁇ Si ⁇ 0.9 wt% and 0.2 wt%. -% ⁇ Al ⁇ 0.7 wt .-%.
  • the alloy consists essentially of 0 wt% ⁇ V ⁇ 0.01 wt%, 2.3 wt% ⁇ Cr ⁇ 3.0 wt%, 1.25 wt% ⁇ Mn ⁇ 1.5 wt%, 0.75 wt% ⁇ Mo ⁇ 1 wt%, 0.6 wt% ⁇ Si ⁇ 0.9 wt% and 0.1 wt%.
  • -% ⁇ Al ⁇ 0.2 wt .-% is.
  • the alloy consists essentially of 0.75 wt% ⁇ V ⁇ 2.75 wt%, 2.3 wt% ⁇ Cr ⁇ 3.5 wt%, 1.25 wt%. % ⁇ Mn ⁇ 1.5 wt%, 0 wt% ⁇ Mo ⁇ 0.01 wt%, 0.6 wt% ⁇ Si ⁇ 0.9 wt% and 0.2 Wt .-% ⁇ Al ⁇ 1.0 wt .-% is.
  • These three alloys have a preferred combination of high electrical resistance, high saturation, and low coercivity.
  • Alloys with the abovementioned compositions have a specific electrical resistance ⁇ > 0.50 ⁇ m or ⁇ > 0.55 ⁇ m or ⁇ > 0.60 ⁇ m or ⁇ > 0.65 ⁇ m. This value provides for an alloy, so that when used as a magnetic core of an actuator system lower eddy currents. This allows the use of the alloy in actuator systems with higher switching times.
  • the proportion of the elements aluminum and silicon in the alloy according to the invention leads to an alloy with a yield strength of R p0.2 > 340 MPa. This higher strength of the alloy can extend the life of the alloy when used as a magnetic core of an actuator system. This is attractive in using the alloy in high frequency actuator systems, such as fuel injection valves in internal combustion engines.
  • the alloy according to the invention has good soft magnetic properties as well as good strength and high electrical resistivity.
  • the alloy has a saturation of J (400A / cm)> 2.00 T or> 1.90 T, and / or a coercive force H c ⁇ 3.5 A / cm or H c ⁇ 2.0 A / cm or and / or H c ⁇ 1.0 A / cm has a maximum permeability ⁇ max > 1000 or ⁇ max > 2000.
  • the inventive content of chromium and manganese and molybdenum and aluminum and silicon and vanadium is between 4.0 wt .-% and 9.0 wt .-%. This higher content allows to provide an alloy that has a higher electrical resistance of ⁇ > 0.6 ⁇ m and a low coercive force H c ⁇ 2.0 A / cm. This combination of properties is particularly suitable for use with fast switching actuators.
  • the invention further provides a soft magnetic core or flux guide for an electromagnetic actuator made of an alloy according to one of the preceding embodiments.
  • This soft magnetic core is in various embodiments a soft magnetic core for a solenoid valve of an internal combustion engine, a soft magnetic core for a fuel injection valve of an internal combustion engine, a soft magnetic core for a direct fuel injection valve of a gasoline engine or a diesel engine, or a soft magnetic component for electromagnetic valve timing such as intake and exhaust valves.
  • the different actuator systems such as solenoid valves and fuel injection valves have different requirements for strength and magnetic properties. These requirements can be met by selecting an alloy having a composition within the ranges described above.
  • the invention also provides a fuel injection valve of an internal combustion engine with a soft magnetic alloy component according to one of the preceding embodiments.
  • the fuel injector is a direct fuel injection valve of a gasoline engine and a direct fuel injection valve of a diesel engine.
  • the invention provides an electromagnetic actuator return member and a soft magnetic rotor and a soft magnetic stator for an electric motor and a soft magnetic component for electromagnetic valve timing on an intake valve or exhaust valve used in an engine compartment of, for example, a motor vehicle, of an alloy according to one of the preceding embodiments.
  • the invention also provides a process for the production of semi-finished products from a cobalt-iron alloy, in which first workpieces made of a soft magnetic alloy are produced by melting and hot working, which essentially consist of 10% by weight ⁇ Co ⁇ 22% by weight. %, 0 wt% ⁇ V ⁇ 4 wt%, 1.5 wt% ⁇ Cr ⁇ 5 wt%, 1 wt% ⁇ Mn ⁇ 2 wt%, 0 wt% % ⁇ Mo ⁇ 1 wt .-%, 0.5 wt .-% ⁇ Si ⁇ 1.5 wt .-%, 0.1 wt .-% ⁇ Al ⁇ 1.0 wt .-%, balance iron.
  • the alloy of the workpieces can also have a composition according to one of the preceding embodiments.
  • the alloy can be melted by various methods. In theory, all common techniques are possible, such as air melting or VIM (vacuum induction melting). For this, e.g. the arc furnace or inductive techniques are used. Treatment with VOD (Vacuum Oxygen Decarburization) or AOD (Argon Oxygen Decarburization) or ESU (Electric Slag Remelting) improves the quality of the product.
  • VIM vacuum induction melting
  • the VIM method is preferred, since thus the contents of the alloying elements more exactly can be set and non-metallic inclusions in the solidified alloy can be better avoided.
  • the melting process is followed by a different series of process steps, depending on the semifinished product to be produced.
  • the ingot resulting from the melting process is converted by pre-blocking into a slab.
  • Preblocking is understood to mean the forming of the ingot into a rectangular section slab by a hot rolling operation at a temperature of, for example, 1250 ° C. After blooming, the scale formed on the surface of the slab is removed by grinding. The grinding is followed by another hot rolling process by which the slab is formed into a strip at a temperature of, for example, 1250 ° C. Subsequently, the impurities formed on the surface of the belt during hot rolling are removed by grinding or pickling, and the strip is cold-worked to the final thickness, which may be in the range of 0.1 mm to 2 mm. Finally, the tape is subjected to a final annealing. During final annealing, the lattice defects resulting from the forming processes heal and crystalline grains are formed in the microstructure.
  • the manufacturing process is when turning parts are produced.
  • billets are made by pre-blocking the ingot with a square cross-section.
  • the so-called pre-blocking takes place at a temperature of for example 1250 ° C.
  • the scale formed during pre-blocking is removed by grinding.
  • Another hot rolling process through which the billets in bars or wires up to a diameter of, for example 13 mm to be formed.
  • distortions of the material are corrected and, on the other hand, the impurities forming on the surface during the hot rolling process are removed.
  • the material is subjected to a final annealing.
  • the final annealing can be carried out in a temperature range of 700 ° C to 1100 ° C. In one embodiment, the final annealing is carried out in the temperature range from 750 ° C to 850 ° C.
  • the final annealing can be carried out under inert gas, hydrogen or vacuum.
  • the conditions such as temperature and duration of the final annealing can be selected so that after the final annealing the alloy has tensile strain parameters of elongation at break A L > 2% or A L > 20%.
  • the alloy is cold worked prior to final annealing.
  • a coil 22 is supplied with power from a current source 23, so that upon energization of the coil 22, a magnetic field is induced.
  • the coil 22 is disposed around the magnetic core 21 so that, due to the induced magnetic field, the magnetic core 21 moves from a first position 24 shown by the dotted line in FIG. 1 to a second position 25.
  • the first position 24 is a closed position and the second position is an open position. Consequently, the current 26 is controlled by the channel 27 from the actuator system 20.
  • the actuator system 20 is a fuel injection valve of a gasoline engine or a diesel engine, or a direct fuel injection valve of a gasoline engine or a diesel engine.
  • the soft magnetic alloy of the magnetic core 21 has a content of chromium and manganese, which leads to a specific electrical resistance p in the annealed state of 0.572 ⁇ m. This higher resistivity allows for smaller shutter times on the actuator as eddy currents are reduced. At the same time, the alloy has a high saturation J (400 A / cm), measured at a magnetic field strength of 400 A / cm, of 2.137 T and a permeability ⁇ max of 1915, so that good soft magnetic properties are maintained.
  • the elements Si and Al of the alloy provide improved strength of the magnetic core 21 without significantly deteriorating the soft magnetic properties.
  • the yield strength R p0.2 of this alloy is 402 Mpa.
  • the aluminum content enables a higher annealing temperature, which leads to good soft magnetic properties of a coercive force H c of only 2.57 A / cm and a maximum permeability ⁇ max of 1915. A high permeability is desired because this leads to lower drive currents when using the alloy as the magnetic core of an actuator.
  • the content of Mo has been kept low to prevent the formation of carbides, which may lead to deterioration of the magnetic properties.
  • Table 1 shows compositions of various alloys according to the invention.
  • the alloy is first melted in a melting process 1.
  • the alloy can be melted by various methods. In theory, all common techniques are possible, such as air melting or VIM (vacuum induction melting). For example, the arc furnace or inductive Techniques are used. Treatment with VOD (Vacuum Oxygen Decarburization) or AOD (Argon Oxygen Decarburization) or ESU (Electric Slag Remelting) improves the quality of the product.
  • VIM vacuum induction melting
  • AOD Aractive Oxygen Decarburization
  • ESU Electro Slag Remelting
  • the VIM method is preferred because it allows the content of the alloying elements to be adjusted more accurately and non-metallic inclusions in the solidified alloy can be better avoided.
  • the melting process 1, depending on the semifinished product to be produced, is followed by a different series of process steps.
  • the ingot resulting from the melting process 1 is converted by pre-blocking 2 into a slab.
  • Pre-blocking is understood to mean the forming of the ingot into a slab of rectangular cross-section by a hot rolling operation at a temperature of 1250 ° C.
  • the scale formed on the surface of the slab is removed by grinding 3.
  • the grinding 3 is followed by another hot rolling process 4, by which the slab is formed at a temperature of 1250 ° C in a band having a thickness of, for example, 3.5 mm.
  • the impurities formed on the surface of the strip during hot rolling are removed by grinding or pickling 5, and the strip is cold-rolled 6 to the final thickness in the range of 0.1 to 2 mm.
  • the strip is subjected to a final annealing 7 at a temperature of> 700 ° C. During final annealing, the lattice defects resulting from the forming processes heal and crystalline grains are formed in the microstructure.
  • the manufacturing process is when turning parts are produced.
  • billets are made by pre-blocking 8 of the ingot with a square cross-section.
  • the so-called pre-blocking takes place at a temperature of 1250 ° C.
  • the scale formed during pre-blocking 8 is removed by grinding 9.
  • another hot rolling operation 10 by which the billets are converted into rods or wires up to a diameter of 13 mm.
  • straightening and peeling 11 on the one hand, distortions of the material are corrected and, on the other hand, the impurities forming during the hot rolling process 10 are removed on the surface.
  • the material is also subjected to a final annealing 12 here.
  • the coercive force H c was measured as a function of the annealing temperature for the alloys of Table 1. The results are shown in FIG. From Figure 3 it can be seen that with increasing temperature, the coercive field strength initially decreases and increases at even higher temperatures, which are at the boundary to the two-phase region.
  • the annealing temperature is selected according to the composition, so that the coercive force remains low.
  • the annealing was carried out at a temperature of 760 ° C.
  • Figure 4 shows the coercive force for the alloys 1 to 4, 8, 10, 11 and 13.
  • the alloys 8, 10, 11 and 13 were also cold worked after hot rolling.
  • the alloys 1 to 4 were only hot rolled.
  • FIG. 4 shows the influence of different alloying elements on H c at different annealing temperatures.
  • the increase of H c shows the upper limit of the ferritic phase.
  • Alloys 2, 10, 11 and 13 having a lower H c at higher annealing temperatures have an aluminum content of at least 0.68 wt%.
  • Alloys 10 and 11 have a particularly low coercive force H c of less than 1.5 A / cm at annealing temperatures above 850 ° C.
  • These alloys have an aluminum content of 0.84% by weight and 0.92% by weight and a vanadium content of 2.51% by weight and 1.00% by weight, respectively.
  • the phase transition temperature is further shifted upwards. This has the advantage that the magnetic properties can be further improved by using a higher annealing temperature.
  • the specific electrical resistance p of each alloy is above 0.5 ⁇ m. This leads to a suppression of the eddy currents, so that the alloys are suitable for actuator applications with short switching times.
  • the yield strength was measured for the alloys 1 to 7 in the magnetically final annealed condition and is above 340 MPa for each alloy. These alloys can thus be used in applications where higher mechanical loads arise.
  • An alloy according to a first embodiment consists essentially of 18.1 wt .-% Co, 2.24 wt .-% Cr, 1.40 wt .-% Mn, 0.01 wt .-% Mo, 0.83 wt % Si, 0.24 wt% Al, balance Fe and was prepared as described above.
  • the alloy was annealed at 760 ° C and, when annealed, has a resistivity ⁇ el of 0.542 ⁇ m, a coercive force H c of 2.34 A / cm, a saturation J at a magnetic field strength of 160 A / cm, J (160 A / cm) of 2.029 T, a saturation J at a magnetic field strength of 400 A / cm, J (400 A / cm), 2.146 T, a maximum permeability ⁇ max of 2314, a yield strength R m of 623 MPa, R p0 , 2 of 411 MPa, an elongation at break AL of 29.6% and an E modulus of 220 GPa.
  • An alloy according to a second embodiment consists essentially of 18.2 wt .-% Co, 1.67 wt .-% Cr, 1.39 wt .-% Mn, 0.01 wt .-% Mo, 0.82 wt % Si, 0.68 wt% Al, balance Fe and was prepared as described above.
  • the alloy was annealed at 800 ° C and, when annealed, has a resistivity ⁇ el of 0.533 ⁇ m, a coercive force H c of 1.94 A / cm, a saturation J at a magnetic field strength of 160 A / cm, J (160 A / cm), 2.019 T, a saturation J at a magnetic field strength of 400 A / cm, J (400 A / cm), 2.151 T, a maximum permeability ⁇ max of 1815 , a yield strength R m of 661MPa, R p0.2 of 385 MPa, an elongation at break AL of 25.4% and an E modulus of 221 GPa.
  • An alloy according to a third embodiment consists essentially of 18.3 wt .-% Co, 2.62 wt .-% Cr, 1.37 wt .-% Mn, 0.01 wt .-% Mo, 0.85 wt % Si, 0.21 wt% Al, balance Fe and was prepared as described above.
  • the alloy was annealed at 760 ° C and, when annealed, has a resistivity ⁇ el of 0.572 ⁇ m, a coercive force H c of 2.57 A / cm, a saturation J at a magnetic field strength of 160 A / cm, J (160 A / cm), of 2.021 T, a saturation J at a magnetic field strength of 400 A / cm, J (400 A / cm), of 2.137 T, a maximum permeability ⁇ max of 1915, a yield strength R m of 632 MPa, R p0 , 2 of 402 MPa, an elongation at break AL of 28.0% and an E modulus of 217 GPa.
  • An alloy according to a fourth embodiment consists essentially of 18.3 wt .-% Co, 2.42 wt .-% Cr, 1.45 wt .-% Mn, 0.01 wt .-% Mo, 0.67 wt % Si, 0.23 wt% Al, balance Fe and was prepared as described above.
  • the alloy was annealed at 730 ° C and, when annealed, has a resistivity ⁇ el of 0.546 ⁇ m, a coercive force H c of 2.73 A / cm, a saturation J at a magnetic field strength of 160 A / cm, J (160 A / cm), of 2.037 T, a saturation J at a magnetic field strength of 400 A / cm, J (400 A / cm), 2.156T, a maximum permeability ⁇ max of 2046, a yield strength R m of 615 MPa, R p0.2 of 395 MPa, an elongation at break AL of 29.5% and an E modulus of 223 GPa on.
  • An alloy according to a fifth embodiment consists essentially of 15.40 wt% Co, 2.34 wt% Cr, 1.27 wt% Mn, 0.85 wt% Si, 0.23 wt % Al, balance Fe and was prepared as described above.
  • the alloy was annealed at 760 ° C and, when annealed, has a resistivity ⁇ el of 0.5450 ⁇ m, a coercive force H c of 1.30 A / cm, a saturation J at a magnetic field strength of 160 A / cm, J (160 A / cm), of 1.986 T, a saturation J at a magnetic field strength of 400 A / cm, J (400 A / cm), of 2.105T and a maximum permeability ⁇ max of 3241.
  • An alloy according to a sixth embodiment consists essentially of 18.10 wt% Co, 2.30 wt% Cr, 1.37 wt% Mn, 0.83 wt% Si, 0.24 wt % Al, balance Fe and was prepared as described above.
  • the alloy was annealed at 760 ° C and, when annealed, has a resistivity ⁇ el of 0.5591 ⁇ m, a coercive force H c of 1.39 A / cm, a saturation J at a magnetic field strength of 160 A / cm, J (160 A / cm), of 2.027 T, a saturation J at a magnetic field strength of 400 A / cm, J (400 A / cm), of 2.138 T and a maximum permeability ⁇ max of 2869.
  • An alloy according to a seventh embodiment consists essentially of 21.15 wt .-% Co, 2.31 wt .-% Cr, 1.38 wt .-% Mn, 0.84 wt .-% Si, 0.23 wt % Al, balance Fe and was prepared as described above.
  • the alloy was annealed at 760 ° C and, when annealed, has a resistivity ⁇ el of 0.5627 ⁇ m, a coercive force H c of 1.93 A / cm, a saturation J at a magnetic field strength of 160 A / cm, J (160 A / cm), of 2.066 T, a saturation J at a magnetic field strength of 400 A / cm, J (400 A / cm), of 2.165 T and a maximum permeability ⁇ max of 1527.
  • the sum of the additions is slightly higher and is between 6 wt .-% and 9 wt .-%.
  • These alloys each have a specific electrical resistance ⁇ el ⁇ 0.60 ⁇ m in the annealed state.
  • An alloy according to an eighth embodiment consists essentially of 18.0 wt% Co, 2.66 wt% Cr, 1.39 wt% Mn, ⁇ 0.01 wt% Mo, 0.87 Wt% Si, 0.17 wt% Al, 1.00 wt% V, balance Fe and was prepared as described above. This alloy was cold worked even after hot rolling.
  • the alloy was annealed at 780 ° C and, when annealed, has a resistivity ⁇ el of 0.627 ⁇ m, a coercive force H c of 1.40 A / cm, a saturation J at a magnetic field strength of 160 A / cm, J (160 A / cm), of 1.977 T, a saturation J at a magnetic field strength of 400 A / cm, J (400 A / cm), 2.088 T, a maximum permeability ⁇ max of 2862, a yield strength R m of 605 MPa, R p0.2 of 374 MPa, an elongation at break AL of 29.7% and an E modulus of 222 GPa.
  • An alloy according to a ninth embodiment consists essentially of 18.0 wt% Co, 2.60 wt% Cr, 1.35 wt% Mn, 0.99 wt% Mo, 0.84 wt % Si, 0.17 wt% Al, ⁇ 0.01 wt% V, balance Fe and was prepared as described above. In addition, this alloy was cold worked.
  • the alloy was annealed at 780 ° C and, when annealed, has a resistivity ⁇ el of 0.604 ⁇ m, a coercive force H c of 2.13 A / cm, a saturation J at a magnetic field strength of 160 A / cm, J (160 A / cm), of 21.969 T, a saturation J at a magnetic field strength of 400 A / cm, J (400 A / cm), 2.092 T, a maximum permeability ⁇ max of 1656, a yield strength R m of 636 MPa, R p0 , 2 of 389 MPa, an elongation at break AL of 29.2% and an E-modulus of 222 GPa.
  • An alloy according to a tenth embodiment consists essentially of 18.0 wt% Co, 1.85 wt% Cr, 1.33 wt% Mn, ⁇ 0.01 wt% Mo, 0.86 Wt% Si, 0.84 wt% Al, 2.51 wt% V, balance Fe and was prepared as described above. Thereafter, the alloy was cold worked.
  • the alloy was annealed at 870 ° C and, when annealed, has a resistivity ⁇ el of 0.716 ⁇ m, a coercive field strength H c of 0.95 A / cm, a saturation J at a magnetic field strength of 160 A / cm, J (160 A / cm), of 1.920 T, a saturation J at a magnetic field strength of 400 A / cm, J (400 A) / cm), from 2.015 T, a maximum permeability ⁇ max of 4038.
  • This alloy of the tenth embodiment has a particularly advantageous combination of a high resistivity ⁇ el of 0.716 ⁇ m, a low coercive force H c of 0.95 A / cm, and a high saturation J at a magnetic field strength of 160 A / cm, J (160 A / cm), from 1.920 T up.
  • An alloy according to an eleventh embodiment consists essentially of 12.0 wt% Co, 2.65 wt% Cr, 1.38 wt% Mn, ⁇ 0.01 wt% Mo, 0.85 Wt% Si, 0.92 wt% Al, 1.00 wt% V, balance Fe and was prepared as described above and additionally clearly deformed.
  • the alloy was annealed at 820 ° C and, when annealed, has a resistivity ⁇ el of 0.658 ⁇ m, a coercive force H c of 0.72 A / cm, a saturation J at a magnetic field strength of 160 A / cm, J (160 A / cm), of 1.880 T, a saturation J at a magnetic field strength of 400 A / cm, J (400 A / cm), 2.008 T, a maximum permeability ⁇ max of 5590, a yield strength R m of 525 MPa, R p0 , 2 of 346 MPa, an elongation at break AL of 33.5% and an E modulus of 216 GPa.
  • the alloy according to the eleventh embodiment has a particularly advantageous combination of high resistivity ⁇ el of 0.658 ⁇ m, low coercive force H c of 0.72 A / cm, and high saturation J at a magnetic field strength of 160 A / cm, J (160 A / cm), 1.880 T on.
  • the twelfth alloy is not according to the invention since the Co content is greater than 22% by weight.
  • An alloy according to a thirteenth embodiment consists essentially of 18.0 wt% Co, 3.00 wt% Cr, 1.32 wt% Mn, ⁇ 0.01 wt% Mo, 0.86 Wt% Si, 0.84 wt% Al, 2.01 wt% V, remainder Fe and was prepared as described above and cold worked after hot rolling.
  • the alloy was annealed at 820 ° C and, when annealed, has a resistivity ⁇ el of 0.769 ⁇ m, a coercive force H c of 1.14 A / cm, a saturation J at a magnetic field strength of 160 A / cm, J (160 A / cm), of 1.896 T, a saturation J at a magnetic field strength of 400 A / cm, J (400 A / cm), of 1, 985 T, a maximum permeability ⁇ max of 3499, a yield strength R m of 674 MPa, R p0.2 of 396 MPa, an elongation at break AL of 33.3% and an E-modulus of 218 GPa.

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Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2451219A (en) * 2007-07-27 2009-01-28 Vacuumschmelze Gmbh & Co Kg Soft magnetic iron-cobalt based alloy
EP2083428A1 (fr) * 2008-01-22 2009-07-29 Imphy Alloys Alliage Fe-Co pour actionneur électromagnétique à grande dynamique
DE102008053310A1 (de) * 2008-10-27 2010-04-29 Vacuumschmelze Gmbh & Co. Kg Werkstück aus weichmagnetischem Werkstoff mit verschleißfester Beschichtung und Verfahren zur Herstellung des Werkstücks
WO2019081670A1 (fr) * 2017-10-27 2019-05-02 Vacuumschmelze Gmbh & Co Kg Alliage magnétique doux à perméabilité élevée et procédé pour produire l'alliage magnétique doux à perméabilité élevée
CN111926268A (zh) * 2019-04-26 2020-11-13 真空融化股份有限公司 板材叠层和制造高磁导率软磁合金的方法

Families Citing this family (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE10134056B8 (de) * 2001-07-13 2014-05-28 Vacuumschmelze Gmbh & Co. Kg Verfahren zur Herstellung von nanokristallinen Magnetkernen sowie Vorrichtung zur Durchführung des Verfahrens
DE102005034486A1 (de) * 2005-07-20 2007-02-01 Vacuumschmelze Gmbh & Co. Kg Verfahren zur Herstellung eines weichmagnetischen Kerns für Generatoren sowie Generator mit einem derartigen Kern
US20070176025A1 (en) * 2006-01-31 2007-08-02 Joachim Gerster Corrosion resistant magnetic component for a fuel injection valve
US8029627B2 (en) * 2006-01-31 2011-10-04 Vacuumschmelze Gmbh & Co. Kg Corrosion resistant magnetic component for a fuel injection valve
ATE418625T1 (de) * 2006-10-30 2009-01-15 Vacuumschmelze Gmbh & Co Kg Weichmagnetische legierung auf eisen-kobalt-basis sowie verfahren zu deren herstellung
US8012270B2 (en) * 2007-07-27 2011-09-06 Vacuumschmelze Gmbh & Co. Kg Soft magnetic iron/cobalt/chromium-based alloy and process for manufacturing it
US9057115B2 (en) * 2007-07-27 2015-06-16 Vacuumschmelze Gmbh & Co. Kg Soft magnetic iron-cobalt-based alloy and process for manufacturing it
US20160329139A1 (en) 2015-05-04 2016-11-10 Carpenter Technology Corporation Ultra-low cobalt iron-cobalt magnetic alloys
US12522898B2 (en) 2020-03-10 2026-01-13 Proterial, Ltd. Method for manufacturing Fe—Co-based alloy bar, and Fe—Co-based alloy bar
US12522900B2 (en) 2021-09-14 2026-01-13 Proterial, Ltd. Fe-Co-based alloy bar
EP4403653A4 (fr) 2021-09-14 2024-11-06 Proterial, Ltd. Matériau de barre en alliage fe-co

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS61253348A (ja) * 1985-05-04 1986-11-11 Daido Steel Co Ltd 軟質磁性材料
JPS6293342A (ja) * 1985-10-17 1987-04-28 Daido Steel Co Ltd 軟質磁性材料
EP0715320A1 (fr) * 1994-11-29 1996-06-05 Vacuumschmelze Gmbh Alliage magnétiquement doux à base de fer contenant du cobalt pour circuits de commutation et d'excitation
DE4444482A1 (de) * 1994-12-14 1996-06-27 Bosch Gmbh Robert Weichmagnetischer Werkstoff
WO2001000895A1 (fr) * 1999-06-23 2001-01-04 Vacuumschmelze Gmbh Alliage fer-cobalt a faibles intensites de champ coercitifs et procede de realisation de demi-produits a partir d'un alliage fer-cobalt
US20040099347A1 (en) * 2000-05-12 2004-05-27 Imphy Ugine Precision Iron-cobalt alloy, in particular for electromagnetic actuator mobile core and method for making same

Family Cites Families (110)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE694374C (de) 1939-02-04 1940-07-31 Brown Boveri & Cie Akt Ges Verfahren zum fortlaufenden Betrieb eines mit einer Glueh- und Waermeaustauschzone versehenen Einkanaldrehherdofens
US2225730A (en) 1939-08-15 1940-12-24 Percy A E Armstrong Corrosion resistant steel article comprising silicon and columbium
US2926008A (en) 1956-04-12 1960-02-23 Foundry Equipment Company Vertical oven
GB833446A (en) 1956-05-23 1960-04-27 Kanthal Ab Improved iron, chromium, aluminium alloys
US2960744A (en) 1957-10-08 1960-11-22 Gen Electric Equilibrium atmosphere tunnel kilns for ferrite manufacture
US3255512A (en) 1962-08-17 1966-06-14 Trident Engineering Associates Molding a ferromagnetic casing upon an electrical component
US3502462A (en) 1965-11-29 1970-03-24 United States Steel Corp Nickel,cobalt,chromium steel
US3337373A (en) 1966-08-19 1967-08-22 Westinghouse Electric Corp Doubly oriented cube-on-face magnetic sheet containing chromium
US3401035A (en) 1967-12-07 1968-09-10 Crucible Steel Co America Free-machining stainless steels
US3634072A (en) 1970-05-21 1972-01-11 Carpenter Technology Corp Magnetic alloy
DE2045015A1 (de) 1970-09-11 1972-03-16 Siemens Ag Energieversorgungsanlage, insbes. für Flugzeuge, mit einem durch eine Kraftmaschine mit veränderlicher Drehzahl angetriebnen Asynchrongenerator
US3624568A (en) 1970-10-26 1971-11-30 Bell Telephone Labor Inc Magnetically actuated switching devices
US3977919A (en) 1973-09-28 1976-08-31 Westinghouse Electric Corporation Method of producing doubly oriented cobalt iron alloys
US4059462A (en) * 1974-12-26 1977-11-22 The Foundation: The Research Institute Of Electric And Magnetic Alloys Niobium-iron rectangular hysteresis magnetic alloy
JPS5180998A (fr) 1975-01-14 1976-07-15 Fuji Photo Film Co Ltd
JPS5192097A (fr) 1975-02-10 1976-08-12
US4076525A (en) 1976-07-29 1978-02-28 General Dynamics Corporation High strength fracture resistant weldable steels
US4120704A (en) 1977-04-21 1978-10-17 The Arnold Engineering Company Magnetic alloy and processing therefor
JPS546808A (en) 1977-06-20 1979-01-19 Toshiba Corp Magnetic alloy of iron-chromium-cobalt base
US4160066A (en) 1977-10-11 1979-07-03 Teledyne Industries, Inc. Age-hardenable weld deposit
DE2816173C2 (de) 1978-04-14 1982-07-29 Vacuumschmelze Gmbh, 6450 Hanau Verfahren zum Herstellen von Bandkernen
US4201837A (en) 1978-11-16 1980-05-06 General Electric Company Bonded amorphous metal electromagnetic components
DE2924280A1 (de) 1979-06-15 1981-01-08 Vacuumschmelze Gmbh Amorphe weichmagnetische legierung
JPS57164935A (en) 1981-04-04 1982-10-09 Nippon Steel Corp Unidirectionally inclined heating method for metallic strip or metallic plate
JPS599157A (ja) 1982-07-08 1984-01-18 Sony Corp 非晶質磁性合金の熱処理方法
SU1062298A1 (ru) 1982-07-28 1983-12-23 Центральный Ордена Трудового Красного Знамени Научно-Исследовательский Институт Черной Металлургии Им.И.П.Бардина Магнитом гкий сплав
JPS5958813A (ja) 1982-09-29 1984-04-04 Toshiba Corp 非晶質金属コアの製造方法
US4601765A (en) 1983-05-05 1986-07-22 General Electric Company Powdered iron core magnetic devices
DE3427716C1 (de) 1984-07-27 1985-11-14 Daimler-Benz Ag, 7000 Stuttgart Drehherdofen in Ringbauart zur Waermebehandlung von Werkstuecken
EP0216457A1 (fr) 1985-09-18 1987-04-01 Kawasaki Steel Corporation Procédé pour la fabrication des aimants permanents de la série séparation en deux phases du type Fe-Cr-Co
CH668331A5 (en) 1985-11-11 1988-12-15 Studer Willi Ag Magnetic head core mfr. from stack of laminations - involves linear machining of patterns from adhesively bonded and rolled sandwich of permeable and non-permeable layers
DE3542257A1 (de) 1985-11-29 1987-06-04 Standard Elektrik Lorenz Ag Vorrichtung zum tempern in einem magnetfeld
US4706525A (en) * 1986-01-07 1987-11-17 Cornell Research Foundation, Inc. Vehicle door unlocking device
US4881989A (en) 1986-12-15 1989-11-21 Hitachi Metals, Ltd. Fe-base soft magnetic alloy and method of producing same
EP0299498B1 (fr) 1987-07-14 1993-09-29 Hitachi Metals, Ltd. Noyau magnétique et procédé pour sa fabrication
EP0301561B1 (fr) 1987-07-31 1992-12-09 TDK Corporation Poudre magnétique de fer doux pour former un écran magnétique, composition et procédé pour faire celle-ci
KR910009974B1 (ko) 1988-01-14 1991-12-07 알프스 덴기 가부시기가이샤 고포화 자속밀도 합금
JP2698369B2 (ja) 1988-03-23 1998-01-19 日立金属株式会社 低周波トランス用合金並びにこれを用いた低周波トランス
JP2710949B2 (ja) 1988-03-30 1998-02-10 日立金属株式会社 超微結晶軟磁性合金の製造方法
JPH0215143A (ja) 1988-06-30 1990-01-18 Aichi Steel Works Ltd 冷間鍛造用軟磁性ステンレス鋼
DE3824075A1 (de) 1988-07-15 1990-01-18 Vacuumschmelze Gmbh Verbundkoerper zur erzeugung von spannungsimpulsen
US4994122A (en) 1989-07-13 1991-02-19 Carpenter Technology Corporation Corrosion resistant, magnetic alloy article
US5091024A (en) 1989-07-13 1992-02-25 Carpenter Technology Corporation Corrosion resistant, magnetic alloy article
EP0429022B1 (fr) 1989-11-17 1994-10-26 Hitachi Metals, Ltd. Alliage magnétique contenant des grains de cristaux ultrafins et procédé de fabrication
JPH03223444A (ja) 1990-01-26 1991-10-02 Alps Electric Co Ltd 高飽和磁束密度合金
US5268044A (en) 1990-02-06 1993-12-07 Carpenter Technology Corporation High strength, high fracture toughness alloy
JPH0559498A (ja) 1990-12-28 1993-03-09 Toyota Motor Corp フエライト系耐熱鋳鋼およびその製造方法
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
US5622768A (en) * 1992-01-13 1997-04-22 Kabushiki Kaishi Toshiba Magnetic core
JPH0633199A (ja) 1992-07-16 1994-02-08 Hitachi Metal Precision Ltd プリンタヘッド用ヨークコア
US5534081A (en) 1993-05-11 1996-07-09 Honda Giken Kogyo Kabushiki Kaisha Fuel injector component
JP3688732B2 (ja) 1993-06-29 2005-08-31 株式会社東芝 平面型磁気素子および非晶質磁性薄膜
JP3233313B2 (ja) 1993-07-21 2001-11-26 日立金属株式会社 パルス減衰特性に優れたナノ結晶合金の製造方法
DE69408916T2 (de) 1993-07-30 1998-11-12 Hitachi Metals Ltd Magnetkern für Impulsübertrager und Impulsübertrager
AUPM644394A0 (en) 1994-06-24 1994-07-21 Electro Research International Pty Ltd Bulk metallic glass motor and transformer parts and method of manufacture
US5611871A (en) 1994-07-20 1997-03-18 Hitachi Metals, Ltd. Method of producing nanocrystalline alloy having high permeability
US5594397A (en) 1994-09-02 1997-01-14 Tdk Corporation Electronic filtering part using a material with microwave absorbing properties
US5817191A (en) 1994-11-29 1998-10-06 Vacuumschmelze Gmbh Iron-based soft magnetic alloy containing cobalt for use as a solenoid core
DE19514612A1 (de) * 1995-04-25 1996-10-31 Fritz Dr Kueke Verfahren zur Herstellung einer wässrigen Chlordioxid-Lösung
EP0741191B1 (fr) 1995-05-02 2003-01-22 Sumitomo Metal Industries, Ltd. Tôle d'acier magnétique ayant des propriétés magnétiques améliorées et ayant une aptitude améliorée à l'estampage
US5501747A (en) 1995-05-12 1996-03-26 Crs Holdings, Inc. High strength iron-cobalt-vanadium alloy article
DE29514508U1 (de) 1995-09-09 1995-11-02 Vacuumschmelze Gmbh, 63450 Hanau Blechpaket für Magnetkerne zum Einsatz in induktiven Bauelementen mit einer Längsöffnung
DE19635257C1 (de) 1996-08-30 1998-03-12 Franz Hillingrathner Rundtaktofen zum Behandeln von Werkstücken
EP0927479B1 (fr) 1996-09-17 2002-04-10 Vacuumschmelze GmbH Transformateur d'impulsions pour interfaces en u selon le principe de la compensation d'echo
FR2755292B1 (fr) 1996-10-25 1998-11-20 Mecagis Procede de fabrication d'un noyau magnetique en materiau magnetique doux nanocristallin
FR2756966B1 (fr) 1996-12-11 1998-12-31 Mecagis Procede de fabrication d'un composant magnetique en alliage magnetique doux a base de fer ayant une structure nanocristalline
DE19653428C1 (de) 1996-12-20 1998-03-26 Vacuumschmelze Gmbh Verfahren zum Herstellen von Bandkernbändern sowie induktives Bauelement mit Bandkern
DE19802349B4 (de) 1997-01-23 2010-04-15 Alps Electric Co., Ltd. Weichmagnetische amorphe Legierung, amorphe Legierung hoher Härte und ihre Verwendung
US5769974A (en) 1997-02-03 1998-06-23 Crs Holdings, Inc. Process for improving magnetic performance in a free-machining ferritic stainless steel
US5741374A (en) 1997-05-14 1998-04-21 Crs Holdings, Inc. High strength, ductile, Co-Fe-C soft magnetic alloy
US5914088A (en) 1997-08-21 1999-06-22 Vijai Electricals Limited Apparatus for continuously annealing amorphous alloy cores with closed magnetic path
DE19741364C2 (de) 1997-09-19 2000-05-25 Vacuumschmelze Gmbh Verfahren und Vorrichtung zur Herstellung von aus Blechlamellen bestehenden Paketen für Magnetkerne
JPH11102827A (ja) 1997-09-26 1999-04-13 Hitachi Metals Ltd 可飽和リアクトル用コア、およびこれを用いた磁気増幅器方式多出力スイッチングレギュレータ、並びにこれを用いたコンピュータ
IL128067A (en) 1998-02-05 2001-10-31 Imphy Ugine Precision Iron-cobalt alloy
DE19818198A1 (de) 1998-04-23 1999-10-28 Bosch Gmbh Robert Verfahren zum Herstellen eines Läufers oder Ständers einer elektrischen Maschine aus Blechzuschnitten
JP4755340B2 (ja) 1998-09-17 2011-08-24 ヴァキュームシュメルツェ ゲーエムベーハー ウント コンパニー カーゲー 直流電流公差を有する変流器
US6462456B1 (en) 1998-11-06 2002-10-08 Honeywell International Inc. Bulk amorphous metal magnetic components for electric motors
JP2002530854A (ja) 1998-11-13 2002-09-17 バクームシユメルツエ、ゲゼルシヤフト、ミツト、ベシユレンクテル、ハフツング 変流器での使用に適した磁心、磁心の製造方法及び変流器
JP2000182845A (ja) 1998-12-21 2000-06-30 Hitachi Ferrite Electronics Ltd 複合磁心
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
US6181509B1 (en) 1999-04-23 2001-01-30 International Business Machines Corporation Low sulfur outgassing free machining stainless steel disk drive components
JP2001068324A (ja) 1999-08-30 2001-03-16 Hitachi Ferrite Electronics Ltd 粉末成形磁芯
JP3617426B2 (ja) 1999-09-16 2005-02-02 株式会社村田製作所 インダクタ及びその製造方法
DE10024824A1 (de) 2000-05-19 2001-11-29 Vacuumschmelze Gmbh Induktives Bauelement und Verfahren zu seiner Herstellung
DE10031923A1 (de) 2000-06-30 2002-01-17 Bosch Gmbh Robert Weichmagnetischer Werkstoff mit heterogenem Gefügebau und Verfahren zu dessen Herstellung
DE10045705A1 (de) 2000-09-15 2002-04-04 Vacuumschmelze Gmbh & Co Kg Magnetkern für einen Transduktorregler und Verwendung von Transduktorreglern sowie Verfahren zur Herstellung von Magnetkernen für Transduktorregler
CZ20031263A3 (cs) 2000-10-10 2003-09-17 Crs Holdings, Inc. Magneticky měkké slitiny Co-Mn-Fe
US6737784B2 (en) 2000-10-16 2004-05-18 Scott M. Lindquist Laminated amorphous metal component for an electric machine
US6685882B2 (en) 2001-01-11 2004-02-03 Chrysalis Technologies Incorporated Iron-cobalt-vanadium alloy
JP3593986B2 (ja) 2001-02-19 2004-11-24 株式会社村田製作所 コイル部品及びその製造方法
JP4284004B2 (ja) 2001-03-21 2009-06-24 株式会社神戸製鋼所 高強度圧粉磁心用粉末、高強度圧粉磁心の製造方法
JP2002294408A (ja) 2001-03-30 2002-10-09 Nippon Steel Corp 鉄系制振合金およびその製造方法
DE10119982A1 (de) 2001-04-24 2002-10-31 Bosch Gmbh Robert Kraftstoffeinspritzeinrichtung für eine Brennkraftmaschine
DE10128004A1 (de) 2001-06-08 2002-12-19 Vacuumschmelze Gmbh Induktives Bauelement und Verfahren zu seiner Herstellung
US6616125B2 (en) 2001-06-14 2003-09-09 Crs Holdings, Inc. Corrosion resistant magnetic alloy an article made therefrom and a method of using same
DE10134056B8 (de) 2001-07-13 2014-05-28 Vacuumschmelze Gmbh & Co. Kg Verfahren zur Herstellung von nanokristallinen Magnetkernen sowie Vorrichtung zur Durchführung des Verfahrens
JP3748055B2 (ja) 2001-08-07 2006-02-22 信越化学工業株式会社 ボイスコイルモータ磁気回路ヨーク用鉄合金板材およびボイスコイルモータ磁気回路用ヨーク
DE10211511B4 (de) 2002-03-12 2004-07-08 Fraunhofer-Gesellschaft zur Förderung der angewandten Forschung e.V. Verfahren zum Fügen von planaren übereinander angeordneten Laminaten zu Laminatpaketen oder Laminatbauteilen durch Laserstrahlschweißen
DE10216098A1 (de) 2002-04-12 2003-10-23 Bosch Gmbh Robert Rotor für eine elektrische Maschine
DE10320350B3 (de) 2003-05-07 2004-09-30 Vacuumschmelze Gmbh & Co. Kg Hochfeste weichmagnetische Eisen-Kobalt-Vanadium-Legierung
EP1503486B1 (fr) 2003-07-29 2009-09-09 Fanuc Ltd Moteur et dispositif pour fabriquer un moteur
JP2006193779A (ja) 2005-01-13 2006-07-27 Hitachi Metals Ltd 軟磁性材料
JP2006322057A (ja) 2005-05-20 2006-11-30 Daido Steel Co Ltd 軟質磁性材料
DE102005034486A1 (de) 2005-07-20 2007-02-01 Vacuumschmelze Gmbh & Co. Kg Verfahren zur Herstellung eines weichmagnetischen Kerns für Generatoren sowie Generator mit einem derartigen Kern
JP4764134B2 (ja) 2005-10-21 2011-08-31 日本グラスファイバー工業株式会社 導電性不織布
US8029627B2 (en) 2006-01-31 2011-10-04 Vacuumschmelze Gmbh & Co. Kg Corrosion resistant magnetic component for a fuel injection valve
US20070176025A1 (en) 2006-01-31 2007-08-02 Joachim Gerster Corrosion resistant magnetic component for a fuel injection valve
ATE418625T1 (de) 2006-10-30 2009-01-15 Vacuumschmelze Gmbh & Co Kg Weichmagnetische legierung auf eisen-kobalt-basis sowie verfahren zu deren herstellung
US8012270B2 (en) 2007-07-27 2011-09-06 Vacuumschmelze Gmbh & Co. Kg Soft magnetic iron/cobalt/chromium-based alloy and process for manufacturing it
US9057115B2 (en) 2007-07-27 2015-06-16 Vacuumschmelze Gmbh & Co. Kg Soft magnetic iron-cobalt-based alloy and process for manufacturing it

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS61253348A (ja) * 1985-05-04 1986-11-11 Daido Steel Co Ltd 軟質磁性材料
JPS6293342A (ja) * 1985-10-17 1987-04-28 Daido Steel Co Ltd 軟質磁性材料
EP0715320A1 (fr) * 1994-11-29 1996-06-05 Vacuumschmelze Gmbh Alliage magnétiquement doux à base de fer contenant du cobalt pour circuits de commutation et d'excitation
DE4444482A1 (de) * 1994-12-14 1996-06-27 Bosch Gmbh Robert Weichmagnetischer Werkstoff
WO2001000895A1 (fr) * 1999-06-23 2001-01-04 Vacuumschmelze Gmbh Alliage fer-cobalt a faibles intensites de champ coercitifs et procede de realisation de demi-produits a partir d'un alliage fer-cobalt
US20040099347A1 (en) * 2000-05-12 2004-05-27 Imphy Ugine Precision Iron-cobalt alloy, in particular for electromagnetic actuator mobile core and method for making same

Cited By (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2451219A (en) * 2007-07-27 2009-01-28 Vacuumschmelze Gmbh & Co Kg Soft magnetic iron-cobalt based alloy
GB2451219B (en) * 2007-07-27 2009-09-23 Vacuumschmelze Gmbh & Co Kg Soft magnetic iron-cobalt-based alloy and process for manufacturing it
EP2083428A1 (fr) * 2008-01-22 2009-07-29 Imphy Alloys Alliage Fe-Co pour actionneur électromagnétique à grande dynamique
JP2011525945A (ja) * 2008-01-22 2011-09-29 アルセロールミタル−ステンレス・アンド・ニツケル・アロイ ダイナミックレンジが大きい電磁アクチュエータ用のＦｅ−Ｃｏ合金
DE102008053310A1 (de) * 2008-10-27 2010-04-29 Vacuumschmelze Gmbh & Co. Kg Werkstück aus weichmagnetischem Werkstoff mit verschleißfester Beschichtung und Verfahren zur Herstellung des Werkstücks
WO2019081670A1 (fr) * 2017-10-27 2019-05-02 Vacuumschmelze Gmbh & Co Kg Alliage magnétique doux à perméabilité élevée et procédé pour produire l'alliage magnétique doux à perméabilité élevée
WO2019081672A1 (fr) * 2017-10-27 2019-05-02 Vacuumschmelze Gmbh & Co Kg Alliage magnétique doux à perméabilité élevée et procédé pour produire l'alliage magnétique doux à perméabilité élevée
CN111373494A (zh) * 2017-10-27 2020-07-03 真空融化股份有限公司 高磁导率软磁合金和制造高磁导率软磁合金的方法
CN111373494B (zh) * 2017-10-27 2022-02-18 真空融化股份有限公司 高磁导率软磁合金和制造高磁导率软磁合金的方法
EP3971919A1 (fr) * 2017-10-27 2022-03-23 Vacuumschmelze GmbH & Co. KG Procédé de fabrication d'un alliage magnétique tendre à perméabilité élevée
CN111926268A (zh) * 2019-04-26 2020-11-13 真空融化股份有限公司 板材叠层和制造高磁导率软磁合金的方法

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ATE418625T1 (de) 2009-01-15
US20090145522A9 (en) 2009-06-11
DE502007000329D1 (de) 2009-02-05
EP1918407B1 (fr) 2008-12-24
US7909945B2 (en) 2011-03-22

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