WO2017017256A1 - Tôle ou bande en alliage feco ou fesi ou en fe et son procédé de fabrication, noyau magnétique de transformateur réalisé à partir d'elle et transformateur le comportant - Google Patents
Tôle ou bande en alliage feco ou fesi ou en fe et son procédé de fabrication, noyau magnétique de transformateur réalisé à partir d'elle et transformateur le comportant Download PDFInfo
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- WO2017017256A1 WO2017017256A1 PCT/EP2016/068172 EP2016068172W WO2017017256A1 WO 2017017256 A1 WO2017017256 A1 WO 2017017256A1 EP 2016068172 W EP2016068172 W EP 2016068172W WO 2017017256 A1 WO2017017256 A1 WO 2017017256A1
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- 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- 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 by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
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- 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
- C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
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- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
- C21D1/76—Adjusting the composition of the atmosphere
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- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
- C21D1/773—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material under reduced pressure or vacuum
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- 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 by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1233—Cold rolling
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- 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 by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1266—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest between cold rolling steps
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- 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 by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1272—Final recrystallisation annealing
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- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- 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
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- 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
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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
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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
- H01F1/14766—Fe-Si based alloys
- H01F1/14775—Fe-Si based alloys in the form of sheets
- H01F1/14783—Fe-Si based alloys in the form of sheets with insulating coating
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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
- H01F1/16—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 in the form of sheets
- H01F1/18—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 in the form of sheets with insulating coating
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
- H01F41/02—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets
- H01F41/0206—Manufacturing of magnetic cores by mechanical means
- H01F41/0233—Manufacturing of magnetic circuits made from sheets
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- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- 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 by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1222—Hot rolling
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- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- 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
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- 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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
Definitions
- the present invention relates to alloys of iron and cobalt, particularly those having a content of the order of 10 to 35% of Co, and also pure iron and alloys of iron and silicon which have a content of 3% of Si. These materials are used to form magnetic parts such as transformer cores, especially for aeronautics.
- the low-frequency transformers ( ⁇ 1 kHz) embedded in the aircraft consist mainly of a magnetic core magnetic soft alloy, laminated, stacked or wound according to the constraints of construction, and primary and secondary windings (s) copper.
- the primary supply currents are variable in time, periodic but not necessarily purely sinusoidal, which does not fundamentally change the needs of the transformer.
- the transformer shall operate on a roughly sinusoidal frequency power supply network, with an amplitude of the output voltage that may vary transiently by up to 60% from one moment to the next, and in particular when when the transformer is energized or when an electromagnetic actuator is suddenly switched on. This has the consequence, and by construction, a current draw to the primary of the transformer through the nonlinear magnetization curve of the core magnetic.
- the elements of the transformer (insulators and electronic components) must be able to withstand, without damage, large variations of this inrush current, the so-called "inrush effect".
- the noise emitted by the transformer due to electromagnetic forces and magnetostriction must be low enough to comply with the standards in force or to meet the requirements of users and personnel posted near the transformer.
- pilots and co-pilots want to be able to communicate either with helmets but directly.
- the thermal efficiency of the transformer is also very important to consider, since it sets both its internal operating temperature and the heat flows that must be discharged, for example by means of an oil bath surrounding the windings and the cylinder head, associated with oil pumps dimensioned accordingly.
- the thermal power sources are mainly Joule losses from primary and secondary windings, and magnetic losses from magnetic flux variations over time and in the magnetic material.
- the volume thermal power to be extracted is limited to a certain threshold imposed by the size and power of the oil pumps, and the internal operating limit temperature of the transformer.
- the cost of the transformer must be kept as low as possible in order to ensure the best technical-economic compromise between cost of materials, design, manufacturing and maintenance, and optimization of the electrical power density (mass or volume). ) of the device through taking into account the thermal regime of the transformer.
- the transformer comprises a magnetic circuit wound when the power is Single phase.
- the structure of the core of the transformer is formed by two toric cores of the preceding type contiguous, and surrounded by a third torus wound and forming an "eight" around the two previous ring cores.
- This form of circuit in practice imposes a small thickness of the magnetic sheet (typically 0.1 mm). In fact, this technology is used only when the supply frequency constrains, taking into account the currents induced, to use strips of this thickness, that is to say typically for frequencies of a few hundred Hz.
- cut-stack core a stacked magnetic circuit is used, regardless of the thicknesses of magnetic sheets envisaged. This technology is therefore valid for any frequency below a few kHz. However, special care must be taken in deburring, juxtaposing or even electrical insulation of the sheets, in order to reduce both the parasitic air gaps (and thus optimize the apparent power) and to limit the currents induced between sheets.
- a soft magnetic material with high permeability is used in embedded power transformers, and whatever the band thickness envisaged.
- Two families of these materials exist in thicknesses of 0.35 mm to 0.1 or even 0.05 mm, and are clearly distinguished by their chemical compositions:
- Fe-3% Si alloys (the compositions of the alloys are given throughout the text in% by weight) whose brittleness and electrical resistivity are mainly controlled by the Si content; their magnetic losses are quite low (non-oriented N.O. grain alloys) to low (G.O. grain oriented alloys), their saturation magnetization Js is high (of the order of 2T), their cost is very moderate;
- Fe-3% Si subfamilies used either for embedded transformer core technology or for another:
- NO Non-Oriented Grain Fe-3% Si
- Fe-48% Co-2% V alloys whose brittleness and electrical resistivity are mainly controlled by vanadium; they owe their high magnetic permeabilities not only to their physical characteristics (low K1) but also to the cooling after final annealing which sets K1 at a very low value; because of their fragility, these alloys must be shaped in the hardened state (by cutting, stamping, folding ...), and only once that the piece has its final shape (rotor or stator of rotating machine, profile E or I transformer) the material is then annealed in the last step; moreover, because of the presence of V, the quality of the annealing atmosphere must be perfectly controlled so as not to be oxidizing; finally the price of this material, very high (20 to 50 times that of Fe-3% Si - G.O.), is related to the presence of Co and is roughly proportional to the content of Co; Fe-Co alloys with lower levels of Co (typically 18 or 27%) also exist; they have the advantage of being cheaper than the previous ones, as they contain less Co, while providing
- the high saturation materials (pure Fe, Fe-Si or Fe-Co at less than 40% Co) have a magnetocrystalline anisotropy of several tens of kJ / m 3 , which does not allow them to have a high permeability in the case of a random distribution of the final crystallographic orientations.
- magnetic plates less than 48% Co for medium-frequency on-board transformers, it has long been known that the chances of success necessarily pass through an acute texture characterized by the fact that in each grain, an axis ⁇ 100> is very close to the rolling direction.
- the so-called "Goss" ⁇ 1 10 ⁇ ⁇ 001> texture obtained in Fe-Si by secondary recrystallization is an illustrative case.
- the sheet should not contain cobalt.
- a transformer-optimized Fe-48% Co-2% V alloy has a B 800 of approximately 2.15 T ⁇ 0.05 T, which allows an increase in magnetic flux at 800 A / m for a same breech section from about 13% ⁇ 3%, to 2500 A / m from about 15%, to about 5000 A / m from about 16%.
- B 1 should be lowered to about 1 T, instead of 1.4 to 1.7 T for Fe-Si or Fe-Co in the absence of noise requirements. It is also often necessary to pad the transformer, resulting in an increase in weight and bulk.
- nanocrystallines pose a major problem in the case of a solution "embedded transformer”: their thickness is about 20 ⁇ and they are wound torus amorphous soft state around a rigid support, so that the shape torus either preserved throughout the heat treatment resulting in the nanocrystallization. And this support can not be removed after the heat treatment, always so that the shape of the torus can be preserved, and also because the torus is then often cut in half to allow a better compactness of the transformer by using the technology of the previously wound circuit described. Only impregnating resins of the wound core can maintain it in the same form in the absence of the support which is removed after polymerization of the resin.
- the nanocrystallines have a saturation magnetization Js significantly lower than the other soft materials (iron, FeSi3%, Fe-Ni50%, FeCo, amorphous iron base), which requires significantly increase the transformer, since the increase magnetic core section will have to compensate for the drop in work induction imposed by Js. Also the solution "nanocrystalline" would be used as a last resort, if the maximum noise level required is low and if another solution lighter and low noise did not appear.
- the object of the invention is to propose a material for constituting transformer cores exhibiting only very low magnetostriction, even when they are subjected to a strong induction of work which would make it possible not to use a mass of magnetic core. too important, therefore to provide transformers having a high specific power density (or volume). In this way, the transformers they would achieve could advantageously be used in environments such as an aircraft cockpit where a low magnetostriction noise would be advantageous for the comfort of users.
- the subject of the invention is a sheet or strip made of cold rolled and annealed ferrous alloy, characterized in that its composition consists of, in weight percentages:
- the rest being iron and impurities resulting from the elaboration, in that, for an induction of 1, 8 T, the maximum difference (Max ⁇ ) between the magnetostriction deformation amplitudes ⁇ , measured parallel to the magnetic field ( Ha) applied ( ⁇ // ⁇ ) and perpendicular to the applied magnetic field (Ha) (A-LH) on three rectangular samples (2, 3, 4) of said sheet or strip whose long sides are respectively parallel to the direction rolling (DL) of said sheet or strip, either parallel to the transverse direction (DT) of said sheet or strip, or parallel to the direction forming an angle of 45 ° with said rolling direction (DL) and said transverse direction ( DT), being at most 25ppm, and in that its recrystallization rate is 80 to 100%.
- Max ⁇ the maximum difference between the magnetostriction deformation amplitudes ⁇ , measured parallel to the magnetic field ( Ha) applied ( ⁇ // ⁇ ) and perpendicular to the applied magnetic field (Ha) (A-LH) on three rectangular samples (2
- the strip or sheet has not more than 30% of any texture component ⁇ hkl ⁇ ⁇ uvw> defined by a disorientation of less than 15 ° around a defined crystallographic orientation ⁇ h 0 kolo ⁇ ⁇ u 0 VoWo>.
- the invention also relates to a method for manufacturing a ferrous alloy strip or sheet of the above type, characterized in that:
- a ferrous alloy is produced whose composition consists of: - traces ⁇ C ⁇ 0.2%, preferably traces ⁇ C ⁇ 0.05%, better traces ⁇ C ⁇
- said ingot or semi-continuous casting product is hot-shaped in the form of a strip or a sheet 2 to 5 mm thick, preferably 2 to 3.5 mm thick;
- At least two cold rolling operations of said strip or sheet each having a reduction ratio of 50 to 80%, preferably 60 to 75%, at a temperature which is: from ambient temperature to 350 ° C., if the alloy has a Si content such that 3.5 - 0.1% Co ⁇ Si + 0.6% Al ⁇ 4.5 - 0.1% Co and Co ⁇ 35%, or if the alloy contains Co ⁇ 35% and Si ⁇ 1%; and if the cold rolling is preceded by reheating, preferably baking, for a period of 1 h to 10 h and at a maximum temperature of 400 ° C;
- said cold rolling being each separated by static annealing or by passing in the ferritic range of the alloy, for 1 minute to 24 hours, preferably for 2 minutes to 1 hour, at a temperature of at least 650 ° C. C, preferably at least 750 ° C, and at most:
- said annealing separating two cold rolling operations taking place in an atmosphere containing at least 5% of hydrogen, preferably 100% of hydrogen, and less than 1% in total of gaseous oxidizing species for the alloy, preferably less than 100 ppm, and having a dew point below + 20 ° C, preferably below 0 ° C, more preferably below -40 ° C, optimally below -60 ° C;
- the final recrystallization anneal can be carried out under vacuum, or in a non-oxidizing atmosphere for the alloy, or in a hydrogenated atmosphere.
- the final recrystallization annealing can be carried out in an atmosphere containing at least 5% hydrogen, preferably 100% hydrogen, and less than 1% in total of gaseous oxidizing species for the alloy, preferably less than 100 ppm, and having a dew point below + 20 ° C, preferably below 0 ° C, more preferably below -40 ° C, optimally below -60 ° C.
- the first cold rolling may be preceded by static or bypass annealing, in the ferritic range of the alloy, for 1 min to 24 h, preferably for 2 min to 10 h, at a temperature of at least 650 ° C, preferably at least 700 ° C, and at most:
- said annealing taking place in an atmosphere containing at least 5% hydrogen, preferably 100% hydrogen, and less than 1% total oxidizing gaseous species for the alloy, preferably less than 100 ppm, and having a dew point below + 20 ° C, preferably below 0 ° C, more preferably below -40 ° C, optimally below -60 ° C.
- the final recrystallization annealing can be followed by cooling carried out at a speed of less than or equal to 2000 ° C./h, preferably less than or equal to 600 ° C./h.
- the final recrystallization annealing may be preceded by heating carried out at a speed of less than or equal to 2000 ° C./h, preferably less than or equal to 600 ° C./h.
- an oxidation annealing can be carried out at a temperature of between 400 and 700 ° C., preferably between 400 and 550 ° C., for a period of time which makes it possible to obtain an insulating oxidized layer of thickness. 1 to 10 ⁇ on the surface of the sheet or strip.
- the invention also relates to a magnetic transformer core, characterized in that it is composed of stacked or wound sheets, at least some of which have been manufactured from a sheet or strip of the above type.
- the subject of the invention is a transformer comprising a magnetic core, characterized in that said core is of the preceding type.
- the invention is based on the use as a material intended to constitute magnetic parts, such as elements of a transformer core, of an iron-cobalt or iron-silicon or iron-type alloy.
- -Silicon-aluminum on which we carried out well-defined thermal and mechanical treatments, the heat treatments being all in the ferritic field of the alloy.
- pure iron or very low alloy is also envisaged.
- this magnetostriction presents a remarkable isotropy, even for these high fields. It remains, in almost nil in both the rolling direction of the sheet, in the transverse direction (perpendicular to the rolling direction) and in the direction forming an angle of 45 ° with these two directions, to a field ambient magnet at least 1 T. Beyond 1 T, the difference between the magnetostrictions observed in these three directions remains remarkably reduced down to a field of at least 1.8 T or even 2 T.
- transformers having low magnetostrictive noise are obtained in all directions of the sheets constituting their cores, and therefore a particularly low overall magnetostriction noise, making them suitable for constituting, in particular, embedded transformers for aircraft which can be placed in the station. without hindering the direct conversations between its occupants.
- FIGS. 2, 3, 10, 11 and 12 which show the magnetostriction curves, as a function of the intensity of the magnetic field in various directions, of samples of a FeCo27 alloy obtained by methods which are not in accordance with FIG. invention;
- FIGS. 4 to 9 which show the magnetostriction curves, as a function of the intensity of the magnetic field in various directions, of FeCo27 alloy samples obtained by methods in accordance with the invention.
- the metals and alloys to which the invention applies are iron and ferrous alloys ferritic structure, containing, in addition to iron and impurities and residual elements resulting from their development, the following chemical elements. All percentages are percentages by weight.
- a small amount of the element in question is detected by the analysis apparatus in the final alloy, because of its almost unavoidable presence in some of the raw materials used or because of the pollution introduced during the preparation of the liquid metal.
- This pollution may be due, for example, to the wear of the refractory materials, in particular containing magnesia and / or alumina and / or silica, which coat the containers (melting furnace, ladle, etc.). where the liquid metal dwells.
- the contact of the liquid metal with the atmosphere can also lead to the absorption of nitrogen, and also oxygen which can be combined with the most deoxidizing elements (Al, Si, Mn, Ti, Zr ...) to form non-metallic inclusions some of which will remain in the final metal.
- the alloys composing the sheets or strips according to the invention contain C at a content between traces resulting from the elaboration, without the C having been added to raw materials, and 0.2%, preferably between traces and 0.05%, better between traces and 0.015%.
- the FeCo27 and FeSi3 type alloys under which certain possible variants of the invention fall typically have C contents of 0.005 to 0.15%, which result much more from the deoxidation conditions of the liquid metal (including the formation of CO within of liquid metal during vacuum passes) than a deliberate desire to recover these C contents in the final product for reasons related to the mechanical or magnetic properties of the alloy.
- the Co may be present in limited quantity, only in the state of traces resulting from the elaboration, so not to be added voluntarily, but if Co ⁇ 35% it is necessary Si + 0.6% AI ⁇ 4.5 - 0 , 1% Co and also Si ⁇ 3.5%. Thus, for example, in the absence of cobalt, a trace content of 3.5% Si and 1% traces of Al are required to remain within the scope of the invention. It is then in the case of an alloy of the class of iron-silicon or iron-silicon-aluminum alloys, or even a pure iron or very little alloy, to which the invention can also be applied.
- the alloy to which the invention applies contains an Si content which is:
- a content of Si + 0.6% AI ⁇ 4.5 - 0.1% Co can be accepted if the rolling is carried out not strictly cold, but "warm”, that is to say at a temperature up to 350 ° C, this rolling temperature being preferably obtained by a stoving, that is to say a heating in a static chamber at a low temperature.
- This warm rolling (which it is agreed is fully comparable to cold rolling in the context of the invention, the term "cold rolling”, when no more details on the temperature of its performance, should be understood in the present text to include also warm rolling up to 350 ° C. It is used as opposed to hot-rolling known metallurgists, which are carried out at significantly higher temperatures.
- the reheating temperature is to be determined also as a function of the cooling that the band or the sheet will undergo, predictably, during its transfer between the heating system and the rolling mill.
- the reheating temperature must be sufficient for the actual temperature of the strip or sheet at the time of warm rolling to be the target, but it must not exceed 400 ° C to avoid significant oxidation of the material during reheating. or even during the transfer to the rolling mill.
- the use of a neutral or reducing atmosphere during the parboiling, or reheating in general, is not excluded.
- the Si content is also governed by the desire to permanently retain during the manufacture of the material a ferritic structure, which is important for obtaining the low and isotropic magnetostriction on which the invention is based.
- the Cr content can range from 10% traces.
- An addition of Cr modifies only very little the stacking fault energy of the Fe, and therefore does not significantly modify the texture filiations during the treatments carried out according to the invention. It lowers saturation magnetization J sat , and it is not desirable to add an amount exceeding 10% for this reason.
- just like Si it substantially increases the electrical resistivity, and therefore advantageously decreases the magnetic losses. Cooling the transformer allows, however, to tolerate further magnetic losses, and a low or even trace Cr content may be acceptable in this case.
- the total contents of V, W, Mo and Ni are between traces and 4%, preferably between traces and 2%. These elements increase the electrical resistivity, but they lower the saturation magnetization, which we do not generally want.
- the Mn content is between traces and 4%, preferably between traces and 2%.
- the reason for this relatively low maximum content is that Mn reduces the saturation magnetization which is one of the major contributions of FeCo. Mn only slightly increases the electrical resistivity. Especially it is a gamma element, which reduces the temperature range allowing a ferritic annealing. We have seen that for questions related to the inheritance of ferritic microstructures, it was undesirable to leave the ferritic domain during treatments, and an excessive presence of Mn would increase the risks of such an exit.
- the Al content is between traces and 3%, preferably between traces and 1%. Al reduces saturation magnetization and is much less efficient than Si or Cr to increase electrical resistivity. But Al can be used to extend the range of cold rolling ability of highly alloyed FeCo grades when reaching the limits of silicon additions, as previously mentioned.
- the S content is between traces and 0.005%. Indeed, S tends to form sulphides with manganese, and oxysulfides with Ca and Mg, which strongly degrades the magnetic performances and in particular the magnetic losses.
- the P content is between traces and 0.007%. Indeed, P can form phosphides of metal elements harmful to the magnetic properties and development of the microstructure.
- Ni content is between traces and 3%, and preferably less than 0.5%. Indeed, Ni does not increase the electrical resistivity, reduces the saturation magnetization thus degrades the power density and the electrical efficiency of the transformer. Its addition is not necessary.
- the Cu content is between traces and 0.5%, preferably less than 0.05%.
- Cu is very poorly miscible in Fe, Fe-Si or Fe-Co, and thus forms copper-rich, non-magnetic phases, significantly degrading the magnetic performance of the material as well as greatly impeding the development of its microstructure.
- Nb and Zr are each between trace amounts and 0.1%, preferably less than 0.01% because Nb and Zr are well known to be potent inhibitors of grain growth, and thus will strongly and adversely interfere. with the metallurgical mechanism of texture filiation that is suspected to be at the origin of the good results obtained thanks to the invention.
- the Ti content is between traces and 0.2% in order to limit the harmful formation of nitrides, which would significantly degrade the magnetic properties (increased losses) and could interfere with the texture transformation mechanisms during rolling-annealing .
- the N content is between traces and 0.01%, again to avoid excessive formation of nitrides of all kinds.
- the Ca content is between traces and 0.01% to avoid the formation of oxides and oxysulphides which would be harmful for the same reasons as Ti nitrides.
- the Mg content is between traces and 0.01% for the same reasons as Ca.
- the content of Ta is between traces and 0.01% because it can hinder strongly the growth of the grain.
- the B content is between traces and 0.005% to avoid the formation of boron nitrides which would have the same effects as the nitrides of Ti.
- the content of O is between traces and 0.01% to prevent oxidized inclusions formed in excessive amounts have the same adverse effects as nitrides.
- a continuously cast ingot or semi-finished product having the composition described above is prepared.
- all methods of preparation and casting to obtain this composition are usable.
- methods are recommended such as slag arc melting, vacuum slag induction melting (VIM for Vacuum Induction Melting). They are preferably followed by remelting processes to obtain a secondary ingot.
- VIM vacuum slag induction melting
- the ESR (Electroslag Remelting) or VAR (Vacuum Arc Remelting) type processes are particularly suitable for obtaining alloys having optimum purity and small fractions of precipitates for the preferred applications of the invention.
- the preformed ingot, or the continuous casting product is hot-rolled in the usual way until a sheet or strip 2 to 5 mm thick, preferably between 2 and 3.5 mm, for example with a thickness of the order of 2.5 mm.
- This hot rolling is therefore the last step (or only) of the hot forming of the method according to the invention.
- a static or on-going annealing of said sheet or strip is carried out in the ferritic field, therefore at a temperature of between 650, preferably 700 ° C., and a temperature which guarantees that no will not come out of the purely ferritic domain and which therefore depends on the composition of the alloy, for 1 minute to 10 hours.
- the heat treatment temperature T tth of this annealing can go up to 1400 ° C.
- the temperature T tth heat treatment of the annealing is such that T tth ⁇ T a.
- This annealing must be carried out in a dry hydrogenated atmosphere.
- the atmosphere should contain between 5% and ideally 100% hydrogen, the remainder being one or more neutral gases such as argon or nitrogen. Such an atmosphere can result from the use of cracked ammonia.
- a maximum content of 1% in total of gaseous oxidizing species for the alloy may be present, preferably less than 100 ppm.
- the dew point of the atmosphere is at most + 20 ° C, preferably at most 0 ° C, better at most -40 ° C, optimally at most -60 ° C.
- This hydrogenated, thus reducing, atmosphere functions as compared to an atmosphere that would be simply neutral, a fortiori oxidizing: to prevent oxidation of the surface of the sheet or strip and the grain boundaries; such an oxidation of the grain boundaries is very unfavorable to the descent of the texture, and if it was confirmed that one of the reasons for the success of the invention was this very good texture filiation during thermal treatments and laminates. cold, it would be an important condition for the implementation of the invention;
- H 2 is by far the most heat-carrying gas, and it makes it possible to obtain laminatable strips without any risk of breakage at the annealing outlet, by avoiding a weakening order, thanks to an efficient extraction of the heat from the strip annealed in the ordering zone (between 500 and 700 ° C).
- the process is carried out (either after the optional annealing above, or after the hot rolling), then at a first cold rolling at a reduction ratio of 50 to 80%, preferably 60 to 75%, and at a temperature between room temperature (for example 20 ° C) and 350 ° C.
- the upper limit of 350 ° C corresponds to the case where, as we have seen, a "warm" lamination is practiced, the heating being preferably carried out by a parboiling, for alloys relatively rich in Si.
- the temperature of the cold rolling is between ambient temperature and 100 ° C.
- a reduction rate too low (less than 50%) in at least one of the cold rolling or "warm” does not, as we shall see, to obtain the weak and isotropic magnetostriction sought.
- An excessively high reduction rate (greater than 80%) would be likely to modify the texture of the material too much so that the magnetostriction will be degraded.
- Static or by-pass annealing in the ferritic range is then carried out at a bearing temperature of between 650 and 930 ° C., preferably between 800 and 900 ° C., and for 1 minute at 24 hours, preferably 2 minutes. at 1 h, in a hydrogenated atmosphere (partial or total) dry as defined above, for reasons seen about the optional annealing following hot rolling, followed by cooling to be performed under conditions similar to those described for the optional annealing and for the same reasons.
- a second cold rolling is then carried out, the characteristics of which are in the same ranges as those already exposed for the first cold rolling.
- this final annealing can also be carried out under vacuum, under neutral gas (argon for example) or even in air, in the ferritic range, at a temperature of 650 to 900 (2 x% Co)] ° C, for a period of 1 minute to 48 hours.
- a hydrogenated atmosphere is not necessarily necessary for this last annealing, because at this stage the metal may have already reached its final dimensions, especially in thickness, or even in terms of its perimeter, especially if a cutting has already occurred. place to give the pieces of the future stack their final shapes and dimensions. In this case, even if a lack of hydrogen led to embrittlement of the metal during this recrystallization annealing, it would be without consequences if it only remained to stack the pieces to form the core.
- Static annealing whose rate of rise in temperature is lower than for an annealing with the parade and which lasts longer, has the advantage of making the ferritic grain greasier than an annealing with the parade, which is favorable to the obtaining low magnetic losses.
- this final annealing is concluded by a relatively slow cooling such as a natural cooling in air, or a cooling under a hood or other device limiting the heat loss by radiation.
- a relatively slow cooling such as a natural cooling in air, or a cooling under a hood or other device limiting the heat loss by radiation.
- Faster cooling would be likely to introduce internal stresses by establishing a thermal gradient in the material, which would degrade the magnetic losses.
- Cooling after annealing other than final annealing does not have any special advantage to be performed at a low speed. Too slow cooling could even reduce the laminability of the material in the next step.
- This relatively slow cooling is preferably coupled to a temperature rise rate for annealing which is also less than or equal to 2000 ° C / h, more preferably less than or equal to 600 ° C / h.
- the rate of rise in temperature for the final annealing and the rate of cooling which follows this final annealing are among the parameters that can be used to achieve the desired objectives in terms of low and isotropic magnetostiction of the alloys used in the invention, in addition to the composition of the alloy and the conditions of its thermal and thermomechanical treatments during cold or warm rolling and annealing.
- a supplementary oxidation annealing of the material at a temperature between 400 and 700 ° C., preferably between 400 and 550 ° C., allowing a strong but superficial oxidation of the material on at least one of its faces, without the risk of intergranular oxidation since it is known to occur at higher temperatures.
- This oxidation layer has a thickness of 0.5 at 10 ⁇ and guarantees electrical insulation between the stacked parts of the transformer magnetic core, which substantially reduces the induced currents and therefore the magnetic losses of the transformer.
- this oxidation layer can easily be determined by those skilled in the art using conventional experiments, depending on the precise composition of the material and the oxidizing power of the chosen treatment atmosphere. (air, pure oxygen, oxygen-gas mixture neutral ...) vis-à-vis this material. Conventional analyzes of the composition of the oxidation layer and its thickness make it possible to determine for which treatment conditions of a given material (temperature, duration, atmosphere) the desired oxidation layer can be obtained.
- a manufacturing method has been described comprising two cold rolling steps and two or three annealing. But it would remain in accordance with the invention to perform more cold rolling steps similar to those described, which can be separated by intermediate annealing similar to the first mandatory annealing that has been described.
- each of the cold rollings with a reduction rate of 50 to 80%, preferably 60 to 75%, which has been mentioned can be carried out gradually, in several successive passes not separated by an intermediate annealing.
- the final result is a cold-rolled annealed sheet or strip whose thickness is typically 0.05 to 0.3 mm, preferably at most 0.25 mm, better at most 0.22 mm to limit the magnetic losses, which has the peculiarity of presenting very low magnetostrictions ⁇ in the three directions DL (rolling direction), DT (transverse direction) and 45 ° (median direction between DL and DT), measured both parallel and perpendicularly to the direction of the applied field, and especially a very small difference between the magnetostrictions the highest and the lowest of those measured, and this for different inductions of 1, 2 T to 1, 8 T.
- the criterion of user satisfaction is the maximum deviation "Max ⁇ " between the magneto-striction amplitudes observed during measurements made on three types of sample from the same material and represented in FIG. 1.
- Max ⁇ the maximum deviation between the magneto-striction amplitudes observed during measurements made on three types of sample from the same material and represented in FIG. 1.
- the examples which follow will be based on this evaluation method. These samples are taken on a strip 1 prepared according to the invention or according to a reference method, according to the example. Its rolling direction DL, its direction through DT and its median direction 45 ° are represented by arrows. Three types of samples are taken from the sheet 1 for carrying out the magnetostriction tests.
- Type 1 elongate rectangular samples 2 (eg 120x15 mm) cut so that the LONG direction of sample 2 is parallel to DL.
- the magnetic field Ha will be applied during the deformation measurement, by an excitation coil of the same axis as the LONG direction of the sample 2, thus also in the LONG direction of the sample 2.
- the deformation measures ⁇ named // A H DL, are performed both in the direction of the field (K H "DI Z / / H), and perpendicular thereto (A // H DL gj_ H) and hence two values of magnetostriction for sample 2 of type 1.
- Type 2 elongate rectangular samples (e.g. 120x15 mm) cut so that the LONG direction of sample 3 is parallel to the 45 ° axis of DL and DT.
- the magnetic field Ha will be applied during the deformation measurement, by an excitation coil of the same axis as the LONG direction of the sample 3, also in the LONG direction of the sample 3.
- the deformation measures, called ⁇ ⁇ // 45 °, are carried out both in the direction of the field ( ⁇ ⁇ // 45 ° ⁇ // ), and perpendicularly thereto ( ⁇ ⁇ // 45 ° ⁇ ⁇ ⁇ ) and thus results in two magnetostriction values for sample 3 type 2.
- Type 3 elongate rectangular samples 4 (eg 120x15 mm) cut so that the LONG direction of sample 4 is parallel to DT.
- the magnetic field Ha will be applied during the deformation measurement, by an excitation coil of the same axis as the LONG direction of the sample 4, also in the LONG direction of the sample 4.
- the deformation measurements, called A H // DT are performed both in the direction of the field ( ⁇ TM 1 ⁇ ), and perpendicular thereto (A H // DT £ j_ H ) and therefore results in two magnetostriction values for the sample 4 type 3.
- a total of six different strain measurements are thus measured at each induction level B (measured) of each of the three sample types.
- the Magnetoctric behavior of the material not only three directions (types) of sampling are used (DL, DT and the direction making an angle of 45 ° with Dl and DT) but also several levels of induction such as for example 1 T , 1, 5T, 1, 8T.
- Max ⁇ measured for an induction amplitude B in the material and which can also be noted Max ⁇ ( ⁇ )
- Max ⁇ is representative of the isotropy of the magnetostriction. It is therefore calculated by taking into account the highest value and the lowest value among these six values of ⁇ measured on samples 2, 3, 4 coming from the same band 1 of material as indicated in FIG. This is the highest value that can be found among the six absolute values of the algebraic differences between each possible pair of magnetostriction measurements described above. In other words :
- ⁇ 8 ⁇ ( ⁇ ) ⁇ 8 ⁇
- V 0.01 0.01 ⁇ 0.005 0.51 ⁇ 0.005 ⁇ 0.005 ⁇ 0.005 ⁇ 0.005 ⁇ 0.005 2.03 ⁇ 0.005 ⁇ 0.005 ⁇ 0.005 ⁇ 0.005 ⁇ 0.005
- the alloy was developed in a vacuum induction furnace, and then cast in the form of a frustoconical ingot of 30 to 50 kg, with a diameter of 12 cm to 15 cm and a height of 20 to 30 cm. it was then rolled on a roughing mill to a thickness of 80 mm, and then hot rolled at a temperature of about 1000 ° C to a thickness of 2.5 mm.
- sample 2 LAF 1 at 84% reduction rate; annealing 1 at parade at 1100 ° C for 3 min; LAF 2 at 50% reduction rate; annealing 2 static at 700 ° C, 1 h;
- sample 3 annealing 1 at the parade at 900 ° C for 8 min; LAF 1 at 70% reduction rate; annealing 2 at parade for 8 min at 900 ° C; LAF 2 at 70% reduction rate; annealing 3 static at 660 ° C, 1 h;
- sample 4 annealing 1 at 900 ° C on the parade for 8 min; LAF 1 at 70% reduction rate; annealed 2 at 900 ° C on the parade for 8 min; LAF 2 at 70% reduction rate; annealing 3 static at 680 ° C, 1 h;
- sample 5 annealing 1 at 900 ° C parade for 8 min; LAF 1 at 70% reduction rate; annealed 2 at 900 ° C for 8 min; LAF 2 at 70% reduction rate; annealing 3 static at 700 ° C, 1 h;
- sample 6 annealing 1 at the parade at 900 ° C for 8 min; LAF 1 at 70% reduction rate; annealing 2 at the parade at 900 ° C for 8 min; LAF 2 at 70% reduction rate; annealing 3 static at 720 ° C, 1 h;
- sample 7 annealing 1 at parade for 8 min at 900 ° C; LAF 1 at 70% reduction rate; annealing 2 at parade for 8 min at 900 ° C; LAF 2 at 70% reduction rate; annealing 3 static at 750 ° C, 1 h;
- sample 8 annealing 1 at parade for 8 min at 900 ° C; LAF 1 at 70% reduction rate; annealing 2 at parade for 8 min at 900 ° C; LAF 2 at 70% reduction rate; annealing 3 static at 810 ° C, 1 h.
- sample 9 annealing 1 at parade for 8 min at 900 ° C; LAF 1 at 70% reduction rate; annealing 2 at parade for 8 min at 900 ° C; LAF 2 at 70% reduction rate; annealing 3 static at 900 ° C, 1 h.
- sample 10 annealing 1 at parade for 8 min at 900 ° C; LAF 1 at 70% reduction rate; annealing 2 at parade for 8 min at 900 ° C; LAF 2 at 70% reduction rate; annealing 3 static at 1100 ° C, 1 h.
- sample 1 1 annealing 1 parade for 8 min at 900 ° C; LAF 1 at 80% reduction rate; annealing 2 at parade for 8 min at 900 ° C; LAF 2 at 40% reduction rate; annealing 3 static at 700 ° C, 1 h.
- sample 12 annealing 1 on the parade for 8 min at 900 ° C .; LAF 1 at 70% reduction rate; annealing 2 at parade at 1100 ° C for 8 min; LAF 2 at 70% reduction rate; annealing 3 static at 700 ° C, 1 h.
- the static annealing concluding the elaboration were, for all the samples, preceded by a rise in temperature at a speed of 300 ° C / s and followed by a cooling at a speed of the order of 200 ° C / h, carried out simply leaving the samples in the annealing furnace.
- the rates of rise in temperature before the final annealing and cooling after the final annealing were therefore relatively moderate, which contributed in all cases to obtain a final product relatively little textured, as will be seen in the Table 2.
- the reference samples 1 and 2 were cold-rolled directly after the heat treatments, followed by a high-temperature annealing (1100 ° C) in the austenitic range, then a second cold rolling, and then a final annealing. at 900 ° C (test 1) or 700 ° C (test 2) in the ferritic field.
- the samples according to the invention 3 to 9 have begun, after the heat treatments, to undergo annealing at 900 ° C., then a first cold rolling, then a second annealing at 900 ° C. and then a second cold rolling, then a final annealing at a variable temperature according to the tests, from 660 to 900 ° C. All the anneals thus took place in the ferritic field, in accordance with the invention, and were three in number, as against two for the first two reference samples 1 and 2. All the cold lamination was carried out with a rate of 70% discount.
- the reference sample was first ferritically annealed at 900 ° C as the samples according to the invention and in contrast to the other two reference samples, followed by a first cold rolling and then an intermediate annealing at 900 ° C. , therefore in the ferritic field, then a second cold rolling, and then a final annealing at a temperature of 1100 ° C, thus in the austenitic field. It has thus been subjected to a treatment comparable to that of samples 3 to 9 according to the invention, except that the final annealing has taken place in the austenitic field. All its cold rolling was performed at 70% reduction rate, as for the samples according to the invention.
- the reference sample 1 after the heat treatments, annealed at 900 ° C, then a first cold rolling at 80% instead of 70% as all samples 3 to 10 (which remains in conformity with the invention), then a second annealing at 900 ° C, then a second cold rolling at 40%, so not according to the invention, instead of 70% as all samples 3 to 10, then annealing final at a temperature of 700 ° C, so in the ferritic field.
- the reference sample 12 is quite similar to the sample 10, due to its passage through the austenitic domain, which however takes place at a different stage of the treatment. It first underwent ferritic annealing at 900 ° C, just like the samples according to the invention and unlike the first two reference samples, then a first cold rolling, then an intermediate annealing in the austenitic field at 1100 ° C. C, so not in accordance with the invention, then a second cold rolling, and then a final annealing at a temperature of 700 ° C, so in the ferritic field. It has thus been subjected to a treatment comparable to that of samples 3 to 9 according to the invention, except that the intermediate annealing has taken place in the austenitic range. All its cold rolling was performed at 70% reduction rate, as for the samples according to the invention.
- Table 2 Texture, grain diameter and recrystallization rate of the tested samples according to their treatment conditions
- the different ranges of applied metallurgical treatments have led to substantially identical final grain sizes between the references and the tests according to the invention, that is to say a grain size range of approximately 300 to 15 ⁇ : more precisely from 16 to 95 ⁇ for the tests according to the invention, that is to say when all the anneals are carried out in the ferritic field; from 15 to 285 ⁇ for references, that is to say when at least one step of the process goes beyond the ferritic domain. It can be seen that the grain size range is similar and has no link with the low magnetostrictions obtained.
- test 2 the final annealing was performed at 700 ° C, has leads to a much smaller grain size than that of the tests 1 and 10 of reference and 9 according to the invention, and which is of the same order of magnitude as those of the tests according to the invention 3 to 8 which were also carried out at temperatures close to 700 ° C.
- the metallurgical ranges of the tests according to the invention provide a grain size (between 16 and 95 ⁇ according to the tests) relatively close to that of the reference tests, and in any case quite consistent with what one could wait a priori, especially given the conditions of the final annealing.
- the performance of annealing at 900 ° C. before the first cold rolling in the tests according to the invention and the reference test does not substantially affect, on its own, the size of the grains obtained at the result of the whole process compared to the reference tests 1 and 2 where the cold rolling was carried out directly on the hot rolled sample.
- the reference test 1 1 shows that the low and isotropic magnetostriction target is not obtained either when one of the cold rolling is carried out at a low reduction rate, even if all the annealing takes place in the ferritic field.
- the reference test 12 shows that the low and isotropic magnetostriction target is not obtained either when the second of the three annealing is performed in the austenitic domain.
- Reference Examples 1 and 2 had austenitic annealing performed at the start of treatment after the first cold rolling, and Reference Example 10 had austenitic annealing performed at the very end of treatment. Example 12 thus completes the demonstration of the harmfulness of the austenitic annealing regardless of its position in the treatment.
- Figure 2 shows the magnetostriction results observed during the reference test 1.
- the magnetostriction according to DT begins to become significant and increases very rapidly with induction.
- the magnetostriction begins to increase substantially and rapidly. This leads to significant magnetostrictive deformations of up to several tens of ppm in certain directions at inductions of the order of 2 T, and to a strong anisotropy of these deformations, all in the direction of the creation of a noise of magnetostriction too intense for the preferred applications of the invention envisaged.
- FIG. 3 shows the magnetostriction results observed during the reference test 2. It is observed that, compared to the test 1, the isotropy of the magnetostriction is a little improved, and certain extreme values of the magnetostriction are a little less. But from an induction of 1 T, the magnetostriction begins to become important in the three directions considered. The material thus obtained would therefore not be well suited, either, to the preferred applications of the invention. The significantly smaller grain size in the test 2 sample than in the test 1 sample therefore did not fundamentally improve the magnetostriction results.
- FIG. 4 shows the magnetostriction results observed during test 3 according to the invention.
- the shape of the curves changes radically.
- the magnetostriction differences between the different directions remain relatively small, even for the high fields.
- At 2 or -2 T we have a magnetostriction that does not reach 15 ppm or -10 ppm, and this for all directions considered.
- FIG. 5 shows the magnetostriction results observed during the test 7 according to the invention.
- Magnetostriction curves are qualitatively comparable to those of Test 3 ( Figure 4), with, in addition, a magnetostriction which starts to become significant only for inductions of at least ⁇ 1.5 T. ⁇ 2 T, the magnetostriction can be less than 5 ppm and never exceeds 10 ppm.
- Test 3 differs from Test 3 only in its final annealing temperature of 750 ° C., instead of 660 ° C., which led to a total recrystallization whereas it was not was only 90% in test 3.
- FIG. 6 shows the magnetostriction results observed during the test 8 according to the invention, which had a final annealing temperature of 810 ° C. Magnetostriction curves are qualitatively comparable to those of Run 3 ( Figure 4) and Run 7 ( Figure 5). Quantitatively, the results are good, with maximum values of magnetostriction which remain of the order of ⁇ 10 ppm even for inductions of ⁇ 2 T, and a Max ⁇ of 15 ppm to 1, 8T.
- FIGS. 7 to 9 compare the magnetostriction measurements recorded for tests 5 and 9 according to the invention.
- FIG. 7 shows the tests carried out according to the direction DT
- FIG. 8 shows the tests carried out in the direction 45 °
- FIG. 9 shows the tests carried out according to the direction DT.
- the results are very comparable and excellent for the two tests according to the directions DL and DT up to inductions of ⁇ 1, 8 T.
- the magnetostriction begins to be no longer quite negligible from 1 , 8 T approximately in the case of the test 5, while in the test 9 it remains very low still beyond 2 T.
- a final annealing temperature of 900 ° C thus gives results of magnetostriction better than a final annealing at 700 ° C.
- the magnetostriction at 1, 8T does not exceed ⁇ 5 ppm in the three directions of measurement, which is very significantly better than for the reference tests, both for the absolute value of the magnetostriction and for its isotropy.
- the results of the test 9 are particularly remarkable at high inductions of 1, 8 T or a little beyond, both on the weakness of magnetostriction and its isotropy.
- Figure 10 shows the results of the reference test in which the final anneal was carried out at 1100 ° C, thus in the austenitic domain, while both Prior anneals 1 and 2, carried out at 900 ° C as all annealing 1 and 2 of the tests according to the invention, had been in the ferritic field.
- Magnetostriction curves are found in the various comparable directions, qualitatively and quantitatively, with those of the other reference tests 1 and 2, seen in FIGS. 3 and 4. It can be concluded that the passage of the alloy in the austenitic domain during one of its anneals, even if it occurs only at the end of the treatment, constitutes a very important factor in the non-obtaining of a weak and isotropic magnetostriction.
- Test 11 in which the second cold rolling was carried out with a reduction rate of only 40%, shows, according to FIG. 11, a conventional parabolic and not very isotropic behavior of magnetostriction as a function of induction. , therefore a behavior outside the invention, with for example a magnetostriction according to LD of more than 35ppm to 1, 5T, from about 60ppm to 1, 8T. It can be concluded that textural parentage, modulated by cold rolling reduction rates, is effectively controlled by texture transformations during cold rolling, which restricts the invention to certain reduction rate ranges. .
- FIG. 12 shows the results of the reference test in which the intermediate annealing was carried out at 1100 ° C., thus in the austenitic range, while both anneals 1 and 3 were carried out at 900 ° C., as all annealing 1 and 3 tests according to the invention, so in the ferritic field.
- Magnetostriction curves are found in the various directions comparable to those of the other reference tests 1, 2 and 10, seen in FIGS. 3, 4 and 10, with, however, a fairly significant isotropy of the magnetostriction. But the level of magnetostriction remains too high, even for relatively low inductions. It can be concluded, in conjunction with the test 10, that the passage of the alloy in the austenitic domain during any of its annealing is a very important factor in not obtaining a magnetostriction at the once weak and isotropic
- the magnetic losses of the samples produced according to the invention and having reduced size grains and a structure not completely recrystallized (tests 3 and 4) or completely recrystallized thanks to a final annealing of 700 ° C. or more are not not particularly high, and remain competitive with that obtained on the reference samples.
- the 100% recrystallized and produced samples with a final annealing at 720 ° C and more show magnetic losses still significantly improved compared reference samples, including Test 1, which has a high grain size and a 100% recrystallized structure. This advantage over magnetic losses is, for the moment, not clearly explained by the inventors.
- the results are all the more favorable in terms of magnetic losses as the final ferritic annealing temperature is higher, the best results being obtained for the sample of test 9 which has been annealed at 900 ° C. .
- the ferritic annealing temperatures between 800 and 900 ° C show a weakly to very weakly marked deformation anisotropy and Magnetostriction magnitudes Max ⁇ not exceeding, in any case, not 6 ppm to 1, 5T , 15 ppm to 1, 8T, therefore significantly better than those of the reference test samples.
- the invention is defined by saying, in particular, that all the anneals must take place in the ferritic range, at a minimum temperature of 650 ° C. and at a maximum temperature which, taking into account the effective composition of the alloy, is well in the purely ferritic field, without a transformation of at least a portion of the ferrite into austenite does not occur.
- this maximum temperature as a function of the Si, Co and C contents of the alloy.
- the strips obtained according to the invention can be used to form transformer cores which are both of the "cut-stacked” type and of the "wound” type as defined above. In the latter case, to achieve the winding, it is necessary to use very thin strips of the order of 0.1 to 0.05 mm thick for example.
- an annealing performed before the first cold rolling is preferably carried out within the scope of the invention.
- this annealing is not essential, especially in the case where the hot-rolled strip has been in the wound state for a long time during its natural cooling.
- the winding temperature is often of the order of 850-900 ° C, the duration of this stay can be quite sufficient to obtain on the microstructure of the band at this stage very comparable effects to those that would provide a real annealing in the ferritic field performed under the conditions that have been said for the optional annealing before the first cold rolling.
- Table 5 recalls the results obtained in the previously described tests 1 and 9 on the isotropy of magnetostriction and the magnetic losses at 1.5 T, 400 Hz, and it adds information on cold rolling ability or lukewarm samples before being applied a treatment according to the method of the invention, and saturation magnetization Js of the final product. These results are also compared to those obtained during tests numbered 13 to 24, in which alloys of compositions conforming (13 to 19 and 23, 24) or not (20 to 22) to the invention were also tested. The compositions of these new alloys are also specified, with those of tests 1 and 9 as a reminder. Samples K and L of tests 21 and 22 having proved unfit for cold or warm rolling (breakages due to brittleness, starting from the middle of the strip towards the edges), these tests were not continued at the rolling attempt, hence the lack of results for them in Table 5.
- the final thickness is 0.2 mm.
- test 1 underwent, without prior annealing, an LAF 1 with a reduction rate of 84%, then an annealing R1 on the parade at 1100 ° C. for 3 minutes, then a LAF 2 at a 50% reduction rate, then a static R2 annealing at 900 ° C. for 1 hour.
- Samples B to H were R1 annealed on the parade at 900 ° C for 8 min, then LAF 1 at 70% reduction, followed by R2 annealing at 900 ° C for 8 min. min at 900 ° C, then a LAF 2 at 70% reduction rate, then a static annealing R3 at different temperatures and times, noted in Table 5.
- Sample I (Run 19) was annealed R1 at 900 ° C for 8 min, followed by warm rolling 1 at 150 ° C with 70% reduction, followed by R2 annealing at 900 ° C for 8 min, then a warm rolling 2 at 150 ° C with a reduction rate of 70% and a static annealing R3 at 850 ° C for 30 min.
- Sample J (Run 20) was R1 static annealed at 935 ° C for 1 h, then LAF 1 at 70% reduction, followed by R 2 annealing at 900 ° C for 8 min, followed by LAF 2 at 70% reduction rate, then a static R3 annealing at 880 ° C for 1 h.
- the test according to the invention 9 carried out on the alloy B which is also a FeCo27, for which all the anneals have taken place in the ferritic domain, has, on the other hand, led to an excellent isotropy of the magnetostriction.
- Example 13 also shows relatively significant levels of Si, Cr, Al, Ca, Ta.
- Example 14 also shows significant Si, V and Ti contents. But all these contents remain within the limits defined for the invention.
- the test 24 concerns a 15% Co alloy and devoid of significant contents of other alloying elements, in particular Cr. He too has a particularly weak and isotropic magnetostriction.
- the magnetic losses and the saturation magnetization are of the same order of magnitude as for the other samples treated according to the invention.
- the absence of Cr in the test 24 this absence tending to increase the saturation magnetization, is compensated by a slightly lower presence of Co which goes into the sense of a decrease in saturation magnetization.
- the absence of Cr in the test 24 is in the direction of an increase of the magnetic losses compared to the test 13, but the lower content of Co in the test 24 goes in the direction of a decrease of these same magnetic losses.
- the differences in the composition of the alloy between the tests 13 and 24 tend to offset each other, from the point of view of the magnetic losses and of Js.
- Test 15 shows that a relatively low Co content
- the test 16 according to the invention relates to a Fe-Si-Al alloy with a very low content of
- the test 17 according to the invention relates to an alloy which is practically 99% pure Fe, with relatively low Mn, Ca, Mg presences.
- the isotropy of the magnetostriction is less than in the other tests according to the invention, but it is nevertheless very good in absolute terms, since Max ⁇ at 1.8 T remains ⁇ 25 ppm as required on the sheets or strips according to the invention. 'invention.
- the magnetic losses are also a little higher than for the other tests according to the invention, but remain at a good level, and are lower than those found on the reference test 1.
- Test 18 relates to an alloy of FeCo27 type with a high content of Cr (6%) and also containing Mn (0.81%) and some Mo and B. The good isotropy of the magnetostriction is confirmed, and the magnetic losses are as low as for the test 16 despite the presence of 7 ppm of B. The saturation magnetization remains of the order of that found in the other tests, such as the contents of Cr, Mn and Mo are not so high that they deteriorate undesirably.
- Test 19 relates to a Fe-Si alloy containing 3.5% Si and not containing AI, and shows that the operating conditions of the process according to the invention are also applicable with advantage to this type of FeSi3 alloys to obtain the desired magnetostrictive isotropy.
- this example has particularly low magnetic losses.
- Table 6 presents experimental results obtained by varying the treatment conditions, the composition of the treated alloy and the final thickness of the sample. The results of the previous Tests 1 and 9 were repeated, and new tests 25 to 31 carried out on alloys having the compositions B (FeCo27), I
- Table 6 Influence of the treatment conditions on the isotropy of magnetostriction for different alloy compositions and final thicknesses of the sample If the results of the different tests according to the invention, carried out on samples of the same composition, are compared, sees that varying LAF parameters and annealing within the limits of the definition of the invention still allows to obtain an isotropy of the magnetostriction unusually good in all cases.
- the strips and sheets according to the invention make it possible to manufacture, in particular, after cutting, transformer cores composed of stacked or wound sheets, without requiring modifications of the general design of the cores of these types usually used. It is thus possible to take advantage of the properties of these sheets to produce transformers producing only low magnetostriction noise compared to existing transformers of similar design and dimensioning.
- Transformers for aircraft intended to be installed in a cockpit are a typical application of the invention.
- These sheets can also be used to form cores of higher mass transformers, thus intended for transformers of particularly high power, while retaining a magnetostriction noise remaining within acceptable limits.
- Transformer cores according to the invention may consist entirely of sheets made from strips or sheets according to the invention, or only partially in cases where it would be considered that their combination with other materials would be advantageous technically or financially.
Abstract
Description
Claims
Priority Applications (10)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CN201680044566.1A CN107849665B (zh) | 2015-07-29 | 2016-07-29 | FeCo合金、FeSi合金或Fe片材或带材以及其生产方法,由所述片材或带材生产的变压器磁芯及包括其的变压器 |
BR112018001734-5A BR112018001734B1 (pt) | 2015-07-29 | 2016-07-29 | Chapa ou faixa de liga ferrosa laminada a frio e recozida, método de fabricação de uma faixa ou chapa de liga ferrosa, núcleo magnético de transformador e transformador |
MX2018000925A MX2018000925A (es) | 2015-07-29 | 2016-07-29 | Lamina o tira de aleacion de hierro-cobalto, de aleacion de hierro-silicio o de hierro y su metodo de produccion, nucleo magnetico de transformador producido a partir de la lamina o tira, y transformador que comprende el nucleo. |
JP2018504237A JP7181083B2 (ja) | 2015-07-29 | 2016-07-29 | FeCo合金、FeSi合金またはFeシートもしくはストリップおよびその製造方法、前記シートまたはストリップから製造された磁気変圧器コア、ならびにそれを備える変圧器 |
CA2992271A CA2992271C (fr) | 2015-07-29 | 2016-07-29 | Tole ou bande en alliage feco ou fesi ou en fe et son procede de fabrication, noyau magnetique de transformateur realise a partir d'elle et transformateur le comportant |
US15/748,577 US11767583B2 (en) | 2015-07-29 | 2016-07-29 | FeCo alloy, FeSi alloy or Fe sheet or strip and production method thereof, magnetic transformer core produced from said sheet or strip, and transformer comprising same |
KR1020187004717A KR102608662B1 (ko) | 2015-07-29 | 2016-07-29 | FeCo 합금, FeSi 합금 또는 Fe 시트 또는 스트립, 및 이의 제조 방법, 시트 또는 스트립으로부터 제조된 자기 변압기 코어 및 이를 포함하는 변압기 |
RU2018102986A RU2724810C2 (ru) | 2015-07-29 | 2016-07-29 | ЛИСТ ИЛИ ПОЛОСА FeCo СПЛАВА, FeSi СПЛАВА ИЛИ Fe, СПОСОБ ИХ ИЗГОТОВЛЕНИЯ, МАГНИТНЫЙ СЕРДЕЧНИК ТРАНСФОРМАТОРА, ИЗГОТОВЛЕННЫЙ ИЗ УКАЗАННОГО ЛИСТА ИЛИ ПОЛОСЫ, И ТРАНСФОРМАТОР, ВКЛЮЧАЮЩИЙ ТАКОЙ СЕРДЕЧНИК |
EP16745720.9A EP3329027B1 (fr) | 2015-07-29 | 2016-07-29 | Tôle ou bande en alliage feco ou fesi ou en fe et son procédé de fabrication, noyau magnétique de transformateur réalisé à partir d'elle et transformateur le comportant |
ES16745720T ES2886036T3 (es) | 2015-07-29 | 2016-07-29 | Lámina o tira de aleación de FeCo o FeSi o de hierro y su procedimiento de fabricación, núcleo magnético de transformador producido a partir la misma y transformador que lo comprende |
Applications Claiming Priority (2)
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PCT/EP2015/067443 WO2017016604A1 (fr) | 2015-07-29 | 2015-07-29 | Tôle ou bande en alliage feco ou fesi ou en fe et son procédé de fabrication, noyau magnétique de transformateur réalisé à partir d'elle et transformateur le comportant |
EPPCT/EP2015/067443 | 2015-07-29 |
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WO2017017256A1 true WO2017017256A1 (fr) | 2017-02-02 |
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PCT/EP2015/067443 WO2017016604A1 (fr) | 2015-07-29 | 2015-07-29 | Tôle ou bande en alliage feco ou fesi ou en fe et son procédé de fabrication, noyau magnétique de transformateur réalisé à partir d'elle et transformateur le comportant |
PCT/EP2016/068172 WO2017017256A1 (fr) | 2015-07-29 | 2016-07-29 | Tôle ou bande en alliage feco ou fesi ou en fe et son procédé de fabrication, noyau magnétique de transformateur réalisé à partir d'elle et transformateur le comportant |
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PCT/EP2015/067443 WO2017016604A1 (fr) | 2015-07-29 | 2015-07-29 | Tôle ou bande en alliage feco ou fesi ou en fe et son procédé de fabrication, noyau magnétique de transformateur réalisé à partir d'elle et transformateur le comportant |
Country Status (11)
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US (1) | US11767583B2 (fr) |
EP (1) | EP3329027B1 (fr) |
JP (1) | JP7181083B2 (fr) |
KR (1) | KR102608662B1 (fr) |
CN (1) | CN107849665B (fr) |
BR (1) | BR112018001734B1 (fr) |
CA (1) | CA2992271C (fr) |
ES (1) | ES2886036T3 (fr) |
MX (1) | MX2018000925A (fr) |
RU (1) | RU2724810C2 (fr) |
WO (2) | WO2017016604A1 (fr) |
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WO2019127867A1 (fr) * | 2017-12-28 | 2019-07-04 | 青岛云路先进材料技术股份有限公司 | Alliage nanocristallin à base de fer-cobalt et son procédé de fabrication |
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WO2019127867A1 (fr) * | 2017-12-28 | 2019-07-04 | 青岛云路先进材料技术股份有限公司 | Alliage nanocristallin à base de fer-cobalt et son procédé de fabrication |
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Publication number | Publication date |
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RU2018102986A (ru) | 2019-07-29 |
KR20180035833A (ko) | 2018-04-06 |
CN107849665B (zh) | 2020-06-02 |
CA2992271C (fr) | 2023-07-11 |
BR112018001734B1 (pt) | 2022-03-03 |
KR102608662B1 (ko) | 2023-12-04 |
EP3329027A1 (fr) | 2018-06-06 |
CN107849665A (zh) | 2018-03-27 |
CA2992271A1 (fr) | 2017-02-02 |
BR112018001734A2 (pt) | 2018-09-18 |
EP3329027B1 (fr) | 2021-08-11 |
US20180223401A1 (en) | 2018-08-09 |
WO2017016604A1 (fr) | 2017-02-02 |
JP2018529021A (ja) | 2018-10-04 |
RU2018102986A3 (fr) | 2020-01-20 |
RU2724810C2 (ru) | 2020-06-25 |
US11767583B2 (en) | 2023-09-26 |
JP7181083B2 (ja) | 2022-11-30 |
ES2886036T3 (es) | 2021-12-16 |
MX2018000925A (es) | 2018-05-30 |
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