EP3329027B1 - 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 PDF

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EP3329027B1
EP3329027B1 EP16745720.9A EP16745720A EP3329027B1 EP 3329027 B1 EP3329027 B1 EP 3329027B1 EP 16745720 A EP16745720 A EP 16745720A EP 3329027 B1 EP3329027 B1 EP 3329027B1
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traces
annealing
alloy
magnetostriction
strip
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French (fr)
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EP3329027A1 (fr
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Rémy BATONNET
Thierry Waeckerle
Thierry BAUDIN
Anne-Laure HELBERT
Olivier Hubert
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Aperam SA
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Aperam SA
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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
    • 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
    • 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
    • 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
    • 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
    • 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
    • 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
    • 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
    • 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
    • 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
    • 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
    • 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
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    • 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
    • C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
    • C—CHEMISTRY; METALLURGY
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    • 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
    • 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
    • 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
    • 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
    • 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
    • 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
    • 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
    • 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
    • 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
    • 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
    • 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
    • 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
    • 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
    • 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
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt

Definitions

  • the present invention relates to alloys of iron and cobalt, particularly those which have a content of the order of 10 to 35% Co, and also pure iron and alloys of iron and silicon which have a content of around 3% of Si. These materials are used to constitute magnetic parts such as transformer cores, in particular intended for aeronautics.
  • Low frequency transformers ( ⁇ 1 kHz) on board aircraft consist mainly of a magnetic core in soft magnetic alloy, laminated, stacked or wound according to construction constraints, and primary and secondary windings in copper.
  • the primary supply currents are variable over time, periodic but not necessarily of purely sinusoidal form, which does not fundamentally change the needs of the transformer.
  • the transformer must operate on a power supply network with a roughly sinusoidal frequency, with an amplitude of the output rms voltage which may vary transiently up to 60% from one moment to another, and in particular when switching on. when the transformer is energized or when an electromagnetic actuator is suddenly engaged. This has the consequence, and by construction, a current inrush at the primary of the transformer through the nonlinear magnetization curve of the core. magnetic.
  • the transformer elements (insulators and electronic components) must be able to withstand strong variations in this inrush current without damage, which is called the “inrush effect”.
  • In 2.Bt + Br - Bsat, where Bt is the nominal working induction of the magnetic core of the transformer, Bsat is the nucleus saturation induction and Br is its remanent induction
  • the noise emitted by the transformer due to electromagnetic forces and magnetostriction must be low enough to comply with current standards or to meet the requirements of users and personnel stationed near the transformer. More and more, pilots and co-pilots of aircraft want to be able to communicate no longer using headsets but by direct means.
  • the thermal efficiency of the transformer is also very important to consider, since it fixes both its internal operating temperature and the heat flows that must be removed, for example by means of an oil bath surrounding the windings and the cylinder head, associated with oil pumps sized accordingly.
  • the sources of thermal power are mainly the losses by the Joule effect resulting from the primary and secondary windings, and the magnetic losses resulting from the variations of the magnetic flux over time and in the magnetic material.
  • the volumetric 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 the cost of materials, design, manufacture and maintenance, and optimization of the electrical power density (mass or volume). ) of the device by taking into account the thermal regime of the transformer.
  • the transformer comprises a wound magnetic circuit when the power supply is single phase.
  • the structure of the transformer core is made by two toroidal cores of the previous type placed side by side, and surrounded by a third toroid wound and forming an “eight” around the two previous toric cores.
  • This form of circuit imposes in practice a small thickness of the magnetic sheet (typically 0.1mm). In fact, this technology is used only when the supply frequency forces, given the induced currents, to use bands of this thickness, that is to say typically for frequencies of a few hundred Hz.
  • a stacked magnetic circuit is used, whatever the thicknesses of the magnetic sheets envisaged. This technology is therefore valid for any frequency lower than a few kHz. However, special care must be taken in deburring, juxtaposition, or even electrical insulation of the sheets, in order to both reduce parasitic air gaps (and therefore optimize the apparent power) and limit the currents induced between sheets.
  • 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 sheets with less than 48% Co for on-board medium-frequency transformers it has therefore been known for a long time that the chances of success necessarily depend on an acute texture characterized by the fact that in each grain, an axis ⁇ 100> is very close to the direction of rolling.
  • the so-called “Goss” texture ⁇ 110 ⁇ ⁇ 001> obtained in Fe-Si by secondary recrystallization is a case in point.
  • the sheet should not contain cobalt.
  • an Fe-48% Co-2% V alloy optimized for a transformer has a B 800 of approximately 2.15 T ⁇ 0.05 T, which allows an increase in magnetic flux to 800 A / m for a same cylinder head section of about 13% ⁇ 3%, at 2500 A / m about 15%, at 5000 A / m about 16%.
  • JP 2001181803 A discloses for a sheet a maximum difference between the magnetostriction deformation amplitudes of less than 25 ppm for a recrystallized microstructure.
  • nanocrystallines pose a major problem in the case of an “on-board transformer” solution: their thickness is around 20 ⁇ m and they are wound in a torus in the flexible amorphous state around a rigid support, so that the shape of the torus either retained throughout the heat treatment resulting in nanocrystallization. And this support cannot 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 using the technology of the previously wound circuit. described. Only resins for impregnating the wound toroid can maintain it in the same shape in the absence of the support which is removed after polymerization of the resin.
  • nanocrystallines have a magnetization at saturation Js which is markedly lower than other soft materials (Iron, FeSi3%, Fe-Ni50%, FeCo, amorphous iron base), which necessitates significantly increasing the transformer weight, since the increase of section of the magnetic core will have to compensate for the drop in work induction imposed by Js. Also the “nanocrystalline” solution would only be used as a last resort, if the maximum noise level required is low and if another lighter and quieter solution does not appear.
  • the aim of the invention is to provide a material for forming transformer cores exhibiting only a very low magnetostriction, including when they are subjected to a strong work induction which would make it possible not to use a magnetic core mass. too high, therefore to provide transformers having a high specific (or volume) power density. In this way, the transformers that they would make it possible to produce could advantageously be used in environments such as an aircraft cockpit where low magnetostriction noise would be advantageous for the comfort of the users.
  • the invention relates to a sheet or strip of cold-rolled and annealed ferrous alloy, characterized by the claims.
  • 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 well-defined thermal and mechanical treatments have been carried out, the heat treatments all being in the ferritic range of the alloy.
  • the use of pure or very low alloyed iron is also envisaged.
  • this magnetostriction presents a remarkable isotropy, even for these high fields. It remains, in fact, almost zero both in 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, up to 'at an ambient magnetic field of at least 1 T. Beyond 1 T, the difference between the magnetostrictions observed in these three directions remains remarkably small up to a field of at least 1.8 T, or even 2 T.
  • transformers are obtained having a low magnetostriction noise in all directions of the sheets constituting their cores, therefore a particularly low overall magnetostriction noise, making them suitable for constituting, in particular, on-board transformers for aircraft which can be placed in the substation. piloting without interfering with direct conversations between its occupants.
  • the metals and alloys to which the invention applies are iron and ferrous alloys with a ferritic structure, containing, in addition to iron and the impurities and residual elements resulting from their production, the following chemical elements. All percentages are weight percentages.
  • This pollution can be due, for example, to the wear of refractory materials, containing in particular magnesia and / or alumina and / or silica, which coat the receptacles (melting furnace, ladle, etc. .) where the liquid metal stays.
  • the contact of the liquid metal with the atmosphere can also lead to the absorption of nitrogen, and also of oxygen which can combine 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 precision of the analysis apparatus for the detection and measurement of the content of the element in question is also to be taken into account.
  • the alloys making up the sheets or strips according to the invention contain C at a content between traces resulting from the production, without C having been added to the raw materials, and 0.2%, preferably between traces and 0.05%, better between traces and 0.015%.
  • the FeCo27 and FeSi3 type alloys to which certain possible variants of the invention fall typically have C contents of 0.005 to 0.15%, which result much more from the conditions of deoxidation of the liquid metal (in particular from the formation of CO within liquid metal during vacuum passages) than a deliberate desire to find these C contents in the final product for reasons related to the mechanical or magnetic properties of the alloy.
  • the Co can be present in limited quantity, only in the state of traces resulting from the production, therefore not to be added voluntarily, but if Co ⁇ 35% it is necessary to Si + 0.6% Al ⁇ 4.5 - 0 , 1% Co and also Si ⁇ 3.5%. Thus, for example, in the absence of cobalt, a content of traces at 3.5% of Si, and of traces at 1% of Al is required to remain within the scope of the invention.
  • the invention is most typically applicable to Fe-Co alloys of a conventional type containing approximately 27% Co and to Fe-Si alloys containing approximately 3% Si.
  • an Si content + 0.6% Al ⁇ 4.5 - 0.1% Co can be accepted if the rolling operations are carried out not strictly cold, but "lukewarm", that is to say at a temperature ranging up to 350 ° C., this rolling temperature preferably being obtained by steaming, that is to say heating in a static chamber at a low temperature.
  • This lukewarm rolling (which it is agreed that it is fully comparable to cold rolling in the context of the invention; the term "cold rolling”, when no further details are given on the temperature of its execution, should be understood, in the present text, to also include lukewarm rolling carried out up to 350 ° C. It is employed as opposed to the "hot” rolling mills well known to metallurgists, which are carried out at temperatures considerably higher.
  • the reheating temperature is also to be determined as a function of the cooling that the strip or sheet will undergo, predictably, during its transfer between the reheating installation and the rolling mill.
  • the reheating temperature must be sufficient so that the actual temperature of the strip or sheet at the time of warm rolling is that targeted, but it must not exceed 400 ° C to avoid significant oxidation of the material during reheating, and even also during transfer to the rolling mill.
  • the Si content is also governed by the desire to permanently retain a ferritic structure during the manufacture of the material, which proves to be important for obtaining the low and isotropic magnetostriction on which the invention is based.
  • the Cr content can range from traces to 10%.
  • An addition of Cr only slightly modifies the Fe stacking fault energy, and therefore does not greatly modify the texture filiations during the treatments carried out according to the invention. It lowers the magnetization to saturation J sat , and it is undesirable to add an amount exceeding 10% for this reason.
  • just like Si it appreciably increases the electrical resistivity, therefore advantageously decreases the magnetic losses. Cooling of the transformer allows, however, to tolerate more magnetic losses, and a low Cr content, even in the state of traces, may be acceptable in this case.
  • 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 is generally not desired.
  • 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. Above all, it is a gammagenic element, which therefore reduces the temperature range allowing ferritic annealing.
  • the Al content is between traces and 3%, preferably between traces and 1%. Al reduces saturation magnetization and is much less effective than Si or Cr at increasing electrical resistivity. But Al can be used to extend the cold-rollability range of high alloy FeCo grades when reaching the limits of silicon additions, as previously discussed.
  • the S content is between traces and 0.005%. Indeed, S tends to form sulphides with manganese, and oxysulphides with Ca and Mg, which greatly degrades the magnetic performance and in particular the magnetic losses.
  • the P content is between traces and 0.007%.
  • P can form phosphides of metallic elements which are harmful to the magnetic properties and to the 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 and therefore degrades the power density and the electrical efficiency of the transformer. Its addition is therefore not necessary.
  • the Cu content is between traces and 0.5%, preferably less than 0.05%.
  • Cu is very poorly miscible with Fe, Fe-Si or Fe-Co, and therefore forms copper-rich, non-magnetic phases, significantly degrading the magnetic performance of the material as well as greatly hindering the development of its microstructure.
  • Nb and Zr are each between traces and 0.1%, preferably less than 0.01% since Nb and Zr are well known to be potent inhibitors of grain growth, and therefore will interfere strongly and unfavorably. with the metallurgical mechanism of texture filiation which one suspects 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 (increase in 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 Ta content is between traces and 0.01% because it can greatly hinder 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 Ti nitrides.
  • the O content is between traces and 0.01% to prevent oxidized inclusions formed in too large quantities from having the same harmful effects as nitrides.
  • An ingot or a continuously cast semi-finished product is prepared, having the composition described above.
  • all production and casting methods making it possible to obtain this composition can be used.
  • processes such as arc melting processes under slag, induction melting under slag or under vacuum (VIM for Vacuum Induction Melting) are recommended. They are preferably followed by remelting processes to obtain a secondary ingot.
  • ESR Electrode Remelting
  • VAR Vacuum Arc Remelting
  • the ingot optionally shaped beforehand, or the continuous casting semi-finished product is hot-rolled, in the usual way, until a sheet or strip with a thickness of 2 to 5 mm is obtained, preferably between 2 and 3.5 mm, for example of a thickness of the order of 2.5 mm.
  • This hot rolling therefore constitutes the last step (or the only one) in the hot forming of the process according to the invention.
  • an annealing is carried out, static or in scrolling, of said sheet or strip, in the ferritic range, therefore at a temperature between 650, preferably 700 ° C, and a temperature which guarantees that no will not leave the purely ferritic range 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.
  • This annealing should 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 oxidizing gaseous 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 maximum -40 ° C, optimally at maximum -60 ° C.
  • a natural or forced cooling of the sheet or strip is carried out, under conditions which prevent excessive weakening of the strip.
  • this cooling rate must be at least 1000 ° C / h.
  • a first cold rolling at a reduction rate of 50 to 80%, preferably 60 to 75%, and at a temperature between ambient temperature (eg 20 ° C) and 350 ° C.
  • the upper limit of 350 ° C. corresponds to the case where, as we have seen, a “warm” rolling is carried out, the reheating being preferably carried out by a baking, for the alloys relatively rich in Si.
  • the temperature of cold rolling is between room temperature and 100 ° C.
  • Too low a reduction rate (less than 50%) during at least one of the cold or “warm” rolling operations does not make it possible, as will be seen, to obtain the low and isotropic magnetostriction sought. Too high a reduction rate (greater than 80%) would be liable to modify the texture of the material too strongly, so that the magnetostriction will be degraded.
  • An annealing is then carried out, static or by scrolling, in the ferritic range, at a bearing temperature of between 650 and 930 ° C, preferably between 800 and 900 ° C, and for 1 min to 24 hours, preferably 2 min at 1 h, in a dry hydrogenated atmosphere (partial or total) as defined above, for the reasons seen in connection with the optional annealing following the hot rolling, followed by cooling to perform 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 located in the same ranges as those already described for the first cold rolling.
  • a final recrystallization annealing is carried out under a preferably hydrogenated atmosphere (partial or total) like the atmospheres of the previous anneals.
  • 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 no longer necessarily necessary for this last annealing, because at this stage the metal may have already reached its final dimensions, in particular in thickness, or even also with regard to its perimeter, in particular if a cutting has already had place to give the pieces of the future stack their final shapes and dimensions. In this case, even if an absence of hydrogen led to an embrittlement of the metal during this recrystallization annealing, this would be without consequences if it only remained to stack the pieces to form the core.
  • Static annealing whose temperature rise rate is lower than for step annealing and which lasts longer, has the advantage of increasing the ferritic grain better than step annealing, which is favorable to the process. obtaining low magnetic losses.
  • This final annealing ends with relatively slow cooling such as natural cooling in air, or cooling under a hood or other device limiting heat loss by radiation.
  • relatively slow cooling such as natural cooling in air, or cooling under a hood or other device limiting heat loss by radiation.
  • a faster cooling would be likely to introduce internal stresses by establishing a thermal gradient in the material, which would degrade the magnetic losses.
  • Coolings following annealing other than final annealing need not be particularly advantageous at low speed. Too slow cooling would even risk reducing the laminability of the material in the following step.
  • This relatively slow cooling is coupled with a rate of temperature rise for the purpose of annealing which is itself less than or equal to 2000 ° C./h, better still less than or equal to 600 ° C./h.
  • final annealing are among the parameters on which one can play 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 heat and thermomechanical treatments during cold or warm rolling and annealing.
  • the inventors obtain on the final product no more than 30% of Goss texture component or of ⁇ 111 ⁇ ⁇ 110> texture component (these are the orientations which are found to be most present in the sheets and strips according to the invention. ) and, in general, not more than 30% of any marked ⁇ hkl ⁇ ⁇ uvw> texture component, that is to say a component characterized by the fact that at most 30% volume fraction of the grains of the material have orientation ⁇ hkl ⁇ ⁇ uvw> less than 15 ° in disorientation of a specific orientation ⁇ h 0 k 0 l 0 ⁇ ⁇ u 0 v 0 w 0 > ..
  • an additional oxidation annealing of the material can be added, at a temperature between 400 and 700 ° C, preferably between 400 and 550 ° C, allowing strong but superficial oxidation of the material on at least one of its faces, without risking intergranular oxidation since this is known to occur at higher temperatures.
  • This oxidation layer has a thickness of 0.5 to 10 ⁇ m and guarantees electrical insulation between the stacked parts of the transformer magnetic core, which makes it possible to substantially reduce the induced currents and therefore the magnetic losses of the transformer.
  • a manufacturing process has been described comprising two stages of cold rolling and two or three anneals. But it would still be in accordance with the invention to carry out more cold rolling steps similar to those which have been described, which can be separated by intermediate anneals similar to the first of the compulsory anneals which have been described.
  • each of the cold rolling 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 end result is a cold rolled and 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 magnetic losses, which has the particularity of exhibiting very low magnetostrictions ⁇ in the three directions DL (rolling direction), DT (transverse direction) and 45 ° (middle direction between DL and DT), measured both parallel and perpendicular to the direction of the applied field, and above all a very small difference between the highest and lowest magnetostrictions of those measured, and this for different inductions from 1.2 T to 1.8 T.
  • Table 1 Compositions of the alloys of the tests Element (%) A Invention B Invention C Invention D Invention E Invention F Invention G Invention H Invention I invention J Reference K Reference L Reference M Invention N Invention VS 0.010 0.009 0.007 0.023 0.012 0.013 0.011 0.012 0.010 0.008 0.009 0.009 0.012 0.015 Mn 0.261 0.256 0.195 0.234 0.248 0.421 0.532 0.810 0.167 0.208 0.520 0.289 0.368 ⁇ 0.010 Yes 0.142 0.153 0.330 0.720 0.031 2,730 0.070 0.013 3.020 0.023 3.07 1.53 0.640 0.083 S 0.0023 0.0042 0.0033 0.0021 0.0048 0.0008 0.0006 0.0028 0.0005 0.0015 0.0007 0.0044 0.0008 ⁇ 0.0005 P 0.0025 0.0055 0.0031 0.0029 0.0029 0.0032 0.0047 0.0037 0.0053 0.0031 0.0043 0.00
  • the alloy was developed in a vacuum induction furnace, then it was cast in the form of an ingot of 30 to 50 kg, frustoconical, with a diameter ranging from 12 cm to 15 cm, with a height of 20 to 30 cm, which it was then rolled on a coarse rolling mill to a thickness of 80 mm, then hot rolled at a temperature of about 1000 ° C to give it a thickness of 2.5 mm.
  • the static annealing concluding the preparation were, for all the samples, preceded by a rise in temperature at a rate of 300 ° C / h and followed by cooling at a rate of the order of 200 ° C / h, carried out simply by leaving the samples in the annealing oven.
  • the temperature rise rates before the final annealing and cooling after the final annealing were therefore relatively moderate, which in all cases contributed to obtaining a relatively low-textured final product, as will be seen in the Table 2.
  • the differences in magnetostriction and its isotropy observed for the samples according to the invention and the reference samples will therefore be attributable to other factors, and in particular to the fact that, for the reference samples, there was a passage in the austenitic domain during annealing.
  • the reference samples 1 and 2 underwent cold rolling directly after the hot treatments, then annealing at high temperature (1100 ° C) in the austenitic domain, then a second cold rolling, then a final annealing at 900 ° C (test 1) or 700 ° C (test 2) in the ferritic range.
  • the samples according to the invention 3 to 9 began, after the hot treatments, by undergoing annealing at 900 ° C, then a first cold rolling, then a second annealing at 900 ° C, then a second cold rolling, then a final annealing at a variable temperature according to the tests, from 660 to 900 ° C. All the annealing operations therefore took place in the ferritic field, in accordance with the invention, and were three in number, against two for the first two reference samples 1 and 2. All the cold rolling were carried out with a rate 70% reduction.
  • the reference sample 10 first underwent a ferritic annealing at 900 ° C just like the samples according to the invention and unlike the other two reference samples, then a first cold rolling, then an intermediate annealing at 900 ° C. , therefore in the ferritic field, then a second cold rolling, then a final annealing at a temperature of 1100 ° C, therefore in the austenitic field. It thus underwent a treatment comparable to that of samples 3 to 9 according to the invention, apart from the fact that the final annealing took place in the austenitic domain. All of its cold rolling was carried out at 70% reduction rate, as for the samples according to the invention.
  • Reference sample 11 after the hot treatments, underwent annealing at 900 ° C, then a first cold rolling at 80% instead of 70% like all samples 3 to 10 (which remains in accordance with l invention), then a second annealing at 900 ° C, then a second cold rolling at 40%, therefore in a manner not in accordance with the invention, instead of 70% like all samples 3 to 10, then a final annealing at a temperature of 700 ° C, therefore in the ferritic range.
  • the reference sample 12 is quite similar to the sample 10, by virtue of its passage through the austenitic domain, which however takes place at a different stage of the treatment. It first underwent a 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 range at 1100 ° C. , therefore in a manner not in accordance with the invention, then a second cold rolling, then a final annealing at a temperature of 700 ° C., therefore in the ferritic range. It thus underwent a treatment comparable to that of samples 3 to 9 according to the invention, apart from the fact that the intermediate annealing took place in the austenitic range. All of its cold rolling was carried out at 70% reduction rate, as for the samples according to the invention.
  • Table 2 Texture, grain diameter and recrystallization rate of the samples tested according to their processing conditions Test Cold rolling reduction rate Final annealing temperature (° C) Alloy % Goss texture % texture ⁇ 111 ⁇ ⁇ 110> Grain diameter ( ⁇ m) Recrystallized fraction 1 Reference 84/50% 900 (but annealed 1 to 1100 ° C) TO 10 10 150 100% 2 Reference 84/50% 700 (but annealed 1 to 1100 ° C) TO 7 10 15 100% 3 Invention 70/70% 660 B 10 10 16 90% 4 Invention 70/70% 680 B 9 11 18 95% 5 Invention 70/70% 700 B 10 12 20 100% 6 Invention 70/70% 720 B 10 11 23 100% 7 Invention 70/70% 750 B 12 10 26 100% 8 Invention 70/70% 810 B 13 11 44 100% 9 Invention 70/70% 900 B 12 15 95 100% 10 Reference 70/70% 1100 (annealed 1 and 2 at 900 ° C) B 4 7 285 100% 11 Reference 80/40% 700 B 17 8 22 100% 12 Reference 70
  • the different ranges of metallurgical treatments applied 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 ⁇ m: more precisely from 16 to 95 ⁇ m for the tests according to the invention, ie when all the annealing operations are carried out in the ferritic range; from 15 to 285 ⁇ m for the references, ie when at least one step of the process takes place outside the ferritic range. It can thus be seen that the grain size range is similar and has no connection with the low magnetostrictions obtained.
  • test 2 the final annealing of which was carried out at 700 ° C, has leads to a grain size markedly smaller than that of the reference tests 1 and 10 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 around 700 ° C.
  • the metallurgical ranges of the tests according to the invention provide a grain size (between 16 and 95 ⁇ m depending on the tests) relatively close to that of the reference tests, and in any case fairly consistent with what could be expected. wait a priori, in particular in view of the conditions of the final annealing.
  • the magnetostrictions (measured in ppm) on the different samples 1 to 3, 5, 7 to 12 cut, in different directions DL, DT and at 45 ° from DL and DT as indicated on the figure 1 were observed, measured either parallel to the large side of the sample (therefore also parallel to the direction of the applied magnetic field and of the magnetic flux of the generated induction B) and noted “// H", i.e. perpendicular to the large side of the sample (therefore perpendicular to the direction of the applied magnetic field and of the magnetic flux of the generated B induction) and noted " ⁇ H".
  • Benchmark Test 11 shows that the target low and isotropic magnetostriction is also not obtained when one of the cold rollings is performed at a low reduction rate, even though all annealing takes place in the field. ferritic.
  • Reference run 12 shows that the target low and isotropic magnetostriction is also not obtained when the second of the three anneals is carried out in the austenitic range.
  • Reference Examples 1 and 2 had austenitic annealing performed at the start of processing, after the first cold rolling, and Reference Example 10 had austenitic annealing performed at the very end of processing. Example 12 therefore completes the demonstration of the harmfulness of austenitic annealing whatever its position in the treatment.
  • the figure 2 translates the magnetostriction results observed during the reference test 1. It can be seen that even for weak inductions of the order, in absolute value, of 0.5T, the magnetostriction according to DT begins to become significant and increases very quickly with induction. For DL and for the 45 ° steering of DT and DL, it is from around 1 T that the magnetostriction begins to increase noticeably and rapidly. This leads to significant magnetostriction deformations which can reach several tens of ppm in certain directions at inductions of the order of 2 T, and to a strong anisotropy of these deformations, all this going in the direction of the creation of a noise of magnetostriction too intense for the privileged applications of the invention envisaged.
  • the figure 3 reflects the magnetostriction results observed during the reference test 2. It is observed there that, compared to test 1, the isotropy of the magnetostriction is slightly improved, and certain extreme values of the magnetostriction are a little lower . 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 to the privileged applications of the invention either. The significantly smaller grain size in the test 2 sample than in the test 1 sample therefore did not very fundamentally improve the magnetostriction results.
  • the figure 4 reflects 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 high fields.
  • At 2 or -2 T we have a magnetostriction which does not reach 15 ppm or -10 ppm, and this for all directions considered.
  • the figure 5 reflects the magnetostriction results observed during test 7 according to the invention.
  • the magnetostriction can be less than 5 ppm and never exceeds 10 ppm.
  • the figure 6 reflects the magnetostriction results observed during test 8 according to the invention, which had a final annealing temperature of 810 ° C.
  • the figures 7 to 9 compare the magnetostriction measurements recorded for tests 5 and 9 according to the invention.
  • the figure 7 shows the tests carried out according to the DT direction
  • the figure 8 shows the tests carried out in the 45 ° direction
  • the figure 9 shows the tests carried out according to the DT direction.
  • the results are very comparable and excellent for the two tests according to the DL and DT directions up to inductions of ⁇ 1.8 T.
  • the magnetostriction begins to no longer be completely negligible from 1 , 8 T approximately in the case of test 5, while in test 9 it remains very low even beyond 2 T.
  • a final annealing temperature of 900 ° C therefore gives results of magnetostriction better than final annealing at 700 ° C.
  • the magnetostriction at 1.8T does not exceed ⁇ 5 ppm in the three measurement directions, which is very significantly better than for the reference tests, both for the absolute value of the magnetostriction and for its isotropy.
  • test 9 results are particularly remarkable at strong inductions of 1.8 T or even slightly beyond, both on the weakness of the magnetostriction and on its isotropy.
  • the figure 10 shows the results of the reference test 10 in which the final annealing was carried out at 1100 ° C, therefore in the austenitic range, while the two previous anneals 1 and 2, carried out at 900 ° C. like all anneals 1 and 2 of the tests according to the invention, had been carried out in the ferritic field.
  • Test 11 in which the second cold rolling was carried out with a reduction rate of only 40%, shows, according to the figure 11 , a conventional parabolic and low isotropic behavior of the magnetostriction as a function of the induction, therefore a behavior outside the invention, with for example a magnetostriction according to DL of more than 35ppm at 1.5T, of nearly 60ppm at 1, 8T. It can be concluded that the texture filiation, modulated by the cold rolling reduction rates, is effectively well controlled by the texture transformations during cold rolling, which restricts the invention to certain ranges of reduction rates. .
  • the figure 12 shows the results of the reference test 12 in which the intermediate annealing was carried out at 1100 ° C, therefore in the austenitic range, while the two anneals 1 and 3 were carried out at 900 ° C like all the anneals 1 and 3 tests according to the invention, therefore in the ferritic field.
  • the magnetic losses of the samples produced according to the invention and having grains of reduced size 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 samples according to the invention that are 100% recrystallized and produced with a final annealing at 720 ° C and more exhibit magnetic losses which are still significantly improved compared to to the reference samples, including that of test 1 which has a large grain size and a 100% recrystallized structure. This advantage over magnetic losses is, for the moment, not clearly explained by the inventors.
  • test 9 of the invention which exhibits the lowest magnetic losses.
  • the results are all the more favorable in terms of magnetic losses as the temperature of the final ferritic annealing is higher, the best results being obtained for the sample of test 9 which was annealed at 900 ° C. .
  • ferritic annealing temperatures between 800 and 900 ° C show a weak to very weakly marked deformation anisotropy and Max ⁇ amplitude deviations of magnetostriction not exceeding, in all cases, not 6 ppm at 1.5T , 15 ppm at 1.8T, therefore significantly better than those of the samples of the reference tests.
  • the invention is defined by saying, in particular, that all annealing 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 l
  • the alloy is indeed in the purely ferritic range, without a transformation of at least part of the ferrite into austenite occurring. We saw above what this maximum temperature was as a function of the Si, Co and C contents of the alloy.
  • the strips obtained according to the invention can be used to constitute transformer cores which are both of the “cut-stacked” type and of the “wound” type as defined above. In the latter case, to carry out the winding, it is necessary to use very thin strips of the order of 0.1 to 0.05 mm thick, for example.
  • annealing carried out before the first cold rolling is preferably carried out within the framework of the invention.
  • this annealing is not essential, in particular in the case where the hot-rolled strip has remained in the coiled state for a long time during its natural cooling.
  • the winding temperature often being of the order of 850-900 ° C, the duration of this stay can be quite sufficient to obtain very comparable effects on the microstructure of the strip at this stage. to those which would be provided by a true annealing in the ferritic range carried out under the conditions which have been said for the optional annealing before the first cold rolling.
  • Table 5 recalls the results obtained during tests 1 and 9 previously described on the isotropy of magnetostriction and the magnetic losses at 1.5 T, 400 Hz, and it adds information on the suitability for cold rolling or lukewarm samples before being applied to a treatment according to the method of the invention, and the saturation magnetization Js of the final product. These results are also compared with those obtained during tests numbered 13 to 24, in which alloys of conforming compositions (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.
  • sample A (test 1) underwent, without prior annealing, an LAF 1 at a reduction rate of 84%, then an R1 annealing at 1100 ° C for 3 min, then an LAF 2 at a reduction rate of 50%, then static R2 annealing at 900 ° C. for 1 h.
  • Samples B to H underwent R1 annealing at 900 ° C for 8 min, then LAF 1 at a reduction rate of 70%, then R2 annealing at 900 ° C for 8 min. min at 900 ° C, then an LAF 2 at a reduction rate of 70%, then a static R3 annealing at different temperatures and times, noted in Table 5.
  • Sample I (test 19) underwent R1 annealing at 900 ° C for 8 min, then lukewarm rolling 1 at 150 ° C with a reduction rate of 70%, then R2 annealing at 900 ° C ° C for 8 min, then lukewarm rolling 2 at 150 ° C with a reduction rate of 70% and static R3 annealing at 850 ° C for 30 min.
  • Sample J (test 20) underwent static R1 annealing at 935 ° C for 1 h, then an LAF 1 at 70% reduction rate, then R2 annealing at 900 ° C for 8 min, then a LAF 2 at 70% reduction rate, then static R3 annealing at 880 ° C for 1 h.
  • Example 13 also exhibits relatively significant Si, Cr, Al, Ca, Ta contents.
  • Example 14 also exhibits significant Si, V and Ti contents. But all these contents remain within the limits defined for the invention.
  • test 23 which concerns an FeCo alloy having a Co content of nearly 39%, therefore significantly higher than 27% but remaining within the limit of 40% at the maximum set. for the invention, and an Si content which is significant, but not so high as to compromise cold or warm rollability.
  • the loss magnetic fields and the saturation magnetization are of the same order of magnitude as for the other samples treated according to the invention.
  • test 24 it relates to an alloy containing 15% Co and devoid of significant contents of other alloying elements, in particular Cr. It also exhibits 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 test 24 this absence tending to increase the saturation magnetization, is compensated for by a slightly less presence of Co which, for its part, goes into the sense of a decrease in saturation magnetization.
  • the absence of Cr in test 24 goes in the direction of an increase in magnetic losses compared to test 13, but the lower Co content in test 24 goes in the direction of a reduction of these same magnetic losses. Therefore, the differences in the composition of the alloy between tests 13 and 24 tend to compensate for each other, from the point of view of the magnetic losses and Js.
  • Test 15 shows that a relatively low Co content (4.21%) is not inconsistent with obtaining the desired good magnetostriction isotropy, if the Si and Al contents are sufficiently low. .
  • the presence of 0.005% of Nb does not interfere with obtaining the desired results.
  • Test 16 relates to an Fe-Si-Al alloy with a very low Co content. In its case, the desired isotropic magnetostriction is also obtained, together with low magnetic losses.
  • Test 17 relates to an alloy which is practically 99% pure Fe, with relatively low presences of Mn, Ca, Mg.
  • 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, as Max ⁇ at 1.8 T remains ⁇ 25 ppm as required on the sheets or strips according to l '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 observed on the reference test 1.
  • Test 18 relates to an FeCo27 type alloy with a high Cr content (6%) and also containing Mn (0.81%) and a little Mo and B. The good isotropy of the magnetostriction is confirmed, and the magnetic losses are as low as for test 16 despite the presence of 7 ppm of B. The saturation magnetization remains of the order of that observed during the other tests, such as the contents of Cr, Mn and Mo is not so high that it deteriorates undesirably.
  • Test 19 relates to an Fe-Si alloy containing 3.5% Si and not containing Al, and shows that the operating conditions of the process according to the invention are also applicable with profit to this type of FeSi3 alloys to achieve the desired magnetostriction isotropy. In addition, this example exhibits particularly low magnetic losses.
  • Table 6 presents experimental results obtained by varying the treatment conditions, the composition of the alloy treated and the final thickness of the sample. The results of the previous tests 1 and 9 were taken over, and new tests 25 to 31 carried out on alloys having the compositions B (FeCo27), I (FeSi3) and C (FeCo18) explained in Table 5 were added.
  • the strips and sheets according to the invention make it possible to manufacture, in particular, after their cutting, transformer cores composed of sheets stacked or wound up, without requiring modifications to 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 a low magnetostriction noise compared to existing transformers of similar design and sizing. 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 transformer cores of higher mass, therefore intended for transformers of particularly high power, while retaining a magnetostriction noise remaining within acceptable limits.
  • the transformer cores according to the invention can consist entirely of sheets made from strips or sheets according to the invention, or only partially in cases where it is considered that their association with other materials would be technically or financially advantageous.

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EP16745720.9A 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 Active EP3329027B1 (fr)

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JP2018529021A (ja) 2018-10-04
US20180223401A1 (en) 2018-08-09
JP7181083B2 (ja) 2022-11-30
ES2886036T3 (es) 2021-12-16
BR112018001734B1 (pt) 2022-03-03
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RU2724810C2 (ru) 2020-06-25
EP3329027A1 (fr) 2018-06-06
RU2018102986A3 (ko) 2020-01-20
MX2018000925A (es) 2018-05-30
BR112018001734A2 (pt) 2018-09-18
WO2017017256A1 (fr) 2017-02-02
US11767583B2 (en) 2023-09-26
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