Classifications

• • 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
  • C21D6/00—Heat treatment of ferrous alloys
  • C21D6/007—Heat treatment of ferrous alloys containing Co
• • A—HUMAN NECESSITIES
  • A63—SPORTS; GAMES; AMUSEMENTS
  • A63B—APPARATUS FOR PHYSICAL TRAINING, GYMNASTICS, SWIMMING, CLIMBING, OR FENCING; BALL GAMES; TRAINING EQUIPMENT
  • A63B21/00—Exercising apparatus for developing or strengthening the muscles or joints of the body by working against a counterforce, with or without measuring devices
  • A63B21/40—Interfaces with the user related to strength training; Details thereof
  • A63B21/4001—Arrangements for attaching the exercising apparatus to the user's body, e.g. belts, shoes or gloves specially adapted therefor
  • A63B21/4017—Arrangements for attaching the exercising apparatus to the user's body, e.g. belts, shoes or gloves specially adapted therefor to the upper limbs
• • A—HUMAN NECESSITIES
  • A63—SPORTS; GAMES; AMUSEMENTS
  • A63B—APPARATUS FOR PHYSICAL TRAINING, GYMNASTICS, SWIMMING, CLIMBING, OR FENCING; BALL GAMES; TRAINING EQUIPMENT
  • A63B23/00—Exercising apparatus specially adapted for particular parts of the body
  • A63B23/035—Exercising apparatus specially adapted for particular parts of the body for limbs, i.e. upper or lower limbs, e.g. simultaneously
  • A63B23/12—Exercising apparatus specially adapted for particular parts of the body for limbs, i.e. upper or lower limbs, e.g. simultaneously for upper limbs or related muscles, e.g. chest, upper back or shoulder muscles
  • A63B23/14—Exercising apparatus specially adapted for particular parts of the body for limbs, i.e. upper or lower limbs, e.g. simultaneously for upper limbs or related muscles, e.g. chest, upper back or shoulder muscles for wrist joints
• • 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
  • 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
  • C21D8/1261—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 following hot rolling
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C19/00—Alloys based on nickel or cobalt
  • C22C19/07—Alloys based on nickel or cobalt based on cobalt
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C30/00—Alloys containing less than 50% by weight of each constituent
• • 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
  • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/10—Ferrous alloys, e.g. steel alloys containing 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
  • C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
  • C22C38/105—Ferrous alloys, e.g. steel alloys containing cobalt containing Co and Ni
• • 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
  • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
• • 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
  • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
• • 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
  • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
• • 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
  • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
• • 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
  • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
• • 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
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
  • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
  • C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
  • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
  • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
• • 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
  • H01F1/16—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
• • 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
• • A—HUMAN NECESSITIES
  • A63—SPORTS; GAMES; AMUSEMENTS
  • A63B—APPARATUS FOR PHYSICAL TRAINING, GYMNASTICS, SWIMMING, CLIMBING, OR FENCING; BALL GAMES; TRAINING EQUIPMENT
  • A63B2208/00—Characteristics or parameters related to the user or player
  • A63B2208/12—Characteristics or parameters related to the user or player specially adapted for children
• • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
  • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
  • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
  • Y10T29/00—Metal working
  • Y10T29/49—Method of mechanical manufacture
  • Y10T29/49002—Electrical device making
  • Y10T29/49009—Dynamoelectric machine
• • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
  • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
  • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
  • Y10T29/00—Metal working
  • Y10T29/49—Method of mechanical manufacture
  • Y10T29/49826—Assembling or joining

Definitions

• the present invention relates to the manufacture of soft magnetic alloy strip of iron-cobalt type.
• Electrotechnical equipment includes magnetic parts and in particular magnetic yokes made of soft magnetic alloys. This is the case in particular of the electric generators embedded in vehicles in particular in the field of aeronautics, railway or automobile.
• the alloys used are alloys of the iron-cobalt type and in particular alloys comprising approximately 50% by weight of cobalt. These alloys have the advantage of having a very high saturation induction, a high permeability to working inductions equal to or greater than 1, 6 Tesla and a fairly high resistivity allowing a reduction of AC and high induction losses. When in common use, these alloys have a strength corresponding to a yield strength of between about 300 and 500 MPa.
• HLE alloys are particularly useful for producing miniaturized alternators embedded on aircraft. These alternators are characterized by very high speeds of rotation exceeding 20,000 rpm which require a high mechanical resistance of the components constituting the magnetic yokes.
• various alloying elements such as Niobium, Carbon and Boron in particular.
• Static annealing in the state of the art of Fe-Co alloys, a heat treatment during which the cut pieces are maintained above 200 ° C for at least 1 hour and are passed through a temperature greater than or equal to 700 ° C, at which a bearing is imposed.
• step is meant a period of time of at least 10 minutes during which the temperature varies at most 20 ° C above or below a set temperature.
• an industrial "static" annealing treatment includes for this a temperature step of one to several hours: the "static" annealing thus takes several hours.
• the cold rolling is carried out on strips of thickness generally of the order of 2 to 2.5 mm, obtained by hot rolling and then subjected to a quenching. .
• This makes it possible to avoid, to a large extent, the order / disorder transformation in the material, which therefore remains almost disordered, but little changed with respect to its structural state at a temperature above 700 ° C.
• the material can then be cold rolled unhindered to the final thickness.
• the strips thus obtained then have sufficient ductility to be cut by mechanical cutting.
• these alloys are sold to users in the form of strips in the hardened state.
• the user then cuts the pieces, stacks them and assembles or assembles the magnetic yokes, and then carries out the thermal treatment of quality necessary to obtain the desired properties.
• This quality heat treatment aims to obtain a certain development of grain growth after recrystallization, because it is the grain size that sets the compromise between mechanical and magnetic performance. Depending on the parts considered of the electrotechnical machine, the performance compromises, and therefore the heat treatments, may be different.
• aeronautical edge generator stators and rotors are cut together in the same strip portion to minimize metal scrap.
• the rotor undergoes a heat treatment favoring relatively high mechanical performance, typically a temperature below 800 ° C
• the stator undergoes a heat treatment optimizing the magnetic performance (therefore with larger average grain size) typically a higher temperature at 800 ° C.
• this quality heat treatment may comprise for each type of cut piece, two anneals, one to adjust the magnetic and mechanical properties as we have just seen and the other to oxidize the surfaces of the sheets in order to reduce the inter-laminar magnetic losses.
• This second annealing may also be replaced by a deposit of an organic material, mineral or mixed.
• HLE performance 500 to 1200 MPa of elastic limit
• a "static annealing" as defined above by applying temperature steps between 700 and 720 ⁇ , therefore in a metallurgical state ranging from the hardened state then restored to a more or less crystallized state and suitable for this type of annealing; but in practice, in this range 500-1200 MPa, the elastic limit depends very substantially on the bearing temperature to the nearest degree; this hypersensitivity of performance at bearing temperature prohibits industrial transposition since static industrial furnaces can not in general ensure a temperature homogeneity of the charge to be annealed better than + O 'C, ie the extent of the adjustment range of the elastic limit between 500 and 1200 MPa; exceptionally this homogeneity may be +/- 5XI; however, this is not enough to control industrial manufacturing. the difficulty of reaching precise dimensions of the finished part when the final static annea
• the object of the present invention is to remedy these drawbacks by proposing a method for manufacturing a thin strip of soft magnetic alloy type iron-cobalt which, from the same alloy, allows to propose an easily cutable strip that can have as well , in a predefined manner, a yield strength that is both medium and very high while retaining the possibility of obtaining good to very good magnetic properties by subsequently applying a second static heat treatment or parade, the alloy being able to pass from a high yield state to a high magnetic performance state under the effect of an annealing such as, for example, a conventional static annealing, the alloy having, in addition, a good aging resistance of its mechanical properties up to 200 ' ⁇ .
• the subject of the invention is a process for producing a band of a soft magnetic alloy capable of being mechanically cut, the chemical composition of which comprises, by weight:
• a strip obtained by hot rolling of a half product made of this alloy is cold rolled to obtain a cold-rolled strip of thickness typically less than 0.6 mm and, after cold rolling, performs on-band annealing treatment by passing through a continuous furnace, at a temperature between the order / disorder order transition temperature of the alloy (for example 700-710 ⁇ for alloy Fe-49% Co-2% V well known to those skilled in the art) and the ferritic / austenitic transformation start temperature of the alloy (typically 880 to 950%). for the FeCo alloys of the invention), followed by rapid cooling to a temperature of less than 200%.
• the annealing temperature is preferably from 700 ° to 930 ° C.
• the running speed of the strip is adapted so that the residence time of the strip at the annealing temperature is less than 10 minutes.
• the cooling rate of the strip at the outlet of the treatment furnace is greater than 1,000 ° C./h.
• the speed of travel of the strip in the furnace and the annealing temperature are adapted to adjust the mechanical strength of the strip.
• the chemical composition of the alloy is such that:
• This method has the advantage of making it possible to manufacture a thin strip which can be easily cut by mechanical means and which is distinguished from bands known by its metallurgical structure.
• the band obtained by this method is a cold-rolled soft magnetic alloy strip, less than 0.6 mm thick, made of an alloy whose chemical composition comprises, by weight:
• crystals or grains are totally hardened, that is to say that the crystalline order is totally dislocated at long distance, and that the notion of crystals or "grain” no longer exists. .
• the annealing treatment with the parade then makes it possible to "crystallize” this matrix worked in crystals or grains. This phenomenon is nevertheless also called recrystallization because it is not the first crystallization undergone by the alloy since its development phase from the solidified liquid metal.
• the chemical composition of the soft magnetic alloy is such that:
• the elastic limit R P0,2 is between 590 MPa and 1100 MPa
• the coercive field Hc is between 120 A / m and 900 A / m
• the magnetic induction B for a field of 1600 A / m is between 1, 5 and 1, 9 Tesla.
• the saturation magnetization of the band is greater than 2.25 T.
• this strip it is possible to manufacture parts for magnetic components, for example rotor and stator parts, and in particular for magnetic yokes, and magnetic components such as magnetic yokes, by directly cutting the parts in a strip according to the invention. then, if necessary, by assembling the parts thus cut in such a way as to constitute components such as cylinder heads, and possibly causing some of them (for example the stator parts only) or to some of them (for example stator yokes) a complementary annealing treatment to optimize the magnetic properties, and in particular to minimize magnetic losses.
• parts for magnetic components for example rotor and stator parts, and in particular for magnetic yokes, and magnetic components such as magnetic yokes
• the invention also relates to a method for manufacturing a magnetic component according to which a plurality of parts is cut by mechanical cutting in a strip obtained by the preceding method, and, after cutting, the parts are assembled to form a magnetic component. .
• the magnetic component or the parts can be subjected to a static annealing of quality, that is to say, an annealing of optimization of the magnetic properties.
• the static annealing of quality or of optimization of the magnetic properties is annealing at a temperature of between 820 ° C. and 880 ° C. for a time of between 1 hour and 5 hours.
• the magnetic component is for example a magnetic yoke.
• an alloy known per se is used, the chemical composition of which comprises by weight: from 18% to 55% of cobalt, 0% to 3% Vanadium and / or Tungsten, 0% to 3% Chromium, 0% to 3% Silicon, 0% to 0.5% Niobium, 0% to 0.05% % boron, 0% to 0.1% C, 0% to 0.5% zirconium and / or tantalum, 0% to 5% nickel, 0% to 2% manganese, the rest being iron and impurities resulting from the elaboration.
• the alloy contains 47% to 49.5% Cobalt, 0% to 3% Vanadium plus Tungsten, 0% to 0.5% Tantalum, 0% to 0.5% of Nobium, less than 0.1% chromium, less than 0.1% silicon, less than 0.1% nickel, less than 0.1% manganese.
• the vanadium content should preferably be greater than or equal to 0.5% in order to improve the magnetic properties and better escape the weakening ordering during rapid cooling, and remain less than or equal to 2, 5% in order to avoid the presence of the second non-magnetic austenitic phase, tungsten not being indispensable, and the niobium content should preferably be greater than or equal to 0.01% in order to control the growth of the grain at high temperature and to facilitate hot processing.
• Niobium is indeed a growth inhibitor to limit the germination of crystallization and grain growth in conjunction with parboiling.
• the alloy contains a little carbon so that, during the preparation, the deoxidation is sufficient, but the carbon content must remain less than 0.1% and preferably less than 0.02% or even 0, 01% to avoid forming too many carbides which deteriorate the magnetic properties.
• This alloy is for example the alloy known as AFK 502R which contains essentially 49% cobalt, 2% vanadium and 0.04% niobium, the remainder consisting of iron and impurities and small quantities of elements such as C, Mn, Si, Ni and Cr.
• This alloy is produced in a manner known per se and cast in the form of semi-finished products such as ingots.
• a semi-finished product such as an ingot
• is hot rolled to obtain a hot strip whose thickness depends on the practical conditions of manufacture. As an indication, this thickness is generally between 2 and 2.5mm.
• the resulting strip is subjected to a quenching.
• This treatment largely avoids the order / disorder transformation in the material so that it remains in an almost disordered structural state, little changed with respect to its structural state at a temperature above 700 ° C and which therefore, is sufficiently ductile to be cold rolled.
• the hypertrempe therefore allows the hot strip to be then cold rolled without clutter up to the final thickness.
• the quenching can be carried out directly at the hot rolling outlet if the rolling end temperature is sufficiently high, or, otherwise, after reheating to a temperature above the order / disorder transformation temperature.
• the weakening order is established between 720 ⁇ and the ambient, or the metal is violently cooled, with water for example (typically at a speed greater than 1000 ° C / min), rolling output hot from a temperature of 800 to 1000 ° C to the ambient temperature, ie the hot-rolled metal which is then slowly cooled, therefore brittle, is heated to between 800 and 1 000 ° C before violent cooling to ambient temperature .
• Such a treatment is known in itself to the skilled person who knows how to make it on the equipment that he usually has.
• the hot strip is cold rolled to obtain a cold strip having a thickness of less than 1 mm, preferably less than 0.6 mm, generally of between 0.5 mm and 0.2 mm, and which can be as low as at 0.05 mm.
• the annealing temperature should be between 700 ° C and 930 ° C.
• the range of temperature of the annealing at the parade can be all the more extended towards the low temperatures that the cobalt content will approach 18%.
• the annealing temperature should be between 500 and 950%. The person skilled in the art knows how to determine this annealing temperature according to the composition of the alloy.
• the rate of passage in the oven can be adapted taking into account the length of the oven so that the passage time in the homogeneous temperature zone of the oven is less than 10 minutes and preferably between 1 and 5 minutes.
• the holding time at the treatment temperature must be greater than 30s.
• the speed must be greater than 0.1 meters per minute.
• the speed of movement must be greater than 2 meters per minute, and preferably 7 to 40m / min.
• the skilled person knows how to adapt the scrolling speeds according to the length of the furnaces which he has.
• the treatment furnace used can be of any type.
• it may be a conventional resistance furnace or a thermal radiation furnace, a Joule annealing furnace, a fluidised bed annealing plant or any other type of furnace.
• the strip At the furnace outlet, the strip must be cooled at a fast enough speed to avoid a complete order-disorder transformation.
• a thin strip (0.1 to 0.5 mm) intended to be machined , stamped, punched may be subject only to a partial ordering which results in a weak degree of fragility so that a hyperemperature is not necessary.
• the cooling rate - determined between the order / disorder temperature (700% for a conventional alloy of composition close to Fe-49% Co-2% V) and 200% - must be greater than 600 ° C per hour, and preferably greater than 1000 ° C per hour or even 2000 Oh. In practice, it is not necessary to exceed 10,000 ° C / h and a speed of between 2,000 ° C / h and 3,000 ° C / h is generally sufficient.
• the inventors have found, surprisingly, that with such a run-off treatment, and contrary to what is observed with static heat treatments making it possible to obtain comparable mechanical or magnetic properties, sufficiently ductile strips were obtained in order to be able to be cut mechanically to make parts to be stacked to form magnetic yokes or other magnetic components.
• the inventors have also found that by adjusting the passage time in the oven it is possible to adjust the mechanical characteristics obtained on the strip so that, from a standard iron-cobalt alloy, it is possible to obtain both alloys with usual mechanical characteristics, that is to say with a yield strength of between 300 and 500 MPa, as alloys of the high yield strength (HLE) type, that is to say having a yield strength greater than 500 MPa, preferably from 600 to 1000 MPa, and up to 1200 MPa.
• HLE high yield strength
• the standard iron-cobalt alloy is for example an iron-cobalt alloy of the AFK 502R type containing essentially 49% of cobalt, 2% of vanadium and 0.04% Nb, the remainder being iron and impurities,
• the inventors have found that this set of unusual performances, namely cutability in the annealed state, while at the same time fixing the elastic limit between 300 and 1200 MPa, was closely related to the particular metallurgical structure obtained by the continuous annealing according to the invention. which is different from the metallurgical structure resulting from static annealing. This concerns in particular the rate of crystallization and, for sufficiently crystallized materials, the distribution of grain sizes, which is very different from that obtained with static annealing to obtain the same properties of use of the material. .
• T is the annealing temperature in ⁇ C
• B1600 is the magnetic induction expressed in Tesla, for a magnetic field of 1600 A / m (about 20 Oe).
• Br / Bm is the ratio of the remanent magnetic induction Br to the maximum magnetic induction Bm obtained at magnetic saturation of the sample.
• Hc is the coercive field in A / m
• Losses are the magnetic losses in W / kg dissipated by the currents induced when the sample is subjected to a variable magnetic field which, in this case, is an alternating field of frequency 400 Hz inducing an induction sinusoidal alternative through the use of an electronic control of the applied magnetic field, which is known in itself to the skilled person; the maximum value of the magnetic field is 2 Tesla.
• Rpo , 2 is the conventional yield strength measured in pure tension on standardized samples.
• the compromise mechanical properties / magnetic properties can be adjusted by the annealing temperature parade.
• an alloy having the chemical composition of these examples can be used by a customer who wishes to manufacture both parts with high mechanical characteristics as well as with current mechanical characteristics and which can perform static optimization annealing only on the parts it has cut to simply optimize the magnetic losses if necessary.
• the run-in annealing was done at three speeds of 1m 2 per minute to obtain the magnetic and mechanical properties corresponding to the use to make magnetic stator yokes for which low to medium magnetic loss levels are sought. ; a speed of 2.4 m per minute to obtain the mechanical characteristics suitable for producing magnetic rotor yokes, and at 3.6 and 4.8 m per minute to obtain mechanical characteristics corresponding to the HLE quality.
• samples were subjected to static annealing at a temperature of 760 ° C for two hours.
• This annealing is a conventional annealing of conventional "static annealing optimization" which leads to properties comparable to those of the annealing at the speed of 1, 2 m per minute at 880 'C.
• the yield strength R P0,2 can be set within a very wide range of values between 400 MPa and 1200 MPa by varying the annealing parameters which are the speed of passage, that is to say say the residence time high temperature, and the annealing temperature and this, under satisfactory conditions for industrial production. Indeed, the properties obtained vary slowly enough with the processing parameters to be able to control an industrial manufacturing. These results also show that there is a strong correlation between the elastic limit, the coercive field and the various other properties of the alloy.
• these tests made it possible to identify the effects of heat treatments on the metallographic structure of the alloy produced by the process according to the invention.
• the tests were carried out in particular on casting JD 842.
• the measurements were made in particular on a sheet having been annealed at the parade at 880 ° C with different speeds of scrolling.
• the temperature of 880 ° C was chosen because it is the one that corresponds to the optimum for obtaining good magnetic properties, that is to say, at a temperature allowing to obtain at the same time low values of magnetic losses and a wide range of elasticity limits (for example from 300 MPa to 800 MPa) by simple variation of the running speed with values leaving the alloy only a few minutes ( ⁇ 10 minutes) in the temperature plateau zone .
• B1600 Magnetic induction obtained for a magnetic field of 1600 A / m
• micrographs were made with immersion etching for 5 seconds in a bath of iron perchloride at room temperature containing (per 100 ml): 50 ml of FeCl 3 and 50 ml of water after polishing with 1200 paper then electrolytic polishing with a bath A2 consisting (for 1 liter) of 78 ml of perchloric acid, 120 ml of distilled water, 700 ml of ethyl alcohol, 100 ml of butylglycol.
• the micrographs show a very specific structure very distinct from the structures obtained by static annealing. It is a structure apparently close to that of the hardened metal.
• the inventors have also found that the micrographs made on the materials which were annealed at 880 ° C. at a speed of 4.8 m per minute had a very anisotropic structure (very elongated grains), much more anisotropic than the structure obtained by annealed at 785 ° C with a flow rate of 4.8 m per minute.
• an anisotropic specific structure obtained for parades at the highest speeds (2.4 m per minute, 3.6 m per minute and 4.8 m per minute).
• This structure is a restored or partially crystallized structure which can be confirmed by an X-ray examination which shows that the texture is that of a restored weakly recrystallized material, very similar to the hardening texture;
• the grain size was also determined. Since the coercive field of a magnetic alloy is closely related to the size of the grain, in order to be able to make meaningful comparisons between two modes of treatment of the same material, it is necessary to make observations on materials having equivalent coercive fields. Also, to carry out these measurements, samples with adjacent coercive fields were chosen, and measurements were made on a material which had been subjected to static annealing at 760 ° C for two hours, and on the other hand for a material which had been annealed in the parade at 880 ° C with a pass rate of 1.2 m per minute.
• the grading was done using automatic image analysis equipment to detect the grain boundary, calculate the perimeter of each of them, convert this perimeter to equivalent diameter and finally , to calculate the surface of the grain.
• This device also makes it possible to obtain a total number of grains as well as their surface.
• Such automatic grain size image analysis devices are known per se. In order to obtain results that have a satisfactory statistical significance, the rating was performed on a plurality of sample areas. The quotation was made by defining the following grain size classes:
• grains having a surface area ranging from 10 ⁇ 2 to 140 ⁇ 2 in steps of 10 ⁇ 2 .
• grains ranging in size from 480 to 560 ⁇ 2 grains ranging in size from 560 to
• continuously annealed materials show a structure in which there are fewer small grains but larger grains between 200 and 1000 ⁇ 2 .
• the grains between 30 and 50 ⁇ 2 occupy a surface equivalent to that occupied by large grains of size between 500 ⁇ 2 and 1,100 ⁇ 2 .
• grain gradings were carried out on four strips of thickness 0.34 mm on which on the one hand an annealing was carried out at 880 ° C. under hydrogen at a speed of 1.2 m per minute and on the other hand a static annealing optimization at 760 ° C for two hours under Hydrogen.
• These bands correspond to the castings JE 686, JE798, JD 842, JE 799 and JE 872 whose compositions are reported in Table 3.
• These examinations show that for these flows, the distribution of the finest grains and in particular smaller than 80 ⁇ 2 is very different for samples that have been subjected to a static classification anneal at 760% of what it is for samples that result from a run-on treatment at 880 ° C.
• the fine grains are much more numerous on the samples which have been subjected to a static annealing than on the samples which have been subjected to a parade annealing. It should be noted in particular that for grains smaller than 40 ⁇ 2 , the number of grains, by size class, on the samples having undergone static annealing is greater than the maximum number of grains obtained on samples annealed at the parade. All of these results show that, especially with runway annealing, the grain size distribution does not have a dominant grain size. The maximum number of grains recorded in a grain size class never exceeds 30, unlike static annealing where the number of grains can reach 160 for the same size class, especially for small grains.
• either the structure is of the "partially crystallized" type, that is to say that, on at least 10% of the surface of samples observed under a microscope with a magnification of x 40 after chemical attack with iron perchloride, it is not possible to identify grain boundaries;
• either the structure is of the "crystallized" type, that is to say that on at least 90% of the surface of samples observed under a microscope with a magnification of x 40 after chemical attack with iron perchloride, it is possible to identify a network of grain boundaries and, in the range of grain sizes from 0 to 60 ⁇ 2 , there is at least one class of 10 ⁇ 2 of grain size width comprising at least twice as many grains that the same size class of grains corresponding to the observation of a comparative cold-rolled strip having the same composition, not having been subjected to continuous annealing but having been subjected to static annealing at a temperature such that the difference between the coercive field obtained with the static annealing and the coercive field obtained with the parboiled annealing is less than half the value of the coercive field obtained by the parade treatment and, in the grain size range from 0 to 60 ⁇ 2 , there is at least one grain class size of 10 ⁇ 2 of width whose ratio of the number of grains to
• stators were cut on samples which, according to the invention, were annealed at temperatures of 785 ° C., 800 ° C., 840 ° C., with travel speeds of 1.2 m per hour. minute for a useful oven length of 1.2 m, which corresponds to a residence time of one minute at the annealing temperature.
• These cuts were made on punched industrial punching plants using a punch and a die. The cuts were made on the strips of thickness of 0.20 mm and 0.35 mm.
• the quality of the cut was determined by evaluating the cutting radius and the presence or absence of burrs. The results are shown in Table 6. On reading, it appears that whatever the thickness and regardless of the annealing temperature on the parade, the quality of the cut is satisfactory according to the usual criteria corresponding to the requirements of the customers.
• This alloy was manufactured in the form of strips of different thicknesses cold-rolled, and then subjected to annealing by a passage at a continuous speed in a furnace under a protective atmosphere, at temperatures of plateau equal to 700 ⁇ C, 750 ° C, 800 ° C, 850 ⁇ C, 900 ° C or 950 ⁇ C for a time equal to bearing 30 s, 1 min, or 2 min.
• the bands After this annealing, the bands have been cooled to a temperature below 200 ⁇ C at cooling speeds of 600 ° C / h and 35000 ⁇ C / h.
• the specimens were subjected to a standard tape fragility test in accordance with IEC 404-8-8.
• This test consists of bending the flat specimen at 90 ° alternately from each initial position, according to a device and a procedure described in the IS07799 standard.
• the bending radius chosen by the IEC 404-8-8 standard for extra-thin sheets (FeCo type) used at medium frequencies is 5mm.
• a 90 ° bend from the initial position with return to the home position counts as one unit.
• the test is stopped at the appearance of the first crack visible to the naked eye in the metal. The last folding is not counted.
• the tests were carried out at 20 ° C. on widgets of width 20 mm in FeCo alloy, by a slow and uniform movement of alternating folding.
• the samples in the form of plates were subjected to a cutting test on punched industrial punching plants using a punch and a die.
• the quality of the cut was determined by evaluating the cutting radius and examining the wafer for the burrs and the proportion of thickness of the metal that yielded by transgranular fracture without significant plastic elongation of the material (origin of the cutting burrs). ).
• a very good cutability corresponds to a metal cut with a reduced press force compared to what was known in the state of the art on a hardened FeCo alloy, to a cutting zone without smudge and to a high proportion of transgranular rupture thickness.
• Good cutability corresponds to a metal cut with a high press force and in accordance with what was known in the state of the art on a FeCo alloy.
• the band In this metallurgical state (hardened or even slightly restored) the band is very elastic and strong and deforms widely before the punch begins its penetration, and as during penetration with a very large press force.
• the cutting zone is made by completely transgranular rupture without burr with a very large elastic return of the band after perforation.
• a medium cutability is an alloy for which cutting is easy but the cutting area becomes irregular and burrs or tearing of metal appear on the exit face of the punch. Cutability is described as bad when cracks appear around the punch before the punch has finished puncturing the sheet. The beginning of elastic pressure of the band by the punch may be sufficient to cause cracking and rupture of the sample.
• T is the annealing temperature in ⁇ C
• V R is the cooling rate up to a temperature below 200 ° C in ° C / h
• Losses (1) are the magnetic losses in W / kg dissipated by the currents induced when the sample is subjected to a variable magnetic field which, in this case, is an alternating field of frequency 400 Hz inducing a sinusoidal induction by means of the use of an electronic control of the applied magnetic field, known in itself to the skilled person, whose maximum value is 2 Tesla.
• the metal has only undergone annealing.
• Losses (2) are the magnetic losses in W / kg after the optimization annealing, after the annealing at the parade.
• Table 7 Effect of the annealing temperature and the cooling rate of the strip at the outlet of the oven on the mechanical and magnetic properties
• a number of folds greater than or equal to 20 obtained following a run-on annealing at a bearing temperature of less than 720 ° C., or a bearing time of less than or equal to 30 seconds, is associated with good cutability (tests 1, 7, 16); , 28, 32);
• the metal has systematically at least good cutability, or very good for partially or completely recrystallized materials, ie subjected to annealing temperatures at the runway. at least 710 ° C. Below 710 ° C. (tests 1 and 7), it would also be possible, by increasing the dwell time, to obtain a partial recrystallization, but this dwell time should be of long duration, very little compatible with annealing at room temperature. industrial fashion show. An annealing temperature greater than 700 ° C., or even greater than 720 ° C., is therefore favorable.
• the coercive fields of the materials obtained are very high, at least 150 °, which corresponds to materials mostly hardened and restored, without significant crystallization. Nevertheless, the magnetic losses exceed 500 W / kg. It is therefore preferable to apply bearing temperatures greater than or equal to 720 ° C., making it possible to obtain, for bearing times of less than 3 minutes, limited magnetic losses (less than 500 W / kg for a thickness of 0.2mm).
• the magnetic strips according to the invention advantageously have, for a thickness of between 0.05 mm and 0.6 mm, magnetic losses of less than 500 W / kg, preferably less than 400 W / kg.
• the annealed at 900 ⁇ do not alter or low magnetic losses after static annealing additional 3h with respect to temperatures below Thus it is considered the most relevant bearing temperature zone is between 720 ⁇ and 900 ⁇ C.
• the magnetic losses must remain at a level that can remove the heat to the rotor: typically the magnetic losses at 2T / 400Hz for a thickness of 0.2mm must be less than 500W / kg, and preferably less than 400 W / kg. The method according to the invention makes it possible to achieve such values.
• the method according to the invention makes it possible to cut all the parts in the annealed state of annealing with a predetermined and high elastic limit, for example according to the requirements of the rotor, it is necessary to apply after cutting , specifically to the stator cut pieces, an annealing of optimization of the magnetic properties (of the 850 ° C-3h type under pure H 2 ), the stator needing generally and mainly very low magnetic losses.
• a predetermined and high elastic limit for example according to the requirements of the rotor
• Example A corresponds to an alloy of the same composition as that used for the tests given in Table 7.
• Example A is identical to Test 10 of Table 7.
• Example B includes a decrease in the percentage of vanadium and additions of niobium and tantalum, the latter being used to replace the role of moderator of the ordering of vanadium, while niobium is a growth inhibitor to limit germination of recrystallization and grain growth in conjunction with runway annealing. It can thus be seen that the performances are in the range of the properties concerned and at the same time shifted towards higher elastic limits and magnetic losses compared with Example A.
• Example C contains more Si, S, Nb, Ta and B than the reference alloy A while being consistent with the target range of properties: the silicon added moderately hardens a little the metal by its presence in solid solution while boron and sulfur precipitate at grain boundaries and niobium slows crystallization / growth. This causes a strong slowdown in crystallization, visible on the higher elastic limit, as well as an acceptable increase in magnetic losses.
• Example D shows stronger additions of Mn and B while tantalum remains at the same level as in alloy C, and vanadium is lowered to 1%.
• the performances are always in accordance with the invention.
• the much higher boron addition results in strong trapping of seeds and grain boundaries, further increasing elastic limits and magnetic losses.
• Example E has undergone strong additions of C, Si, Cr and Nb while the percentage of cobalt is reduced to 27%, making it a substantially less magnetically powerful alloy, but also much less expensive.
• the percentage of vanadium is reduced to a very low level because there is no more ordering weakening for such a percentage of cobalt.
• the magnetic performances obtained still remain in the target range of property, even if the magnetic losses after additional annealing of magnetic optimization reach a rather high level (81 W / kg) but nevertheless in accordance with the targeted properties ( ⁇ 100 W / kg).
• Example F part of the vanadium is replaced by tungsten, compared with the reference alloy A.
• the performances are only slightly changed, and in any case remain in the range of properties sought.
• Example G part of the vanadium is replaced by zirconium. Zr being a germination inhibitor and grain growth a little less powerful than Nb, we see that the elastic limit values and magnetic losses are increased (relative to alloy A), and in any case in the spectrum of properties referred.
• Example H more than 3% Ni is added which is known to further increase the ductility of the material as well as the electrical resistivity. However saturation magnetization is reduced but still in accordance with the invention, like all other properties characterized.
• composition according to Example J contains 3.8% vanadium, which exceeds the maximum limit of 3% V + W. With such a percentage, we penetrate significantly in the two-phase ⁇ + ⁇ domain, which causes a sharp degradation of magnetic performance after additional performance optimization anneal (850 ⁇ / 3h), placing them well above the desired limit of 100W / kg.
• composition according to Example K contains 3.5% of chromium, but not of vanadium, which enables it to have sufficient saturation magnetization (2.26T) but very poor folding and cutting ability. This is due to the fact that unlike vanadium, chromium does not have the capacity to slow the weakening order of FeCo around 50% Co +/- 25%. The hot-rolled and cold-rolled strips then annealed at the parade are therefore fragile.
• Example L bypasses the previous problem by reintroducing 2% of vanadium, as in the reference alloy A, with in addition, and as in the previous example K, a percentage of chromium greater than 3%.
• the metal becomes ductile and cut after annealing, but the rate of addition of non-magnetic elements is too high and, by dilution of the atomic magnetic moments of iron and cobalt, the saturation magnetization Js becomes lower (2, 21 T) at the required lower limit of 2.25T.
• composition according to Example M does not contain vanadium but contains
• the composition according to Example N contains 2% vanadium, just like the reference alloy A, and also contains 0.65% of niobium, which is greater than the limit of 0.5% according to the invention.
• niobium is known not only as a potent inhibitor of germination, recrystallization and grain growth, but also as a creator of carbonitrides of Nb and Laves (Fe, Co) 2 Nb phases, when the percentage of niobium becomes important. These phases and precipitates further slow the migration of the grain boundaries, but especially deteriorate the magnetic properties by effective anchoring of the walls of Bloch. This results in high losses (143W / kg) after additional annealing of magnetic performance optimization.
• composition according to Example O contains 0.1% boron, which is well above the maximum limit of boron according to the invention (0.05%). This causes a very great fragility of the material to the fold and poor cutability: The precipitation of Fe and Co borides is such that the grains are weakened and that the metal has lost any ductility.
• Example P explores the important addition of nickel (6.03%) while the composition remains very similar to the reference alloy A: not only the saturation magnetization becomes too weak (2.23 T ⁇ 2.25T minimum), but the magnetic losses after additional annealing of magnetic performance optimization (850 ° C-3h) become very high (328 W / kg). Nickel indeed stabilizes the ⁇ phase, and such an alloy causes the strong presence of non-magnetic ⁇ phase in the middle of the ferromagnetic ferrite phase. The material is therefore magnetically soft and the magnetic losses are very important.
• the metal cooling rate in annealing output in the parade and determined between the temperature level to 200 ⁇ is at least 600 Oh, and preferably at least 1000 ⁇ C / h the bearing temperature is at least 700%, preferably at least 720 ° C,
• the bearing temperature is at most 900 ' ⁇ .
• aging tests were carried out at 200 ° C. with holding times of 100 hours and 100 hours + 500 hours cumulative. These tests were carried out at 200 ° C. because this temperature corresponds approximately to the maximum temperature at which materials constituting the yokes of rotating electrotechnical machines used under normal operating conditions can be subjected.
• tests were made with an alloy of the AFK502R type for two standard grades corresponding to static annealing of 760 ° for two hours and 850 ° C. for three hours, and for bands according to the invention corresponding to annealing at the runway.
• the induction B for a field of 1600 A / m varies by at most 2% following the annealing and the coercive field Hc of at most 23%.
• the annealed annealed alloys are not more sensitive to aging than the annealed annealed alloys.
• an alloy as defined above that is to say containing from 18 to 55% of Co, from 0 to 3% of V + W, from 0 to 3% of Cr, from 0 to 3% of Si, from 0 to 0.5% of Nb, from 0 to 0.05% of B from 0 to 0.1% of C, from 0 to 0.5% of Ta + Zr, from 0 to 5% of Ni, from 0 to 2% Mn, the rest being iron and impurities resulting from the preparation and in particular an alloy of the AFK502R type, it is possible to manufacture magnetic components and especially magnetic shields, by cutting by mechanical cutting parts in cold rolled strips continuously annealed to obtain the desired mechanical characteristics taking into account the intended application and, according to this application, by performing or not performing on these possibly assembled cut pieces, a complementary annealing of quality intended for optimize the magnetic properties of the alloy.
• the cold-rolled strips are obtained by cold rolling hot-rolled hyper-tempered strips to maintain a substantially disordered structure.
• the person skilled in the art knows how to manufacture such hot-rolled strips.
• an oxidation heat treatment can be performed to ensure the electrical isolation of the parts of a stack as is known to those skilled in the art.

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