Classifications

• • H—ELECTRICITY
  • H01—ELECTRIC ELEMENTS
  • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
  • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
  • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
  • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
  • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
  • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
  • H01F1/147—Alloys characterised by their composition
  • H01F1/14708—Fe-Ni based alloys
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
• • 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
• • 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
  • C21D6/001—Heat treatment of ferrous alloys containing Ni
• • 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
  • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
• • 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
• • 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
  • C22C38/16—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
  • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
• • H—ELECTRICITY
  • H01—ELECTRIC ELEMENTS
  • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
  • H01F10/00—Thin magnetic films, e.g. of one-domain structure
  • H01F10/08—Thin magnetic films, e.g. of one-domain structure characterised by magnetic layers
  • H01F10/10—Thin magnetic films, e.g. of one-domain structure characterised by magnetic layers characterised by the composition
  • H01F10/12—Thin magnetic films, e.g. of one-domain structure characterised by magnetic layers characterised by the composition being metals or alloys
• • 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
  • C21D2211/001—Austenite

Definitions

• the present invention relates to an austenitic iron-nickel chromium-copper alloy, more particularly intended for the manufacture of electromagnetic devices.
• Nickel-rich iron-nickel and iron-nickel-chromium alloys have been known for a long time and are used in many applications in electrical engineering (electronics, electrical engineering), visualization, energy transport, thermal regulation or electrical engineering. electrical safety, thanks to their original and varied physical properties.
• thermal dilatabilities between 20 and 100 0 C between 2 and 13.10 "6 Z 0 C according to their composition, which is an exceptional feature for a ductile material, specific to a few materials.
• iron-nickel and iron-nickel-chromium alloys have long been used in electromagnetic applications where it is imperative either to save energy (watchmaking electric motors, high-sensitivity differential circuit breaker relays, high-speed motors and low temperature, etc.), have a very small hysteresis to significantly limit the measurement dispersion of the magnetic sensors (current transformer, DC sensor, resolvers and synchro-resolvers) or hysteretic losses (measurement transformer, modem ...), or still to offer a very privileged channel of the magnetic fluxes as in some magnetic cylinder of high dynamics actuator (electromagnetic injector of gasoline for example), in the motor-wheel, in the passive magnetic shieldings with strong attenuation.
• Iron-nickel alloys whose coercive field is generally less than 125 mOe, thus allow a real jump in the energy consumption of electrical systems, compared with traditional silicon-type materials, since they reach coercive fields. of the order of 190 mOe in a single direction which is of little interest, or more generally are 500 to 1250 mOe when the application needs to convey the magnetic flux in different directions of the material (motors, generators, etc.).
• the object of the present invention is to remedy these drawbacks by proposing an alloy composition having an acidic aqueous corrosion resistance and improved salt spray corrosion, capable of forming a solid surface oxidation layer. and adherent, which can be used for many applications and has a reduced cost.
• the invention firstly relates to an austenitic iron-nickel-chromium-copper alloy whose composition comprises in% by weight:
• the proposed solution is a family of austenitic and ferromagnetic Fe-Ni-Cr-Cu alloys suitable for economical industrial production, by induction or arc furnace, having few expensive elements and offering high or original performances for several areas of applications that will be detailed later. It was never discovered until now an alloy family could satisfy all these properties.
• the use of the same alloy for very different applications (for example by satisfying at the same time the need for reduced dilatability, resistance to corrosion, magnetism and Curie point) makes it possible to produce a larger tonnage. , to have a greater experience of industrial production and therefore a more reliable alloy in terms of reproducibility of the properties.
• the present inventors have found the ability of silicon, chromium and copper to mechanically and chemically strengthen the surface-oxidized protective layer and to make it very adherent.
• the oxidized layer becomes very stable in the time of the heat treatment or the use in an oxidizing ambient atmosphere, very chemically stable with respect to external chemicals and very mechanically stable with respect to shocks and friction between metal parts during the cycle. industrial production.
• this very stable oxide generally has a thin thickness of a few microns, depending on the heat treatment cycle used.
• This small thickness of oxide is particularly interesting in watchmaking, because it limits and calibrates at the same time the air gap between the stator and magnetic coil core, respectively leading to both a limitation of the energy consumed by the battery of the watch and a reduction in the industrial dispersion of watch engines.
• the alloy according to the invention comprises, in% by weight, the contents defined below.
• the nickel content is limited to 36%, preferably 35% by weight and more preferably 34%, or even 29%. Such a limitation makes it possible to strongly limit the cost of the grade. She permits also to have an electrical resistivity of at least 70 ⁇ .cm, or even at least 80 ⁇ .cm if the nickel content is less than 34%, which is one of the elements of a good magnetization dynamics (the two others being a small thickness of metal and a weak coercive field). For some applications, such as bimetallic manufacturing, it is preferred to maintain the nickel content at 30% or higher to ensure a high Curie point. The nickel content is at least 24% in order to guarantee the obtaining of an austenitic structure throughout the composition range according to the invention.
• the chromium content is greater than or equal to 0.02% because it requires a minimum of chromium to have the required corrosion resistance properties. Furthermore, when the nickel content is between 32.5 and 36%, the chromium content is limited to 7.5%, in order to limit the cost of all elements other than iron and silicon. These characteristics make it possible to improve the resistance to acidic aqueous corrosion, atmospheric corrosion and hot oxidation of the grade, since the formation of a very chemically stable superficial oxide is observed, which is also very adherent to the metal. In addition, the addition of these elements does not significantly degrade the other properties of use of the alloy, such as the Curie point or the saturation magnetization.
• the copper content is greater than or equal to 0.1% and is limited to a content of 15% and preferably to a content of 10% (in order to limit the cost of all elements other than iron and silicon ), possibly substituted by cobalt.
• copper significantly improves the adhesion of the oxidized layer forming hot to the surface of the alloy.
• the grade does not contain cobalt because of its cost and for the same reason, if cobalt is present, it is necessary that its content be lower than that of copper.
• cobalt must be limited to not more than 4%, and preferably 2%, because we want to limit the cost of all elements other than iron and silicon
• the addition of at least 0.02% of silicon makes it possible to significantly improve the mechanical wear resistance of the surface oxide layer.
• the silicon may be added up to 2% to the alloy according to the invention to participate in its deoxidation in the arc furnace, without harming the other properties of the alloy.
• the manganese content is between 0.01 and 6% by weight, and preferably between 0.02 and 6% by weight, which makes it possible to obtain an alloy which transforms well under heat thanks to the formation of sulphides, without degrade the properties of use of the alloy, such as the Curie point or the saturation magnetization.
• the manganese content In order to maintain saturation induction values Bs greater than 4000 G, it is preferred that the manganese content remain below 5%. More preferably, the manganese content is between 0.1 and 1% by weight.
• chromium its effect on saturation induction is aggravated, hence the need to limit it as follows: Mn ⁇ Ni - 27.5 + Cu - Cr if Eq3> 205
• the alloy may also include addition elements such as carbon, titanium, aluminum, molybdenum, vanadium, tungsten, niobium, zirconium, tin, boron, sulfur, selenium, antimony, calcium or magnesium.
• the carbon can be added to the alloy by up to 2% and preferably up to 1% to harden the alloy by carbide formation.
• Hc coercive field
• the carbon content will be kept below 0.1% after development-solidification in ingot or slab because its presence strongly degrades this characteristic.
• a decarburizing heat treatment may be applied to the thin sheet in the final state in order to significantly reduce the percentage of carbon to less than 100 ppm, and preferably to less than 50ppm.
• Titanium and aluminum can be added to the 3% cumulative alloy in order to harden the grade by precipitation of Ni 3 (Ti 1 Al) compounds.
• the addition of aluminum can also improve the weldability of the alloy on glass.
• the nitrogen combines as low temperature anneals in AIN or TiN type compounds, and it is therefore necessary to reduce the Al, Ti residual content to the lowest to ensure the compatibility between high magnetic performance and gas heat treatment comprising nitrogen. This point applies in particular to any application requiring high magnetic performance and involving annealing in an atmosphere containing nitrogen.
• the combined titanium and aluminum content is limited to 30 ppm and preferably 20 ppm.
• Molybdenum can be added up to 8% to improve both the mechanical strength and the hot oxidation resistance of the alloy. It will be limited preferably to 4% to limit the cost of elements other than Fe and Si. Vanadium and tungsten may be added to the alloy at a cumulative height of 6%, in order to improve its toughness, and are added preference to less than 3% in order to limit the cost of all elements other than iron and silicon.
• Niobium and zirconium can be added to the alloy at a cumulative height of 0.5% to improve its mechanical strength.
• Tin can be added to the alloy at a level of 1% partially substituted for chromium.
• the boron may be added to the alloy according to the invention in amounts ranging from 2 to 60 ppm, and preferably from 5 to 10 ppm, in order to improve its cutability by formation of boron nitrides. Below this range, its effect is no longer observable, while this effect saturates above 60ppm.
• Sulfur is an impurity present in the scrap used for the preparation of the alloy, but may also be added in amounts ranging from 5 to 80 ppm, and preferably from 10 to 30 ppm in order to also improve the cutability and machinability of the alloy by formation of manganese sulfide.
• the combined sulfur and boron contents are preferably between 5 and 60 ppm and preferably these two elements are combined within their respective preferred range.
• the rest of the composition consists of iron and unavoidable impurities from the elaboration. Among these, mention will be made more particularly of phosphorus, nitrogen and oxygen which are contained at a maximum height of 500 ppm. For some applications, it is necessary to limit the cumulative oxygen and nitrogen contents to 100 ppm in order to maintain the coercive field within the desired limits.
• the alloy according to the invention can be produced and manufactured in the form of a hot-rolled strip, then a cold strip before being annealed and then optionally cold-worked.
• One can also stop at the stage of the hot rolled strip.
• the alloy according to the invention can also be used in the form of massive products, forged or not, bars or son from a hot rolling possibly completed with a drawing.
• the strips or alloy piece may be obtained by any suitable method, as known in the art can do.
• the alloy according to the invention will preferably be melted in vacuum induction furnace ingots.
• the ingots can be forged between 1100 and
• cold rolling is carried out with an overall degree of hardening of 90 to 99% in several passes without intermediate annealing between each pass.
• the cold rolling At the end of the cold rolling, it is preferably annealed between 800 and 1100 0 C for 1 hour to soften the band alloy and thus facilitate its cutting or subsequent shaping. But it can be even more advantageous to cut by punching, stamping at high speed in the hardened state at the end of cold rolling, especially if the metal has been optimized vis-à-vis this implementation by the elements mentioned above such as B, S, Ca, Mg, Se ...
• the parts obtained can advantageously be annealed at 1100 ° C. for 3 hours under purified H2 (dew point ⁇ -70 ° C.) in order, in particular, to optimize the magnetic properties of the alloy.
• this annealing can be quite useless if it is particularly desirable to obtain dilatation or curie point properties or corrosion resistance properties.
• the alloys according to the invention can be produced in industrial annealing under any type of gas.
• the alloys according to the invention have potential applications in many fields. Preferred composition domains are thus defined, grouping together alloys that are more particularly adapted to a given application, which will be described in detail below.
• the percentages of nickel, chromium, copper, cobalt, molybdenum, manganese, vanadium, tungsten, silicon and aluminum are such that the alloy also satisfies the following conditions: 0.02 ⁇ Mn
• This composition is more particularly adapted to the manufacture of electromagnetic devices with self-regulation of temperature.
• a soft ferromagnetic material has a permeability ⁇ much higher than the permeability of the vacuum.
• T c characteristic value known as the Curie point
• the saturation magnetization of the material, its magnetic losses and therefore its generation of thermal power decreases as one approaches T c .
• the temperature autoregulation is then performed around the Curie point of the alloy if the residual magnetic losses specific to any non-magnetic conductor are removed, ie the heat flow from the alloy is greater than the flow.
• EP 1 455 622 where the temperature self-regulation is obtained by combining alloys at low T c between 30 and 350 0 C and at least 32.5% nickel, with an aluminum heat diffuser to remove the magnetic losses of the Fe-Ni-Cr alloy when it reaches Tc.
• the main property of use therefore remains the functional Curie point which is sought between 30 0 C and 400 0 C for induction cooking, industrial induction heating for example of injectors nozzles, composite molds, reheating beverage foods, foods, medical products, blood and constituents, soft or organic materials etc.
• alloys having a coefficient of expansion between 20 and 100 ° C. greater than 4.10 "6 Z 0 C, or even greater than 7.10 " 6 Z 0 C. are also preferably sought. to reduce the possible bimetal effect that may exist between the alloy and a conductor layer closely associated with the alloy by plating, seizing, welding, plasma deposition, etc.
• temperature self-regulation is however not restricted to induction cooking of liquids and food solids, but is more generally intended for any domestic or industrial system using an electromagnetic inductor and at least one thermally active part on passage elements which must be momentarily heated without exceeding certain critical temperature.
• thermosetting composites needle to regulate the temperature between 200 and 350 ° C. according to the type of composite
• thermoplastics needle to regulate the temperature between 150 and 250 ° C. according to the type of composite
• the alloy may further be such that:
• This composition is more particularly adapted to the manufacture of self-regulating magnetic flux devices.
• the magnetic flux regulation of a device as a function of the ambient temperature is based on the decrease of the saturation magnetization with the temperature in the vicinity of the Curie point, with a rate of decay that is substantially constant and fairly high. This allows a flow bypass system to compensate for exactly the magnetization decay of the magnets by varying magnetic flux passage section ratios between magnet and compensating alloy and thus still provide the same magnetic flux in a given range. temperature.
• This self-regulation of magnetic flux is most commonly performed around the ambient temperature, and in particular between 30 ° C. and + 100 ° C. There is therefore a need for different alloys which will have a Curie point Tc within this temperature range.
• the coercive field can be very degraded compared to the limit of 10A / m corresponding to the performance potential of the new alloys according to the invention.
• up to 2% carbon and preferably up to 1% carbon may be added.
• the alloy may further be such that:
• controlled expansion alloy means alloys with lower expansion coefficients than other metal alloys (0: 20-100> 10.10 "6 Z 0 C), ie typically 0: 20-100 ⁇ 10.10 "6 Z 0 C or 0: 20-300 ⁇ 13.10 " 6 Z 0 C.
• Another application is the manufacture of transistor supports and housings, optoelectronic circuit semiconductors (AsGa for example), RX tubes, sealed glass bushings ...
• the controlled expansion alloy is tightly bonded to a semiconductor or a glass or ceramic, and the expandability requirements can range from 4 to 5.10 "6 Z 0 C to 11.10 ⁇ 6 / ° C.
• One example is the support / strapping of large automotive roof windows
• the controlled expansion alloy provides only this function in the application, while being able to be shaped precisely by folding, stamping, stamping, spinning, mechanical or chemical machining (engraving ), welding, etc .:
• the mechanical part with precise dimensions made in the controlled expansion alloy has the advantage of expanding slightly and in a predefined manner over a wide temperature range.
• the parts of an electron gun heat up under the effect of electrons, by offering them only certain holes to pass (calibration of the electron beam) which is the function of these parts: we therefore need dilating alloy as little as possible throughout the working temperature range, and having good fitness.
• good resistance to aqueous acid corrosion In addition to dilatability, good resistance to aqueous acid corrosion, good resistance to salt spray corrosion and good resistance to mechanical wear of the oxide layer are desirable properties. These properties are obtained with inexpensive industrial annealing (low dew or dew point) or in harsh environments without the need for additional protection.
• the alloy may further be such that:
• This composition is more particularly adapted to the manufacture of current sensors or measurement transformers.
• an aptitude is sought to obtain good magnetic performances under any type of non-oxidizing industrial atmosphere such as neutral gas, He, H2, N2, NH3, etc., which then makes it necessary to reduce the Titanium content as much as possible.
• any type of non-oxidizing industrial atmosphere such as neutral gas, He, H2, N2, NH3, etc., which then makes it necessary to reduce the Titanium content as much as possible.
• neutral gas He, H2, N2, NH3, etc.
• Current sensor or measurement transformer means the current detection or magnetic field detection devices with a threshold overrun (electronic differential circuit breaker) or current measurement, field (current transformer, voltage , energy meter, DC sensor). This type of application particularly requires a weak coercive field while the saturation magnetization may be low (4000 to 8000G to
• the main magnitude of the application is the measurement accuracy which is strongly related to the coercive field of the alloy used, as well as in many cases the linearity BH of the magnetization curve or the hysteresis cycle: plus Hc is low, better is the measurement accuracy.
• a very low dynamic hysteresis is required to ensure good measurement accuracy at medium frequencies, which can be achieved by closed-loop structures operating at the same time. low induction, but also by choosing low Hc materials and high electrical resistivity.
• the linearity of the magnetization curve B-H is also sought up to the bend of the magnetization curve.
• This linearity is characterized by the Br / Bm ratio of the residual induction on an induction measured in the saturation approach zone. If Br / Bm ⁇ 0.3 the linearity becomes exploitable in these specific applications with magnetic cores without localized air gap.
• the alloys according to the invention make it possible to achieve all of these properties.
• the composition adapted to these applications is also suitable for the manufacture of magneto-harmonic sensors.
• a material with high permeability and low coercive field is subjected to the magnetic polarization greater or less of a semi-remanent magnetic material; the magnetization state of the latter (magnetized, demagnetized or partially magnetized) corresponds to an information or an alarm which is transmitted to the soft material through the polarization thereof.
• the soft material is excited at medium frequency by an external magnetic field, producing no, little or much of the fundamental harmonic emitted according to whether the soft material was subjected to respectively a semi-remanent demagnetized, partially magnetized or magnetized.
• the detected harmonic amplitude is the image of the polarization level of the semi-remnant.
• this device is slipped in the magnetic state in the jacket of each book stored.
• the book is saved and at the same time demagnetized to pass safely the security portal (no harmonic emission). If the book has not been demagnetized by the specific equipment, the high rate of harmonic emission triggers the start of the warning signal when passing to the output under the detection portal.
• To react dynamically to such pulses requires a large magnetization dynamic ie a high electrical resistivity, a very small band thickness typically less than 50 .mu.m, and preferably less than 30 .mu.m, and a low coercive field, typically Hc less than 63 mOe, and preferably less than 25 mOe.
• the coercive field also controls the 1st order the sensitivity of the magneto-harmonic sensor and will trigger it for a distance from the excitation antenna all the greater as Hc is weak.
• the coercive field is the most restrictive property for the compositional field which will have to be limited in copper for this reason.
• a material adapted to these applications must have the following characteristics: - Hc ⁇ 63 m ⁇ e (preferably ⁇ 25 mOe) both to have a good sensitivity of the sensor to the field of excitation medium frequency and to limit the dynamic hysteresis (thus to promote the dynamics of magnetization) - Resistivity electric r e ⁇ > 60 ⁇ .cm (preferably r e ⁇ > 80 ⁇ .cm) to have a good dynamic response to the external excitation medium frequency.
• the alloys according to the invention make it possible to achieve all of these properties.
• the alloy may further be such that:
• This composition is particularly suitable for the manufacture of electromagnetic motors and actuators.
• an aptitude is sought for obtaining good magnetic performances under any type of non-oxidizing industrial atmosphere such as neutral gas, He, H2, N2, NH3, etc., which then makes it necessary to reduce the Titanium content as much as possible, preferably ⁇ 30 ppm, preferably ⁇ 20 ppm.
• the electromagnetic motors and actuators that can be manufactured according to the invention have a medium to high power density, a high precision of movement, a low dissipation and a low cost.
• This application will include all non-polarized electromagnetic devices comprising a moving part (rotor for a rotary system, motor, alternator, synchro-resolver, reluctant torque sensor, motor-wheel, etc., pallet or core for systems in translation tq engine linear, solenoid valve, injector, impulsive linear actuator type camless etc ..) made of soft magnetic material with high electrical resistivity and low magnetic losses, and a static part comprising a magnetic magnetic material.
• the magnetic yokes can be made by stacking cut pieces at relatively low thicknesses.
• the alloy has an isotropy the best possible of its magnetic performance because otherwise it introduces oscillations of torque depending on the pitch (motors case) ), magnetic reluctance fluctuations as a function of the position of the moving part (in the case of the resolver-sync, the reluctant torque sensor, etc.).
• the problem is solved either by using rolling-annealing sequences that do not develop a crystallographic texture, or by developing a "planar" type texture, for example ⁇ 100 ⁇ ⁇ 0vw> or ⁇ 111 ⁇ ⁇ uvw>.
• non-polarized electromagnetic safety actuator device such as those used to prevent domestic gas leakage on gas heating systems (eg water heaters)
• low inrush currents are required and triggering of the device (and a small difference between these currents) which necessarily pass through weak coercive fields (see above) and low gaps between magnetic yoke and movable core of the actuator, but also by a low remanence to ensure release even with very small air gaps, to reduce the difference in switching and tripping currents, to reduce the dispersion of production performance of the device.
• EyBm application 3x ⁇ 0.5 and preferably ⁇ 0.3 B max induction for a magnetic field at least equal to 3H C ).
• the alloy may further be such that:
• This composition is more particularly suited to the manufacture of stators for clockwork engines, in particular of the step-by-step type.
• an aptitude is sought for obtaining good magnetic performances under any type of non-oxidizing industrial atmosphere such as neutral gas, He, H2, N2, NH3, etc., which then forces the content to be reduced as much as possible.
• Titanium preferably ⁇ 30 ppm, preferably ⁇ 20 ppm.
• alloys are sought at a low cost while satisfying a certain number of properties.
• a good cutability of the alloy strip is sought by punching, stamping or any other suitable method, allowing a low tool wear and a high rate of cutting.
• the metal is delivered by the producer to the hardened or softened state in order to maintain sufficient mechanical hardness of the metal conducive to the cutability by stamping and high speed. Yet this hardness is not enough to achieve cutting hundreds of thousands of stator parts without significant burrs and without using the cutting die and especially the cutting punch to the point of re-sharpening or replacing it. To achieve this, it is also necessary to insert into the metal some fine inclusional distributions playing the role of "cut along the dotted line" during the process of cutting between punch and die.
• the alloys according to the invention intended for this application incorporate from 8 to 40 ppm of S, Se 1 Sb and / or from 2 to 20 ppm and / or from 10 to 150 ppm of Ca, Mg.
• the alloy must have an electrical resistivity of more than 70 .mu.m, and preferably greater than 80. ⁇ .cm and a low coercive field Hc less than 125 mOe and preferably less than 75 mOe before mounting in the watch.
• the power consumption of the watch should not increase significantly when the ambient temperature increases. Indeed, if the working magnetization decreases significantly when the temperature increases, then to always provide the minimum torque for the rotation of a half-turn of the rotor, the energy generator must provide much more energy to maintain the magnetization level of the stator and thus the motor torque applying to the rotor. Thus in the case of use of the watch in a hot atmosphere, the consumption will increase significantly.
• the saturation magnetization Js remains stable in the potential operating range of the watch, namely from -40 ° C. to + 60 ° C., such a characteristic is systematically obtained when the Curie point of the Tc alloy is greater than or equal to 100 ° C.
• the requirement of resistance to acid corrosion will be higher or lower. Indeed, the life of the watch does not exceed the time of significant degradation of the alloy of the stator by atmospheric corrosion. If it is a quality watchmaking engine entering renowned manufacturing areas such as "Swiss-made” or “Japan-made”, the watch is made to last a few years and the alloy watch must not corrode significantly in this period of time. If it is a high-end watchmaking engine or transparent watch including visible engine parts, it should in principle operate without problems during the life of a person.
• the different levels of resistance to corrosion can then be evaluated according to:
• the alloy may further be such that:
• This composition is more particularly suited to the manufacture of inductors or transformers for power electronics.
• the magnetic circuits of the passive magnetic components used in power electronics or in any other medium-frequency energy conversion system require the use of smoothing inductance or transformers which constitute often large parts of the power supplies.
• a good passive magnetic component magnetic core type storage inductor or smoothing, or power transformer must first have a high saturation induction at operating temperatures, which are typically around 100-120 0 C. and search a saturation induction Bs 100 ° C greater than or equal to 4000G, which corresponds to a saturation induction at 2O 0 C, Bs 20 ° c which is greater than 8000G or else at a Curie point Tc of greater than or equal to 150 ° C.
• the residual losses of the alloys according to the invention can be compensated for by a much better ability to extract these losses due to the high thermal conduction of metal alloys and the very high fitness to shape and work of these yokes very ductile magnets and to easily install cooling circuits or give a complex shape to the magnetic circuit.
• the alloy may further be such that:
• This composition is more particularly suitable for the manufacture of bimetallic strips.
• a temperature variation can be transformed either in deformation of the bimetallic strip, or in elevation of the end of the bimetallic strip, the other end being held in position, or in force exerted by the free end of bimetal, thanks to the close connection of two materials in the form of a narrow and flat strip of different dilatabilities.
• the bimetallic pieces can serve both as an overcurrent sensor through the electrical resistivity of the multilayer material and its deflection, temperature sensor through the deflection of the bimetal which then cuts an electrical circuit or thermomechanical actuator to through the force generated by the unbalanced expansion of the different components of bimetallic.
• the bimetallic action passes through its deflection whose amplitude is proportional to the difference in expansion between the two external components of the bimetallic strip.
• the sensitivity of the bimetallic actuator will be all the greater as the expansion gap will be large for given band thicknesses and a given temperature difference.
• the electrical resistivity p e ⁇ Another important quantity when the heat source comes from the electric current flowing through the bimetallic strip, is the electrical resistivity p e ⁇ .
• a bimetallic having a high average electrical resistivity will heat much more and will rise to a higher temperature than a bimetallic low electrical resistivity. This will result in either an arrow or deflection amplitude bimetallic in the same ratio, or a bimetallic-actuator force in the same ratios.
• the electrical resistivity is inversely proportional to the thermal conductivity, which in turn ensures the uniformization of the temperature and thus ensures the dynamics of the bimetallic response.
• a third metal layer such as copper or nickel between the low and high dilatability layers allows different resistivity / conductivity trade-offs to be set without changing the dilatabilities.
• the alloy may further be such that:
• This composition is more particularly adapted to the manufacture of watch motor coil cores or electromagnetic relays with high sensitivity.
• an aptitude is sought to obtain the good magnetic performances under any type of non-oxidizing industrial atmosphere such as neutral gas, He, H2, N2, NH3, etc., which then forces to reduce as much as possible the titanium content.
• any type of non-oxidizing industrial atmosphere such as neutral gas, He, H2, N2, NH3, etc., which then forces to reduce as much as possible the titanium content.
• neutral gas He, H2, N2, NH3, etc.
• the magnetic field intended to magnetize the clock magnetic circuit must be produced with the minimum of electric current, that is to say with the maximum of turns of the excitation coil, this which results in the use of a very fine wire and magnetic core with a high magnetic flux to reduce the section of the core and to place a coil as large as possible.
• the magnetic alloy of the core must therefore necessarily offer a high magnetic saturation since the magnetic flux is the product of the magnetization by the section of the material. Alloys having a saturation induction Bs at 20 ° C. which is greater than 10 000 G are therefore sought.
• the alloy must also offer a low coercive field Hc and a high electrical resistivity to reduce magnetic losses, and thus limit the power consumption of the watch. Therefore, alloys having a coercive field Hc at 20 ° C. which is less than 125 mOe and preferably less than 75 mOe and an electrical resistivity ⁇ e ⁇ that is greater than 60 ⁇ .cm and preferably greater than 80 ⁇ .cm are sought.
• the alloys according to the invention intended for this application preferably have good cutability and can therefore optionally incorporate from 8 to 40ppm of S, Se, Sb and / or from 2 to 20ppm and / or from 10 to 150 ppm of Ca, Mg.
• the alloys according to the invention make it possible to achieve all of these properties.
• the alloys according to the invention have a saturation induction Bs greater than 13 000G and their composition must then comply with equation 9:
• compositions suitable for the manufacture of clockwork motor cores are also suitable for the manufacture of high sensitivity electromagnetic relays.
• An electromagnetic relay is a mechanical actuator with electrical control, where a generally massive magnetic yoke for reasons of ease and low cost of production / shaping, is closed by a piece of material and tilts on a breech leg end.
• the rocking position between "open” and “closed” results from the equilibrium between a mechanical force of return of a spring (placed outside the cylinder head and tending to open the magnetic circuit by rotating the mobile pallet around of the breech leg) and an electromagnetic force formed at rest of the sole magnetic attraction force of the magnetized yoke by a magnet on the pallet. At rest, the pallet closes the breech.
• a winding surrounds a leg of the cylinder head so that if an electric current from an external event and to be converted into a mechanical signal passes through it, there is added a magnetic force of repulsion of the pallet with respect to the cylinder head, which decreases the amplitude of the magnetic attraction force.
• the repulsive force can reach a level sufficient for the action of the spring to prevail by opening the relay and actuating a mechanical system. It is on this principle that electrical circuit breakers operate in particular.
• a minimum resistance to corrosion is required because the relays are often protected by non-hermetic packages, allowing the potentially hot, humid, oxidizing environment (Cl, S, etc.) to pass through the atmosphere while the non-oxidized state metal during its operation for years is important to ensure the reproducibility of trigger conditions by the non-drift of its magnetic performance.
• the ox max must remain below 5 mA and preferably below 3 mA, or even below 1 mA.
• the alloy may further be such that:
• This composition is more particularly suitable for the manufacture of temperature measuring devices or marking temperature overruns, without contact.
• Magnetic parts of non-contact temperature measurement labels use at the same time very different materials, such as magnetically soft materials ("the alloy”) and permanent magnet magnetic materials (MAP) in a stabilized configuration of temperature and magnetic fields surrounding.
• This temperature monitoring is, by the very principle of the label, carried out in the temperature range immediately below and around the Curie point of the soft magnetic alloy. In this application, it is possible, for example, to use a plate of
• MAP section S1 secured to a plate of very high permeability material of section S 2 , such as a thin FeNi alloy or an amorphous alloy, leaving a small air gap d between the two materials.
• the MAP material acts as a magnetic polarizer of the adjacent magnetically soft material.
• a third plate consisting of an alloy according to invention having a Curie point Tc.
• the ambient temperature approaches the Curie point Tc of the alloy according to the invention, it is less magnetized and the magnetic flux of the MAP closes for a larger part on the high-grade material.
• permeability which is polarized at a level of increasing magnetization and dependent on the ratio T / Tc.
• the functional Curie point which is sought is between -50 ° C. and 400 ° C., and in particular between -30 ° C. and + 100 ° C. for many applications for monitoring the temperature of edible products such as the cold chain.
• This Curie point is limited to a maximum of 400 ° C. and is preferably between -30 ° C. and 100 ° C.
• a sufficiently weak coercive field ( ⁇ 75 mOe, and preferably ⁇ 32.5 mOe) is required to obtain, on the one hand, a high sensitivity of the sensor to the medium-frequency excitation field, and on the other hand, a high dynamic range.
• the sensor by association with a high electrical resistivity (> ⁇ O ⁇ .cm, and preferably> ⁇ O ⁇ .cm) and preferably a small thickness of material. This restriction to low coercive fields makes it necessary to limit the percentage of copper to 10% maximum and preferably less than 6% in combination with a maximum nickel content of 34%.
• the alloys according to the invention make it possible to achieve all of these properties.
• the alloy may further be such that: Mn ⁇ 2%
• the alloy also satisfies at least one of the following relationships:
• niobium and / or zirconium It is further preferred to add 0.003 to 0.5% niobium and / or zirconium.
• compositions are more particularly suitable for the manufacture of hyper-textured substrates for epitaxy.
• One-component texture is not a non-random distribution of the crystallographic orientations of the poly-crystal, so that they are all located in a solid angle (from half-angle to the vertex ⁇ ) surrounding the ideal target orientation, noted [ hkl] (uvw) in Miller index, ⁇ is called average texture disorientation and can have different values depending on whether it is measured in the rolling plane or out of the plane.
• These deposited materials have particular physical properties, such as, for example, the superconductivity of Y-Ba-Cu-O type oxides. These properties are greatly improved by low density defects at the grain boundaries, which pass through small disorientations between adjacent crystals (role of an acute texture) and by a grain size of the order of a few tens of microns to reduce the density of defects with disorientation of identical texture.
• one of the widely used methods is the epitaxial technique from a vapor or liquid phase, on a substrate itself which is hyper-textured with a mesh parameter fairly close to that of the deposited product.
• hyper-textured substrates are mainly including the presence of a surface fraction of twinning and other different orientations orientations centered within 15th disorientation of cubic ideal orientation [10O] (OOI ), preferably less than 10%, and preferably less than 5% and a disorientation ⁇ of the main cubic texture component ⁇ 100 ⁇ ⁇ 001>: less than 10 ° and preferably less than 7 °.
• OOI cubic ideal orientation
• Hc coercive field at 20 ° C., measured in mOe.
• L ox maximum current at imposed potential, measured in mA
• Br / Bm ratio of the Br residual induction on the induction measured in the approach zone at saturation
• Bm B 0C20-100 average coefficient of expansion (also called “dilatability") of the material, measured between 20 and 100 ° C and expressed in 10 ⁇ / 0 C and 0C20-300: average coefficient of expansion of the material, measured between 20 and 300 0 C and expressed in 10 "6 / ° C and ⁇ 20- 77 ⁇ : average coefficient of expansion of the material, measured between 77K and 20 0 C expressed in 10 ' 6 / ° C.
• the annealed metal is first annealed at a thickness of 0.6 mm, at a temperature of 1100 ° C., for 3 hours under pure hydrogen and water vapor such that the dew point is -30 ° C. (simulation of an industrial annealing). Two sheets thus annealed are then stacked under a uniformly distributed mass giving a pressure equivalent to 1 kg for 10 cm 2 . We then make 100 forward and backward sliding up to one half length of one sheet relative to the other then we observe the wear of the surfaces noted with 3 levels of wear resistance after examination of the surface of the metal:
• Corrosion resistance of alloys in corrosive atmospheric media or in acidic aqueous media can be evaluated by measuring the maximum current obtained when immersing an alloy sample-plate in a bath of sulfuric acid 0.01 M and the alloy being connected by a conductor to another electrode-platinum plate, applying different voltage values. Different intensity values I are thus measured on the conductor connecting the two electrodes and the maximum value l ox ma ⁇ of I (U) is then determined.
• alloys were developed to a final thickness of 0.6 mm to characterize the properties of use.
• the alloys are made from 99.9% pure materials, melted in a vacuum induction furnace to a 50kg ingot.
• the ingot is forged between 1100 and 1300 0 C, then hot rolled to a thickness of 2.5 mm, between 1000 and 1200 0 C and then etched chemically.
• the strip is then cold rolled from the thickness of hot rolled to the thickness of 0.6mm, then annealed between 800 and
• a series of tests are carried out to determine salt spray corrosion resistance, mechanical wear resistance, saturation induction, Curie point, acid corrosion resistance and dilatability values between 20 and 20. 100 0 C.
• part of the alloys according to the invention contains less than
• Example SV298-1 It is also seen in Example SV298-1 that high dilatabilities can be obtained between 20 and 100 ° C. (11.10 ° 6 ° C. in the example) by regulating the Ni, Cr and Cu contents adequately and no more than 30% Ni. The choice of composition adjusts the Curie point at the same time.
• alloys were developed to a final thickness of 0.6 mm to characterize the properties of use. Alloys are made from 99.9% pure materials, melted in a vacuum induction furnace 50kg. The ingot is forged between 1100 and 1300 0 C 1 and then hot rolled to a thickness of 2.5 mm, between 1000 and 1200 0 C and then etched chemically. The strip is then cold rolled from the thickness of hot rolled to the thickness of 0.6 mm, then annealed between 800 and 1100 0 C for 1 hour, then degreased, cut into different pieces or washers for measurements then annealed at 1100 ° C / 3h under purified H2 (dew point ⁇ -70 ° C).
• the shades tested include the elements mentioned in the following table, the balance being iron and unavoidable impurities.
• a series of tests are carried out to determine salt spray corrosion resistance, mechanical wear resistance, saturation induction, Curie point, acid corrosion resistance and dilatability values between 20 and 20. 100 0 C.
• alloys were developed to a final thickness of 0.6 mm to characterize the properties of use.
• the alloys are made from 99.9% pure materials, melted in a vacuum induction furnace to a 50kg ingot.
• the ingot is forged between 1100 and 1300 0 C, then hot rolled to a thickness of 2.5 mm, between 1000 and 1200 0 C and then etched chemically.
• the strip is then cold rolled from the thickness of hot rolled to the thickness of 0.6mm, then annealed between 800 and
• the dilatability measurements are carried out on a "Chevenard dilatometer" between -196 ° C. and 800 ° C.
• the shades tested include the elements mentioned in the following table, the balance being iron and unavoidable impurities.
• a series of tests are carried out to determine the resistance values to salt spray corrosion, resistance to mechanical wear, Curie point, resistance to acid corrosion and dilatability between 20 and 100 ° C. and between 20 and 100 ° C. and 300 ° C.
• Example 36 compared to Invar®, it appears that substitute 3.5% Ni by 4% Cu and low levels of Si and Cr can maintain a dilatancy of less than 3.10 "6 Z 0 C between 20 and 100 0 C, which is sufficient for many applications requiring to limit both the cost and the expansion towards the ambient as the shadow masks of the screens of cathode-ray tubes with high definition, the actuator supports of piezoelectric fuel automobile injector, the solid molds of aeronautical parts in carbon fiber and others, and also requiring that the material oxidizes little industrial annealing in a very weakly reducing atmosphere or even in an oxidizing atmosphere, and avoids using a protective gas atmosphere, thus simplifying the industrial implementation.
• alloys have been developed to the final thickness of 0.6 mm to characterize the properties of use.
• the alloys are made from 99.9% pure materials, melted in a vacuum induction furnace to a 50kg ingot.
• the ingot is forged between 1100 and 1300 0 C, then hot rolled to a thickness of 2.5 mm, between 1000 and 1200 0 C and then etched chemically.
• the strip is then cold rolled without intermediate annealing from the thickness of hot rolled to the thickness of 0.6 mm, then cut into different pieces or washers for measurements (see previously the different types of characterization used) before degreasing then annealed at 1100 ° C. for 3 hours under purified H2 (dew point ⁇ -70 ° C.).
• the shades tested include the elements mentioned in the following table, the balance being iron and unavoidable impurities.
• a series of tests are carried out to determine the values of resistance to salt spray corrosion, resistance to mechanical wear, saturation induction at 20 ° C., rectangularity of the hysteresis cycle to 2O 0 C, coercive field at 20 0 C 1 of electrical resistivity at 20 0 C and acid corrosion resistance.
• alloys with more than 10% Cu have very high coercive fields of 200 to 40OmOe incompatible with a measurement transformer type application.
• the alloy SV330-4 is particularly economical with its 28% Ni and 3% Cu, with a very low Hc of 19mOe allowing a high accuracy of the transformer of measurement, on the other hand its low saturation (4430G) restricts it to applications towards the ambient temperature.
• the SV317-5 alloy with high saturation (11540G) and low coercive field (34mOe) allows the realization of open loop current sensor of high precision, and economically (34% Ni) while ensuring good resistance to corrosion in many environments thanks to the conjunction of 2% Cr and 4% Cu associated with silicon.
• alloys have been developed up to a final thickness of 0.04 mm in order to characterize the properties of use.
• the alloys are made from 99.9% pure materials, melted in a vacuum induction furnace to a 50kg ingot.
• the ingot is forged between 1100 and 1300 0 C 1 and then hot rolled to a thickness of 2.5 mm, between 1000 and 1200 0 C and then etched chemically.
• the strip is then cold rolled from the thickness of hot rolled to the thickness of 0.6 mm, then annealed between 800 and 1100 0 C for 1 hour, then rolled to the final thickness of 40 .mu.m and then degreased, cut into different pieces or cores wound for measurement then annealed at 1100 0 C for 3 hours under purified H2 (dew point ⁇ -70 ° C.).
• the shades tested include the elements mentioned in the following table, the balance being iron and unavoidable impurities.
• a series of tests are carried out to determine the values of resistance to salt spray corrosion, resistance to mechanical wear, saturation induction at 20 0 C, coercive field at 2O 0 C, electrical resistivity at 20 0 C and acid corrosion resistance.
• alloys have been developed to the final thickness of 0.6 mm to characterize the properties of use.
• the alloys are made from 99.9% pure materials, melted in a vacuum induction furnace to a 50kg ingot.
• the ingot is forged between 1100 and 1300 ° C, then hot rolled to a thickness of 2.5 mm, between 1000 and 1200 0 C and chemically etched.
• the strip is then cold rolled without intermediate annealing since the laminate thickness to warm up the thickness of 0.6mm, and cut into various pieces or washers for measurements before degreasing and then annealed at 1100 0 C for 3 hours with purified H 2 (dew point ⁇ - 7O 0 VS).
• the shades tested include the elements mentioned in the following table, the balance being iron and unavoidable impurities.
• a series of tests are carried out to determine the values of resistance to salt spray corrosion, resistance to mechanical wear, saturation induction at 20 ° C., coercive field at 20 ° C., electrical resistivity at 20 ° C. 0 C and resistance to acid corrosion.
• the SV292-4mod alloy does not check the equation 2, which results in too low saturation (4800G) related to an insufficient% Cu with respect to the nickel content.
• the alloy SV304-2mod does not verify the invention since its saturation is much too low (4080G instead of the minimum of 5000G), which is due to its too high manganese content.
• TD560-8 alloy has 35% Ni and high saturation. Its permeability ⁇ max was measured along the 0 °, 45 ° and 90 ° directions with respect to the rolling direction. We obtain respectively 19000, 17200 and 17600, which shows that the alloy is almost perfectly isotropic thanks to the succession of high rolling and final annealing at high temperature. By this property the magnetic flux will circulate isotropically and will not favor certain directions of the sheet, frequent origin of fluctuation of electromagnetic torque in the electrical machines.
• the alloys according to the invention therefore also have the property, through cold rolling and appropriate annealing, to be able to present if necessary a good isotropy of the magnetic properties.
• the alloys according to the invention have a low remanence (rectangularity of the hysteresis cycle Br / Bm ⁇ 0.3) which allows either to demagnetize largely naturally as soon as the excitation is cut off (“defluxing "Natural"), or not to be sensitive to disturbing parasitic fields (superimposed fields, very strong and very fugitive overcurrent that saturates the material for a very short time). It is noted in particular that it is advantageous to lower the% nickel and the chromium to lower the rectangularity Br / Bm to very low values such as 0.17 on alloys TD560-1, 3 and 5 containing a minimum of% Cr, 28 to 32% Ni and 10% Cu.
• Example 7 Stators for watch engines Several alloys were developed up to the final thickness of 0.6 mm in order to characterize the properties of use.
• the alloys are made from 99.9% pure materials, melted in a vacuum induction furnace to a 50kg ingot.
• the ingot is forged between 1100 and 1300 0 C, then hot rolled to a thickness of 2.5 mm, between 1000 and 1200 0 C and then etched chemically.
• the strip is then cold rolled without intermediate annealing from the thickness of hot rolled to the thickness of 0.6 mm, then cut into different parts or washers for measurements before degreasing and then annealed at 1100 0 C for 3 hours under Purified H2 (dew point ⁇ -70 ° C).
• the shades tested include the elements mentioned in the following table, the balance being iron and unavoidable impurities.
• the Curie point is determined by a round trip of the thermomagnetometer to a temperature of 800 ° C.
• Example 8 Inductance and transformer for power electronics Several alloys were developed up to a final thickness of 0.6 mm to characterize the properties of use. The alloys are made from 99.9% pure materials, melted in a vacuum induction furnace to a 50kg ingot. The ingot is forged between 1100 and 1300 0 C, then hot rolled to a thickness of 2.5 mm, between 1000 and 1200 0 C and then etched chemically.
• the strip is then cold rolled from the thickness of hot rolled to the thickness of 0.6 mm, then annealed at 800 to 1100 0 C for 1 hour, then degreased, cold rolled to the thickness 0.05mm, sheared, coated with a mineral insulator to avoid the bonding of the sires during the annealing and wound into torus diameters 30x20mm, height 20mm, then annealed at 1100 ° C / 3h under purified H2 (dew point ⁇ - 70 ° C).
• the shades tested include the elements mentioned in the following table, the balance being iron and unavoidable impurities.
• all the alloys according to the invention have at least 80 ⁇ .cm electrical resistivity at 20 ° C and a coercive force of less than 75mOe, and generally less than 41mOe at 20c C: these performance combined with low Thickness and good inter-turn insulation guarantee low magnetic losses, all the more permissible in these magnetic cores of passive magnetic components that their good thermal conduction makes it possible to easily extract these magnetic losses.
• Example 9 - Bilames Several alloys were developed up to the final thickness of 0.6 mm in order to characterize the properties of use.
• the alloys are made from 99.9% pure materials, melted in a vacuum induction furnace to a 50kg ingot.
• the ingot is forged between 1100 and 1300 0 C, then hot rolled to a thickness of 2.5 mm, between 1000 and 1200 0 C and then etched chemically.
• the strip is then cold rolled to a thickness of 0.6 mm, then annealed at 800 to 1100 ° C. for 1 hour, then degreased, cut into different pieces or washers for measurements and then annealed at 1100 ° C. for 3 hours under purified H2. (dew point ⁇ -70 ° C).
• the shades tested include the elements mentioned in the following table, the balance being iron and unavoidable impurities.
• a series of tests is carried out to determine the values of resistance to salt spray corrosion, resistance to mechanical wear, Curie point, electrical resistivity at 20 ° C., coefficient of expansion between 20 and 200 ° C. and between 20 and 300 ° C.
• Example 10 Cores of clockwork motor coils and electromagnetic relay with high sensitivity
• alloys have been developed to the final thickness of 0.6 mm to characterize the properties of use.
• the alloys are made from 99.9% pure materials, melted in a vacuum induction furnace to a 50kg ingot.
• the ingot is forged between 1100 and 1300 0 C, then hot rolled to a thickness of 2.5 mm, between 1000 and 1200 0 C and then etched chemically.
• the strip is then cold rolled without intermediate annealing from the thickness of hot rolled to the thickness of 0.6 mm, then cut into different parts or washers for measurements before degreasing and then annealed at 1100 0 C for 3 hours under Purified H2 (dew point ⁇ -70 ° C).
• the shades tested include the elements mentioned in the following table, the balance being iron and unavoidable impurities.
• Example 11 Devices for measuring temperature and temperature-limiting marking, without contact
• alloys were developed to a final thickness of 0.6 mm to characterize the properties of use.
• the alloys are made from 99.9% pure materials, melted in a vacuum induction furnace to a 50kg ingot.
• the ingot is forged between 1100 and 1300 0 C, then hot rolled to a thickness of 2.5 mm, between 1000 and 1200 0 C and then etched chemically.
• the strip is then cold rolled from the thickness of hot rolled to the thickness of 0.6 mm, then annealed between 800 and 1100 0 C for 1 hour, then degreased, cut into different parts or washers for measurements ( see previously the different types of characterization used) and then annealed at 1100 ° C. for 3 hours under purified H2 (dew point ⁇ -70 ° C.).
• the shades tested include the elements mentioned in the following table, the balance being iron and unavoidable impurities.
• a series of tests are carried out to determine the values of resistance to salt spray corrosion, resistance to mechanical wear, saturation induction at 20 ° C., Curie point, coercive field at 20 ° C. and resistance to acid corrosion.
• Example 12 Hyper-textured Substrates for Epitaxy
• the alloys have been developed up to the final thickness of 0.1 mm in order to characterize their properties of use.
• the alloys are made from 99.9% pure materials, melted in a vacuum induction furnace to a 50kg ingot.
• the ingot is forged between 1100 and 1300 0 C, then hot rolled to a thickness of 5mm, between 1000 and 1200 0 C and chemically etched.
• the strip is then cold rolled to a thickness of 0.1 mm without intermediate annealing, and then mechanically polished with abrasive polishing felt to a very fine polishing grain of the order of one micron.
• the metal is then annealed between 800 and 1100 0 C for 1 hour, then cut into different pieces for measurements of pole figures by RX to evaluate the type and intensity of the texture obtained.
• the shades tested include the elements mentioned in the following table, the balance being iron and unavoidable impurities.
• a series of tests are carried out to determine the values of resistance to salt spray corrosion, resistance to mechanical wear, Curie point, resistance to acid corrosion, dilatability between 20 and 300 ° C., rate of of twinning and mean texture disorientation.
• the alloys according to the invention have a high ability to cubic texturing ⁇ 100] ⁇ 001> with a low macle level ( ⁇ 10%) and a low texture average misorientation ⁇ ( ⁇ 10 °), a strong resistance to mechanical wear of the oxidized layer in a degraded operating or annealing atmosphere by the addition of minimum levels of Cr, Si and Cu, and variable dilatabilities in a wide range to meet most needs of substrate deposition dilation for epitaxy.

Priority Applications (1)

Applications Claiming Priority (3)

Publications (2)

Family

ID=38374659

Family Applications (2)

Family Applications Before (1)

Country Status (11)

Families Citing this family (35)

Family Cites Families (13)

• 2007
  • 2007-03-30 EP EP07290382A patent/EP1975269A1/de not_active Withdrawn
• 2008
  • 2008-03-26 EP EP08787849.2A patent/EP2129808B1/de active Active
  • 2008-03-26 JP JP2010500315A patent/JP5840361B2/ja active Active
  • 2008-03-26 RU RU2009140089/02A patent/RU2456366C2/ru active
  • 2008-03-26 US US12/593,726 patent/US20100102910A1/en not_active Abandoned
  • 2008-03-26 CA CA2682233A patent/CA2682233C/fr active Active
  • 2008-03-26 KR KR1020097022683A patent/KR101835139B1/ko active IP Right Grant
  • 2008-03-26 WO PCT/FR2008/000403 patent/WO2008142229A2/fr active Application Filing
  • 2008-03-26 CN CN2008800169385A patent/CN101680070B/zh active Active
  • 2008-03-26 ES ES08787849.2T patent/ES2672020T3/es active Active
  • 2008-03-26 MX MX2009010504A patent/MX2009010504A/es active IP Right Grant
  • 2008-03-26 BR BRPI0809850-6A patent/BRPI0809850A2/pt not_active Application Discontinuation
• 2014
  • 2014-07-24 JP JP2014150931A patent/JP2015007287A/ja not_active Withdrawn

Non-Patent Citations (1)

Also Published As

Similar Documents

Legal Events