EP1281182B1 - Eisen-kobalt-legierung insbesondere für elektromagnetischen aktuator mit beweglichem kernteil und herstellungsverfahren - Google Patents

Eisen-kobalt-legierung insbesondere für elektromagnetischen aktuator mit beweglichem kernteil und herstellungsverfahren Download PDF

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EP1281182B1
EP1281182B1 EP01934103A EP01934103A EP1281182B1 EP 1281182 B1 EP1281182 B1 EP 1281182B1 EP 01934103 A EP01934103 A EP 01934103A EP 01934103 A EP01934103 A EP 01934103A EP 1281182 B1 EP1281182 B1 EP 1281182B1
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Prior art keywords
iron
traces
cobalt alloy
contents
sum
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French (fr)
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EP1281182A1 (de
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Thierry Waeckerle
Lucien Coutu
Marc Leroy
Laurent Chaput
Hervé FRAISSE
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Aperam Alloys Imphy SAS
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ArcelorMittal Stainless and Nickel Alloys SA
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • 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
    • C22C38/10—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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

Definitions

  • the invention relates to the field of magnetic iron-cobalt alloys. More specifically, it relates to iron-cobalt alloys intended to constitute electromagnetic actuator cores.
  • An electromagnetic actuator is an electromagnetic device that converts electrical energy into mechanical energy. Some actuators of this type are so-called linear actuators, converting electrical energy into a rectilinear movement of a moving part. Such actuators are found in solenoid valves and electro-injectors. A preferred application of such electro-injectors is the direct injection of fuel into combustion engines, especially diesel engines. Another preferred application relates to a particular type of solenoid valve used for the electromagnetic control of valves of internal combustion engines (gasoline or diesel).
  • the electrical energy is supplied in a winding by a series of current pulses, creating a magnetic field that magnetizes a non-closed magnetic yoke, thus having a gap.
  • the geometric characteristics of the cylinder head make it possible to direct most of the magnetic field lines axially vis-à-vis the gap zone.
  • the air gap is subjected to a magnetic potential difference.
  • the actuator also comprises a core made mobile by the action of the electric current in the coil. Indeed, the magnetic potential difference introduced by the coil between the mobile core resting on a pole of the cylinder head and the opposite pole of the cylinder head creates an electromagnetic force on the magnetized core, via a magnetic field gradient.
  • the magnetized core is thus set in motion.
  • the rest position can also be located in the middle of the air gap, thanks to two symmetrical springs, favoring by their stiffness the dynamics of the moving part (case of the electromagnetically controlled valves).
  • the movement of the mobile core occurs with a phase shift with respect to the moment of creation of the electrical pulses.
  • the metal that composes it it is shown that it is necessary for the metal that composes it to have high electrical resistivity and a low coercive field. These conditions make it possible to obtain low currents induced in the cylinder head and the magnetic core, making it possible to quickly reach the minimum magnetization of the nucleus which causes it to move.
  • the core has a high saturation magnetization so as to allow as high a maximum pulse force as possible. It is indeed this force which guarantees the maintenance of the open or closed position of the actuator, which is particularly important when it comes, for example, to completely interrupt the flow of a fluid at a high level. pressure, and / or to compensate for the restoring force of one or more springs.
  • These magnetic cores have various shapes and can be made from wires or bars. In this case, they must have a high plastic aptitude for deformation, so that they can be deformed without risk of rupture. It is favorable to have an elongation at break of the material of at least 35%.
  • Such cores can also be manufactured by cutting plates or rolled sheets. In this case, they must have a high punching ability, for which minimum hardness and strength are required. A good resistance of the magnetic properties to repeated mechanical shocks to which the core will be subjected is also necessary. These characteristics of hardness and mechanical strength are also favorable to a good efficiency of the cutting of the core. It is recommended to have a material hardness after annealing greater than 200 HV for these uses.
  • a first category consists of iron-silicon alloys comprising from 2 to 3% of silicon. They have the advantage of having relatively high resistivities. On the other hand, their saturation magnetization is relatively low.
  • a second category consists of iron-cobalt alloys with a high cobalt content, of the order of 50%. Such alloys have a significantly higher saturation magnetization higher than that of previous iron-silicon alloys. On the other hand, their resistivity is somewhat lower. In addition, because of the massive presence of cobalt, these alloys are very expensive. Finally, their mechanical properties are not optimal, which makes the manufacture of the cores difficult.
  • a third category consists of iron-cobalt alloys containing about 6 to 30% cobalt and various other alloying elements.
  • the document EP-A-715,320 give an example of such alloys. It describes iron-cobalt alloys for electromagnetic actuator cores comprising 6 to 30% cobalt, 3 to 8% of one or more elements selected from chromium, molybdenum, vanadium and tungsten, the balance being iron .
  • the cobalt content is from 10 to 20% and the content of chromium, molybdenum, vanadium and / or tungsten is from 4 to 8%.
  • alloys have a good electrical resistivity, which may be greater than 50 ⁇ .cm, but their saturation magnetization is relatively low, of the order of 1.9 to 2T, except for the most heavily loaded cobalt variants (which are therefore the most expensive) where this saturation magnetization can reach 2.3 T.
  • the coercive field of the alloys given as examples in this document is also high, substantially greater than 1.5 Oe. In general, the alloys given as examples in this document do not make it possible to reach an optimal compromise between a high saturation magnetization, a low coercive field and a high resistivity.
  • the document WO 96/19001 proposes to use iron / cobalt alloys containing between 5 and 20% of cobalt, and having an aluminum and manganese or vanadium content of up to several%: up to 7% of aluminum, and up to 8% of manganese or 4% vanadium. Alloys described in this document have a very high resistivity (greater than 60 ⁇ .cm), and a fairly high saturation magnetization (from 2 to 2.2 T). But no precise information is given on the mechanical properties of these alloys, as well as on their coercive field.
  • a yoke and a core made of an iron-cobalt alloy also comprising Si, Mn, Al, Mo and V are known from JP 060933199 .
  • the object of the invention is to provide iron / cobalt alloys particularly suitable for the manufacture, economically, cores for electromagnetic actuators. These nuclei should present a more favorable compromise than the existing materials between the different electromagnetic characteristics, namely the saturation magnetization, the resistivity and the coercive field. They should also have mechanical properties making their manufacture particularly easy.
  • this iron-cobalt alloy comprises 14 to 20% of Co and the sum of the contents of Ta and Nb is between 0.05 and 0.8%.
  • the sum of the contents of Cr and V is between 1.1 and 3%, preferably between 1.5 and 3%, and the sum of the contents of Si, Al and Mo is between traces and 1% to obtain an elongation at break of at least 35%.
  • the sum of the contents of Si and Al is between 1 and 2.6%, and the sum of Cr, V, Mo, Ta, Nb content is between traces and 2% to obtain a hardness of at least 200 HV after annealing.
  • the saturation magnetization of the alloys according to the invention is at least 2.1 T at 150 ° C and at least 2.12 T at 20 ° C, their resistivity is at least 35 ⁇ .cm at 150 ° C. ° C and at least 31 ⁇ .cm at 20 ° C, their coercive field is less than 1.5 Oe at 20 and 150 ° C, and preferably less than or equal to 1 Oe.
  • the invention also relates to a bar, a wire, a plate or a rolled sheet of iron-cobalt alloy, characterized in that said alloy is of the preceding type, and in that the bar, the wire, the plate or the sheet has a preferential fiber texture of ⁇ 100> axis for a bar or wire, or a strong texture component ⁇ 100> for a rolled plate or sheet, deviated by less than 20 ° from the rolling direction at least 30% (by volume of the material) of the grains, preferably for at least 50%.
  • the subject of the invention is also a method for producing a bar, a wire, a plate or a rolled sheet of the above type, characterized in that a bar, a wire or a plate is produced. or a sheet rolled from a blank made of an alloy according to the invention by performing a rolling beginning in the austenitic phase and ending in ferritic phase, the reduction in thickness experienced by the bar, the wire, the plate or the sheet in ferritic phase being at least 30%, preferably at least 50%, and any subsequent annealing is carried out at a temperature below the austenitic transformation temperature.
  • the invention also relates to a mobile electromagnetic actuator core, characterized in that it has been manufactured from a bar or a wire or a plate or sheet rolled according to the preceding method , and an electromagnetic actuator comprising a mobile core of iron-cobalt alloy, characterized in that said core is of the above type and in that it has a preferential texture of axis ⁇ 100>, this axis being substantially parallel to the main direction of the field of excitation.
  • the invention also relates to an injector for a combustion engine controlled by electronic control comprising an electromagnetic actuator with high power density, low response time and high reliability of use of the previous type.
  • the invention finally relates to an electromagnetic valve actuator of an electronically controlled internal combustion engine, characterized in that it is of the preceding type.
  • the iron / cobalt alloy according to the invention is in the category of Fe-Co alloys with a low or medium cobalt content, and contains contents of other relatively moderate alloying elements.
  • these alloying elements must be present in respective proportions well defined. It is only in these conditions that, for these alloys and for the electromagnetic actuator cores derived therefrom, optimum properties are obtained, both magnetically and mechanically, at a cost of material (related to the presence of cobalt) very moderate compared to Fe-Co alloys at 50% cobalt.
  • the alloys according to the invention have resistivities similar to those of iron / silicon alloys containing 2 to 3% of silicon.
  • This resistivity at 150 ° C. is greater than 35 ⁇ .cm, so as to maintain good reactivity of the actuator to the stresses to which it is subjected at its operating temperature. At 20 ° C, this resistivity is greater than 31 ⁇ .cm.
  • this good responsiveness of the actuator is also due to a low coercive field, limited to 1.5 Oe at 20 and 150 ° C.
  • This low value of the coercive field is obtained according to the invention by imposing on the alloy a carbon content of less than 0.0100% and a total content of oxygen, nitrogen and sulfur limited to 70 ppm.
  • This weak coercive field strengthens the reduction of pulse time. It is also advisable, for the same purpose, to give the part from which the core will be made a preferential texture of axis ⁇ 100>, and to ensure that in the core in use, this texture preferential is found substantially parallel to the main direction of field excitation.
  • the alloys according to the invention exhibit a saturation magnetization at 150 ° C. of greater than 2.1 T. This value is quite superior to those usually observed with iron / silicon alloys containing 3% silicon. At 20 ° C., the saturation magnetization of the alloys according to the invention is greater than 2.12 T.
  • the alloys according to the invention have particularly favorable mechanical characteristics for the preparation of electromagnetic actuator cores.
  • the alloys exhibit a high plastic deformation by stamping or stamping because they have a maximum elongation at break of at least 35%.
  • these alloys are suitable for a good quality of cutting and machining, thanks to their hardness after annealing which is at least 200 HV.
  • the iron / cobalt alloys according to the invention necessarily have the following characteristics. All percentages are percentages by weight.
  • the cobalt content is between 10 and 22%, and preferably between 14 and 20%, in order to significantly increase the saturation magnetization with respect to the iron / silicon alloys, while maintaining a high resistivity.
  • the limitation to 22% of the cobalt content provides mechanical properties and a cost more favorable than in the case of iron / cobalt alloys at 50% cobalt.
  • the silicon content does not exceed 2.5%; the aluminum content does not exceed 2%; each of the contents of chromium, molybdenum and vanadium does not exceed 3%, as is the sum of their contents; the manganese content is between 0.1 and 1%, preferably between 0.1 and 0.5% to facilitate the hot conversion.
  • Each of these elements may be present only in the form of traces resulting from the elaboration.
  • the sum of the contents of silicon, aluminum, chromium, vanadium, molybdenum, manganese is between 1.1 and 3.5%, and preferably between 1.5 and 3.5%. It is in these conditions that we obtain a resistivity of the alloy equivalent to that of iron / silicon alloys containing 2 to 3% silicon.
  • the contents of these elements must verify the two following equations: 1 , 23 x al + MB % + 0 , 84 ⁇ Yes + Cr + V - 0 , 15 x Co % - 15 % ⁇ 2 , 1 to ensure that the saturation magnetization at 150 ° C is greater than or equal to 2.1T and greater than or equal to 2.12 T at 20 ° C; 14 , 5 x al + Cr % + 12 x V + MB % + 25 x Si % ⁇ 21 , preferably ⁇ 40 to ensure a resistivity greater than or equal to 35 ⁇ ohm-cm at 150 ° C and greater than or equal to 31 ⁇ .cm at 20 ° C.
  • the sum of the chromium, molybdenum and vanadium contents must be at most 3%, in order not to degrade the saturation magnetization of the material.
  • tantalum and niobium and the sum of their contents must each be less than or equal to 1%. Preferably, the sum of these contents is between 0.05 and 0.08%.
  • the purpose of tantalum is to increase the ductility of the alloy, and niobium to increase the mechanical strength and wear resistance, as well as the resistivity. The upper limit of 1% is motivated by the need not to degrade the saturation magnetization of the material. These elements can be present only in the state of traces resulting from the elaboration.
  • the carbon content must be less than or equal to 100 ppm, and the sum of the oxygen, nitrogen and sulfur contents must be less than or equal to 70 ppm. These conditions make it possible to limit the coercive field and to increase the dynamic permeability of the alloy. These elements carbon, oxygen, nitrogen and sulfur are considered as impurities and can be present only in the state of traces resulting from the elaboration.
  • Such cold stamping and stamping operations are performed on an alloy which is initially in the form of bars, wires or thick plates (at least 1 mm).
  • Table 1 gives, for examples of alloys according to the invention and alloys according to the prior art, their chemical composition, as well as the characteristics at 20 ° C. of elongation at break, of hardness after annealing, of saturation magnetization, resistivity and coercive field resulting from these compositions.
  • the 100% complement of the compositions is consisting of iron and impurities resulting from the elaboration.
  • the results of the calculation of the first members of equations (1) and (2) were also reported.
  • Reference alloy 9 is an iron / cobalt alloy with about 50% cobalt. Its magnetic characteristics are excellent, as well as its hardness which makes it suitable to be cut or machined. On the other hand, it has an extremely low elongation at break which renders it unfit to undergo large plastic deformations. In addition, it is an extremely expensive alloy.
  • Reference Example 10 is an iron / cobalt alloy with about 30% cobalt. Compared to the previous one, its resistivity is very significantly lower. In addition, if its elongation at break is better, without being excellent, this alloy has a substantially lower hardness after annealing which makes it less suitable for undergoing cutting or machining.
  • Reference alloy 11 is an iron / silicon alloy with 3% silicon. It presents satisfactory values for the resistivity and the coercive field; on the other hand, its saturation magnetization is relatively weak. In addition, its elongation at break remains very limited.
  • Reference alloy 12 is an approximately 20% cobalt alloy containing vanadium. Its composition verifies equation (1), and it therefore has good saturation magnetization. On the other hand, it does not check equation (2) and its resistivity is mediocre. In addition, its O + N + S content is relatively high, which gives it a coercive field too strong.
  • Reference alloy 13 is an 18% chromium-containing cobalt alloy. He checks equation (2) (if we take into account the elements Al, V, Mo and Si inevitably present as impurities) and verifies equation (1). Its saturation magnetization and resistivity are therefore satisfactory. Its high elongation at break would make it suitable for shaping by plastic deformation. On the other hand, its O + N + S content is high, which gives it a coercive field that is too strong.
  • Reference alloy 14 is similar to the previous one, except that tantalum has been added thereto. The elongation at break is further improved, but the coercive field remains too high for this composition is within the scope of the invention.
  • Reference alloy 15 is a 15% cobalt alloy, also containing silicon and aluminum. It checks equation (2), which gives it a good resistivity, but not equation (1), resulting in saturation magnetization a little too weak compared to what is desired. It is noted that its O + S + N content is low, which gives it a very low coercive field, and that silicon and aluminum give it a high hardness after annealing.
  • the reference alloys 16 and 17 have characteristics comparable to the previous one. They do not check equation (1) because of a cobalt content that is too low compared to the total silicon and aluminum contents, and their saturation magnetization at 20 ° C is slightly too low.
  • Reference alloy 18 is a cobalt iron with 15% cobalt containing no other alloying elements at significant levels. If its saturation magnetization and its coercive field are good (equation (1) is checked and its O + N + S content is low), its resistivity is mediocre (equation (2) is not verified) . In addition, its mechanical properties are not particularly good, either for elongation at break or hardness after annealing.
  • Reference alloy 19 is a cobalt iron with 15% cobalt containing only 1% silicon. The same comments can be made about it as for alloy 16, except that the presence of silicon improves the hardness and the resistivity, without bringing the latter to a sufficient level.
  • Reference alloy 20 is a cobalt iron with 18% cobalt containing 3.2% vanadium. Its electromagnetic characteristics are good, but its elongation at break is insufficient, due to the presence of vanadium in excess relative to the maximum quantity allowed (3%).
  • the alloys 1-8 have a hardness after high annealing, greater than 210 HV, which makes them particularly suitable for being cut or machined. They will therefore be used preferentially to form bars, plates or sheets, from which will be manufactured the desired parts.
  • These are iron-cobalt alloys containing about 15 or 18% cobalt, and significant amounts of silicon and possibly aluminum. Alloy 1 additionally contains tantalum and alloy 2 molybdenum; alloy 3 has no additional alloying elements in large amounts. These alloys have excellent electromagnetic characteristics, both in terms of saturation magnetization and resistivity, and therefore have a very good compromise between the various requirements of the applications envisaged.
  • tantalum and molybdenum in alloys 1 and 2 gives them relatively high elongations at break, which would make these alloys equally suitable for forming by stamping or stamping under conditions that would be acceptable, or which would be even mentally good for the alloy 1.
  • a composition is chosen that comprises 18% of cobalt, 0.5 to 1% of chromium + vanadium, 0.05 to 0.5% of tantalum + silicon and 1 to 2.5% silicon + aluminum + molybdenum.
  • the alloys 4-8 according to the invention have a high elongation at break (at least 35%) which makes them suitable for being formed by stamping or stamping. They will be used preferentially to form bars or wires from which the desired parts will be manufactured. These are iron-cobalt alloys with about 18% cobalt, containing little or no silicon and aluminum. On the other hand, they contain chromium (2 to 2.9%). This element could be replaced at least partially by molybdenum and / or vanadium. Their electromagnetic characteristics present the same favorable compromise between the various requirements as the 1-3 alloys.
  • a composition is chosen that comprises 18% cobalt, 2 to 3% chromium, 0 to 1% vanadium, 0.05 to 0.5% tantalum + silicon and 0 to 0, 5% silicon + aluminum + molybdenum.
  • the alloy according to the invention in the form of bars, wires, plates or sheet metal, if one wants to use this alloy to constitute electromagnetic actuators (or any other part for which similar characteristics would be required), it's important to subject the metal a thermomechanical treatment that gives it the optimal texture required.
  • This treatment must aim at obtaining for at least 30%, and preferably at least 50% (by volume of the material), grains or crystals having a crystallographic orientation having a ⁇ 100> axis deviated by less than 20 ° relative to the hot or cold rolling direction. If we approximate some axes ⁇ 100> of the crystals of the main directions of use of the magnetic flux by a particular texturing, significantly improves the magnetic properties of steels and soft magnetic alloys.
  • alloys of the invention in the form of plates or rolled sheets, these must have a preferential texture of the ⁇ 100 ⁇ or ⁇ 110 ⁇ type parallel to the rolling plane, the proportion of which in the volume of the material and the ⁇ 100> orientation with respect to the rolling direction must meet the criteria mentioned above.
  • austenoferritic rolling is meant a rolling beginning in the austenitic phase, therefore above the transformation temperature ⁇ ⁇ ⁇ + ⁇ (T ⁇ / ⁇ which is specified for each alloy given as an example in Table 1) and ending in phase ferritic, therefore below T ⁇ / ⁇ .
  • This hot rolling must comprise a reduction step with a degree of work-up of at least 30% (and preferably at least 50%) when the alloy is in the ferritic phase (the degree of curling being defined by the ratio ( initial section - final section) / initial section).
  • ferritic phase For example, if one wants to obtain a bar diameter of 20 mm, it is necessary, during hot rolling, to be in ferritic phase with an intermediate diameter of at least 24 mm, preferably at least 28 mm. Similarly, if one wants to obtain a 2.5 mm thick plate, during hot rolling, it is necessary to be in the ferritic phase at an intermediate thickness of at least 3.6 mm, preferably at least 5 mm.
  • the anneals possibly carried out after the hot rolling should never bring the product to a temperature above T ⁇ / ⁇ , this temperature ranging from 930 to 990 ° C for the alloys according to the invention shown in Table 1.
  • the mass decrease of the products following these operations should not exceed 10%, or better 5%.
  • a preferred application of the alloys according to the invention is the manufacture of cores for electromagnetic actuators.
  • Such compact, fast and reliable actuators comprising such cores can advantageously be used in injectors of direct injection combustion engines, especially diesel engines, and in moving parts of electromagnetic actuators controlling the movement of combustion engine valves. internal.

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Claims (16)

  1. Eisen-Cobalt-Legierung, dadurch gekennzeichnet, dass sie in Gewichtsprozent Folgendes umfasst:
    - 10 bis 22 % Co;
    - Spuren bis 2,5 % von Si;
    - Spuren bis 2 % von Al;
    - 0,1 bis 1 % Mn;
    - Spuren bis 0,0100 % von C;
    - eine Summe der Gehalte an O, N und S im Bereich zwischen Spuren und 0,0070 %;
    - eine Summe der Gehalte an Si, Al, Cr, V, Mo, Mn im Bereich zwischen 1,1 und 3,5 %, bevorzugt zwischen 1,5 und 3,5 %;
    - eine Summe der Gehalte an Cr, Mo und V im Bereich zwischen Spuren und 3 %;
    - eine Summe der Gehalte an Ta und Nb im Bereich zwischen Spuren und 1 %;
    wobei der Rest aus Eisen und Verunreinigungen besteht, die aus der Verarbeitung resultieren, dass: 1 , 23 x Al + Mo % + 0 , 84 ⁢ Si + Cr + V % - 0 , 15 x Co % - 15 ≤ 2 , 1
    Figure imgb0010
    dass: 14 , 5 x Al + Cr % + 12 x V + Mo % + 25 x Si % ≥ 40.
    Figure imgb0011
  2. Eisen-Cobalt-Legierung nach Anspruch 1, dadurch gekennzeichnet, dass sie 14 bis 20 % Co umfasst.
  3. Eisen-Cobalt-Legierung nach Anspruch 1 oder 2, dadurch gekennzeichnet, dass die Summe der Gehalte an Ta und Nb im Bereich zwischen 0,05 und 0,8 % liegt.
  4. Eisen-Cobalt-Legierung nach einem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass die Summe ihrer Gehalte an Cr und V im Bereich zwischen 1,1 und 3 %, bevorzugt zwischen 1,5 und 3 %, liegt, und dadurch, dass die Summe ihrer Gehalte an Si, Al und Mo im Bereich zwischen Spuren und 1 % liegt.
  5. Eisen-Cobalt-Legierung nach Anspruch 4, dadurch gekennzeichnet, dass ihre Bruchdehnung 35 % beträgt.
  6. Eisen-Cobalt-Legierung nach einem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass die Summe ihrer Gehalte an Si und Al im Bereich zwischen 1 und 2,6 % liegt, und dadurch, dass die Summe ihrer Gehalte an Cr, V, Mo, Ta, Nb im Bereich zwischen Spuren und 2 % liegt.
  7. Eisen-Cobalt-Legierung nach Anspruch 6, dadurch gekennzeichnet, dass ihre Vickershärte nach dem Glühen ≥ 200 beträgt.
  8. Eisen-Cobalt-Legierung nach einem der Ansprüche 1 bis 7, dadurch gekennzeichnet, dass ihre Sättigungsmagnetisierung > 2,1 T bei 150 °C ist und ≥ 2,12 T bei 20 °C ist, und dadurch, dass ihr spezifischer Widerstand ≥ 35 µΩ.cm bei 150 °C und ≥ 31 µΩ.cm bei 20 °C ist.
  9. Eisen-Cobalt-Legierung nach einem der Ansprüche 1 bis 8, dadurch gekennzeichnet, dass ihre Koerzitivkraft bei 20 und 150 °C kleiner als 1,5 Oe, bevorzugt kleiner als 1 Oe ist.
  10. Stab, Draht oder Platte aus Eisen-Cobalt-Legierung, dadurch gekennzeichnet, dass die Legierung eine Legierung nach einem der Ansprüche 1 bis 9 ist, und dadurch, dass der Stab, der Draht oder die Platte eine bevorzugte Fasertextur der [100]-Achse, die, bezogen auf die Warmwalzrichtung, weniger als 20° abweicht, für mindestens 30 % (in Materialvolumen), bevorzugt für mindestens 50 % der Körner, aufweist.
  11. Walzplatte oder Walzblech aus Eisen-Cobalt-Legierung, dadurch gekennzeichnet, dass die Legierung eine Legierung nach einem der Ansprüche 1 bis 9 ist, und dadurch, dass sie/es einen starken Bestandteil mit Fasertextur der [100]-Achse, die, bezogen auf die Warmwalzrichtung, weniger als 20° abweicht, für mindestens 30 % (in Materialvolumen), bevorzugt für mindestens 50 % der Körner, aufweist.
  12. Verfahren zur Herstellung eines Stabs, eines Drahts, einer Platte oder eines Walzblechs nach Anspruch 10 oder 11, dadurch gekennzeichnet, dass ein Stab, ein Draht, eine Platte oder ein Walzblech aus einem Rohling aus einer Legierung nach einem der Ansprüche 1 bis 9 verarbeitet wird, indem ein Walzen mit einem Verformungsgrad in Ferritphase von mindestens 30 %, bevorzugt mindestens 50 %, durchgeführt wird, und dadurch, dass gegebenenfalls anschließend ein Glühen bei einer Temperatur durchgeführt wird, die kleiner ist als die Temperatur der austenitischen Umwandlung.
  13. Tauchkern einer elektromagnetischen Stellvorrichtung, dadurch gekennzeichnet, dass er aus einem Stab oder einem Draht oder einer Platte oder einem Walzblech nach Anspruch 10 oder 11 gefertigt wurde.
  14. Elektromagnetische Stellvorrichtung, die einen Tauchkern aus Eisen-Cobalt-Legierung umfasst, dadurch gekennzeichnet, dass der Kern ein Kern nach Anspruch 13 ist und dadurch, dass die bevorzugte Textur des Kerns eine [100]-Achse umfasst, die im Wesentlichen parallel zur Hauptrichtung des Erregerfelds ist.
  15. Einspritzdüse für einen Verbrennungsmotor mit elektronischer Regelung, die eine elektromagnetische Stellvorrichtung mit hoher Leistungsdichte, niedriger Ansprechzeit und großer Betriebszuverlässigkeit umfasst, dadurch gekennzeichnet, dass die Stellvorrichtung eine Stellvorrichtung nach Anspruch 14 ist.
  16. Elektromagnetische Stellvorrichtung eines elektronisch gesteuerten Ventils eines Verbrennungsmotors, dadurch gekennzeichnet, dass sie eine elektromagnetische Stellvorrichtung nach Anspruch 14 ist.
EP01934103A 2000-05-12 2001-05-11 Eisen-kobalt-legierung insbesondere für elektromagnetischen aktuator mit beweglichem kernteil und herstellungsverfahren Expired - Lifetime EP1281182B1 (de)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
FR0006088A FR2808806B1 (fr) 2000-05-12 2000-05-12 Alliage fer-cobalt, notamment pour noyau mobile d'actionneur electromagnetique, et son procede de fabrication
FR0006088 2000-05-12
PCT/FR2001/001440 WO2001086665A1 (fr) 2000-05-12 2001-05-11 Alliage fer-cobalt, notamment pour noyau mobile d'actionneur électromagnétique et son procédé de fabrication

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EP1281182A1 EP1281182A1 (de) 2003-02-05
EP1281182B1 true EP1281182B1 (de) 2010-04-21

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JP (1) JP5027372B2 (de)
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AT (1) ATE465500T1 (de)
AU (1) AU2001260412A1 (de)
DE (1) DE60141900D1 (de)
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US8029627B2 (en) * 2006-01-31 2011-10-04 Vacuumschmelze Gmbh & Co. Kg Corrosion resistant magnetic component for a fuel injection valve
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US7909945B2 (en) 2006-10-30 2011-03-22 Vacuumschmelze Gmbh & Co. Kg Soft magnetic iron-cobalt-based alloy and method for its production
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US9057115B2 (en) * 2007-07-27 2015-06-16 Vacuumschmelze Gmbh & Co. Kg Soft magnetic iron-cobalt-based alloy and process for manufacturing it
DE102007035774B9 (de) 2007-07-27 2013-03-14 Vacuumschmelze Gmbh & Co. Kg Weichmagnetische Legierung auf Eisen-Kobalt-Basis sowie Verfahren zu deren Herstellung
EP2083428A1 (de) 2008-01-22 2009-07-29 Imphy Alloys Fe-Co-Legierung für hochdynamische elektromagnetische Stellglieder
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CN115279926B (zh) * 2020-03-10 2024-09-10 株式会社博迈立铖 Fe-Co系合金棒材的制造方法及Fe-Co系合金棒材
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AU2001260412A1 (en) 2001-11-20
ES2342766T3 (es) 2010-07-14
DE60141900D1 (de) 2010-06-02
ATE465500T1 (de) 2010-05-15
WO2001086665A1 (fr) 2001-11-15
EP1281182A1 (de) 2003-02-05
FR2808806A1 (fr) 2001-11-16
US20070029013A1 (en) 2007-02-08
US7819990B2 (en) 2010-10-26
KR100711188B1 (ko) 2007-04-24
US20040099347A1 (en) 2004-05-27
US7128790B2 (en) 2006-10-31
JP2004515644A (ja) 2004-05-27
FR2808806B1 (fr) 2002-08-30
KR20020091831A (ko) 2002-12-06

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