EP4214342A2 - Procédé de fabrication et de conception d'éléments de blindage magnétiques tridimensionnels complexes, éléments de blindage et leur utilisation - Google Patents

Procédé de fabrication et de conception d'éléments de blindage magnétiques tridimensionnels complexes, éléments de blindage et leur utilisation

Info

Publication number
EP4214342A2
EP4214342A2 EP21782652.8A EP21782652A EP4214342A2 EP 4214342 A2 EP4214342 A2 EP 4214342A2 EP 21782652 A EP21782652 A EP 21782652A EP 4214342 A2 EP4214342 A2 EP 4214342A2
Authority
EP
European Patent Office
Prior art keywords
annealing
iron alloy
magnetic
tool
nickel
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Pending
Application number
EP21782652.8A
Other languages
German (de)
English (en)
Inventor
Bas-Jan Hoogenberg
Robert Vehof
Brian Brady
Guillermo DOMÍNGUEZ
Karl Radlmayr
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Voestalpine Metal Forming GmbH
Mogema BV
Original Assignee
Voestalpine Metal Forming GmbH
Mogema BV
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Voestalpine Metal Forming GmbH, Mogema BV filed Critical Voestalpine Metal Forming GmbH
Priority to EP23205888.3A priority Critical patent/EP4310200A3/fr
Publication of EP4214342A2 publication Critical patent/EP4214342A2/fr
Pending legal-status Critical Current

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
    • C22C19/057—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being less 10%
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/02—Stamping using rigid devices or tools
    • B21D22/022—Stamping using rigid devices or tools by heating the blank or stamping associated with heat treatment
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D37/00—Tools as parts of machines covered by this subclass
    • B21D37/16—Heating or cooling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/60—Treatment of workpieces or articles after build-up
    • B22F10/64—Treatment of workpieces or articles after build-up by thermal means
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/60—Treatment of workpieces or articles after build-up
    • B22F10/66—Treatment of workpieces or articles after build-up by mechanical means
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/12—Both compacting and sintering
    • B22F3/16—Both compacting and sintering in successive or repeated steps
    • B22F3/162—Machining, working after consolidation
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/12—Both compacting and sintering
    • B22F3/16—Both compacting and sintering in successive or repeated steps
    • B22F3/164—Partial deformation or calibration
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
    • B22F5/006—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product of flat products, e.g. sheets
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F7/00—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression
    • B22F7/02—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite layers
    • B22F7/04—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite layers with one or more layers not made from powder, e.g. made from solid metal
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F7/00—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression
    • B22F7/06—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite workpieces or articles from parts, e.g. to form tipped tools
    • B22F7/08—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite workpieces or articles from parts, e.g. to form tipped tools with one or more parts not made from powder
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y10/00—Processes of additive manufacturing
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y40/00—Auxiliary operations or equipment, e.g. for material handling
    • B33Y40/20—Post-treatment, e.g. curing, coating or polishing
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y80/00—Products made by additive manufacturing
    • 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
    • C21D1/26—Methods of annealing
    • 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
    • C21D1/26—Methods of annealing
    • C21D1/32—Soft annealing, e.g. spheroidising
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/007—Heat treatment of ferrous alloys containing Co
    • 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
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
    • C21D7/10—Modifying the physical properties of iron or steel by deformation by cold working of the whole cross-section, e.g. of concrete reinforcing bars
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing
    • 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
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/0421—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing characterised by the working steps
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
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    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/0447—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing characterised by the heat treatment
    • 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
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the working steps
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
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    • C21D8/1244—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
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    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2251/00—Treating composite or clad material
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C2202/00—Physical properties
    • C22C2202/02—Magnetic
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

Definitions

  • the invention relates to a method for manufacturing complex three-dimensional magnetic shields, devices for magnetic shielding and their use.
  • CA 2080177 C discloses a transfer molding process for small parts. In addition, it is also known to produce complex components by milling from solid material.
  • the object of the invention is to provide a method with which complex three-dimensional magnetic shielding devices can be produced in a simple, cost-effective manner.
  • the inventors have found that, on the one hand, in the field of high-tech (including semiconductor technology, electron microscopy) and, on the other hand, in the field of automotive applications, in particular due to the trend towards electric vehicles combined with autonomous driving, mechatronic systems with a very high level of precision and accuracy and, on the other hand, high Power outputs are more and more required, which requires a higher proportion of magnetic shielding devices.
  • the problem is that, as already explained, very large three-dimensional objects cannot be manufactured from these materials, since in particular the high temperature during annealing of 1,000 - 1,400°C on the one hand and relatively large surfaces and possibly also small thicknesses on the other hand are currently hardly possible show.
  • the reason for this is that such large components creep and deform at the temperatures mentioned simply because of their size.
  • Corresponding devices to avoid creep, which could support the components at different points, are very complex and very expensive.
  • the method envisages two possible processing routes to create complex three-dimensional magnetic shielding devices.
  • a first method route envisages producing the complex three-dimensionally shaped part from the appropriate materials in a cold deep-drawing process. This complex three-dimensional part is then annealed in a vacuum or in a hydrogen atmosphere and then placed in a tool while hot, which corresponds to the target shape or target geometry of the finished component and is held there until it is creep-resistant and can be removed.
  • the shape deviation is corrected by creeping of the material during the annealing process.
  • the material is not quenched here, but the molded part is held in its shape in the mold and pressed. It can now cool down in the mold, with the mold possibly being preheated in order to set the optimal cooling rate.
  • the parts have the absolutely correct shape, i.e. correspond to the target geometry, even if this is complex three-dimensional, since deformations due to creeping of the material cannot occur in this step. Since the shape correction, calibration or forming that may take place still takes place at very high temperatures, the magnetic properties can largely be retained.
  • suitable components especially if the material does not have a very high forming resistance, can be allowed to cool after magnetic annealing and placed in the tool at a suitable temperature, for example room temperature, and calibrated.
  • a suitable temperature for example room temperature
  • the forming speed can be adjusted if necessary and, in particular, abrupt forming can be avoided and instead a slower "pressing into shape" can take place.
  • the second solution envisages inserting a steel sheet or, in particular, a steel plate made of the soft magnetic material, annealed in a vacuum or hydrogen atmosphere for the purpose of adjusting the permeability, in the hot state into a pressing tool in which the part is formed in one step and in the formed state is held and cools in the mould, optionally preheating the mold to reduce the cooling rate.
  • the tool can be preheated or heated during cooling in such a way that the cooling rate is adapted to the requirements of the soft magnetic material.
  • the advantage of the invention is that through the defined holding and cooling in a tool, which is shaped in such a way that it corresponds to the end component and through the setting of cooling conditions that allow optimal magnetic permeability, creep tendencies of the material can be counteracted and that Material is dimensionally stable and true to form with high permeability can be produced. Changes in shape of a cold, finished material that occur during magnetic annealing can be corrected in the tool without the magnetic properties deteriorating too much (i.e. in the range of a factor of 10 and greater).
  • the invention thus relates to a method for producing three-dimensional magnetic shields with sufficient permeability from unannealed, soft-annealed or magnetically annealed soft-magnetic metal sheets, the metal sheet being either cold-formed in a one-stage or multi-stage process to form the three-dimensional component, followed by a (magnetic ) is subjected to annealing to increase the permeability and then transferred to a mold by being held and/or pressed in a tool in the hot state or at room temperature, which has the target contour of the component and is optionally shape-corrected or calibrated by the tool and, is allowed to cool in the tool, or a metal sheet is heated for the purpose of forming and increasing permeability and then formed and held in a hot forming tool to the desired geometry and allowed to cool in the tool, or the three-dimensional ional component is produced by additive manufacturing and then subjected to (magnetic) annealing to increase permeability.
  • sheet metal made from a magnetizable nickel-iron alloy, a magnetizable silicon-iron alloy, a magnetizable cobalt-iron alloy or other magnetizable metal alloys is used as the soft-magnetic metal sheet.
  • the sheet metal is subjected to soft annealing before cold forming or after cold forming, or the sheet metal is subjected to soft annealing before hot forming.
  • One embodiment provides that, in the case of a nickel-iron alloy, the soft annealing is carried out at 600 to 900° C., in particular up to 700 to 800° C.
  • One embodiment provides that, in the case of a nickel-iron alloy, the magnetic annealing is carried out at 1000 to 1400° C., in particular 1100 to 1300° C., in particular at 1150° C.
  • One embodiment provides that, in the case of a nickel-iron alloy, the hot forming is carried out at 500 to 800°C, in particular 600 to 800°C, preferably 600°C.
  • One embodiment provides that, in the case of a nickel-iron alloy, the hot calibration is carried out at 500 to 800°C, in particular 600 to 800°C, preferably 600°C.
  • One embodiment provides that, in the case of a cobalt-iron alloy, the magnetic annealing is carried out at 700 to 950° C., in particular 730 to 900° C.
  • One embodiment provides that, in the case of a cobalt-iron alloy, the hot forming is carried out at 500 to 800° C., in particular 600 to 800° C.
  • One embodiment provides that, in the case of a cobalt-iron alloy, the hot calibration is carried out at 500 to 800° C., in particular 600 to 800° C.
  • One embodiment provides that, in the case of a silicon-iron alloy, the soft annealing is carried out at 600 to 950° C., in particular up to 700 to 800° C.
  • One embodiment provides that, in the case of a silicon-iron alloy, the magnetic annealing is carried out at 700 to 1100° C., in particular 750 to 1050° C.
  • One embodiment provides that, in the case of a silicon-iron alloy, the hot forming is carried out at 500 to 800° C., in particular 600 to 800° C.
  • One embodiment provides that, in the case of a silicon-iron alloy, the hot calibration is carried out at 500 to 800° C., in particular 600 to 800° C.
  • the cycle time for nickel-iron alloys is 2 to 10 hours for soft annealing.
  • One embodiment provides that the cycle time for nickel-iron alloys is 2 to 150 hours for magnetic annealing.
  • One embodiment provides that the cycle time for nickel-iron alloys during hot forming is 1 second. is up to 2 hours.
  • One embodiment provides that the cycle time for nickel-iron alloys during hot calibration is 1 second. is up to 2 hours.
  • One embodiment provides that the cycle time for nickel-iron alloys during cold forming is 1 second. is up to 2 hours.
  • One embodiment provides that the cycle time for nickel-iron alloys during cold calibration is 1 sec. is up to 2 hours.
  • One embodiment provides that the cycle time for cobalt-iron alloys is 2 to 150 hours for magnetic annealing.
  • One embodiment provides that the cycle time for cobalt-iron alloys during hot forming is 1 second. is up to 2 hours.
  • One embodiment provides that the cycle time for cobalt-iron alloys during hot calibration is 1 second. is up to 2 hours.
  • One embodiment provides that the cycle time for cobalt-iron alloys during cold forming is 1 second. is up to 2 hours.
  • One embodiment provides that the cycle time for cobalt-iron alloys is 1 second for cold calibration. is up to 2 hours.
  • One embodiment provides that the cycle time for silicon-iron alloys is 0.25 to 10 hours for soft annealing.
  • cycle time for silicon-iron alloys is 0.5 to 10 hours for magnetic annealing.
  • cycle time for silicon-iron alloys during hot forming is 1 second. is up to 2 hours.
  • One embodiment provides that the cycle time for silicon-iron alloys during hot calibration is 1 sec. is up to 2 hours.
  • One embodiment provides that the cycle time for silicon-iron alloys during cold forming is 1 second. is up to 2 hours.
  • One embodiment provides that the cycle time for silicon-iron alloys during cold calibration is 1 sec. is up to 2 hours.
  • the forming speed is preferably between 5 mm/min and 60 mm/min tool speed.
  • One embodiment provides for the component to be removed after hot forming or after being held in the tool at a temperature at which the component is stable against material flow and can cool in air and in particular at 200 to 600° C., in particular 300 to 500° C is removed.
  • the sheet metal is produced by means of welds from a number of blanks, in particular combinations of a number of blanks made from different alloys, thicknesses or degrees of tempering or degrees of annealing, in particular with regard to soft, solution and/or stress-relieving annealing.
  • the welded blanks are planar or three-dimensionally shaped components that are welded to one another before, during or after the process.
  • a further aspect of the invention relates to a shielding device made from a three-dimensional metal sheet of high permeability or composed of a plurality of metal sheets, in particular produced by a method according to one of the preceding claims, the metal sheet being formed into the three-dimensional component either in a single-stage or multi-stage process is cold formed, then subjected to (magnetic) annealing to increase the permeability and then transferred to a mold by being held and/or pressed in a tool in the hot state or at room temperature, which has the desired contour of the Component has and is optionally corrected or calibrated by the tool and, in the tool is allowed to cool, or a sheet is heated for the purpose of forming and increasing permeability and then formed in a hot forming tool to the desired geometry and is held and in the tool is allowed to cool, or the three-dimensional component is produced by additive manufacturing and then subjected to (magnetic) annealing to increase permeability.
  • the sheet metal consists of a magnetizable nickel-iron alloy, a magnetizable silicon-iron alloy, a magnetizable cobalt-iron alloy or other magnetizable metal alloys.
  • nickel-iron alloys the nickel content is between 30 and 90% by weight, the nickel content being in particular between 50-80% by weight, with the nickel-iron alloy containing further elements such as molybdenum and/or chromium in the range of up to 10% by weight and other elements such as manganese, silicon and/or carbon in the range of up to 1% by weight each and the balance iron and unavoidable impurities consists. .
  • the silicon content of a silicon-iron alloy is between 0.1-8% by weight, with the silicon-iron alloy containing up to 1% by weight manganese and up to 2% aluminum by weight. % may contain and the rest consists of iron and unavoidable impurities.
  • cobalt-iron alloys the cobalt content is 9-60% by weight, preferably 10-27% by weight, with the cobalt-iron alloy containing chromium from 2 to 10% by weight and molybdenum, vanadium, niobium, tantalum, aluminum, zirconium and/or manganese in the range of up to 2% by weight each and up to 5% by weight in total and the remainder consists of iron and unavoidable impurities .
  • a further aspect of the invention relates to the use of a shielding device as described above for coverings, linings and shields made from individual metal sheets or complex shielding components made from a number of metal sheets assembled together.
  • a further aspect of the invention relates to the use of a shielding device as described above for the formation of housings, chambers, spaces and the like.
  • FIG. 1 Various process sequences of embodiments with separate forming and calibrating steps for nickel-iron alloys
  • FIG. 2 Various process sequences of embodiments with individual forming steps for nickel-iron alloys
  • FIG. 3 Various process sequences of embodiments with a separate shaping and calibrating step for cobalt-iron alloys
  • FIG. 4 Various process sequences of embodiments with individual forming steps for cobalt-iron alloys
  • FIG. 5 Various process sequences of embodiments with a separate shaping and calibrating step for silicon-iron alloys
  • FIG. 6 Various process sequences of embodiments without a soft annealing step for silicon-iron alloys
  • FIG. 7 Different process sequences of embodiments with individual forming steps for silicon-iron alloys
  • the invention relates to the complex 3D shaping of sheet metal made from, for example, nickel-iron alloys, which have soft-magnetic properties. These materials inherently require complex and costly processing due to the need for an end-of-process heat treatment under controlled conditions. This heat treatment optimizes the magnetic properties, which are largely lost when the material is reshaped after heat treatment.
  • a method is created which adds additional method steps to existing method routes, which allow a modified procedure and thus on the one hand make the process considerably more effective and in particular make a final heat treatment step after a necessary forming unnecessary.
  • the soft-magnetic materials used according to the invention are characterized by high magnetic permeability.
  • the group of materials includes not only nickel-iron alloys, but also silicon-iron alloys, cobalt-iron alloys and others.
  • the nickel content is 30-90% by weight.
  • Such materials develop an exceptionally high magnetic permeability of r > 1000, thereby allowing high magnetic flux density of the material to be tolerated. Although the original permeability is very high, it can be further increased by the heat treatment already mentioned.
  • the nickel-iron alloy undergoes a phase transformation from BCC to FCC.
  • the FCC for the material is stable up to the melting point, allowing very high heat treatment temperatures.
  • the Curie temperature ranges from 200°C at 35% by weight nickel to a maximum of 600°C at about 70% by weight nickel.
  • the nickel content can preferably be between 50-80% by weight.
  • the nickel-iron alloy can include other elements such as molybdenum and/or chromium in the range of up to 10%.
  • the nickel-iron alloy can include other elements such as manganese, silicon and/or carbon in the range of up to 1% each.
  • the soft annealing can take place in a temperature range of 600 - 900°C with a cycle time of 1-10h
  • the magnetic annealing can take place in a temperature range of 1000 - 1400°C with a cycle time of 0.5 - 150h.
  • Cycle time or treatment time within the meaning of the invention is the total time in which the material is heat treated, i.e. the heating time and cooling time is included.
  • the cycle time can preferably be based on the thickness of the material, i.e. with thin sheets of 0.1 mm the lower limit of the cycle time is preferably used, while with thicker sheets > 5 mm thickness you can work towards the upper limit.
  • the silicon content is typically from 0.1-8% by weight. With a silicon content above 2% by weight, only the BCC phase is present up to the melting point, which also allows high temperature treatment here.
  • the Curie temperature ranges from 660°C with 8% by weight silicon to a maximum of 770°C in the absence of silicon.
  • the silicon-iron alloys can contain manganese up to 1% and aluminum up to 2%. These alloys can preferably be soft annealed in the temperature range from 550 -
  • the cycle time can be between 10 minutes and 10 hours.
  • the optional soft annealing can ensure a further improvement in the forming behavior of certain alloys.
  • Cold forming as the first processing step for grades with a lower Si content, preferably below 1.5%, and hot forming for high-alloy Si alloys, preferably above 1.5% Si, may be preferable to soft annealing in order to ensure good forming behavior.
  • the magnetic annealing can take place in the temperature range of 750 - 1050°C, the cycle time is preferably 5 seconds to 10 hours. In a continuous annealing process, the cycle time can be reduced to 5 seconds. up to 30 sec. can be set, which can reduce the production time. In a batch annealing process, the cycle time can be between 1 hour and 10 hours.
  • the cobalt content is 9-60% by weight, preferably 10-27% by weight.
  • These alloys are characterized by a high magnetic saturation of up to 2.4 T.
  • the permeability does not surpass the nickel-iron alloys (less than about 20,000 p), its high saturation makes it a preferred choice for achieving high flux density in magnetic shielding or other flux conductors (e.g. actuators).
  • the Curie temperature ranges from 850°C at 9 wt% cobalt to a maximum of 980°C at about 40 wt% cobalt.
  • the cobalt-iron alloy undergoes a phase transformation from BCC (ferrite) to FCC (austenite), therefore the heat treatment should preferably take place at temperatures below 900°C. In addition, at a concentration of 50/50 wt. Therefore, the desired temperature for complex molding operations is between these two phase transitions.
  • the cobalt-iron alloy can contain other elements such as chromium. Chromium increases the protection against corrosion and is preferably added in the range of 2 to 10%. Other elements such as molybdenum, vanadium, niobium, tantalum, aluminium, zirconium and/or manganese can be alloyed in the range of up to 2% each and up to 5% in total.
  • Magnetic fields Materials capable of absorbing and guiding lines of magnetic flux are required if magnetic fields are to be shielded. This applies, for example, to precision sensor instruments where magnetic fields could form parasitic effects. Examples are scientific applications (electron microscopes, atomic force microscopes, etc.), medical devices, the field of energy, semiconductors (subnanometers, precision mechatronics) and others. In addition, it can be foreseen that the transition to electrically powered vehicles and the transition to autonomous driving will be much stronger The type and scope of magnetic shielding is required, since the high voltages in DC motors negatively affect the electronics, which in particular analyze the surrounding traffic.
  • a heat treatment is provided in which a nickel-iron alloy is heated for a specific time, typically to 700°C - 800°C. For the respective material, this temperature is above the so-called recrystallization temperature.
  • This recrystallization anneal is typically performed for 0.5 to 10 hours and the result is material softening and increased ductility (except for the cobalt alloy) to prepare the material for subsequent processes. This process is referred to below as soft annealing.
  • a high-temperature heat treatment is provided when using nickel-iron alloys, which also heats the material for a specific period of time, with the temperature range from 1000°C - 1400°C, in particular 1050°C for a time of 1 to 6 hours is held.
  • the crystals in the material grow to a size where they are readily visible even to the naked eye.
  • This process significantly improves the shielding properties by increasing the permeability (p) even by a factor of 10 or more.
  • This heating is preferably carried out in a vacuum or in a hydrogen atmosphere, the two methods in vacuum or in a hydrogen atmosphere serving to eliminate impurities. The removal of impurities in turn allows greater or further grain growth.
  • This process is referred to below as magnetization annealing.
  • the cycle time of the first soft annealing can preferably be run through faster, ie shorter, than that of any subsequent magnetization annealing. This can support the structure formation.
  • FIG. 1(a) A possible process sequence for nickel-iron alloys is shown in FIG. 1(a).
  • a sheet of an alloy with adjustable soft-magnetic properties such as a nickel-based alloy with a thickness of 0.1 to 50 mm, is first subjected to soft annealing.
  • Forming then takes place either in the cold or warm state.
  • a cold forming for example shown in Fig. 1 (b)
  • this is done in a single or multi-stage process to the finished component.
  • a single-stage forming takes place at temperatures of 500 to 800°C.
  • the heat from soft annealing can be used for hot forming, or it can be heated up again.
  • the shaped bodies which may have warped as a result of the magnetization heat treatment or in which the material has crept due to the influence of heat or its own weight when warm, are brought back into the target geometry.
  • the tool has the appropriate geometry that corresponds to the target geometry of the formed component.
  • the heat from the component from magnetization annealing can also be used for this purpose.
  • the cooling rate can be adjusted in such a way that the cooling curve runs in such a way that maximum permeability is maintained.
  • the first shaping step is omitted, here magnetization annealing takes place directly after soft annealing, with a final shaping step taking place in particular using the heat from magnetization annealing.
  • magnetization annealing takes place directly after soft annealing, with a final shaping step taking place in particular using the heat from magnetization annealing.
  • This is preferably designed in such a way that the sheet metal blank is hot-formed in one step and then held in the tool and allowed to cool, at least until mechanical stability is reached and for as long as the cooling rate is necessary to maintain permeability.
  • the blank is directly subjected to the magnetization annealing, so that the soft annealing is integrated in this step.
  • the final shaping then corresponds to the previously described embodiment. All of the steps mentioned can be followed by cutting, milling, drilling, welding, surface and cleaning steps. In addition, further layers or volumes can be applied additively to components made of sheet metal, for example with 3D printing.
  • FIGS. 3 to 7 show possible production methods for other alloy compositions.
  • Figures 3 and 4 show the possible route for cobalt-iron alloys and Figures 5 to 7 show possible routes for silicon-iron alloys.
  • the advantage of the invention is that the formation of monolithic complex components has functional advantages over the prior art in that the parts are cold-formed and then heat-treated.
  • the combination of the heat treatment step and the hot forming leads to precisely shaped components with a high magnetic shielding effect. Hot forming while maintaining the required temperatures also enables complex shapes, which are particularly advantageous where installation space is limited, for example in electromobility.
  • complex components can then also be combined to form complex shielding devices, for example to form entire housings, claddings, chambers and the like.
  • complex components or shielding devices can also be made from different material thicknesses. An example of this is given in the table below.
  • circuit boards with a length of up to 3500 mm and a width of up to 2500 mm can be produced from a soft-annealed nickel-iron alloy with a Ni content of 48% by weight and formed into a three-dimensional shield. All fusion welding processes, preferably laser welding, can be used as the joining process for producing blanks of this size.
  • a spherical dome 50 mm deep and 100 mm in diameter, was formed from 2 mm thick blanks made of a nickel-iron alloy containing 48% by weight Ni by cold forming, ie deep drawing, at room temperature. This deformation degrades the magnetic properties, so this would be of a Experts are not used as a magnetic shielding element.
  • Such parts are used to demonstrate the effect of the invention and are therefore referred to as reference parts.
  • test parts were formed using the same process to a draw depth of 48mm (and 100mm diameter). These parts are test parts to characterize the calibration process and are finish drawn to 50mm after thermal treatment. The magnetic properties of the test and reference parts were characterized prior to heat treatment.
  • Test and reference parts were magnetized together at 1150°C for 4 hours in a hydrogen atmosphere. After this process step, the reference parts are finished (the parts are manufactured according to FIG. 1 (c)).
  • test parts 48mm were finished by means of cold forming, i.e. deep drawing at room temperature to a depth of 50mm and a diameter of 100mm. This step is calibrated by 2mm (from 48mm to 50m), which leads to a calculated global strain of approx. 4% (the parts are made according to the process shown in Figure 1 (c)).
  • the magnetic properties of the test parts were characterized again between the final drawing and the next process steps. After the final drawing, these test parts were subjected to a second magnetization annealing at 1150° C. for a period of 4 hours in a hydrogen atmosphere and tested for their magnetic properties.
  • the characterization showed that the magnetic shielding had the best values after magnetization annealing.
  • a magnetic flux of 36.7 mT is measured without shielding. This value is reduced to 58 pT (with a reduction factor of 633) for the reference parts after magnetization annealing, while a value of 1.8 mT was measured on the reference parts before annealing (this corresponds to a reduction factor of 20).
  • the anneal provides more than a 30X improvement in shielding compared to the just cold worked part.
  • a significantly larger magnetic shield according to the invention was produced and characterized (approx. 600 ⁇ 300 ⁇ 80 mm).
  • a dome-shaped geometry was produced from a soft-annealed 48% by weight nickel-iron alloy sheet with a thickness of 2 mm in a forming step at room temperature and was geometrically characterized.
  • the component was subjected to magnetization annealing at 1150°C for 4 hours in a hydrogen atmosphere. After that, a magnetic and geometric characterization was carried out. The geometric measurements showed a deviation of 1% from the geometry after the first forming step. This is due to creep during magnetization annealing.
  • the magnetic characterization shows that, with a relatively high magnetic flux density of 1.2 mT, the products according to the invention achieve a 9% lower magnetic shielding compared to the annealed parts before calibration. No difference was measured at a lower flux density of about 300 pT. This can be explained by the fact that no (local) saturation occurs at the lower flux density.
  • the presented method with a calibration step can have large local effects on permeability, but can achieve well-functioning shielding globally.
  • shape of this method corresponds to the target geometry on the test parts, where there is a shape deviation on the reference parts due to material creep. Extremely precise and complex geometries can be produced with a calibration step, which is advantageous for applications with limited installation space or miniaturization.

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  • Manufacturing & Machinery (AREA)
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Abstract

L'invention concerne un procédé de fabrication de blindages magnétiques tridimensionnels présentant une perméabilité suffisante à partir de tôles métalliques magnétiques douces non recuites, ayant subi un recuit doux ou ayant subi un recuit magnétique, la tôle métallique étant déformée à froid en un processus à une ou plusieurs étapes sous la forme d'une pièce tridimensionnelle, puis soumise à un recuit (magnétique) à des fins d'augmentation de perméabilité et transférée ensuite vers un outil de formage, en étant maintenue et/ou pressée à l'état chaud ou à température ambiante dans un outil, qui possède le contour de consigne de la pièce, et éventuellement corrigée du point de vue de sa forme ou calibré au moyen de l'outil, et laissée à refroidir dans l'outil, ou une tôle étant chauffée à des fins de formage et d'augmentation de perméabilité, puis déformée et maintenue dans un outil de formage à chaud jusqu'à présenter la géométrie de consigne, puis laissée à refroidir dans l'outil, ou la pièce tridimensionnelle étant créée par fabrication additive et étant ensuite soumise à un recuit (magnétique) à des fins d'augmentation de perméabilité, ainsi qu'un dispositif de blindage.
EP21782652.8A 2020-09-16 2021-09-16 Procédé de fabrication et de conception d'éléments de blindage magnétiques tridimensionnels complexes, éléments de blindage et leur utilisation Pending EP4214342A2 (fr)

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DE102020124189.5A DE102020124189A1 (de) 2020-09-16 2020-09-16 Verfahren zum Herstellen und Design komplexer dreidimensionaler magnetischer Abschirmelemente, Abschirmelemente und deren Verwendung
PCT/EP2021/075544 WO2022058461A2 (fr) 2020-09-16 2021-09-16 Procédé de fabrication et de conception d'éléments de blindage magnétiques tridimensionnels complexes, éléments de blindage et leur utilisation

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EP23205888.3A Pending EP4310200A3 (fr) 2020-09-16 2021-09-16 Procédé de fabrication et de conception d'éléments de blindage magnétiques tridimensionnels complexes, éléments de blindage et leur utilisation

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US20230332276A1 (en) 2023-10-19
EP4310200A3 (fr) 2024-05-08
KR102944239B1 (ko) 2026-03-31
EP4310200A2 (fr) 2024-01-24
WO2022058461A3 (fr) 2022-05-12
KR20230070251A (ko) 2023-05-22
WO2022058461A2 (fr) 2022-03-24

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