US3108912A - Magnetic material - Google Patents

Magnetic material Download PDF

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Publication number
US3108912A
US3108912A US60720A US6072060A US3108912A US 3108912 A US3108912 A US 3108912A US 60720 A US60720 A US 60720A US 6072060 A US6072060 A US 6072060A US 3108912 A US3108912 A US 3108912A
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United States
Prior art keywords
weight percent
bodies
magnetic
permeability
iron
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.)
Expired - Lifetime
Application number
US60720A
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English (en)
Inventor
Peter G Frischmann
John L Walter
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.)
General Electric Co
Original Assignee
General Electric Co
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
Priority to NL269815D priority Critical patent/NL269815A/xx
Application filed by General Electric Co filed Critical General Electric Co
Priority to US60720A priority patent/US3108912A/en
Priority to LU40591D priority patent/LU40591A1/xx
Priority to FR875110A priority patent/FR1311884A/fr
Priority to US269645A priority patent/US3162554A/en
Application granted granted Critical
Publication of US3108912A publication Critical patent/US3108912A/en
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/14766—Fe-Si based alloys
    • H01F1/14775—Fe-Si based alloys in the form of sheets
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1272—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
    • C21D8/1222—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1261—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest following hot rolling

Definitions

  • the construction of the many types of induction apparatus magnetic materials having diverse and often special magnetic properties are required.
  • the applications in which any given magnetic material may be used depend upon such properties as the coercive force, permeability and residual induction.
  • the construction and operation of certain types of communications equipment have required the use of special alloys or specially constructed bodies to achieve essential magnetic properties.
  • the permeability should be substantially constant and the eddy current losses low, particularly at low field strengths, to obtain true reproduction of sound.
  • Perminvars which are alloys usually containing from about to 55 weight percent nickel, to 60 weight percent cobalt, remainder substantially all iron, have substantially constant permeability but the particular metals used render them comparatively expensive.
  • the Perminvar composition ranges listed are not intended as limiting since other proportions of the constituent metals may deliver suitable properties for some uses. Further information regarding Perminvars and related alloys can be obtained from publications such as Ferromagnetism, by Richard M. Bozorth, published in 1956 by D. Van Nostrand Company, Inc.
  • a principal object of this invention is to provide bodies of silicon-iron alloys having substantially constant magnetic permeability.
  • Another object of this invention is to provide ironbase bodies containing from 4 to 6 weight percent silicon which have substantially constant permeabilities in low magnetic fields.
  • a further object of this invention is to provide siliconiron alloy bodies oriented in the (110) [001] crystalline orientation, which bodies have substantially constant magnetic permeability.
  • An additional object of this invention is to provide a process for producing silicon-iron alloy bodies having substantially constant magnetic permeabilities.
  • FIG. 1 shows hysteresis curves for oriented siliconiron alloy bodies used to produce bodics'according to the present invention
  • FIG. 2 shows hysteresis curves of the unique bodies of this invention.
  • FIG. 3 shows the hysteresis curves of the bodies of FIG. 2 following additional treatment.
  • the bodies of the present invention are made of high-purity iron-base alloys containing from 4 to 6 weight percent silicon and not more than about 0.01 Weight percent incidental impurities. These bodies, when processed according to the method of the invention, have substantially constant magnetic permeabilities.
  • the novel process of this invention comprises preparing a highpurity alloy of the composition previously mentioned and processing it through a plurality of hot and cold rolling stages with intermediate anneals to develop a strong (110) [001] crystalline orientation. The oriented bodies are then given a final anneal in selected atmospheres to produce the constant permeability.
  • cast ingots are prepared by vacuum melting high-purity iron and silicon together in proportions such that the silicon content of the final alloy falls between 4 to 6 percent.
  • the impurity content of the cast alloy should not exceed 0.010 weight percent as a maximum and should preferably not exceed more than about 0.006 weight percent.
  • the normal content for some of the more usual impurities is carbon, 0.001; sulfur, 0.001; oxygen, 0.001; and nitrogen, 0.0005; the remainder being minor metallic impurities which are normally present.
  • a cast ingot is obtained, it is hot rolled to 0.25 inch.
  • the material is annealed at 700 C. to 1200 C. for-from about 0.1 to 1.0 hour in dry hydrogen, that is, hydrogen which is substantially nonoxidizing to silicon, viz., dew point no higher than 40 F.
  • the slabs are then rolled at from 700 to 1000 C. to about 0.100 inch thickness.
  • the material at this stage is subjected to an annealing at temperatures ranging from about 700 C. to 1200" C. for a time sufficient to recrystallize the hot-worked texture, e.g., about 0.1 to 10 hours in a substantially nonoxidizing atmosphere such as dry hydrogen.
  • dry hydrogen means hydrogen having a dew point no higher than 40 F., unless specified to the contrary.
  • the annealed product is then cold worked at least 25 percent in substantially the same direction (e.g., over the range of 40 percent to 99.5 percent) using intermediate anneals where required when more than one reduction stage is used to arrive at thicknesses ranging up to about 0.015 inch.
  • the intermediate anneal which is also carried out under substantially nonoxidizing conditions may range in temperature from about 700 C. to 1200 C. for a time sufficient to effect recrystallization, such as 0.1 hour to 10 hours.
  • the coldworked material is then subjected to an anneal at an elevated temperature in a selected environment for a suificient time to effect secondary recrystallization.
  • Temperatures for the final anneal may range from about 1000 C. to 1350 C. for times ranging up to about 16 hours for thicknesses ranging up to about 0.015 inch, the annealing time increasing with increasing thickness and decreasing with increasing temperature. Generally, times as low as 1 hour are adequate at the high temperatures.
  • Suitable environments for use during the final anneal include hydrogen having a dew point no higher than about F. and vacuum, pressures no higher than 1 10 mm. of mercury being suitable.
  • the oxygen then diffuses into the ried out in such a Way that the bodies are subjected to body of the material, causing the change in magnetic the presence of a minor amount of oxygen, th oxygen proper-ties. It is believed that the oxygen can be supplied being 'felt responsible for the achievement of the unique by means other than alumina plate as, for example, by magnetic properties.
  • a dry hydrogen atmosphere can be providing a small amount of free oxygen in the hydrogen used for this a al a xygen introduced aCC P atmosphere during annealing. Test results indicate that the desired properties.
  • An alumina supporting plate has it the material is annealed in dry hydrogen alone, no been found efiective in supplying the required oxygen, as change in the magnetic properties is obtained. Similarly, later shown.
  • the properties remain unchanged if the material is placed samples are cooled at the rate ranging from about 50 to on plates of alumina and annealed in an argon atmos- 200 C. per hour. phere at the same temperature.
  • an initial body of 0.012 inch thickness stant permeability is obtained and specifically to deter- Was produced according to the procedure outlined earlier, mine whether the effect was caused by an oxide layer at and after the final reduction to 0.012 inch, was annealed the surface of the alloy specimen which exerted compresat 1200 C. in a vacuum at a pressure of about 6 X10- sive or tensile stresses on the material, the samples were mm. of mercury for 6 hours. This heat treatment caused electropolished to remove about 1 mil from the over-all the samples to orient in the (110) [001] crystalline thickness of the specimens.
  • said body having substantially constant magnetic permea ability when subjected to applied magnetic fields of from about 0.1 oersted to fields wherein induction approaches saturation.
  • An article of manufacture comprising, a high-purity alloy body of up to 15 mils thickness having a majority of its constituent grains oriented in the [001] crystalline orientation and consisting of from about 4 to 6 weight percent silicon, remainder substantially all iron, and containing not more than about 0.010 weight percent incidental impurities, said body having substantially constant magnetic permeability.
  • An article of manufacture comprising, a high-purity alloy body of up to 15 mils thickness having a majority of its constituent grains oriented in the (110) [001] crystalline orientation and consisting of from about 4 to 6 weight percent silicon, remainder substantially all iron, and containing not more than about 0.010 weight percent incidental impurities, said body having substantially constant magnetic permeability when subjected to applied fields of up to about 2 oersteds.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Electromagnetism (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Manufacturing & Machinery (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Dispersion Chemistry (AREA)
  • Power Engineering (AREA)
  • Soft Magnetic Materials (AREA)
US60720A 1960-10-05 1960-10-05 Magnetic material Expired - Lifetime US3108912A (en)

Priority Applications (5)

Application Number Priority Date Filing Date Title
NL269815D NL269815A (ja) 1960-10-05
US60720A US3108912A (en) 1960-10-05 1960-10-05 Magnetic material
LU40591D LU40591A1 (ja) 1960-10-05 1961-09-11
FR875110A FR1311884A (fr) 1960-10-05 1961-10-05 Matériaux magnétiques
US269645A US3162554A (en) 1960-10-05 1963-04-01 Heat treatment of grain oriented steel to obtain a substantially constant magnetic permeability

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
US60720A US3108912A (en) 1960-10-05 1960-10-05 Magnetic material

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US3108912A true US3108912A (en) 1963-10-29

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US60720A Expired - Lifetime US3108912A (en) 1960-10-05 1960-10-05 Magnetic material

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LU (1) LU40591A1 (ja)
NL (1) NL269815A (ja)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3247031A (en) * 1963-10-14 1966-04-19 Armco Steel Corp Method of hot rolling nickel-iron magnetic sheet stock
US3259530A (en) * 1963-09-18 1966-07-05 Permag Corp Method of double ageing a magnetic hysteresis alloy
US3355724A (en) * 1964-10-20 1967-11-28 Bell Telephone Labor Inc Magnetic material and devices utilizing same

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US1569355A (en) * 1920-12-21 1926-01-12 Westinghouse Electric & Mfg Co Method of annealing sheet steel
US1932308A (en) * 1932-02-18 1933-10-24 Edward M Freeland Electrical steel
US2242234A (en) * 1936-01-22 1941-05-20 American Rolling Mill Co Producing silicon steel sheets or strips
US2535420A (en) * 1947-09-10 1950-12-26 Armco Steel Corp Process of producing silicon steel of high-directional permeability
US2875113A (en) * 1957-11-15 1959-02-24 Gen Electric Method of decarburizing silicon steel in a wet inert gas atmosphere
US2939810A (en) * 1956-12-31 1960-06-07 Gen Electric Method for heat treating cube-on-edge silicon steel

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US1569355A (en) * 1920-12-21 1926-01-12 Westinghouse Electric & Mfg Co Method of annealing sheet steel
US1932308A (en) * 1932-02-18 1933-10-24 Edward M Freeland Electrical steel
US2242234A (en) * 1936-01-22 1941-05-20 American Rolling Mill Co Producing silicon steel sheets or strips
US2535420A (en) * 1947-09-10 1950-12-26 Armco Steel Corp Process of producing silicon steel of high-directional permeability
US2939810A (en) * 1956-12-31 1960-06-07 Gen Electric Method for heat treating cube-on-edge silicon steel
US2875113A (en) * 1957-11-15 1959-02-24 Gen Electric Method of decarburizing silicon steel in a wet inert gas atmosphere

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3259530A (en) * 1963-09-18 1966-07-05 Permag Corp Method of double ageing a magnetic hysteresis alloy
US3247031A (en) * 1963-10-14 1966-04-19 Armco Steel Corp Method of hot rolling nickel-iron magnetic sheet stock
US3355724A (en) * 1964-10-20 1967-11-28 Bell Telephone Labor Inc Magnetic material and devices utilizing same

Also Published As

Publication number Publication date
LU40591A1 (ja) 1961-11-11
NL269815A (ja)

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