US3849212A - Primary recrystallized textured iron alloy member having an open gamma loop - Google Patents

Primary recrystallized textured iron alloy member having an open gamma loop Download PDF

Info

Publication number
US3849212A
US3849212A US00312681A US31268172A US3849212A US 3849212 A US3849212 A US 3849212A US 00312681 A US00312681 A US 00312681A US 31268172 A US31268172 A US 31268172A US 3849212 A US3849212 A US 3849212A
Authority
US
United States
Prior art keywords
alloy
silicon
temperature
alloy member
grains
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
US00312681A
Other languages
English (en)
Inventor
D Thornburg
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.)
ABB Inc USA
Original Assignee
Westinghouse Electric Corp
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 BE795763D priority Critical patent/BE795763A/fr
Application filed by Westinghouse Electric Corp filed Critical Westinghouse Electric Corp
Priority to US00312681A priority patent/US3849212A/en
Priority to ZA730567A priority patent/ZA73567B/xx
Priority to IN176/CAL/73A priority patent/IN138984B/en
Priority to PH14334*A priority patent/PH9779A/en
Priority to ES411577A priority patent/ES411577A1/es
Priority to DE19732307464 priority patent/DE2307464A1/de
Priority to CA163,942A priority patent/CA973736A/en
Priority to GB799873A priority patent/GB1417250A/en
Priority to DD168957A priority patent/DD102413A5/xx
Priority to AR246718A priority patent/AR193583A1/es
Priority to AU52465/73A priority patent/AU477551B2/en
Priority to IT41531/73A priority patent/IT976648B/it
Priority to FR7306324A priority patent/FR2173189B1/fr
Priority to JP48020721A priority patent/JPS4897718A/ja
Application granted granted Critical
Publication of US3849212A publication Critical patent/US3849212A/en
Assigned to ABB POWER T&D COMPANY, INC., A DE CORP. reassignment ABB POWER T&D COMPANY, INC., A DE CORP. ASSIGNMENT OF ASSIGNORS INTEREST. Assignors: WESTINGHOUSE ELECTRIC CORPORATION, A CORP. OF PA.
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Images

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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C—CHEMISTRY; METALLURGY
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • 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
    • 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
    • C21D8/1216—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
    • C21D8/1227—Warm 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

  • ABSTRACT An iron base alloy is described which contains low amounts of alloying elements and is suitable for use as a transformer core material.
  • the alloy is characterized lg! a (110) tte ture, and a primary recrystallized 4 Claims, 12 Drawing Figures Pmammfivw 3.8492 1 2 1 sum 10F e ROLLING DIRECTION DlGIT CONTOUR 50 I 1'.0 2 2.0
  • FIG. 3A OI F l l l l l l l I I l I l' l I I I I 7 ALPHA FIG. 3A
  • the present invention relates to an iron base alloy which contains low amounts of alloying components and which, when processed in accordance with either one of the two methods set forth hereinafter, will produce an oriented grain structure in the finished product which is characterized by a cube-on-edge orientation or as described in Miller lndices as (I10) [001] grain orientation, and comprising a primary recrystallized and normal grain growth microstructure.
  • Such magnetic materials are useful, for example, as core materials in power and distribution transformers.
  • the alloy of the present invention also employs a trade-off of the various magnetic characteristics.
  • the observed magnetic characteristics especially those where the material is used as in transformer core approach those of the commercially produced 3.25 silicon steel materials employed today.
  • the present low alloy composition is radically altered from the 3.25% silicon containing iron, but the same orientation is attained by means of the processes set forth hereinafter so that the microstructure is primarily recrystallized with normal grain growth.
  • the alloy of the present invention produced comparable magnetic characteristics without employing the costly secondarily recrystallized microstructure, yet obtains the same orientation in a composition which is quite diverse from that of the commercially used materials.
  • FIG. 1 is a (1 l0) Pole Figure and FIG. 1A is a Histogram for Heat No. 1482;
  • FIG. 2 is a (200) Pole Figure and FIG. 2A is a Histogram for the same material of FIG. 1;
  • FIG. 3 is a (1 l0) Pole Figure and FIG. 3A is a Histogram for a commercial size heat identified as Heat No. 3524;
  • FIG. 4 is a (200) Pole Figure and FIG. 4A is a Histogram for the material of FIG. 3;
  • FIG. 5 is a I I0) Pole Figure andFIG. 5A is a Histogram for another commercial size heat identified as Heat No. 3523;
  • FIG. 6 is a (200) Pole Figure and FIG. 6A is a Histogram of the material of FIG. 5.
  • the present invention relates to an iron base alloy containing up to about 0.03% carbon, up to 1% manganese, from about 0.3% to about 4% of at least one of the volume resistivity improving elements selected from the group consisting of up to about 2% silicon, up to 2% chromium, and up to about 3% cobalt, and the balance essentially iron with incidental impurities.
  • This alloy is processed by hot working and cold working in either a two or a three stage operation, the final stage of working effecting only a moderate reduction in the cross-sectional area of the material being processed, said last reduction in cross-sectional area lying generally within the range between about 50% and about
  • the finish gauge material is thereafter subjected to a final anneal at a temperature which is in the range between about 750C and the Ac, temperature exhibited by the alloy.
  • the alloy exhibits a cube-on-edge or a I l0)[00l texture as the predominant texture, a primarily recrystallized and normal grain growth microstructure.
  • the magnetic characteristic exhibited by the alloy approached those of commercially produced 3.25% silicon steels in use today.
  • the alloy of the present invention has a composition which includes up to about 0.03% carbon, up to about 1% manganese, at least 0.3% up to about 4% of at least one of the volume resistivity improving elements selected from the group consisting of up to 2% silicon, up to about 2% chromium, and up to about 3% cobalt, and the balance being essentially iron with incidental impurities.
  • the carbon in the final product which is maintained as low as possible is usually included with the composition initially for deoxidation purposes in the normal melting of the components. While it is desirable to maintain the carbon content in the melt as low as possible, up to about 0.03% can be employed without adversely affecting the magnetic characteristics of the alloy as melted. With about 0.03% carbon, it is possible to decarburize the finished alloy and remove the carbon content to the desired low level.
  • the alloy also contemplates the use of manganese in amounts up to 1% usually for the purpose of deoxidizing the material. It will be noted hereinafter however that the addition of manganese also improves the volume resistivity of the alloy but not to the same extent as silicon. Good results have been obtained where the manganese content of the alloy is about 0.5%.
  • At least 0.3% and up to 4% of at least one element of the group consisting of silicon, chromium and cobalt is necessary in the alloy of the present invention.
  • silicon is employed, amounts of up to 2% can be utilized in order to improve the volume resistivity. Good results have been obtained where the silicon content is maintained within the range between about 0.5% to 1.5%.
  • the silicon content is preferably limited to the foregoing range in order that the alloy will exhibit an open gamma loop to enable one to utilize a primary recrystallization technique for developing the desired grain texture within the alloy.
  • chromium is used as the volume resistivity improving element, a minimum of about 0.3% chromium should be employed and amounts in excess of about 2% chromium should be avoided.
  • cobalt also improves the saturation value of the alloy, up to about 3% is contemplated within the composition for improving the volume resistivity as well as the saturation value of the alloy. Combinations of any two or all three of these resistivity improving components are particularly effective. Sulfur should be as low as practicable since the element will not be removed during subsequent processing.
  • sulfur should not exceed about 0.012% and preferably it should be below about 0.010%. It has been noted that sulfur appears to adversely affect the coercive force and hence the core loss properties of the alloys. In contrast to presently available commercial oriented silicon-iron wherein sulfur unites with manganese to form a particle which is effective in developing a high degree of texture in the final product, such mechanism is not believed to be involved in developing the texture observed in the alloy of the present inven tion. Moreover, when it is considered that in the commercially available material the final heat treatment temperature is in excess of about 1000C which is effective for dissacating the manganese sulfide, the sulfur is removed from the alloy after it has served its purpose. However, this can only occur at temperatures in excess of about 1000C.
  • the open gamma loop alloy of the present invention is finished hot working, it is never heated above its Ac, temperature. Consequently, any sulfur which is present will not be significantly reduced during such subsequent operations. Accordingly, it is necessary to control the sulfur content and outstanding results have been obtained where the sulfur content is maintained at about 0.005 maximum.
  • the balance consists essentially of iron with the usual incidental impurities that are found in the manufacture of magnetic alloys on a commercial scale.
  • the alloy having the composition as set forth hereinbefore is melted and is cast into ingots in the regular commercial manner.
  • the metal may be continuously cast into slabs or bars.
  • the cast ingots are thereafter hot worked usually at a temperature within the range about 1000C and 1100C to a desired intermediate gauge.
  • the alloy is to be processed by employing two-stage cold working operation it is preferred to hot work the metal to a thickness of about 0.10 0.025 inch.
  • the preferred finished hot work gauge is about 0.180 $0.030 inch. While it is not absolutely essential to protect the steel during such hot working operation, an argon or other non-oxidizing atmosphere may be used in order to prevent excessive scaling of the alloy during such hot working.
  • the alloy is hot work the alloy at a temperature of about 1050C to the desired final hot work gauge depending upon the cold working operation to which the alloy will be subjected. Following such hot working to the desired gauge, the alloy is descaled, usually by pickling in order to remove any scale which may have formed on the surface thereof during such hot working operation.
  • the alloy is thereafter cold worked in two or more operations or stages to finish gauge.
  • cold rolling it may be usually necessary to pass the alloy strands a number of times through said cold working rolls in order to attain the desired reduction in area.
  • the several cold working operations require an intervening intermediate anneal at a temperature within the range between about 750C and the Ac temperature of the alloy being processed.
  • the initial hot worked material of about 0.10 inch in thickness is first cold worked-to about 0.025 inch and then annealed for l hour at a temperature of about 850C in an atmosphere preferably of hydrogen having a dew point of less than about 40C.
  • the alloy sheet or strip is given the second stage cold working to the finish gauge usually within a thickness of between about 0.010 inch and about 0.014 inch.
  • an approximately reduction in crosssectional area is effected on the alloy in the initial cold working operation and, following intermediate annealing, a reduction in cross-sectional area of about 50% to finish gauge is produced in the second stage operation.
  • Thefirst stage of cold rolling may effect high reductions of up to or more. It is imperative that only moderate amounts of cold work be employed in the final cold working operation such that the reduction in cross-sectional area will range between about 50% and 75% reduction in cross-sectional area from the thickness or the cross-sectional area of the material of intermediate gauge resulting from the initial cold working operation. Excellent results have been achieved where the final cold reduction effects a reduction in crosssectional area of between about 60% and about 70% to finish gauge.
  • a three-stage cold working operation may be performed with each cold working stage being followed by an intervening intermediate anneal at a temperature within the range between about 750C and about the Ac temperature of the alloy.
  • each of the cold working operations only moderate amounts of cold work are effected, usually within the range between about 50% and about 75% reduction in cross sectional area from the preceding gauge material.
  • a typical three-stage cold working operation would start with a hot work gauge of about 0.18 inch strand thickness, which strand is thereafter descaled, usually by pickling and annealing for about 5 hours at a temperature of between 850C and 900C.
  • the annealedalloy strand is then first cold worked to a thickness of about 0.080 inch in thickness, i.e., 55% reduction, annealed for about 5 hours at a temperature within the range between about 800 and 900C, cold worked to a thickness of about 0.020 inch in thickness, (i.e.
  • a 75% reduction annealed for about 1 hour at a temperature within the range between about 800C and 900C and thereafter cold worked to a finish thickness usually within the range between about 0.005 and about 0.007 inch in thickness, a reduction of about 75% to 65%.
  • part of the cold working operation except the last one may be performed at an elevated temperature between room temperature and about 300C.
  • the working at elevated temperatures is referred to as hotcold working.
  • Such hot-cold working can take place at any temperature above ,room temperature and below the recrystallization temperature of the alloy being processed.
  • a protective atmosphere and preferably a hydrogen atmosphere having a dew point of less than about 40C is employed.
  • one or more of the intermediate anneals can be accomplished by means of a strip anneal versus a box anneal.
  • a single strand from a coil of the alloy may be continuous fed into a strip annealing furnace where the material is heated to a temperature typically of about 900C wherein each increment of the strip is maintained at this temperature for a time period of typically 3 minutes.
  • a hydrogen atmosphere having a dew point of 40C may be advantageously employed.
  • the alloy sheet or strip is subjected to a final anneal, usually a box anneal, at a temperature within the range between about 750C and the Ac temperature of the alloy such box annealing usually being carried out in an atmosphere of hydrogen having a dew point of less than about 40C.
  • the alloy is maintained at a temperature which is always below the alpha to gamma transformation temperature in order to obtain a primary recrystallized microstructure with normal grain growth. It has been found that the alloy so processed and subjected to the final annealing attains the desired degree of orientation usually within a time period within the range between the 24 hours and 48 hours while at the box annealing temperature.
  • the alloy Upon cooling to room temperature following such box annealing, the alloy will possess a grain structure having a preponderance of the grains aligned in the cube-on-edge or l l0)[00l orientation. It has been found that the grains which attain the preferred orientation have cube edges which are aligned within ten degrees of the rolling direction.
  • PROCESS NUMBER 1 PROCESS NUMBER 2 I-Iot roll at l050C in argon to 0.180 inch in thickness pickle and anneal 5 hours at a temperature within the range between 850C and 900C employing dry hydrogen. Warm roll at 260C, employing argon, to 0.080
  • Epstein strips were cut in the rolling direction and one inch diameter torque discs were punched from alloys which were finally annealed at a temperature of 850C to 950C for 48 hours in dry hydrogen and thereafter the test specimens were furnace cooled.
  • Nominal Thickness P615 P015 m al! un all! HEAT (mils) (W/lb (VA/lb) (W/lb) (VA/lb) (W/lb) (VA/1b) ence is directed to Table 2 which lists the torque and the DC magnetic data.
  • Process 2 produced some general improvements in the peak torque values and slightly higher peak ratios in comparison with the commercial 3.20% silicon steel.
  • Heats 3524 and 3523 were both air induction melted heats having a weight of approximately 5000 lbs. for
  • the hot rolled band had a thickness of 0.160 inch.
  • the hot rolled band was thereafter descaled, cold rolled to 0.08 inch, annealed for 1 hour at 850C in dry hydrogen followed by cold rolling to 0.02 inch in thickness.
  • the 0.02 inch thick material was then subjected to a strip anneal at 900C in an atmosphere of dry hydrogen. The material was maintained at the temperature of 900C for a time period of 3 minutes. 3 After annealing, the material was cold rolled to a thickness of 0.006 inch which was the desired finished gauge.
  • the finished gauge material was subjected to a final annealing for a time period of 48 hours at a temperature of 900C while employing a hydrogen 3 atmosphere having a due point of less than -C.
  • the samples were placed in the furnace cold and program heated at the rate of 50C per hour to 900C and after holding at 900C for 48 hours, they were program cooled at 50C per hour until a temperature of 300C 40 was attained. From the foregoing, it will be apparent that the processing of Heat No. 3524 involved a threestep cold rolling sequence and closely approaches Process No. 2 as set forth hereinbefore.
  • 3523 was also hot rolled in air to the same hot rolled band thickness of 0.160 inch. It was thereafter cleared by descaling followed by an anneal for 1 hour at a temperature of 850C in dry hydrogen.
  • the first cold rolling involved a hot-cold rolling at a temperature of ing which the material was cold rolled to fi nish gauge of 0.006 inch in thickness.
  • the finished gauge material was subjected to a final box anneal for a time period of 48 hours at a temperature of 850C while employing a hydrogen atmosphere having a dew point of less than 40C.
  • the samples of Heat No. 3523 were placed into the furnace at temperature and following the annealing they were program cooled at a rate of centigrade degree per hour until a temperature of 300C was achieved.
  • the saturation value nominally the B 'value is approximately 21,300 kilogauss. Comparing the B data with the saturation data, it is seen that these alloys are so highly textured that they all exhibited in excess of 85% of the saturation value at a magnetizing force of 10 oersted, thereby confirming the high degree of texture within the alloys.
  • a decarburizing anneal may minor (I00) planar component being aligned in the be employed in order to obtain extremely low carbon same manner as the I I0) plane the improved magcontents without adversely affecting the magnetic charnetic characteristics are noted.
  • I00 minor planar component being aligned in the be employed in order to obtain extremely low carbon same manner as the I I0) plane the improved magcontents without adversely affecting the magnetic charnetic characteristics are noted.
  • mium content is within the range between about 0.3 to about 0.9%.
  • a heat treated alloy member having an open gamma loop and improved magnetic characteristics consisting essentially of up to 0.03% carbon, up to 0.5% manganese, less than 0.010% sulfur, from 0.3% to 4% of at least one of the volume resistivity improving elements selected from the group consisting essentially of up to 2% silicon, up to 2% chromium, and up to 3% cobalt, the balance being iron with incidental impuri-' ties, the alloy having a major proportion of the grains exhibiting a 1 10) texture and in which a major proportion of the oriented grains have the cube edges of their crystal lattices aligned within 12 of the rolling direction, and a primary recrystallized and normal grain 2.
  • the alloy member of claim 1 in which the chrogrowth microstructure.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Manufacturing & Machinery (AREA)
  • Electromagnetism (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Dispersion Chemistry (AREA)
  • Power Engineering (AREA)
  • Soft Magnetic Materials (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
  • Heat Treatment Of Articles (AREA)
US00312681A 1972-02-22 1972-12-11 Primary recrystallized textured iron alloy member having an open gamma loop Expired - Lifetime US3849212A (en)

Priority Applications (15)

Application Number Priority Date Filing Date Title
BE795763D BE795763A (fr) 1972-02-22 Alliages ferreux et procedes pour fabriquer de tels alliages
US00312681A US3849212A (en) 1972-02-22 1972-12-11 Primary recrystallized textured iron alloy member having an open gamma loop
ZA730567A ZA73567B (en) 1972-12-11 1973-01-25 An improvement in or relating to(110)(001)textured low-alloy iron and process for producing the same
IN176/CAL/73A IN138984B (fr) 1972-02-22 1973-01-25
PH14334*A PH9779A (en) 1972-02-22 1973-02-09 Textured low alloy iron and process for producing the same
ES411577A ES411577A1 (es) 1972-02-22 1973-02-13 Un procedimiento para producir textura (110)n001nen alea- ciones a base de hierro.
DE19732307464 DE2307464A1 (de) 1972-02-22 1973-02-15 Eisenlegierungen und verfahren zu deren herstellung
CA163,942A CA973736A (en) 1972-02-22 1973-02-16 Primary recrystallized textured iron alloy member having an open gamma loop
GB799873A GB1417250A (en) 1972-02-22 1973-02-19 Iron base alloys and process for producing such alloys
DD168957A DD102413A5 (fr) 1972-02-22 1973-02-20
AR246718A AR193583A1 (es) 1972-02-22 1973-02-21 Una aleacion a base de hierro y un procedimiento para su preparacion
AU52465/73A AU477551B2 (en) 1972-02-22 1973-02-22 Improvements in or relating to iron base alloys and process for producing such alloys
IT41531/73A IT976648B (it) 1972-02-22 1973-02-22 Procedimento per produrre leghe a base di ferro particolarmente utili per la fabbricazione di nuclei di trasformatori
FR7306324A FR2173189B1 (fr) 1972-02-22 1973-02-22
JP48020721A JPS4897718A (fr) 1972-02-22 1973-02-22

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
US22831872A 1972-02-22 1972-02-22
US00312681A US3849212A (en) 1972-02-22 1972-12-11 Primary recrystallized textured iron alloy member having an open gamma loop

Publications (1)

Publication Number Publication Date
US3849212A true US3849212A (en) 1974-11-19

Family

ID=26922259

Family Applications (1)

Application Number Title Priority Date Filing Date
US00312681A Expired - Lifetime US3849212A (en) 1972-02-22 1972-12-11 Primary recrystallized textured iron alloy member having an open gamma loop

Country Status (13)

Country Link
US (1) US3849212A (fr)
JP (1) JPS4897718A (fr)
AR (1) AR193583A1 (fr)
BE (1) BE795763A (fr)
CA (1) CA973736A (fr)
DD (1) DD102413A5 (fr)
DE (1) DE2307464A1 (fr)
ES (1) ES411577A1 (fr)
FR (1) FR2173189B1 (fr)
GB (1) GB1417250A (fr)
IN (1) IN138984B (fr)
IT (1) IT976648B (fr)
PH (1) PH9779A (fr)

Cited By (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3977919A (en) * 1973-09-28 1976-08-31 Westinghouse Electric Corporation Method of producing doubly oriented cobalt iron alloys
US4251295A (en) * 1979-05-11 1981-02-17 Westinghouse Electric Corp. Method of preparing an oriented low alloy iron from an ingot alloy having a high initial sulfur content
US4251296A (en) * 1979-05-11 1981-02-17 Westinghouse Electric Corp. Method of preparing an oriented-low-alloy iron from an ingot of controlled sulfur, manganese and oxygen contents
US4255215A (en) * 1979-05-11 1981-03-10 Westinghouse Electric Corp. Oriented low-alloy iron containing critical amounts of silicon and chromium
US4265683A (en) * 1979-02-07 1981-05-05 Westinghouse Electric Corp. Development of grain-oriented iron sheet for electrical apparatus
US4269634A (en) * 1979-12-04 1981-05-26 Westinghouse Electric Corp. Loss reduction in oriented iron-base alloys containing sulfur
US20020000272A1 (en) * 1999-12-16 2002-01-03 Vladimir Segal Alloys formed from cast materials utilizing equal channel angular extrusion
US20040072009A1 (en) * 1999-12-16 2004-04-15 Segal Vladimir M. Copper sputtering targets and methods of forming copper sputtering targets
US20060118212A1 (en) * 2000-02-02 2006-06-08 Turner Stephen P Tantalum PVD component producing methods
US7101447B2 (en) 2000-02-02 2006-09-05 Honeywell International Inc. Tantalum sputtering target with fine grains and uniform texture and method of manufacture
US20070084527A1 (en) * 2005-10-19 2007-04-19 Stephane Ferrasse High-strength mechanical and structural components, and methods of making high-strength components
US20070251818A1 (en) * 2006-05-01 2007-11-01 Wuwen Yi Copper physical vapor deposition targets and methods of making copper physical vapor deposition targets
CN105296863A (zh) * 2015-09-30 2016-02-03 北京北冶功能材料有限公司 一种半硬磁合金及其制造方法
CN113897558A (zh) * 2021-10-08 2022-01-07 北京北冶功能材料有限公司 一种高饱和磁感高磁导率铁基软磁材料及其制备方法

Families Citing this family (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS53129116A (en) * 1977-04-18 1978-11-10 Nippon Steel Corp Oriented electromagnetic steel sheet with excellent magnetic characteristic s
JPS6037172B2 (ja) * 1978-03-11 1985-08-24 新日本製鐵株式会社 一方向性珪素鋼板の製造法

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3130094A (en) * 1959-06-11 1964-04-21 Armco Steel Corp Manufacture of silicon-iron having cubic texture
US3180767A (en) * 1962-10-08 1965-04-27 Armco Steel Corp Process for making a decarburized low carbon, low alloy ferrous material for magnetic uses
US3287184A (en) * 1963-10-22 1966-11-22 Bethlehem Steel Corp Method of producing low carbon electrical sheet steel
US3347718A (en) * 1964-01-20 1967-10-17 Armco Steel Corp Method for improving the magnetic properties of ferrous sheets

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3130094A (en) * 1959-06-11 1964-04-21 Armco Steel Corp Manufacture of silicon-iron having cubic texture
US3180767A (en) * 1962-10-08 1965-04-27 Armco Steel Corp Process for making a decarburized low carbon, low alloy ferrous material for magnetic uses
US3287184A (en) * 1963-10-22 1966-11-22 Bethlehem Steel Corp Method of producing low carbon electrical sheet steel
US3347718A (en) * 1964-01-20 1967-10-17 Armco Steel Corp Method for improving the magnetic properties of ferrous sheets

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
Lyman et al., Metals Handbook, Cleveland (ASM) 1961, pp. 62 & 785 787. *
Pyr, R., Development Met. Structure and Mag. Prop. in Fe Si Alloys, in J. Appl. Phys. Suppl. to Vol. 30 (1959) 1895 1935. *

Cited By (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3977919A (en) * 1973-09-28 1976-08-31 Westinghouse Electric Corporation Method of producing doubly oriented cobalt iron alloys
US4265683A (en) * 1979-02-07 1981-05-05 Westinghouse Electric Corp. Development of grain-oriented iron sheet for electrical apparatus
US4251295A (en) * 1979-05-11 1981-02-17 Westinghouse Electric Corp. Method of preparing an oriented low alloy iron from an ingot alloy having a high initial sulfur content
US4251296A (en) * 1979-05-11 1981-02-17 Westinghouse Electric Corp. Method of preparing an oriented-low-alloy iron from an ingot of controlled sulfur, manganese and oxygen contents
US4255215A (en) * 1979-05-11 1981-03-10 Westinghouse Electric Corp. Oriented low-alloy iron containing critical amounts of silicon and chromium
US4269634A (en) * 1979-12-04 1981-05-26 Westinghouse Electric Corp. Loss reduction in oriented iron-base alloys containing sulfur
US6723187B2 (en) 1999-12-16 2004-04-20 Honeywell International Inc. Methods of fabricating articles and sputtering targets
US20040072009A1 (en) * 1999-12-16 2004-04-15 Segal Vladimir M. Copper sputtering targets and methods of forming copper sputtering targets
US20020000272A1 (en) * 1999-12-16 2002-01-03 Vladimir Segal Alloys formed from cast materials utilizing equal channel angular extrusion
US6878250B1 (en) 1999-12-16 2005-04-12 Honeywell International Inc. Sputtering targets formed from cast materials
US20060118212A1 (en) * 2000-02-02 2006-06-08 Turner Stephen P Tantalum PVD component producing methods
US7101447B2 (en) 2000-02-02 2006-09-05 Honeywell International Inc. Tantalum sputtering target with fine grains and uniform texture and method of manufacture
US7517417B2 (en) 2000-02-02 2009-04-14 Honeywell International Inc. Tantalum PVD component producing methods
US20070084527A1 (en) * 2005-10-19 2007-04-19 Stephane Ferrasse High-strength mechanical and structural components, and methods of making high-strength components
US20070251818A1 (en) * 2006-05-01 2007-11-01 Wuwen Yi Copper physical vapor deposition targets and methods of making copper physical vapor deposition targets
CN105296863A (zh) * 2015-09-30 2016-02-03 北京北冶功能材料有限公司 一种半硬磁合金及其制造方法
CN113897558A (zh) * 2021-10-08 2022-01-07 北京北冶功能材料有限公司 一种高饱和磁感高磁导率铁基软磁材料及其制备方法

Also Published As

Publication number Publication date
AU5246573A (en) 1974-08-22
GB1417250A (en) 1975-12-10
IN138984B (fr) 1976-04-24
BE795763A (fr) 1973-08-22
IT976648B (it) 1974-09-10
ES411577A1 (es) 1976-06-01
AR193583A1 (es) 1973-04-30
FR2173189A1 (fr) 1973-10-05
CA973736A (en) 1975-09-02
FR2173189B1 (fr) 1977-09-02
JPS4897718A (fr) 1973-12-12
DD102413A5 (fr) 1973-12-12
DE2307464A1 (de) 1973-08-30
PH9779A (en) 1976-03-17

Similar Documents

Publication Publication Date Title
US3849212A (en) Primary recrystallized textured iron alloy member having an open gamma loop
US3632456A (en) Method for producing an electromagnetic steel sheet of a thin sheet thickness having a high-magnetic induction
US3287183A (en) Process for producing single-oriented silicon steel sheets having a high magnetic induction
US3159511A (en) Process of producing single-oriented silicon steel
US3770517A (en) Method of producing substantially non-oriented silicon steel strip by three-stage cold rolling
JPH0651887B2 (ja) 粒子方向性珪素鋼ストリップの超急速熱処理方法および製造法
US3905843A (en) Method of producing silicon-iron sheet material with boron addition and product
US3977919A (en) Method of producing doubly oriented cobalt iron alloys
US3892605A (en) Method of producing primary recrystallized textured iron alloy member having an open gamma loop
KR850001253B1 (ko) 전자기용 이방성 강판의 제조방법
US3163564A (en) Method for producing silicon steel strips having cube-on-face orientation
JPH0651889B2 (ja) 無方向性珪素鋼の超高速焼なましによる製造方法
US3287184A (en) Method of producing low carbon electrical sheet steel
US3881967A (en) High saturation cobalt-iron magnetic alloys and method of preparing same
US3868278A (en) Doubly oriented cobalt iron alloys
US3148092A (en) Process for producing sheets of magnetic materials
JP2639227B2 (ja) 無方向性電磁鋼板の製造方法
US3144363A (en) Process for producing oriented silicon steel and the product thereof
US3793092A (en) Fine-grained, completely decrystallized, annealed cobalt-iron-vanadium articles and method
CA2048014C (fr) Procede de fabrication de tole d'acier au silicium oriente
JPH0689805A (ja) 超高磁束密度一方向性電磁鋼板
US3105782A (en) Method of producing magnetic material
US3124491A (en) Heavy gauge double oriented magnetic sheet material
JPH042723A (ja) 磁束密度の高い二方向性電磁鋼板の製造方法
EP0535651B1 (fr) Procédé pour la fabrication de bandes d'acier au silicium à grains orientés

Legal Events

Date Code Title Description
AS Assignment

Owner name: ABB POWER T&D COMPANY, INC., A DE CORP., PENNSYLV

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST.;ASSIGNOR:WESTINGHOUSE ELECTRIC CORPORATION, A CORP. OF PA.;REEL/FRAME:005368/0692

Effective date: 19891229