[go: up one dir, main page]

US2534141A - Heat-treatment of cold rolled silicon steel strip - Google Patents

Heat-treatment of cold rolled silicon steel strip Download PDF

Info

Publication number
US2534141A
US2534141A US2327A US232748A US2534141A US 2534141 A US2534141 A US 2534141A US 2327 A US2327 A US 2327A US 232748 A US232748 A US 232748A US 2534141 A US2534141 A US 2534141A
Authority
US
United States
Prior art keywords
growth
crystals
cold rolled
temperature
silicon steel
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
US2327A
Inventor
Morrill Weston
Cecil G Dunn
Ward Raymond
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
Application filed by General Electric Co filed Critical General Electric Co
Priority to US2327A priority Critical patent/US2534141A/en
Application granted granted Critical
Publication of US2534141A publication Critical patent/US2534141A/en
Anticipated expiration legal-status Critical
Expired - Lifetime 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
    • 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
    • C21D3/00—Diffusion processes for extraction of non-metals; Furnaces therefor
    • C21D3/02—Extraction of non-metals
    • C21D3/04—Decarburising
    • 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
    • C21D8/1233—Cold 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
    • C21D8/1255—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 with diffusion of elements, e.g. decarburising, nitriding
    • 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
    • C21D8/1266—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 between cold rolling steps

Definitions

  • This invention relates to silicon steel. More particularly it relates to a method of heat treating cold rolled silicon steel strip to enhance its magnetic qualtities.
  • a usual practice comprises cold rolling the material in one or more stages from a thickness of about 0.10 to about 0.014" with intervening heat treatment followed. by a decarburia ing heat treatment and a final single stage texture developing and mechanical strain relieving heat treatment at a temperature in exces of 1100" C.
  • the final structure consists of well-oriented, i. e. (110) [001], crystals mixed with more or less poorly oriented crystals.
  • the ultimate goal in the various processings and heat treatment is to attain the maximum preferred (110) [001] magnetic crystal orientation in the steel, thus en- I hancing its application and use in electro-mag netic products.
  • An object or the present invention is to provide a method for further improving the magnetic characteristics of cold rolled silicon steel strip.
  • an object of the invention is to provide a two-stage final texture developing anneal which will improve the magnetic orientation of the crystals in cold rolled silicon steel.
  • a material of superior magnetic qualities can be obtained by subjecting the silicon strip as it comes from the final cold rolling stage and after decarburization to a two part heat treatment which comprises holding it for a time at a temperature which encourages and permits the nucleation or first appearance of Well oriented crystals and their growth at the expense of the suitably prepared matrix and then holding at a temperature which will permit the completion of growth of any well oriented crystals which have not already attained maximum size to develop the maximum metal texture.
  • the silicon steel strip is usually reduced to final thickness in one or more stages separated by heat treatment normally at a temperature under 1000 C.
  • a decarburization treatment followed by a decarburization treatment and a final one stage anneal or heat treatment at a temperature of about 1175 C. to produce an improved crystal orientation.
  • a two-stage heat treatment or anneal after the final cold rolling and decarburization stages by means of which better magnetic qualities are achieved than in the prior one-stage final anneal.
  • the optimum temperature range for the nucleation or appearance and growth of crystals in most magnetic cold rolled silicon steels with from about 1.5 to 4% silicon and low impurities falls between about 850 C. to 900 C. with the optimum mean temperature at about 875 C.
  • the 875 C. temperature is somewhat above the temperature of nucleation or first appearance of well oriented, i. e. (110) [001], crystals which usually occurs at about 850 C., but the rate of growth at such a low temperature is too slow from the practical viewpoint.
  • the growth of well oriented crystals is rapid enough to give complete crystal growth in from about i to 24 hours depending upon the specific steel composition. It has also been noted that at 875 C.
  • the nucleation and growth of well oriented crystals is still definitely favored as against the formation and growth of poorly oriented crystals, a condition which still exists in a comparative sense at 900 C.
  • the poorly oriented crystals growth has increased to the point where the percentage of crystals with preferred orientation and magnetic quality has proportionately decreased.
  • the purpose of the present invention is to obtain a growth of the maximum number of favorably oriented crystals without encouraging the growth of such numbers of poor magnetic crystals as will detract appreciably from the overall magnetic improvement.
  • This result can be obtained by a heat treatment between 850 C. and 900 C. for the above material with the optimum temperature at about 875 C.
  • the material should be maintained at the 850 C. to 900 C. temperature until the great majority or at least 75% of the fine-grained matrix has been absorbed by (110) [001] crystals which condition will usually occur within about 4 to 24 hours depending upon the particular steel being treated.
  • the temperature may bevaried rather widely from about 900 C. to about 1l'75 C. depending upon such factors as the length of time economically available and desirable for treatment, the temperature attainable with furnaces on hand, the problem of laminations sticking together, and other considerations.
  • Heat treatment at temperature slightly below 1000 C., realizable at low cost in many furnaces, will obviate the sticking together of stacked laminations without specialtreatment and will assure any desired completion of crystal growth, per-- fection of the texture of the strip or absorption of any remaining crystallites and the relief of most mechanical strains in from about one to eight hours depending upon the constituents in the steel.
  • the best temperature for the second step of the heat treatment one which will afford any necessary further crystal growth, perfection of the well oriented crystals as well as complete relief of mechanical strain in a very are hydrogen, nitrogen, helium and various partially combusted or cracked gases.
  • the final texture perfecting stage for preferably oriented crystals and the relief of me- 5 chanical strain is carried out at temperatures ranging from 900 C. to about 1200 C. depending upon the factors mentioned heretofore. Any necessary completion of crystal growth will likewise occur in this stage.
  • a temperature of 980 C. for eight hours will afford maximum crystal growth and absorption of small crystallites and relieve most strains.
  • holding at 1175" C. for about one hour will give maximum crystal size if growth has not already been completed in the first stage, perfect the texture and relieve all mechanical strain.
  • the two stage heat treatment according to the present invention may be carried on continuously in one cycle or the material may be cooled in the usual manner after the first part and the final part resumed at any convenient time.
  • the first set of figures is for steel with a final single anneal at 1175 C. for several hours, followed by data for a two part anneal first at 875 C. for about 8 hours followed by heating at 980 C. for about eight hours which is not comletely effective in eliminating all mechanical :3. strain.
  • the last set of results is for steel of the same composition which has been held at 875 C. for about 8 hours followed by treatment at 1175 C. for about one hour.
  • the final rolled and decarburized product is heat treated preferably in a reducing (or nonoxidizing) atmosphere at a temperature of from 850 C. to 900 C. with a preferable mean tern perature of 875 C. for from about 4 hours to 24 hours, or until at least about of the finegrained matrix has been absorbed by vre1loriented crystals. In the case of the preferred steel this will occur in about 23 hours.
  • Gases which will afford a reducing or non -oxidizing atmosphere suitable for this stage of the treatment qualities of cold rolled silicon steel strip are developed by a two stage final anneal at temperatures of 875 C. and 980 C. to essentially the same degree and more cheaply than with a single 1175 C. anneal.
  • the method of heat treating cold rolled silicon steel strip containing 1.5 to 4% silicon which has been decarburized at about 800 C. which method comprises holding the strip in a temperature range of from 850 to 900 C. which encourages the nucleation or first appearance and growth of (110) [001] crystals until at least 75% of the fine grained matrix has been absorbed by the growth of such crystals followed by heat treatment at a higher temperature of from 900 to 1200 C. which will permit further growth of the (110) [001] crystals and perfection of the texture of said cold rolled strip and relieve mechanical strain.
  • the method of heat treating cold rolled silicon steel strip containing 1.5 to 4% silicon which comprises decarburizing said cold rolled strip at about 800 C. holding the strip at a temperature of from 850 C. to 900 C. in a non-0X idizing atmosphere for from about four to about twenty-four hours and thereafter subjecting the strip to a heat treatment at a higher temperature between 900 C. and about 1000 C. in-a reducing atmosphere for from about one to eight hours.
  • the method of heat treating cold rolled silicon steel strip containing 1.5 to 4% silicon which comprises decarburizing the strip at 800 C. and thereafter subjecting the strip to a temperature of from 850 C. to 900 C. in a non-oxidizing atmosphere for from four to about twenty-four hours followed by treatment in a reducing atmosphere at a higher temperature of from 900 C. to 1000 C. for from about one to eight hours.
  • silicon which has been cold reduced from about 0.10 inch to about 0.014 inch in two stages separated by a continuous anneal at about 925 C. the final cold reduction being of the order of 50%; which comprises decarburizing the cold rolled strip material at 800 C. and thereafter holding the final rolled and decarbonized material at a temperature of from about 850 C. to about 900 C. in a non-oxidizing atmosphere for from about 4 to about 24 hours followed by a heat treatment in a reducing atmosphere at about 1175 C. for about one hour.

Landscapes

  • Engineering & Computer Science (AREA)
  • Chemical & Material Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Electromagnetism (AREA)
  • Manufacturing & Machinery (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)

Description

Patented Dec. 12, 1950 HEAT-TREATMENT OF GOLD ROLLED SILICON STEEL STRIP Weston Moi-rill and Cecil G. Dunn, Pittsfield, Mass, and Raymond Ward, Richland, Wash, assignors to General Electric Company, a corporation of New York No Drawing. Appiication January 14, 1948, Serial No. 2,327
7 Claims.
This invention relates to silicon steel. More particularly it relates to a method of heat treating cold rolled silicon steel strip to enhance its magnetic qualtities.
In the production of magnetic cold rolled silicon steel strip a usual practice comprises cold rolling the material in one or more stages from a thickness of about 0.10 to about 0.014" with intervening heat treatment followed. by a decarburia ing heat treatment and a final single stage texture developing and mechanical strain relieving heat treatment at a temperature in exces of 1100" C. The final structure consists of well-oriented, i. e. (110) [001], crystals mixed with more or less poorly oriented crystals. The ultimate goal in the various processings and heat treatment is to attain the maximum preferred (110) [001] magnetic crystal orientation in the steel, thus en- I hancing its application and use in electro-mag netic products.
An object or the present invention is to provide a method for further improving the magnetic characteristics of cold rolled silicon steel strip.
More specifically an object of the invention is to provide a two-stage final texture developing anneal which will improve the magnetic orientation of the crystals in cold rolled silicon steel.
Other objects will become apparent and the invention wil1 be better understood from the following description, and the features of novelty which characterize the invention will be pointed out in the claims annexed to and forming a part of this specification.
It has been found that a material of superior magnetic qualities can be obtained by subjecting the silicon strip as it comes from the final cold rolling stage and after decarburization to a two part heat treatment which comprises holding it for a time at a temperature which encourages and permits the nucleation or first appearance of Well oriented crystals and their growth at the expense of the suitably prepared matrix and then holding at a temperature which will permit the completion of growth of any well oriented crystals which have not already attained maximum size to develop the maximum metal texture.
More specifically it has been found that holding a cold rolled -silicon steel strip containing about 1.5% to 4% silicon with low impurities after it comes from the final rolling and decarburization stages at a temperature of about 850 C. to 900 C. preferably in a reducing or non-oxidizing atmosphere for a period of time sufficient to permit the nucleation or first appearance and preliminary growth of crystals of preferred magnetic orientation, and then holding it at a tempera-' ture ranging from 900 C. to about 1200 C. preierably in reducing atmosphere to permit the maximum growth of such preferably oriented crystals which have not completed their growth and to developthe metal texture by bringing about the absorption of any remainin crystallites results in a material having enhanced magnetic characteristics and freedom from mechanical strain. The lower temperatures for the final treatment normally take a longer time to accomplish the result than the higher temperatures.
In accordance with prior practice the silicon steel strip is usually reduced to final thickness in one or more stages separated by heat treatment normally at a temperature under 1000 C.,
followed by a decarburization treatment and a final one stage anneal or heat treatment at a temperature of about 1175 C. to produce an improved crystal orientation. In the present invention there is employed a two-stage heat treatment or anneal after the final cold rolling and decarburization stages by means of which better magnetic qualities are achieved than in the prior one-stage final anneal.
It has been found that the optimum temperature range for the nucleation or appearance and growth of crystals in most magnetic cold rolled silicon steels with from about 1.5 to 4% silicon and low impurities falls between about 850 C. to 900 C. with the optimum mean temperature at about 875 C. The 875 C. temperature is somewhat above the temperature of nucleation or first appearance of well oriented, i. e. (110) [001], crystals which usually occurs at about 850 C., but the rate of growth at such a low temperature is too slow from the practical viewpoint. At 875 C. the growth of well oriented crystals is rapid enough to give complete crystal growth in from about i to 24 hours depending upon the specific steel composition. It has also been noted that at 875 C. the nucleation and growth of well oriented crystals is still definitely favored as against the formation and growth of poorly oriented crystals, a condition which still exists in a comparative sense at 900 C. However, at about 925 C. the poorly oriented crystals growth has increased to the point where the percentage of crystals with preferred orientation and magnetic quality has proportionately decreased. The purpose of the present invention is to obtain a growth of the maximum number of favorably oriented crystals without encouraging the growth of such numbers of poor magnetic crystals as will detract appreciably from the overall magnetic improvement. This result can be obtained by a heat treatment between 850 C. and 900 C. for the above material with the optimum temperature at about 875 C. The material should be maintained at the 850 C. to 900 C. temperature until the great majority or at least 75% of the fine-grained matrix has been absorbed by (110) [001] crystals which condition will usually occur within about 4 to 24 hours depending upon the particular steel being treated.
After a preponderant number of well oriented crystals have been produced in the strip, it is subjected to higher temperatures to complete the maximum growth of any crystals which have not already attained maximum size, to absorb any remaining small crystallites to make the large well oriented crystals more perfect, and to relieve strain. The temperature may bevaried rather widely from about 900 C. to about 1l'75 C. depending upon such factors as the length of time economically available and desirable for treatment, the temperature attainable with furnaces on hand, the problem of laminations sticking together, and other considerations. Heat treatment at temperature slightly below 1000 C., realizable at low cost in many furnaces, will obviate the sticking together of stacked laminations without specialtreatment and will assure any desired completion of crystal growth, per-- fection of the texture of the strip or absorption of any remaining crystallites and the relief of most mechanical strains in from about one to eight hours depending upon the constituents in the steel. However, the best temperature for the second step of the heat treatment, one which will afford any necessary further crystal growth, perfection of the well oriented crystals as well as complete relief of mechanical strain in a very are hydrogen, nitrogen, helium and various partially combusted or cracked gases.
The final texture perfecting stage for preferably oriented crystals and the relief of me- 5 chanical strain is carried out at temperatures ranging from 900 C. to about 1200 C. depending upon the factors mentioned heretofore. Any necessary completion of crystal growth will likewise occur in this stage. For the above material holding at a temperature of 980 C. for eight hours will afford maximum crystal growth and absorption of small crystallites and relieve most strains. On the other hand, holding at 1175" C. for about one hour will give maximum crystal size if growth has not already been completed in the first stage, perfect the texture and relieve all mechanical strain.
The two stage heat treatment according to the present invention may be carried on continuously in one cycle or the material may be cooled in the usual manner after the first part and the final part resumed at any convenient time.
Employing the present two-part final anneal for a cold rolled silicon steel strip of the composition described above, as compared with the prior practice, there have been obtained the results set forth in the magnetization data below. The first set of figures is for steel with a final single anneal at 1175 C. for several hours, followed by data for a two part anneal first at 875 C. for about 8 hours followed by heating at 980 C. for about eight hours which is not comletely effective in eliminating all mechanical :3. strain. The last set of results is for steel of the same composition which has been held at 875 C. for about 8 hours followed by treatment at 1175 C. for about one hour.
short period or up to about one hour is a tem- 4'.) Hang: perature of about 1175 C.
actual practlce It! 15 to Start \Vltgh 10 25 0 500 1 000 I 15090 17050 a high quality open hearth silicon steel strip 0.10 inch thick containing from 1.5 %-4% silicon. Prior Method The manganese-sulfur ratio is preferably be- 43 ever s.
011170 0.).-- .035 .009 .094 .170 .00 0.0 tween 2.1 and 4.1 Wlbh manganese not over present 0.06% and sulfur not over 0.025%. The material & l" 051 98 is cold rolled from 0.10 inch to about 0.014 inch 875 G 41155;; 1 I 151 -0 in tw stages the last cold reduction being of 025 017 064 17 the order of with a 925 C. continuous anneal 50 0elk=15,500]
R d 1 C H t Watts/Lb.
CS1 11B, O'BICIVG ys OIGSlS Annegl HM Br Hc Ergs/co/cyc.
0 Prior Method 1175 o. 1 42 12050 .003 050 .449 .071 .733 Present Method s75+9s0 1 15 13000 .100 040 .408 .686 .740 Do 875+1175 0 14500 .005 I 200 .420 .010 .008
interposed between the two stages. Carbon From the above it will be seen the magnetic which in the ladle stage should be less than 0.03 is reduced to 0.005% or under by a continuous heat treatment at about 800 C.
The final rolled and decarburized product is heat treated preferably in a reducing (or nonoxidizing) atmosphere at a temperature of from 850 C. to 900 C. with a preferable mean tern perature of 875 C. for from about 4 hours to 24 hours, or until at least about of the finegrained matrix has been absorbed by vre1loriented crystals. In the case of the preferred steel this will occur in about 23 hours. Gases which will afford a reducing or non -oxidizing atmosphere suitable for this stage of the treatment qualities of cold rolled silicon steel strip are developed by a two stage final anneal at temperatures of 875 C. and 980 C. to essentially the same degree and more cheaply than with a single 1175 C. anneal. On the other hand heat treatment after the final cold rolling stage for about 8 hour at 875 C. followed by a one hour treatment at 1175" C. gives definitely better results as concerns values of H for varying B where 3: 11; lower hysteresis loss and a substantial reduction in watt losses per pound.
What we claim as new'and desire to secure by Letters Patent of the United States is:
1. The method of heat treating cold rolled silicon steel strip containing 1.5 to 4% silicon which has been decarburized at about 800 C. which method comprises holding the strip in a temperature range of from 850 to 900 C. which encourages the nucleation or first appearance and growth of (110) [001] crystals until at least 75% of the fine grained matrix has been absorbed by the growth of such crystals followed by heat treatment at a higher temperature of from 900 to 1200 C. which will permit further growth of the (110) [001] crystals and perfection of the texture of said cold rolled strip and relieve mechanical strain.
2. The method of heat treating cold rolled silicon steel strip containing 1.5 to 4% silicon which comprises decarburizing said cold rolled strip at about 800 C. holding the strip at a temperature of from 850 C. to 900 C. in a non-0X idizing atmosphere for from about four to about twenty-four hours and thereafter subjecting the strip to a heat treatment at a higher temperature between 900 C. and about 1000 C. in-a reducing atmosphere for from about one to eight hours.
3. The method of heat treating cold rolled silicon steel strip containing 1.5 to 4% silicon material which comprises decarburizing said steel at about 800 C. and thereafter holding the material at a temperature of about 875 C. for about four to twenty-four hours in a non-oxidizing atmosphere followed by heat treatment at a temperature of about 980 C. in a reducing atmosphere for about one to eight hours.
4. The method of heat treating cold rolled silicon steel strip containing 1.5 to 4% silicon which comprises decarburizing the strip at 800 C. and thereafter subjecting the strip to a temperature of from 850 C. to 900 C. in a non-oxidizing atmosphere for from four to about twenty-four hours followed by treatment in a reducing atmosphere at a higher temperature of from 900 C. to 1000 C. for from about one to eight hours.
5. The method of heat treating cold rolled silicon steel strip containing from about 1.5-4% silicon which has been cold reduced from about 0.10 inch to about 0.014 inch in two stages separated by a continuous anneal at about 925 C. the final cold reduction being of. the order of 50%; which comprises decarburizing said strip at 800 C. and thereafter holding the final rolled and decarburized material at a temperature of 6 from about 850 C. to about 900 C. in a nonoxidizing atmosphere; for from about four to about twenty-four hours followed by a heat treatment in a reducing atmosphere at a higher temperature of from about 900 C. to 1200 C. for from about one to eight hours.
6. The method of heat treating cold rolled silicon steel strip containing from about l.5%-4% silicon which has been cold reduced from about 0.10 inch to about 0.014 inch in two stages separated by a continuous anneal at about 925 C. the final cold reduction being of the order of 50%; which comprises decarburizing the cold rolled strip material at 800 C. and thereafter holding the final rolled and decarbonized material at a temperature of from about 850 C. to about 900 C. in a non-oxidizing atmosphere for from about 4 to about 24 hours followed by a heat treatment in a, reducing atmosphere at a higher temperature of from about 900 C. to about 1000 C. for from about one hour to about 8 hours.
7. The method of heat treating cold rolled silicon steel strip containing from about 1.5%4%
. silicon which has been cold reduced from about 0.10 inch to about 0.014 inch in two stages separated by a continuous anneal at about 925 C. the final cold reduction being of the order of 50%; which comprises decarburizing the cold rolled strip material at 800 C. and thereafter holding the final rolled and decarbonized material at a temperature of from about 850 C. to about 900 C. in a non-oxidizing atmosphere for from about 4 to about 24 hours followed by a heat treatment in a reducing atmosphere at about 1175 C. for about one hour.
, WESTON MORRILL.
CECIL G. DUNN. RAYMOND WARD.
REFERENCES CITED The following references are of record in the file of this patent:
UNITED STATES PATENTS Number Name Date 1,919,983 Merrill July 25, 1933 1,932,308 Freeland Oct. 24, 1933 2,209,687 Crafts July 30, 1940 2,264,859 Ruder Dec. 2, 1941 2,303,343 Engel Dec. 1, 1942

Claims (1)

1. THE METHOD OF HEAT TREATIN GCOLD ROLLED SILICON STEEL STRIP CONTAINING 1.5 TO 4% SILICON WHICH HAS BEEN DECARBURIZED AT ABOUT 800*C. WHICH METHOD COMPRISES HOLDING THE STRIP IN A TEMPERATURE RANGE OF FROM 850* TO 900*C. WHICH ENCOURAGES THE NUCLEATION OR FIRST APPEARANCE AND GROWTH OF (110) (001) CRYSTALS UNTIL AT LEAST 75% OF THE FINE GRAINED MATRIX HAS BEEN ABSORBED BY THE GROWTH OF SUCH CRYSTALS FOLLOWED BY HEAT TREATMENT AT A HIGHER TEMPERATURE OF FROM 900* TO 200*C. WHICH WILL PERMIT FUTHER GROWTH OF THE (110) (001) CRYSTALS AND PERFECTION OF THE TEXTURE OF SAID COLD ROLLED STRIP AND RELIEVE MECHANICAL STRAIN.
US2327A 1948-01-14 1948-01-14 Heat-treatment of cold rolled silicon steel strip Expired - Lifetime US2534141A (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
US2327A US2534141A (en) 1948-01-14 1948-01-14 Heat-treatment of cold rolled silicon steel strip

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
US2327A US2534141A (en) 1948-01-14 1948-01-14 Heat-treatment of cold rolled silicon steel strip

Publications (1)

Publication Number Publication Date
US2534141A true US2534141A (en) 1950-12-12

Family

ID=21700262

Family Applications (1)

Application Number Title Priority Date Filing Date
US2327A Expired - Lifetime US2534141A (en) 1948-01-14 1948-01-14 Heat-treatment of cold rolled silicon steel strip

Country Status (1)

Country Link
US (1) US2534141A (en)

Cited By (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE1029845B (en) * 1955-12-01 1958-05-14 Vacuumschmelze Ag Process for the production of cube texture in the manufacture of objects from iron-silicon alloys
US2875113A (en) * 1957-11-15 1959-02-24 Gen Electric Method of decarburizing silicon steel in a wet inert gas atmosphere
DE1101471B (en) * 1955-12-01 1961-03-09 Vacuumschmelze Ag Process for the production of cube texture in the manufacture of objects from iron-silicon alloys
DE1106354B (en) * 1955-12-01 1961-05-10 Vacuumschmelze Ag Process for the production of cube texture in the manufacture of objects from iron-silicon alloys
US2986485A (en) * 1958-07-28 1961-05-30 Gen Electric Annealing process for magnetic steel strip
US3069299A (en) * 1956-12-31 1962-12-18 Gen Electric Process for producing magnetic material
US3105780A (en) * 1960-09-19 1963-10-01 Gen Electric Method of decarburizing ferrous materials
US3657022A (en) * 1965-08-10 1972-04-18 Nippon Kokan Kk Process for the manufacture of cold-rolled steel strip with superior mechanical workability, especially deep forming properties
US4054471A (en) * 1976-06-17 1977-10-18 Allegheny Ludlum Industries, Inc. Processing for cube-on-edge oriented silicon steel
EP0130674A3 (en) * 1983-07-05 1985-05-15 Allegheny Ludlum Corporation Process for producing cube-on-edge oriented electromagnetic silicon steel
US4693762A (en) * 1983-07-05 1987-09-15 Allegheny Ludlum Corporation Processing for cube-on-edge oriented silicon steel
US20110219836A1 (en) * 2008-10-13 2011-09-15 Thyssenkrupp Steel Europe Ag Method for determining shape changes of a workpiece

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US1919983A (en) * 1932-03-01 1933-07-25 Gen Electric Method for producing low loss nonaging silicon steel sheets
US1932308A (en) * 1932-02-18 1933-10-24 Edward M Freeland Electrical steel
US2209687A (en) * 1938-07-25 1940-07-30 Electro Metallurg Co Sheared silicon electrical steel sheet
US2264859A (en) * 1939-02-23 1941-12-02 Gen Electric Annealing silicon steel strip
US2303343A (en) * 1941-01-14 1942-12-01 Carnegie Illinois Steel Corp Silicon steel electrical strip

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US1932308A (en) * 1932-02-18 1933-10-24 Edward M Freeland Electrical steel
US1919983A (en) * 1932-03-01 1933-07-25 Gen Electric Method for producing low loss nonaging silicon steel sheets
US2209687A (en) * 1938-07-25 1940-07-30 Electro Metallurg Co Sheared silicon electrical steel sheet
US2264859A (en) * 1939-02-23 1941-12-02 Gen Electric Annealing silicon steel strip
US2303343A (en) * 1941-01-14 1942-12-01 Carnegie Illinois Steel Corp Silicon steel electrical strip

Cited By (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE1106354C2 (en) * 1955-12-01 1973-01-04 Vacuumschmelze Ag Process for the production of cube texture in the manufacture of objects from iron-silicon alloys
DE1101471B (en) * 1955-12-01 1961-03-09 Vacuumschmelze Ag Process for the production of cube texture in the manufacture of objects from iron-silicon alloys
DE1106354B (en) * 1955-12-01 1961-05-10 Vacuumschmelze Ag Process for the production of cube texture in the manufacture of objects from iron-silicon alloys
DE1029845B (en) * 1955-12-01 1958-05-14 Vacuumschmelze Ag Process for the production of cube texture in the manufacture of objects from iron-silicon alloys
US3069299A (en) * 1956-12-31 1962-12-18 Gen Electric Process for producing magnetic material
US2875113A (en) * 1957-11-15 1959-02-24 Gen Electric Method of decarburizing silicon steel in a wet inert gas atmosphere
US2986485A (en) * 1958-07-28 1961-05-30 Gen Electric Annealing process for magnetic steel strip
US3105780A (en) * 1960-09-19 1963-10-01 Gen Electric Method of decarburizing ferrous materials
US3657022A (en) * 1965-08-10 1972-04-18 Nippon Kokan Kk Process for the manufacture of cold-rolled steel strip with superior mechanical workability, especially deep forming properties
US4054471A (en) * 1976-06-17 1977-10-18 Allegheny Ludlum Industries, Inc. Processing for cube-on-edge oriented silicon steel
EP0130674A3 (en) * 1983-07-05 1985-05-15 Allegheny Ludlum Corporation Process for producing cube-on-edge oriented electromagnetic silicon steel
US4693762A (en) * 1983-07-05 1987-09-15 Allegheny Ludlum Corporation Processing for cube-on-edge oriented silicon steel
US20110219836A1 (en) * 2008-10-13 2011-09-15 Thyssenkrupp Steel Europe Ag Method for determining shape changes of a workpiece
US8215143B2 (en) * 2008-10-13 2012-07-10 Thyssenkrupp Steel Europe Ag Method for determining shape changes of a workpiece

Similar Documents

Publication Publication Date Title
US3159511A (en) Process of producing single-oriented silicon steel
US3632456A (en) Method for producing an electromagnetic steel sheet of a thin sheet thickness having a high-magnetic induction
US2534141A (en) Heat-treatment of cold rolled silicon steel strip
JP2983128B2 (en) Manufacturing method of grain-oriented electrical steel sheet with extremely low iron loss
US3163564A (en) Method for producing silicon steel strips having cube-on-face orientation
US3959033A (en) Process for manufacturing silicon-aluminum steel sheet with oriented grains for magnetic applications, and products thus obtained
JPS60121222A (en) Production of grain-oriented silicon steel sheet
US3180767A (en) Process for making a decarburized low carbon, low alloy ferrous material for magnetic uses
US3892605A (en) Method of producing primary recrystallized textured iron alloy member having an open gamma loop
GB1266941A (en)
US3843424A (en) Normal grain growth(110)(001)textured iron-cobalt alloys
US3151005A (en) Method of producing grain-oriented electrical steel
JPS5843444B2 (en) Manufacturing method of electromagnetic silicon steel
US3096222A (en) Grain oriented sheet metal
US3144363A (en) Process for producing oriented silicon steel and the product thereof
US3147157A (en) Fabrication of magnetic material
US3574003A (en) Method of treating semi-hard magnetic alloys
JP3392579B2 (en) Manufacturing method of grain-oriented electrical steel sheet with extremely low iron loss
US4115160A (en) Electromagnetic silicon steel from thin castings
US4251296A (en) Method of preparing an oriented-low-alloy iron from an ingot of controlled sulfur, manganese and oxygen contents
US3586545A (en) Method of making thin-gauge oriented electrical steel sheet
US3115430A (en) Production of cube-on-edge oriented silicon iron
US3976517A (en) Processing for grain-oriented silicon steel
US3392063A (en) Grain-oriented iron and steel and method of making same
JPH01139722A (en) Manufacture of bidirectional oriented magnetic steel sheet