CA1202549A - Method for producing cube-on-edge oriented silicon steel - Google Patents
Method for producing cube-on-edge oriented silicon steelInfo
- Publication number
- CA1202549A CA1202549A CA000422374A CA422374A CA1202549A CA 1202549 A CA1202549 A CA 1202549A CA 000422374 A CA000422374 A CA 000422374A CA 422374 A CA422374 A CA 422374A CA 1202549 A CA1202549 A CA 1202549A
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- CA
- Canada
- Prior art keywords
- steel
- cold rolling
- final
- cold
- annealing
- 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.)
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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
-
- 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
- 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
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Crystallography & Structural Chemistry (AREA)
- Thermal Sciences (AREA)
- Manufacturing & Machinery (AREA)
- Electromagnetism (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
- Soft Magnetic Materials (AREA)
- Metal Rolling (AREA)
Abstract
ABSTRACT OF THE DISCLOSURE
An improvement in the manufacture of cube-on-edge oriented silicon steel; the improvement comprises normalizing said steel followed by cold deformation prior to final texture annealing, whereby reduced watt loss is achieved.
An improvement in the manufacture of cube-on-edge oriented silicon steel; the improvement comprises normalizing said steel followed by cold deformation prior to final texture annealing, whereby reduced watt loss is achieved.
Description
~2a~i4~
This invention relates to a method of impxoving core loss in cube-on-edge oriented silicon steel at low inductions. More particularly, this invention relates to cold deformation of the decarburized strip before final texture annealing to reduce watt losses.
Cube-on-edge oriented silicon steel, in the form of sheets, is known for use in various electrical applications, including the manufacture of transformer cores~ With cube-on-edge silicon steel the alloy is characterized by secondary recrystallization in the ~llO)[OOlJ position, which is termed the cube-on-edge position. This material in sheet form has the direction of easy magnetization in the direction of rolling. In applications for this material, and speciflcally when used in the manufacture of transformer cores, the material is required to have re-duced watt loss, because the consumption of electrical energy decreases as watt loss decreases. Reduced watt loss may be promoted by achieving fine secondary grain size during texture annealillg.
It is accordingly an object of the present invention to provide a method whereby cube-on edge silicon steel may be provlded with a fine secondary grain or crystal structure after texture annealing, which achieves reduced watt loss.
This and other objects of the invention, as well as a more complete understanding thereof, may be obtained from the Eollowing description and speciEic ~xamples.
;25~9 1 SUMM~RY OF THE INVENTION
In accordance with the present invention~ a method is provided for reducing watt loss, including hot rolling, cold rolliny to final gauge with intermediate annealing, normalizing the steel to decarburize and effect primary recrystallization and final texture anrlealing.
The method includes uniformly providing a light cold ~deformation of the decarburized steel prior to final texture annealing to reduce grain size. The method i5 par-ticularly useful for reducing core losses at low inductionsof 15 kG or less. Also, the cold deformation may include cold rolling to effect elongations of the steel of 0.5 to 15%~ ~
DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS
With respec~ to cube-on-edge silicon steel to which the present in~ention is directed, this steel is conventionally processed by hot rolling followed by one or more cold rolling operations with intermediate anneals. After cold rolling, -~he steel is subjected to a normalizing operation to achieve primary recrystallization and decarburization. Typically, normalizing is conducted at tempPratures within the range o~ 1300 to 1600OF. In accordance with the invention, after normalizing, the steel is subjected to uniform cold deformation as by a cold-rolling operation. After cold deformation, the steel is- final texture annealed in the conventional manner to achieve secondary recrystallization. It has been found that by a light and uniform cold deforming in accordance ~ .
. . - .
1 wLth the invelltion following normalizing and prior to texture annealing, secondary grain grow~h is inhibited during final texture annealing, which results in reduced watt loss. For this purpose, cold rolliny to achieve an elongation within the range of 0.5 to 15% has been found to be effective for the purpo~e. It has been found that by varying the amount of cold reduction, the grain size after texture annealing may be regulated. Although the practice of the invention finds utility with cube~on-edge silicon steels, generally it is particularly adapted to steels of this type within the following composition limits in percent by weight:
Steel Mn C S Si B Fe .
SX-14 .025-.045 .020-.060 .005-.040 2.70-3.50 .0005-.0030 Bal.
SX-ll .050-.080 .020-.060 .020-.035 3.00 3.70 - Bal.
E~AMPLE 1 .
By way of specific example, two Heats of the alloy identified SX-14 (Heat Nos. 154684 and 153595) wexe melted to the following composition in percent by weight:
Heat No. Mn S C Si B Fe 154684 .036 .019 .028 3.21 .0011 Balance 153595 .038 .020 .025 3.25 .0013 Balance This material was processed in the conventional manner by hot rolling followed by a cold-rolling operation. Then it was subjected to a final normalizing treatment comprising continuous annealing at a temperature of 1475F ~800 C) ~which served to decarburize the steel and effect primary ~z~
1 recrystallization. The normalized steel in strip form was cut to lengths suitable for cold rolling and rolled in a 4-high cold-rolling mill at ambient temperature. The extent o~ plastic deformation was determined by measuring the percent elongation over a 24" span scribed on the steel strip be~ore cold rolling. For control purposes, samples of the steel were retained prior to cold rolling. The material was cut into s~andard Esptein strip samples and roller coated with a water slurry of MgO~ .75%B. Texture annealing was performed in dry hydrogen. The anneal cycle consisted of charging the steel into a furnace at 1400F
(760 C), heating at 50 F (28 C) per hour to 2150 F (1175 C), holding 20 hours at 2150F (1175C) and furnace cooling.
Magnetic testing and grain size measurements were made after this texture annealing operation. Table I lists the magnetic properties and grain size of the matexial tested.
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~2V~S9~9 1 The methoa of the present invention reduces both the permeability at high induction levels and the size of the grains formed during final texture annealing. The current trend in electrical steel usage is toward lower inductions and significant improvements have been made-in lowering core losses or watt losses by reducing the sheet thickness.
Commerciall~ available material typically ranges from .01 to .011 inch (r 35 to .2g mm~, and may be ~009 inch (.23 mm) and lower~
As such materials are used at l~wer inductions, on the order o~ 15 kilogauss or lower, the reduction in permeability at high inductions becomes less important in electrical e~uipment. Also, as the sheet thicknesses are reduced, core losses arising from eddy currents appear to be more dependent upon the material grain size, i.e., core losses decrease with decreasing grain size. ~he advantages of the present invention establish that it is of substantial i~portance in the manufacture of thin sheet, on the order of less than .015 inch to .004 inch (.38 to .1 mm~ thickr preferably less than .010 inch ~.25 mm) and suitable for use in transformers.
.
~2~
SUPPLEMENTARY DISCLOSUR~
In addition to the subject mat~er described in the principal disclosure~ this invention includes carr~ing out cold deformation of the decarburized steel by cold rolling to effect a reduction in area between .5% and 5~, preferably between .5% and 3%. This method i3 very effective in reducing core losses at low inductions of 15 kG or less.
The following examples show the effect of percentage reduction in area due to cold rolling upon magnetic properties of the final-texture annealed samples.
EX~MPLE 2 By Examplel, the cold reduction o~ temper rolling o~ decarburized silicon steel, demonstrates that the final annealed grain size in SX-14, compositions can be dramatically reduced. Further samples were prepared in a manner similar to the above Example to a nominal gauge o~
10 mils to determine if core losses could be improved at lower inductions. The decarburized samples which were ~0 temper rolled to the specified percent reduction in area have the properties set forth in Table II.
TABLE II
.
% Reduction Core Loss ~WPP) @
Heat Code in Area 13 KG17KG ~ @ 10 H
163012 A 0 .360 .673 1906 ~control~
B 1 .339 .629 1900 C 1 .343 .643 1896 D 3 .355 .727 1829 E 3 .348 .697 1850 F 5 ~834 .97g 1709 G 5 .810 .926 1724 `~ .
~Z~ 919 1 At a 1% reduction in area of the decarburized strip,.for Samples B and C there was a slight improvement ~lowering~ of the core loss at 17 kG and only a slight reduction in permeability at 10 oersteds. At 1~ area reduction, the core losses at.a lower.induction of 13 kG
are also improved.. Samples D and E, which were given a 3%
reduction in area, exhibited substantially increased core losses ak 17 k~ compared to.the control Sample A having 0%
reduction in axea. Th~ core losses at 13 kG are not as good as those for Samples B and C;.however, they are better than the control Sample A at 0% reducti~n in area. These impro~ements are attributable to a substantially reduced grain size resulting from the cold reduction of the de-carburi~ed strip. For Samples F and G, a severe degradation in magnetic properties.:of core..loss ~or inductions between 10 kG and 17 kG as well as for permeability at 10 H
resulted from 5% reduction ln area.
Additional samples of SX-14 were prepared and processed to nominally 9 mi.ls in a similar manner as Examples 1 and 2. The hot-rolled band was annealed at 1750F ~949C~ for about 2 minutes,. then air cooled and cold rolled to about 0.0086 inch. The samples were flnal normalized at 1475F (.800 C) in 80% N2-20% H2 atmosphere to decarburize the steel. Control samples were retained prior to cold rolling and other samples were rolled an additional 1, 2, 3 or 5% as shown in Table III. Epstein strip samples were prepared and coated with a water slurry 1 of MgO ~ 0.75% B. The samples were then final texture annealed in hydrogen in the laboratory by heating at 50F
(28~C~ per hour to 21500F (11?5C) and held for 10 hours and furnace cooled. The magnetic properties of the final texture annealed samples are shown in Ta~le III.
TABLE III
. ~ Temper _ _ Core Loss (WPP) @ . ~ @
Heat Code Roll13 KG 15 KG 17 KG 10H
189001 ~ 0 .372 .~92 .647 1900 1. .368 .503 . .6811885 3.3~9 .482 .666 1886 B 0.383 .520 .700 lB78 1.404 . .561 .816 1779 3.403 . .566 .839 1766 C 0.375 .504 .6~2 1896 1.377 .513 .686 18E7 3~361 .~97 . .68~ 1869 D 0.375 .509 .676 1887 1.373 .517 .737 183~
3.391 .551 .822 1788 E 0,380 .513 .669 1892
This invention relates to a method of impxoving core loss in cube-on-edge oriented silicon steel at low inductions. More particularly, this invention relates to cold deformation of the decarburized strip before final texture annealing to reduce watt losses.
Cube-on-edge oriented silicon steel, in the form of sheets, is known for use in various electrical applications, including the manufacture of transformer cores~ With cube-on-edge silicon steel the alloy is characterized by secondary recrystallization in the ~llO)[OOlJ position, which is termed the cube-on-edge position. This material in sheet form has the direction of easy magnetization in the direction of rolling. In applications for this material, and speciflcally when used in the manufacture of transformer cores, the material is required to have re-duced watt loss, because the consumption of electrical energy decreases as watt loss decreases. Reduced watt loss may be promoted by achieving fine secondary grain size during texture annealillg.
It is accordingly an object of the present invention to provide a method whereby cube-on edge silicon steel may be provlded with a fine secondary grain or crystal structure after texture annealing, which achieves reduced watt loss.
This and other objects of the invention, as well as a more complete understanding thereof, may be obtained from the Eollowing description and speciEic ~xamples.
;25~9 1 SUMM~RY OF THE INVENTION
In accordance with the present invention~ a method is provided for reducing watt loss, including hot rolling, cold rolliny to final gauge with intermediate annealing, normalizing the steel to decarburize and effect primary recrystallization and final texture anrlealing.
The method includes uniformly providing a light cold ~deformation of the decarburized steel prior to final texture annealing to reduce grain size. The method i5 par-ticularly useful for reducing core losses at low inductionsof 15 kG or less. Also, the cold deformation may include cold rolling to effect elongations of the steel of 0.5 to 15%~ ~
DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS
With respec~ to cube-on-edge silicon steel to which the present in~ention is directed, this steel is conventionally processed by hot rolling followed by one or more cold rolling operations with intermediate anneals. After cold rolling, -~he steel is subjected to a normalizing operation to achieve primary recrystallization and decarburization. Typically, normalizing is conducted at tempPratures within the range o~ 1300 to 1600OF. In accordance with the invention, after normalizing, the steel is subjected to uniform cold deformation as by a cold-rolling operation. After cold deformation, the steel is- final texture annealed in the conventional manner to achieve secondary recrystallization. It has been found that by a light and uniform cold deforming in accordance ~ .
. . - .
1 wLth the invelltion following normalizing and prior to texture annealing, secondary grain grow~h is inhibited during final texture annealing, which results in reduced watt loss. For this purpose, cold rolliny to achieve an elongation within the range of 0.5 to 15% has been found to be effective for the purpo~e. It has been found that by varying the amount of cold reduction, the grain size after texture annealing may be regulated. Although the practice of the invention finds utility with cube~on-edge silicon steels, generally it is particularly adapted to steels of this type within the following composition limits in percent by weight:
Steel Mn C S Si B Fe .
SX-14 .025-.045 .020-.060 .005-.040 2.70-3.50 .0005-.0030 Bal.
SX-ll .050-.080 .020-.060 .020-.035 3.00 3.70 - Bal.
E~AMPLE 1 .
By way of specific example, two Heats of the alloy identified SX-14 (Heat Nos. 154684 and 153595) wexe melted to the following composition in percent by weight:
Heat No. Mn S C Si B Fe 154684 .036 .019 .028 3.21 .0011 Balance 153595 .038 .020 .025 3.25 .0013 Balance This material was processed in the conventional manner by hot rolling followed by a cold-rolling operation. Then it was subjected to a final normalizing treatment comprising continuous annealing at a temperature of 1475F ~800 C) ~which served to decarburize the steel and effect primary ~z~
1 recrystallization. The normalized steel in strip form was cut to lengths suitable for cold rolling and rolled in a 4-high cold-rolling mill at ambient temperature. The extent o~ plastic deformation was determined by measuring the percent elongation over a 24" span scribed on the steel strip be~ore cold rolling. For control purposes, samples of the steel were retained prior to cold rolling. The material was cut into s~andard Esptein strip samples and roller coated with a water slurry of MgO~ .75%B. Texture annealing was performed in dry hydrogen. The anneal cycle consisted of charging the steel into a furnace at 1400F
(760 C), heating at 50 F (28 C) per hour to 2150 F (1175 C), holding 20 hours at 2150F (1175C) and furnace cooling.
Magnetic testing and grain size measurements were made after this texture annealing operation. Table I lists the magnetic properties and grain size of the matexial tested.
~3~
~2gJ 2~
11~ N U~ ~`1 CO ~ ~ ,1 ~1 S-l rl ~ ~
rl ~rcn rl m r~
~n _,, Q~
C~ V ~ ~ r~ ~ oo ~ co ~ ~ ~r o~a~.
o ~ ~ co ~r r~J ~D ~I~ r~ ,1 HO :: cs~ (S 00 oo 1` ~ ~ co oo t--_~
E~ 1- ~ o ~9 rr~ ,1 CO ~ ~I COS~
Voe I~ ~ I-- t-- l 1~ I --~ CS~ 1- ~ ~D t` ~ I` ~D O ) H U~~ P~ L~ r` r- ~ I` I co ~1 ~ ~`1 coo 1~1 P~ ~ I` r~ I' t-- t` 00 ~ r~ t~ co ~ ~) H ;~ ~1 a:~
a) ~ ~ ~ ~ ~ ,~ ~
;~ ~ ~ ~ ~ ~ ~ ~ o o o o cn ~
H l ~1 ~J
Z ~ ~o~
O ~ ~ o Ln ~7 ~ r` r` o Ir) u~
O O
h o ~ ~ m ~ a C~
~1 Ln ~ CO
Ln ~D
~ Ln Lr :~
. ~ ., .
~2V~S9~9 1 The methoa of the present invention reduces both the permeability at high induction levels and the size of the grains formed during final texture annealing. The current trend in electrical steel usage is toward lower inductions and significant improvements have been made-in lowering core losses or watt losses by reducing the sheet thickness.
Commerciall~ available material typically ranges from .01 to .011 inch (r 35 to .2g mm~, and may be ~009 inch (.23 mm) and lower~
As such materials are used at l~wer inductions, on the order o~ 15 kilogauss or lower, the reduction in permeability at high inductions becomes less important in electrical e~uipment. Also, as the sheet thicknesses are reduced, core losses arising from eddy currents appear to be more dependent upon the material grain size, i.e., core losses decrease with decreasing grain size. ~he advantages of the present invention establish that it is of substantial i~portance in the manufacture of thin sheet, on the order of less than .015 inch to .004 inch (.38 to .1 mm~ thickr preferably less than .010 inch ~.25 mm) and suitable for use in transformers.
.
~2~
SUPPLEMENTARY DISCLOSUR~
In addition to the subject mat~er described in the principal disclosure~ this invention includes carr~ing out cold deformation of the decarburized steel by cold rolling to effect a reduction in area between .5% and 5~, preferably between .5% and 3%. This method i3 very effective in reducing core losses at low inductions of 15 kG or less.
The following examples show the effect of percentage reduction in area due to cold rolling upon magnetic properties of the final-texture annealed samples.
EX~MPLE 2 By Examplel, the cold reduction o~ temper rolling o~ decarburized silicon steel, demonstrates that the final annealed grain size in SX-14, compositions can be dramatically reduced. Further samples were prepared in a manner similar to the above Example to a nominal gauge o~
10 mils to determine if core losses could be improved at lower inductions. The decarburized samples which were ~0 temper rolled to the specified percent reduction in area have the properties set forth in Table II.
TABLE II
.
% Reduction Core Loss ~WPP) @
Heat Code in Area 13 KG17KG ~ @ 10 H
163012 A 0 .360 .673 1906 ~control~
B 1 .339 .629 1900 C 1 .343 .643 1896 D 3 .355 .727 1829 E 3 .348 .697 1850 F 5 ~834 .97g 1709 G 5 .810 .926 1724 `~ .
~Z~ 919 1 At a 1% reduction in area of the decarburized strip,.for Samples B and C there was a slight improvement ~lowering~ of the core loss at 17 kG and only a slight reduction in permeability at 10 oersteds. At 1~ area reduction, the core losses at.a lower.induction of 13 kG
are also improved.. Samples D and E, which were given a 3%
reduction in area, exhibited substantially increased core losses ak 17 k~ compared to.the control Sample A having 0%
reduction in axea. Th~ core losses at 13 kG are not as good as those for Samples B and C;.however, they are better than the control Sample A at 0% reducti~n in area. These impro~ements are attributable to a substantially reduced grain size resulting from the cold reduction of the de-carburi~ed strip. For Samples F and G, a severe degradation in magnetic properties.:of core..loss ~or inductions between 10 kG and 17 kG as well as for permeability at 10 H
resulted from 5% reduction ln area.
Additional samples of SX-14 were prepared and processed to nominally 9 mi.ls in a similar manner as Examples 1 and 2. The hot-rolled band was annealed at 1750F ~949C~ for about 2 minutes,. then air cooled and cold rolled to about 0.0086 inch. The samples were flnal normalized at 1475F (.800 C) in 80% N2-20% H2 atmosphere to decarburize the steel. Control samples were retained prior to cold rolling and other samples were rolled an additional 1, 2, 3 or 5% as shown in Table III. Epstein strip samples were prepared and coated with a water slurry 1 of MgO ~ 0.75% B. The samples were then final texture annealed in hydrogen in the laboratory by heating at 50F
(28~C~ per hour to 21500F (11?5C) and held for 10 hours and furnace cooled. The magnetic properties of the final texture annealed samples are shown in Ta~le III.
TABLE III
. ~ Temper _ _ Core Loss (WPP) @ . ~ @
Heat Code Roll13 KG 15 KG 17 KG 10H
189001 ~ 0 .372 .~92 .647 1900 1. .368 .503 . .6811885 3.3~9 .482 .666 1886 B 0.383 .520 .700 lB78 1.404 . .561 .816 1779 3.403 . .566 .839 1766 C 0.375 .504 .6~2 1896 1.377 .513 .686 18E7 3~361 .~97 . .68~ 1869 D 0.375 .509 .676 1887 1.373 .517 .737 183~
3.391 .551 .822 1788 E 0,380 .513 .669 1892
2.37~ .515 .699 1875 5.355 .490 .670 1888 F 0.368 .499 .678 1875 1.~12 .580 .869 1752 : 3~397 .554 .~23 1776 165365 A 0 .362 .477 . .633 1906 1.365 ..488 .654 188g . - 3.342 .~58 .612 1901 B 0.350 .476 .657 1882 1.367 .509 .725 1~38
3.383 .54~ .813 1760 Samples A, C, D and E of Heat 189001 and Sample A
of Heat 165365 all exhibited at least some improvement in core loss at 13 kG induction for reductions in area up to 5%. For those same samples, the core losses at a higher induction of 17 kG were worse. Samples A and E of Heat 189001 . .
'~
~2~1254~
1 and Sample A of Heat 165365 have the most improved core losses with only slight reductions in pexmeability at 10 H.
These improvements are attributable to a reduced grain size resulting from the cGld reduction of the decarburized st~ip~
For Samples B and F of Heat 189001 and Sample B of Heat 165365, which exhibited little or no improvement in core loss at 13 kG induction, the grain size was either relatively unchanged, large or incomplete. This normally cannot be explained.
Most of the samples were temper rolled 1% or 3%, how-evex, Sample E was cold rolled 2% and 5% and showed a significant reduction in losses up to 5% reduction with only a slight reduction in permeability at 10 H~
, . . . ~
. .
of Heat 165365 all exhibited at least some improvement in core loss at 13 kG induction for reductions in area up to 5%. For those same samples, the core losses at a higher induction of 17 kG were worse. Samples A and E of Heat 189001 . .
'~
~2~1254~
1 and Sample A of Heat 165365 have the most improved core losses with only slight reductions in pexmeability at 10 H.
These improvements are attributable to a reduced grain size resulting from the cGld reduction of the decarburized st~ip~
For Samples B and F of Heat 189001 and Sample B of Heat 165365, which exhibited little or no improvement in core loss at 13 kG induction, the grain size was either relatively unchanged, large or incomplete. This normally cannot be explained.
Most of the samples were temper rolled 1% or 3%, how-evex, Sample E was cold rolled 2% and 5% and showed a significant reduction in losses up to 5% reduction with only a slight reduction in permeability at 10 H~
, . . . ~
. .
Claims (5)
1. In a method for producing cube-on-edge oriented silicon steel, characterized by reduced watt loss, including the steps of hot rolling, cold rolling with intermediate annealing to final gauge, normalizing said steel to effect decarburization and primary recrystallization and a final texture annealing to effect secondary recrystallization, the improvement comprising providing a uniform light cold rolling deformation of the decarburized steel prior to final texture annealing to reduce grain size and to effect an elongation of said steel within the range of 0.5 to 5%.
2. The method of claim 1 wherein the cold rolling of the decarburized steel includes at least one cold-rolling operation.
CLAIMS SUPPORTED BY SUPPLEMENTARY DISCLOSURE
CLAIMS SUPPORTED BY SUPPLEMENTARY DISCLOSURE
3. The method of claim 2 wherein said cold rolling of decarburized steel effects a 0.5 to 3% reduction in area.
4. In a method fox producing cube-on-edge oriented silicon steel, characterized by reduced watt loss, including the steps of hot rolling, cold rolling with intermediate annealing to final gauge, normalizing said steel to effect decarburization and primary recrystallization and a final.
texture annealing to effect secondary recrystallization, the
4. In a method fox producing cube-on-edge oriented silicon steel, characterized by reduced watt loss, including the steps of hot rolling, cold rolling with intermediate annealing to final gauge, normalizing said steel to effect decarburization and primary recrystallization and a final.
texture annealing to effect secondary recrystallization, the
Claim 4 continued...
improvement comprising providing a uniform light cold rolling deformation 0.5% to 5% reduction in area of the decarburized steel prior to final texture annealing to reduce grain size.
improvement comprising providing a uniform light cold rolling deformation 0.5% to 5% reduction in area of the decarburized steel prior to final texture annealing to reduce grain size.
5. The method of claim 4 for reducing watt losses in the steel at inductions of 15 kG or less.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US39967482A | 1982-07-19 | 1982-07-19 | |
| US399,674 | 1982-07-19 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA1202549A true CA1202549A (en) | 1986-04-01 |
Family
ID=23580516
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA000422374A Expired CA1202549A (en) | 1982-07-19 | 1983-02-25 | Method for producing cube-on-edge oriented silicon steel |
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| Country | Link |
|---|---|
| EP (1) | EP0099617B1 (en) |
| JP (1) | JPS5928523A (en) |
| KR (1) | KR860000349B1 (en) |
| BR (1) | BR8301547A (en) |
| CA (1) | CA1202549A (en) |
| DE (1) | DE3368685D1 (en) |
| PL (1) | PL242745A1 (en) |
| RO (1) | RO86076B (en) |
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| CN1084647C (en) * | 1999-11-30 | 2002-05-15 | 沈阳工业大学 | Technology for manufacturing fully-threaded bright and high-strength very long screw bolt |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB610440A (en) * | 1945-04-12 | 1948-10-15 | British Thomson Houston Co Ltd | Improvements in and relating to the production of preferred crystal orientation in thin gauge silicon steel |
| GB816705A (en) * | 1954-12-29 | 1959-07-15 | Gen Electric | Improved process for treating silicon steel |
| BE622386A (en) * | 1959-06-11 | |||
| FR1438853A (en) * | 1964-07-01 | 1966-05-13 | Yawata Iron & Steel Co | Process for producing thin extremely low carbon steel sheets |
| US3770517A (en) * | 1972-03-06 | 1973-11-06 | Allegheny Ludlum Ind Inc | Method of producing substantially non-oriented silicon steel strip by three-stage cold rolling |
| JPS5220297A (en) * | 1975-08-08 | 1977-02-16 | Nippon Steel Corp | Method of manufacture of uni-directional electromagnetic steel plate h aving excellent magnetic properties |
| 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 |
-
1983
- 1983-02-25 CA CA000422374A patent/CA1202549A/en not_active Expired
- 1983-03-03 KR KR1019830000855A patent/KR860000349B1/en active IP Right Grant
- 1983-03-04 RO RO110223A patent/RO86076B/en unknown
- 1983-03-25 BR BR8301547A patent/BR8301547A/en unknown
- 1983-04-11 DE DE8383302009T patent/DE3368685D1/en not_active Expired
- 1983-04-11 EP EP83302009A patent/EP0099617B1/en not_active Expired
- 1983-05-31 JP JP58096852A patent/JPS5928523A/en active Pending
- 1983-06-29 PL PL24274583A patent/PL242745A1/en unknown
Also Published As
| Publication number | Publication date |
|---|---|
| EP0099617A3 (en) | 1984-06-06 |
| PL242745A1 (en) | 1984-03-12 |
| EP0099617B1 (en) | 1986-12-30 |
| DE3368685D1 (en) | 1987-02-05 |
| KR860000349B1 (en) | 1986-04-12 |
| EP0099617A2 (en) | 1984-02-01 |
| RO86076B (en) | 1985-05-01 |
| RO86076A (en) | 1985-04-17 |
| KR840004173A (en) | 1984-10-10 |
| BR8301547A (en) | 1984-04-17 |
| JPS5928523A (en) | 1984-02-15 |
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