CA1197758A - Method for producing grain-oriented silicon steel - Google Patents
Method for producing grain-oriented silicon steelInfo
- Publication number
- CA1197758A CA1197758A CA000394919A CA394919A CA1197758A CA 1197758 A CA1197758 A CA 1197758A CA 000394919 A CA000394919 A CA 000394919A CA 394919 A CA394919 A CA 394919A CA 1197758 A CA1197758 A CA 1197758A
- Authority
- CA
- Canada
- Prior art keywords
- less
- steel
- ingot
- hot
- manganese
- 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
Links
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
- B21B1/24—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process
- B21B1/26—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process by hot-rolling, e.g. Steckel hot mill
-
- 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
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Materials Engineering (AREA)
- Physics & Mathematics (AREA)
- Organic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Thermal Sciences (AREA)
- Electromagnetism (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
- Soft Magnetic Materials (AREA)
Abstract
ABSTRACT OF THE DISCLOSURE
A method for producing grain oriented silicon steel wherein the steel may be hot rolled directly from ingot to hot band at lower than conventional temperatures without adversely affecting the magnetic properties thereof. In addition, the steel is characterized by a manganese to sulfur ratio less than about 2.5 and preferably about 1 to less than about 2.5. Hot rolling is conducted at a temperature of less than 2300°F and preferably 2200 to less than 2300°F. Preferably the steel contains copper in an effective amount up to 0.4% by weight and preferably about 0.2 to less than 0.58% by weight.
A method for producing grain oriented silicon steel wherein the steel may be hot rolled directly from ingot to hot band at lower than conventional temperatures without adversely affecting the magnetic properties thereof. In addition, the steel is characterized by a manganese to sulfur ratio less than about 2.5 and preferably about 1 to less than about 2.5. Hot rolling is conducted at a temperature of less than 2300°F and preferably 2200 to less than 2300°F. Preferably the steel contains copper in an effective amount up to 0.4% by weight and preferably about 0.2 to less than 0.58% by weight.
Description
7~
1 ABSTRA~T OF THE DISCLOSURE
A me~hod for producing grain oriented silicon s~eel : wherein the steel may be hot rolled directly from ingot to hot band at lower than conventional temper~tures without adversely affecting the magnetic properties thereof. In addition, the steel i characterized by a manganese to sulur ratio less than about 2.5 and preferably about 1 to less than about 2.5. Hot rolling is conducted at a temperature of less than 2300F and preferably 2200 to less than 2300F. Preferably the steel co~tain~ copper in an effec~i~e amount up to 0.4~ by weight and preferably about.O.2 to less than 0.58% by wei~ht.
~**,~.**
Grain oriented silicon steel in the form of sheets is known for use in variou~ elec~rical applica~ions, inclu~ing ~he ,manufacture of transformer cores. The ste~l is produced by ~. . .
ingot casting, heating the ingot, typically in gas-fired soaking pi~s, ~o a temperature suitable for ho~ rolling either to the form o a slab or directly ~o hot band~ The hot band, after ~nne~line a~d pi~kl ;n~ iS cold rolled in one or more stages with inter~di~te annealIng. The steel is then normalized during which decarburization is achieved. Thereafter, it is subjected to a firlal texture annealing, wherein the desired crys~al orientation is achieved. Conven~ionally, when rolled directly from -ingot to hot band the ingot ~emperature is on the order of ~450F.
During final ~ex~ure annealing the si].icon steel under goes secondary recrystallization where the aggregate of grains grow and have cube-on-edge or (110) [001] orien~ation or ~ex~ure.
' ~e377~
- 1 lnese large grains have ~heir [OOlJ axes parallel ~o the roll-ing direction and (110) faces p~rallel to ~he rolli~g plar.~.
hus, the materi21 which is in shee~ form, has 2 single direetion of easy magnetization, in the direction of rolling.
In applications for US2 of this material, and speci~.ically ~ en used in the manufac~ure of transformer cores, the material is required to have low core loss, beeause the consumption of thermal energy decreases as core loss decreases. In addition, for ease of magne~ization ~he s~eel should be charaeterized by good m~gnetic permeability.
To achieve these required magnetic properties, e.g.
core loss and magnet~c permeability, it has been necessary ~o hot roll at an ingot ~emperature on the order of 2450F.
Co~seq~e~tlys the coL,~.L ional practice is ~o hot roll from lS ingot or sla~ to hot band at te~pera~ures above about 2300~F
and up to abou~ 2550F. These extremely high ~emperatures, however, are ~i~ff ~ult t~ work wlth and specifically cr~ate probLe~s with disposal of slag which forms during ingot heating to ~hese hi:~h temp~ratures in ~he soaking pit. Also, ~he high . . .
2D hea~ing requirem~ts add ~o ~he energy cos~s o the ov2rall oper tion, i~ addition ~o incrc2sing the refrac~ory costs of the heating apparatus.
It i~ accordingly a prim~ry objeet of ~he presen~
i~vention ~o pro~ide a method for producing g~ain orien~ed silicon steel ~herein lower than conven~ional ho~ rolling ; ~emperatures m~y be used without adversely affecting ~he magnetic properties of the steel, principallv core loss a~d agnetic permeability.
1 ABSTRA~T OF THE DISCLOSURE
A me~hod for producing grain oriented silicon s~eel : wherein the steel may be hot rolled directly from ingot to hot band at lower than conventional temper~tures without adversely affecting the magnetic properties thereof. In addition, the steel i characterized by a manganese to sulur ratio less than about 2.5 and preferably about 1 to less than about 2.5. Hot rolling is conducted at a temperature of less than 2300F and preferably 2200 to less than 2300F. Preferably the steel co~tain~ copper in an effec~i~e amount up to 0.4~ by weight and preferably about.O.2 to less than 0.58% by wei~ht.
~**,~.**
Grain oriented silicon steel in the form of sheets is known for use in variou~ elec~rical applica~ions, inclu~ing ~he ,manufacture of transformer cores. The ste~l is produced by ~. . .
ingot casting, heating the ingot, typically in gas-fired soaking pi~s, ~o a temperature suitable for ho~ rolling either to the form o a slab or directly ~o hot band~ The hot band, after ~nne~line a~d pi~kl ;n~ iS cold rolled in one or more stages with inter~di~te annealIng. The steel is then normalized during which decarburization is achieved. Thereafter, it is subjected to a firlal texture annealing, wherein the desired crys~al orientation is achieved. Conven~ionally, when rolled directly from -ingot to hot band the ingot ~emperature is on the order of ~450F.
During final ~ex~ure annealing the si].icon steel under goes secondary recrystallization where the aggregate of grains grow and have cube-on-edge or (110) [001] orien~ation or ~ex~ure.
' ~e377~
- 1 lnese large grains have ~heir [OOlJ axes parallel ~o the roll-ing direction and (110) faces p~rallel to ~he rolli~g plar.~.
hus, the materi21 which is in shee~ form, has 2 single direetion of easy magnetization, in the direction of rolling.
In applications for US2 of this material, and speci~.ically ~ en used in the manufac~ure of transformer cores, the material is required to have low core loss, beeause the consumption of thermal energy decreases as core loss decreases. In addition, for ease of magne~ization ~he s~eel should be charaeterized by good m~gnetic permeability.
To achieve these required magnetic properties, e.g.
core loss and magnet~c permeability, it has been necessary ~o hot roll at an ingot ~emperature on the order of 2450F.
Co~seq~e~tlys the coL,~.L ional practice is ~o hot roll from lS ingot or sla~ to hot band at te~pera~ures above about 2300~F
and up to abou~ 2550F. These extremely high ~emperatures, however, are ~i~ff ~ult t~ work wlth and specifically cr~ate probLe~s with disposal of slag which forms during ingot heating to ~hese hi:~h temp~ratures in ~he soaking pit. Also, ~he high . . .
2D hea~ing requirem~ts add ~o ~he energy cos~s o the ov2rall oper tion, i~ addition ~o incrc2sing the refrac~ory costs of the heating apparatus.
It i~ accordingly a prim~ry objeet of ~he presen~
i~vention ~o pro~ide a method for producing g~ain orien~ed silicon steel ~herein lower than conven~ional ho~ rolling ; ~emperatures m~y be used without adversely affecting ~he magnetic properties of the steel, principallv core loss a~d agnetic permeability.
2-1 This and other objects of the invention, as ~lell as a more complete understanding thereof, may be obtained from the following description and specific examples.
Broadly, in accordance with the practice of the invention, grain oriented silicon steel of otherwise conventional composition may be hot rolled d1rectly from ingot to hot band, which hot band typically has a thickness of about 0.1" or less, if said steel has a manganese to sulfur ratio of less than about 2.S and preferably a manganese to sulfur ratio within the range of about 1 to less than about 2.5. Preferably, in accortance w~th the in~en~ion hot rolling is conducted with a s~eel having a manganese to sulfur ra~io in accordance with -the above wi~h said ingot a~ a ~emperature of 2200 to less ~han 2300F. It has been found, as will be demons~rated hereinafter by way of specific examples, ~hat these lower than normal hot rolling tcmperatures will not adversely affect ~he eore loss and ma~netic permeability of the steel if the aforementioned low mangane5e to sulfur ratios a~e adhered to. Further, in aecordance with the in~en~ion, the core loss values may be further improved i the steel contains copper in an effeotive amount up to about 0.4% by weigh~ and preferably about 0.2 to less than about 0.58% by weigh~. Hence, in hot rolling direc~ly from ingot to hot band optimum core loss and magnetic permeability values are ob~ained if ~he s~eel is characterized by both the low m~n~ne~e to sulfur ratios set for~h hereinabove as well as cont~in;ng copper within the prescribed amounts. If these teachings of ~he invention are followed the relatively high hot rolling temperatures conventionally necessarv to achieve good magnetic properties are no longer required.
Broadly, in accordance with the practice of the invention, grain oriented silicon steel of otherwise conventional composition may be hot rolled d1rectly from ingot to hot band, which hot band typically has a thickness of about 0.1" or less, if said steel has a manganese to sulfur ratio of less than about 2.S and preferably a manganese to sulfur ratio within the range of about 1 to less than about 2.5. Preferably, in accortance w~th the in~en~ion hot rolling is conducted with a s~eel having a manganese to sulfur ra~io in accordance with -the above wi~h said ingot a~ a ~emperature of 2200 to less ~han 2300F. It has been found, as will be demons~rated hereinafter by way of specific examples, ~hat these lower than normal hot rolling tcmperatures will not adversely affect ~he eore loss and ma~netic permeability of the steel if the aforementioned low mangane5e to sulfur ratios a~e adhered to. Further, in aecordance with the in~en~ion, the core loss values may be further improved i the steel contains copper in an effeotive amount up to about 0.4% by weigh~ and preferably about 0.2 to less than about 0.58% by weigh~. Hence, in hot rolling direc~ly from ingot to hot band optimum core loss and magnetic permeability values are ob~ained if ~he s~eel is characterized by both the low m~n~ne~e to sulfur ratios set for~h hereinabove as well as cont~in;ng copper within the prescribed amounts. If these teachings of ~he invention are followed the relatively high hot rolling temperatures conventionally necessarv to achieve good magnetic properties are no longer required.
-3-7~
1 Cc-.sequentl~, b~ the use of lower ~.an nor~.al .olli~g -e=?~râtu-es .he disadvant2ges fro~. the processing a~.~ c-s S G?.d?Oin~ as discussed hereinabc~Je ~.-a~ be avoideG. ~ re~o-~
the invention provides a practice ;~herein a graln orie~.~e~
silicon steel may De produced ha~-ing good ~agnetic p~o?e-ties at significan~ cost advantage over conventlcnal practice. ~-way of specific example, and specifically to demonstrate ~ne significance o manganese to sulrur ra~ios in accordance wi~h the invention on the magnetic properties of the steel, the following silicon steel com~ositions as set forth in Table I
were p~oduced and hot rolled within the range of 2200 to 2300F
TABLE I
10.8 ~lil Magnet ic Quality HR WPP
Heat C ~ S Si Al Gu B Mn Temp, F 17KB ~lQH
63~1 .030 .038 .035 3 u 04 .005 .20 . ~004 1.10 2200 .758 1854 6352 .030 .040 . ~36 3. ~5 .005 .1~ .0004 1.10 2200 .755 1850 6344 .030 .043 .035 3.00 .00~ .20 . OG04 i .20 2200 .772 1864 ~345 . Q~8 .042 .035 3. oa . oo~ .20 .0004 1.20 2200 .753 1~58 6341 .030 .042 .034 2.95 .005 .20 .0005 1. ?3 2250 .761 1845 6168 . ~33 .049 .030 ~ .12 .004 . i8 .0007 ~ .6~ 23QO .704 1845 9 .0~0 .055 .023 3.1~ .004 .18 .0~04 2.4~ 2300 .7Q4 1812 ~16~ .04~ . ~65 .0~0 3.00 .0~ .20 .0~10 3.25 2300 .882 1693 1 . The ste~ls as set forth in Table I were hot rolled directly from ingot to hot band with the hot band having a thickness on the order o 0.080 to 0.090". The ho~ band was annealed at 1650F.and cold rolled to an in~ermediate thickness of .028 to 0.030l'. The intermPdiate gage strip was annealed a~ a temperature of 1740F before cold rolling to a final gage o~ 0.108".
As may be seen from Table I, the core 19ss values (WPP, 17KB~ are improved for the steels having manganese to sulfur ratio~ less than 2.5 over steel Hea~ No. 6162 having a relatively high manganese to sulfur ratio of 3.25 which is typical of conventional steels of ~his type.
The effec~ of copper with respec~ to further improv-ing core loss is shown by the heats reported on Tabl~ II.
.
TABLE II
10 . 8 Mil MgO- Coated Ma~;ne~ic Qual ity HR WPP
He~t C ~ln S Sl Al Cu B ~ O S - Temp, F 17KB ~10ll 6369 . ~34 . ~39 . 022 3 . O . ~5 . ~9 . 0006 1 . 8û 2250 . 73~ 1~6(~
6370 . 031 . 042 . 022 3 . ~ . 0~5 . 4~ . O~Q5 1 . 90 225~ . 721 1~6 6364 . 030 . 04~ . 026 3 ~0 . Oû5 . 58 . aoo7 l . ~5 2250 . 768 -1849 6433 . 030 . 042 . 022 3 . O . ~05 . 20 . 0û14 1 . ~1 2250 . 710 1869 ~37 7 . 028 . 042 . Q21 3 ~ O . 005 . 42 . 0009 2 . 00 2~50 . 71 9 1874 6 3 7 6 . Q~9 . 047 . 074 3 . O . ~5 . 58 . 0009 1 . 96 2~50 . 763 1843 The-steeIs reported on Table II we~e hot rolled directly from ingot to hot band having a thickness o~ O . 090" .
The hot band was cold rolled to inal gage in two stages with .~ a~ intermediate anneal. Initial annealing, prior to cold rolling, was at a temperature of 1650F whereupon the material was rolled to a thickness of 0.028"; 1~ was then annealed at a : temperature of 1740F and rolled to a thickness o 0.0108".
: The material was ~hen final normalized at a tempera~ure of 1475F during which deearburization was achieved. Finally, ~he decarburized strip was conventionally coated with magnesium oxide and annealed in a hydrogen atmosphere of 2150F. As may .~ be seen from the core loss values (WPP 17KB) repor~ed in . , .
Table II the presenCQ of copper in an amount above about 0.2%
as shown by the ~t el identified as Heat 6370 shows improved core loss over steel iden~ified as Heat No. 6369 having 0.19%
r copper. The core los~ values deteriorate, hcwever, if copper is not maintained a~ a~leYel less than about 0.58%, as m~y be seen from the steel identified as Heat No. 636h, which shows a significant deterioration in core loss at a copper con~ent .~ 20 O~ 0,5~V/4, .~ :
--8~
1 Cc-.sequentl~, b~ the use of lower ~.an nor~.al .olli~g -e=?~râtu-es .he disadvant2ges fro~. the processing a~.~ c-s S G?.d?Oin~ as discussed hereinabc~Je ~.-a~ be avoideG. ~ re~o-~
the invention provides a practice ;~herein a graln orie~.~e~
silicon steel may De produced ha~-ing good ~agnetic p~o?e-ties at significan~ cost advantage over conventlcnal practice. ~-way of specific example, and specifically to demonstrate ~ne significance o manganese to sulrur ra~ios in accordance wi~h the invention on the magnetic properties of the steel, the following silicon steel com~ositions as set forth in Table I
were p~oduced and hot rolled within the range of 2200 to 2300F
TABLE I
10.8 ~lil Magnet ic Quality HR WPP
Heat C ~ S Si Al Gu B Mn Temp, F 17KB ~lQH
63~1 .030 .038 .035 3 u 04 .005 .20 . ~004 1.10 2200 .758 1854 6352 .030 .040 . ~36 3. ~5 .005 .1~ .0004 1.10 2200 .755 1850 6344 .030 .043 .035 3.00 .00~ .20 . OG04 i .20 2200 .772 1864 ~345 . Q~8 .042 .035 3. oa . oo~ .20 .0004 1.20 2200 .753 1~58 6341 .030 .042 .034 2.95 .005 .20 .0005 1. ?3 2250 .761 1845 6168 . ~33 .049 .030 ~ .12 .004 . i8 .0007 ~ .6~ 23QO .704 1845 9 .0~0 .055 .023 3.1~ .004 .18 .0~04 2.4~ 2300 .7Q4 1812 ~16~ .04~ . ~65 .0~0 3.00 .0~ .20 .0~10 3.25 2300 .882 1693 1 . The ste~ls as set forth in Table I were hot rolled directly from ingot to hot band with the hot band having a thickness on the order o 0.080 to 0.090". The ho~ band was annealed at 1650F.and cold rolled to an in~ermediate thickness of .028 to 0.030l'. The intermPdiate gage strip was annealed a~ a temperature of 1740F before cold rolling to a final gage o~ 0.108".
As may be seen from Table I, the core 19ss values (WPP, 17KB~ are improved for the steels having manganese to sulfur ratio~ less than 2.5 over steel Hea~ No. 6162 having a relatively high manganese to sulfur ratio of 3.25 which is typical of conventional steels of ~his type.
The effec~ of copper with respec~ to further improv-ing core loss is shown by the heats reported on Tabl~ II.
.
TABLE II
10 . 8 Mil MgO- Coated Ma~;ne~ic Qual ity HR WPP
He~t C ~ln S Sl Al Cu B ~ O S - Temp, F 17KB ~10ll 6369 . ~34 . ~39 . 022 3 . O . ~5 . ~9 . 0006 1 . 8û 2250 . 73~ 1~6(~
6370 . 031 . 042 . 022 3 . ~ . 0~5 . 4~ . O~Q5 1 . 90 225~ . 721 1~6 6364 . 030 . 04~ . 026 3 ~0 . Oû5 . 58 . aoo7 l . ~5 2250 . 768 -1849 6433 . 030 . 042 . 022 3 . O . ~05 . 20 . 0û14 1 . ~1 2250 . 710 1869 ~37 7 . 028 . 042 . Q21 3 ~ O . 005 . 42 . 0009 2 . 00 2~50 . 71 9 1874 6 3 7 6 . Q~9 . 047 . 074 3 . O . ~5 . 58 . 0009 1 . 96 2~50 . 763 1843 The-steeIs reported on Table II we~e hot rolled directly from ingot to hot band having a thickness o~ O . 090" .
The hot band was cold rolled to inal gage in two stages with .~ a~ intermediate anneal. Initial annealing, prior to cold rolling, was at a temperature of 1650F whereupon the material was rolled to a thickness of 0.028"; 1~ was then annealed at a : temperature of 1740F and rolled to a thickness o 0.0108".
: The material was ~hen final normalized at a tempera~ure of 1475F during which deearburization was achieved. Finally, ~he decarburized strip was conventionally coated with magnesium oxide and annealed in a hydrogen atmosphere of 2150F. As may .~ be seen from the core loss values (WPP 17KB) repor~ed in . , .
Table II the presenCQ of copper in an amount above about 0.2%
as shown by the ~t el identified as Heat 6370 shows improved core loss over steel iden~ified as Heat No. 6369 having 0.19%
r copper. The core los~ values deteriorate, hcwever, if copper is not maintained a~ a~leYel less than about 0.58%, as m~y be seen from the steel identified as Heat No. 636h, which shows a significant deterioration in core loss at a copper con~ent .~ 20 O~ 0,5~V/4, .~ :
--8~
Claims (4)
1. In a method for producing a manganese-sulfide inhibited grain oriented silicon steel including the steps of casting an ingot, heating said ingot for hot-rolling, hot rolling said heated ingot to hot-rolled band, cold rolling said band in one or more stages with intermediate annealing, decarburization to final thickness, coating and final high-temperature texture annealing, the improvement comprising conducting said hot rolling with said ingot at a temperature of less than 2300°F and providing said steel containing about 0.20% or more sul-fur, about 0.2 to less than about 0.58% copper, by weight, and having a manganese to sulfur ratio of less than about 2.5.
2. The method of claim 1 wherein said steel has a manganese to sulfur ratio within the range of about 1 to less than about 2.5.
3. The method of claim 1 wherein said hot rolling is conducted with said ingot at a temperature of 2200 to less than 2300°F.
4. The method of claim 1, 2 or 3 wherein said steel contains copper in an effective amount up to about 0.4% by weight.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US24556681A | 1981-03-19 | 1981-03-19 | |
| US245,566 | 1981-03-19 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA1197758A true CA1197758A (en) | 1985-12-10 |
Family
ID=22927185
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA000394919A Expired CA1197758A (en) | 1981-03-19 | 1982-01-26 | Method for producing grain-oriented silicon steel |
Country Status (14)
| Country | Link |
|---|---|
| JP (1) | JPS57158322A (en) |
| KR (1) | KR830008744A (en) |
| AT (1) | ATA69782A (en) |
| BE (1) | BE892532A (en) |
| BR (1) | BR8201340A (en) |
| CA (1) | CA1197758A (en) |
| DE (1) | DE3210075A1 (en) |
| ES (1) | ES509302A0 (en) |
| FR (1) | FR2502179A1 (en) |
| GB (1) | GB2095287A (en) |
| IT (1) | IT1147814B (en) |
| PL (2) | PL128759B1 (en) |
| RO (1) | RO84750B (en) |
| SE (1) | SE8107844L (en) |
Families Citing this family (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5472521A (en) * | 1933-10-19 | 1995-12-05 | Nippon Steel Corporation | Production method of grain oriented electrical steel sheet having excellent magnetic characteristics |
| MX167814B (en) * | 1987-06-04 | 1993-04-13 | Allegheny Ludlum Corp | METHOD FOR PRODUCING GEAR ORIENTED SILICON STEEL WITH SMALL BORO ADDITIONS |
| EP0392535B2 (en) * | 1989-04-14 | 2002-10-16 | Nippon Steel Corporation | Process for preparation of grain-oriented electrical steel sheet having superior magnetic properties |
| US5261971A (en) * | 1989-04-14 | 1993-11-16 | Nippon Steel Corporation | Process for preparation of grain-oriented electrical steel sheet having superior magnetic properties |
| KR960010811B1 (en) * | 1992-04-16 | 1996-08-09 | 신니뽄세이데스 가부시끼가이샤 | Process for production of grain oriented electrical steel sheet having excellent magnetic properties |
| DE69428537T2 (en) * | 1993-11-09 | 2002-06-20 | Po Hang Iron & Steel | METHOD FOR PRODUCING STEEL SHEET WITH DIRECTIONAL MAGNETIZATION USING LOW SLAM HEATING TEMPERATURES. |
| US5855694A (en) * | 1996-08-08 | 1999-01-05 | Kawasaki Steel Corporation | Method for producing grain-oriented silicon steel sheet |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3671337A (en) * | 1969-02-21 | 1972-06-20 | Nippon Steel Corp | Process for producing grain oriented electromagnetic steel sheets having excellent magnetic characteristics |
| US3855018A (en) * | 1972-09-28 | 1974-12-17 | Allegheny Ludlum Ind Inc | Method for producing grain oriented silicon steel comprising copper |
| US3905843A (en) * | 1974-01-02 | 1975-09-16 | Gen Electric | Method of producing silicon-iron sheet material with boron addition and product |
| US3976517A (en) * | 1975-07-15 | 1976-08-24 | Allegheny Ludlum Industries, Inc. | Processing for grain-oriented silicon steel |
| US4078952A (en) * | 1976-06-17 | 1978-03-14 | Allegheny Ludlum Industries, Inc. | Controlling the manganese to sulfur ratio during the processing for high permeability silicon steel |
| US4113529A (en) * | 1977-09-29 | 1978-09-12 | General Electric Company | Method of producing silicon-iron sheet material with copper as a partial substitute for sulfur, and product |
-
1981
- 1981-12-30 SE SE8107844A patent/SE8107844L/en not_active Application Discontinuation
-
1982
- 1982-01-15 GB GB8201186A patent/GB2095287A/en not_active Withdrawn
- 1982-01-19 KR KR1019820000202A patent/KR830008744A/en unknown
- 1982-01-26 CA CA000394919A patent/CA1197758A/en not_active Expired
- 1982-01-29 IT IT47692/82A patent/IT1147814B/en active
- 1982-02-03 ES ES509302A patent/ES509302A0/en active Granted
- 1982-02-15 PL PL1982235082D patent/PL128759B1/en unknown
- 1982-02-15 PL PL23508282A patent/PL235082A1/xx unknown
- 1982-02-24 AT AT0069782A patent/ATA69782A/en not_active IP Right Cessation
- 1982-02-26 JP JP57030448A patent/JPS57158322A/en active Pending
- 1982-03-11 RO RO106877A patent/RO84750B/en unknown
- 1982-03-12 BR BR8201340A patent/BR8201340A/en unknown
- 1982-03-18 BE BE2/59634A patent/BE892532A/en not_active IP Right Cessation
- 1982-03-19 FR FR8204773A patent/FR2502179A1/en not_active Withdrawn
- 1982-03-19 DE DE19823210075 patent/DE3210075A1/en not_active Ceased
Also Published As
| Publication number | Publication date |
|---|---|
| ES8302789A1 (en) | 1983-01-16 |
| PL235082A1 (en) | 1982-09-27 |
| RO84750B (en) | 1984-09-30 |
| IT8247692A0 (en) | 1982-01-29 |
| PL128759B1 (en) | 1984-02-29 |
| KR830008744A (en) | 1983-12-14 |
| FR2502179A1 (en) | 1982-09-24 |
| GB2095287A (en) | 1982-09-29 |
| RO84750A (en) | 1984-07-17 |
| DE3210075A1 (en) | 1983-01-05 |
| JPS57158322A (en) | 1982-09-30 |
| ES509302A0 (en) | 1983-01-16 |
| BE892532A (en) | 1982-09-20 |
| BR8201340A (en) | 1983-01-25 |
| IT1147814B (en) | 1986-11-26 |
| ATA69782A (en) | 1986-07-15 |
| SE8107844L (en) | 1982-09-20 |
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