CA1119919A - Electrical steels - Google Patents
Electrical steelsInfo
- Publication number
- CA1119919A CA1119919A CA000316581A CA316581A CA1119919A CA 1119919 A CA1119919 A CA 1119919A CA 000316581 A CA000316581 A CA 000316581A CA 316581 A CA316581 A CA 316581A CA 1119919 A CA1119919 A CA 1119919A
- Authority
- CA
- Canada
- Prior art keywords
- range
- temperature
- annealed
- hot
- hot band
- 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
-
- 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
- C21D8/1261—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest following hot rolling
Landscapes
- 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)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
ABSTRACT OF THE DISLCOSURE:
A method for producing a silicon bearing steel strip for electro magnetic applications. This method comprises the steps of hot rolling to sheet a slab having by weight, 2% to 4% of silicon 0.05% to 0.1% of manganese, 0.02% to 0.035% of sulphur, 0.02% to 0.06% of carbon, 0.002% to 0.01 of nitrogen, and 0.01% to 0.1% of vanadium, together with incidental impurities, and cold rolling the hot band with a final reduction of at least 70% before decarburising at a temperature within the range 900 to 1050°C. Advantageously, the magnetic properties of the strip derived from the above-listed, starting material may be up-grated by suitable selection of the process parameters.
A method for producing a silicon bearing steel strip for electro magnetic applications. This method comprises the steps of hot rolling to sheet a slab having by weight, 2% to 4% of silicon 0.05% to 0.1% of manganese, 0.02% to 0.035% of sulphur, 0.02% to 0.06% of carbon, 0.002% to 0.01 of nitrogen, and 0.01% to 0.1% of vanadium, together with incidental impurities, and cold rolling the hot band with a final reduction of at least 70% before decarburising at a temperature within the range 900 to 1050°C. Advantageously, the magnetic properties of the strip derived from the above-listed, starting material may be up-grated by suitable selection of the process parameters.
Description
This invention rela-tes to the production of grain oriented silicon steels intended for electromagne-tic appli-cations. ~ore specifically the invention is concerned with such steels having a " cube on edge" texture or in terms of Miller indices a (110~ ~0~ tex-ture. Such steels are used primarily as the core material for trans-formers and other electric machines and it is desirable that they should be characterised by a high magnetic permeabill-ty together with a low core loss at a given flux density.
Such magnetic properties may be optimised by adop-ting a process in which individual grains within a polycrys-talline sheet of the steel become aligned with the crystalline directions yielding the best magnetic properties lying in the plane of the sheet and parallel to -the rolling direction.
One conventional process for producing grain oriented steel sheets is based on the recognition that a fine dispersed precipitate of manganese sulphide is res-ponsible for producing a final well oriented grain structure.
The present invention is based on -the appreciation that this dispersion of manganese sulphide may be supplemented by a precipitate of vanadium nitride and that -the magnetic properties of strip derived from a starting material containing these two preci.pitates may be up graded by sui-table of process parameters. .
~ccording to the p:resent invention, there is proposcd a method of producing silicon steel strip intended for electromagnetic applicat.ions comprises hot rolling to sheet a slab having by weight, 2% to 4~ of silicon, 0~05%
to 0.1'~ of manganese, 0.02~ to 0.035~ of sulphur, 0~02%
to 0.06% of carbon, 0.002% to 0.01~
oE ni-trog~ell, an(l 0.01% -to 0.1% oI vanac~ nl togethel with illC'i.-denta] impurities, and cold rolling the hot band with a final reduc-tion o~ at least 70% be~ore decarburising at a temperature within ~he range 900 to 1050C.
Preferably the cold reduction is in a single stage. In -this case the hot balld must be annealed suitably at a temperature within the range 900 to 1100C and selectively cooledO
Al-ternatively9 -two stage cold reduction with an intermediate anneal may be employedO In this case the intermediate anneal should be the same as the hot band anneal, followed by the same selective cooling, and the hot band anneal may be omitted if desired. The second cold reduction must be at least 70%.
Suitably the slab is reheated and hot rolled to a gauge in the range 1.90 - 3.00 mm. and pre~erably 2.30 - 2.85 mm.
which permits a higher cold reduction when rolling to the commercially desirable ~inal gauges within the range ,28 .35mm.
The hot band is then side-trimmed and continuously annealed a~ a temperature in the range 900 to 1100C for between
Such magnetic properties may be optimised by adop-ting a process in which individual grains within a polycrys-talline sheet of the steel become aligned with the crystalline directions yielding the best magnetic properties lying in the plane of the sheet and parallel to -the rolling direction.
One conventional process for producing grain oriented steel sheets is based on the recognition that a fine dispersed precipitate of manganese sulphide is res-ponsible for producing a final well oriented grain structure.
The present invention is based on -the appreciation that this dispersion of manganese sulphide may be supplemented by a precipitate of vanadium nitride and that -the magnetic properties of strip derived from a starting material containing these two preci.pitates may be up graded by sui-table of process parameters. .
~ccording to the p:resent invention, there is proposcd a method of producing silicon steel strip intended for electromagnetic applicat.ions comprises hot rolling to sheet a slab having by weight, 2% to 4~ of silicon, 0~05%
to 0.1'~ of manganese, 0.02~ to 0.035~ of sulphur, 0~02%
to 0.06% of carbon, 0.002% to 0.01~
oE ni-trog~ell, an(l 0.01% -to 0.1% oI vanac~ nl togethel with illC'i.-denta] impurities, and cold rolling the hot band with a final reduc-tion o~ at least 70% be~ore decarburising at a temperature within ~he range 900 to 1050C.
Preferably the cold reduction is in a single stage. In -this case the hot balld must be annealed suitably at a temperature within the range 900 to 1100C and selectively cooledO
Al-ternatively9 -two stage cold reduction with an intermediate anneal may be employedO In this case the intermediate anneal should be the same as the hot band anneal, followed by the same selective cooling, and the hot band anneal may be omitted if desired. The second cold reduction must be at least 70%.
Suitably the slab is reheated and hot rolled to a gauge in the range 1.90 - 3.00 mm. and pre~erably 2.30 - 2.85 mm.
which permits a higher cold reduction when rolling to the commercially desirable ~inal gauges within the range ,28 .35mm.
The hot band is then side-trimmed and continuously annealed a~ a temperature in the range 900 to 1100C for between
2 and 5 minutes. A pre~erable range is 950 to 1075C.
It has been found that selection of the cooling rate a~ter this anneal is important ~or the vanadium bearing steel in obtaining the best final magnetic properties. A cooling rate of 5 16C/sec down to a temperature in the range 750 to 900 C gives optimum results, followed by more rapid cooling down to substantially room temperature, such as natural air cooling, ~orced air or gas jet cooling, or water spray cooling, This represents a two stage cooling cycle and may be associated Wit}l the need to precipitate vanadium nitride in a speci~ic morphology a~ter hot band annealing, but to prevent ~urther particle coarsening which may occur during a prolonged cool to room temperature.
After hot balld anneallng tl~ steel is piclcled and cold-rolled to final ga-uge~ with or wi.~hout low-temperature ageing during the rolling~ in such a ~ay that the final cold reduction is between 70 and 95%. After cold-rvlling the steel is decarburised on a continuous annealing line in an atmosphere o wet hydrogen or a wet nitrogen/hydrogen mixture and at a temperature in the range 900-1050C and preferably 950-1050C
for about 4 minutesO ~his decarburisation temperature ran~e is distinctly higher than the 800-850C range conventionally used for grain-oriented steel production and has been found to overcome the difficulties in obtaining complete secondary recrystallisation in this material when using conventional and relatively lower temperature decarburising. A~ter decarburi-sation the strip is magnesia coated and box-annealed at a temperature above 1100C for some 24 hours.
Examples of the invention will now be described:
Example 1 A steel melt derived from an open hearth refining process was innoculated in the ladle with vanadium to given an overall composition of 0.022% carbon, 0.026% sulphur, 0.0056% nitrogen, 0~092% manganese, 2.86% silicon and 0.062% vanadium the balance being iron and incidental impuritiesn Slabs made from ingo~s of this composition were reheated at 1400C and rolled to hot-band of 2.85mm thickness at a finish temperature of 960C. The ho~-band which now contained dispersed precipitates of mar.ganese sulphide and vanadi.um nitride as grain-grow~h inhibitors, was - ~
L99~L~
annealed at 1050 C for S minutes~ cooled to 850~C at an average rate of 10,5C/sec an~ oil-queTIched to room temperature.
The material was cold-rolled to a final gauge of .35mm and du~ing rolling an ageing anneal of 200C for 5 minutes was applied to the material at 6 equispaced gauges during the reduction. After cold reduction the strip was decarburised at 1050C for 4 minutes in hydrogen with a dew-point of ~ 60C prior to coating and box-annealing in conventional manner. A steel produced by this method gave a core loss of 1~30 Wjkg at 107T and 50 Hz and a permeability of 1.92T at H=l.0 kA/m.
Example 2 Hot-band stock produced as above was annealed at 1000C for 5 minutes, cooled to 850C at 7.7C/sec and oil-quenched~ After cold-rolling to .35mm with a similar ageing sequence~ and decarburising at 1050C for 5 minutes, the strip was coated and box-annealed in the conventional rnanner. This steel had a core loss of la34 W/kg at 1.7T and 50Hz and a permeability o~ 1.8gT
at Ha 1~ 0 kA/m~ f .
Example 3 Hot-band stock produced as above was annealed at 1050C ror 5 minutes, cooled to 750~C at a rate of ll.O~C/sec and cold-rolled to .35mm using the ageing sequence described above. After decarburising at 1050C for 5 minutes, the strip was coated and box-annealed in the conventional manner. This steel had a core loss of 1~39 W/kg at 1,7T and 50 Hz and a permeability o~ 1,89T
at H= 100 kA/m.
~xample 4 Hot-band stock produced according to example 1 was annealed at 1000C for 2 minutes3 cooled to 900C in air at 15C/~ then quenched ~nto oil at about room temperature~ The annealed hot-band was then cold-rolled with an ~g~ing treatme~t to .35mm decarburised at 1000C for 4 minutes and box-annealed at 1200C
for 24 hours. Steel made in this way had a core loss at 1.7T and 50Hæ of 1.32 W/kg and a permeability of 1.89T at }I= 1~0 kA/m.
Example 5 Hot-band was processed as in example 4, except that after initial annealing the hot-band was cooled at 6C/s to 900C then quenched into oil at about room temperature. The steel made in this way ha~ a core loss at 1.7T and 50Hz of 1 34 ~/kg and a permeability of 1.89T at H= 1.0 kA/m..
Example 6 ~ot-band stock made according to example 1 was annealed at 1050C
for 2 minutes and cooled to 900C at 8C¦s before quenching into oil at substantially room temperature. The annealed hot-band was then cold-rolled with ageing to ~35mmg decarburised at 1050C
for 4 minut s and box-annealed at 1200C for 24 hoursO Steel made by this route had a core loss of 1.30 W~kg at 1.7T and 50 Hz, and a permeability at H= 1.0 kA/m of 1.93T.
Example 7 Hot-band made as in example 1 was initial annealed a~ 1025C
for 2 mlnutes, and cooled to 900C in air at 16~/s and oil-quenched to room temperature. The annealed hot-band was then cold-rolled with ageing, decarburised at 1050C for 4 minutes and box-annealed at 1200C ~or 24 hours. Steel made in this way had a core Loss of 1037 W/kg at 107T and 50 Hz and a permeability at H= 1.O kA/m of 1.88T.
5_ Example 8 The same hot-band stoclc was processed as in example 7 except that the decarburisation was carried out at 1000C for 4 minutes.
This steel llad a core loss of 1.34 W/kg at 1.7T and 50Hz and a permeability at ~ 0 kAtm of 1.89r.
Example 9 A sample of steel from the stock as in example 1 was annealed at 950C for 5 minutes, cooled to 850C at 5C/sec and forced a~r cooled to room temperature~ The sample was cold-rolled witho-lt ageing, decarburised at 1050C for 4 minutes and box-annealed at 1200C for 24 hours. Steel processed on this route had a core loss at 1.7T and 50Hz of 1.36 Wlkg, and a permeability of l.91T.
, ' .
: ~
.' ' '. '.' - ~
It has been found that selection of the cooling rate a~ter this anneal is important ~or the vanadium bearing steel in obtaining the best final magnetic properties. A cooling rate of 5 16C/sec down to a temperature in the range 750 to 900 C gives optimum results, followed by more rapid cooling down to substantially room temperature, such as natural air cooling, ~orced air or gas jet cooling, or water spray cooling, This represents a two stage cooling cycle and may be associated Wit}l the need to precipitate vanadium nitride in a speci~ic morphology a~ter hot band annealing, but to prevent ~urther particle coarsening which may occur during a prolonged cool to room temperature.
After hot balld anneallng tl~ steel is piclcled and cold-rolled to final ga-uge~ with or wi.~hout low-temperature ageing during the rolling~ in such a ~ay that the final cold reduction is between 70 and 95%. After cold-rvlling the steel is decarburised on a continuous annealing line in an atmosphere o wet hydrogen or a wet nitrogen/hydrogen mixture and at a temperature in the range 900-1050C and preferably 950-1050C
for about 4 minutesO ~his decarburisation temperature ran~e is distinctly higher than the 800-850C range conventionally used for grain-oriented steel production and has been found to overcome the difficulties in obtaining complete secondary recrystallisation in this material when using conventional and relatively lower temperature decarburising. A~ter decarburi-sation the strip is magnesia coated and box-annealed at a temperature above 1100C for some 24 hours.
Examples of the invention will now be described:
Example 1 A steel melt derived from an open hearth refining process was innoculated in the ladle with vanadium to given an overall composition of 0.022% carbon, 0.026% sulphur, 0.0056% nitrogen, 0~092% manganese, 2.86% silicon and 0.062% vanadium the balance being iron and incidental impuritiesn Slabs made from ingo~s of this composition were reheated at 1400C and rolled to hot-band of 2.85mm thickness at a finish temperature of 960C. The ho~-band which now contained dispersed precipitates of mar.ganese sulphide and vanadi.um nitride as grain-grow~h inhibitors, was - ~
L99~L~
annealed at 1050 C for S minutes~ cooled to 850~C at an average rate of 10,5C/sec an~ oil-queTIched to room temperature.
The material was cold-rolled to a final gauge of .35mm and du~ing rolling an ageing anneal of 200C for 5 minutes was applied to the material at 6 equispaced gauges during the reduction. After cold reduction the strip was decarburised at 1050C for 4 minutes in hydrogen with a dew-point of ~ 60C prior to coating and box-annealing in conventional manner. A steel produced by this method gave a core loss of 1~30 Wjkg at 107T and 50 Hz and a permeability of 1.92T at H=l.0 kA/m.
Example 2 Hot-band stock produced as above was annealed at 1000C for 5 minutes, cooled to 850C at 7.7C/sec and oil-quenched~ After cold-rolling to .35mm with a similar ageing sequence~ and decarburising at 1050C for 5 minutes, the strip was coated and box-annealed in the conventional rnanner. This steel had a core loss of la34 W/kg at 1.7T and 50Hz and a permeability o~ 1.8gT
at Ha 1~ 0 kA/m~ f .
Example 3 Hot-band stock produced as above was annealed at 1050C ror 5 minutes, cooled to 750~C at a rate of ll.O~C/sec and cold-rolled to .35mm using the ageing sequence described above. After decarburising at 1050C for 5 minutes, the strip was coated and box-annealed in the conventional manner. This steel had a core loss of 1~39 W/kg at 1,7T and 50 Hz and a permeability o~ 1,89T
at H= 100 kA/m.
~xample 4 Hot-band stock produced according to example 1 was annealed at 1000C for 2 minutes3 cooled to 900C in air at 15C/~ then quenched ~nto oil at about room temperature~ The annealed hot-band was then cold-rolled with an ~g~ing treatme~t to .35mm decarburised at 1000C for 4 minutes and box-annealed at 1200C
for 24 hours. Steel made in this way had a core loss at 1.7T and 50Hæ of 1.32 W/kg and a permeability of 1.89T at }I= 1~0 kA/m.
Example 5 Hot-band was processed as in example 4, except that after initial annealing the hot-band was cooled at 6C/s to 900C then quenched into oil at about room temperature. The steel made in this way ha~ a core loss at 1.7T and 50Hz of 1 34 ~/kg and a permeability of 1.89T at H= 1.0 kA/m..
Example 6 ~ot-band stock made according to example 1 was annealed at 1050C
for 2 minutes and cooled to 900C at 8C¦s before quenching into oil at substantially room temperature. The annealed hot-band was then cold-rolled with ageing to ~35mmg decarburised at 1050C
for 4 minut s and box-annealed at 1200C for 24 hoursO Steel made by this route had a core loss of 1.30 W~kg at 1.7T and 50 Hz, and a permeability at H= 1.0 kA/m of 1.93T.
Example 7 Hot-band made as in example 1 was initial annealed a~ 1025C
for 2 mlnutes, and cooled to 900C in air at 16~/s and oil-quenched to room temperature. The annealed hot-band was then cold-rolled with ageing, decarburised at 1050C for 4 minutes and box-annealed at 1200C ~or 24 hours. Steel made in this way had a core Loss of 1037 W/kg at 107T and 50 Hz and a permeability at H= 1.O kA/m of 1.88T.
5_ Example 8 The same hot-band stoclc was processed as in example 7 except that the decarburisation was carried out at 1000C for 4 minutes.
This steel llad a core loss of 1.34 W/kg at 1.7T and 50Hz and a permeability at ~ 0 kAtm of 1.89r.
Example 9 A sample of steel from the stock as in example 1 was annealed at 950C for 5 minutes, cooled to 850C at 5C/sec and forced a~r cooled to room temperature~ The sample was cold-rolled witho-lt ageing, decarburised at 1050C for 4 minutes and box-annealed at 1200C for 24 hours. Steel processed on this route had a core loss at 1.7T and 50Hz of 1.36 Wlkg, and a permeability of l.91T.
, ' .
: ~
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Claims (22)
1. A method for producing silicon bearing steel strip intended for electro-magnetic applications comprising hot rolling to sheet a slab having by weight, 2% to 4% of silicon, 0.05% to 0.1% of manganese, 0.02% to 0.035% of sulphur, 0.02% to 0.06% of carbon, 0.002% to 0.01% of nitrogen, and 0.01% to 0.1% of vanadium, together with incidental impurities, and cold rolling the hot band with a final reduc-tion of at least 70% before decarburising at a temperature within the range 900 to 1050°C.
2. A method as claimed in Claim 1 wherein the cold reduced strip is decarburise annealed at a temperature within the range 900 to 1050°C.
3. A method as claimed in Claim 2 wherein the decarburise anneal is at a temperature within the range 950 to 1050°C.
4. A method as claimed in Claim 3 or 4 wherein the decarburise anneal is a continuous anneal.
5. A method as claimed in Claim 1 wherein the cold reduction is in a single stage and the hot band is annealed and selectively cooled before cold reduction.
6. A method as claimed in Claim 5 wherein the hot band is annealed at a temperature within the range 900 to 1100°C.
7. A method as claimed in Claim 6 wherein the hot band is annealed at a temperature within the range 95 to 1075°C.
8. A method as claimed in Claim 5, 6 or 7 wherein the selective cooling is at a rate of 5 - 16°C per second to a temperature within the range 750 to 900°C.
9. A method as claimed in Claim 5 wherein the selective cooling is followed by rapid cooling to substantially room temperature.
10. A method as claimed in Claim 9 wherein the rapid cooling is carried out by natural or forced air, gas jet or water spray.
11. A method as claimed in Claim 1 wherein cold reduction is in two stages with an intermediate anneal followed by selective cooling.
12. A method as claimed in Claim 11 wherein the intermediate anneal is within the temperature range 900 to 1100°C.
13. A method as claimed in Claim 12 wherein the intermediate anneal is at a temperature within the range 950 to 1075°C.
14. A method as claimed in Claim 11, 12 or 13 wherein the selective cooling is at a rate of 5 - 16°C per second to a temperature within the range 750 to 900°C.
15. A method as claimed in Claim 11 wherein the selective cooling is followed by rapid cooling to substantially room temperature.
16. A method as claimed in Claim 15 wherein the rapid cooling is carried out by natural or forced air, gas jet or water spray.
17. A method as claimed in Claim 11 wherein the hot band is annealed before cold reduction.
18. A method as claimed in Claim 17 wherein the hot band is annealed at a temperature within the range 900 to 1100°C.
19. A method as claimed in Claim 18 wherein the hot band is annealed at a temperature within the range 950 to 1075°C.
20. A method as claimed in Claim 1 wherein the slab is re-heated and hot rolled to a gauge within the range 1.90 to 3.00 mm.
21. A method as claimed in Calim 20 wherein the slab is hot rolled to a gauge within the range 2.
22. A method as claimed in Claim 5 wherein the annealed hot band is cooled at a rate of 5 to 16°C per second to a temperature within the range 750 to 900°C.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| GB48596/77 | 1977-11-22 | ||
| GB48596/77A GB1594826A (en) | 1977-11-22 | 1977-11-22 | Electrical steels |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA1119919A true CA1119919A (en) | 1982-03-16 |
Family
ID=10449187
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA000316581A Expired CA1119919A (en) | 1977-11-22 | 1978-11-21 | Electrical steels |
Country Status (12)
| Country | Link |
|---|---|
| JP (1) | JPS5493622A (en) |
| AU (1) | AU538791B2 (en) |
| BE (1) | BE872142R (en) |
| CA (1) | CA1119919A (en) |
| DD (1) | DD140568A6 (en) |
| DE (1) | DE2850249A1 (en) |
| FR (1) | FR2409313B2 (en) |
| GB (1) | GB1594826A (en) |
| IT (1) | IT1160946B (en) |
| PL (1) | PL211104A1 (en) |
| SE (1) | SE427473B (en) |
| YU (1) | YU271778A (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0324230A (en) * | 1989-06-21 | 1991-02-01 | Sumitomo Metal Ind Ltd | Manufacture of grain-oriented silicon steel sheet |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| SE358413B (en) * | 1968-11-01 | 1973-07-30 | Nippon Steel Corp | |
| YU36756B (en) * | 1973-07-23 | 1984-08-31 | Centro Speriment Metallurg | Method of manufacturing unidirectional plates of silicon steel with a high magnetic induction |
| GB1512632A (en) * | 1974-03-08 | 1978-06-01 | British Steel Corp | Grain-oriented steel |
| IT1041114B (en) * | 1975-08-01 | 1980-01-10 | Centro Speriment Metallurg | PROCEDURE FOR THE PRODUCTION OF SILICON STEEL TAPES FOR MAGNETIC USE |
-
1977
- 1977-11-22 GB GB48596/77A patent/GB1594826A/en not_active Expired
-
1978
- 1978-11-20 FR FR7832604A patent/FR2409313B2/en not_active Expired
- 1978-11-20 DE DE19782850249 patent/DE2850249A1/en not_active Ceased
- 1978-11-20 BE BE191832A patent/BE872142R/en not_active IP Right Cessation
- 1978-11-21 YU YU02717/78A patent/YU271778A/en unknown
- 1978-11-21 PL PL21110478A patent/PL211104A1/en unknown
- 1978-11-21 SE SE7811978A patent/SE427473B/en not_active IP Right Cessation
- 1978-11-21 CA CA000316581A patent/CA1119919A/en not_active Expired
- 1978-11-22 JP JP14489678A patent/JPS5493622A/en active Pending
- 1978-11-22 AU AU41835/78A patent/AU538791B2/en not_active Expired
- 1978-11-22 DD DD78209252A patent/DD140568A6/en unknown
- 1978-11-22 IT IT69670/78A patent/IT1160946B/en active
Also Published As
| Publication number | Publication date |
|---|---|
| IT7869670A0 (en) | 1978-11-22 |
| DD140568A6 (en) | 1980-03-12 |
| PL211104A1 (en) | 1979-08-27 |
| FR2409313A2 (en) | 1979-06-15 |
| AU4183578A (en) | 1979-05-31 |
| GB1594826A (en) | 1981-08-05 |
| IT1160946B (en) | 1987-03-11 |
| SE427473B (en) | 1983-04-11 |
| YU271778A (en) | 1982-06-30 |
| FR2409313B2 (en) | 1985-09-13 |
| JPS5493622A (en) | 1979-07-24 |
| SE7811978L (en) | 1979-05-23 |
| AU538791B2 (en) | 1984-08-30 |
| DE2850249A1 (en) | 1979-05-23 |
| BE872142R (en) | 1979-03-16 |
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