GB2095287A - Method for producing grain- oriented silicon steel - Google Patents
Method for producing grain- oriented silicon steel Download PDFInfo
- Publication number
- GB2095287A GB2095287A GB8201186A GB8201186A GB2095287A GB 2095287 A GB2095287 A GB 2095287A GB 8201186 A GB8201186 A GB 8201186A GB 8201186 A GB8201186 A GB 8201186A GB 2095287 A GB2095287 A GB 2095287A
- Authority
- GB
- United Kingdom
- Prior art keywords
- ingot
- steel
- hot
- less
- hot rolling
- 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.)
- Withdrawn
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
Abstract
The steel may be hot rolled directly from ingot to hot band at lower than conventional temperatures without adversely affecting the magnetic properties thereof, when it has a manganese to sulfur ratio of not more than 2.5 and preferably about 1 to less than 2.5. Hot rolling is conducted at a temperature of not more than 1260 DEG C (2300 DEG F) and preferably 1204 DEG C (2200 DEG F) to less than 1269 DEG C (2300 DEG 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. The composition and processing are otherwise conventional.
Description
SPECIFICATION
Method for producing grain-oriented silicon steel
This invention relates to a method for producing grain-oriented silicon steel.
Grain-oriented silicon steel in the form of sheets is known for use in various electrical applications, including the manufacture of transformer cores. The steel is produced by ingot casting, heating the ingot, typically in gas-fired soaking pits, to a temperature suitable for hot rolling either to the form of a slab or directly to hot band. The hot band, after annealing and pickling, is cold rolled in one or more stages with intermediate annealing. The steel is then normalized during which decarburization is achieved. Thereafter, it is subjected to a final texture annealing, wherein the desired crystal orientation is achieved. Conventionally, when rolled directly from ingot to hot band the ingot temperature is of the order of 1 3430C (24500 F).
During final texture annealing the silicon steel undergoes secondary recrystallization where the aggregate of grains grow and have cube-on-edge or (110) (001) orientation or texture. These large grains have their (001) axes parallel to the rolling direction and (110) faces parallel to the rolling plane.
Thus, the material which is in sheet form, has a single direction of easy magnetization, in the direction of rolling. In applications for use of this material, and specifically when used in the manufacture of transformer cores, the material is required to have low core loss, because the consumption of thermal energy decreases as core loss decreases. In addition, for ease of magnetization the steel should be characterized by good magnetic permeability.
To achieve these required magnetic properties, e.g., core loss and magnetic permeability, it has been necessary to hot roll at an ingot temperature of the order of 1 3430C (24500 F). Consequently, the conventional practice is to hot ro!l from ingot or slab to hot band at temperatures above 1 2600C (23000 F) and up to about 1 3990C (25500 F). These extremely high temperatures, however, are difficult to work with and specifically create problems with disposal of slag which forms during ingot heating to these high temperatures in the soaking pit. Also, the high heating requirements add to the energy costs of the overall operation, in addition to increasing the refractory costs of the heating apparatus.
It is accordingly a primary object of the present invention to provide a method for producing grain oriented silicon steel wherein lower than conventional hot rolling temperatures may be used without adversely affecting the magnetic properties of the steel, principally core loss and magnetic permeability.
The present invention provides a method for producing grain oriented silicon steel including the steps of casting an ingot, heating said ingot for hot-roliing, hot rolling said heated ingot to hot-rolled band, cold rolling said band in one or more stages with intermediate annealing, decarburization at final thickness, coating and final high-temperature texture annealing, the improvement comprising conducting said hot rolling with said ingot at a temperature of not more than 1 2600C (23000 F) with said steel having a manganese to sulfur ratio of not more than 2.5.
In accordance with the practice of the invention, grain oriented silicon steel of otherwise conventional composition may be hot rolled directly from ingot to hot band, which hot band typically has a thickness of about 2.54 mm (0.1") or less, if said steel has a manganese to sulfur ratio of not more than 2.5 and preferably a manganese to sulfur ratio within the range of about 1 to less than 2.5.
Preferably, in accordance with the invention hot rolling is conducted with a steel having a manganese to sulfur ratio in accordance with the above with said ingot at a temperature of 1 2040C (22000 F) to less than 1 2600C (23000 F). It has been found, as will be demonstrated hereinafter by way of specific examples, that these lower than normal hot rolling temperatures will not adversely affect the core loss and magnetic permeability of the steel if the aforementioned low manganese to sulfur ratios are adhered to. Further, in accordance with the invention, the core loss values may be further improved if the steel contains copper in an effective amount up to 0.4% by weight and preferably about 0.2 to less than about 0.58% by weight.Hence, in hot rolling directly from ingot to hot band optimum core loss and magnetic permeability values are obtained if the steel is characterized by both the low manganese to sulfur ratios set forth hereinabove as well as containing copper within the prescribed amounts. If these teachings of the invention are followed the relatively high hot rolling temperatures conventionally necessary to achieve good magnetic properties are no longer required. Consequently, by the use of lower than normal rolling temperatures the disadvantages from the processing and cost standpoint as discussed hereinabove may be avoided. Therefore the invention provides a practice wherein a grain oriented silicon steel may be produced having good magnetic properties at significant cost advantage over conventional practice.By way of specific example, and specifically to demonstrate the significance of manganese to sulfur ratios in accordance with the invention on the magnetic properties of the steel, the following silicon steel compositions as set forth in Table I were produced and hot rolled within the range of 1204 to 1 2600C (2200 to 23000F).
TABLE I
10.8 Mil
Magnetic Quality
HR WPP Heat C Mn S Si Al Cu B Mn:STemp,F 17KB u y10H 6351 .030 .038 .035 3.04 .005 .20 .0004 1.10 2200 .758 1854
6352 .030 .040 .036 3.05 .005 .19 .0004 1.10 2200 .755 1850
6344 .030 .043 .035 3.00 .005 .20 .0004 1.20 2200 .772 1864
6345 .028 .042 .035 3.00 .005 .20 .0004 1.20 2200 .753 1858
6341 .030 .042 .034 2.95 .005 .20 .0005 1.23 2250 .761 1845
6168 .033 .049 .030 3.12 .004 .18 .0007 1.60 2300 .704 1845
6169 .030 .055 .023 3.10 .004 .18 .0004 2.40 2300 .704 1812
6162 .049 .065 .020 3.00 .005 .20 .0010 3.25 2300 .882 1693
The steels as set forth in Table I were hot rolled directly from ingot to hot band with the hot band
having a thickness of the order of 2.032 to 2.286 mm (0.080 to 0.090").The hot band was annealed at 8990C(1 6500 F) and cold rolled to an intermediate thickness of 0.711 to 0.762 mm (.028 to 0.030").
The intermediate gauge strip was annealed at a temperature of 9490C (17400 F) before cold rolling to a
final gauge of 0.2743 mm (0.0108").
As may be seen from Table I, the core loss values (WPP, 1 7KB) are improved for the steels having
manganese to sulfur ratios less than 2.5 over steel Heat No. 61 62 having a relatively high manganese
to sulfur ratio of 3.25 which is typical of conventional steels of this type.
The effect of copper with respect to further improving core loss is shown by the heats reported in
Table II.
TABLE II
10.8 Mil
MgO-Coated
Magnetic Quality
HR WPP
Heat C Mn S Si Al Cu B Mn:S Temp,F 17KB y10H 6369 .034 .039 .022 3.0 .005 .19 .0006 1.80 2250 .736 1860
6370 .031 .042 .022 3.0 .005 .42 .0005 1.90 2250 .721 1868
6364 .030 .048 .026 3.0 .005 .58 .0007 1.85 2250 .768 1849
6433 .030 .042 .022 3.0 .005 .20 .0014 1.91 2250 .710 1869
6377 .028 .042 .021 3.0 .005 .42 .0009 2.00 2250 .719 1874
6376 .029 .047 .024 3.0 .005 .58 .0009 1.96 2250 .763 1843
The steels reported in Table II are hot rolled directly from ingot to hot band having a thickness of 21286 mm (0.090"). The hot band was cold rolled to final gauge in two stages with an intermediate anneal. Initial annealing, prior to cold rolling, was at a temperature of 8990C (1 6500F) whereupon the material was rolled to a thickness of 0.711 mm (0.028"); it was then annealed at a temperature of 9490C (17400 F) and rolled to a thickness of 0.2743 mm (0.0108"). The material was then final normalized at a temperature of 8020C (14750F) during which decarburization was achieved. Finally the decarburized strip was conventionally coated with magnesium oxide and annealed in a hydrogen atmosphere of 11 770C (21500 F). As may be seen from the core loss values (WPP 17KB) reported in
Table II the presence of copper in an amount above about 0.2% as shown by the steel identified as
Heat 6370 shows improved core loss over steel identified as Heat No. 6369 having 0.19% copper. The core loss values deteriorate, however, if copper is not maintained at a level less than about 0.58%, as may be seen from the steel identified as Heat No. 6364, which shows a significant deterioration in core loss at a copper content of 0.58%.
Claims (6)
1. A method for producing grain oriented silicon steel including the steps of casting an ingot, heating said ingot for hot rolling, hot rolling said ingot to hot rolled band, cold rolling said band in one or more stages with intermediate annealing, decarburization at final thickness, coating and final high temperature texture annealing, the improvement comprising conducting said hot rolling with said ingot at a temperature of not more than 12600C (23000 F) with said steel having a manganese to sulfur ratio of not more than 2.5.
2. The method of claim 1, wherein said steel has a manganese to sulfur ratio within the range of 1 to less than 2.5.
3. The method of claims 1 and 2, wherein said hot rolling is conducted with said ingot at a temperature of 12040C (22000F) to less than 1 2600C (23000 F).
4. The method of claims 1, 2 and 3 wherein said steel contains copper in an effective amount up
to 0.4% by weight.
5. The method of claims 1, 2 and 3 wherein said steel contains copper in an amount of from 0.2 to
less than 0.58% by weight.
6. A method according to claim 1 and substantially according to any one of the specific Examples
herein.
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US24556681A | 1981-03-19 | 1981-03-19 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| GB2095287A true GB2095287A (en) | 1982-09-29 |
Family
ID=22927185
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| GB8201186A Withdrawn GB2095287A (en) | 1981-03-19 | 1982-01-15 | 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) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4878959A (en) * | 1987-06-04 | 1989-11-07 | Allegheny Ludlum Corporation | Method of producing grain-oriented silicon steel with small boron additions |
| EP0392535A2 (en) * | 1989-04-14 | 1990-10-17 | 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 |
| EP0648847A1 (en) * | 1993-10-19 | 1995-04-19 | Nippon Steel Corporation | Production method of grain oriented electrical steel sheet having excellent magnetic characteristics |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR960010811B1 (en) * | 1992-04-16 | 1996-08-09 | 신니뽄세이데스 가부시끼가이샤 | Process for production of grain oriented electrical steel sheet having excellent magnetic properties |
| US5653821A (en) * | 1993-11-09 | 1997-08-05 | Pohang Iron & Steel Co., Ltd. | Method for manufacturing oriented electrical steel sheet by heating slab at low temperature |
| 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 DE DE19823210075 patent/DE3210075A1/en not_active Ceased
- 1982-03-19 FR FR8204773A patent/FR2502179A1/en not_active Withdrawn
Cited By (6)
| 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 |
| US4878959A (en) * | 1987-06-04 | 1989-11-07 | Allegheny Ludlum Corporation | Method of producing grain-oriented silicon steel with small boron additions |
| EP0392535A2 (en) * | 1989-04-14 | 1990-10-17 | Nippon Steel Corporation | Process for preparation of grain-oriented electrical steel sheet having superior magnetic properties |
| EP0392535A3 (en) * | 1989-04-14 | 1992-09-30 | 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 |
| EP0648847A1 (en) * | 1993-10-19 | 1995-04-19 | Nippon Steel Corporation | Production method of grain oriented electrical steel sheet having excellent magnetic characteristics |
Also Published As
| Publication number | Publication date |
|---|---|
| ATA69782A (en) | 1986-07-15 |
| RO84750B (en) | 1984-09-30 |
| KR830008744A (en) | 1983-12-14 |
| FR2502179A1 (en) | 1982-09-24 |
| ES8302789A1 (en) | 1983-01-16 |
| IT1147814B (en) | 1986-11-26 |
| ES509302A0 (en) | 1983-01-16 |
| PL128759B1 (en) | 1984-02-29 |
| IT8247692A0 (en) | 1982-01-29 |
| PL235082A1 (en) | 1982-09-27 |
| JPS57158322A (en) | 1982-09-30 |
| CA1197758A (en) | 1985-12-10 |
| BE892532A (en) | 1982-09-20 |
| BR8201340A (en) | 1983-01-25 |
| DE3210075A1 (en) | 1983-01-05 |
| SE8107844L (en) | 1982-09-20 |
| RO84750A (en) | 1984-07-17 |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| WAP | Application withdrawn, taken to be withdrawn or refused ** after publication under section 16(1) |