CA1194386A - Method for producing cube-on-edge oriented silicon steel - Google Patents
Method for producing cube-on-edge oriented silicon steelInfo
- Publication number
- CA1194386A CA1194386A CA000422372A CA422372A CA1194386A CA 1194386 A CA1194386 A CA 1194386A CA 000422372 A CA000422372 A CA 000422372A CA 422372 A CA422372 A CA 422372A CA 1194386 A CA1194386 A CA 1194386A
- Authority
- CA
- Canada
- Prior art keywords
- silicon steel
- cube
- texture annealing
- edge
- 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.)
- Expired
Links
Classifications
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/147—Alloys characterised by their composition
- H01F1/14766—Fe-Si based alloys
- H01F1/14775—Fe-Si based alloys in the form of sheets
- H01F1/14783—Fe-Si based alloys in the form of sheets with insulating coating
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/68—Temporary coatings or embedding materials applied before or during heat treatment
- C21D1/70—Temporary coatings or embedding materials applied before or during heat treatment while heating or quenching
-
- 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
- C21D8/1277—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular surface treatment
- C21D8/1283—Application of a separating or insulating coating
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C10/00—Solid state diffusion of only metal elements or silicon into metallic material surfaces
- C23C10/28—Solid state diffusion of only metal elements or silicon into metallic material surfaces using solids, e.g. powders, pastes
-
- 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
- C21D8/1294—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a localized treatment
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Electromagnetism (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Dispersion Chemistry (AREA)
- Power Engineering (AREA)
- Manufacturing & Machinery (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Metal Rolling (AREA)
Abstract
ABSTRACT OF THE DISCLOSURE
An improvement in the manufacture of cube-on-edge oriented silicon steel; the improvement comprises coating the surface of the silicon steel with a manganese-bearing material prior to texture annealing, whereby secondary grain growth is inhibited during texture annealing to achieve reduced watt loss.
Cube-on-edge oriented silicon steel in the form of sheets is known for use in various electrical applications including transformer cores. With cube on-edge silicon steel the alloy is characterized by secondary recrystallization in the (110)[001]
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 materiel, and specifically when used in the manufacture of transformer cores, the material is required to have reduced watt loss, because the consumption of electrical energy decreases as iron loss decreases.
Reduced watt loss may be promoted by achieving fine secondary grain size during texture annealing.
It is accordingly an object of the present invention to provide a method whereby during the texture annealing of cube-on-edge silicon steel the secondary grain growth is inhibited to provide a relatively fine grained material after texture annealing with reduced watt loss.
This and other objects of the invention, as well as a more complete understanding thereof, may be obtained from the following description and specific examples.
Broadly, in the practice of the invention a silicon steel which has been conventionally processed by hot rolling and
An improvement in the manufacture of cube-on-edge oriented silicon steel; the improvement comprises coating the surface of the silicon steel with a manganese-bearing material prior to texture annealing, whereby secondary grain growth is inhibited during texture annealing to achieve reduced watt loss.
Cube-on-edge oriented silicon steel in the form of sheets is known for use in various electrical applications including transformer cores. With cube on-edge silicon steel the alloy is characterized by secondary recrystallization in the (110)[001]
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 materiel, and specifically when used in the manufacture of transformer cores, the material is required to have reduced watt loss, because the consumption of electrical energy decreases as iron loss decreases.
Reduced watt loss may be promoted by achieving fine secondary grain size during texture annealing.
It is accordingly an object of the present invention to provide a method whereby during the texture annealing of cube-on-edge silicon steel the secondary grain growth is inhibited to provide a relatively fine grained material after texture annealing with reduced watt loss.
This and other objects of the invention, as well as a more complete understanding thereof, may be obtained from the following description and specific examples.
Broadly, in the practice of the invention a silicon steel which has been conventionally processed by hot rolling and
Description
~ Q~3'~3~ 1 i ABSTRACT OF THE DISC~OSURE
An improvement in ~he manuacture of cube on-edge ~ oriented silicon steel; the improvement comprises coating the ! surface of the silicon steel with a manganese-b~aring material ¦prior to t~x~ure annealing, whereby secondary grain growth is ¦inhibited during tex~ure annealing to achieve reduced watt loss.
****** ., Cube-on-edge oriented silicon steel în the form of sheets is known for use in various electrical applications including transformer cores. With cube on-edge silicon steel the alloy ¦ is characterized by secondary recrystallization in the (110)[001]
position, which i~ 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 specifically when used in the manufacture of ~ransformer cores, S the material is required to have reduced watt loss, because the consumption of electrical energy decreases as iron loss decreases.
Reduced watt loss may be pro~oted by achieving fine secondary grain size during texture annealing.
It is accordingly an objec~ of the present invention to I
provide a method whereby during the texture annealing of cube-on- i edge silicon steel the secondary grain growth is inhibited to provide a relatively flne grained material after texture annealing with reduced watt loss.
This and other obiects of the invention, as well as a S more complete understandlng thereof, may be obtained from the ~ollowing description and specific examples.
1, Broadly, in the practice of the invention a silicon l ~teeL whlch has been conventionally processed by hot rolling and !l ,1 ll ~
~ 3~
~¦ cold rolling with intermediate anneals is surface coated with a manganese-bearing material prior to texture annealing aIld i5 ¦ texture annealed in the conventional manner wîth said manganese-¦ bearing material ~hereon. A manganese-bearing material Ij particularly suited for use in the :invention is Mn3(N02). It has ,j been found that the presence of the manganese-bearing compound i during annealing inhibits secondary grain growth and thus reduces~
i watt loss. This may be further enhanced if ~he steel is serra~ed !I prior to texture annealing. Although the practice of the i invention finds utility with cube-on-edge orien~ed silicon steelsl ,¦ generally, it is particularly adapted to steels of this type withln ¦ the following composition limits in percent by weight:
ISteel Mn C _ S _ Si B Fe ~l !¦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.
By the practice of coating steel with a manganese-bear-ing compound and texture annealing with the compound being presen~
, on the steel, said practice is believed to be effective for the Il purpose by difusing manganese into the steel during annealing, l! which promotes primary grain coarsening by interaction with the solute sul~ur, which sulfur would tend to inhibit grain growth.
¦ Hence a region is provided in which primary grain growth occurs and restricts the growth oE secondary grains through this region.
It would appear that the extent of grain refinement of the secondary grains after texture annealing depends on the spacing , of the regi.ons of primary grain growth on the areas o~ application I of the manganese-containing material, provided that the width o~
il the treated region is su~icient to act as a barrier to the ~! secondary grains. This ef~ect may be supplemented by creating Il i , ' , -2-~ 9 94:~86 similar barriers by subjecting the steel to serrating or the ! like.
The silicon steel composi~ion used in the specific l examples, and ider.tified as SX-14, was of the following nominal ¦ composition in percent by weight.
Mn S C_ Si B Fe l .035 .~16 .030 3.15 .0010 Balance ! Epstein packs of final no~malized SX-14 composition, llidentified as Heat No. 154684, were coated with a wa~er slurry llcomprising 300 cc of water, 46 gm. of MgO and 2 gm. of H3BO3. This material with the coating thereon was then texture anneal~d in a hydrogen atmosphere in the conven~ional manner. Specifically, the texture annealing consisted of charging the ~at~rial into a ~ furnace at a temperature of 1400°F, heating at a rate of 50°F per ¦ hour to a temperature of 2150°F, holding at temperature for 12 hours and then cooling to 1200°F, at which time the material was removed from the furnace. One of the Epstein packs, prior to the above slurry coating, was painted with a mixture of 30 cc of 50%
Mn(NO3)2 and an inert thickener, which was applied in 1 mm stripes' perpendicular to the sheet rolling direction at intervals of 10 m 1;
I this painted coating was then air dried. This Epstein pack i constituted treatment in accordance with the practice o the invention; whereas, the second pack was used as a control and ` typifled a conventional practice. Following the texture annealing i procedure, as deseribed above, the average lineal dimension of the secondary graLns of the conventional, control pack specimen in the sheet rolling direction was 13 mm. In contrast, the average i lineal dimension o~ the secondary grain of the specimen treated ~ wlth Mn(NO3)2 in accordance with the practice of the invention ll !! -3-~ ~9~ 1Yb l¦was 7 mm; tnese grains it was observed were often separated by the.
aforementioned bands of smaller primary grains where normal grain growth was stimulated by the application of the manganese-bearing ~¦compound.
¦ In a second specific example, a single Epstein strip ofl ¦ final nor~alized SX-14 composition from the same heat as in the ! aforementioned Example 1 was scribed wi~h a metal scribe to . produce serrations in the strip perpendicular to the rolling I direction a~ intervals of 10 mm. After the scribing operation, the strip was slurry coated and texture annealed under the conditions described above with respect to the first specific l¦example. Following this tex~ure annealing, the average lineal ¦¦dimension in the sheet rollin~ di.rection of t'ne secondary grain l in the scribed strip was 9.5 mm.
I
I!
I
.,
An improvement in ~he manuacture of cube on-edge ~ oriented silicon steel; the improvement comprises coating the ! surface of the silicon steel with a manganese-b~aring material ¦prior to t~x~ure annealing, whereby secondary grain growth is ¦inhibited during tex~ure annealing to achieve reduced watt loss.
****** ., Cube-on-edge oriented silicon steel în the form of sheets is known for use in various electrical applications including transformer cores. With cube on-edge silicon steel the alloy ¦ is characterized by secondary recrystallization in the (110)[001]
position, which i~ 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 specifically when used in the manufacture of ~ransformer cores, S the material is required to have reduced watt loss, because the consumption of electrical energy decreases as iron loss decreases.
Reduced watt loss may be pro~oted by achieving fine secondary grain size during texture annealing.
It is accordingly an objec~ of the present invention to I
provide a method whereby during the texture annealing of cube-on- i edge silicon steel the secondary grain growth is inhibited to provide a relatively flne grained material after texture annealing with reduced watt loss.
This and other obiects of the invention, as well as a S more complete understandlng thereof, may be obtained from the ~ollowing description and specific examples.
1, Broadly, in the practice of the invention a silicon l ~teeL whlch has been conventionally processed by hot rolling and !l ,1 ll ~
~ 3~
~¦ cold rolling with intermediate anneals is surface coated with a manganese-bearing material prior to texture annealing aIld i5 ¦ texture annealed in the conventional manner wîth said manganese-¦ bearing material ~hereon. A manganese-bearing material Ij particularly suited for use in the :invention is Mn3(N02). It has ,j been found that the presence of the manganese-bearing compound i during annealing inhibits secondary grain growth and thus reduces~
i watt loss. This may be further enhanced if ~he steel is serra~ed !I prior to texture annealing. Although the practice of the i invention finds utility with cube-on-edge orien~ed silicon steelsl ,¦ generally, it is particularly adapted to steels of this type withln ¦ the following composition limits in percent by weight:
ISteel Mn C _ S _ Si B Fe ~l !¦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.
By the practice of coating steel with a manganese-bear-ing compound and texture annealing with the compound being presen~
, on the steel, said practice is believed to be effective for the Il purpose by difusing manganese into the steel during annealing, l! which promotes primary grain coarsening by interaction with the solute sul~ur, which sulfur would tend to inhibit grain growth.
¦ Hence a region is provided in which primary grain growth occurs and restricts the growth oE secondary grains through this region.
It would appear that the extent of grain refinement of the secondary grains after texture annealing depends on the spacing , of the regi.ons of primary grain growth on the areas o~ application I of the manganese-containing material, provided that the width o~
il the treated region is su~icient to act as a barrier to the ~! secondary grains. This ef~ect may be supplemented by creating Il i , ' , -2-~ 9 94:~86 similar barriers by subjecting the steel to serrating or the ! like.
The silicon steel composi~ion used in the specific l examples, and ider.tified as SX-14, was of the following nominal ¦ composition in percent by weight.
Mn S C_ Si B Fe l .035 .~16 .030 3.15 .0010 Balance ! Epstein packs of final no~malized SX-14 composition, llidentified as Heat No. 154684, were coated with a wa~er slurry llcomprising 300 cc of water, 46 gm. of MgO and 2 gm. of H3BO3. This material with the coating thereon was then texture anneal~d in a hydrogen atmosphere in the conven~ional manner. Specifically, the texture annealing consisted of charging the ~at~rial into a ~ furnace at a temperature of 1400°F, heating at a rate of 50°F per ¦ hour to a temperature of 2150°F, holding at temperature for 12 hours and then cooling to 1200°F, at which time the material was removed from the furnace. One of the Epstein packs, prior to the above slurry coating, was painted with a mixture of 30 cc of 50%
Mn(NO3)2 and an inert thickener, which was applied in 1 mm stripes' perpendicular to the sheet rolling direction at intervals of 10 m 1;
I this painted coating was then air dried. This Epstein pack i constituted treatment in accordance with the practice o the invention; whereas, the second pack was used as a control and ` typifled a conventional practice. Following the texture annealing i procedure, as deseribed above, the average lineal dimension of the secondary graLns of the conventional, control pack specimen in the sheet rolling direction was 13 mm. In contrast, the average i lineal dimension o~ the secondary grain of the specimen treated ~ wlth Mn(NO3)2 in accordance with the practice of the invention ll !! -3-~ ~9~ 1Yb l¦was 7 mm; tnese grains it was observed were often separated by the.
aforementioned bands of smaller primary grains where normal grain growth was stimulated by the application of the manganese-bearing ~¦compound.
¦ In a second specific example, a single Epstein strip ofl ¦ final nor~alized SX-14 composition from the same heat as in the ! aforementioned Example 1 was scribed wi~h a metal scribe to . produce serrations in the strip perpendicular to the rolling I direction a~ intervals of 10 mm. After the scribing operation, the strip was slurry coated and texture annealed under the conditions described above with respect to the first specific l¦example. Following this tex~ure annealing, the average lineal ¦¦dimension in the sheet rollin~ di.rection of t'ne secondary grain l in the scribed strip was 9.5 mm.
I
I!
I
.,
Claims (3)
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 and a final texture annealing, the improvement comprising surface coating said steel with a manganese-bearing material prior to texture annealing and texture annealing said steel with said coating thereon, whereby secondary grain growth is inhibited during texture annealing.
2. The method of claim 1 wherein said manganese-bearing material is Mn(N03)2.
3. The method of claims 2 or 3 wherein said steel is serrated prior to texture annealing.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US39968082A | 1982-07-19 | 1982-07-19 | |
| US399,680 | 1982-07-19 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA1194386A true CA1194386A (en) | 1985-10-01 |
Family
ID=23580545
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA000422372A Expired CA1194386A (en) | 1982-07-19 | 1983-02-25 | Method for producing cube-on-edge oriented silicon steel |
Country Status (6)
| Country | Link |
|---|---|
| EP (1) | EP0099619A3 (en) |
| JP (1) | JPS5928524A (en) |
| KR (1) | KR890000126B1 (en) |
| BR (1) | BR8301545A (en) |
| CA (1) | CA1194386A (en) |
| PL (1) | PL242750A1 (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4897131A (en) * | 1985-12-06 | 1990-01-30 | Nippon Steel Corporation | Grain-oriented electrical steel sheet having improved glass film properties and low watt loss |
| JPS6196080A (en) * | 1986-04-03 | 1986-05-14 | Nippon Steel Corp | Separating agent for annealing for grain-oriented electrical steel sheet |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE1249049B (en) * | 1959-03-05 | |||
| JPS5112450B1 (en) * | 1966-03-18 | 1976-04-20 | ||
| JPS4837193B1 (en) * | 1969-07-07 | 1973-11-09 | ||
| JPS5021928A (en) * | 1973-06-28 | 1975-03-08 | ||
| JPS5423647B2 (en) * | 1974-04-25 | 1979-08-15 | ||
| US4160681A (en) * | 1977-12-27 | 1979-07-10 | Allegheny Ludlum Industries, Inc. | Silicon steel and processing therefore |
-
1983
- 1983-02-25 CA CA000422372A patent/CA1194386A/en not_active Expired
- 1983-03-04 KR KR1019830000879A patent/KR890000126B1/en not_active IP Right Cessation
- 1983-03-25 BR BR8301545A patent/BR8301545A/en unknown
- 1983-04-11 EP EP83302013A patent/EP0099619A3/en not_active Withdrawn
- 1983-05-26 JP JP9332483A patent/JPS5928524A/en active Granted
- 1983-06-29 PL PL24275083A patent/PL242750A1/en unknown
Also Published As
| Publication number | Publication date |
|---|---|
| JPS5928524A (en) | 1984-02-15 |
| JPH0515765B2 (en) | 1993-03-02 |
| BR8301545A (en) | 1984-04-17 |
| KR840004174A (en) | 1984-10-10 |
| KR890000126B1 (en) | 1989-03-08 |
| EP0099619A2 (en) | 1984-02-01 |
| PL242750A1 (en) | 1984-03-12 |
| EP0099619A3 (en) | 1984-07-25 |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| MKEC | Expiry (correction) | ||
| MKEX | Expiry |