US3266955A - Process for producing silicon steel sheet having (100) plane in the rolling plane - Google Patents

Process for producing silicon steel sheet having (100) plane in the rolling plane Download PDF

Info

Publication number
US3266955A
US3266955A US332423A US33242363A US3266955A US 3266955 A US3266955 A US 3266955A US 332423 A US332423 A US 332423A US 33242363 A US33242363 A US 33242363A US 3266955 A US3266955 A US 3266955A
Authority
US
United States
Prior art keywords
rolling
hot
steel sheet
orientation
silicon steel
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 - Lifetime
Application number
US332423A
Other languages
English (en)
Inventor
Taguchi Satoru
Sakakura Akira
Takechi Hiroshi
Takashima Hironori
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Yawata Iron and Steel Co Ltd
Original Assignee
Yawata Iron and Steel Co Ltd
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Yawata Iron and Steel Co Ltd filed Critical Yawata Iron and Steel Co Ltd
Application granted granted Critical
Publication of US3266955A publication Critical patent/US3266955A/en
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Images

Classifications

    • 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
    • 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
    • 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
    • C21D8/1227—Warm rolling
    • 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
    • C21D8/1272—Final recrystallisation annealing

Definitions

  • PROCESS FOR PRODUCING SILICON STEEL SHEET HAVING 100) PLANE IN THE ROLLING PLANE Filed Dec. 23, 1963 5 SheetsSheet 4 Fl6.5
  • RD INVENTORS By Soforu'Taquchi Akira Sakakura Hiroshi Takechi Hironori Takashima Aug. 16, 1966 Filed Dec.
  • This invention relates to a process for producing silicon steel sheet. More particularly, the present invention relates to a process for producing silicon steel sheet or strip having (100) plane in the rolling plane of the sheet.
  • Silicon steel sheet is widely used as soft magnetic materials for iron cores of transformers and generators.
  • silicon steel has a cubic lattice texture, in which there are three easy magnetization directions vertical to one another and has an advantage of the least energy being required for magnetizing the silicon steel core when a magnetic field is applied in parallel with such directions. Due to this advantage various attempts have been heretofore made in controlling the crystal orientation of the silicon steel sheet in accordance with its object of use.
  • iron cores made of the double-oriented silicon steel may be lighter in weight than those made of the single-oriented silicon steel sheet.
  • iron cores made of the double-oriented silicon steel sheet are not suited for a small-sized rotor, because there occurs a striking deviation between the magnetic flux passing direction and the easy magnetization direction in some part of the iron core. For that reason the non-directional oriented silicon steel sheet has been usually used to make iron cores for smallsized rotors in order to eliminate the above said devia tion.
  • the object of the present invention is to provide a process of producingsilicon steel sheets, in which the (100) plane appears in the rolling plane, by means of an easily operative metallurgical technique, or as a typical form thereof, a double-oriented silicon steel possessing such excellent magnetic characteristics as adapted for 3,266,955 Patented August 16, 1966 making iron cores for use in a large-sized rotor or a plane non-directional oriented silicon steel sheet particularly adapted for making iron cores for use in a smallsized rotor.
  • Another object of the present invention is to provide a process of producing a double-oriented silicon steel sheet having (100) plane in the rolling plane or a nondirectional oriented silicon steel sheet having (100) plane by regulating the ratio of recrystallization grains having 100) [001] orientation to recrystallization grains having 100) [011] orientation.
  • FIGURE 1 shows diagrams showing the crystal orientation and easy magnetization direction of crystal grains forming oriented silicon steel sheets of the following three types (the silicon steel sheet so designated hereinafter shall include steel strip), that is, a single-oriented silicon steel sheet (a), a double-oriented silicon steel sheet (b) and a Wassermann-oriented silicon steel sheet (c).
  • FIGURE 2 shows diagrams showing magnetic torque curves of (100) [001] orientation, (100) [011] orientation and a resultant of them.
  • FIGURE 3 shows a pole figure (a) showing the crystal orientation of a hot-rolled steel sheet, which has been crosswise hot-rolled, and a ⁇ 110 ⁇ pole figure (b) showing the crystal orientation of a hot-rolled steel sheet, which has been hot-rolled in a single direction.
  • FIGURE 4 shows ⁇ 110 ⁇ pole figures showing the respective crystal orientations of primary recrystallization grains obtained by cold-rolling and sequentially annealing the hot-rolled silicon steel sheet, which has been crosswise hot-rolled (a) and the hot-rolled silicon steel sheet, which has been hot-rolled in a single direction (b).
  • FIGURE 5 shows (100) pole figures showing the respective crystal orientations of secondary recrystallization grains and microsketches showing the respective crystal structures of secondary recrystallization grains thereof obtained by further annealing the primary recrystallization grains of two kinds as of the hot-rolled steel sheets (a) and (b) as shown in FIGURE 4.
  • FIGURE 6 is a diagram showing the ratios of the (100) [001] orientation to (100) [011] orientation appearing in the products of the present invention in response to the variation of carbon content of an ingot used as the starting material.
  • the edge of the lattice that is, the 100 orientation is the easiest to magnetize and then the direction of the diagonal of the lattice plane or the 110 direction is the next easiest to ,magnetize and the most difiicult to magnetize is the direction of the cubic diagonal of the lattice or the lll direction.
  • the designations of the planes and directions here mentioned are shown in the notation of Millers indices. The detailed description of the definitions may be found, for example, on pages 1 to 25 of Structure of Metals, second edition, written by C. S. Barrent and published by McGraw-Hill Co., New York, 1952.
  • the single-oriented silicon steel sheet that first fulfilled the requirement to apply a magnetic field in parallel with the easy magnetization direction.
  • This is formed of crystal grains having such crystal orientation as shown in FIGURE 1(a) and is crystallographically designated as (110) [001] orientation, in which the easy magnetization axis is parallel with the rolling direction.
  • the single-oriented silicon steel is characterized by the magnetic induction and other magnetic characteristics being excellent in the rolling direction, but low in another direction in the rolling plane, for instance, in the direction at a right angle to the rolling direction, because the ll axis appears in the latter direction, and the lowest in the 1ll direction.
  • the present invention is to provide a process of producing so-called (100) plane silicon steel sheets having no 1l1 axis, which is the most difficult to magnetize, in the rolling plane.
  • a preferred example thereof is the double-oriented silicon steel sheet which is formed of crystal grains having such crystal orientation as is shown in FIGURE 1(b) and is crystallographically designated as (100) [001] orientation, and in which the easy magnetization axis is parallel with the two directions as of the rolling direction and the direction at a right angle thereto. Accordingly, the double-oriented silicon steel sheet is charactertized by that the magnetic induction and other magnetic characteristics are excellent in both of the above mentioned two directions and that the 1ll axis does not appear in the rolling plane.
  • FIGURE 1(a) shows a kind of the double-oriented silicon steel sheet known as a silicon steel sheet of Wassermann-orientation, which is designated crystallographically as (100) [011] orientation.
  • the double-oriented silicon steel sheet of Wasserrnannorientation is characterized in that the easy magnetization axis 100 appears in direction 45 degrees from the rolling direction and at a right angle thereto. The 1ll axis does not also appear in the rolling plane.
  • the double-oriented silicon steel sheet which is a preferred product of the present invention is suited for making iron cores for use in a largesized rotor, but not in a small-sized one.
  • non-directional oriented silicon steel sheet is used, which is also a preferred object of the present invention and is characterized in having a (100) plane in the rolling plane and having grains of (100) [00L] orientation and those of (100) [011 orientation in the same ratio. It is desirable that the permability is made both high and substantially equal in all directions in the plane of the silicon steel sheet, when punching iron cores for use in a smallsized rotor.
  • the silicon steel sheet of random crystal orientation heretofore used for iron cores for use in a small-sized rotor was defective in that its permeability was low, though substantially equal in all directions in the plane of the sheet.
  • the non-directional oriented silicon steel sheet obtained by the present invention fulfills the requirements that the permeability should be both high and substantially equal in all directions in the plane.
  • FIG. 2(a) is a magnetic torque curve of (100) [001] orientation
  • FIG. 2(b) that of (100) [011] orientation
  • FIG. 2(0) is when two aforesaid curves are overlapped one over the other. As seen from the last figure, these two curves cancel each other when they are overlapped, as the four ridges or peaks of each orientation no longer appear, and the sheet becomes non-directional oriented.
  • the magnetizability of the double-oriented silicon steel sheet is expressed by B which means a magnetic induction in gausses at 10 oersteds
  • B the magnetizability of the non-directional oriented silicon steel sheet
  • B the magnetizability of the non-directional oriented silicon steel sheet
  • a double-oriented silicon steel sheet showing a B value of 19,000 gausses in both the rolling direction and the direction at a right angle thereto may be said to be substantially ideal as a silicon steel sheet containing about 3% Si for making iron cores for use in a large-sized rotor.
  • a B value of 16,000 gausses will be sufiicient to meet the properties required for iron cores for use in a small-sized rotor.
  • the present invention has succeeded in obtaining the (100) plane silicon steel sheet, more preferably the doubleoriented silicon steel sheet, which has 100% of recrystallization grains of substantial (100) [001] orientation, and the (100) plane non-directional oriented silicon steel sheet, which has 50% of recrystallization grains of (100) [001] orientation and 50 of recrystallization grains of (100) [011] orientation respectively, by means of the novel method, in which an ingot containing a small amount of Aland an amount of C regulated in accordance with the object of application, which is the starting material of the present invention, is first crosswise hot-rolled and then the thus obtained hot-rolled material is subjected to the conventional cold-rolling and annealing treatments.
  • the present invention is distinguished by the cross hot-rolling of the starting material from any conventional method, which is characterized by the step of hot-rolling in a single direction or cold-rolling and annealing treatments.
  • the practical importance of the present invention resides in the conditions, in which the cross hot-rolling is carried out.
  • this novel process of the present invention it has been also discovered that the ratio of two component groups of recrystallization grains contained in silicon steel sheet to be obtained by the present invention-a group of recrystallization grains of substantial (100) [001] orientation and a group of recrystallization grains of substantial (100) [011] orientationdepends upon the carbon content of an ingot to be crosswise hot-rolled.
  • the present invention has succeeded in obtaining the double-oriented silicon steel sheet having 100% of recrystallization grains of substantial (100) [001] orientation or the (100) non-directional oriented silicon steel sheet having 50% of recrystallization grains of substantial (100) [001] orientation and 50% of recrystallization grains of substantial (100) [011] orientation respectively by regulating the amount of carbon to be added to the ingot.
  • the present invention has succeeded in obtaining the double-oriented silicon steel sheet and the non-directional oriented silicon steel sheet of any desired thickness and of excellent properties by subjecting the crosswise hot-rolled sheet to a conventional cold-rolling and annealing which may be carried out in a normal industrial atmosphere, for instance, in gas such as H N and Ar.
  • the cross hot-rolling of an ingot is used in the production of structural carbon steels or low alloy steels, but has never been applied to the production of silicon steel sheets.
  • the hotrolling of an ingot or slab is usually carried out only in' the longitudinal direction of the ingot and the thus obtained hot-rolled steel sheet is subjected to cold-rolling and annealing.
  • the crystal orientation of the hot-rolled steel sheet belongs to a group of (X 1 I [011] orientation (wherein X is an arbitrary number), which makes the 011 axis parallel with the hot-rolling direction a rotating axis with the (100) [001] orientation as the center.
  • FIGURE 3(b) is the ⁇ 110 ⁇ pole figure showing the crystal orientation in the center part of the thickness of a hot strip of 3 mm. thick which has been prepared as follows: A ton-ingot of silicon steel sheet containing 3.0% Si, 0.04% C and 0.03% Al which has been made in an electric furnace and then cast, was bloomed in the longitudinal direction to make a slab of about 100 mm. thick and then the thus produced slab was soaked at a temperature of 1,250 C. for 30 minutes and subsequently hotrolled in the longitudinal direction to make the hot strip of 3 mm. thick.
  • the crystal orientation after hot-rolled shows an excellent concentration of the (110) poles in the hot-rolling direction but a considerably dispersed concentration of the (110) poles in the direction at a right angle to the hot-rolling direction, demonstrating that this crystal orientation is a group of (X 1 1) [011] orientation with the (100) [011] orientation as the central orientation.
  • FIGURE 3(a) is the (110) pole figure showing the crystal orientation in the center part of the thickness of a hot strip of about 3 mm. thick which has been prepared as follows: A 500 kg.-ingot of silicon steel sheet containing 3% Si, 0.04% C and 0.03% A1, which has been made in an electric furnace and then cast, was bloomed in the longitudinal direction to make a slab about 90 mm. thick and then the thus obtained slab was soaked at a temperature of 1,280 C. for one hour and subsequently hot-rolled first in the direction at a right angle to the longitudinal direction of the slab at a re duction rate of about 70% so as to make an intermediate gauge slab of 27 mm.
  • the crystal orientation after crosswise hot-rolled shows a considerably similar degree of concentration of the ⁇ 110 ⁇ poles both in the last hot-rolling direction (in the direction of RD) and in the direction at a right angle thereto.
  • the ratio thereof is 6.0X233X (wherein 1X is a random orientation intensity), considerably smaller than in the case of the hot-rolling in the single direction, in which the ratio of above 12X:4X is shown.
  • FIGURES 4(a) and (b) are (110) pole figures in the center parts of the steel sheets after each of the above mentioned two kinds of hot-rolled steel sheets has been subjected to the following processes: At first each of them was annealed for 5 minutes in an H atmosphere containing 75% N by volume, the thus annealed steel sheet was pickled and then cold-rolled at the reduction rate of 65% so as to obtain a cold-rolled sheet of about 1 mm. thick and then the thus obtained cold-rolled sheet was annealed at a temperature of 800 C. for 5 minutes. As seen from these figures, the orientation of the primary recrystallization grains produced by the annealing carried out at a temperature of 800 C.
  • FIGURES 5(a) and (b) are pole figures showing the orientations of recrystallization grains after the above two kinds of steel sheets already treated as above mentioned were further annealed in an atmosphere of 50% N +50% H by volume at a temperature of 1,200 C. for 20 minutes.
  • recrystallization grains of substantial [001] orientation were produced in the case of single hot-rolling (FIGURE 5(b)) and recrystallization grains of substantial 100) [001] orientation were produced in the case of cross-hotrolling (FIGURE 5 (a) Further, in this process, the following interesting fact has been discovered by the inventors that even in carrying out exactly the same cold-rolling and annealing processes as mentioned above, when more than 0.050% C was contained in an ingot, recrystallization grains of (100) [011] orientation came to be mixed in after final annealing in response to the C content of the ingot.
  • FIGURE 6 shows the percentages of recrystallization grains of 100) [001] orientation and those of (100) [011] orientation forming a silicon steel sheet after being cold-rolled and annealed, varying in accordance with the change in percentage of C to be contained in the ingot. That is to say, depending on the percentage of C to :be contained in the ingot, grains of [001] orientation and those of [011] orientation are produced in the silicon steel sheet at percentages corresponding to the content of C of the ingot, though both grains have substantially the (100) plane in the rolling plane.
  • the percentage of (100) [001] orientation and (100) [011] orientation of recrystallization grains after final annealing may be selected as desired, thereby the production of the (100) plane silicon steel sheets as mentioned in the introduction of this specification became possible.
  • recrystallization grains having (110) [001] orientation as shown in FIGURE 5( b) are produced, even if the carbon content of the material exceeds 0.05%. Further inthe method of producing the double-oriented silicon steel sheet having recrystallization grains of (100) [001] orientation, which has been discovered by the present inventors before the present invention and in which the hot-rolled silicon steel sheet is subjected to cross coldrolling, it has been confirmed that recrystallization grains of (100) [011] orientation did not appear, regardless of the carbon content of the ingot, provided that the hotrolling is carried'out only in a single direction.
  • the silicon steel ingot used as the starting material in the present invention may be obtained by any of the ordinarily used steel making process, melting process and casting process. Further, the thickness of the hot-rolled sheet obtained by the cross hot-rolling is never to be limited. But, in view of the subsequent cold-rolling process, a too large thickness is disadvantageous and a too small thickness is not adapted to the capacity of the hot-rolling machine.
  • the mos-t desirable thickness of the hot-rolled sheet before it is subjected to the cold-rolling treatment will be 1.0 to 7 mm.
  • the thickness of the hot-rolled sheet will reach 1 to 7 mm.
  • the cross hot-rolling may be carried out several times or the steel may be reheated.
  • the most important factors for assuring the successful result of the present invention are the conditions of hot-rollings in the last hot-rolling step and the penultimate hot-rolling step.
  • the rolling step here designated means an operating step in which the steel is rolled in one direction, but not the number of passes of the steel through the rolls.
  • the conditions for carrying out the cross hot-rolling according to the present invention are as follows:
  • the cross hot-rolling should be carried out in directions forming a right angle :20 degrees .or preferably a substantially right angle with each other. If the angle made between the above two rolling directions is other than that, the ratio of the concentration degree of ⁇ 110 ⁇ poles in the direction of the final hot-rolling step to that in the direction at a right angle thereto will not come within a range of 4:1 to 1:4.
  • the second condition is that the hot-rolling in the second last step should be carried out in the temperature range of 800 to 1,250 C. and should be accompanied by a reduction rate of more than 20% or preferably 30 to 93%.
  • the third condition is that after the second last hot-rolling step is finished, the last hot-rolling step should be started by turning the direction of rolling and the hotrolling should be completed at least at a temperature of 600 C.
  • the reduction rate of the thickness in the last hot-rolling should be at least 40% or preferably 40 to 97%.
  • the ratio of the concentration degree of ⁇ 110 ⁇ poles in the direction of the final hot-rolling step to that in the direction at a right angle thereto will not come within the range of 4:1 to 1:4. Further, if carrying out the hot-rolling in the second last step at a temperature above 1,250 C. the concentration of ⁇ 110 ⁇ poles in this direction will not be effected. The reason why the hot-rolling in the second last hot-rolling step should not be carried out at a temperature below 800 C. arises from in reference to the temperature at which the last hot-rolling is to be carried out.
  • the last hot-rolling must be completed at a temperature above 600 C.
  • the fourth condition is that the steel should be heated at a temperature always lower than the temperature, at which the hot-rolling of said steel in the second last step has (been completed, in case it is necessary to reheat the steel which has been once cooled after the completion of the second last hot-rolling. If the steel is heated to a temperature higher than the temperature, at which the hot-rolling in the second last step has been completed, it will recrystallize and the concentration :of ⁇ 110 ⁇ poles in this direction will be completely lost.
  • C is less than 0.010%, recrystallization grains having a (100) plane parallel with the rolling plane will not be produced and, if the content of C is more than 0.15%, a greater labor will be required in decarburization thereof. Thus, C is limited to be within the range of 0.010-0.150%. The most desirable carbon content shall be described more in detail. In order to obtain the double-oriented silicon steel sheet of recrystallization grains of substantial (100)[001] orientation, C should be less than 0.05% as seen from FIGURE 6.
  • C in which equivalents of recrystallization grains of substantial (100) [001] orientation and recrystallization grains of a substantial (100)[011] orientation are mixed, C should be about 0.075%. If C is in a range of ODS-0.075%, the recrystallization grains of substantial (100)[001] orientation will ⁇ be more than 50%. Further, if C is more than 0.075%, recrystallization grains of substantial (100) [011] orientation will be more than 50% and the product will be no longer the perfect non-directional oriented silicon steel sheet.
  • Si is less than 2%, there will be caused a disadvantage of the increase in the iron core loss due to the low electric resistance of the product. If Si is more than 9 4%, the cold-rolling treatment will be diflicult due to brittleness. Therefore, Si is limited to 24%.
  • Al is added to form Al nitride, thereby to inhibit the growth of crystal grains of other orientations when producing recrystallization grains of substantial (100) [001] orientation and of substantial (100) [011] orientation.
  • the content of soluble Al is defined to be in the range of 0.0l0.060%.
  • the reduction rate should be in the range of 50 to 80%. If it is less than 50% or more than 80%, recrystallization grains having (100) plane parallel with the rolling plane will not be produced after subjected to the sequent annealing.
  • the cold rolling may 'be carried out at the reduction rate of a wider range. If the reduction rate in the first coldrolling is 30 to 60%, the reduction rate in the cold-rolling in the crossing direction should be made in the range of 20 to 50%, and, if the reduction rate in the first coldrolling is 60 to 80%, the reduction rate in the crossing direction should be made in the range of 50 to 70%.
  • the first cold-rolling in one direction or the second cold-rolling which is carried out in the crossing direction it may be carried out at any angle with the final hot-rolling direction.
  • the cold-rolling direction be 45 degrees with the final hot-rolling direction, when the production of recrystallization grains having (100) [001] orientation is intended, though any deviation in angle from 45 degrees will bring substantially no trouble on attaining the object.
  • the thus cold-rolled steel sheet is further subjected to the final high temperature annealing treatment.
  • the temperature range of annealing is 1,000 to 1,300 C. When the temperature is below 1,000 C., recrystallization grains will not be completely produced. Further, annealing at a temperature above 1,300 C. is a condition more than is required.
  • the atmosphere of annealing may be any kind of atmosphere, unless it contains such impurities as will extremely impair the magnetic characteristics as of the magnetic steel sheet. Usually, the most preferably used gas is H But, Ar and vacuum may be also applied.
  • the above mentioned high temperature annealing process may be commonly applied to obtain both of recrystallization grains having (100) [001] orientation and recrystallization grains having (100) [011] orientation.
  • the decarburization annealing should be carried out prior to the final annealing treatment.
  • any decarburization annealing process adapted to the operating conditions may be selected from various known conventional ones. As there are so many kinds of the decarburization annealing conditions these need not be specified. However, for example, an atmosphere containing moisture and a temperature range of 750 to 1,000 C. may be recommended therefor.
  • the (100) plane magnetic silicon steel sheet of any thickness formed of recrystallization grains having substantial 100) [001] orientation and substantial (100) [011] orientation may be obtained.
  • a particularly thin (100) plane silicon steel sheet may be obtained by repeating the above mentioned cold-rolling and annealing treatments.
  • Example 1 A 500 kg.-ingot made by melting in an electric furnace and containing 0.045% C, 3.02% Si and 0.035% acidsoluble Al was bloomed in its longitudinal direction to make a slab about 100 mm. thick.
  • the sla-b was soaked at 1,250 C. for 30 minutes and was then hot-rolled at a reduction rate of about 70% in a direction at a right angle to the longitudinal direction of the slab to make an intermediate 30 mm. thick; At that time, the temperature of the slab was 1,100 C. Then this slab was turned by degrees in the direction and was hot-rolled by about 90% so as to be a hot-rolled sheet about 3 mm. thick.
  • the finish temperature was 750 C.
  • the thus obtained hot-rolled sheet was annealed at 950 C. for 5 minutes.
  • the annealed sheet was pickled and was then cold-rolling at a reduction rate of 64% in the same direction as of the final hot-rolling direction so as to be a cold-rolled sheet 1.08 mm. thick.
  • the sheet was decarburized in wet hydrogen at 750 C. for 5 hours and was then annealed in an atmosphere of 50% N and 50% H at 1,200 C. for 20 hours, thereby recrystallization grains of [001] orientation have been produced.
  • the sheet was then cold-rolled by 70% in the same direction as of the previous cold-rolling so as to be of a final gauge of 0.32 mm.
  • the sheet was annealed in H at a temperature of l,200 C. for 20 hours, there was obtained an excellent double-oriented silicon steel sheet having such magnetic characteristics (Epstein test) as are shown in Table l in the final cold-rolling direction (L) and the direction at a right angle thereto (C).
  • W 10/50 and W 15/50 stand for 1 1 iron core less values when Bm (maximum fiux density) was 10,000 gausses and 15,000 gausses at 50 cycle/ second, respectively and B B B and B stand for magnetic inductions when the magnetizing force was B S 10 and 25 respectively.
  • the finish temperature was about 700 C.
  • the sheet was annealed at 950 C. for 5 minutes.
  • the annealed sheet was pickled and was then cold-rolled at a reduction rate of 70% in the same direction as the final hot-rolling direction so as to be a cold-rolled sheet 0.48 mm. thick.
  • the sheet was decarburized in wet hydrogen at 750 C. for 5 hours (then C:0.003%) and was then annealed in H at a temperature of 1,200 C. for 20 hours.
  • Example 3 A 500 kg.-ingot of about 250 mm. thick made in an electric furnace and containing 0.045% C, 3.05% Si, 0.030% acid-soluble Al was heated to 1,250 C. and hotrolled in the longitudinal direction of said ingot to make a slab of about mm. thick. The slab was once cooled 12 and then again heated to 1,200 C. The thus reheated slab was hot-rolled in the same direction as the previous hot-rolling direction at the reduction rate of 52% to make a sheet of 12 mm. thick. Thereon, by turning the rolling direction, the hot-rolled sheet was again hot-rolled in the direction at a right angle to the said rolling direction at the reduction rate of thereby a sheet of 3 mm. thick was prepared.
  • the finish temperature was After the hot-rolled sheet was pickled, it was coldrolled in the same direction as the direction of the final hot-rolling stage by 73% and then again cold-rolled in the direction at a right angle to the previous cold-rolling to make a sheet of the final gauge as of 0.3 mm. thick.
  • the final gauge sheet was subjected to the decarburization treatment in wet hydrogen for 5 minutes at a temperature of 800 C. After the decarburized sheet was then annealed in an atmosphere of H for 20 hours at a temperature of 1,200 C., the double-oriented silicon steel sheet having magnetic characteristics (Epstein test) in the final cold-rolling direction and in the direction at a right angle thereto, as are shown in Table 3, was obtained.
  • a process for producing a silicon steel sheet having a (100) plane which comprises hot-rolling a steel ingot, repeating the hot-rolling until a steel sheet 1.0 to 7 mm. thick is obtained, cold-rolling t-he thus-obtained hot-rolled sheet to final gauge, and annealing; the improvement wherein (1) said steel ingot consists essentially of iron, 2 to 4% Si, 0.01 to 0.15% C, and 0.01 to 0.06% acid soluble Al, and (2) said steel ingot is subjected to the second-last hot-rolling in a temperature range of from 800 to 1,250 C. at a reduction rate of from.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Electromagnetism (AREA)
  • Manufacturing & Machinery (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
US332423A 1962-12-28 1963-12-23 Process for producing silicon steel sheet having (100) plane in the rolling plane Expired - Lifetime US3266955A (en)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
JP5937662 1962-12-28

Publications (1)

Publication Number Publication Date
US3266955A true US3266955A (en) 1966-08-16

Family

ID=13111484

Family Applications (1)

Application Number Title Priority Date Filing Date
US332423A Expired - Lifetime US3266955A (en) 1962-12-28 1963-12-23 Process for producing silicon steel sheet having (100) plane in the rolling plane

Country Status (4)

Country Link
US (1) US3266955A (en:Method)
BE (1) BE641812A (en:Method)
DE (1) DE1294401B (en:Method)
GB (1) GB1078721A (en:Method)

Cited By (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3537918A (en) * 1968-04-25 1970-11-03 Westinghouse Electric Corp Method for producing cube-on-face oriented structure in a plain carbon iron
US3632456A (en) * 1968-04-27 1972-01-04 Nippon Steel Corp Method for producing an electromagnetic steel sheet of a thin sheet thickness having a high-magnetic induction
US3636579A (en) * 1968-04-24 1972-01-25 Nippon Steel Corp Process for heat-treating electromagnetic steel sheets having a high magnetic induction
US3855018A (en) * 1972-09-28 1974-12-17 Allegheny Ludlum Ind Inc Method for producing grain oriented silicon steel comprising copper
US3855020A (en) * 1973-05-07 1974-12-17 Allegheny Ludlum Ind Inc Processing for high permeability silicon steel comprising copper
US3947296A (en) * 1972-12-19 1976-03-30 Nippon Steel Corporation Process for producing steel sheet of cube-on-face texture having improved magnetic characteristics
US4006044A (en) * 1971-05-20 1977-02-01 Nippon Steel Corporation Steel slab containing silicon for use in electrical sheet and strip manufactured by continuous casting and method for manufacturing thereof
US4427462A (en) 1981-06-18 1984-01-24 Matsushita Electric Industrial Co., Ltd. Electric apparatus and its magnetic core of (100)[011] silicon-iron sheet made by rapid quenching method
EP0318051A3 (en) * 1987-11-27 1991-02-20 Nippon Steel Corporation Process for production of double-oriented electrical steel sheet having high flux density
CN120060725A (zh) * 2025-04-28 2025-05-30 太原科技大学 一种双取向硅钢及其制备方法

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2046717A (en) * 1934-09-18 1936-07-07 Westinghouse Electric & Mfg Co Magnetic material and process for producing same
US3163564A (en) * 1958-03-18 1964-12-29 Yawata Iron & Steel Co Method for producing silicon steel strips having cube-on-face orientation
US3164496A (en) * 1956-09-20 1965-01-05 Gen Electric Magnetic material and method of fabrication

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE741077C (de) * 1939-12-15 1943-11-04 Krupp Ag Walzverfahren zur Herstellung magnetischer Vorzugsrichtungen bei Transformatoren- und Dynamoblechen sowie magnetisierbaren Baendern

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2046717A (en) * 1934-09-18 1936-07-07 Westinghouse Electric & Mfg Co Magnetic material and process for producing same
US3164496A (en) * 1956-09-20 1965-01-05 Gen Electric Magnetic material and method of fabrication
US3163564A (en) * 1958-03-18 1964-12-29 Yawata Iron & Steel Co Method for producing silicon steel strips having cube-on-face orientation

Cited By (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3636579A (en) * 1968-04-24 1972-01-25 Nippon Steel Corp Process for heat-treating electromagnetic steel sheets having a high magnetic induction
US3537918A (en) * 1968-04-25 1970-11-03 Westinghouse Electric Corp Method for producing cube-on-face oriented structure in a plain carbon iron
US3632456A (en) * 1968-04-27 1972-01-04 Nippon Steel Corp Method for producing an electromagnetic steel sheet of a thin sheet thickness having a high-magnetic induction
US4006044A (en) * 1971-05-20 1977-02-01 Nippon Steel Corporation Steel slab containing silicon for use in electrical sheet and strip manufactured by continuous casting and method for manufacturing thereof
US3855018A (en) * 1972-09-28 1974-12-17 Allegheny Ludlum Ind Inc Method for producing grain oriented silicon steel comprising copper
US3947296A (en) * 1972-12-19 1976-03-30 Nippon Steel Corporation Process for producing steel sheet of cube-on-face texture having improved magnetic characteristics
US3855020A (en) * 1973-05-07 1974-12-17 Allegheny Ludlum Ind Inc Processing for high permeability silicon steel comprising copper
US4427462A (en) 1981-06-18 1984-01-24 Matsushita Electric Industrial Co., Ltd. Electric apparatus and its magnetic core of (100)[011] silicon-iron sheet made by rapid quenching method
EP0318051A3 (en) * 1987-11-27 1991-02-20 Nippon Steel Corporation Process for production of double-oriented electrical steel sheet having high flux density
CN120060725A (zh) * 2025-04-28 2025-05-30 太原科技大学 一种双取向硅钢及其制备方法

Also Published As

Publication number Publication date
GB1078721A (en) 1967-08-09
DE1294401B (de) 1969-05-08
BE641812A (en:Method) 1964-04-16

Similar Documents

Publication Publication Date Title
US3159511A (en) Process of producing single-oriented silicon steel
US3287183A (en) Process for producing single-oriented silicon steel sheets having a high magnetic induction
US4046602A (en) Process for producing nonoriented silicon sheet steel having excellent magnetic properties in the rolling direction
CA2164466A1 (en) High magnetic density, low iron loss, grainoriented electromagnetic steel sheet and a method for making
US3266955A (en) Process for producing silicon steel sheet having (100) plane in the rolling plane
US3163564A (en) Method for producing silicon steel strips having cube-on-face orientation
US3287184A (en) Method of producing low carbon electrical sheet steel
US3892604A (en) Method of producing normal grain growth (110) {8 001{9 {0 textured iron-cobalt alloys
US3892605A (en) Method of producing primary recrystallized textured iron alloy member having an open gamma loop
US4478653A (en) Process for producing grain-oriented silicon steel
JP2639227B2 (ja) 無方向性電磁鋼板の製造方法
JP7698649B2 (ja) 二方向性電磁鋼板およびその製造方法
JPH10140297A (ja) 高磁束密度方向性電磁鋼板用一次再結晶焼鈍板
CA2048014C (en) Method of manufacturing an oriented silicon steel sheet having improved magnetic flux density
JP7307354B2 (ja) 磁気特性が優れた方向性電磁鋼板
US4608100A (en) Method of producing thin gauge oriented silicon steel
US3136666A (en) Method for producing secondary recrystallization grain of cube texture
US4251295A (en) Method of preparing an oriented low alloy iron from an ingot alloy having a high initial sulfur content
US3586545A (en) Method of making thin-gauge oriented electrical steel sheet
JPH01139722A (ja) 二方向性電磁鋼板の製造方法
JPH04224624A (ja) 磁気特性に優れた電磁鋼板の製造方法
EP0585956B1 (en) Thick grain-oriented electrical steel sheet exhibiting excellent magnetic properties
JPH0733547B2 (ja) 磁束密度の高い二方向性電磁鋼板の製造方法
JPH0623411B2 (ja) 異方性の小さい電磁鋼板の製造方法
US6858095B2 (en) Thick grain-oriented electrical steel sheet exhibiting excellent magnetic properties