US3636579A - Process for heat-treating electromagnetic steel sheets having a high magnetic induction - Google Patents

Process for heat-treating electromagnetic steel sheets having a high magnetic induction Download PDF

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US3636579A
US3636579A US817795A US3636579DA US3636579A US 3636579 A US3636579 A US 3636579A US 817795 A US817795 A US 817795A US 3636579D A US3636579D A US 3636579DA US 3636579 A US3636579 A US 3636579A
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percent
steel sheet
annealing
content
cold
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Akiri Sakakura
Satoru Taguchi
Toshiya Wada
Kiyoshi Ueno
Takaaki Yamamoto
Nabuo Urushiyama
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Nippon Steel Corp
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    • 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
    • C21D8/1244—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
    • 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
    • C21D8/1233—Cold 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
    • C21D8/1266—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 between cold rolling steps

Definitions

  • a method for producing a single-oriented silicon steel sheet having a very high magnetic induction by subjecting a steel [30] Foreign Application Priority Data sheet containing C and acid-soluble Al to the following process steps; rolling the steel sheet to an intermediate gauge, Apr. 24, Japan j g the toned Steel Sheet to an li g i a p ture range of 750 to l,200 C. for 30 seconds to 30 minutes [52] U.S.
  • This invention relates to a method for producing singleoriented electromagnetic steel sheets having an easy magnetization axis l in the rolling direction of the steel sheet.
  • Single-oriented steel sheets which are soft magnetic materials are used mostly as iron cores for transformers and other electric devices. Therein magnetic characteristics, excitation characteristics and core loss values must be favorable.
  • the present inventors use the magnetic induction B (gausses) generated in the iron core at the intensity H (oersted) of the magnetic field as a value for expressing the excitation characteristics, and the core loss W 15/50 (W/kg.) at 50 cycles and an alternating current magnetic induction of 15,000 gausses as a value for expressing the core, that is, an energy loss lost from the iron core when a prescribed altemating current magnetic induction is given to the iron core.
  • the core loss value generally increases, and as compared with a material having low B characteristics a steel sheet having B characteristics has a much lower core loss in the region of high magnetic induction, and moreover the increase in the core loss is at a lower rate as the magnetic induction rises.
  • the present invention has for its object the supply of products which can meet the requirements described above. That is, according to the method of the present invention it is possible to produce electromagnetic steel sheets which are markedly superior to any conventional single-oriented silicon steel sheets with respect to the magnetic induction 13 in the rolling direction, that is, steel sheets which have a magnetic induction as high as at least 18,500 gausses, and even up to 20,100 gausses.
  • the present inventors have discovered the following new fact in regard to the production of single-oriented electromagnetic steel sheets which have a low Si content or no Si content in order to improve B,, that is, B, is a physical property which is a determined by the chemical composition of an alloy steel and can not be influenced by treating conditions.
  • B is a physical property which is a determined by the chemical composition of an alloy steel and can not be influenced by treating conditions.
  • the Si content has a great influence on B,. For instance, when Si is 0 percent, B, is about 21,600 gausses, and when Si is 1 percent, B, is about 21,300 gausses, when Si is 2 percent, B, is about 20,800 gausses and when Si is 3 percent, B, is about 20,300 gausses. That is to say, the lower the Si content, the higher B,.
  • the present invention has succeeded in providing a method for manufacturing ideal single-oriented electromagnetic steel sheets with high magnetic induction, that is, a high B value, and moreover having a high B, value on account of the Si content being low, by producing secondary recrystallization grains having a very well selected ⁇ 1 l0 ⁇ l00 -orientation, extending over a wide range of silicon content from 0 to 4 percent.
  • the treating method according to the present invention relates to a method for producing single-oriented silicon steel sheet having a high magnetic induction, in which a normal steel material or silicon steel material which contains C and Al as indispensable elements is produced according to known steelmaking methods, melting methods and casting methods which are used as normal industrial techniques, the thus obtained steel material is hot-rolled and then subjected to an annealing process and cold-rolling process one time or more than one time respectively to reach the final gauge, the thus obtained product is decarburized and then subjected to a final annealing to generate secondary recrystallization grains having a ⁇ 1l0 ⁇ l00 -orientation in the steel material.
  • the present invention modifies this conventional method in that the final cold-rolling is carried out at a reduction rate of 65 to percent depending upon the Si content and an intermediate annealing, preferably an annealing immediately before the final cold-rolling, is carried out in such a temperature range, that is, in the range of 750 to l,200 C., that 'y-transformation can occur at least in a part of the steel material, that is, in the range of 750 to 1,200 C., and thereupon the quenching is carried out from this temperature range, in which the transformation of 'y to a has been completed, to a temperature below the said range, that is, to a temperature below the range from 750 to 950 C.
  • the Si content so as to cause AlN of preferred size to precipitate in the steel sheet, so that after the final annealing the magnetic induction B in the said rolling direction may well be at a high level, that is, at least 18,500 gausses and at a maximum 20,100 gausses.
  • An object of the present invention is to provide a method for producing a single-oriented silicon steel sheet having a high magnetic induction.
  • Another object of the present invention is to provide a method for producing a single-oriented silicon steel sheet having a high magnetic induction from a steel sheet having no silicon or a low silicon content
  • a further object of the present invention is to provide a chemical composition most suitable for producing a singleoriented silicon steel sheet having a high magnetic induction from a steel sheet having no silicon content or a low silicon content. 7
  • FIG. 1 is a graph showing a comparison of the excitation characteristics of products of the present invention with those of known products on the market.
  • FIG. 2 is a graph showing a comparison of the core loss values of products of the present invention with those of known products on the market.
  • FIG. 3 is a graph showing the relationship between the C- acid-soluble Al values of products of the present invention and the excitation characteristics.
  • FIG. 4 is a graph showing the relationship between the cooling rate after the annealing according to the present invention and the excitation characteristics.
  • the normal steel or silicon steel material which is a starting material in the present invention is an ingot made by solidifying by any casting method a molten steel made by a steelmaking method which is already known such, as, for example, by an open-hearth furnace, electric furnace or converter or melted by a known melting method such as, for example, by a high-frequency electric furnace or vacuum-melting furnace.
  • a slablike ingot obtained by a continuous casting method, which recently has come into wide use, can also be used as a material in the present invention.
  • the atmosphere in the case casting is usually air but may be vacuum or of an inert gas as well.
  • the material of the present invention can be made by any steelmaking, melting and casting methods. But the composition of the material must satisfy the following conditions, irrespective of the methods for producing the same, that is, steelmaking, melting or casting methods.
  • C less than 0.085 percent Si percent to 4.0 percent Al 0.010 to 0.065 percent Al means an acid-soluble A1, which, however, will be hereihafter referred to simply as Al.
  • the rest is Fe and unavoidable impurities. It is necessary that C in the above-mentioned material should be present in an amount sufficient to produce a -y-transformation at least in apart of the steel in response to the Si content. According to our experiences, C in a steel ingot must be at least 0.025 percent where Si is 3 percent but may be about 0.005 percent in case Si is 0 percent. As regards the added elements, the inventors have the following view.
  • the restricting effect of the general precipitates is also an important factor for effecting the secondary recrystallization. Therefore, the presence of precipitate-forming elements is permissible so far it does not hinder the formation of the said AlN.
  • S, Se and the like may be present in an amount of less than a maximum of 0.1 percent respectively.
  • Te may be included in an amount less than 0.20 percent.
  • care must be taken unless such elements form precipitates like carbide.
  • a silicon steel ingot which contained about 1.8 percent Si and in which the contents of C and Al varied, was hot-rolled to a steelsheet about 2.0 mm. thick.
  • the sheet was at first annealed in N at 1,050" C. for 2 minutes and then sprayed with atomized water drops. After the steel sheet was cooled down to a room temperature in about 50 seconds, it was cold-rolled to a steel sheet 0.35 mm. thick.
  • the thus cold-rolled steel sheet was decarburized at 800 C. and was finally subjected to a box-annealin g at 1,050 C. for 15 hours.
  • Si is kept less than 4 percent.
  • the present invention has it as an object to improve the B characteristic and B, characteristic. Therefore, there is no lower limit.
  • the principal object of which is to obtain a single-oriented silicon steel sheet having a low Si content there are some variations in the said operating conditions according to the Si content.
  • the annealing should be carried out in the temperature range of 850 to 1,200 C. when the Si content is l to 2.5 percent and in the temperature range of 750 to l,200 C. when the Si content is less than 1 percent.
  • substantially the same annealing conditions as those above mentioned are also required, although there can be some variations in the temperature range depending on the Si content as above mentioned.
  • the annealing time can be in the range of 30 seconds to 30 minutes for any Si content.
  • the annealing time and the temperature range are such so as to be able to effect the 'y-transformation at least in a part of the steel sheet according to the Si content.
  • FIG. 4 shows relationship between the magnetic induction B of a product and the cooling rate when the product is produced from a silicon steel ingot containing 2.2 percent Si, 0.045 percent C and 0.025 percent Al by the following steps, that is, blooming and hot-rolling the said steel ingot to a hotrolled steel sheet 2.3 mm. thick, then annealing the hot-rolled steel sheet in nitrogen for 2 minutes at each temperature as shown in FIG. 4 and thereafter gradually cooling the annealed steel sheet down to 850 C. at a certain cooling rate and thereafter cooling the steel sheet to temperature below 850 C. at various cooling rates as shown by 10 different cooling curves in FIG. 4. From this figure the following facts have been ascertained. When the annealing temperature was 800 C.
  • the cooling from the annealing temperature to 850 C. may be carried out at any cooling rate. If the annealing temperature is higher than l,200 C., the secondary recrystallization will not occur due to the final annealing. On the other hand, if the annealing temperature is as low as 800' C.
  • C should be adjusted to be below 0.080 percent so that a 7- transformation will occur in at least a part of the steel sheet due to the presence of Si in carrying out the annealing prior to the final cold-rolling.
  • the C in the steel ingot is 0.005 percent higher than before the annealing prior to the final cold-rolling, because the amount decarburized during the ordinary hot-rolling is taken into consideration.
  • the C content in the steel sheet is important in carrying out the annealing prior to the final cold-rolling.
  • the C content of the steel sheet at the time of carrying out the annealing can easily be caused to be in the specified range as above mentioned, because the said annealing is carried out after the hot-rolling.
  • the annealing temperature is in the range of 750 to l,200 C. in which a -ytransformation will occur because of the Si content. In summary the annealing temperature should be:
  • the annealing time in this temperature range is 30 seconds to 30 minutes.
  • the annealing time exceeds 30 minutes, the growth of crystal grains will occur during the annealing and the development of the secondary recrystal grains in the final annealing will become imperfect. Therefore, it is not favorable. Further, because this annealing is generally carried out continuously, an annealing exceeding 30 minutes is industrially disadvantageous. On the other hand, with an annealing for less than 30 seconds, the effect which is the object of the present invention can not be obtained.
  • the steel band, the annealing of which has been completed as above mentioned, is then subjected to a cooling which is, however, carried out at any cooling rate within a temperature range, in which 'y formed by the said annealing is transformed into a, that is, a range of 750 to l,200 C., 850 to l,200 C. or 950 to l,200 C. according to the Si content.
  • the steel sheet, in which tit-transformation has been efiected by the said cooling is quenched from the temperature range of 750 to l,200 C., 850 to l,200 C. or 950 to l,200 C. according to the Si content to a temperature below 400 C. by using any adequate artificial means.
  • the cooling time is in a range of 2 seconds to 200 seconds and it is desirable to cool in a shorter time where the Si content is high. in general, the higher the cooling rate, the better the B value irrespective of the Si content.
  • the cooling rate of shorter than 2 seconds the generation of the secondary recrystallization grains by the final annealing is perfect, but the 8, value is deteriorated.
  • various cooling curves are possible, but in all cases the effect of the present invention can be obtained if the cooling rate at each moment is greater than an average cooling rate, that is,
  • the cooling from 400 C. to a lower temperature there is no particular limitation in the present invention.
  • the cooling rate of the present invention for the final cooling.
  • the steel sheet is usually cooled from the temperature range of 750 to 950 C. according to the Si content down to near room temperature along a continuous curve.
  • AlN should be precipitated at least in an amount of 0.0005 percent (N as AlN) in the steel sheet after the annealing and cooling thereof have been completed.
  • the annealing atmosphere is related to the precipitation of AlN required for the secondary recrystallization as already described.
  • the steel ingot obtained in an open-hearth furnace contains, more than 0.0040 percent N which is sufficient to precipitate 0.0005 percent AlN (N as AlN). Therefore, so long as no great denitrification occurs, the annealing atmosphere can be a reducing or neutral atmosphere such as, for example, H Ar, a gaseou's'mixture of them or air.
  • the N content will be so small that it will be necessary to add nitrogen during annealing.
  • the method of adding nitrogen is not critical but, in the present invention, it is recommended to carry out the annealing in a neutral or reducing gas containing at least 10 percent N, by volume.
  • a precipitate which can selectively grow secondary recrystallization grains having a very well regulated, though not complete, orientation during the final annealing no precipitate is satisfactory other than AlN, as is mentioned at the beginning of the present specification.
  • the crux of the present invention resides in causing AlN of adequate size to precipitate in the steel sheet before it is subjected to the final heavy cold-rolling.
  • the composition of the steel sheet (C, Si and Al) has a close mutual relation with the temperature and time of annealing and the cooling rate through the medium of the y to a transformation.
  • the cold-rolling is carried out one or more times and the cold-rolling step can be carried out at a reduction rate of 65 to 95 percent depending on the Si content so that, the higher the Si content, the higher the reduction rate.
  • any intermediate annealing to be carried out between multistage cold-rolling steps can be carried out at a temperature and for a time which are sufficient to make the coldrolled structure a primary recrystallized structure and these conditions are not set forth in detail.
  • the above-mentioned AlN-precipitating annealing as an intermediate annealing.
  • the number of times of the cold-rolling step is performed can be determined by the thickness of the hot-rolled sheet and the specified final cold-rolling reduction rate.
  • the hot-rolled sheet is usually 1.5 to 7 mm. thick.
  • the steel sheet having a sheet thickness after the final coldrolling is then subjected to a decarburizing annealing.
  • This annealing is to make the cold-rolled structure a primary recrystal structure and at the same time to remove C which is detrimental .for developing secondary recrystal grains in the ⁇ 110 ⁇ l direction in the final annealing.
  • Any known process can be used for the decarburizing annealing.
  • the final annealing should be carried out at such temperature and for such a time that secon ary recrystal grains in the ⁇ llO ⁇ l00 direction can develop well. It is preferable to develop the secondary recrystal grains in a temperature range wherein no y-transformation is produced due to the Si content and at a temperature as high as industrially possible, because the generation of 'y-transformation will change the once-obtained secondary recrystal grains in the ⁇ 110 ⁇ l00 direction so that they are in another direction.
  • Si is less than 1 percent
  • final annealing should be carried out at 950 C. or usually at a temperature lower than this. However, the higher the Si content, the higher the temperature can be elevated.
  • EXAMPLE 1 An al-killed steel ingot containing 0.050 percent C and 0.041 percent Al was bloomed and hot-rolled to a hot-rolled steel sheet 2.2 mm. thick. After the steel sheet was annealed in N at 1,000 C. for 2 minutes, it was cooled in warm water having a temperature of C. The cooling rate was about 10 seconds for the temperature descent from l,000 C. to 750 C. and about 25 seconds from 750to 100 C. The content of AlN after the annealing was 0.0045 percent (N as AIN). After pickling, the sheet was cold-rolled at a reduction rate of 77.3 percent to make the thickness of the sheet 0.50 mm. The coldrolled sheet was then decarburized at 750 C. for 5 hours by an open coil system and thereafter finally annealed in H at 870 C. for 20 hours.
  • EXAMPLE 2 A silicon steel ingot containing 0.32 percent C, 1.05 percent Si and 0.036 percent Al was hot-rolled to a hot-rolled steel sheet 2.2 mm. thick. The content of C in the hot-rolled steel sheet was 0.030 percent. After the steel sheet was annealed in N: at l,050 C. for 2 minutes, it was cooled by slightly spraying N gas onto the both surfaces of the steel sheet. The cooling rate was about 13 seconds for the temperature descent from l,050 to 850 C. and about 70 seconds for that from 850 to 400 C. The content of AlN after'this annealing was 0.0062 percent (N as AlN).
  • the steel sheet was then cold-rolled at a reduction rate of 84.1 percent to a cold-rolled steel sheet 0.35 mm. thick. After the cold-rolled sheet was decarburized in wet H, at 800 C. for 3 minutes, it was finally annealed in H at 950 C. for 10 hours.
  • EXAMPLE 3 A silicon steel sheet containing 0.043 percent C, 2.10 percent Si and 0.036 percent Al was bloomed and hot-rolled to a hot-rolled steel sheet 3 mm. thick. The content of C of the hotrolled sheet was 0.041 percent, indicating that only a slight decarburization was effected.
  • the hot-rolled steel sheet was cold-rolled at a reduction rate of 30 percent make the thickness of the sheet to 2.1 mm. Then, it was annealed in N, at 1,100" C. for 2 minutes, and thereafter cooled by blowing a jet air steam against the sheet. The cooling rate was about 18 seconds for the temperature descent from l,l00 C. to 850 C. and about 27 seconds for that from 850 to 400 C.
  • the content of AlN after this annealing was 0.0055 percent (N as AlN).
  • the steel sheet was cold-rolled at a reduction rate of 83.3 percent to a cold-rolled steel sheet 0.35 mm. thick.
  • the cold-rolled steel sheet was decarburized in wet H, at 800 C. for 3 minutes, it was annealed at 1,200 C. for 20 hours.
  • the magnetic characteristics in the rolling direction of the product were as shown by FIG. 1C, that is:
  • EXAMPLE 4 A silicon steel ingot containing 0.045 percent C, 2.05 percent Si and 0.020 percent Al was bloomed and hot-rolled to a hot-rolled steel sheet 2.3 mm. thick. The content of C of the hot-rolled steel sheet was 0.041 percent. After the hot-rolled steel sheet was annealed in N at 1,050 C. for 2 minutes, it was cooled by slightly blowing N gas onto the steel sheet. The cooling rate was substantially the same as in example 2, and the content of AlN after this annealing was 0.0032 percent (N as AlN). Then, the steel sheet was cold-rolled at a reduction rate of 84.8 percent to a cold-rolled sheet 0.35 mm. thick. Thereafter, the cold-rolled steel sheet was decarburized in wet H at 800 C. for 3 minutes and then finally annealed at 1,200 C. for 20 hours. The magnetic characteristics in the rolling direction of the product were:
  • io is/so EXAMPLE 5
  • a silicon steel ingot containing 0.043 percent C, 2.96 percent Si, 0.029 percent Al, 0.10 percent Mn and 0.029 percent S was bloomed and hot-rolled to a hot-rolled steel sheet 2.8 mm. thick.
  • the contentof C after the hotrolling was 0.040 percent.
  • After the hot-rolled steel band was continuously annealed in N, at 1,l50 C. for 2 minutes, it was subjected to a slow cooling to 950 C. in the cooling zone of a furnace, which was followed by a quenching by spraying with high-pressure water.
  • the cooling rate was about 20 seconds for the temperature descent from l,l50 to 950 C. and about 9 seconds for that from 950 to 20 C.
  • FIG. 2 shows the core loss characteristics of this example as compared with those of a known commercial product, which is shown by FIG. 2B.
  • EXAMPLE 6 A silicon steel ingot containing 0.050 percent C, 3.15 percent Si, 0.035 percent S and 0.021 percent Al, said ingot being prepared in an open-hearth furnace, was bloomed and hotrolled to a hot-rolled steel sheet 3.0 mm. thick. After the hotrolled steel sheet was maintained in a continuous annealing furnace having N atmosphere at 1,050 C. for 1 minute, it was subjected to a forced cooling by using an N -gas-blowing device installed at the port of the furnace. After pickling, the steel was cold-rolled at a reduction rate of 51 percent to a cold-rolled sheet having an intermediate gauge as of 1.47 mm. Thereupon, the cold-rolled steel sheet was annealed at 800 C.
  • a process for producing a single-oriented electromagnetic steel sheet having an excellent excitation characteristic and a high saturated magnetic induction in the rolling direction of the steel sheet which process includes the steps of: subjecting a steel ingot containing 0 to 4.0 weight percent Si, less than 0.085 weight percent C and 0.010 to 0.065 weight percent acid-soluble Al to blooming and hot-rolling; subjecting the hot-rolled steel sheet to: (a) at least one annealing, said one annealing when it is the only annealing being an annealing for causing at least 0.0005 weight percent AlN (N as AlN) to precipitate before a final cold-rolling, and when there is a plurality of annealing treatments, one of the treatments being an annealing for causing at least 0.0005 weight percent AlN (N as AIN) to precipitate before a final cold-rolling; and to (b) at least one cold-rolling, said one cold-rolling when it is the only cold-rolling and one of the cold-
  • the Si content when the Si content is up to 1 weight percent and the C content is up to 0.080 weight percent, to a temperature of 850-l ,200 C. when the Si content is from 1.0 to 2.5 weight percent and the C content is from 0.010 to 0.080 weight percent, and to a temperature of 950-l,200 C. when the Si content is from 2.5 to 4.0 weight percent and the C content is from 0.020 to 0.080 weight percent, holding the sheet at the annealing temperature for a time of from 30 sec. to 30 min., and then quenching the annealed sheet to a temperature at least as low as 400 C. in a time of from 2 to 200 sec.

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US817795A 1968-04-24 1969-04-21 Process for heat-treating electromagnetic steel sheets having a high magnetic induction Expired - Lifetime US3636579A (en)

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BE (1) BE731991A (de)
CA (1) CA939238A (de)
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Cited By (25)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE2348249A1 (de) * 1972-09-28 1974-04-04 Allegheny Ludlum Ind Inc Kornorientierter siliciumstahl und verfahren zu seiner herstellung
US3841924A (en) * 1972-04-05 1974-10-15 Nippon Steel Corp Method for producing a high magnetic flux density grain oriented electrical steel sheet
DE2435413A1 (de) * 1973-07-23 1975-02-13 Centro Speriment Metallurg Verfahren zum herstellen von kornorientierten blechen fuer magnetische zwecke sowie kornorientiertes blech
US3873381A (en) * 1973-03-01 1975-03-25 Armco Steel Corp High permeability cube-on-edge oriented silicon steel and method of making it
US3990924A (en) * 1972-08-01 1976-11-09 Nippon Steel Corporation Method for producing high magnetic flux density grain-oriented electrical steel sheet and strips having excellent characteristics
US4014717A (en) * 1974-10-09 1977-03-29 Centro Sperimentale, Metallurgico S.P.A. Method for the production of high-permeability magnetic steel
EP0019289A2 (de) * 1979-05-16 1980-11-26 Nippon Steel Corporation Verfahren zum Herstellen eines kornorientierten Siliziumstahlbandes
US4265683A (en) * 1979-02-07 1981-05-05 Westinghouse Electric Corp. Development of grain-oriented iron sheet for electrical apparatus
US4319936A (en) * 1980-12-08 1982-03-16 Armco Inc. Process for production of oriented silicon steel
FR2506784A1 (fr) * 1981-05-30 1982-12-03 Nippon Steel Corp Procede de fabrication d'une tole en acier electromagnetique a grain oriente ayant une haute densite de flux magnetique
US4371405A (en) * 1979-08-22 1983-02-01 Nippon Steel Corporation Process for producing grain-oriented silicon steel strip
US4416707A (en) * 1981-09-14 1983-11-22 Westinghouse Electric Corp. Secondary recrystallized oriented low-alloy iron
EP0098324A1 (de) * 1982-07-08 1984-01-18 Nippon Steel Corporation Verfahren zum Herstellen eines aluminiumhaltigen, kornorientierten Siliciumstahlbandes
EP0100638A2 (de) 1982-07-30 1984-02-15 Armco Advanced Materials Corporation Laserbehandlung von Elektrostahl
EP0101321A2 (de) * 1982-08-18 1984-02-22 Kawasaki Steel Corporation Verfahren zum Herstellen kornorientierter Bleche oder Bänder aus Siliziumstahl mit hoher magnetischer Induktion und geringen Eisenverlusten
US4517032A (en) * 1982-03-15 1985-05-14 Kawasaki Steel Corporation Method of producing grain-oriented silicon steel sheets having excellent magnetic properties
US4563226A (en) * 1981-11-16 1986-01-07 Nippon Steel Corporation Process for producing a grain-oriented electrical steel sheet
US4596614A (en) * 1984-11-02 1986-06-24 Bethlehem Steel Corporation Grain oriented electrical steel and method
EP0253904A1 (de) * 1986-07-03 1988-01-27 Nippon Steel Corporation Verfahren zur Herstellung kornorientierter Siliciumstahlbleche mit hervorragenden magnetischen Eigenschaften
US4824493A (en) * 1986-02-14 1989-04-25 Nippon Steel Corporation Process for producing a grain-oriented electrical steel sheet having improved magnetic properties
US5393321A (en) * 1991-07-27 1995-02-28 British Steel Plc Method and apparatus for producing strip products by a spray forming technique
EP0835944A1 (de) * 1996-10-11 1998-04-15 Kawasaki Steel Corporation Verfahren zum Herstellen kornorientierter Elektrobleche
EP0837148A2 (de) * 1996-10-21 1998-04-22 Kawasaki Steel Corporation Kornorientiertes elektromagnetisches Stahlblech
US6146033A (en) * 1998-06-03 2000-11-14 Printronix, Inc. High strength metal alloys with high magnetic saturation induction and method
US7204894B1 (en) 2004-03-18 2007-04-17 Nucor Corporation Annealing of hot rolled steel coils with clam shell furnace

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JPS5432412B2 (de) * 1973-10-31 1979-10-15
DK154349C (da) * 1974-01-15 1989-05-01 Kawasaki Steel Co Fremgangsmaade til fremstilling af baand og elektrisk ledende staal orienteret i en retning og med hoej magnetisk induktion
GB1521680A (en) * 1974-09-23 1978-08-16 British Steel Corp Steels for electromagnetic applications
JPS5920745B2 (ja) * 1980-08-27 1984-05-15 川崎製鉄株式会社 鉄損の極めて低い一方向性珪素鋼板とその製造方法
BR9800978A (pt) * 1997-03-26 2000-05-16 Kawasaki Steel Co Chapas elétricas de aço com grão orientado tendo perda de ferro muito baixa e o processo de produção da mesma
KR102559250B1 (ko) 2023-01-04 2023-07-26 (주)일신오토클레이브 실링 카트리지 및 이를 구비하는 실링구 커버

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US3841924A (en) * 1972-04-05 1974-10-15 Nippon Steel Corp Method for producing a high magnetic flux density grain oriented electrical steel sheet
US3990924A (en) * 1972-08-01 1976-11-09 Nippon Steel Corporation Method for producing high magnetic flux density grain-oriented electrical steel sheet and strips having excellent characteristics
DE2348249A1 (de) * 1972-09-28 1974-04-04 Allegheny Ludlum Ind Inc Kornorientierter siliciumstahl und verfahren zu seiner herstellung
US3873381A (en) * 1973-03-01 1975-03-25 Armco Steel Corp High permeability cube-on-edge oriented silicon steel and method of making it
DE2435413A1 (de) * 1973-07-23 1975-02-13 Centro Speriment Metallurg Verfahren zum herstellen von kornorientierten blechen fuer magnetische zwecke sowie kornorientiertes blech
US3959033A (en) * 1973-07-23 1976-05-25 Mario Barisoni Process for manufacturing silicon-aluminum steel sheet with oriented grains for magnetic applications, and products thus obtained
US4014717A (en) * 1974-10-09 1977-03-29 Centro Sperimentale, Metallurgico S.P.A. Method for the production of high-permeability magnetic steel
US4265683A (en) * 1979-02-07 1981-05-05 Westinghouse Electric Corp. Development of grain-oriented iron sheet for electrical apparatus
EP0019289A3 (en) * 1979-05-16 1981-11-25 Nippon Steel Corporation Process for producing grain-oriented silicon steel strip
EP0019289A2 (de) * 1979-05-16 1980-11-26 Nippon Steel Corporation Verfahren zum Herstellen eines kornorientierten Siliziumstahlbandes
US4371405A (en) * 1979-08-22 1983-02-01 Nippon Steel Corporation Process for producing grain-oriented silicon steel strip
US4319936A (en) * 1980-12-08 1982-03-16 Armco Inc. Process for production of oriented silicon steel
FR2506784A1 (fr) * 1981-05-30 1982-12-03 Nippon Steel Corp Procede de fabrication d'une tole en acier electromagnetique a grain oriente ayant une haute densite de flux magnetique
US4806176A (en) * 1981-05-30 1989-02-21 Nippon Steel Corporation Process for producing a grain-oriented electromagnetic steel sheet having a high magnetic flux density
US4416707A (en) * 1981-09-14 1983-11-22 Westinghouse Electric Corp. Secondary recrystallized oriented low-alloy iron
US4563226A (en) * 1981-11-16 1986-01-07 Nippon Steel Corporation Process for producing a grain-oriented electrical steel sheet
US4517032A (en) * 1982-03-15 1985-05-14 Kawasaki Steel Corporation Method of producing grain-oriented silicon steel sheets having excellent magnetic properties
EP0098324A1 (de) * 1982-07-08 1984-01-18 Nippon Steel Corporation Verfahren zum Herstellen eines aluminiumhaltigen, kornorientierten Siliciumstahlbandes
EP0100638A2 (de) 1982-07-30 1984-02-15 Armco Advanced Materials Corporation Laserbehandlung von Elektrostahl
EP0101321A3 (en) * 1982-08-18 1985-11-06 Kawasaki Steel Corporation Method of producing grain oriented silicon steel sheets or strips having high magnetic induction and low iron loss
EP0101321A2 (de) * 1982-08-18 1984-02-22 Kawasaki Steel Corporation Verfahren zum Herstellen kornorientierter Bleche oder Bänder aus Siliziumstahl mit hoher magnetischer Induktion und geringen Eisenverlusten
US4596614A (en) * 1984-11-02 1986-06-24 Bethlehem Steel Corporation Grain oriented electrical steel and method
US4824493A (en) * 1986-02-14 1989-04-25 Nippon Steel Corporation Process for producing a grain-oriented electrical steel sheet having improved magnetic properties
EP0253904A1 (de) * 1986-07-03 1988-01-27 Nippon Steel Corporation Verfahren zur Herstellung kornorientierter Siliciumstahlbleche mit hervorragenden magnetischen Eigenschaften
US4797167A (en) * 1986-07-03 1989-01-10 Nippon Steel Corporation Method for the production of oriented silicon steel sheet having excellent magnetic properties
US5393321A (en) * 1991-07-27 1995-02-28 British Steel Plc Method and apparatus for producing strip products by a spray forming technique
EP0835944A1 (de) * 1996-10-11 1998-04-15 Kawasaki Steel Corporation Verfahren zum Herstellen kornorientierter Elektrobleche
US5885371A (en) * 1996-10-11 1999-03-23 Kawasaki Steel Corporation Method of producing grain-oriented magnetic steel sheet
EP0837148A3 (de) * 1996-10-21 1998-07-15 Kawasaki Steel Corporation Kornorientiertes elektromagnetisches Stahlblech
EP0837148A2 (de) * 1996-10-21 1998-04-22 Kawasaki Steel Corporation Kornorientiertes elektromagnetisches Stahlblech
US6083326A (en) * 1996-10-21 2000-07-04 Kawasaki Steel Corporation Grain-oriented electromagnetic steel sheet
US6444050B1 (en) 1996-10-21 2002-09-03 Kawasaki Steel Corporation Grain-oriented electromagnetic steel sheet
US20030121566A1 (en) * 1996-10-21 2003-07-03 Kawasaki Steel Corporation Grain-oriented electromagnetic steel sheet
US6929704B2 (en) 1996-10-21 2005-08-16 Jfe Steel Corporation Grain-oriented electromagnetic steel sheet
US6146033A (en) * 1998-06-03 2000-11-14 Printronix, Inc. High strength metal alloys with high magnetic saturation induction and method
US6423155B1 (en) 1998-06-03 2002-07-23 Printronix, Inc. High strength metal alloys with high magnetic saturation induction and method
US7204894B1 (en) 2004-03-18 2007-04-17 Nucor Corporation Annealing of hot rolled steel coils with clam shell furnace

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DE1920968B2 (de) 1972-03-02
BE731991A (de) 1969-10-01
CA939238A (en) 1974-01-01
DE1966231A1 (de) 1972-02-17
DE1920968A1 (de) 1971-04-22
FR2006864A1 (de) 1970-01-02
DE1966231C3 (de) 1975-06-26
SE358412B (de) 1973-07-30
DE1966231B2 (de) 1974-10-10
GB1276309A (en) 1972-06-01

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