US3203839A - Process for producing nonoriented silicon steel sheets - Google Patents

Process for producing nonoriented silicon steel sheets Download PDF

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Publication number
US3203839A
US3203839A US259190A US25919063A US3203839A US 3203839 A US3203839 A US 3203839A US 259190 A US259190 A US 259190A US 25919063 A US25919063 A US 25919063A US 3203839 A US3203839 A US 3203839A
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magnetic
rolling
steel sheet
silicon steel
steel sheets
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Takahashi Kenji
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Yawata Iron and Steel Co Ltd
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Yawata Iron and Steel Co Ltd
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    • 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
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • 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

  • silicon steel sheets are largely classified by the producing processes into hot-rolled silicon steel sheets and cold-rolled silicon steel sheets.
  • the main rolling for the reduction of the thickness of the hot-rolled silicon steel sheet is carried out at a high temperature above 700 C. and most of the crystal grains of the produced steel sheet are arranged in disorder and are so-called nonoriented.
  • the cold-rolled silicon steel sheet so treated to reduce the thickness is specially worked, e.g., the so-called strain treatment (U.S. Pat. 2,236,519), it will become a so-called anisotropic steel sheet in which the characteristics parallel to the rolling direction and those transverse to the rolling direction are different from each other.
  • the steel sheet produced by the coldrolling process has advantages in that it can be made longer and is therefore not only economically very advantageous in the production of the steel sheet but also is uniform and the surface of such sheet is smooth and beautiful and the space factor may be far elevated in assembling an iron core.
  • the oriented silicon steel sheet most of the crystal grains forming the steel sheet are so arranged by directing the direction of easy magnetization 100 direction) in the rolling direction or in both the rolling direction and the transverse direction. It is therefore very effective for an iron core for electric machines in which such steel sheet can be used as magnetized in both the rolling direction and the direction at right angles thereto.
  • the magnetic characteristics in any other direction is far inferior to that in the rolling direction or the direction at right angles thereto. Thus it has no uniform characteristic in every direction. Therefore, it can not help being disadvantageous as an iron core for rotary machines and any other electric machines forming complicated magnetic paths.
  • it is not only required from the characteristics of electric machines but also convenient in designing machines, to produce an iron core for rotary electric machines which has as little difference as possible when magnetized in the rolling direction and when magnetized in another direction or is so-called nonoriented.
  • Processes for producing nonoriented silicon steel sheets by cold rolling have been studied of late.
  • One of the known processes is a process wherein, when less than about 3% silicon is added, the growth of oriented crystals is inhibited by utilizing the 11- lattice transformation of the silicon steel in finish-annealing. Said process is intended specifically for once strong cold rolling having no intermediate annealing. Therefore, as the chance of de- 'ice carburizing is relatively small, there is a defect that, unless a steel of good quality is used, no favorable results are generally obtained in general magnetic characteristics.
  • anisotrophy will occur because of delicate skin pass rolling.
  • An object of the present invention is to provide a process wherein nonoriented silicon steel sheets high in magnetic characteristics are obtained as uniform stable products by a simple process.
  • Another object of the present invention is to provide a process wherein nonoriented silicon steel sheets high in magnetic characteristics are obtained by hot-rolling an Fe-Si-Al steel having a specific composition, in a known manner, and then two stage cold-rolling and heat-treating the steel.
  • a further object of the present invention is to provide a process wherein nonoriented silicon steel sheets high in magnetic characteristics are obtained by carrying out the above mentioned cold-rolling step one to more than three times.
  • FIGURES 1 and 2 show the pole figures of planes prepared with X-rays on the crystal grains of nonoriented magnetic steel sheets treated by the process of the present invention.
  • FIGURE 3 shows magnetic torque curves of nonoriented silicon steel sheets produced by the process of the present invention
  • FIGURE 4 shows magnetization curves of nonoriented silicon steel sheets produced by the process of the present invention as compared respectively with the characteristics of a commercial nonoriented silicon steel sheet.
  • the process of the present invention comprises the step of hot-rolling into a steel sheet, according to a process known per se, an ingot composed of 15-35% Si and 0.5-1.5% Al, the rest being Fe and unavoidable impurities and the sum of Si and Al content being in the range of 25-45%, the step of cold-rolling said steel sheet at a reduction rate of 50-80% and intermediately annealing it at a temperature of from 750-950 C. in a reductive or neutral atmosphere for 3 minutes to 1 hour and the step of cold'rolling said steel sheet at a reduction rate of 50-80% and finally annealing it at LOGO-1,100 C. for 5-40 hours.
  • the contents of silicon and aluminum in the present invention shall be explained.
  • the sum of the contents of silicon and aluminum is made substantially 25-45%. If this sum is less than 2.5%, the specific resistance will be reduced and, as a result, the core loss will increase. If it is more than 4.5%, the cold-rolling will be difiicult and, therefore, not only the production will be more difiicult but also the magnetic induction will be reduced. Further, it has become evident that, in such case, in order that the magnetic characteristics may be good and satisfy the conditions of nonorientation and other conditions, the silicon content should be kept higher than, or at least equal to, the aluminum content.
  • T able 1 .-Cmposili0ns 0f ingots The ingot having such composition is soaked at 1,200 C. in a soaking furnace in a manner known, per se, and is forged or is merely divided into blooms.
  • Such bloom is heated at l,1501,250 C. (which heating temperature is not specifically defined) for minutes and is hot-rolled at a rolling finishing temperature of 850- 900 C. to be about 2.5 mm. thick according to the object product.
  • the hot-rolled steel sheet is pickled with a 15% H 80 solution at about 80 C. to remove any oxidized film deposited on the surface during the hotrolling. Thus the thickness of the steel sheet will be reducedby about 0.2 mm.
  • This steel sheet is cold-rolled twice.
  • the proper reduction rate by the cold-rolling, each time, is 5080% but may be diiferent depending on the thickness of the final product.
  • the steel sheet may be heated to about 200 C. and then rolled. Thus the thickness of the sheet will become about 1 to 0.2 mm.
  • the above mentioned intermediate annealing is then carried out at a temperature of 750 to 950 C. for a short time (less than about minutes) in an NH crackered gas having a dew point of about +30 C.
  • the atmosphere need not always be the above mentioned gas but may be a simple inert atmosphere.
  • nitrogen gas is likely to form aluminum nitride which is very detrimental to the magnetic property and is not recommendable. It is effective to attempt decarburization by elevating the dew point of the atmosphere.
  • the heat-treating temperature and time will have such great influence on the characteristics expected in the product that they must be selected in accordance with the required magnetic characteristics.
  • the time of the heat-treatment will have to be for a comparatively long time (about 60 minutes) but, if said temperature is as high as 900 or 950 C., the heat-treatment will have to be for a short time of less than about 3 minutes.
  • the finish annealing is carried out in an atmosphere having a low dew point (below C.) which may be either inert or reductive or in a vacuum below 10- mm. Hg. However, a nitrogen atmosphere has such a bad influence on the magnetic property that it should not be used.
  • An annealing temperature of about 1,000-1,100 C. will give favorable results.
  • An annealing temperature above 1100 C. may give orientation and is not desirable.
  • the annealing time is not specifically limited but should be comparatively long (about 5 to 40 hours).
  • the cooling rate should be such so as to give no undesirable internal strain in the steel sheet or less than about 50 C./hr.
  • the intermediate annealing may be omitted and the above mentioned cold-rolling may be done only once with a reduction rate of 50-85% Further, the object product may be obtained by carrying out the cold-rolling more than three times.
  • FIGURES 1 and 2 represent the examples of the (110') pole figures of crystals which form steel sheet, analyzing samples No. 4 in Table 3 and No. 10 in Table 4 with X-rays (using MoKot line) and the pole of the rolled plane being the north pole, R.D. being the rolling direction and TD. being the direction transverse to the rolling direction.
  • the concentration of the (110) pole is weak and is not in a fixed place. It can be substantially said that some of the (111) plane of the crystals are seen to be parallel to the rolling plane but do not take any specific direction and weak structure of the deviated [001] type. Some other examples show weak structure of the (111)[1l2] type.
  • FIGURE 3 show magnetic torque curves of sample Nos. 4(IV) and 10(X) and a commercial product (P).
  • the maximum magnetic torque is about 3x10 dynecm./cm. at most and is very low, showing the facts above mentioned.
  • Table 2 shows magnetic characteristics of a commercial cold-rolled nonoriented silicon steel sheet.
  • Table 3 the product produced by the process of the present invention shows superior nonorientation character than the commerical product and its magnetic characteristics are also favorable.
  • Table 3 and Table 4 show characteristics of examples of different contents of silicon and aluminum in the composition range of Example 1 and Example 2 in Table 1 respectively.
  • the core loss value is about 0.80 W/kg. in the direction L and about 0.90 W/kg. in the direction C and is only about 10% larger in the direction C. It is evident that nonorientation is improved much more than in the commercial product in Table 2. Further, the difference between the maximum magnetic permeability in one direction and that in the other is also less than about 30%. Thus, the magnetic anisotropy is far smaller.
  • P is a magnetic torque curve of a commercial nonoriented silicon steel sheet and IV and X are magnetic torque curves of steel sheets produced by the process of the present invention (IV represents a sample No. 4 in Table 3 and X represents a sample No. 10 in Table 4).
  • the maximum magnetic torque is 5x10 dyne-cm./cm. in the fromer but is less than 3x10 dyne-cm./cm. and evidently lower in the latter. It is thus evident that the latter is less oriented and has characteristics close to nonorientation.
  • a sample No. 7 and those following it in Table 3 show various characteristics in the case of different contents of silicon and aluminum in the composition range in Example 2 in Table 1 in which the carbon content is reduced.
  • FIGURE 4 shows the characteristics in the direction L (QL) and the characteristics in the direction C (QC) of the example of a sample No. 5 (which shall be represented as sample Q) in the example in Table 3 in the present invention as compared with the characteristics in the direction L (PL) and the characteristics in the direction C (PC) of the commercial nonoriented silicon steel sheet P. It is shown that the low magnetic induction is improved very much in the direction C though high magnetic induction at higher magnetic field is a little lowered in the direction L, but that the difference between them in the direction L and C is very small.
  • H and H denote the coersive force at max. magnetic induction 10,000 and 15,000 guasses respectively, B, and B,- the residual magnetic induction at max. Magnetic induction 10,000 and 15,000 gausses respectively, W10/50 and W15/50 the core loss in watts per kilogram at max. induction 10,000 and 15,000 guasses and at 50 c.p.s. and B B and B magnetic induction in gausses at magnetizing field 10, 25 and 50 oersted respectively.
  • Table 4Magnetic characteristics of products produced by the process of the present invention Samples, percent Values of alternating current magnetic characteristics Intermediate Finish, Maximum annealing annealing magnetic Samconditions, conditions, Residual torque, plo temperature temperature Coercive magnetic Core loss in Maximum Magnetic induction in dyne- No. Al in 0.x in 0.x force in O. induction W/kg. magnetic gausses cnr/cm.
  • Example-The composition of a vacuum-smelted 100 kg.-ingot was as follows (weight percent):
  • the above mentioned ingot was forged into a slab 7 mm. thick and 220 mm. wide.
  • the sla'b was hot-rolled to the gauge of 2.3 mm. It was cold-rolled for the first stage at reduction rate of 60%, was intermediately annealed and was further cold-rolled for the second stage at a reduction rate of 70% to be a final gauge 0.3 mm. thick.
  • Cooling rate 50 C./hr.
  • Atmosphere Argon (dew point- C.)
  • a process for producing a non-oriented silicon steel sheet in which the crystal grains are in a state of random alignment and, when magnetized, has equal degree of magnetization in all directions which comprises ('1) hotrolling an ingot to produce a steel sheet, said ingot consisting essentially of 1.5 to 3.5 wt. percent Si, 1.09 to 1.34 wt. percent Al, and Fe, the sum of Si and Al being from 2.5 to 4.5 wt. percent, and the amount of Si in said ingot being greater than the amount of Al, (2) coldrolling the steel sheet to effect reduction of 50 to in thickness, (3) intermediately annealing the cold-rolled sheet at a temperature of from 750 to 950 C.

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US259190A 1962-02-23 1963-02-18 Process for producing nonoriented silicon steel sheets Expired - Lifetime US3203839A (en)

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Cited By (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3868280A (en) * 1967-12-12 1975-02-25 Takaaki Yamamoto Method of forming electric insulating films oriented silicon steel
US3935038A (en) * 1971-10-28 1976-01-27 Nippon Steel Corporation Method for manufacturing non-oriented electrical steel sheet and strip having no ridging
US3948691A (en) * 1970-09-26 1976-04-06 Nippon Steel Corporation Method for manufacturing cold rolled, non-directional electrical steel sheets and strips having a high magnetic flux density
US4046602A (en) * 1976-04-15 1977-09-06 United States Steel Corporation Process for producing nonoriented silicon sheet steel having excellent magnetic properties in the rolling direction
US4066479A (en) * 1972-07-08 1978-01-03 Nippon Steel Corporation Process for producing non-directional electric steel sheets free from ridging
DE2747660A1 (de) * 1976-11-26 1978-06-01 Kawasaki Steel Co Verfahren zum herstellen von nichtorientierten siliciumstaehlen mit hoher magnetischer induktion und niedrigen kernverlusten
EP0084569A4 (en) * 1981-08-05 1983-08-01 Nippon Steel Corp METHOD FOR PRODUCING AN ISOTROPICAL ELECTROMAGNETIC STEEL PLATE WITH EXCELLENT MAGNETIC CHARACTERISTICS.
EP0418424A1 (en) * 1988-07-12 1991-03-27 Nippon Steel Corporation High strength non-oriented electrical steel sheet and method of manufacturing same
US5482107A (en) * 1994-02-04 1996-01-09 Inland Steel Company Continuously cast electrical steel strip
US20130125601A1 (en) * 2010-08-04 2013-05-23 Nippon Steel & Sumitomo Metal Corporation Manufacturing method of non-oriented electrical steel sheet
CN115491468A (zh) * 2022-10-20 2022-12-20 重庆钢铁股份有限公司 一种无取向硅钢rh精炼过程控制氮含量的方法

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2307391A (en) * 1938-10-14 1943-01-05 American Rolling Mill Co Art of producing magnetic material
US2378321A (en) * 1943-01-06 1945-06-12 Matti H Pakkala Electrical silicon steel
DE1009214B (de) * 1954-03-27 1957-05-29 Ver Deutsche Metallwerke Ag Verfahren zur Erzeugung ausgepraegter Wuerfeltextur in magnetisierbaren Baendern undBlechen aus silizium- und/oder aluminiumhaltigen Eisenlegierungen
US2875114A (en) * 1957-04-12 1959-02-24 Westinghouse Electric Corp Iron-aluminum materials for magnetic applications
US2965526A (en) * 1958-10-03 1960-12-20 Westinghouse Electric Corp Method of heat treating silicon steel
GB870220A (en) * 1959-05-27 1961-06-14 Armco Int Corp Non oriented silicon-iron sheet stock and process of making it

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2287467A (en) * 1940-01-03 1942-06-23 American Rolling Mill Co Process of producing silicon steel

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2307391A (en) * 1938-10-14 1943-01-05 American Rolling Mill Co Art of producing magnetic material
US2378321A (en) * 1943-01-06 1945-06-12 Matti H Pakkala Electrical silicon steel
DE1009214B (de) * 1954-03-27 1957-05-29 Ver Deutsche Metallwerke Ag Verfahren zur Erzeugung ausgepraegter Wuerfeltextur in magnetisierbaren Baendern undBlechen aus silizium- und/oder aluminiumhaltigen Eisenlegierungen
US2875114A (en) * 1957-04-12 1959-02-24 Westinghouse Electric Corp Iron-aluminum materials for magnetic applications
US2965526A (en) * 1958-10-03 1960-12-20 Westinghouse Electric Corp Method of heat treating silicon steel
GB870220A (en) * 1959-05-27 1961-06-14 Armco Int Corp Non oriented silicon-iron sheet stock and process of making it

Cited By (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3868280A (en) * 1967-12-12 1975-02-25 Takaaki Yamamoto Method of forming electric insulating films oriented silicon steel
US3948691A (en) * 1970-09-26 1976-04-06 Nippon Steel Corporation Method for manufacturing cold rolled, non-directional electrical steel sheets and strips having a high magnetic flux density
US3935038A (en) * 1971-10-28 1976-01-27 Nippon Steel Corporation Method for manufacturing non-oriented electrical steel sheet and strip having no ridging
US4066479A (en) * 1972-07-08 1978-01-03 Nippon Steel Corporation Process for producing non-directional electric steel sheets free from ridging
US4046602A (en) * 1976-04-15 1977-09-06 United States Steel Corporation Process for producing nonoriented silicon sheet steel having excellent magnetic properties in the rolling direction
DE2747660A1 (de) * 1976-11-26 1978-06-01 Kawasaki Steel Co Verfahren zum herstellen von nichtorientierten siliciumstaehlen mit hoher magnetischer induktion und niedrigen kernverlusten
EP0084569A4 (en) * 1981-08-05 1983-08-01 Nippon Steel Corp METHOD FOR PRODUCING AN ISOTROPICAL ELECTROMAGNETIC STEEL PLATE WITH EXCELLENT MAGNETIC CHARACTERISTICS.
US4560423A (en) * 1981-08-05 1985-12-24 Nippon Steel Corporation Process for producing a non-oriented electromagnetic steel sheet having excellent magnetic properties
EP0418424A1 (en) * 1988-07-12 1991-03-27 Nippon Steel Corporation High strength non-oriented electrical steel sheet and method of manufacturing same
US5482107A (en) * 1994-02-04 1996-01-09 Inland Steel Company Continuously cast electrical steel strip
US20130125601A1 (en) * 2010-08-04 2013-05-23 Nippon Steel & Sumitomo Metal Corporation Manufacturing method of non-oriented electrical steel sheet
EP2602335A4 (en) * 2010-08-04 2016-11-30 Nippon Steel & Sumitomo Metal Corp METHOD FOR PRODUCING A NON-ORIENTED ELECTROMAGNETIC STEEL PLATE
US9579701B2 (en) * 2010-08-04 2017-02-28 Nippon Steel & Sumitomo Metal Corporation Manufacturing method of non-oriented electrical steel sheet
CN115491468A (zh) * 2022-10-20 2022-12-20 重庆钢铁股份有限公司 一种无取向硅钢rh精炼过程控制氮含量的方法

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GB1037943A (en) 1966-08-03
BE628759A (en, 2012)

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