US3163564A - Method for producing silicon steel strips having cube-on-face orientation - Google Patents

Method for producing silicon steel strips having cube-on-face orientation Download PDF

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US3163564A
US3163564A US208277A US20827762A US3163564A US 3163564 A US3163564 A US 3163564A US 208277 A US208277 A US 208277A US 20827762 A US20827762 A US 20827762A US 3163564 A US3163564 A US 3163564A
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silicon steel
rolling
steel
rolled
cold rolling
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Taguchi Satoru
Sakakura Akira
Yasunari Takashi
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Yawata Iron and Steel Co Ltd
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B3/02—Rolling special iron alloys, e.g. stainless steel
    • 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
    • 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

  • the present invention relates to a method for producing a so-called double oriented magnetic silicon steel strip which has easy magnetization axes [001] in two rightangled directions in the rolling plane of the steel strip and in which a (001) plane appears in the rolling plane.
  • silicon steel sheets (and this term is used hereinafter to include steel strips) have been used as a soft magnetic material, for iron cores of transformer, electric generators and the like.
  • Many attempts have been made 3,1635% Patented Eec. 29, 1964 2 process for producing double oriented silicon steel having a desired thickness greater than that of the known doubleoriented sheets, which process can be carried out successfully in a conventional industrial atmosphere.
  • An additional object of this invention is to provide a process for producing double oriented silicon steel having excellent magnetic characteristics, particularly in a comparatively high magnetic field, along two directions, a finally rolled direction and a transverse direction perpendicular thereto.
  • FIG. 1 shows the crystal orientations and easy magnetization directions of crystal grains constituting single oriented silicon steel ([1) and double oriented silicon steel (b) and Wassermann type oriented silicon steel (0).
  • FIG. 2 shows views of iron cores for transformers punched from single oriented steel (a) and from double oriented steel (b).
  • FIG. 3 shows views of iron cores for rotors punched from single oriented steel (a) and from double oriented to control the crystal orientations of such silicon steel 7 sheets destined for the aforesaid uses in order to obtain sheets of oriented silicon steel having a cubic crystal structure, in which there exist 3 mutually-perpendicular directions of easy magnetization (directions of cube axes l00 and, which results in the advantage that, when a magnetic field is applied parallel to any of these 10G directions, a minimum amount of energy is required to magnetize the silicon steel.
  • the first type of oriented silicon steel that satisfied such requirement was single-oriented silicon steel.
  • Single-oriented steel consists of cubes standing on edge, hence it is often referred to as having cube-on-edge orientation which is of the (110) [001] type, as illustrated in FIG. 1(a) of the accompanying drawings.
  • the arrow indicates that easy magnetization is possible only along a single direction which is usually the direction of rolling. In fact, lines representing the other cube axis would extend out from the top and the bottom of the sheet at angles of 45. Therefore, as is well known to those skilled in the art, the magnetic induction and other magnetic properties are outstanding in the rollin direction, i.e., the [100] direction. However, in any other direction, for example, the direction transverse to the rolling direction of the sheet, the magnetic properties are greatly inferior because of the magnetization is not parallel to the edge of the cubic crystal structure.
  • An object of this invention is to provide a process for producing double oriented silicon steel consisting substantially of a cube-on-face crystal, i.e., a (100) [001] type crystal and having consequently excellent magnetic characteristics along the two transverse directions, from a hotrolled steel plate prepared by subjecting to a conventional hot rolling a silicon steel body and which is produced by a conventional melting (steelmaking) method or casting method.
  • a further object of this invention is to provide a process for producing double oriented silicon steel by a heat-treat ment in a usual industrial atmosphere.
  • a still further object of this invention is to provide a steel (b).
  • FIG. 4 shows the reiation between the Al contents after hot rolling on the one hand, and the magnetic characteristics after final annealing (the magnetic induction B and the iron loss W15/50 in the two outstanding directions, i.e., the final rolling direction and the direction perpendicular to it), on the other hand, as a result of a process mode A described hereinafter.
  • FIG. 5 shows the relation between the Al content after hot rolling and the magnetic characteristics after final annealing (the magnetic induction B and the iron loss W15/50 in 2 directions, i.e., the final rolling direction and the direction perpendicular to it), as a result of a process mode B described hereinafter; six different hot rolled sili con steel materials (plate thickness: 2.0 mm.) having chemical analyses as indicated in Table l are cold rolled with a reduction of about 30% in the same direction as that of hot rolling, then cold rolled with a reduction of about 30% in a direction approximately at a right angle thereto, then annealed for a period of 5 hours at the maximum holding temperature at 1100 C., then again cold rolled with a reduction of in the same direction as that of the second cold rolling, and thereafter finally an nealed for a period of 15 hours at the temperature of 1150 C.
  • FIG. 6 is a graph with two curves showing the relationship between short time anneal temperature andcore loss after final anneal of the magnetic material produced according to mode A of the process according to our invention.
  • FIG. 7 is a graph showing the effects of the temperature of an intermediate box anneal over the magnetic properties of the magnetic material produced by mode A of the process according to this invention, and will be described in detail hereinafter.
  • FIG. 8 is a graph showing the relationship between the,
  • FIGURES 48 a solid' line plotting black circle Q shows an iron loss in the final cold-rolling direction
  • the easy magnetization direction does not coincide with the direction of the magnetic field in the art of the teeth 7, which results in a reduced magnetic capacity of the rotor.
  • the iron core punched from the double oriented silicon steel sheet has good magnetizability at full capacity, and therefore the weight of the iron core may be light.
  • double-oriented silicon steel sheet offers considerable industrial advantages as compared With the conventional single-oriented silicon steel sheet, but special metallurgical processes are needed in order to produce the desired double orientation because the cube-on-face, i.e., the (100)[001] orientation is not the usual configuration found in silicon steel.
  • double-oriented silicon steel is produced by hot rolling a silicon steel ingot obtained by vacuum melting, subjecting the hot rolled steel to several stages of cold rolling and repeated intermediate heat-treatments and, after final gauge has been attained, annealing finally in an oxygen-free inert atmosphere of high purity.
  • this method requires many stages of cold rollings and intermediate heat-treatments, and it is also necessary that the atmosphere should be substantially free from oxygen, moisture and other oxidizing agents, so that SiO (silica) will not be produced on the surface of the steel sheet during the annealing and, furthermore, in case S is formed, it can be reduced to Si during the annealing treatment. It is, however, extremely difficult to maintain such annealing condition, at least on an industrial scale.
  • double-oriented silicon steel is very difficult to realize particularly on an industrial scale.
  • a silicon steel element containing a small amount of Al is made by a conventional steel making method, and the steel is subjected to a conventional hot rolling to obtain a hotrolled sheet, which is then treated with a novel mode of cold rollings including a cross rolling and heat-treatments in a conventional industrial atmosphere.
  • any conventional steel melting method can be used, any specific measures are completely unnecessary in the necessary hot-rolling work, and the heat-treatment in the process according to this invention can be carried out under conventional conditions without the necessity of providing any specifically prepared atmosphere.
  • the process of this invention represents a marked improvement over the known processes for producing double-oriented silicon steel sheets in which only articles having very limited thickness have been produced.
  • the objects of the present invention can be achieved by hot rolling a silicon steel element containing small but critical amounts of Si and Al, and treating it by a process including a cross cold rolling and in this case, the process of this invention is based on a new phenomenon, namely that the crystal grain having a (100)[001] orientation grows only when the hot rolled sheet contains a critical amount of Al and is cross-rolled and heat-treated.
  • the silicon steel material (steel ingot) used as starting material in this invention is preferably produced by a melting method and must contain above 2, and, to be really satisfactory, about 2.5% and up to 4% of Si and above 0.010 and indeed from 0.014% up to 0.040% of A1 when using process mode A, or above 0.010 to 0.050% and better, from 0.015 to 0.041% of Al, when using process mode B (all percentages are by weight).
  • Other allowable impurities may be contained in the starting material just as in conventional single oriented silicon steel and no unconventional restrictions need be imposed as to these impurities, except the aforesaid limits for Al and Si.
  • the Si and Al contents of the steel, after hot-rolling should be from 2.7 to 3.8% of Si and from 0.016 to 0.030% of Al.
  • carbon is not a limiting element in the composition of the material of the present invention. However, in the ordinary industrially obtained ingot, it is diflicult to make the carbon content less than 0.02% On the other hand, if the carbon content is more than 0.06%, it will be very difficult in decarburization to eliminate the detrimental eiiect of the residual carbon on the magnetic characteristics of the product. Therefore, a carbon content from 0.02 to 0.06% shall be adopted.
  • the ingot becomes brittle when it is rolled, in particular, cold-rolled as will be stated later, which causes undesirable phenomena such as rupture and if the Si content is less than 2%, a ferriteaustenite transformation occurs during the annealing pros ess which will be explained later, whereby the crystal orientation, the production of which is the object of this invention, disappears. Also, in general, if the content "of Si is low, the electric resistance of the steel sheet is lowered, which results in increasing eddy-current loss and iron loss. Therefore, in this invention, the content of Si is limited to higher than 2.5 and up to 4%.
  • an aluminum-containing silicon steel strip is produced by forming an Al-containing silicon steel having a suitable, composition (Si 15%, Al 0.0l- 1.00% and C 0.02%), rolling the steel into a steel strip and then annealing the. steel strip continuously at a tem- .perature of 1500 to 1750" F. in a decarburization atmosphere to reduce the content of C to lower than 0.02%.
  • silicon steel sheets has been disclosed as being of any advantage, and where, aluminum has been present in singl -oriented steel, it was merely incidently, but since then, its presence was never provided for intentionally. in fact, the presence of Al in magnetizable steel has usually been avoided as far as possible, since Al is apt to form oxides such as A1 0 and the like in steel, which are harmful to the magnetic characteristics of the steel; and therefore, except for an unavoidable presence of less than 0.01% Al, stemming from the starting materials from which the steel is made, any content of Al has been, in general, eliminated. In double-oriented silicon steel sheet, no such effects as were adscribed to the addition of Al in the case of non-oriented silicon steel sheets, was generally expected, and, therefore, efforts were usually made to maintain the Al content, if any, as low as possible.
  • steel 0 l which is to be given (i00)[00l] cube texture, not by cross rolling treatment (90), but by an inclined-angle rolling to 70), must have, in the case of silicon iron alloys, a content of between 0.5 and 2.5% of Si, in the case of aluminum iron alloys, a content between 0.5 and 2.0% A1, and, in the case of silicon-aluminum iron alloys, the sum of the quantities of silicon and aluminum together should be between 0.5 and 2.5%.
  • the silicon steel ingot used in our process has an Al content above 0.010 and up to 0.040%, when used in process mode A, or up to 0.050% if used in mode B.
  • the presence of aluminum within the stated critical limits is desirable in the process according to this invention the advantages attained by the addition of Al more than make up for the disadvantages. stated above, subject to certain conditions which will be explained I further hereinafter.
  • Aluminum can be present in silicon steel in two forms, namely as acid-insoluble Al and acid-soluble Al.
  • the former consists mainly of A1 0 produced due to the strong aflini-ty of Al to oxygen and since it is harmful to the magnetic properties of steel, its formation must be avoided as much as possible, in this invention also.
  • A1 0 produced due to the strong aflini-ty of Al to oxygen and since it is harmful to the magnetic properties of steel, its formation must be avoided as much as possible, in this invention also.
  • due to the progress nrade in steel-making and melting techniques it has become possible.
  • Al present in a solid solution in silicon steel and Al which is present as a nitride such as AlN, of which the ratio depends upon the contents of total Al in the silicon steel and thermal conditions, such as melting conditions, hot-rolling conditions and annealing conditions, the reaction equation being as follows:
  • N is present in the steel, and if Al is also present in the steel, Al is deposited as AlN.
  • specific melting apparatus such as a vacuum melting furnace and the like, are used, N is absent from the steel, and in this case hardly any AlN is formed even if a considerable amount of Al is contained in the steel.
  • specific melting apparatus is used in the production of steel ingot, but the latter is produced by the common industrial techniques, and is hot-rolled, the acid-soluble A1 present in the hot rolled product consists partly of AlN.
  • the AlN content should amount to at least 0.0029% and preferably at least 0.0043 to 0.0045 and may be as high as 0.0073% and higher, calculated on the weight of the hot-rolled silicon steel.
  • Wiener teaches in the United States i atent 2,965,526 a process for producing a single-oriented silicon steel strip by cold-rolling and heat-treating a hot-rolled silicon steel containing in a range of 0.001 to 0.05% at least one substance of a group consisting of metal sulfides, oxides and nitrides.
  • the object product of said US. Patent 2,965,526 is a singleoriented silicon steel sheet consisting of crystal grains of such (110) [001] orientation as is shown in (a) in FIG- URE 1 and shows favorable magnetic characteristics in the rolling direction only
  • that of the present invention is a double-oriented silicon steel sheet consisting of crystal grains of such (100) [001] orientation as is shown in (b) in FIGURE 1 and shows favorable magnetic characteristics in the two directions of the rolling direction and the direction at right angles thereto. How industrially significant this is, is as already shown with examples in FIGURES 2 and 3.
  • the starting material of said US Patent 2,965,526 is a hot-rolled silicon steel containing about 2.2 to 5.25% Si, 0.001 to 0.05% of at least one substance of a group consisting of metal oxides, sulphides and nitrides and maximum of 0.02% C, the rest being iron
  • that of the present invention is a hot-rolled silicon steel containing above 2.5 and up to 4.0% Si, 0.010 to 0.050% Al, the larger part of which must exist as acid-soluble aluminum consisting to a substantial portion of AlN, apart from the unavoidably present small amount of acid-insoluble aluminum, and carbon in the range of 0.02 to 0.06% and is evidently a material quite different from the above.
  • the treating process of the US. Patent 2,965,526 is the two-step cold-rolling method developed by N. P. Goss, whereas that of the present invention is a two-step or three-step cold-rolling method including cross-rolling and is quite different from the above.
  • PROCESS MODE A Hot-rolled sheets, preferably in the form of strips of 1.6 mm. in thickness obtained by subjecting to a conventional hot rolling ingots containing the above-defined critical contents of Si and Al, that are produced by a conventional electric furnace steel-making process, permitting formation of aluminum nitride as described above, are used as starting material.
  • FIG. 4 gives the curves showing the relationship between the aluminum content prior to final anneal, core loss after final anneal, and magnetic induction radius when various specimens of the aforesaid start-.
  • ing material designated as A, B, C, D and E with the composition shown in Table 1 below or similar compositions including varying contents of aluminum and silicon within the above-defined limits are subjected to hot rolling to a thickness of 1.6 mm., pickling to remove scale resulting therefrom, an initial cold rolling in one direction with a reduction of 60%, then a final cold rolling in a direction approximately at right angle thereto with a reduction of then a short time anneal for about four minutes at the temperature of 800 C., and lastly a final anneal for fifteen hours at the temperature of 1150 C.
  • Unit watts per kilogram; Wis/an Watts 15 kilogausses at a frequency of 50 c.p.s. Unit: watts per kilogram.
  • upper analysis refers to that of hot rolled silicon steel stock while the lower to that of prior to final anneal.
  • Each specimen consists of the above composition and the balance, iron and incidental impurities, de-
  • the magnetic induction B is less than 17,000 gausses in each product, in the case of the starting materials B, C and D, the magnetic induction B in each product is about 18,000 gausses in both outstanding directions, namely the direction of final rolling and the direction perpendicular thereto, and the products thus show the outstanding properties of double oriented silicon steel.
  • B is a value of a magnetic induction in a magnetic field of 10 oerstcds
  • the value of B in an oriented silicon steel sheet is usually higher than 17,000 gausses. Since, moreover, in single oriented silicon steel, an easy magnetization axis does not appear in the direction perpendicular to the rolling direction as shown in FIG. 1(a), the value of B in the said transverse direction is far lower.
  • Al content after hot rolling must be restricted to the range between 0.010 and 0.040% in the case of the treatment by the aforesaid process mode A.
  • the magnetic induction B of the final product is higher than 18,000 gausses in the direction of the final rolling, as Well as in the direction perpendicular thereto, which values are even better than the best values of magnetic induction B of a conventional single. oriented silicon steel in the rolling direction.
  • the thickness or gauge of the hot rolled steel is an important requirement for the production of a doubly oriented silicon steel sheet or strip.
  • the thickness or gauge of the starting material should be preferably 2.5 to 10 times of the desired final thickness
  • the final gauge of the product will be too thick after the predetermined cold rollingreduct-ion, which results in an increase of eddy loss.
  • the gauge of the hot rolled silicon steel is preferred to be from 1 mm. to 4 mm. Particularly, about 1.6 mm. is most preferred, which is about three to five. times the final gauge, taking both the final and the necessary cold rolling into account.
  • the hot rolled silicon steel with a predetermined gauge is subjected to a pickling step, and then to cold rolling.
  • the reduction in thickness by cold rolling is of the greatest important in view of the combination of two cold rolling directions.
  • the overall reduction is preferred tobe within the range of 60% to 90%.
  • the embodiment which comprises'cold rolling the steel in one direction first with a reduction of 40% to again cold rolling it in another direction at light angle thereto, with a reduction of 30% to 70%, and finally annealing the thus cold rolled steel, has resulted in the desired cube oriented silicon steel sheet or strip we have in view.
  • the hot rolled silicon steel containing more than 2.5 and up to 4% of silicon and between 0.010% and 0.040% aluminum is cold rolled in one direction, then sheared off to a sheet of length, and
  • another silicon steel strip is produced by welding sheared sheets end to end together in such manner that the longitudinal direction of the strip makes a direction at right angle, or deviating by less than 15 therefrom on either side, to the direction of initial cold rolling, whereupon the strip is again cold rolled continuously.
  • a preferred commercial production carrying out the process of the invention with the hot rolled silicon steel strip as starting material comprises the following steps:
  • a hot rolled silicon steel strip having a predetermined thickness is pickled to remove scale resulting from hot rolling with the above-defined definite reduction to produce cold rolled silicon strip.
  • the cold rolled silicon strip is sheared off to a number of sheets of desired length.
  • a new silicon steel strip is produced by Welding the sheared length of sheets end to end together in such a manner that the longitudinal direction of the new strip forms a direction at right angle or deviating less than 15 therefrom, to the direction initial cold rolling, then the thus produced strip is again cold rolled continuously with a predetermined reduction.
  • a sheared length of sheet is again cold rolled sheet by sheet in a direction at right angle or deviating less than :15" from the direction of initial cold rolling, with a predetermined reduction, then a number of twice coldrolled sheets are welded end to end together to produce a new cold rolled strip.
  • the above-described subsequent treatment will be given to the cold-rolled strip thus obtained.
  • the temperature of the short time anneal to be imparted to the silicon steel sheet or strip which has been cold rolled to the final gauge has an influential effect on the primary recrystallization structure resulting from the anneal, and the secondary recrystallization of the seed crystal grain having a (100) [001] type orientation will depend upon the primary recrystallization structure.
  • FIGURE "6 shows the influence of the annealing temperature on the iron core loss after the final anneal of a product which has been obtained by the process of the invention wherein a hot-rolled silicon steel containing 0.03% carbon, 3.02% silicon, 0.018% aluminum in all, and 0.013% acid-soluble aluminum with a gauge of 1.75 mm. was first cold-rolled in one direction with a reduction of 60%, and then again cold rolled to final gauge in another direction approximately at right angles to the direction of the first cold rolling, with a reduction of 50% and then annealed for four minutes at a temperature ranging between 700 and 1,200 C.
  • the temperature at which a short time anneal should be carried out is preferably a temperature between 750 and 1,000 C., in order to obtain a product having good magnetic properties, while at a higher temperature than the above upper limit, even for a short period of time only, the grain growth of primary recrystallization structure may become so considerable that selective secondary recrystallization in the final anneal will be prevented, although the advantage of the present invention may not be entirely lost. Further, it is to be understood that the advantage of the invention will not be lost as long as the temperature of the short time anneal is Within the range between less than 750 C. and higher than the recrystallization temperature. However, the temperature ranging between 750 and 1,000 C.
  • the time required for anneal at the above temperature range takes usually about one minute for the cold rolled structure of the steel to be converted into the recrystallized structure. Since the silicon steel stock contains approximately 0.04% carbon, decarburization is required at the same time to an extent at which crystal growth may not be interfered with by the presence of carbon in the final anneal. We have discovered that a maximum of up to four minutes is required for continuous anneal in view of the thickness of the material and other requirements. It is to be understood, however, that the period of time for the short time anneal should not limit the present invention.
  • This anneal is carried out usually in a neutral or reducing atmosphere, but is not necessarily limited thereto. Further, it is considered that the temperature ranging between 750 and 1,000 C. specified above is beneficial to commercial production because a decarburizing reaction is most actively going on at the above temperature in the presence of a small amount of moisture.
  • a silicon steel sheet or strip which has been annealed for a short period of time may be subjected to pickling depending on its surface conditions.
  • an anneal at a temperature above 900 C. in the reducing atmosphere for a period of time more than at least five hours is required in order to produce a cube-oriented silicon steel strip having low core loss and high magnetic induction values.
  • the complete secondary recrystallization may not be developed by an anneal at either lower temperature or shorter time than that defined above.
  • a practical temperature available for the commercial production of the invention is preferred to be between 900 and 1,300 C., since an anneal at either a temperature above l,300 C. or for a time longer than forty hours is not so effective. Annealing at a temperature outside the range described above, however, will not lose the fundamental advantage of our invention.
  • PROCESS MODE B In the following Table 2 there are compiled data obtained by applying above-mentioned mode B of carrying out the process of the invention to hot-rolled sheets or strips of 2 mm. thickness, which are produced by subjecting to a conventional hot-rolling process the ingots produced, in turn, by a conventional open-hearth steel-making process; the hot-rolled ingots are cold-rolled to a direction which is identical with the hot-rolling direction, at a reduction rate of about 30%, then cold-rolled in the direction perpendicular to the first cold-rolling direction at a reduction rate of approximately 30%, thereafter annealed for 5 hours at a maximum temperature maintained at 1100 C., cold-rolled again at a reduction rate of in a direction coincident with the last-preceding rolling direction in the aforesaid cross rolling, and then finally annealed for 15 hours at 1150 C.
  • FIG. 5 there are shown the relations between the Al contents in the hot-rolled sheets and the iron loss values and magnetic induction values of the final-annealed sheets.
  • W means an iron core loss at 15,000 gausses measured per frequency of 50, and its unit is wJkg.
  • B means a magnetic induction at 10 oersteds, and its unit is gauss.
  • the upper one is the value measured along the final rolling diree tion and the lower is that along the direction at a right angle thereto.
  • the magnetic induction B is less than 17,000 gausses
  • the magnetic induction B of each product is about 18,000 gausses in the two outstanding directions, i.e., the direction of final rolling and the direction perpendicular thereto, which shows that the products are indeed, improved double-oriented silicon steels.
  • they content of Al must be limited to the range between 0.010 and 0.050% in the case of the treatment by process mode B.
  • the magnetic induction B of the final product is higher than 17,000 gausses, yet, as the content of Al is more. than 0.050%, the amount of acid-insoluble Al increases, as already stated, which influences the iron loss and other magnetic properties in an undesirable manner. Therefore, the Al content is in a range of 0.020 to 0.035%, the magnetic induction B of the final product is higher than 18,000 gausses in the direction of final rolling and the direction perpendicular thereto, which is an excellent increase above the value of magnetic induction B which a conventional single-oriented silicon steel shows in the rolling. direction.
  • the gauge or thickness of hot rolled steel is an important factor in order to manufacture a double-oriented silicon steel sheet or strip we have in view.
  • the gauge of the hot-rolled silicon steel starting material should be preferably 5 to 30 times as thick as the final desired gauge.
  • This gauge is closely related tothe total reduction of cold rolling described hereinbelow, an excessiveiy thin gauge of the hot-rolled material leading to the same diificulties as described under Process mode A, and, conversely, an extremely thick gauge thereof resulting in a thick gauge of the final product obtained by the reduction required for cold rolling, will also result in an undesirable increase of eddy current loss due to, the thick gauge.
  • the gauge of the starting material is usually preferred to, be from 0.7 to 13 mm., and particu larly, about 3 mm. gauge of the starting material is desired taking both the final gauge and the necessary cold rolling reduction into account.
  • the hot rolled silicon steel is pickled in the usual mannor in order to remove scale resulting from hot rolling.
  • the reduction in thickness by cold rolling carried out after pickling in two stages in directions at right angle to each other is of utmost importance depending on the combination of rolling directions.
  • an overall reduction of 44-80% is preferred: the primary c old rolling reduction in one direction should be 3060*%, and the seoondary cold rolling reduction in the other direction at a right angle thereto. -50%.
  • the most desirable gauge, 3 mm., of the above hot rolled steel is adopted, the combination of a cold rolling reduction of 40% in one direction and a second reduction of 40 in the other direction at right angle thereto is preferable.
  • Two types of the final product are obtained by the process of this invention: one is obtained by the process which involves a direction of primary cold rolling coinciding with that of the preceding hot rolling, and the other is obtained by the process which involves a direction of primary cold rolling being at a certain angle to that of hot rolling.
  • a hot rolled steel strip as silicon steel starting material.
  • the silicon steel strip having a predetermined gauge is first pickled toremove hot rolling scale, then cold rolled with the necessary reduction to obtain a cold rolled steel strip, which is cutinto a number of sheets of a predetermined length, two or more sheets are welded together end to end in order to make a new steel strip the longitudinal direction of which is in a direction at an angle of approximately 90 (with a deviation within the range of :15) to the direction of the primary cold rolling, whereupon the welded strip is subjected to the secondary cold rolling, further followed by the subsequent treatment described further below.
  • a first cold rolling is applied to the steel in the form of a strip, and the subsequent processing steps are applied to it in the form of a sheet;
  • a first cold rolling is applied to a steel strip which is then cut into a number of sheets of a predetermined length, then a second cold rolling is applied to the steel in the form of a sheet in a direction at an angle of 90 (with a deviationwithin the range of :15 to the direc tion of the first cold rolling, then two or more of such twice cold rolled sheets are welded together end to end to form a new strip whose longitudinal direction is equal to either one of the two directions of cold rolling, and thereafter the subsequent processing steps described further below are applied to this new strip;
  • a first cold rolling is applied to a steel strip, which is then cut into a number of sheets of predetermined length, then a second cold rolling and an intermediate box anneal. (described hereinafter) are applied to the steel in the form of a sheet under the required conditions, then two. or more sheets are welded together end to end to form a new strip whose longitudinal direction is equal to either of the two directions of cold rolling, and thereafter the subsequent processing steps are applied to the new strip; and
  • a first cold rolling is applied to the steel in the form of a strip, which is then cut into a number of sheets of predetermined length, then a second cold rolling, an intermediate box anneal and a final cold rolling, described further below, are applied to the steel in the form of a sheet under the required conditions, then two or more 15 sheets are welded end to end together to form a new strip whose longitudinal direction is equal to either of the two directions of cold rolling, and thereafter the subsequent processing steps are applied to this new strip.
  • a first cold rolling is applied to a steel sheet in one direction, then this steel sheet is cut into sheets of a predetermined length, then two or more sheets of this length are welded together end to end to form a new steel strip whose longitudinal direction is at an angle of 90 (with a deviation within the range of :15") to the direction of the first cold rolling, and thereafter the second cold rolling and subsequent processing steps are applied to this new steel strip;
  • An intermediate box anneal imparted to the silicon steel sheet or strip reduced in thickness to an intermediate gauge by two cold rolling steps in two mutually crossing directions has an important influence on the recrystallized structure to be produced by subsequent annealing.
  • the maximum holding temperature range should be preferably from 850 to 1200 C. during the intermediate box anneal.
  • FIG. 7 is a graph showing the effect of the temperature of the intermediate box anneal on the magnetic properties of a magnetic material produced by the process of this invention, wherein a hot rolled silicon steel containing 3.02% Si, and 0.026% Al was subjected to a first cold rolling with a reduction of about 30% in the same direction as that of hot rolling, then again to a second cold rolling with a reduction of about 30% in a direction approximately at right angles thereto, then to anneal for a period of 5 hours at a temperature if 800 to 1200 C. as the maximum holding temperature, then again to a final cold rolling with a reduction of 70% in the same direction as that of the second cold rolling, and lastly to a final anneal for a period of 15 hours at a temperature of 1150 C.
  • FIG. 7 shows that the higher the maximum holding temperature, the more effective the anneal, but FIG. 7 also shows that this effect changes very little at temperatures above 1000 C. However, the magnetic properties will decrease at temperatures below 850 C. Accordingly, from a commercial point of view, we prefer the maximum holding temperature range for the intermediate box anneal to be 850 to 1200 C. An atmosphere of either neutral or reducing gas medium is usually employed, but we do not limit the process of our invention thereto. Sufiicient nitrogen should, of course, be present in this medium.
  • the reduction in thickness of the final cold rolling procedure is an important factor for attaining the doubleoriented silicon steel we have in view, and the direction at which this final cold rolling is carried out should be a direction approximately equal to either of two crosswise directions of the preceding two cold rolling stages. From a commercial point of view, the selection of the same direction as that of the second cold rolling is most practical.
  • FIG. 8 is a graph showing the relationship between the magnetic induction and the cold rolling reduction of a magnetic material manufactured by the process of the invention wherein a hot rolled silicon steel material of 3.0 mm. thickness and containing 3.05% Si and 0.034% Al was subjected to a first cold rolling, with a reduction of 40%, in the same direction as that of hot rolling, then again to a second cold rolling in a direction approximately at right angle thereto with a reduction of 40%, then to an anneal for a period of 5 hours at a temperature of 1100 C., the maximum holding temperature, then to a final cold rolling in the same direction as that of the second cold rolling with a reduction ranging from 19 to 84%, and lastly to a final anneal for a period of 15 hours at a temperature of 1150 C.
  • the foregoing results show that the reduction in thickness by the third or final cold rolling procedure is preferably within the range of 50 to 84%, and more particularly, a reduction of approximately 70% is most desirable.
  • the silicon steel sheet reduced in thickness to the final gauge by the foregoing processing steps is subjected to a final anneal.
  • a final anneal With a view to attaining a double-oriented silicon steel strip having a low iron core loss, it is required to anneal the steel for a period of more than 5 hours at the maximum holding temperature of above 1000 C. in a neutral or reducing atmosphere.
  • a complete growth of crystal cannot be developed.
  • an anneal either at an elevated temperature of above 1300 C. or for an extended period of more than 40 hours will not develop the desired effect in a satisfactory manner despite of the elevated temperature or the extended anneal time.
  • the fundamental effect of the present invention will not be lost completely by an anneal deviating from the range of either temperature or period of time mentioned above.
  • the desired double oriented silicon steel sheet or strip can be manufactured in accordance with the complete process of this invention described hereinabove. It is to be understood that the carbon content of the product after the final anneal should be the least possible, and more particularly, a content of less than 0.005% C is most desirable.
  • Silicon steel used as starting material in carrying out the process of invention may usually contain 0.020.06% C. Therefore, a decarburizing anneal should be effected in order to reduce the carbon content, provided that it has not been reduced as desired by the intermediate and final box anneals.
  • various known processes of anneal may be applied in practicing our invention, and We do not intend to limit our to a particular one.
  • decarburization can be achieved by a process which comprises subjecting a hot rolled material with scale thereon to a box anneal, and also by a process which comprises subjecting a steel material either after two cross cold rolling steps or after the final cold rolling step to a short time anneal in an atmosphere containing either neutral or reducing gas and a small amount of moisture.
  • the carbon content of the final product can be easily reduced to less than 0.0 05 by means of either of the above two processes of decarburization or by both combined.
  • the number of steps in the process mode B is, as stated above, more than that of l 7 the process mode A and consequently that the process mode B is not as economical as the process mode A.
  • the permissible range of Al content for imparting the magnetic properties of double oriented silicon steel is broader in process mode B, the latter is less subjected to the troubles which may be caused by the segregation of Al in the material.
  • the magnetic properties of the product obtained from a material containing the most suitable amount of Al by the process mode B are somewhat better than'those of the product obtained by the process mode A.
  • Example 1 Hot rolled silicon steel stock containing 0.04% C, 2.98% Si, a total content of 0.019% Al, comprising 0.015% acid-soluble Al and 0.0061 of AlN, and having a thickness of 1.6 mm., was pickled, cold rolled with a reduc tion of 60% in one direction, then again cold rolled with a reduction of 50% in another direction approximately at right angle thereto to a final gauge of about 0.33 mm. thickness.
  • the thus treated silicon steel was subjected to a continuous anneal for four minutes at the temperature of 800 C. in order to decarburize and recrystallize it, and to a final box anneal for hours at the temperature of 1150 C., to develop the magnetic properties thereof.
  • Magnetic tests according to Epstein were conducted on a sample taken from the above material with regard to the direction of the final cold rolling and also the direction at right angle thereto after the stress relief anneal, the results of which test are shown in the respective columns of Sample C of Table 1 as magnetic induction and iron core loss. As illustrated in FIG. 9, the magnetic torque curve diagram of this product shows that it is favored with an excellent structure of cube orientation.
  • Example 2 Hot rolled silicon steel strip containing 0.04% C, 2.99% Si, a total content of 0.023% A1 comprising 0.018% acid-soluble Al and 0.006l% AlN, and having a thickness of 1.6 mm., was pickled, cold rolled with a reduction of 60% in the same direction as that of the preceding hot rolling to produce a cold rolled silicon steel strip of 0.64 mm. thickness. Subsequently, the silicon steel strip was sheared off to a number of sheet of definite length, which were Welded together sheet by sheet in order to produce a new silicon steel strip Whose longitudinal direction was approximately at'right angle to the direction of the initial cold rolling.
  • the new silicon steel strip was again cold rolled with a reduction of about 50% to a thickness of 0.33 mm.
  • the cold rolled strip was subjected to a continuou anneal for four minutes at a temperature of 800 C. followed by a box anneal for 15 houre at a temperature of l l50 C.
  • Magnetic tests were conducted on an Epstein test sample taken from the above magnetic material with regard to its longitudinal direction and also to the direction approximately at right angle thereto, after the stress relief anneal, the results of which tests are shown in the respective column of Sample D of Table 1 as magnetic induction and iron core loss.
  • Example 3 A hot rolled silicon steel material of 2 mm. thickness, containing 0.04% C, 3.06% Si and 0.030% A1 (comprising 0.024% of acid-soluble Al, and 0.0069% of AlN) is cold rolled with reduction of 30% in one direction, then again cold rolled with a reduction of 30% in another direction displaced approximately at a right angle to the first rolling direction to an intermediate gauge of 0.98 mm., and annealed for a period of 10 hours at the maximum holding temperature of 950 C.
  • A1 comprising 0.024% of acid-soluble Al, and 0.0069% of AlN
  • this steel is further cold rolled with a reduction of 68% in the same direction as that of the second cold rolling step described above to a final gauge of 0.31 mm; and then finally box-annealed for a period of 20 hours at a maximum holding temperature of 1200 C. to develop the magnetic properties thereof.
  • Epstein samples are taken alongthe final rolling direction and also along the direction displaced at a right angle thereto, respectively, and magnetic tests are conducted on them after the stress relieving anneal, the results of which are as follows:
  • Example 4 The same hot rolled silicon steel material as in Example 3 with scale thereon is box-annealed for a period of 5 hours at a temperature of 680 C., then cold rolled with a reduction of 30% in one direction, then again cold rolled with a. reduction of 30% in another direction displaced approximately at a right angle the first direction of rolling to an intermediate gauge of 0.98 mm., and box-annealed for a period of 5 hours at a maximum holding temperature of 1100 C.
  • this' steel is further cold rolled with a reduction of 70% in the same direction as that of the second cold rolling step described to a final gauge of 0.30 mm, and finally box-annelaed for a period of 15 hours at a maximum holding temperature of 1150 C. to develop the magnetic properties thereof.
  • Epstein samples are taken along the final rolling direction and also along the direction displaced at a right angle thereto, respectively, and magnetic tests are conducted on them after the stress relieving anneal, the results of which are as follows:
  • Example 5 gitudinal direction is displaced at a right angle to the direction of the first cold rolling.
  • This new strip is cold rolled with a reduction of 40% to an intermediate gauge of 1.08 mm. It is then annealed at a maximum holding tempearture of 1100 C. for a period of 10 hours, then again cold rolled with a reduction of 72% in the direc- 7 tion of its longitudinal length to the final gauge, then annealed at a temperature of 800 C. for a period of 3 minutes in a wet hydrogen atmosphere to decarburize it, and finally box-annealed at a maximum holding temperature of 1200 C. for a period of 20 hours in order to develop its magnetic properties.
  • Epstein samples are taken along its longitudinal direction "and also along a direction displaced at a right angle thereto, respectively, and magnetic tests are conducted on 310 Wis/s (w-l e) Longitudinal Direction 18, 340 0.98 Right Angle Direction 18,150 1.
  • a process for producing double-oriented silicon steel sheet having (100) [001] crystal orientation and good magnetic properties in the final-rolling direction and the direction perpendicular thereto which comprises (a) pickling a hot-rolled silicon steel material consisting essentially of iron, from 2.5 to 4.0% by weight Si, and from 0.010 to 0.040% by weight A1, a substantial portion of said Al being in acid-soluble form which consists essentially of aluminum nitride,
  • a process for producing double-oriented silicon steel having (100) [001] crystal orientation and good magnetic 5 properties in the final-rolling direction and the direction perpendicular thereto which comprises (a) pickling a hot-rolled silicon steel material consisting essentially of iron, from 2.98 to 3.11% by weight of Si, and from 0.016 to 0.030% by weight of A1, a substantial portion of said Al being in acid-soluble form which consists essentially of 0.0029%0.007 3% by weight, based on the hot-rolled silicon steel, of aluminum nitride,

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Cited By (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3266955A (en) * 1962-12-28 1966-08-16 Yawata Iron & Steel Co Process for producing silicon steel sheet having (100) plane in the rolling plane
US3278348A (en) * 1965-01-28 1966-10-11 Westinghouse Electric Corp Process for producing doubly oriented cube-on-face magnetic sheet material
US3640780A (en) * 1970-06-25 1972-02-08 United States Steel Corp Method of producing electrical sheet steel with cube texture
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
EP0318051A2 (fr) * 1987-11-27 1989-05-31 Nippon Steel Corporation Procédé pour la production de tôles d'acier électriques à doubles orientation ayant une haute densité de flux
EP0452153A2 (fr) * 1990-04-12 1991-10-16 Nippon Steel Corporation Procédé pour la production de tôles d'acier électriques à double orientation ayant une haute densité de flux magnétique
EP0453284A2 (fr) * 1990-04-20 1991-10-23 Nippon Steel Corporation Procédé de fabrication de tôles d'acier électriques à double orientation ayant une densité de flux magnétique élevée
US5082509A (en) * 1989-04-14 1992-01-21 Nippon Steel Corporation Method of producing oriented electrical steel sheet having superior magnetic properties
ES2259561A1 (es) * 2005-03-23 2006-10-01 Manufacturas Y Artes De Toledo, S.L. Acero para espadas y procedimiento de obtencion de las espadas con dicho acero.
WO2007049915A1 (fr) * 2005-10-25 2007-05-03 Posco Tole d’acier a resistance amelioree a la corrosion pour pot d’echappement d’automobile et son procede de fabrication
CN101297055B (zh) * 2005-10-25 2012-11-28 Posco公司 用于机动车消音器的抗蚀性提高的钢板及该钢板的生产方法
CN108931476A (zh) * 2017-05-25 2018-12-04 宝山钢铁股份有限公司 一种判别取向硅钢缝合缝质量的方法
CN109048374A (zh) * 2018-09-27 2018-12-21 浙江华赢特钢科技有限公司 一种硅钢片一体成型设备及工艺流程
US11220723B2 (en) 2016-03-25 2022-01-11 Arcelormittal Method for manufacturing cold-rolled, welded steel sheets, and sheets thus produced

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DE2841961A1 (de) * 1978-10-05 1980-04-10 Armco Inc Verfahren zur herstellung von kornorientiertem siliciumstahl
KR102323332B1 (ko) * 2019-12-20 2021-11-05 주식회사 포스코 이방향성 전기강판 및 그의 제조방법

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DE741077C (de) * 1939-12-15 1943-11-04 Krupp Ag Walzverfahren zur Herstellung magnetischer Vorzugsrichtungen bei Transformatoren- und Dynamoblechen sowie magnetisierbaren Baendern
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US2173240A (en) * 1936-03-06 1939-09-19 Siemens Ag Method for manufacturing magnetic material of high permeability in sheet form
US2867557A (en) * 1956-08-02 1959-01-06 Allegheny Ludlum Steel Method of producing silicon steel strip
US3008856A (en) * 1957-02-16 1961-11-14 Ver Deutsche Metallwerke Ag Process for the production of sheets or strips with oriented magnetic properties from silicon and/or aluminum containing iron alloys
US2965526A (en) * 1958-10-03 1960-12-20 Westinghouse Electric Corp Method of heat treating silicon steel

Cited By (23)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3266955A (en) * 1962-12-28 1966-08-16 Yawata Iron & Steel Co Process for producing silicon steel sheet having (100) plane in the rolling plane
US3278348A (en) * 1965-01-28 1966-10-11 Westinghouse Electric Corp Process for producing doubly oriented cube-on-face magnetic sheet material
US3640780A (en) * 1970-06-25 1972-02-08 United States Steel Corp Method of producing electrical sheet steel with cube texture
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
EP0318051A2 (fr) * 1987-11-27 1989-05-31 Nippon Steel Corporation Procédé pour la production de tôles d'acier électriques à doubles orientation ayant une haute densité de flux
EP0318051A3 (fr) * 1987-11-27 1991-02-20 Nippon Steel Corporation Procédé pour la production de tôles d'acier électriques à doubles orientation ayant une haute densité de flux
US4997493A (en) * 1987-11-27 1991-03-05 Nippon Steel Corporation Process for production of double-oriented electrical steel sheet having high flux density
US5082509A (en) * 1989-04-14 1992-01-21 Nippon Steel Corporation Method of producing oriented electrical steel sheet having superior magnetic properties
EP0452153A2 (fr) * 1990-04-12 1991-10-16 Nippon Steel Corporation Procédé pour la production de tôles d'acier électriques à double orientation ayant une haute densité de flux magnétique
EP0452153A3 (en) * 1990-04-12 1992-12-30 Nippon Steel Corporation Process for manufacturing double oriented electrical steel sheet having high magnetic flux density
US5346559A (en) * 1990-04-12 1994-09-13 Nippon Steel Corporation Process for manufacturing double oriented electrical steel sheet having high magnetic flux density
EP0453284A2 (fr) * 1990-04-20 1991-10-23 Nippon Steel Corporation Procédé de fabrication de tôles d'acier électriques à double orientation ayant une densité de flux magnétique élevée
EP0453284A3 (fr) * 1990-04-20 1991-10-30 Nippon Steel Corporation Procédé de fabrication de tôles d'acier électriques à double orientation ayant une densité de flux magnétique élevée
ES2259561A1 (es) * 2005-03-23 2006-10-01 Manufacturas Y Artes De Toledo, S.L. Acero para espadas y procedimiento de obtencion de las espadas con dicho acero.
WO2007049915A1 (fr) * 2005-10-25 2007-05-03 Posco Tole d’acier a resistance amelioree a la corrosion pour pot d’echappement d’automobile et son procede de fabrication
US20080257461A1 (en) * 2005-10-25 2008-10-23 Won-Ho Son Corrosion Resistance Improved Steel Sheet for Autmotive Muffler and Method of Producing the Steel Sheet
US7922968B2 (en) 2005-10-25 2011-04-12 Posco Corrosion resistance improved steel sheet for automotive muffler and method of producing the steel sheet
CN101297055B (zh) * 2005-10-25 2012-11-28 Posco公司 用于机动车消音器的抗蚀性提高的钢板及该钢板的生产方法
US11220723B2 (en) 2016-03-25 2022-01-11 Arcelormittal Method for manufacturing cold-rolled, welded steel sheets, and sheets thus produced
US11959150B2 (en) 2016-03-25 2024-04-16 Arcelormittal Welded steel sheets, and sheets thus produced
CN108931476A (zh) * 2017-05-25 2018-12-04 宝山钢铁股份有限公司 一种判别取向硅钢缝合缝质量的方法
CN108931476B (zh) * 2017-05-25 2020-10-27 宝山钢铁股份有限公司 一种判别取向硅钢缝合缝质量的方法
CN109048374A (zh) * 2018-09-27 2018-12-21 浙江华赢特钢科技有限公司 一种硅钢片一体成型设备及工艺流程

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DE1259368B (de) 1968-01-25

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