PROCESS FOR PRODUCING NONORIENTED ELECTRIC STEEL SHEET

Abstract: PCT No. PCT/JP89/00241 Sec. 371 Date Oct. 17, 1989 Sec. 102(e) Date Oct. 17, 1989 PCT Filed Mar. 7, 1989 PCT Pub. No. WO89/08720 PCT Pub. Date Sep. 21, 1989.A steel slab containing not more than 0.005 wt % carbon, 1.0 to 4.0 wt % silicon, 0.1 to 1.0 wt % manganese, not more than 0.1 wt % phosphorus, not more than 0.005 wt % sulfur, and 0.1 to 2.0 wt % aluminum is directly sent to a hot rolling step without brief soaking, whereby Al and N are made soluble with respect to species other than AlN inevitably precipitated during hot rolling, and uniform and coarse AlN precipitation is formed by a subsequent annealing treatment in which the hot rolled plate is soaked at a temperature of 800 DEG to 1000 DEG C. for a period of time t defined as exp (-0.018T+19.4) </=t</=exp (-0.022T+25.4) wherein T is the soaking temperature ( DEG C.) and t is the soaking time (minutes). Uniform and satisfactory ferrite grain growth at the recrystallization annealing is provided thereby.

Description: TECHNICAL FIELD This invention relates to a method of making non-oriented electrical steel sheets. BACKGROUND OF THE INVENTION As important factors of governing magnetic properties of electrical steel sheets, sizes and dispersing conditions of AlN and MnS precipitates in steels are taken up. This is why these precipitates themselves become to obstacles to movements of magnetic domain walls and deteriorate not only the magnetic flux density under a low magnetic field but also the iron loss, and in addition they hinder grain growth during recrystallization annealing, and immature grain growth thereby of ferrite grains give bad influences to developments of recrystallization texture preferable to the magnetic properties. It is known that rougher and coarser precipitates are preferable for the movements of the magnetic domain walls during magnetization. Based on such background, there has been disclosed prior art trying to provide the precipitations and coarsenings of AlN or MnS before the recrystallization annealing in the processes of making the electrical steel sheets. For example, Japanese Patent Laid-Open Specification 38814/74 checks dissolution of the coarse AlN during slab soaking by lowering the heating temperature thereof; Japanese Patent Laid-Open Specification 22,931/81 lowers amounts of S and O accompanying growthes of fine non-metal lic inclusions; Japanese Patent Laid-Open Specification 8,409/80 controls formation of sulphides by addition of Ca or REM; Same 108,318/77, 41,219/79 and 123,825/83 coarsen AlN by brief soaking of the slab before the hot rolling; and Same 76,422/79 utilize self-annealing effect by coiling at super high temperature after hot rolling for coarsing AlN and accelerating growth of ferrite grain. From a viewpoint of saving the energy in the process, it is advantageous to carry out a hot direct rolling from the continuous casting of a slab when performing the hot rolling. However, if depending upon this process, a problem occurs that the coarse precipitations of AlN and MnS are made insufficient, and for solving the problem, the slab is subjected to the brief soaking before the hot rolling. However, although the soaking time is short, such a process which once transfers the slab into the heating and soaking furnaces, could not enjoy merits of saving energy brought about by the hot direct rolling, and further for providing precipitation of AlN, if the soaking time is short, the precipitation will be non-uniform at the inside and outside of the slab. DISCLOSURE OF THE INVENTION In view of these problems of the prior art, in the invention the slab is directly sent to the hot rolling without the brief soaking, whereby Al and N are made in solution with respect to others than AlN inevitably precipitated during hot rolling, and uniform and coarse AlN precipitation is formed by a subsequent annealing treatment, thereby to enable to provide uniform and satisfied ferrite grain growth at the recrystallization annealing. That is, the invention comprises hot rolling a slab immediately after continuously casting thereof without brief soaking at specified temperature range, said slab containing C: not more than 0.005 wt%, Si: 1.0 to 4.0 wt%, Mn: 0.1 to 1.0 wt%, P: not more than 0.1 wt%, S: not more than 0.005 wt%, Al: 0.1 to 2.0 wt%; coiling at temperature of not more than 650°C; annealing the hot rolled plate by soaking it at the temperature of 800 to 1000°C for a period of time satisfying exp (-0.018T + 19.4) ≦ t ≦ exp (-0.022T + 25.4) herein, T: soaking temperature (°C) t: soaking time (min); cold rollings of once or more than twice interposing an intermediate annealing; and a final continuous annealing at range of temperature between 850 and 1100°C. BRIEF DESCRIPTION OF THE DRAWINGS Fig. 1 shows, with respect to 3% Si steel, influences of the soaking time of the hot rolled band on average size of AlN during hot rolling and magnetic properties; and Fig. 2 shows optimum ranges of the soaking temperature and the soaking time during hot band's annealing. DETAILED DESCRIPTION OF THE INVENTION In the invention, the hot rolling is performed on the slab immediately after continuously casting thereof without brief soaking at specified temperature range (called as "Hot Direct Rolling"), said slab containing C: not more than 0.005 wt%, Si: 1.0 to 4.0 wt%, Mn: 0.1 to 1.0 wt%, P: not more than 0.1 wt%, S: not more than 0.005 wt%, Al: 0.1 to 2.0 wt%, and the coiling is operated at temperature of not more than 650°C. The present invention is based on a premise of the hot direct rolling, and is to optimize sizes and dispersing conditions of AlN and MnS which are problems in the magnetic property. In them, bad influences of MnS can be avoided by controlling the steel composition, but with respect to AlN, a measure is indispensable in the process. The precipitating nose of AlN is 800 to 1000°C. For precipitating AlN when the steel material is a slab, it is necessary to carry out a recrystallization annealing after precipitation for securing a rolling temperature. However, the heating and the heat-maintaining at the slab age spoil characteristics of the hot direct rolling in the energy cost. Therefore, in the invention, AlN is precipitated in a heating treatment after the hot rolling, and the brief soaking is not done when the steel is a slab, and the coiling is operated at temperature of not lower than 650°C after the hot rolling, whereby the whole amounts of others than AlN inevitably precipitated are made in solution. The hot rolled band is sent to a following annealing furnace. The annealing is, in the invention, performed at temperature between 800 and 1000°C nearly around the precipitating nose of AlN for providing perfect precipitation of Al and N as AlN, coasening thereof and recrystallization of ferrite grain and grain growth thereof. If the annealing temperature is lower than 800°C, coarsening of AlN are not satisfied, and if it is higher than 1000°C, the ferrite grain grow extraordinarily, and ridge like defects appear on the steel surface under the cold rolling and recrystallizingly annealing. The soaking time t in the annealing furnace is defined in a determined range in relation with the above stated soaking temperature T. Fig. 1 shows, with respect to 3% Si steel (Steel 5 of Table 1), influences of the soaking time of the hot rolled band to average size of AlN during hot rolling and magnetic properties after the final annealing, and it is seen the best range exists in the annealing time of the hot rolled band in response to the soaking temperature. As a result of experiments including also the above case it is seen that the soaking t (min) should satisfy a following condition in relation with the soaking temperature T (°C) exp(-0.018T + 19.4) ≦ t ≦ exp(-0.022T + 25.4). That is, for full coarsening of AlN at which the present invention aims, t ≧ exp(-0.018T + 19.4) must be satisfied. If the soaking is carried out more than necessary, the ferrite grains grow abnormally at the temperature of higher than 900°C, and the magnetic properties are deteriorated by formation of nitride layer at the temperature of below 900°C. If the soaking time t (min) exceeds exp(-0.022T + 25.4), the above mentioned problems occur. Against nitrization, it is useful to preliminarily remove scales by pickling, but as practicable allowance, the above limit is specified. The steel sheet having passed the hot rolling procedure and the annealing process is subjected to the cold rollings of once or more than twice interposing an intermediate annealing, and to the final finish annealing within the range between 850 and 1100°C. If the soaking temperature of the final annealing is less than 850°C, desired excellent iron loss and the magnetic flux density could not be obtained. But if exceeding 1100°C, such temperatures are not practical to passing of the coil and the cost of the energy. In addition, also in the magnetic properties, the iron loss value increases reversely by the abnormal grain growth of ferrite. A next reference will be made to reasons for limiting the steel composition. C is set not more than 0.005 wt% when producing a steel slab so as to secure the ferrite grain growth by lowering C during heat treatment of the hot rolled band and affect coarsening of AlN via decreasing of the solubility limit of AlN accompanied with stabilization of ferrite phases. Si of less than 1.0 wt% cannot satisfy the low iron loss due to lowering of proper electrical resistivity. On the other hand, if it exceeds 4.0 wt%, the cold rolling is difficult by shortening of ductility of steel. The upper limit of S is specified for improving the magnetic properties by decreasing an absolute amount of MnS. If S is set below 0.005 wt%, it may be decreased to a level negligible of bad influences of MnS in the direct hot rolling. Al of less than 0.1 wt% cannot fully coarsen AlN and nor avoid fine precipitation of AlN. If exceeding 2.0 wt%, effects of the magnetic properties are not brought about, and a problem arises about weldablity and brittleness. Depending upon the present invention, it is possible to secure satisfactorily precipitation and coarsening of AlN in the hot rolling process and the ferrite grain growth, while performing the hot direct rolling. Therefore, it is possible to produce economically the non-oriented electrical steel sheet with the excellent magnetic properties, by fully making use of the merits of the direct hot rolling. EXAMPLE The continuously cast slabs having the chemical compositions of Table 1 were passed through Hot Rolling - Annealing - Pickling - Cold Rolling - Final Continuous Annealing, and the non-oriented electrical steel sheets were produced. The magnetic properties of the produced electrical steel sheets and the characteristics of the hot rolled bands are shown in Table 2 together with the conditions of the hot rolling, annealing and final annealing. INDUSTRIAL APPLICABILITY The present invention may be applied to production of the non-oriented electrical steel sheets.

Claims: A method of making non-oriented electrical steel sheets having excellent magnetic properties, comprising hot rolling a slab immediately after continuously casting thereof without maintaining the heat or heating at specified temperature range, said slab containing C: not more than 0.005 wt%, Si: 1.0 to 4.0 wt%, Mn: 0.1 to 1.0 wt%, P: not more than 0.1 wt%, S: not more than 0.005 wt%, Al: 0.1 to 2.0 wt%; coiling at temperature of not more than 650°C; annealing the hot rolled plate by soaking it at the temperature of 800 to 1000°C for a period of time satisfying exp (-0.018T + 19.4) ≦ t ≦ exp (-0.022T + 25.4) herein, T: soaking temperature (°C) t: soaking time (min); cold rollings of once or more than twice interposing an intermediate annealing; and a final continuous annealing at range of temperature between 850 and 1100°C.

Inventors: HOSOYA, YOSHIHIRO, JITSUKAWA, MASAHARU, NISHIMOTO, AKIHIKO, TOMITA, KUNIKAZU, URABE, TOSHIAKI, HOSOYA, Yoshihiro, c/o NKK Corporation, JITSUKAWA, Masaharu, c/o NKK Corporation, NISHIMOTO, Akihiko, c/o NKK Corporation, TOMITA, Kunikazu, c/o NKK Corporation, URABE, Toshiaki, c/o NKK Corporation
Applicants: NKK CORPORATION
Application year: 1989
Main classification: C21D8
IPC codes: C21D8, C22C38