WO2011155183A1 - 無方向性電磁鋼板の製造方法および連続焼鈍設備 - Google Patents

無方向性電磁鋼板の製造方法および連続焼鈍設備 Download PDF

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Publication number
WO2011155183A1
WO2011155183A1 PCT/JP2011/003203 JP2011003203W WO2011155183A1 WO 2011155183 A1 WO2011155183 A1 WO 2011155183A1 JP 2011003203 W JP2011003203 W JP 2011003203W WO 2011155183 A1 WO2011155183 A1 WO 2011155183A1
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Prior art keywords
temperature
less
heating
steel sheet
width direction
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Ceased
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PCT/JP2011/003203
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English (en)
French (fr)
Japanese (ja)
Inventor
大村　健
善彰 財前
早川　康之
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JFE Steel Corp
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JFE Steel Corp
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    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/16—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys in the form of sheets
    • 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
    • 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
    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/05—Grain orientation

Definitions

  • the present invention relates to a method for producing a non-oriented electrical steel sheet mainly used as an iron core material for electrical equipment.
  • the present invention also relates to a continuous annealing facility suitable for use in manufacturing the non-oriented electrical steel sheet.
  • One means for improving the efficiency of electrical equipment and the like is to improve the magnetic properties of non-oriented electrical steel sheets that are the core material of these equipment.
  • a means for improving iron loss a method of increasing the content of Si, Al, Mn, etc. has been generally used with the aim of reducing eddy current loss due to an increase in electrical resistance.
  • this method has an essential problem that a decrease in magnetic flux density is inevitable.
  • Patent Document 1 discloses a texture improvement technique by warm rolling
  • Patent Document 2 discloses a technique for improving the texture by hot-rolled sheet annealing and cold rolling reduction ratio
  • Document 4 discloses a technique for improving the texture by applying rapid heating during primary recrystallization annealing.
  • Patent Document 3 and Patent Document 4 have a large effect of improving the texture, and can greatly improve both the iron loss and the magnetic flux density.
  • this technique when this technique is applied, there remains a problem in that the fluctuation of the magnetic characteristics in the coil is larger than in the prior art.
  • the present invention advantageously solves the above-described problems, and is advantageous for a non-oriented electrical steel sheet in which fluctuations in magnetic properties in the coil are small even when rapid heating treatment is performed during primary recrystallization annealing.
  • the object is to propose a manufacturing method.
  • Another object of the present invention is to propose a continuous annealing facility suitable for use in manufacturing the non-oriented electrical steel sheet.
  • the inventors investigated the cause of the fluctuation in the coil of the magnetic characteristics becoming larger than before when the rapid heat treatment is applied to the primary recrystallization annealing.
  • fluctuations in the magnetic characteristics in the coil were caused by uneven temperature distribution in the plate width direction caused by rapid heating. That is, when a temperature distribution is generated in the sheet width direction by rapid heating, this sheet width direction temperature distribution is not canceled even during the subsequent soaking, so that the primary recrystallized grain size in the sheet width direction becomes non-uniform. This caused variations in magnetic characteristics in the coil.
  • the inventors have performed a primary recrystallization annealing step in order to eliminate non-uniformity of primary recrystallized grains caused by temperature distribution caused by rapid heating.
  • a rapid heating process a temperature lowering process (first cooling process), a reheating process, a soaking process, and a second cooling process, and in particular, the conditions in the temperature lowering process and the reheating process after rapid heating can be appropriately controlled.
  • the present invention is based on the above findings.
  • the gist configuration of the present invention is as follows. 1. % By mass C: 0.02% or less and Si: 4.5% or less Mn: 3.0% or less, One or two or more types selected from Al: 3.0% or less and P: 0.50% or less, with the balance being Fe and unavoidable impurities, rolled to the final thickness, and then primary recrystallization
  • the direct heating method is first heated to a temperature range of 700 ° C or higher at a heating rate of 150 ° C / s or higher, and then the temperature is once lowered to a temperature range of 700 ° C or lower and then the indirect heating method.
  • the method for producing a non-oriented electrical steel sheet wherein the steel sheet is reheated to a soaking temperature under an average heating rate of 40 ° C./s or less.
  • the steel slab is further in mass%, Sn: 0.5% or less, 2.
  • a continuous annealing facility for non-oriented electrical steel sheets comprising a heating zone having a direct heating means, a first cooling zone, a heating zone and a soaking zone having indirect heating means, and a second cooling zone.
  • the manufacturing method of the present invention even when a rapid heat treatment is performed during primary recrystallization annealing, non-directional having excellent magnetic characteristics over the entire coil without causing variations in magnetic characteristics within the coil An electrically conductive steel sheet can be obtained. Further, by using the continuous annealing equipment of the present invention, it is possible to eliminate the non-uniformity of primary recrystallized grains across the plate width direction, which is a concern at the time of primary recrystallization annealing by rapid heating treatment. It is possible to obtain a non-oriented electrical steel sheet having no magnetic properties and excellent magnetic properties.
  • % indicating the steel composition means “% by mass” unless otherwise specified.
  • a steel slab containing C: 0.0025%, Si: 2.5%, Mn: 0.3%, Al: 0.7% and P: 0.1% with the balance being Fe and inevitable impurities is manufactured by continuous casting at 1100 ° C. After heating, a hot-rolled sheet having a thickness of 1.8 mm was obtained by hot rolling, and subjected to hot-rolled sheet annealing at 900 ° C. for 80 seconds.
  • primary recrystallization annealing was performed in a non-oxidizing atmosphere.
  • this primary recrystallization annealing first, rapid heating to 600-800 ° C at a heating rate of 20-300 ° C / s by the current heating method, and then an average increase of 20 ° C / s up to 1000 ° C by the gas heating method by the radiant tube. Heated at a temperature rate and held at 1000 ° C. for 10 seconds.
  • This experiment examined the magnetic properties and the grain size of the primary recrystallized grains. Evaluation of the magnetic properties was performed according to the method disclosed in JIS C2550 using a half test piece parallel to the rolling direction and a half test piece perpendicular to the rolling direction as it was. In the following experimental examples and examples, the magnetic characteristics were evaluated by the same method. Further, in order to investigate the magnetic fluctuation in the plate width direction, the coil was divided into five in the width direction as shown in FIG. 1, and the respective magnetic characteristics were measured and compared. The grain size of the primary recrystallized grains was obtained by observing the structure with an optical microscope and converting to a circular equivalent diameter. As the temperature and the rate of temperature increase during rapid heating, the lowest temperature and the rate of temperature increase were adopted at five temperature measuring positions in the plate width direction shown in FIG.
  • FIGS. 3A and 3B show the results of examining the influence of the temperature increase rate during rapid heating on the magnetic characteristics at the center position in the width direction. As shown in the figure, it can be seen that both the iron loss and the magnetic flux density are significantly improved by rapid heating to at least 700 ° C. at a heating rate of 150 ° C./s or more.
  • FIGS. 4A and 4B when the temperature is raised to 800 ° C. at a rate of 60 ° C./s and 200 ° C./s, the effect of the rate of temperature rise on the magnetic properties in the width direction of the steel sheet.
  • the result of having investigated about is shown. As shown in the figure, it can be seen that, at the heating rate (200 ° C./s) at which the magnetic characteristics are greatly improved, the fluctuation of the magnetic characteristics in the plate width direction is large.
  • FIG. 5 shows the results of examining the grain size of the primary recrystallized grains in the plate width direction when the temperature is raised to 800 ° C. at a rate of temperature increase of 60 ° C./s and 200 ° C./s.
  • the primary recrystallized grain size varies greatly in the plate width direction, and the temperature distribution varies across the plate width direction. The possibility of increasing was suggested.
  • FIG. 6 shows the relationship between the maximum temperature difference in the plate width direction at the end of rapid heating and during soaking.
  • the temperature difference in the plate width direction was obtained from the temperature measurement results at five locations shown in FIG. From the figure, it can be seen that in order to suppress the temperature distribution during soaking, it is necessary to suppress the temperature distribution at the end of rapid heating.
  • the temperature is once lowered to a certain temperature (800 ° C, 750 ° C, 700 ° C, 650 ° C, 600 ° C, 550 ° C, 500 ° C). Then, it was heated up to 1000 ° C. at an average heating rate of 20 ° C./s by a gas heating method using a radiant tube, and held at 1000 ° C. for 5 seconds. Cooling was performed by so-called gas cooling in which a cooling gas was introduced into the system.
  • FIG. 7 shows the result of examining the relationship between the temperature drop temperature when cooled once after rapid heating and the temperature difference in the plate width direction during soaking.
  • the temperature difference at the time of soaking was calculated
  • the temperature difference in the plate width direction at the end of rapid heating was about 50 ° C. As shown in the figure, it was found that, after rapid heating, the temperature difference in the width direction at the time of soaking is greatly reduced by lowering the temperature to 700 ° C. or less.
  • FIGS. 8A and 8B show the results of investigating the relationship between the temperature drop temperature and the magnetic properties in the plate width direction when cooled once after rapid heating. As shown in the figure, it was found that once the temperature was lowered to 700 ° C or less, the temperature distribution in the plate width direction at the time of soaking was eliminated, and the variation in the magnetic characteristics in the plate width direction was also eliminated. .
  • FIG. 9 shows the results of examining the relationship between the maximum temperature difference at five locations in the plate width direction during soaking and the temperature increase rate during reheating.
  • the temperature increase rate was made into the average temperature increase rate of five places of measurement in the board width direction of FIG.
  • the rate of temperature increase during reheating exceeded 40 ° C./s
  • a tendency that the temperature difference in the plate width direction increased was observed. Therefore, in order to suppress the temperature difference at the time of soaking, it is necessary to suppress the temperature increase rate at the time of reheating to 40 ° C./s or less even in the case of the indirect heating method in which the temperature distribution hardly occurs. found.
  • the problem of large variation in magnetic characteristics in the coil which has been a problem in the past in improving magnetic characteristics by rapid heating treatment, is a problem that the primary recrystallization annealing has a temperature of 700 ° C. or more during rapid heating.
  • the average temperature increase rate to the soaking temperature is 40 ° C / s or lower during subsequent reheating.
  • C 0.02% or less Since the iron loss significantly deteriorates due to magnetic aging when the C content exceeds 0.02%, the C content is limited to 0.02% or less. Moreover, regarding the lower limit, there is no problem even if the slab does not contain C, but industrially, it may be contained in excess of 0%.
  • Si 4.5% or less, Mn: 3.0% or less, Al: 3.0% or less, and P: 0.50% or less, selected from one or any combination of two or more Si, Mn, Al, and P are added.
  • the electric resistance can be increased, and the element is useful for further improving the iron loss without impairing the gist of the present invention. Therefore, two or more types are contained in one or any combination from the group consisting of Si, Mn, Al and P. From the viewpoint of the effect of reducing iron loss, it is preferable to contain 0.5% or more of Si, 0.05% or more of Mn, 0.1% or more of Al, and 0.01% or more of P.
  • Sb, Sn, and Cr known as magnetic property improving elements can be added alone or in combination in any combination. Addition amounts of these elements are Sn: 0.5% or less, Sb: 0.5% or less, and Cr: 5.0% or less. This is because, even if each element is added in excess of the upper limit, the effect of improving the magnetic properties reaches saturation, and no further improvement effect can be expected, but rather the cost increases due to the addition of alloy elements.
  • Preferable lower limits are Sn: 0.005%, Sb: 0.005%, and Cr: 0.05%, but there is no particular problem even if less than these are contained as impurities.
  • the balance other than the above components is inevitable impurities and Fe.
  • unavoidable impurities include O, B, Ti, Nb, V, Ni, Cu, P, and Mo, in addition to Sn, Sb, and Cr below the above-described addition amount.
  • the manufacturing method of the non-oriented electrical steel sheet according to the present invention will be described.
  • the molten steel adjusted to the above-mentioned preferred component composition is melted in a converter or an electric furnace, and then made into a steel slab by a continuous casting method or an ingot-bundling rolling method.
  • the obtained steel slab is rolled to the final thickness.
  • a steel slab is hot-rolled, and hot-rolled hill annealing is performed as necessary, and then cold rolling (including the case of warm rolling) or intermediate annealing is performed. It is preferable to carry out cold rolling (including the case where the warm rolling is partially or wholly employed) twice or more to obtain the final thickness.
  • primary recrystallization annealing is performed.
  • the process conditions from melting to cold rolling based on a well-known technique.
  • this primary recrystallization annealing after rapid heating, the temperature is once lowered, then reheated, soaked, and then cooled.
  • heating is performed at a temperature rising rate of 150 ° C./s or higher up to a temperature range of 700 ° C. or higher by a direct heating method.
  • the temperature is once lowered to a temperature range of 700 ° C. or lower, and then reheated to a soaking temperature by an indirect heating method under the condition of an average rate of temperature increase of 40 ° C./s or less.
  • a preferable upper limit is 820 ° C. from the viewpoint of cost.
  • the rapid heating method is limited to a direct heating method such as induction heating or current heating.
  • the reason why the temperature is once lowered to a temperature range of 700 ° C. or less after the rapid heating described above is to eliminate the temperature distribution in the width direction generated during the rapid heating by the soaking process. Since temperature control in the temperature lowering process also needs to be performed over the entire steel plate, the hottest point in the plate width direction also needs to be set to 700 ° C. or less. That is, cooling is performed so that the hottest point in the plate width direction is 700 ° C. or lower. A preferred lower limit is 500 ° C. from the viewpoint of cost.
  • the cooling method is preferably gas cooling.
  • the reheating performed after equalizing the temperature distribution in the plate width direction is an indirect heating method in which the temperature distribution is less likely to occur, and the temperature rising rate is limited to 40 ° C./s or less.
  • the lower limit is preferably 5 ° C./s or more from the viewpoint of cost.
  • the temperature increase rate at this time is an average temperature increase rate over the plate width direction.
  • the indirect heating method includes, for example, atmosphere heating and radiation heating, but atmosphere heating (such as a gas heating method using a radiant tube) generally employed in a continuous annealing furnace is preferable in terms of cost and maintenance.
  • the soaking temperature may be in a known range, but is preferably in the range of 900 to 1020 ° C.
  • a heating zone having a direct heating means for example, a heating zone having a direct heating means, a first cooling zone, a heating zone and a soaking zone having indirect heating means, and a second cooling And a continuous annealing facility having a belt.
  • the soaking process and the subsequent cooling process are not particularly limited and may be performed according to a conventional method. Thereafter, an insulating film is applied and baked to obtain a product.
  • an insulating film is applied and baked to obtain a product.
  • the non-oriented electrical steel sheet produced according to the present invention not only provides very good magnetic properties, but also has very little variation in the magnetic properties in the width direction.

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PCT/JP2011/003203 2010-06-09 2011-06-07 無方向性電磁鋼板の製造方法および連続焼鈍設備 Ceased WO2011155183A1 (ja)

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Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2014142149A1 (ja) * 2013-03-15 2014-09-18 Ｊｆｅスチール株式会社 高周波鉄損特性に優れる無方向性電磁鋼板
WO2014148328A1 (ja) * 2013-03-22 2014-09-25 Ｊｆｅスチール株式会社 高周波鉄損特性に優れる無方向性電磁鋼板
US9767946B2 (en) 2012-08-21 2017-09-19 Jfe Steel Corporation Non-oriented electrical steel sheet being less in deterioration of iron loss property by punching
US10102951B2 (en) 2013-03-13 2018-10-16 Jfe Steel Corporation Non-oriented electrical steel sheet having excellent magnetic properties
US10597759B2 (en) 2013-08-20 2020-03-24 Jfe Steel Corporation Non-oriented electrical steel sheet having high magnetic flux density and motor
CN112143964A (zh) * 2019-06-28 2020-12-29 宝山钢铁股份有限公司 一种极低铁损的无取向电工钢板及其连续退火工艺
CN118755911A (zh) * 2024-05-28 2024-10-11 包头钢铁（集团）有限责任公司 一种无取向硅钢实验室退火方法

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WO2017086036A1 (ja) 2015-11-20 2017-05-26 Ｊｆｅスチール株式会社 無方向性電磁鋼板の製造方法
JP6402865B2 (ja) * 2015-11-20 2018-10-10 Ｊｆｅスチール株式会社 無方向性電磁鋼板の製造方法
JP6406522B2 (ja) 2015-12-09 2018-10-17 Ｊｆｅスチール株式会社 無方向性電磁鋼板の製造方法
KR101701194B1 (ko) * 2015-12-23 2017-02-01 주식회사 포스코 무방향성 전기강판 및 그 제조방법
JP6769580B1 (ja) 2018-11-26 2020-10-14 Ｊｆｅスチール株式会社 無方向性電磁鋼板の製造方法
CN112430776B (zh) * 2019-08-26 2022-06-28 宝山钢铁股份有限公司 一种磁各向异性小的无取向电工钢板及其制造方法
TWI865077B (zh) * 2022-09-30 2024-12-01 日商日本製鐵股份有限公司 無方向性電磁鋼板

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JPS56112417A (en) * 1980-02-08 1981-09-04 Nippon Steel Corp Continuous treating apparatus of nondirectional electrical sheet
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JP2001316729A (ja) * 2000-04-28 2001-11-16 Kawasaki Steel Corp 鉄損が低くかつ磁束密度の高い無方向性電磁鋼板の製造方法

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JPS56112417A (en) * 1980-02-08 1981-09-04 Nippon Steel Corp Continuous treating apparatus of nondirectional electrical sheet
JPS61124527A (ja) * 1984-11-20 1986-06-12 Sumitomo Metal Ind Ltd 無方向性電磁鋼板の製造方法
JPS6299421A (ja) * 1985-10-24 1987-05-08 Nippon Light Metal Co Ltd 金属ストリツプの連続加熱装置
JPH0559441A (ja) * 1991-09-03 1993-03-09 Sumitomo Metal Ind Ltd 磁気特性の良好な無方向性電磁鋼板の製造方法
JP2001316729A (ja) * 2000-04-28 2001-11-16 Kawasaki Steel Corp 鉄損が低くかつ磁束密度の高い無方向性電磁鋼板の製造方法

Cited By (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US9767946B2 (en) 2012-08-21 2017-09-19 Jfe Steel Corporation Non-oriented electrical steel sheet being less in deterioration of iron loss property by punching
US10102951B2 (en) 2013-03-13 2018-10-16 Jfe Steel Corporation Non-oriented electrical steel sheet having excellent magnetic properties
WO2014142149A1 (ja) * 2013-03-15 2014-09-18 Ｊｆｅスチール株式会社 高周波鉄損特性に優れる無方向性電磁鋼板
JP2014177684A (ja) * 2013-03-15 2014-09-25 Jfe Steel Corp 高周波鉄損特性に優れる無方向性電磁鋼板
EP2975147A4 (en) * 2013-03-15 2016-04-06 Jfe Steel Corp NON-ORIENTED ELECTRIC STEEL PLATE WITH EXCELLENT HIGH FREQUENCY TOOL LOSS CHARACTERISTICS
WO2014148328A1 (ja) * 2013-03-22 2014-09-25 Ｊｆｅスチール株式会社 高周波鉄損特性に優れる無方向性電磁鋼板
JP2014185365A (ja) * 2013-03-22 2014-10-02 Jfe Steel Corp 高周波鉄損特性に優れる無方向性電磁鋼板
US10597759B2 (en) 2013-08-20 2020-03-24 Jfe Steel Corporation Non-oriented electrical steel sheet having high magnetic flux density and motor
CN112143964A (zh) * 2019-06-28 2020-12-29 宝山钢铁股份有限公司 一种极低铁损的无取向电工钢板及其连续退火工艺
CN118755911A (zh) * 2024-05-28 2024-10-11 包头钢铁（集团）有限责任公司 一种无取向硅钢实验室退火方法

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