WO2024022109A1 - 一种高磁感无取向电工钢板及其制造方法 - Google Patents

一种高磁感无取向电工钢板及其制造方法 Download PDF

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WO2024022109A1
WO2024022109A1 PCT/CN2023/106986 CN2023106986W WO2024022109A1 WO 2024022109 A1 WO2024022109 A1 WO 2024022109A1 CN 2023106986 W CN2023106986 W CN 2023106986W WO 2024022109 A1 WO2024022109 A1 WO 2024022109A1
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steel plate
oriented electrical
electrical steel
steel
manufacturing
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French (fr)
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张峰
吕学钧
房现石
王波
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宝山钢铁股份有限公司
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/001—Heat treatment of ferrous alloys containing Ni
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D8/1216—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
    • C21D8/1222—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
    • C21D8/1233—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1272—Final recrystallisation annealing
    • 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
    • C21D8/1277—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular surface treatment
    • C21D8/1283—Application of a separating or insulating coating
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/20—Recycling

Definitions

  • the present invention relates to a steel plate and a manufacturing method thereof, in particular to a non-oriented electrical steel plate and a manufacturing method thereof.
  • non-oriented electrical steel plates are widely used in the current existing technology. Improving the magnetic induction of non-oriented electrical steel plates can effectively reduce the copper losses of motors, compressors, and EI cores, and achieve the purpose of energy saving and consumption reduction. . Therefore, in order to effectively improve the magnetic induction of the finished non-oriented electrical steel sheet, those skilled in the art usually improve the recrystallization performance of the hot-rolled steel sheet by reducing the Si and Al content in the steel, or using normalized intermediate annealing measures. Microstructure to obtain a more favorable crystal texture ratio.
  • the publication number is CN104073715A, and the publication date was October 1, 2014.
  • the Chinese patent document titled "A high magnetic induction non-oriented electrical steel and its manufacturing method" discloses a high magnetic induction non-oriented electrical steel.
  • This technical solution can increase the magnetic induction B 50 by 200-500 Gauss without adding additional alloying elements or changing the annealing process of the finished product, and the physical quality level of iron loss can be increased by 3-5%.
  • the annealing process can also be optimized to further improve the magnetic properties of the product and further enhance the magnetic induction.
  • the Chinese patent document titled "A high magnetic permeability non-oriented silicon steel and its production method" discloses a high magnetic permeability non-oriented silicon steel. Its components and weight percentage content are: C ⁇ 0.003%, Si: 0.1-1.8%, Al ⁇ 0.99%, Mn: 0.1-0.5%, Sn: 0.005-0.08%, Cu ⁇ 0.005%, S ⁇ 0.005%, nothing to gain
  • the production steps of silicon steel include: steelmaking and vacuum treatment; heating of the slab after casting; normalization after hot rolling; cold rolling after pickling; annealing of the finished product; and coating.
  • annealing process relatively coarse spherical MnS-Cu 2 S composite inclusions are obtained, which reduces MnS, Cu 2 S and other sulfides, while reducing the impact of cooling stress on magnetic domains, and obtaining more 180°C magnetic domains or Similar magnetic domains, and the volume ratio can reach more than 60%, thereby improving the magnetic permeability of steel.
  • One of the purposes of the present invention is to provide a high magnetic induction non-oriented electrical steel plate.
  • the high magnetic induction non-oriented electrical steel plate is based on a new chemical composition design and an optimized manufacturing process, and can obtain excellent mechanical properties and electromagnetic properties.
  • the yield ratio is 0.78 ⁇ 0.9, and has the remarkable characteristics of high yield ratio, high magnetic induction and low iron loss.
  • the present invention proposes a non-oriented electrical steel plate, which in addition to Fe and inevitable impurities, also contains the following chemical elements in terms of mass percentage:
  • the non-oriented electrical steel sheet does not contain Sn and Sb.
  • the components of the steel plate are as follows in terms of mass percentage:
  • Si+Al 1.30 ⁇ 3.20%.
  • the C element can strongly hinder the growth of grains in the finished steel strip. It is easy to combine with Nb, V, Ti, etc. to form fine precipitates, thereby causing increased losses and magnetic aging. Based on this, in the high magnetic induction non-oriented electrical steel sheet of the present invention, the mass percentage content of the C element is controlled to C ⁇ 0.003%.
  • Mn element can combine with S element to form MnS, which can effectively reduce the magnetic hazard to steel.
  • Mn element content in steel is less than 0.1%, the effect of Mn element on fixing S is relatively small. Poor; when the Mn element content in steel is higher than 0.6%, the manufacturing cost of steel will be significantly increased. Based on this, in order to give full play to the beneficial effects of Mn element, the mass percentage content of Mn element in the non-oriented electrical steel sheet of the present invention is controlled between 0.1% and 0.6%.
  • Si Adding an appropriate amount of Si element to steel can not only increase the resistivity of the steel, but also effectively reduce the iron loss of the steel.
  • Si element content in the steel is higher than 3.0%, it will significantly reduce the magnetic induction of the steel and easily lead to cold rolling strip breakage; while when the Si element content in the steel is lower than 1.2%, it will not significantly reduce the steel's magnetic induction. Iron loss effect.
  • the mass percentage content of Si element in the non-oriented electrical steel sheet of the present invention is controlled between 1.2 and 3.0%.
  • Al element is an important deoxidizing element. When the Al element content in the steel is less than 0.1%, it will not have a good deoxidation effect; and when the Al element content in the steel exceeds 0.4%, it will cause difficulty in continuous casting. Increases steel manufacturing costs. Based on this, in order to exert the beneficial effects of Al element, in the non-oriented electrical steel sheet of the present invention, the mass percentage content of Al element is controlled between 0.1 and 0.4%.
  • the present invention further limits the sum of the mass percentages of Si and Al elements, that is, the numerical range of "Si+Al" is controlled to be between 1.3 and 1.3. between 3.2%.
  • Ni element is added with a mass percentage of 0.05% to 1.0%, and the range of Ni element is preferably controlled between 0.1% and 0.5%.
  • the purpose of adding Ni to steel is: Ni is a ferromagnetic element with properties similar to that of Fe element. Adding 0.05% or more Ni element to steel can significantly increase the magnetic induction intensity of the steel. However, it is also not advisable to add excessive Ni to steel. The market price of Ni is relatively high. From an economic point of view, it needs to be limited to 1.0% or less.
  • the mass percentage of Ni element is preferably controlled between 0.1% and 0.5%.
  • P element is also added. Adding P element to the steel can significantly improve the strength of the steel.
  • the content of P element in steel is higher than 0.01%, The strength of the steel begins to increase rapidly, but when the mass percentage of the P element in the steel exceeds 0.15%, the cold-rollability of the steel will be significantly reduced, and it will cause abnormalities such as edge cracks and broken strips in the steel plate. situation occurs. Therefore, in the high magnetic induction non-oriented electrical steel sheet of the present invention, the mass percentage content of P element is controlled between 0.01% and 0.15%.
  • the mass percentage of P element between 0.01% and 0.08%.
  • the non-oriented electrical steel sheet of the present invention among the inevitable impurities, S ⁇ 0.004%, N ⁇ 0.0025%, and O ⁇ 0.0025%.
  • the S element, the N element and the O element are all impurity elements in the non-oriented electrical steel plate. They are the raw and auxiliary materials of steel or impurity elements introduced during the production process. When technical conditions permit, In this case, in order to obtain steel with better performance and better quality, the content of impurity elements in the steel should be reduced as much as possible.
  • the mass percentage content of the S, N, and O elements in the steel must be strictly controlled, and the specific control is as follows: S ⁇ 0.004%, N ⁇ 0.0025%, O ⁇ 0.0025%.
  • the composition of the steel plate satisfies at least one of the following in terms of mass percentage:
  • the thickness of the steel plate is 0.2 to 0.5 mm.
  • the proportion of the number of equiaxed crystals with a ratio of the major and minor axes between 1.0 and 4.0 is more than 75%.
  • the yield ratio of the steel plate is 0.78 to 0.9.
  • another object of the present invention is to provide a method for manufacturing the above-mentioned non-oriented electrical steel sheet.
  • the manufacturing method is simple and feasible, the production operation process is simple, and the hot-rolled steel coils prepared by hot rolling and coiling are Without the need for normalized intermediate annealing process, this manufacturing method can achieve excellent mechanical properties. High magnetic induction non-oriented electrical steel plate with excellent performance and electromagnetic properties.
  • the present invention proposes a manufacturing method of non-oriented electrical steel plate, which includes the following steps:
  • the continuous casting billet is heated, rough rolled, finish rolled and coiled in sequence: the thickness of the intermediate billet after rough rolling is controlled to be 20 ⁇ 45mm, and the thickness of the plate after finish rolling is controlled to be 1.2 ⁇ 2.0mm; in coiling After taking it out, it is aged for 1 to 4 hours in the range of 550 to 650°C during the temperature drop process to form a hot rolled steel coil;
  • the inventor optimized the chemical composition design of the steel and defined a reasonable manufacturing process.
  • the continuous casting billet is obtained through smelting and casting, it can be optimized and processed through heating, rough rolling, finish rolling and coiling in sequence.
  • This invention optimizes the thickness of the intermediate billet after hot rolling and rough rolling and the thickness of the plate after hot rolling and finishing, and performs aging treatment on the hot-rolled steel coil after finishing rolling and coiling, which is combined with subsequent pickling and primary cooling.
  • Rolling, continuous annealing and insulating coating processes can effectively prepare non-oriented electrical steel plates with high magnetic induction and high yield ratio.
  • smelting and casting may specifically include the four steps of "molten iron pretreatment”, “converter smelting”, “RH refining” and “continuous casting”. Based on this process, it is possible to ensure that qualified continuous casting slabs that meet the chemical composition design of the present invention are obtained.
  • the thickness of the intermediate billet after rough rolling needs to be controlled to 20 to 45 mm.
  • the thickness of the plate after hot rolling and finishing rolling can be further adjusted to 1.2 to 2.0 mm by optimizing the reduction rate of the finishing rolling pass and the distribution of cooling water.
  • the equiaxed grains in the hot rolling microstructure are continuously elongated along the rolling direction, and the ratio of the long and short axes becomes larger and larger. The bigger it gets, usually more than 4.0.
  • the magnetic anisotropy of the finished steel plate will increase and the yield ratio of the finished steel plate will decrease.
  • step (2) after completing the heating, rough rolling, finish rolling and coiling of step (2), there is no need to perform a normalized intermediate annealing process. It can be directly pickled and cold rolled once to roll to a target thickness of 0.2 ⁇ 0.5mm. Then, continuous annealing can be preferably carried out in a temperature range of 850°C to 1000°C in a mixed atmosphere of nitrogen and hydrogen. The steel plate obtained after continuous annealing is further coated with an insulating coating to obtain the finished product of the present invention with high magnetic induction. Oriented electrical steel plate, the yield-strength ratio of this high magnetic induction non-oriented electrical steel plate can reach 0.78 ⁇ 0.90.
  • step (5) continuous annealing is performed in a temperature range of 850°C to 1000°C in a nitrogen and hydrogen mixed atmosphere.
  • the proportion of nitrogen in the nitrogen and hydrogen mixed atmosphere is 50% to 70%, and the proportion of hydrogen is 30% to 50%.
  • the non-oriented electrical steel plate and its manufacturing method of the present invention have the following advantages and beneficial effects:
  • the inventor has designed a new high magnetic induction non-oriented electrical steel plate through a new chemical composition design and combined with an optimized manufacturing process.
  • the inventor optimized and controlled the thickness of the hot-rolled rough-rolled intermediate billet and the thickness of the hot-rolled finished product on the basis of reasonable chemical composition, and performed aging treatment on the hot-rolled steel coils after finish rolling and coiling. Control the proportion of equiaxed crystals with a ratio of long and short axes in the steel coil between 1.0 and 4.0 to be more than 75%, thereby improving the magnetic induction and increasing the yield ratio of the steel plate.
  • the hot-rolled steel coil does not need to undergo a normalized intermediate annealing process, and its production operation process is simple.
  • the prepared high magnetic induction non-oriented electrical steel plate has the characteristics of high yield ratio, high magnetic induction, and low iron loss.
  • the technical solution designed by the present invention can significantly reduce the difficulty of controlling impurity elements and harmful inclusions in steelmaking. There is no need to add Sn and Sb trace elements to the steel, which can effectively save ingredients and has good promotion prospects and Value.
  • Figure 1 schematically shows the relationship between the Ni element content in the high magnetic induction non-oriented electrical steel plate of the present invention and the magnetic induction intensity of the finished steel plate.
  • Figure 2 schematically shows the relationship between the number ratio of equiaxed crystals with a long and short axis ratio between 1.0 and 4.0 and the yield ratio in the microstructure of the high magnetic induction non-oriented electrical steel plate according to the present invention. .
  • Table 1 lists the mass percentages of each chemical element in the high magnetic induction non-oriented electrical steel plates of Examples 1-6 and the comparative steel plates of Comparative Examples 1-2.
  • the high magnetic induction non-oriented electrical steel plates of Examples 1-6 and the comparative steel plates of Comparative Examples 1-2 are all prepared using the following steps:
  • the obtained continuous casting billet is input into the heating furnace for heating and temperature rise. After the heating is completed, it is discharged from the furnace and rough rolling, finish rolling and coiling are carried out.
  • the rough rolling is controlled after The thickness of the intermediate billet is 20 ⁇ 45mm, and the thickness of the plate after finish rolling is 1.2 ⁇ 2.0mm; after coiling, it is aged for 1 ⁇ 4 hours in the range of 550 ⁇ 650°C during the temperature drop process, and then naturally cooled to Room temperature, so that the proportion of the number of equiaxed crystals in the microstructure of the plate with the ratio of the long and short axes between 1.0 and 4.0 is ⁇ 75%.
  • the target thickness is 0.2 ⁇ 0.5mm.
  • Continuous annealing is performed in a nitrogen and hydrogen mixed atmosphere, and the continuous annealing temperature range is controlled to be 850°C to 1000°C.
  • Insulating coating Apply an insulating coating on the surface of the continuously annealed steel plate.
  • the chemical composition and relevant process parameters of the high magnetic induction non-oriented electrical steel plates of Examples 1-6 all meet the design specification control requirements of the present invention; and in Comparative Examples 1-2, the comparison of Comparative Examples 1-2
  • the steel plate is also produced using the above-mentioned process steps, its chemical element composition and/or related process parameters have parameters that are not in line with the design of the present invention.
  • Table 2 lists the specific process parameters and final finished product thickness in the above-mentioned manufacturing process of the high magnetic induction non-oriented electrical steel plates of Examples 1-6 and the comparative steel plates of Comparative Examples 1-2.
  • Table 3 lists the results of microstructure observation and analysis of the steel plates prepared in Examples 1-6 and Comparative Examples 1-2 after aging treatment.
  • Magnetic induction performance test Based on the national standard GB/T 3655-2008, the Epstein square circle method is used for iron loss performance testing.
  • the test temperature is 20°C constant temperature test.
  • the sample size is 30mm ⁇ 300mm, and the target mass is 0.5kg.
  • the test parameter is B 50 .
  • the magnetic induction B 50 of the sample steel plates of Examples 1-6 and Comparative Examples 1-2 was thus measured.
  • Iron loss performance test Based on the national standard GB/T 3655-2008, the Epstein square circle method is used to conduct the iron loss performance test.
  • the test temperature is a constant temperature test of 20°C.
  • the sample size is 30mm ⁇ 300mm, and the target mass is 0.5kg.
  • the test parameter is P 15/50 .
  • the iron loss P 15/50 of the sample steel plates of Examples 1-6 and Comparative Examples 1-2 was thus measured.
  • Table 4 lists the test results of the yield ratio, magnetic induction B 50 and iron loss P 15/50 of the high magnetic induction non-oriented electrical steel plates of Examples 1-6 and the comparative steel plates of Comparative Examples 1-2.
  • the high magnetic induction non-oriented electrical steel plates of Examples 1-6 have excellent mechanical properties and electromagnetic properties, their yield ratio is between 0.78-0.90, and the magnetic induction B50 is between Between 1.694-1.742T, the iron loss P 15/50 is between 1.82-3.14W/kg, and its comprehensive performance is significantly better than the steel plate of Comparative Examples 1-2. Since Comparative Example 1-2 does not meet the conditions defined by the present invention, its implementation effect is also inferior to that of the present invention.
  • the Ni content in the steel is 0.02%, which is 0.05% lower than the design lower limit requirement of the present invention, and there is no aging treatment for 1 to 4 hours in the range of 550 to 650°C during the temperature drop process, and then naturally cooled to At room temperature, the ratio of the number of equiaxed crystals in the microstructure of the steel plate with the ratio of the long and short axes between 1.0 and 4.0 is only 63%, which is lower than the 75% lower limit required by the design of the present invention.
  • the yield-to-strength ratio of the comparative steel material of Comparative Example 1 finally prepared was only 0.64, which did not meet the lower limit of 0.78 required by the design of the present invention.
  • the P content in the steel is 0.008%, which is 0.01% lower than the design lower limit requirement of the present invention
  • the Al content in the steel is 0.44%, which is 0.4% higher than the design upper limit requirement of the present invention
  • the temperature drop process There is no aging treatment for 1 to 4 hours in the range of 550 to 650°C, and then natural cooling to room temperature, so that the number of equiaxed grains with a ratio of long and short axes between 1.0 and 4.0 in the microstructure of the steel plate is only 73%. , which is 75% lower than the design lower limit requirement of the present invention.
  • the yield-to-strength ratio of the comparative steel material of Comparative Example 2 finally prepared was only 0.75, which did not meet the lower limit of 0.78 required by the design of the present invention.
  • Figure 1 schematically shows the relationship between the Ni element content in the high magnetic induction non-oriented electrical steel plate of the present invention and the magnetic induction intensity of the finished steel plate.
  • Figure 2 schematically shows the relationship between the number ratio of equiaxed crystals with a long and short axis ratio between 1.0 and 4.0 and the yield ratio in the microstructure of the high magnetic induction non-oriented electrical steel plate according to the present invention. .
  • the qualified proportion of equiaxed grain size (proportion of the number of equiaxed grains) in the microstructure with the ratio of the long and short axes between 1.0 and 4.0 is positively related to the yield ratio.
  • the yield ratio of the steel increases accordingly. increase.
  • the yield-strength ratio of the steel will be greater than 0.78, and fluctuate with the chemical composition and production process of the steel in the range of 0.78-0.90.

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  • Soft Magnetic Materials (AREA)

Abstract

一种高磁感无取向电工钢板，其含有Fe和不可避免的杂质，其还含有质量百分含量如下的化学元素：C≤0.003％、Si：1.2~3.0％、Mn：0.1~0.6％、P：0.01~0.15％、Al：0.1~0.4％、Ni：0.05~1.0％；并且满足Si+Al：1.3~3.2％；其不含有Sn和Sb。此外还提供一种上述高磁感无取向电工钢板的制造方法，其包括步骤：(1)冶炼和铸造；(2)加热、粗轧、精轧和卷取：其中控制经过粗轧之后的中间坯厚度为20~45mm，经过精轧之后的板材厚度为1.2~2.0mm；在卷取之后在温降过程中的550~650℃范围内进行1~4h时效处理；(3)酸洗；(4)一次冷轧；(5)连续退火；(6)绝缘涂层。

Description

一种高磁感无取向电工钢板及其制造方法 技术领域
本发明涉及一种钢板及其制造方法，尤其涉及一种无取向电工钢板及其制造方法。
背景技术
众所周知，无取向电工钢板在当前现有技术中的应用十分广泛，提高无取向电工钢板的磁感，可以有效降低马达、压缩机、EI铁芯的铜损，并起到节能、降耗的目的。由此，为了能够有效提高成品无取向电工钢板的磁感，本领域技术人员通常会通过降低钢中的Si、Al含量，或者是采用常化中间退火措施，来改善热轧钢板的再结晶显微组织，以获得更有利的晶体织构比例。
但是，限制钢中的Si、Al含量加入，会导致成品钢板的机械性能劣化，并且不利于大幅提高电动工具的频率、转速等。为此，如何更加有效地制备低成本、高磁感、高强度的无取向电工钢板，具有很强的现实意义。
针对这一需求，当前已有研究人员进行了大量的研究，并取得了一定的研究成果。
例如：公开号为CN104073715A，公开日2014年10月1日，名称为“一种高磁感无取向电工钢及其制造方法”的中国专利文献公开了一种高磁感无取向电工钢，其通过对常化加热段加热速率控制、常化冷却段速度控制，并采取合适的抛丸酸洗工艺制度配合，为后工序提供了板面质量优良的原料。该技术方案在不添加附加合金元素、不改变成品退火工艺的情况下，能够提高200-500高斯的磁感B50，铁损实物质量水平提高3-5％。当然，在专利技术方案中，也可以通过优化退火工艺，以进一步改善产品的磁性能，使磁感进一步提高。
再例如：公开号为CN105239005A，公开日为2016年1月13日，名称为“一种高磁导率无取向硅钢及生产方法”的中国专利文献公开了一种高磁导率无取向硅钢，其组分及重量百分比含量为：C≤0.003％，Si：0.1-1.8％，Al≤0.99％，Mn：0.1-0.5％，Sn：0.005-0.08％，Cu≤0.005％，S≤0.005％，该无取 向硅钢的生产步骤包括：炼钢后并真空处理；铸坯后对铸坯加热；热轧后常化；经酸洗后冷轧；成品退火；涂布涂层。该技术方案在满足磁性能的前提下，由于通过真空处理对S及Cu的控制，以确保Cu+S≤0.006％，Cu/S＝0.5-1.7；再通过热轧+常化及特定的成品退火工艺，获得了较为粗大的球形MnS-Cu2S复合夹杂物，使MnS、Cu2S等硫化物得以降低，同时减少冷却应力对磁畴的影响，获得了较多的180℃磁畴或相近磁畴，且占体积比例可达60％以上，从而提高了钢材的磁导率。
发明内容
本发明的目的之一在于提供一种高磁感无取向电工钢板，该高磁感无取向电工钢板基于全新的化学成分设计并配合优化的制造工艺，可以获得优良的机械性能和电磁性能，其屈强比为0.78～0.9，并具有高屈强比、高磁感、低铁损的显著特点。
为了实现上述目的，本发明提出了一种无取向电工钢板，其除含有Fe和不可避免的杂质之外，还含有以质量百分含量计的如下化学元素：
C≤0.003％、Si：1.2～3.0％、Mn：0.1～0.6％、P：0.01～0.15％、Al：0.1～0.4％、Ni：0.05～1.0％；并且满足Si+Al：1.30～3.20％；
所述无取向电工钢板不含有Sn和Sb。
作为另一实施方式，在本发明所述的无取向电工钢板中，所述钢板的成分以质量百分含量计为如下：
C≤0.003％、Si：1.2～3.0％、Mn：0.1～0.6％、P：0.01～0.15％、Al：0.1～0.4％、Ni：0.05～1.0％；余量为Fe和不可避免的杂质；
其中Si+Al：1.30～3.20％。
在本发明所述的高磁感无取向电工钢板中，各化学元素的设计原理如下所述：
C：C元素能够强烈阻碍成品带钢晶粒长大，其容易与Nb、V、Ti等结合形成细小析出物，从而引起损耗增加并产生磁时效。基于此，在本发明所述的高磁感无取向电工钢板中，将C元素的质量百分含量控制为C≤0.003％。
Mn：Mn元素能够与S元素结合生成MnS，其可以有效降低对钢材的磁性危害。当钢中Mn元素含量低于0.1％时，则Mn元素所起到的固S效果较 差；而当钢中Mn元素含量高于0.6％时，则会大幅增加钢材的制造成本。基于此，为了充分发挥Mn元素的有益效果，在本发明所述的无取向电工钢板中，将Mn元素的质量百分含量控制在0.1～0.6％之间。
Si：钢中添加适量的Si元素不仅能够提高钢材的电阻率，还可以有效降低钢材的铁损。当钢中Si元素含量高于3.0％时，会显著降低钢材的磁感，并容易导致冷轧断带；而当钢中Si元素含量低于1.2％时，则又起不到大幅降低钢的铁损作用。基于此，为了发挥Si元素的有益效果，在本发明所述的无取向电工钢板中，将Si元素的质量百分含量控制在1.2～3.0％之间。
Al：Al元素是重要的脱氧元素，当钢中Al元素含量低于0.1％时，起不到良好的脱氧效果；而当钢中Al元素含量超过0.4％时，则会造成连铸浇铸困难，增加钢的制造成本。基于此，为发挥Al元素的有益效果，在本发明所述的无取向电工钢板中，将Al元素的质量百分含量控制在0.1～0.4％之间。
此外，需要注意的是，本发明在控制单一化学元素质量百分含量的同时，还进一步地限定Si、Al元素的质量百分含量之和，即将“Si+Al”的数值范围控制在1.3～3.2％之间。
这是因为，当钢中Si、Al元素的质量百分含量总和低于1.3％时，无法有效提高钢材的强度，并降低钢材的铁损；而当钢中Si、Al元素的质量百分含量总和高于3.2％时，无法有效提高钢材的磁感，需要额外增加常化中间退火，以改善热轧钢板的再结晶显微组织。本发明人发现，将Si、Al元素的质量百分含量的总和控制在1.3～3.2％范围内，可在不采用常化中间退火条件下，获得一种具有高磁感、低铁损、高屈强比的无取向电工钢板。
在本发明所设计的无取向电工钢板中，钢中加入质量百分含量为0.05％～1.0％的Ni元素，优选将Ni元素的范围控制在0.1％～0.5％之间。向钢中加入Ni的目的是：Ni是铁磁性元素，其性质与Fe元素类似，钢中添加0.05％或以上的Ni元素可以明显提高钢材的磁感应强度。但是，钢中同样也不宜添加过量的Ni，Ni的市场价格较高，从经济性的角度出发，需要限制在1.0％或以下。
在一些优选的实施方式中，为了获得更优的实施效果，优选地将Ni元素的质量百分含量控制在0.1～0.5％之间。
此外，在本发明所设计的这种无取向电工钢板中，同时还添加有P元素，向钢中加入P元素可以显著提升钢的强度。当钢中P元素的含量高于0.01％时， 钢材的强度即开始快速升高，但当钢中P元素的质量百分含量高于0.15％之后，会使得钢材的冷轧可轧性显著降低，并会导致钢板出现边裂、断带等异常情况发生。因此，在本发明所述的高磁感无取向电工钢板中，将P元素的质量百分含量控制在0.01～0.15％之间。
在一些优选的实施方式中，为了获得更优的实施效果，优选将P元素的质量百分含量控制在0.01～0.08％之间。
优选地，在本发明所述的无取向电工钢板中，在不可避免的杂质中，S≤0.004％，N≤0.0025％、O≤0.0025％。
在本发明所述的无取向电工钢板中，S元素、N元素和O元素均为无取向电工钢板中的杂质元素，其是钢铁原辅料或生产过程中所引入的杂质元素，在技术条件允许情况下，为了获得性能更好且质量更优的钢材，应尽可能降低钢中杂质元素的含量。
在本发明中，钢中S、N、O元素含量过高，均会对钢材的性能产生不利影响，因此必须严格控制钢中S、N、O元素的质量百分含量，并具体控制为：S≤0.004％，N≤0.0025％、O≤0.0025％。优选地，在本发明所述的无取向电工钢板中，所述钢板的成分以质量百分含量计满足如下中的至少一个：
Ni：0.1～0.5％；
P：0.01～0.08％。
优选地，在本发明所述的无取向电工钢板中，所述钢板的厚度为0.2～0.5mm。
优选地，在本发明所述的无取向电工钢板中，长短轴之比介于1.0～4.0之间的等轴晶数量比例为75％以上。
优选地，在本发明所述的无取向电工钢板中，所述钢板的屈强比为0.78～0.9。
优选地，在本发明所述的无取向电工钢板中：
当1.30≤Si+Al≤2.20％时，铁损P15/50≤3.2W/kg，磁感B50≥1.725T；
当2.20＜Si+Al≤3.20％时，铁损P15/50≤3.0W/kg，磁感B50≥1.695T。
相应地，本发明的另一目的还在于提供一种用于制造上述无取向电工钢板的方法，该制造方法简单可行，其生产操作工艺简便，且热轧和卷取所制备的热轧钢卷无需进行常化中间退火工艺，通过该制造方法可以获得具有优异机械 性能、电磁性能的高磁感无取向电工钢板。
为了达到上述发明目的，本发明提出了一种无取向电工钢板的制造方法，其包括如下步骤：
(1)根据上述钢的成分进行冶炼和铸造，形成连铸坯；
(2)对连铸坯依次进行加热、粗轧、精轧和卷取：其中控制经过粗轧之后的中间坯厚度为20～45mm，经过精轧之后的板材厚度为1.2～2.0mm；在卷取之后在温降过程中的550～650℃范围内进行1～4h时效处理，形成热轧钢卷；
(3)酸洗热轧钢卷；
(4)对热轧钢卷进行一次冷轧，形成钢板；
(5)对钢板进行连续退火；
(6)在钢板表面涂覆绝缘涂层。
在本发明中，发明人优化了钢材的化学成分设计，同时限定了合理的制造工艺，其在冶炼和铸造获得连铸坯后，再依次经过加热、粗轧、精轧和卷取可以优化并获得具有所需显微组织的板材。本发明优化设计了经热轧粗轧的中间坯厚度以及热轧精轧后的板材厚度，并对精轧、卷取之后的热轧钢卷进行时效处理，其配合后续的酸洗、一次冷轧、连续退火以及涂覆绝缘涂层工艺即可有效制备高磁感、高屈强比的无取向电工钢板。
在本发明上述步骤(1)的冶炼和铸造工艺中，冶炼和铸造可以具体包括：“铁水预处理”、“转炉冶炼”、“RH精炼”以及“连续浇铸”这四个步骤。基于这种工艺过程，可以确保获得满足本发明化学成分设计的合格连铸坯。
在本发明中，连铸浇铸成坯之后，依次进行再加热、粗轧、精轧和卷取。其中，根据化学成分控制实绩，并结合电磁性能、机械性能需要，在经过热轧粗轧之后，需要控制经过粗轧之后的中间坯厚度为20～45mm。此时，可以通过优化精轧道次压下率和冷却水分配，能够进一步将热轧精轧之后的板材厚度调整为1.2～2.0mm。
需要说明的是，热轧精轧之后的板材厚度越薄，在同等温度条件下，热轧精轧之后的板材表层、芯部的热流梯度越小，热轧显微组织再结晶就越充分，越有利于形成对成品钢板磁感更有利的等轴晶。此时，在较高的热轧精轧压下率条件下，热轧显微组织中的等轴晶沿轧制方向被不断拉长，长、短轴之比越 来越大，一般会超过4.0。此时，成品钢板的磁各向异性会增大，成品钢板的屈强比会降低。因此，在热轧精轧、卷取之后，需要在降温过程的550～650℃范围进行1～4h时效处理，并在Ni元素的作用下，提高等轴晶沿垂直轧制方向上的生长速度，以降低沿轧制方向上的等轴晶长短轴之比，使介于1.0～4.0之间的等轴晶数量比例≥75％。其中，等轴晶数量比例越高越好，但限于当前技术条件达不到100％。
在本发明中，完成步骤(2)的加热、粗轧、精轧和卷取之后，无须进行常化中间退火工艺，其可以直接进行酸洗、一次冷轧，以轧制成目标厚度0.2～0.5mm。然后，可以优选地在氮、氢混合气氛下850℃～1000℃的温度范围内进行连续退火，连续退火后所获得的钢板进一步涂覆绝缘涂层，即可获得本发明的成品高磁感无取向电工钢板，该高磁感无取向电工钢板的屈强比可以达到0.78～0.90。
优选地，在本发明所述的制造方法中，在步骤(5)中，在氮、氢混合气氛下850℃～1000℃的温度范围内进行连续退火。
优选地，在本发明所述的制造方法中，在步骤(5)中，氮、氢混合气氛中氮气比例为50％～70％，氢气比例为30％～50％。
相较于现有技术，本发明所述的无取向电工钢板及其制造方法具有如下所述的优点以及有益效果：
在本发明所述的无取向电工钢板中，发明人通过全新的化学成分设计，并结合优化的制造工艺，设计了一种全新的高磁感无取向电工钢板。
在本发明中，发明人在合理的化学成分基础上，优化控制了热轧粗轧中间坯厚度以及热轧精轧成品厚度，并对精轧、卷取之后的热轧钢卷进行时效处理，控制钢卷中长短轴之比介于1.0～4.0的等轴晶比例为75％以上，从而改善磁感并提升钢板屈强比。并且，热轧钢卷无需进行常化中间退火工艺，其生产操作工艺简便，所制备的高磁感无取向电工钢板具有高屈强比、高磁感、低铁损的特点。
此外，本发明所设计的这种技术方案能够明显降低炼钢中的杂质元素以及有害夹杂物的控制难度，其钢中无需添加Sn、Sb微量元素，可以有效节约成分，具有良好的推广前景和应用价值。
附图说明
图1示意性地显示了在本发明所述的高磁感无取向电工钢板中的Ni元素含量与成品钢板磁感应强度之间的关系。
图2示意性地显示了在本发明所述的高磁感无取向电工钢板的显微组织中长短轴之比介于1.0～4.0之间的等轴晶数量比例与屈强比之间的关系。
具体实施方式
下面将结合说明书附图和具体的实施例对本发明所述的高磁感无取向电工钢板及其制造方法做进一步的解释和说明，然而该解释和说明并不对本发明的技术方案构成不当限定。
实施例1-6以及对比例1-2
表1列出了实施例1-6的高磁感无取向电工钢板以及对比例1-2的对比钢板的各化学元素的质量百分配比。
表1.(wt％，余量为Fe及除了S、O、N以外的不可避免的杂质)
在本发明中，实施例1-6的高磁感无取向电工钢板以及对比例1-2的对比钢板均采用以下步骤制得：
(1)按照表1所示的化学成分配比进行冶炼和铸造：在炼钢过程中，高炉铁水在依次经过铁水预处理、转炉冶炼、RH精炼和连铸浇铸之后，得到化学成分(按质量百分含量计算)满足本发明要求的合格公称厚度为230mm的连铸坯。
(2)加热、粗轧、精轧和卷取：将获得的连铸坯输入到加热炉中进行加热和升温，加热完成后出炉并进行粗轧、精轧和卷取，其中控制经过粗轧之后 的中间坯厚度为20～45mm，经过精轧之后的板材厚度为1.2～2.0mm；在卷取之后，在温降过程中的550～650℃范围内进行1～4h时效处理，之后自然冷却至室温，以使板材的显微组织中长短轴之比介于1.0～4.0之间的等轴晶数量比例≥75％。
(3)酸洗：经过上述热轧卷取的热轧钢卷不进行常化中间退火，直接进行酸洗。
(4)一次冷轧：经一次冷轧轧制成目标厚度0.2～0.5mm。
(5)连续退火：在氮、氢混合气氛下进行连续退火，并控制连续退火温度范围为850℃～1000℃。
(6)绝缘涂层：在连续退火后的钢板表面涂覆绝缘涂层。
在本发明中，实施例1-6的高磁感无取向电工钢板的化学成分和相关工艺参数均满足本发明设计规范控制要求；而在对比例1-2中，对比例1-2的对比钢板虽然也采用上述工艺步骤制得，但其化学元素成分和/或相关工艺参数存在不符合本发明设计的参数。
需要特别注意的是，在本发明所设计的这种对比例1-2的对比钢板中，其在卷取后，直接自然冷却至室温，并且不进行时效处理。
表2列出了实施例1-6的高磁感无取向电工钢板以及对比例1-2的对比钢板在上述制造工艺流程中的具体工艺参数以及最终的成品厚度。
表2.

需要说明的是，在采用上述工艺步骤制备钢板时，在完成步骤(2)的时效处理后，发明人将实施例1-6和对比例1-2的钢板分别进行了取样，并对各实施例和对比例样品的微观组织进行观察和分析。
通过对于微观组织的观察和分析，可以有效获得各实施例和对比例样品钢板在完成时效处理后的显微组织中长短轴之比介于1.0～4.0之间的等轴晶数量比例，并将相关观察分析结果列于下述表3之中。观察分析测试和统计方法按照国标GB-T 10561 2005执行。
表3列出了实施例1-6和对比例1-2在时效处理后所制备的钢板的显微组织观察分析结果。
表3.
观察发现，在本发明所述的实施例1-6中，卷取之后的钢板在温降过程中完成时效处理后，所获得的钢板的显微组织中长短轴之比介于1.0～4.0之间的 等轴晶数量比例均≥75％，且具体在75-96％之间。
相应地，完成上述显微组织的观察分析后，为了验证最终制备的钢板的性能，发明人将经由上述步骤制备的成品实施例1-6的无取向电工钢板以及对比例1-2的对比钢板分别进行了取样，并对实施例1-6和对比例1-2的样品钢板进行力学性能、磁感B50和铁损P15/50的测试，相关测试结果列于下述表4中。
相关性能测试手段，如下所述：
力学性能试验：基于国家标准GB/T 228.1-2010金属材料拉伸试验第1部分：室温拉伸试验方法进行力学性能测试，测试温度为25℃恒温测试，试样类型为JIS 5#试样，以测得实施例1-6和对比例1-2的样品钢板的屈强比。
磁感性能测试：基于国家标准GB/T 3655-2008，采用爱波斯坦方圈法进行铁损性能测试，测试温度为20℃恒温测试，试样尺寸为30mm×300mm，目标质量为0.5kg，测试参数为B50。由此测得实施例1-6和对比例1-2的样品钢板的磁感B50。
铁损性能测试：基于国家标准GB/T 3655-2008，采用爱波斯坦方圈法进行铁损性能测试，测试温度为20℃恒温测试，试样尺寸为30mm×300mm，目标质量为0.5kg，测试参数为P15/50。由此测得实施例1-6和对比例1-2的样品钢板的铁损P15/50。
表4列出了实施例1-6的高磁感无取向电工钢板以及对比例1-2的对比钢板的屈强比、磁感B50和铁损P15/50的测试结果。
表4.
如上述表4所示，在本发明中，实施例1-6的高磁感无取向电工钢板具有优异的机械性能和电磁性能，其屈强比在0.78-0.90之间，磁感B50在 1.694-1.742T之间，铁损P15/50在1.82-3.14W/kg之间，其综合性能明显优于对比例1-2的钢板。对比例1-2由于没有满足本发明所限定的条件，因此其实施效果也劣于本发明的实施效果。
需要注意的是，在本发明所设计的实施例1-6中，当1.30≤Si+Al≤2.20％时(实施例1、实施例4)，其铁损P15/50均≤3.2W/kg，磁感B50均≥1.725T；
而当2.20＜Si+Al≤3.20％时(实施例2、实施例3、实施例5和实施例6)，其铁损P15/50均≤3.0W/kg，磁感B50均≥1.695T。
结合上述表1、表2、表3和表4所列出的数据，可以进一步对本发明所制备的两个对比例进行分析和说明。
在对比例1中，钢中的Ni含量为0.02％，低于本发明设计下限要求0.05％，且在温降过程中的550～650℃范围内没有进行1～4h时效处理，之后自然冷却至室温，从而使得钢板的显微组织中长短轴之比介于1.0～4.0之间的等轴晶数量之比只有63％，低于本发明设计下限要求75％。相应的，最终所制备的对比例1的这种对比钢材的屈强比仅为0.64，不满足本发明设计要求下限0.78。
在对比例2中，钢中的P含量为0.008％，低于本发明设计下限要求0.01％；钢中的Al含量为0.44％，高于本发明设计上限要求0.4％，且在温降过程中的550～650℃范围内没有进行1～4h时效处理，之后自然冷却至室温，从而使得钢板的显微组织中长短轴之比介于1.0～4.0之间的等轴晶数量之比只有73％，其低于本发明设计下限要求75％。相应的，最终所制备的对比例2的这种对比钢材的屈强比仅为0.75，不满足本发明设计要求下限0.78。
图1示意性地显示了在本发明所述的高磁感无取向电工钢板中的Ni元素含量与成品钢板磁感应强度之间的关系。
如图1所示，对于3％Si的硅钢而言，随着钢中Ni含量的增加，磁感应强度快速升高，并在Ni含量达到0.05％时，磁感应强度可以升高至1.71T或以上。然后，随着钢中Ni含量的继续增加，磁感应强度继续缓慢升高，并维持在1.72-1.73T。
图2示意性地显示了在本发明所述的高磁感无取向电工钢板的显微组织中长短轴之比介于1.0～4.0之间的等轴晶数量比例与屈强比之间的关系。
如图2所示，显微组织中长短轴之比介于1.0～4.0之间的等轴晶尺寸合格比例(等轴晶数量比例)与屈强比正相关。
在本发明所设计的这种高磁感无取向电工钢板中，随着显微组织中长短轴之比介于1.0～4.0之间的等轴晶尺寸合格比例的增加，钢材的屈强比相应的增加。当等轴晶尺寸合格比例达到75％之后，钢材的屈强比会大于0.78，并在0.78-0.90范围内随着钢的化学成分和生产工艺有所波动。
需要说明的是，本发明的保护范围中现有技术部分并不局限于本申请文件所给出的实施例，所有不与本发明的方案相矛盾的现有技术，包括但不局限于在先专利文献、在先公开出版物，在先公开使用等等，都可纳入本发明的保护范围。
此外，本案中各技术特征的组合方式并不限本案权利要求中所记载的组合方式或是具体实施例所记载的组合方式，本案记载的所有技术特征可以以任何方式进行自由组合或结合，除非相互之间产生矛盾。
还需要注意的是，以上所列举的实施例仅为本发明的具体实施例。显然本发明不局限于以上实施例，随之做出的类似变化或变形是本领域技术人员能从本发明公开的内容直接得出或者很容易便联想到的，均应属于本发明的保护范围。

Claims (11)

  1. 一种无取向电工钢板，其特征在于，所述钢板除含有Fe和不可避免的杂质之外，还含有以质量百分含量计的如下化学元素：
    C≤0.003％、Si：1.2～3.0％、Mn：0.1～0.6％、P：0.01～0.15％、Al：0.1～0.4％、Ni：0.05～1.0％；并且满足Si+Al：1.30～3.20％；
    所述无取向电工钢板不含有Sn和Sb。
  2. 如权利要求1所述的无取向电工钢板，其特征在于，所述钢板的成分以质量百分含量计为如下：
    C≤0.003％、Si：1.2～3.0％、Mn：0.1～0.6％、P：0.01～0.15％、Al：0.1～0.4％、Ni：0.05～1.0％；余量为Fe和不可避免的杂质；
    其中Si+Al：1.30～3.20％。
  3. 如权利要求1或2所述的无取向电工钢板，其特征在于，在不可避免的杂质中，S≤0.004％，N≤0.0025％、O≤0.0025％。
  4. 如权利要求1或2所述的无取向电工钢板，其特征在于，所述钢板的成分以质量百分含量计满足如下中的至少一个：
    Ni：0.1～0.5％；
    P：0.01～0.08％。
  5. 如权利要求1或2所述的无取向电工钢板，其特征在于，所述钢板中长短轴之比介于1.0～4.0之间的等轴晶数量比例为75％以上。
  6. 如权利要求1或2所述的无取向电工钢板，其特征在于，所述钢板的厚度为0.2～0.5mm。
  7. 如权利要求1或2所述的无取向电工钢板，其特征在于，所述钢板的屈强比为0.78～0.9。
  8. 如权利要求1或2所述的无取向电工钢板，其特征在于：
    当1.30≤Si+Al≤2.20％时，铁损P15/50≤3.2W/kg，磁感B50≥1.725T；
    当2.20＜Si+Al≤3.20％时，铁损P15/50≤3.0W/kg，磁感B50≥1.695T。
  9. 一种如权利要求1-8中任一项所述的无取向电工钢板的制造方法，其特征在于，所述制造方法包括如下步骤：
    (1)根据权利要求1～4中任一项所示的成分进行冶炼和铸造，形成 连铸坯；
    (2)对连铸坯依次进行加热、粗轧、精轧和卷取：其中控制经过粗轧之后的中间坯厚度为20～45mm，经过精轧之后的板材厚度为1.2～2.0mm；在卷取之后在温降过程中的550～650℃范围内进行1～4h时效处理，形成热轧钢卷；
    (3)酸洗热轧钢卷；
    (4)对热轧钢卷进行一次冷轧，形成钢板；
    (5)对钢板进行连续退火；
    (6)在钢板表面涂覆绝缘涂层。
  10. 如权利要求9所述的制造方法，其特征在于，在步骤(5)中，在氮、氢混合气氛下850℃～1000℃的温度范围内进行连续退火。
  11. 如权利要求9或10所述的制造方法，其特征在于，所述方法不包括在步骤(3)之前对步骤2)中制得的热轧钢卷进行常化中间退火工艺。
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