WO2023131223A1 - 一种磁性能优良的无取向电工钢板及其制造方法 - Google Patents

一种磁性能优良的无取向电工钢板及其制造方法 Download PDF

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WO2023131223A1
WO2023131223A1 PCT/CN2023/070635 CN2023070635W WO2023131223A1 WO 2023131223 A1 WO2023131223 A1 WO 2023131223A1 CN 2023070635 W CN2023070635 W CN 2023070635W WO 2023131223 A1 WO2023131223 A1 WO 2023131223A1
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oriented electrical
electrical steel
steel sheet
steel plate
cold
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English (en)
French (fr)
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李国保
张峰
房现石
王波
吕学钧
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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
    • C22C38/02—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
    • 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
    • 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
    • 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
    • C22C38/04—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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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 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 sheets are usually used to make iron core stators and rotors, so as to be used in products such as motors, generators, compressors, high-speed motors, and drive motors.
  • the publication number is CN103014503A
  • the publication date is April 3, 2013,
  • the Chinese patent document titled "High Magnetic Inductance, Low Iron Loss, Acid Corrosion Resistant, Non-Oriented Silicon Steel and Production Method Without Normalization” points out that adding 0.20 %-0.45% Sn+Cu, using the principle of grain boundary segregation, to improve the texture of the finished strip, so that good magnetic performance can be obtained.
  • both Sn and Cu elements are precious metals, which will significantly increase the manufacturing cost of steel, and Cu elements are also likely to cause related quality defects on the surface of the strip steel. Therefore, in the actual application process, the production process of this technical solution has strict requirements, and the cost performance of the product is relatively low.
  • the Japanese patent documents whose publication numbers are JP-10-183227 and JP-2004-169141 point out that the method of adding an appropriate amount of rare earth and calcium alloy to the steel is used to carry out strong deoxidation and desulfurization of molten steel, which can remove the inclusions of the steel. material and improve the cleanliness of the steel, so that the electromagnetic properties of the finished strip can be improved efficiently and conveniently.
  • the above-mentioned Japanese patent documents also pointed out that by reducing the harmful elements C, S, O, N and Nb, V, Ti in the steel, and at the same time cooperating with the high furnace temperature, high final rolling temperature and high coiling temperature in the hot rolling process , can obtain hot-rolled steel sheets with coarse grains, and is conducive to the coarsening of inclusions, thus playing a good role in promoting the improvement of the magnetic properties of the finished strip.
  • the disadvantage of this technical solution is that the energy consumption of hot rolling is high, and due to the substantial increase of the pre-temperature, the stability of the finishing rolling process is poor due to the migration of the phase transition point, and the high coiling temperature is also easy A red tin defect occurs.
  • the inventor designs and expects to obtain a new non-oriented electrical steel sheet with excellent magnetic properties, which aims to improve the electromagnetic properties of electrical steel, reduce iron loss, and increase magnetic induction.
  • One of the objectives of the present invention is to provide a non-oriented electrical steel sheet with excellent magnetic properties, which aims at improving the electromagnetic properties of the non-oriented electrical steel sheet, reducing iron loss and improving magnetic induction.
  • the present invention proposes a non-oriented electrical steel sheet with excellent magnetic properties, which contains Fe and unavoidable impurities, and also contains the following chemical elements in mass percentage as follows:
  • the mass percentage content of each chemical element is:
  • the C element content in the steel should not be too high.
  • the C element content in the steel is higher than 0.0015%, it will preferentially combine with Nb and Ti to form small-sized inclusions. This in turn leads to increased loss of steel.
  • the mass percentage of the C element is controlled to be 0 ⁇ C ⁇ 0.0015%.
  • Si In the present invention, the inventor designed to add a low content of Si to the non-oriented electrical steel sheet.
  • the mass percentage of Si element When the mass percentage of Si element is higher than 1.8%, it will not only increase the manufacturing cost of the steel, but also significantly deteriorate the magnetic induction of the steel. ; And when the mass percentage of Si is lower than 0.2%, it cannot effectively reduce the iron loss. Based on this, in the non-oriented electrical steel sheet according to the present invention, the mass percentage of Si element is controlled between 0.2% and 1.8%.
  • Mn In the non-oriented electrical steel sheet described in the present invention, adding an appropriate amount of Mn element can combine with S element to form MnS, which is beneficial to control the shape and quantity of inclusions, and can effectively reduce the damage to magnetic properties. Therefore, it is necessary Add more than 0.2% Mn; but when the added Mn content is higher than 0.4%, it will deteriorate the recrystallization texture and reduce the magnetic induction of the steel. Based on this, considering the beneficial effects and adverse effects of the Mn element, in the non-oriented electrical steel sheet according to the present invention, the mass percentage of the Mn element is 0.2-0.4%.
  • the mass percentage content of the Al element is controlled between 0.2% and 0.6%.
  • V In the prior art, in the non-oriented electrical steel sheet, the V element is usually regarded as a harmful element in the steel, and the lower the content, the better, but in the non-oriented electrical steel sheet according to the present invention, the V element is an important element.
  • the use of beneficial elements is adjusted from reducing the V content as much as possible in the past to reduce the content of harmful inclusions as much as possible, and adjusting to consciously adding a certain amount of V content, combined with the adjustment of the production process, by controlling the types of N-containing inclusions, Quantity, to maximize the harmless treatment of Nb, V, Ti content. In this way, the matching and combination of chemical components, which are beneficial to obtaining excellent magnetic properties, and the prerequisites for reasonable control of inclusion types are realized.
  • the mass percentage content of the V element is controlled between 0.002-0.005%.
  • N element is used as a harmful impurity element, and its content should not be too high.
  • the N element content in the steel exceeds 0.002%, it will lead to Nb, V, Ti, Al Such inclusions are greatly increased, which strongly hinders grain growth and deteriorates the magnetic properties of steel.
  • the mass percentage content of N element is controlled to satisfy: N ⁇ 0.002%.
  • Nb element and Ti element are unavoidable impurity elements in the steel, and the impurity elements in the steel should be controlled as low as possible under the premise that the process conditions allow.
  • Nb In the non-oriented electrical steel sheet according to the present invention, when the Nb element content is higher than 0.002%, the NbN-type inclusions in the steel will increase abnormally, which will lead to a significant increase in the iron loss of the finished steel sheet. Therefore, in the present invention, it is necessary to strictly control the impurity element Nb to satisfy: Nb ⁇ 0.002%.
  • the non-oriented electrical steel sheet of the present invention contains N-containing inclusions as its main inclusions, and its N-containing inclusions include single VN, AlN and/or composite VN, AlN , NbN, TiN.
  • single as opposed to “composite” refers to a state in which different inclusions do not mix with each other.
  • the size of the N-containing inclusions is 200-500 nm.
  • VN volume fraction/N-containing inclusion volume fraction 0.75
  • the content of the beneficial element V is controlled between 0.002% and 0.005%, the purpose of which is to generate relatively large VN inclusions instead of smaller NbN and TiN inclusions.
  • the present invention strictly limits the C element content to 0 ⁇ C ⁇ 0.0015%, and in actual production, from the perspective of manufacturing difficulty , can further preferably control the C element to be 0 ⁇ C ⁇ 0.0010%.
  • the inclusions containing N become the main factor restricting the magnetic properties of the finished steel plate.
  • the main principle here is to adjust the V content in the steel to adjust the proportion of VN inclusions in the steel to all N-containing inclusions.
  • the high Al content in the steel which is between 0.2 and 0.6%, a large number of AlN inclusions can be formed in the steel, and after collision, bonding and floating, the size is relatively small AlN inclusions can remain in the steel and combine with VN inclusions to increase the size of the composite inclusions and reduce their damage.
  • another object of the present invention is to provide a manufacturing method for manufacturing the above-mentioned non-oriented electrical steel sheet, the manufacturing method is simple and feasible, and a non-oriented electrical steel sheet with excellent magnetic properties can be obtained through the manufacturing method, which Iron loss P 15/50 ⁇ 4.2W/kg, magnetic induction B 50 ⁇ 1.73T.
  • the present invention proposes a method for manufacturing a non-oriented electrical steel sheet with excellent magnetic properties, which comprises the steps of:
  • the inventor optimized the chemical composition design of the steel and defined a reasonable manufacturing process. After the continuous casting slab obtained by smelting and casting is hot-rolled, it does not need normalizing annealing treatment or bell furnace annealing treatment. ; After directly carrying out pickling and cold rolling, continuous annealing can be carried out in an electromagnetic induction device with rapid heating function, so as to obtain the electromagnetic performance required by the design of the present invention.
  • the present invention there are no special restrictions on the steps of hot rolling, pickling and cold rolling, and the principle is to not increase the manufacturing cost and technical difficulty of the steel.
  • the steel produced by these technical solutions is mostly high-silicon steel, and the content of Si element in the steel is relatively high; Unlike the above-mentioned prior art, the Si element in the steel of the present application is only between 0.2% and 1.8%, which is a medium-low silicon steel, and it does not need the above-mentioned normalization annealing or bell furnace annealing treatment on the basis of the medium-low silicon steel.
  • the steelmaking link of the present invention it is necessary to strictly control the design of the chemical composition of the steel, and focus on controlling the content of the V element in the steel.
  • the steel ingot After smelting and casting, the steel ingot can be obtained; after the steel ingot is hot-rolled, no normalizing annealing treatment is required Or bell furnace annealing treatment, after pickling and rust removal, it can be cold rolled to the target thickness of cold rolling at one time, and continuous annealing treatment can be carried out in the electromagnetic induction device with rapid heating function, and the annealing atmosphere can be controlled It is a mixed gas of H2 and N2 .
  • the electromagnetic induction device with rapid heating function is not limited to longitudinal magnetic or transverse magnetic, but its heating capacity needs to meet the requirements of rapidly heating the cold-rolled steel plate for continuous annealing to the target temperature.
  • the target soaking temperature can generally be 500-1100° C.
  • the starting temperature of heating can be a temperature below the soaking temperature, such as room temperature.
  • the present invention controls the temperature rise rate of the cold-rolled steel plate to be 50-5000°C/s, which is much higher than the temperature rise rate of 1-30°C/s in conventional continuous annealing equipment.
  • the heating rate can also be controlled to be 80-550°C/s.
  • the present invention uses an electromagnetic induction heating device with rapid heating and temperature rise functions for continuous annealing.
  • rapid heating is to effectively inhibit the recovery of cold-rolled steel sheets during continuous annealing, so that the residual deformation energy storage of cold-rolled steel sheets before recrystallization can be significantly increased, which can lead to the accumulation and increase of nucleation driving force, And promote nucleation and large-angle grain boundary migration.
  • the preferred orientation of crystal nuclei is also reduced, and finally the strength of ⁇ 111>//ND recrystallization texture components can be reduced. Therefore, adopting the continuous annealing method can make the steel obtain higher magnetic induction and lower iron loss.
  • the heating rate of rapid heating is too slow, and the heating rate is lower than 50°C/s, the stored energy of cold rolling deformation is released too quickly, which is not conducive to the subsequent favorable texture control; when the heating rate of rapid heating is too fast, the heating rate is higher than When the temperature is 5000°C/s, the requirements for equipment capacity are too high, the cost is expensive, and it will cause the cold-rolled strip to stay in the high temperature stage for too long, and the uniformity of the grain structure is poor.
  • the target soaking temperature is 500-1100°C.
  • step (5) the cold-rolled steel sheet is rapidly heated to the target soaking temperature at a heating rate of 80-550° C./s.
  • step (2) the casting slab is controlled to be in the furnace for 120-360 minutes during hot rolling, the starting rolling temperature is 1000-1250 °C, and the finishing rolling temperature is 650-1000 °C. °C, the coiling temperature is 550-950 °C.
  • step (2) the target thickness of the hot-rolled steel sheet is controlled to be 0.8-3.5 mm;
  • the non-oriented electrical steel sheet with excellent magnetic properties and its manufacturing method according to the present invention have the following advantages and beneficial effects:
  • the present invention takes the V element as a beneficial element in the steelmaking process, and consciously adjusts the content of the V element.
  • the inventor has adopted an optimized design for the distribution ratio of chemical elements, and the continuous casting slab obtained by smelting and casting does not need normalizing annealing or bell furnace after hot rolling Annealing, after pickling and cold rolling, rapid heating is carried out to ensure that the cold-rolled steel plate is rapidly heated to the target soaking temperature at a relatively high heating rate, so that the electromagnetic properties required by the design of the present invention can be obtained.
  • the design idea of the chemical elements of the present invention is completely different from the prior art, and its manufacturing method is simple and feasible.
  • the non-oriented electrical steel sheet has the characteristics of high magnetic induction and low iron loss, and its iron loss P 15/50 ⁇ 4.2W/kg , magnetic induction B 50 ⁇ 1.73T.
  • Figure 1 schematically shows the relationship between the volume fraction of VN compounds in the non-oriented electrical steel sheet of the present invention/the volume fraction of N-containing inclusions in the steel and the iron loss P 15/50 of the finished steel sheet.
  • Fig. 2 schematically shows the relationship between the rapid heating temperature rise rate and the magnetic induction B 50 of the finished steel sheet in the non-oriented electrical steel sheet according to the present invention.
  • Fig. 3 is a photo of the microstructure of the finished non-oriented electrical steel sheet of Example 3.
  • FIG. 4 is a photograph of the microstructure of the comparative steel of Comparative Example 2.
  • Table 1 lists the mass percentage ratio of each chemical element in the non-oriented electrical steel sheets of Examples 1-6 and the comparative steel sheets of Comparative Examples 1-3.
  • Hot rolling during hot rolling, the casting time in the furnace is controlled to be 120 to 360 minutes, the starting rolling temperature is controlled to be 1000 to 1250 °C, the final rolling temperature is controlled to be 650 to 1000 °C, and the coiling temperature is controlled to be 550 to 950 °C.
  • the hot rolling is completed in 2 to 8 passes, and the target thickness of the hot rolled steel plate is controlled to be 0.8 to 3.5mm; the steel coil after hot rolling is not subjected to normalization annealing or bell furnace annealing, but directly proceeds to the next step.
  • Cold-rolling the pickled steel plate cold-rolling the pickled steel plate to a cold-rolled target thickness of 0.50 mm at one time.
  • Continuous annealing The cold-rolled steel plate is rapidly heated by continuous annealing equipment with an electromagnetic induction rapid heating device. From room temperature, the cold-rolled steel plate is rapidly heated to 500-1100°C at a heating rate of 50-5000°C/s. °C target soaking temperature, and soaking for a period of time, such as 10-120s; wherein, the heating rate can be further preferably controlled between 80-550°C/s; during the annealing process, the annealing atmosphere is controlled to be H2 and N2 mixed gas.
  • Table 2 lists the specific process parameters of the non-oriented electrical steel sheets of Examples 1-6 and the comparative steel sheets of Comparative Examples 1-3 in the above-mentioned manufacturing process flow.
  • the non-oriented electrical steel sheets of the final finished product examples 1-6 and the comparison steel sheets of comparative examples 1-3 were sampled respectively, and the steel sheet samples of examples 1-6 and comparative examples 1-3 were observed and analyzed, and observed It is found that there are inclusions in the steels of each embodiment and comparative examples, and the main body of the inclusions is inclusions containing N; through further analysis and testing, the N-containing inclusions in the steel plates of each embodiment and comparative examples can be obtained respectively The average size, as well as the specific components, and the relevant observation and analysis results are listed in Table 3 below.
  • Magnetic induction B 50 test Based on the national standard GB/T 3655-2008, the iron loss performance test is carried out using the Epstein square circle method, 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 the magnetic induction B 50 of the steel plates of each embodiment and comparative example.
  • Iron loss P 15/50 test Based on the national standard GB/T 3655-2008, the iron loss performance test is carried out using the Epstein square circle method, 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 the iron loss P 15/50 of each embodiment and comparative example.
  • Table 4 lists the test results of magnetic induction B 50 and iron loss P 15/50 of the non-oriented electrical steel sheets of Examples 1-6 and the comparative steel sheets of Comparative Examples 1-3.
  • the magnetic induction B 50 of the non-oriented electrical steel sheets of Examples 1-6 is between 1.74-1.80T, and the iron loss P 15/50 is between 3.2-4.2W/kg , which are significantly better than the comparison steel plates of Comparative Examples 1-3.
  • Comparative examples 1-3 do not meet the conditions defined by the technical solution, so their implementation effects are also inferior to those of the present case.
  • Fig. 1 schematically shows the relationship between the VN/N-containing inclusion volume fraction ratio in the steel and the iron loss P 15/50 of the finished steel sheet in the non-oriented electrical steel sheet according to the present invention.
  • the ratio of VN/N-containing inclusion volume fraction in the non-oriented electrical steel sheet increases, and the iron loss P 15/50 of the finished steel sheet decreases no matter for conventional heating or rapid heating, but The iron loss P 15/50 of the finished steel plate corresponding to rapid heating decreases significantly faster, and when the ratio of the volume fraction of VN/N-containing inclusions in the steel reaches 85% or above, for rapid heating, the finished steel plate iron
  • the loss P 15/50 can be lower than 4.2W/kg, which meets the design requirements of the present invention.
  • Fig. 2 schematically shows the relationship between the rapid heating temperature rise rate and the magnetic induction B 50 of the finished steel sheet in the non-oriented electrical steel sheet according to the present invention.
  • the magnetic induction of the finished non-oriented electrical steel sheet gradually increases, and the magnetic induction remains stable in the range of 50-5000 ° C / s, which meets the requirements of the design of the present invention
  • the lower limit is 1.73T control requirements, and after exceeding 5000°C/s, the magnetic induction of the finished non-oriented electrical steel sheet deteriorates rapidly, which is lower than the 1.73T control lower limit, which cannot meet the iron loss control requirements of the invention design.
  • Fig. 3 is a photo of the microstructure of the finished non-oriented electrical steel sheet of Example 3.
  • the microstructure of the non-oriented electrical steel sheet has been completely recrystallized, and the recrystallized grains are relatively uniform equiaxed grains, and the grain size is coarse and well developed. .
  • FIG. 4 is a photograph of the microstructure of the comparative steel of Comparative Example 2.

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Abstract

本发明公开了一种磁性能优良的无取向电工钢板，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下述各化学元素：0＜C≤0.0015％；Si：0.2～1.8％；Mn：0.2～0.4％；Al：0.2～0.6％；V：0.002～0.005％；N＜0.002％。此外本发明还公开了一种制造上述磁性能优良的无取向电工钢板的制造方法，其包括步骤：(1)冶炼和铸造；(2)热轧，热轧之后的钢卷不进行常化退火或罩式炉退火而直接进行下一步骤；(3)酸洗；(4)冷轧；(5)连续退火：将冷轧钢板以50～5000℃/s的升温速率快速加热至目标均热温度。

Description

一种磁性能优良的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
在现有技术中，无取向电工钢板通常被用于制作铁芯的定子、转子，以应用于马达、发电机、压缩机以及高速电机、驱动电机等产品中。
但近年来，随着用户市场对于高效、节能、降耗需求的日益增加，现有的无取向电工钢板已经逐渐难以满足市场需求；由此，为了满足市场对于无取向电工钢板所提出的新技术指标要求，亟需研发一种具有更高磁感以及更低铁损的无取向电工钢板。
为了使无取向电工钢板能够获得尽可能好的电磁性能，当前已有部分研究人员进行了大量的研究，并取得了一定的研究成果，但是实际应用效果均不是很理想：
例如，公开号为CN103014503A，公开日2013年4月3日，名称为“无需常化的高磁感低铁损耐酸蚀无取向硅钢及生产方法”的中国专利文献指出，采用向钢中加入0.20％-0.45％的Sn+Cu，利用晶界偏聚的原理，以改善成品带钢的织构形态，从而可以获得良好的磁感性能。但是，Sn、Cu元素均属于贵重金属，会显著增加钢的制造成本，并且Cu元素还容易使带钢表面产生相关的质量缺陷。因此，在实际应用过程中，该技术方案生产过程要求严格，产品的性价比相对较低。
再例如，公开号为特开平10-183227和特开2004-169141的日本专利文献指出，采用向钢中加入适量稀土、钙合金的方式，对钢液进行强脱氧、脱硫，能够去除钢的夹杂物和改善钢的洁净度，从而可以高效、便捷的提高成品带钢的电磁性能。此外，上述日本专利文献还指出，通过降低钢中的有害元素C、S、O、N和Nb、V、Ti，同时配合热轧过程中的高出炉温度、高终轧温度和 高卷取温度，可以获得晶粒粗大的热轧钢板，并且有利于夹杂物的粗化，从而对成品带钢的磁性能改善起到良好的促进作用。但是，这种技术方案的不利之处在于，热轧能耗高，并且由于前置温度的大幅提高，由于相变点的迁移，精轧轧制过程稳定性较差，高卷取温度还容易产生红铁皮缺陷。
基于此，不同于上述现有的技术方案，发明人设计并期望获得一种新的磁性能优良的无取向电工钢板，其旨在提高电工钢的电磁性能，降低铁损、提高磁感。
发明内容
本发明的目的之一在于提供一种磁性能优良的无取向电工钢板，其旨在提高无取向电工钢板的电磁性能，降低铁损、提高磁感。
为了实现上述目的，本发明提出了一种磁性能优良的无取向电工钢板，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下述各化学元素：
0＜C≤0.0015％；Si：0.2～1.8％；Mn：0.2～0.4％；Al：0.2～0.6％；V：0.002～0.005％；N＜0.002％。
进一步地，在本发明所述的无取向电工钢板中，其各化学元素质量百分含量为：
0＜C≤0.0015％；Si：0.2～1.8％；Mn：0.2～0.4％；Al：0.2～0.6％；V：0.002～0.005％；N＜0.002％；余量为Fe和不可避免的杂质。
在本发明所述的无取向电工钢板中，各化学元素的设计原理如下所述：
C：在本发明所述的无取向电工钢板中，钢中C元素含量不宜过高，当钢中C元素量高于0.0015％时，会优先与Nb、Ti结合，形成尺寸细小的夹杂物，进而导致钢的损耗增加。基于此，为了充分发挥C元素的有益效果，在本发明所述的无取向电工钢板中，控制C元素的质量百分含量为0＜C≤0.0015％。
Si：在本发明中，发明人设计向无取向电工钢板添加中低含量的Si，当Si元素的质量百分比高于1.8％时，不但会增加钢的制造成本，还会显著劣化钢材的磁感；而当Si的质量百分比低于0.2％时，则又起不到有效降低铁损的作用。基于此，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0.2～1.8％之间。
Mn：在本发明所述的无取向电工钢板中，添加适量的Mn元素能够和S 元素的结合生成MnS，有利于控制夹杂物形态、数量，进而可以有效减少对磁性能的危害，因此有必要加入0.2％以上的Mn；但当加入的Mn含量高于0.4％，则会使再结晶织构劣化，降低钢的磁感。基于此，考虑到Mn元素有益效果以及不利影响，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为0.2～0.4％。
Al：在本发明所述的无取向电工钢板中，当钢中加入的Al含量高于0.6％时，会显著劣化钢材；而当钢中加入的Al含量低于0.2％时，则又起不到良好的降低铁损的效果。基于此，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0.2～0.6％之间。
V：在现有技术中，无取向电工钢板中通常将V元素作为钢中的有害元素而希望其含量越低越好，然而在本发明所述的无取向电工钢板中，V元素作为重要的有益元素使用，由以往的尽可能降低V含量，以尽可能的降低有害夹杂物的含量，调整为有意识的添加一定量的V含量，并结合生产工艺调整，通过控制含N夹杂物的种类、数量，最大限度的实现了Nb、V、Ti含量的无害化处理。这样，就实现了有益于获得优良磁性能的化学成分搭配、组合，以及合理的夹杂物种类控制先决条件。
在本技术方案中，当钢中V元素含量低于0.002％时，则并不能起到良好的固C、N效果，其夹杂物种类多、尺寸小；而当钢中V元素含量过高，V元素含量超过0.005％时，将会导致V的C、N夹杂物大大增加，强烈阻碍晶粒长大，劣化钢材的磁性。由此，为了发挥V元素的有益效果，在本发明所述的无取向电工钢板中，将V元素的质量百分含量控制在0.002～0.005％之间。
N：在本发明所述的无取向电工钢板中，N元素作为有害杂质元素，其含量不宜过高，当钢中N元素含量超过0.002％时，将会导致N的Nb、V、Ti、Al等夹杂物大大增加，强烈阻碍晶粒长大，劣化钢的磁性。基于此，在本发明所述的无取向电工钢板中，控制N元素的质量百分含量满足：N＜0.002％。
进一步地，在本发明所述的无取向电工钢板中，其中在不可避免的杂质中，Nb≤0.002％，Ti≤0.002％。
在本发明上述技术方案中，Nb元素和Ti元素均是钢中不可避免的杂质元素，在工艺条件允许的前提下，应控制钢中杂质元素尽可能的低。
Nb：在本发明所述的无取向电工钢板中，当Nb元素含量高于0.002％时， 将使钢中的NbN类夹杂物异常增加，进而导致成品钢板的铁损大幅升高。因此，在本发明中，需要严格控制杂质元素Nb满足：Nb≤0.002％。
Ti：在本发明所述的无取向电工钢板中，当Ti元素含量高于0.002％时，将使钢中的含TiN类夹杂物异常增加，进而导致成品钢板的铁损大幅升高。因此，在本发明中，需要严格控制杂质元素Ti满足：Ti≤0.002％。
进一步地，在本发明所述的无取向电工钢板中无取向电工钢板包含含N的夹杂物作为其主体夹杂物，其含N的夹杂物包括单个的VN、AlN和/或复合的VN、AlN、NbN、TiN。
术语“单个”相对于“复合”，其是指不同夹杂物之间不互相掺杂的状态。
进一步地，在本发明所述的无取向电工钢板中，含N的夹杂物的尺寸为200～500nm。
进一步地，在本发明所述的无取向电工钢板中，VN体积分数/含N的夹杂物体积分数≥0.85。
在本发明中，控制有益元素V的含量在0.002～0.005％之间，其目的是为了尽可能的生成尺寸相对较大的VN夹杂物，而不是尺寸更为细小的NbN、TiN夹杂物。为了避免生成尺寸细小的NbN、TiN以及含C类Nb、V、Ti夹杂物等，本发明严格限制C元素含量满足0＜C≤0.0015％，且在实际生产中，从生产制造难度的角度出发，可以进一步优选地控制C元素为0＜C≤0.0010％。在上述这种化学元素条件下，且钢中含有0.2～0.6％的Al含量条件下，含N的夹杂物就成为了制约成品钢板磁性能的主要因素。
因此，在本发明中，需要优选地限制钢中的VN体积分数/含N的夹杂物体积分数≥0.85，以减少非VN类夹杂物的出现。这里主要是以调整钢中的V含量为控制原则，来调整钢中VN夹杂物占所有含N的夹杂物的比例。除此之外，由于钢中的Al含量很高，其含量在0.2～0.6％之间，因此，钢中可以形成数量众多的AlN夹杂物，在经过碰撞、结合和上浮之后，尺寸相对较小的AlN夹杂物可以残留在钢中，并与VN夹杂物进行结合，从而提高其复合夹杂物的尺寸，减少其危害。
由此，当钢中形成的VN夹杂物数量太少，则起不到复合AlN夹杂物的效果，此时AlN夹杂物尺寸小、不能上浮去除而残留在钢种；相应地，当VN夹杂物数量太多时，则除了与AlN夹杂物复合之外，单个的AlN也会残留在钢 中，随着其数量的增加，危害性增大。
进一步地，在本发明所述的无取向电工钢板中，其铁损P 15/50≤4.2W/kg，磁感B 50≥1.73T。
相应地，本发明的另一目的还在于提供一种用于制造上所述的无取向电工钢板的制造方法，该制造方法简单可行，通过该制造方法可以获得磁性优良的无取向电工钢板，其铁损P 15/50≤4.2W/kg，磁感B 50≥1.73T。
为了达到上述发明目的，本发明提出了一种磁性能优良的无取向电工钢板的制造方法，其包括步骤：
(1)冶炼和铸造；
(2)热轧，热轧之后的钢卷不进行常化退火或罩式炉退火而直接进行下一步骤；
(3)酸洗，获得酸洗后的钢板；
(4)冷轧酸洗后的钢板，获得冷轧钢板；
(5)连续退火：将冷轧钢板以50～5000℃/s的升温速率快速加热至目标均热温度。
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，其冶炼和铸造获得的连铸坯经过热轧之后，不需要进行常化退火处理或罩式炉退火处理；在直接进行酸洗、冷轧之后，可以用带有快速加热功能的电磁感应装置中进行连续退火，从而可以获得本发明设计要求达到的电磁性能。其中，本发明中，对热轧、酸洗和冷轧环节没有特殊的限制要求，以不增加钢的制造成本和技术难度为原则。
需要说明的是，在现有技术中，虽然也有一些技术方案可以不进行常化退火或罩式炉退火处理，但这些技术方案制备的钢材多为高硅钢，其钢中Si元素含量较高；而不同于上述现有技术，本申请钢中Si元素仅在0.2～1.8％之间，其为中低硅钢，其在中低硅钢的基础上无需进行上述常化退火或罩式炉退火处理。
在本发明的炼钢环节中，需要严格控制钢的化学成分设计，并着重控制钢中V元素的含量，经冶炼和铸造后可以获得钢锭；该钢锭经过热轧之后，无需进行常化退火处理或者罩式炉退火处理，在经过酸洗、除锈之后，可以一次性冷轧至冷轧目标厚度，并在带有快速加热功能的电磁感应装置中，进行连续退 火处理，且可以控制退火气氛为H 2和N 2的混合气体。
在本发明上述制造方法的步骤(5)中，带有快速加热功能的电磁感应装置为纵磁或横磁不限，但其加热能力则需要满足将进行连续退火的冷轧钢板快速加热至目标均热温度，其目标均热温度一般可以为500～1100℃，加热的起始温度可以是均热温度以下的温度，例如室温。其中，本发明控制冷轧钢板的升温速率为50～5000℃/s，其大大高于常规的连续退火设备升温速率1～30℃/s。但是，在某些实施方式中，根据成品钢板的生产和实物质量需要，也可控制升温速率为80～550℃/s。
与常规的采用燃气和(或)电加热、慢速升温连续退火方式相比(一般低于30℃/s)，本发明采用了带有快速加热、升温功能的电磁感应加热装置进行连续退火，以实现在较短的时间内将冷轧钢板快速加热至设定目标均热温度。采用快速加热升温的目的是，能够有效抑制冷轧钢板在连续退火过程中的回复，使冷轧钢板在发生再结晶之前的剩余形变储能显著增加，从而可以导致形核驱动力积聚、增加，并促进形核和大角晶界迁移。同时，也降低了晶核择优位向，最终能够降低<111>//ND再结晶织构组分强度。因而，采用该连续退火方式可以使钢材获得更高的磁感，更低的铁损。
需要说明的是，在冷轧钢板的快速加热连续退火过程中，为了进一步增加形核长大驱动力，改善和控制最终的再结晶效果，确保在经过连续退火之后，晶粒组织粗大、均匀，有害的晶粒位向比例少，还需要合适的限制快速加热退火的升温速率在50～5000℃/s之间。当快速加热升温速率太慢，升温速率低于50℃/s时，则冷轧变形的储能释放太快，不利于后续有利织构的控制；当快速加热升温速率太快，升温速率高于5000℃/s时，则对设备能力的要求太高，造价昂贵，并且会导致冷轧带钢在高温阶段的停留时间过长，晶粒组织均匀性差。
进一步地，在本发明所述的制造方法中，在步骤(5)中，目标均热温度为500～1100℃。
进一步地，在本发明所述的制造方法中，在步骤(5)中，将冷轧钢板以80～550℃/s的升温速率快速加热至目标均热温度。
进一步地，在本发明所述的制造方法中，在步骤(2)中，热轧时控制铸坯在炉时间为120～360min，开轧温度为1000～1250℃，终轧温度为650～1000℃，卷取温度为550～950℃。
进一步地，在本发明所述的制造方法中，在步骤(2)中，控制热轧钢板目标厚度为0.8～3.5mm；在步骤(4)中一次性冷轧至冷轧目标厚度。
相较于现有技术，本发明所述的磁性能优良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：
与传统思维方式不同，本发明在炼钢过程中，将V元素作为有益元素，有意识的调整了V元素的含量。
在本发明所述的无取向电工钢板中，发明人对化学元素成分配比采用了优化设计，其经冶炼和铸造制得的连铸坯经过热轧之后，无需进行常化退火或罩式炉退火，在直接进行酸洗、冷轧之后，进行快速加热，确保冷轧钢板以较高的升温速率快速加热至目标均热温度，从而可以获得本发明设计要求达到的电磁性能。
本发明的化学元素设计思路与现有技术截然不同，其制造方法简单可行，制得的无取向电工钢板具有高磁感以及低铁损的特性，其铁损P 15/50≤4.2W/kg，磁感B 50≥1.73T。
附图说明
图1示意性地显示了在本发明所述的无取向电工钢板中VN化物体积分数/钢中的含N的夹杂物体积分数与成品钢板铁损P 15/50之间的关系。
图2示意性地显示了在本发明所述的无取向电工钢板中快速加热升温速率与成品钢板磁感B 50之间的关系。
图3为实施例3的成品无取向电工钢板的显微组织照片。
图4为对比例2的对比钢材的显微组织照片。
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磁性能优良的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1-3
表1列出了实施例1-6的无取向电工钢板以及对比例1-3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Nb、Ti以外的其他不可避免的杂质)
Figure PCTCN2023070635-appb-000001
实施例1-6的无取向电工钢板以及对比例1-3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，优先进行脱碳至设计目标，然后进行脱氧、合金化，根据钢中C、N、Nb、Ti含量，调整V含量至目标设计，以获得满足化学成分设计要求的钢液，而后按照规定尺寸浇铸成钢锭。
(2)热轧：热轧时控制铸坯在炉时间为120～360min，控制开轧温度为1000～1250℃，控制终轧温度为650～1000℃，控制卷取温度为550～950℃，分2～8个道次完成热轧，并控制热轧钢板目标厚度为0.8～3.5mm；热轧之后的钢卷不进行常化退火或罩式炉退火而直接进行下一步骤。
(3)酸洗，获得酸洗后的钢板。
(4)冷轧酸洗后的钢板：将酸洗后的钢板一次性冷轧至0.50mm的冷轧目标厚度。
(5)连续退火：采用带有电磁感应快速加热装置的连续退火设备对冷轧钢板进行快速加热，自室温起，将冷轧钢板以50～5000℃/s的升温速率快速加热至500～1100℃的目标均热温度，并均热保温一段时间，例如10-120s；其中，升温速率可以进一步优选地控制在80～550℃/s之间；在退火过程中，控制退火气氛为H 2和N 2的混合气体。
需要说明的是，在本发明中，实施例1-6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1-3中，具有至少一个化学成分或工艺参数不满足本发明设计要求。
表2列出了实施例1-6的无取向电工钢板以及对比例1-3的对比钢板在上述制造工艺流程中的具体工艺参数。
表2.
Figure PCTCN2023070635-appb-000002
将最终制得的成品实施例1-6的无取向电工钢板以及对比例1-3的对比钢板分别取样，并针对实施例1-6和对比例1-3的钢板样品进行观察和分析，观察发现各实施例和对比例的钢中均具有夹杂物，且其夹杂物的主体为含N的夹杂物；通过进一步地分析测试，可以分别获得各实施例和对比例钢板中的含N夹杂物的平均尺寸，以及具体成分，相关观察分析结果列于下述表3之中。
表3.
Figure PCTCN2023070635-appb-000003
相应地，完成上述夹杂物的观察分析后，可以将最终制得的实施例1-6的无取向电工钢板以及对比例1-3的对比钢板再次取样，并对各实施例和对比例 样品钢板进行磁感B 50和铁损P 15/50的测试，所得的测试结果列于下述表4中。
相关性能测试手段，如下所述：
磁感B 50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，测试参数为各实施例和对比例钢板的磁感B 50。
铁损P 15/50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，测试参数为各实施例和对比例的铁损P 15/50。
表4列出了实施例1-6的无取向电工钢板以及对比例1-3的对比钢板的磁感B 50和铁损P 15/50测试结果。
表4.
Figure PCTCN2023070635-appb-000004
如上述表4所示，在本发明中，实施例1-6的无取向电工钢板的磁感B 50在1.74-1.80T之间，铁损P 15/50在3.2-4.2W/kg之间，其均明显优于对比例1-3的对比钢板。对比例1-3由于没有满足本技术方案所限定的条件，因此其实施效果也劣于本案的实施效果。
图1示意性地显示了在本发明所述的无取向电工钢板中VN/钢中的含N的夹杂物体积分数之比与成品钢板铁损P 15/50之间的关系。
如图1所示，无取向电工钢板中VN/钢中的含N的夹杂物体积分数之比增加，无论是对于常规加热还是快速加热，成品钢板的铁损P 15/50均在降低，但快速加热对应的成品钢板铁损P 15/50下降速率明显更快，并在VN/钢中的含N的夹杂物体积分数之比达到85％或以上时，对于快速加热而言，成品钢板铁损P 15/50可以低于4.2W/kg，达到本发明的设计要求。
图2示意性地显示了在本发明所述的无取向电工钢板中快速加热升温速率与成品钢板磁感B 50之间的关系。
如图2所示，随着无取向电工钢板中快速加热升温速率的增加，成品无取向电工钢板磁感逐渐增加，并在50-5000℃/s范围内磁感保持稳定，满足本发明设计的下限1.73T控制要求，而在超过5000℃/s之后，成品无取向电工钢板磁感快速劣化，低于1.73T控制下限，不能满足发明设计的铁损控制要求。
图3为实施例3的成品无取向电工钢板的显微组织照片。
如图3所示，在实施例3的实施方式中，无取向电工钢板的显微组织已经实现了完全再结晶，再结晶晶粒均为比较匀称的等轴晶，且晶粒尺寸粗大、发达。
图4为对比例2的对比钢材的显微组织照片。
如图4所示，在对比例2的实施方式中，对比钢材的显微组织已经实现了完全再结晶，但已经实现再结晶的晶粒等轴晶比例低、尺寸细小，且其晶粒尺寸比较分散；晶粒尺寸较大的晶粒为异常长大的“岛状晶粒”。
需要说明的是，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替换的，均应属于本发明权利要求的保护范围。

Claims (10)

  1. 一种无取向电工钢板，所述无取向电工钢板含有Fe和不可避免的杂质，其特征在于，其还含有质量百分含量如下的下述各化学元素：
    0＜C≤0.0015％；Si：0.2～1.8％；Mn：0.2～0.4％；Al：0.2～0.6％；V：0.002～0.005％；N＜0.002％。
  2. 如权利要求1所述的无取向电工钢板，其特征在于，所述无取向电工钢板的各化学元素质量百分含量为：
    0＜C≤0.0015％；Si：0.2～1.8％；Mn：0.2～0.4％；Al：0.2～0.6％；V：0.002～0.005％；N＜0.002％；余量为Fe和不可避免的杂质。
  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，Nb＜0.002％，Ti＜0.002％。
  4. 如权利要求1或2所述的无取向电工钢板，其特征在于，所述无取向电工钢板包含含N的夹杂物作为其主体夹杂物，所述含N的夹杂物包括单个的VN、AlN和/或复合的VN、AlN、NbN、TiN。
  5. 如权利要求4所述的无取向电工钢板，其特征在于，含N的夹杂物的尺寸为200～500nm。
  6. 如权利要求4所述的无取向电工钢板，其特征在于，VN体积分数/含N的夹杂物体积分数≥0.85。
  7. 如权利要求1或2所述的无取向电工钢板，其特征在于，所述无取向电工钢板的铁损P 15/50≤4.2W/kg，磁感B 50≥1.73T。
  8. 一种如权利要求1-7中任意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)冶炼和铸造；
    (2)热轧，热轧之后的钢卷不进行常化退火或罩式炉退火而直接进行下一步骤；
    (3)酸洗，获得酸洗后的钢板；
    (4)冷轧所述酸洗后的钢板，获得冷轧钢板；
    (5)连续退火：将冷轧钢板以50～5000℃/s的升温速率加热至目标均热温度。
  9. 如权利要求8所述的制造方法，其特征在于，所述步骤(5)中的条件满足以下的至少之一：
    目标均热温度为500～1100℃；
    将冷轧钢板以80～550℃/s的升温速率加热至目标均热温度。
  10. 如权利要求8所述的制造方法，其特征在于，所述步骤(2)中的条件满足以下的至少之一：
    热轧时控制铸坯在炉时间为120～360min，开轧温度为1000～1250℃，终轧温度为650～1000℃，卷取温度为550～950℃；
    控制热轧钢板目标厚度为0.8～3.5mm，和/或；
    在步骤(4)中，将所述酸洗后的钢板一次性冷轧至冷轧目标厚度。
PCT/CN2023/070635 2022-01-07 2023-01-05 一种磁性能优良的无取向电工钢板及其制造方法 WO2023131223A1 (zh)

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