WO2012068830A1 - 一种磁性能优良的取向硅钢生产方法 - Google Patents

一种磁性能优良的取向硅钢生产方法 Download PDF

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WO2012068830A1
WO2012068830A1 PCT/CN2011/073419 CN2011073419W WO2012068830A1 WO 2012068830 A1 WO2012068830 A1 WO 2012068830A1 CN 2011073419 W CN2011073419 W CN 2011073419W WO 2012068830 A1 WO2012068830 A1 WO 2012068830A1
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Prior art keywords
annealing
martensite
steel
normalization
oriented silicon
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PCT/CN2011/073419
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English (en)
French (fr)
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吴美洪
靳伟忠
孙焕德
杨国华
沈侃毅
黄杰
胡德扬
李国保
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宝山钢铁股份有限公司
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Application filed by 宝山钢铁股份有限公司 filed Critical 宝山钢铁股份有限公司
Priority to JP2013538037A priority Critical patent/JP5845275B2/ja
Priority to US13/988,738 priority patent/US20130299049A1/en
Priority to MX2013005869A priority patent/MX351880B/es
Priority to RU2013127584/02A priority patent/RU2552792C2/ru
Priority to EP11842864.8A priority patent/EP2644715B1/en
Priority to KR20137013154A priority patent/KR101512090B1/ko
Publication of WO2012068830A1 publication Critical patent/WO2012068830A1/zh

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Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
    • B21B37/48—Tension control; Compression control
    • 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
    • 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
    • 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
    • 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
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to a method for producing oriented silicon steel, and more particularly to a method for producing oriented silicon steel having excellent magnetic properties. Background technique
  • Oriented silicon steel is an important soft magnetic alloy that is indispensable in the power, electronics and military industries. It is mainly used as transformer cores, generators and large motors. Excellent magnetic properties are required, especially low iron loss.
  • Oriented silicon steel uses secondary recrystallization technology to make Goss texture (Goss texture: ⁇ 110 ⁇ crystal plane parallel rolling surface, ⁇ 001> crystal grain parallel direction rolling) abnormal grain growth, annexation of other orientation crystal Excellent grain rolling properties are obtained after the granules.
  • the traditional high magnetic induction oriented silicon steel production method is as follows:
  • the slab is heated to a temperature of 1350 ° C ⁇ 1400 ° C in a special high-temperature heating furnace, and the insulation is maintained for more than 1 h, so that the favorable inclusion A1N, MnS or MnSe is fully dissolved, and then rolled, and the final rolling temperature reaches 950 °.
  • the hot-rolled steel strip is coiled after rapid water spray cooling.
  • a fine, dispersed second phase particle i.e., a grain growth inhibitor
  • the hot rolled sheet is usually subjected to pickling to remove the surface scale.
  • decarburization annealing is performed to reduce [C] in the steel sheet to a degree that does not affect the magnetic properties of the finished product ( ⁇ 30 ppm), and then an annealing annealing agent containing MgO as a main component is applied for high-temperature annealing.
  • steel secondary recrystallization occurs, M g2 Si0 4 is formed and the bottom layer of steel purification, the final insulating coating annealing and stretching, high magnetic induction and low iron loss grain oriented silicon steel, high-performance insulation products.
  • the heating temperature is high, and the slab is burnt out
  • the heating furnace needs frequent repair and the production efficiency is low
  • the hot rolling temperature is high, and the hot rolled crimping is large;
  • Russia's new Lipetsk metallurgical plant, VIZ plant, etc. use medium temperature oriented silicon steel production technology
  • the slab heating temperature is 1200-1300 °C, and the chemical composition contains high Cu (0.4%-0.7%), with A1N and CuS as inhibitors.
  • the method can avoid many problems caused by high temperature heating of the slab, and the disadvantage is that only general oriented silicon steel can be produced.
  • NH 3 is introduced into the inside of the steel sheet to form a acquired inhibitor.
  • the slab heating temperature can be lowered to below 1250 ° C.
  • the method can produce both general oriented silicon steel and high magnetic steel oriented silicon steel.
  • control material is highly purified, and the contents of Se, S, N, and O are all reduced to less than 30 ppm, thereby eliminating the effects of Se, S, N, and O segregation, and utilizing high energy grain boundaries and other crystals.
  • the difference in the speed of movement is to create oriented silicon steel.
  • M.Barisoni et al. proposed to cool the steel plate to 800-850 ° C at a rate of 20 ° C / s after normalization, and then quench it at a cooling rate of 100 ° C / s to form a volume percentage of about 8% in the steel, hardness H v ⁇ 600 (the steel substrate ⁇ ⁇ ⁇ 230) of the dispersed martensite phase, while depositing a large amount of about 10 nm ⁇ 1 ⁇ .
  • the martensitic transformation can be caused by rapid cooling (quenching), that is, thermally induced martensitic transformation; in addition, it can also be caused by stress or strain, that is, stress or strain-induced martensitic transformation. From the point of view of the free energy of phase transition, the work of stress-induced martensitic transformation is the same as the change of free energy of the drive phase transition. Therefore, the driving force of martensitic transformation consists of two parts, namely chemical driving force and mechanical driving force.
  • the martensitic transformation temperature decreases.
  • Tc 770 °C
  • the oriented silicon steel exhibits a spontaneous ferromagnetic elongation, which partially offsets the volumetric shrinkage during cooling, resulting in an increase in the martensitic transformation temperature.
  • Martensitic transformation has undergone two stages of nucleation and growth.
  • US Patent US3959033 controls the normalization process after hot rolling, especially the control of normalization
  • the cooling rate of 700 ⁇ 900 °C to room temperature is used to control the amount of martensite, and finally the magnetic properties of the finished product are improved.
  • the shortcoming of this patent is that it is difficult to achieve the uniformity of the cooling rate in the thickness direction of the plate, which leads to the uneven distribution of martensite in the thickness direction; also because of the unevenness, it is difficult to achieve the effective amount of martensite. control.
  • water is used to control the cooling rate from 700 to 900 °C to room temperature. First, it is easily restricted by site conditions, such as temperature, nozzle damage or blockage, which may cause instability of the cooling rate. Secondly, due to the temperature detection of the steel plate. The human factors are large, and it is difficult to achieve precise control, which makes it difficult to achieve fine tuning of the cooling rate. Summary of invention
  • the object of the present invention is to provide a method for producing oriented silicon steel with excellent magnetic properties, and to optimize the martensite content and distribution in the normalized steel sheet by adjusting the stress on the steel sheet during the normalized transformation, so that the martensite content is obtained. It is in the range of obtaining better magnetic properties of the finished product and optimizing the magnetic properties of the finished product.
  • a method for producing oriented silicon steel excellent in magnetic properties comprising the following steps:
  • Two-stage normalization treatment first heating to 1100 ⁇ 1200 °C, then cooling to 900 ⁇ 1000 °C in 50 ⁇ 200s; then quenching in 10 ⁇ 100 °C water; during this period, applying tension to the strip, In the temperature range of 900 °C ⁇ 500 °C, the stress of the strip is l ⁇ 200N/mm 2 ;
  • the invention adjusts the stress received by the steel plate during the normalization phase transformation, so that the stress or the strain induces the martensitic transformation, thereby realizing the reasonable and effective control of the martensite amount in the steel plate after normalization, and finally improving the magnetic properties of the finished product.
  • the present invention can obtain a relatively uniform martensite structure in the thickness direction. By With tension control, it is less restricted by field conditions. For the same thickness of the sample, the required amount of martensite can be stably obtained.
  • the tension control is more quantitative, the human influence factor is small, and it is easier to accurately control, and fine adjustment can be realized.
  • the amount of martensite after normalization is optimized, so that the martensite content in the steel sheet after normalization is in a range capable of obtaining better magnetic properties of the finished product, and finally A finished product with excellent magnetic properties.
  • the composition of the steel sheet is the same, the conditions of the manufacturing process are the same, and the method for measuring the amount of martensite is the same, the amount of martensite is the same. Therefore, the same measurement method can be used to detect the post-conformation and the pre-cold rolling according to the pre-production method.
  • the martensite amount of the steel sheet is determined in advance by the relationship between the amount of martensite and the magnetic properties of the finished product, and the target range of the amount of martensite in the steel sheet after normalization and before cold rolling can be calculated.
  • the first, second, fourth, and fifth steps in the method of the present invention are all conventional technical means for producing oriented silicon steel. I will not repeat them here.
  • the invention adjusts the stress received by the steel plate during the normalization phase transformation, so that the stress or the strain induces the martensitic transformation, thereby realizing the reasonable and effective control of the martensite amount in the steel plate after normalization, and finally improving the magnetic properties of the finished product.
  • the present invention can obtain a relatively uniform martensite structure in the thickness direction, and can finely adjust the martensite content as needed.
  • the invention adopts tension control and is less restricted by field conditions.
  • the required amount of martensite can be stably obtained; the tension control is more quantitative, the human influence factor is small, the control is easier and precise, and the fine adjustment can be realized.
  • Fig. 1 is a view showing the relationship between the martensite content (% by volume) after normalization of the oriented silicon steel of the present invention and the magnetic properties B 8 of the finished product.
  • FIG. 2 is a schematic view showing the martensitic plate thickness distribution of the cross section of the oriented silicon steel of the present invention. Detailed description of the invention
  • the steel sheets of various compositions are normalized.
  • the main components of the steel sheets are shown in Table 1:
  • the steel sheet of the above composition was heated to 1200 ° C and held for 180 minutes. Then directly rolled to 2.0 mm.
  • the hot-rolled sheet was subjected to two-stage normalization treatment, first heating to 1200 °C, then cooling to 900 °C in 200 s, and then quenching the steel sheet in water at 100 °C.
  • By adjusting the tension roller added to the furnace or changing at least one of the front and rear tension rollers it is possible to change the stress on the steel sheet when changing the normalized phase change (range: 900 °C to 500 °C) (l ⁇ 200N/ Mm 2 ), to achieve optimization
  • the purpose of the martensite content and its distribution in the slab is to achieve a range of better magnetic properties.
  • the steel sheet was subjected to 5 passes of single-stage cold rolling, wherein the third and fourth passes were carried out at 220 ° C and pressed to a thickness of 0.30 mm.
  • the cold rolled steel strip was decarburized and nitrided at 850 °C. After nitriding, a surface of the steel strip was coated with a MgO-based annealing separator, heated to 1220 ° C in an atmosphere of 25% N 2 + 75% 3 ⁇ 4, and then kept at a temperature of 30 ° C for 30 hours.
  • the main chemical composition of the steel sheet is: Si 3.05 wt%, C 0.060 wt%, Als 0.0290 wt%, N 0.0077 wt%, Mn 0.13 wt%, S ⁇ 0.006 wt%.
  • the steel sheet of the above composition was heated to 1200 ° C and held for 180 minutes. Then directly rolled to 2.0 mm.
  • the hot-rolled sheet was subjected to two-stage normalization treatment, first heated to 1100 ° C, then cooled to 1000 ° C in 50 s, and then the steel sheet was quenched in 50 ° C water.
  • the tension roller added to the furnace or changing the tension tension it is possible to change the stress of the steel sheet when changing the normalized phase change (range: 900 °C to 500 °C) (l ⁇ 200N/mm) 2 ), to achieve the purpose of optimizing the martensite content and its distribution in the normalized plate, so that it can obtain a better range of magnetic properties of the finished product.
  • the cold rolled steel strip was decarburized and nitrided at 850 °C. After nitriding, a surface of the steel strip was coated with a MgO-based annealing separator, heated to 1220 ° C in an atmosphere of 25% N 2 + 75% 3 ⁇ 4, and then kept at a temperature of 30 ° C for 30 hours.
  • the martensite content after normalization, and the tension and magnetic properties applied to the steel sheet during phase transformation are shown in Table 3.
  • the main chemical composition of the steel plate is: Si 2.9wt%, C 0.048wt%, Als 0.0255wt%, N
  • the steel sheet of the above composition was heated to 1200 ° C and held for 180 minutes. Then directly rolled to 2.0 mm.
  • the hot rolled sheet was subjected to a two-stage normalization treatment, first heated to 1100 ° C, then cooled to 900 ° C with 100 s, and then the steel sheet was quenched in water at 80 ° C.
  • the tension roller added to the furnace or changing the crimping tension By adjusting at least one of the tension roller added to the furnace or changing the crimping tension, the stress of the steel sheet when changing the normalized phase transformation (range: 900 ° C to 500 ° C) (l ⁇ 200 N / mm) 2 ), to achieve the purpose of optimizing the martensite content and its distribution in the normalized plate, so that it can obtain a better range of magnetic properties of the finished product.
  • the steel sheet was subjected to 5 passes of single-stage cold rolling, wherein the 3rd and 4th passes were carried out at 220 ° C and pressed to a thickness of 0.30 mm.
  • the cold rolled steel strip was subjected to decarburization and nitriding annealing at 850 °C. After nitriding, a surface of the steel strip was coated with a MgO-based annealing separator, heated to 1220 ° C in a 25% N 2 + 75% 3 ⁇ 4 atmosphere, and then kept at a temperature of 30 ° C for 30 hours.
  • the main chemical composition of the steel sheet is: Si 3.41wt%, C 0.0542wt%, Als 0.0269wt%, N 0.0083wt%, Mn0.12wt%, S ⁇ 0.006wt%.
  • the steel sheet of the above composition is heated to 1200 ° C for 180 minutes; then directly rolled to
  • the normalization annealing is performed by the following methods:
  • the steel sheet was subjected to 5 passes of single-stage cold rolling, wherein the 3rd and 4th passes were carried out at 220 ° C and pressed to a thickness of 0.30 mm.
  • the cold rolled steel strip was subjected to decarburization and nitriding annealing at 850 °C. After nitriding, a surface of the steel strip was coated with a MgO-based annealing separator, heated to 1220 ° C in a 25% N 2 + 75% 3 ⁇ 4 atmosphere, and then kept at a temperature of 30 ° C for 30 hours.
  • the tension control can obtain a more uniform martensite structure in the thickness direction, and the sample of the same thickness can stably obtain the required amount of martensite; and obtain the optimal finished magnetic properties.

Description

一种磁性能优良的取向硅钢生产方法 发明领域
本发明涉及取向硅钢生产方法，特别是一种磁性能优良的取向硅钢生 产方法。 背景技术
取向硅钢是电力、 电子和军事工业不可缺少的重要软磁合金， 主要用 作变压器铁芯、 发电机和大型电机等。 要求有优良的磁性能， 特别是低的 铁损。
取向硅钢是利用二次再结晶技术， 使 Goss织构 （Goss织构： {110} 晶面平行轧面， <001>晶向平行轧向） 发生异常晶粒长大， 吞并其它位向 的晶粒后得到优良的轧向磁性能。
传统的高磁感取向硅钢生产方法如下：
板坯在专用高温加热炉内加热到 1350°C~1400°C的温度， 并进行 lh 以上的保温，使得有利夹杂 A1N， MnS或 MnSe充分固溶，然后进行轧制， 终轧温度达到 950°C以上， 热轧钢带快速喷水冷却后进行卷取。 在随后的 常化过程中，使基体内析出细小、弥散的第二相质点 (即晶粒长大抑制剂 )， 热轧板常化后进行酸洗， 除去表面氧化铁皮。 进一歩冷轧至成品厚度后， 进行脱碳退火把钢板中的 [C]降低到不影响成品磁性的程度 （≤30ppm) ， 然后涂布以 MgO为主要成分的退火隔离剂进行高温退火， 使钢板发生二 次再结晶、形成 Mg2Si04底层及净化钢质， 最后涂布绝缘涂层并进行拉伸 退火， 得到磁感高、 铁损低和绝缘良好的高性能取向硅钢产品。
以上生产方法存在如下问题：
1. 加热温度高， 板坯烧损大；
2. 加热炉需频繁修补， 生产效率低；
3. 热轧温度高， 热轧卷边裂大；
为了解决这些问题，国外一些公司摸索和开发出了以较低的板坯加热 温度生产取向硅钢的方法， 比如：
1、 中温取向硅钢生产方法
俄罗斯的新利佩茨克冶金常厂、 VIZ 厂等采用中温取向硅钢生产技 术，板坯加热温度 1200— 1300 °C，化学成分中含较高的 Cu( 0.4%— 0.7%) , 以 A1N和 CuS为抑制剂。该方法可以避免板坯高温加热带来的诸多问题， 缺点是只能生产一般取向硅钢。
2、 板坯低温加热、 渗氮方法
在冷轧板通过脱碳退火炉的时候， 通入 NH3对钢板内部进行渗氮， 形成一种后天的获得型抑制剂。通过该方法， 可以使得板坯加热温度降低 到 1250°C以下， 该方法既可以生产一般取向硅钢， 也可以生产高磁钢取 向硅钢。
3、 无抑制剂的取向硅钢生产方法
冶炼的时候， 控制材料的高度纯化， 将 Se、 S、 N、 O的含量都降低 至 30ppm以下， 从而排除了 Se、 S、 N、 O等偏析带来的影响， 利用高能 晶界与其他晶界在移动速度方面的差别来制造取向硅钢。
M.Barisoni等提出常化后以 20°C/s速度将钢板冷却到 800~850°C， 然 后以 100°C/s的冷速进行淬火，使钢中形成体积百分比约 8%，硬度 Hv≥600 (该钢板基体 Ην≥230 ) 的弥散马氏体相， 同时析出大量约 10nm的 Α1Ν。 因为形成了马氏体， 使得储能增高， 冷轧后的储能更高， 而储能使得脱碳 退火时 {110}晶粒更容易再结晶和长大， 脱碳退火后 { 110}组分得以加强， 所以成品的磁性提高。
马氏体相变可由快速冷却 （淬火） 引起， 即热致马氏体相变； 另外， 也可由应力或应变所引起， 即应力或应变诱发马氏体相变。从相变自由能 的角度， 应力诱导马氏体相变所作的功与驱动相变的自由能变化是相同 的。 因此， 马氏体相变的驱动力由两部分组成， 即化学驱动力和力学驱动 力。
在应力状态下， 马氏体相变温度降低。 而在居里点温度 Tc ( 770°C ) 以下， 取向硅钢呈现自发的铁磁伸长， 能够部分地抵消冷却时体积自动收 缩， 使得马氏体相变温度下降增加。
马氏体相变经历了形核和长大两个阶段。
根据固态相变理论可以看到， 变形储能的引入， 使马氏体的形核率大 大提高， 幅度可达数十到几百个数量级。储能对马氏体晶核生长速度影响 并不很大。
美国专利 US3959033 通过控制热轧后的常化工艺， 特别是控制常化 过程中 700~900 °C到室温的冷却速度来控制马氏体的量， 并最终实现提高 成品磁性能。 该专利不足之处在于难以实现板厚度方向上的冷速一致性， 也就导致了在板厚方向上马氏体的分布不均匀性； 也是由于不均匀性， 所 以难以实现马氏体量的有效控制。 而且采用水进行 700~900 °C到室温的冷 却速度控制， 首先， 容易受现场条件的限制， 比如气温、 喷嘴损害或者堵 塞， 可能会导致冷速的不稳定性； 其次， 由于钢板温度检测上的人为因素 较大， 难以实现精确控制， 使得冷速的微调难以实现。 发明概述
本发明的目的在于提供一种磁性能优良的取向硅钢生产方法，通过调 节常化相变时钢板所受的应力来优化常化后钢板中的马氏体含量及其分 布， 使马氏体含量处于能获得更优成品磁性能的范围， 并实现成品磁性能 优化。
为达到上述目的， 本发明的技术方案是：
—种磁性能优良的取向硅钢生产方法， 包括如下歩骤：
1) 常规冶炼、 铸造成坯；
2) 板坯加热、 热轧成带钢；
3) 常化处理
采用两段式常化处理， 首先加热到 1100~1200 °C， 然后在 50~200s内降温到 900~1000 °C ; 随后在 10~100 °C水中进行急冷； 期 间， 对带钢施加张力， 在 900 °C ~500 °C温度区间内使带钢所受应力 的大小为 l~200N/mm2 ;
4) 冷轧
进行一次冷轧， 或带中间退火的二次冷轧；
5) 一次再结晶退火， 接着， 涂布以 MgO为主的退火隔离剂进行包括 二次再结晶退火和净化退火组成的成品退火。
进一歩， 对带钢施加张力采用在常化炉内增设张力辊， 或改变前后张 力辊。
本发明通过调整常化相变时钢板所收的应力，使得应力或者应变诱导 马氏体相变， 从而实现了常化后钢板中马氏体量的合理有效控制， 并最终 提高成品磁性能。本发明可以在板厚方向上得到较均匀的马氏体组织。 由 于采用张力控制， 受现场条件的限制较少， 对于同一厚度的样板， 可以稳 定的得到需要的马氏体量； 张力控制更加量化， 人为影响因素小， 更容易 精确控制， 可以实现微调。
通过控制热轧板常化相变时所受应力的大小，达到优化常化后马氏体 的量， 使常化后钢板中马氏体含量处于能获得更优成品磁性能的范围， 并 最终获得优异磁性能的成品。
合适的马氏体含量有利于提高成品磁性能 88的理由：
( 1 ) 由于马氏体的存在， 使得储能增加， 经过冷轧后， 储能更高， 脱碳退火时 （110 ) 晶粒更容易在结晶和长大， （110 ) 组分加强， 所以磁 性能提高；
( 2 ) 由于马氏体的存在， 经过冷轧和脱碳退火后， 大角度晶界数量 增加， 有利于 Goss织构吞并其它位向的晶粒， 促进二次再结晶；
( 3 ) 马氏体经过冷轧和脱碳退火后， 材料中形成 γ纤维织构， 有利 于二次再结晶的进行； 由于上面分析的相关因素， 实现了提高最终成品的 晶粒取向度， 提高了成品磁性能 Β8。
如果钢板的成分相同、制造过程的条件相同、 马氏体量的测定方法相 同， 则马氏体量相同， 所以可以根据前期制造的样板中， 采用相同的测定 方法检测常化后、冷轧前钢板的马氏体量， 预先求出马氏体量和成品磁性 能的关系， 可以算出常化后、 冷轧前钢板中马氏体量的目标范围。
作为马氏体量的控制手段， 有如下 3种常用方法：
( 1 ) 改变相变时钢板所受拉应力的大小， 达到改变马氏体相变的形 核数目， 从而实现马氏体含量的改变；
( 2 ) 改变常化最高温度， 改变最高温度下的奥氏体量， 实现了相变 时马氏体量的改变；
( 3 ) 改变常化时二次冷却速度， 实现相变后马氏体含量的改变。 将 常化后钢板的马氏体量测定值与目标值进行比较， 根据两者的偏差， 进行 通过调节增设在炉子内的张力辊或改变卷曲张力的至少一种处理来实现 改变常化相变时 （范围： 900°C~500°C ) 的钢板所受应力的大小 ( l~200N/mm2 ) ， 达到优化常化板中马氏体含量及其分布的目的， 使其 处于能获得更优成品磁性能范围。
本发明方法中第 1、 2、 4、 5歩骤均为取向硅钢生产的常规技术手段， 在此不再赘述。
本发明的优点在于：
本发明通过调整常化相变时钢板所收的应力，使得应力或者应变诱导 马氏体相变， 从而实现了常化后钢板中马氏体量的合理有效控制， 并最终 提高成品磁性能。
本发明可以在板厚方向上得到较均匀的马氏体组织，并且可以根据需 求进行马氏体含量的微调。
本发明采用张力控制，受现场条件的限制较少，对于同一厚度的样板， 可以稳定的得到需要的马氏体量； 张力控制更加量化， 人为影响因素小， 更容易精确控制， 可以实现微调。 附图说明
图 1为本发明的取向硅钢常化后马氏体含量（体积比％)与成品磁性 能 B8之间的关系。
图 2为本发明的取向硅钢横截面的马氏体板厚分布示意图。 发明的详细说明
下面结合实施例对本发明做进一歩说明。
实施例 1
对多种成分的钢板进行常化处理， 钢板主要成分如表 1所示：
表 1 单位： 重量百分比
Figure imgf000007_0001
将上述成分的钢板加热到 1200 °C， 保温 180分钟。 然后直接轧制到 2.0mm。对热轧板进行两段式常化处理， 首先加热到 1200 °C， 然后用 200s 降温到 900 °C， 随后将钢板在 100 °C水中进行急冷。 通过调节增设在炉子 内的张力辊或改变前后张力辊的至少一种处理来实现改变常化相变时（范 围： 900 °C至 500 °C ) 的钢板所受应力的大小（l~200N/mm2)， 达到优化常 化板中马氏体含量及其分布的目的， 使其处于能获得更优成品磁性能范 围。
酸洗后对钢板进行 5个道次的单级冷轧轧制，其中第 3和第 4道次在 220 °C进行，压下到 0.30mm厚度。冷轧钢带在 850 °C进行脱碳和渗氮退火。 渗氮后在钢带表面涂覆以 MgO为主的退火隔离剂， 在 25%N2+75%¾的 气氛中加热到 1220 °C， 然后改用纯 ¾在此温度下保温 30小时。
常化后马氏体含量， 相变时施加在钢板上的张力及磁性如表 2。
表 2 施加张力和成品磁性能
Figure imgf000008_0001
实施例 2
钢板主要化学成分为： Si 3.05wt%， C 0.060wt%， Als 0.0290wt%, N 0.0077wt%, Mn 0.13wt%， S<0.006wt%。
将上述成分的钢板加热到 1200 °C， 保温 180分钟。 然后直接轧制到 2.0mm。 对热轧板进行两段式常化处理， 首先加热到 1100 °C， 然后用 50s 降温到 1000 °C， 随后将钢板在 50 °C水中进行急冷。 通过调节增设在炉子 内的张力辊或改变卷曲张力的至少一种处理来实现改变常化相变时 （范 围： 900 °C至 500 °C ) 的钢板所受应力的大小（l~200N/mm2)， 达到优化常 化板中马氏体含量及其分布的目的， 使其处于能获得更优成品磁性能范 围。
酸洗后对钢板进行 5个道次的单级冷轧轧制，其中第 3和第 4道次在
220 °C进行，压下到 0.30mm厚度。冷轧钢带在 850 °C进行脱碳和渗氮退火。 渗氮后在钢带表面涂覆以 MgO为主的退火隔离剂， 在 25%N2+75%¾的 气氛中加热到 1220 °C， 然后改用纯 ¾在此温度下保温 30小时。 常化后马氏体含量， 相变时施加在钢板上的张力及磁性如表 3。
表 3 施加张力和成品磁性能
Figure imgf000009_0001
实施例 3
钢板主要化学成分为： Si 2.9wt%， C 0.048wt%， Als 0.0255wt%， N
0.0073wt%, Mn 0.10wt%， S<0.006wt%。
将上述成分的钢板加热到 1200°C， 保温 180分钟。 然后直接轧制到 2.0mm。对热轧板进行两段式常化处理， 首先加热到 1100°C， 然后用 100s 降温到 900°C， 随后将钢板在 80°C水中进行急冷。通过调节增设在炉子内 的张力辊或改变卷曲张力的至少一种处理来实现改变常化相变时 （范围： 900°C至 500°C ) 的钢板所受应力的大小（l~200N/mm2)， 达到优化常化板 中马氏体含量及其分布的目的， 使其处于能获得更优成品磁性能范围。
酸洗后对钢板进行 5个道次的单级冷轧轧制，其中第 3和第 4道次在 220°C进行，压下到 0.30mm厚度。冷轧钢带在 850°C进行脱碳和渗氮退火。 渗氮后在钢带表面涂覆以 MgO为主的退火隔离剂， 在 25%N2+75%¾的 气氛中加热到 1220°C， 然后改用纯 ¾在此温度下保温 30小时。
常化后马氏体含量， 相变时施加在钢板上的张力及磁性如表 4。
表 4 施加张力和成品磁性能 马氏体含量 施加张力 (N/mm2) B8(T) 对比例 1.5 0 1.85 实施例 9 18 1.93 实施例 4
钢板主要化学成分为： Si 3.41wt%, C 0.0542wt%, Als 0.0269wt%, N 0.0083wt%， Mn0.12wt%, S<0.006wt%。
将上述成分的钢板加热到 1200°C， 保温 180分钟； 然后直接轧制到
2.0mm。 分别采用如下方法进行常化退火：
首先， 加热到 1180°C， 然后采用 200s降温到 920°C， 随后将钢板在 100 °C水中进行急冷。
(1)在冷却的过程中， 对钢板施加 60N/mm2的张力 （对比例） ·' (2)在冷却的过程中 （900°C~500°C) ， 对钢板施加 20N/mm2的张力， 使得常化后马氏体的含量处于能够获得优异成品磁性能的区域（实施例）。
酸洗后对钢板进行 5个道次的单级冷轧轧制，其中第 3和第 4道次在 220°C进行，压下到 0.30mm厚度。冷轧钢带在 850°C进行脱碳和渗氮退火。 渗氮后在钢带表面涂覆以 MgO为主的退火隔离剂， 在 25%N2+75%¾的 气氛中加热到 1220°C， 然后改用纯 ¾在此温度下保温 30小时。
具体结果见表 5。
表 5 施加张力和成品磁性能
Figure imgf000010_0001
对比例和实施例试样横截面的马氏体板厚分布如图 2所示。
从中可以看出，采用张力控制可以在板厚方向上得到较均匀的马氏体 组织， 对于同一厚度的样板， 可以稳定的得到需要的马氏体量； 获得最优 的成品磁性能。

Claims

权 利 要 求 书
1. 一种磁性能优良的取向硅钢生产方法， 包括如下歩骤：
1) 常规冶炼、 铸造成坯；
2) 板坯加热、 热轧成带钢；
3) 常化处理
采用两段式常化处理， 首先加热到 1100~1200 °C， 然后在 50~200s内降温到 900~1000 °C ; 随后在 10~100 °C水中进行急冷； 期 在 900 °C ~500 °C温度区间内使带钢所受应力
Figure imgf000011_0001
进行一次冷轧， 或带中间退火的二次冷轧；
5) 一次再结晶退火， 接着， 涂布以 MgO为主的退火隔离剂进行包括 二次再结晶退火和净化退火组成的成品退火。
2. 如权利要求 1所述的磁性能优良的取向硅钢生产方法， 其特征是， 对 带钢施加张力采用在常化炉内增设张力辊， 或改变前后张力辊。
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