WO2012024939A1 - 一种改善无取向硅钢表面粗晶的方法 - Google Patents

一种改善无取向硅钢表面粗晶的方法 Download PDF

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WO2012024939A1
WO2012024939A1 PCT/CN2011/073358 CN2011073358W WO2012024939A1 WO 2012024939 A1 WO2012024939 A1 WO 2012024939A1 CN 2011073358 W CN2011073358 W CN 2011073358W WO 2012024939 A1 WO2012024939 A1 WO 2012024939A1
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oriented silicon
silicon steel
steel
normalization
controlled
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French (fr)
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陈凌峰
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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Priority to MX2012010150A priority Critical patent/MX2012010150A/es
Priority to RU2012136591/02A priority patent/RU2012136591A/ru
Priority to JP2012549246A priority patent/JP2013517380A/ja
Priority to EP11819314A priority patent/EP2530173A1/en
Publication of WO2012024939A1 publication Critical patent/WO2012024939A1/zh
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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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/1277—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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/16—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys in the form of sheets
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C21D1/28—Normalising

Definitions

  • the present invention relates to a process for producing non-oriented silicon steel, and more particularly to a method for improving the surface coarse grain of a non-oriented silicon steel. Background technique
  • the content of the existing non-oriented silicon steel products is: C ⁇ 0.005%, Si: 0.1% ⁇ 1.80%, Mn: 0.10% ⁇ 0.80%, P: 0.04% or less, Ah 0.20% ⁇ 0.80%, S ⁇ 0.005% or less , N ⁇ 0.005% or less, and the balance is Fe and unavoidable inclusions.
  • the composition of the above molten steel is obtained by a converter and RH refining treatment, and the molten steel is cast into a billet, and then subjected to hot rolling, normalization, pickling, cold rolling, annealing, and a non-oriented silicon steel product obtained after coating.
  • the surface quality of the product is very poor, as shown in Figure 1, there is a serious surface coarse grain problem.
  • the "double preheating and normalizing" pretreatment process for forgings disclosed in Chinese Patent No. CN1073982 overcomes the problem that the prior art cannot sufficiently refine the grains and can not significantly improve the coarse and mixed crystals. It includes a preheating and normalizing process, which is characterized in that the forging is preheated before normalizing, and the preheating temperature is 600 ⁇ 710 °C, and its characteristics are: 1. Refined grains; 2. Improved coarse crystal and Mixed crystals meet the technical requirements; 3. It can be realized by using existing equipment. However, this process can be applied to pre-heat treatment of large forgings. If the non-oriented steel coil is treated by this process, a heat treatment process is added and the cost is increased.
  • Chinese patent CN1804056 discloses "a method for preventing low-order coarse grains of deformed superalloys", which includes two sets of measures.
  • the first set is a precautionary measure for forging process, mainly using computer simulation of DEFORM2D commercial simulation software to determine superalloys.
  • the amount of deformation of the forged part at the minimum deformation point and strictly control the amount of deformation of the effective deformation portion of the single fire.
  • the second set is a preliminary heat treatment precaution, mainly to strictly control the forging heating temperature below 1160 °C. When the first set of measures cannot be used completely or an accident occurs, the second set of measures is adopted.
  • the production process formulated by the invention can make the low-magnification coarse crystal of the deformed high-temperature alloy workpiece reach the qualified level, and is mainly used for the hydraulic and hammer forging deformation of the ordinary high-temperature alloy, and is not suitable for the normalization treatment process of the non-oriented silicon steel, because the non-oriented silicon steel The coil cannot be subjected to forging deformation hot processing at the same time in the normalizing process.
  • Chinese patent CN1733946 discloses "a fine grain treatment of subcritical steam turbine bolt steel" Process method", which is characterized in that a heat treatment is added before the material quenching and tempering treatment, and the steps are as follows: First, the material is heated to 920 ° C ⁇ 20 ° C, and the temperature is kept for 0.5 to 2 hours; The cooling rate of 100 °C ⁇ 20 °C is slowly cooled to 750 °C ⁇ 30 °C, and the temperature is kept for 0.5 ⁇ 2 hours. The third layer is cooled to room temperature. However, the invention is added once before the quenching and tempering treatment of 20CrlMolVNbTiB steel.
  • the material is equalized before heat treatment and quenching and tempering, and the whole fine-grained structure can be obtained after quenching and tempering treatment, thereby solving the coarse crystal defects of 20CrlMolVNbTiB steel, which cannot solve the problem of the non-oriented silicon steel normalization process encountered. Coarse crystal problem.
  • the object of the present invention is to provide a method for improving the surface coarse crystal of non-oriented silicon steel. Under the existing objective conditions, the problem of coarse crystal on the surface of non-oriented silicon steel is solved without increasing the heat treatment process or parallel heat processing. Meet the surface quality requirements of non-oriented silicon steel without affecting the electromagnetic properties of the product.
  • a method for improving coarse crystals on a surface of a non-oriented silicon steel comprising the following steps:
  • the weight percentage of the non-oriented silicon steel is: C 0.001-0.005%, Si: 0.1% ⁇ 1.80%, Mn: 0.10% ⁇ 0.80%, P ⁇ 0.04%, Ah 0.20% ⁇ 0.80%, S ⁇ 0.005%, N ⁇ 0.005%, the balance is Fe and inevitable inclusions;
  • the normalization temperature is controlled at 800 °C ⁇ 900 °C, the normalization soaking time is controlled at 15S -30S; the oxygen content in the normalization furnace is controlled below 0.5%; the maximum grain size and average grain size in the normalized steel sheet The size ratio is controlled below 3; 4) Pickling, cold rolling, annealing, coating, to obtain non-oriented silicon steel products.
  • the ratio of the maximum grain size to the average grain size in the steel sheet after normalization is controlled to be 2 or less.
  • the invention has the surface coarse crystal problem for the non-oriented silicon steel product product, and the normal steel plate is used for normalization treatment, the normalization temperature is controlled at 800 ° C ⁇ 900 ° C, and the normalized soaking time is controlled at 15S ⁇ 30S. If the normalizing temperature is too high and the time is too long, the grain structure will grow abnormally, and severe coarse crystal problems will occur after cold rolling and annealing. When the normalizing temperature is too low and the time is too short, the rolled deformation structure after hot rolling cannot achieve the effect of normalizing recrystallization, corrugated defects occur, and the magnetic induction is deteriorated. That is, the non-oriented silicon steel of the above components and process routes has a critical normalization temperature and time zone during the normalization process, and the critical normalization temperature and time zone are exceeded or not, which inevitably leads to abnormal grain growth and surface coarse crystals. Quality issues.
  • the ratio of the maximum crystal grain size to the average grain size in the steel sheet after normalization is controlled to be 3 or less, and the ratio of the grain size of the normalization treatment is too large, and the surface coarse crystal problem is liable to occur, and it is preferably controlled to be 2 or less.
  • the oxygen content in the normalizing furnace is controlled to be 0.5% or less. If the oxygen content is too high, the surface oxide layer becomes large, and pickling is difficult, which affects the surface quality.
  • the present invention does not use two heat treatment processes, and the process operation is simple and the energy consumption in the manufacturing process is reduced.
  • Figure 1 is a photograph of the surface coarse grain metallographic phase of the finished product of the comparative example.
  • FIG. 2 is a photograph of a metallographic surface of a finished product according to an embodiment of the present invention. Detailed description of the invention
  • the chemical compositions of the examples and comparative steels of the present invention are shown in Table 1, and the normalization process is shown in Table 2.
  • the molten steel is subjected to a converter, RH refining treatment, and cast into a billet, and then subjected to hot rolling, normalization, pickling, cold rolling, annealing, and coating to obtain a non-oriented electrical steel product.
  • the slab is hot rolled into a 2.6 mm strip; then the 2.6 mm hot rolled strip is normalized; the normalized strip passes Cold-rolled into 0.5mm strip, and finally annealed and coated.
  • the final annealing temperature after cold rolling is 820 °C, and the annealing time is controlled at 13 ⁇ 15S to obtain cold-rolled electromagnetic steel sheets.
  • the surface metallographic phases of the cold rolled non-oriented silicon steel sheets obtained in the comparative examples and the examples are shown in Figs. 1 and 2.
  • Table 1 Unit The surface metallographic phases of the cold rolled non-oriented silicon steel sheets obtained
  • Example 2 880 20 1.49
  • Example 3 850 20 1.25
  • Example 4 830 20 1.10
  • Comparative example 1 1000 60 8.5

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Electromagnetism (AREA)
  • Manufacturing & Machinery (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Power Engineering (AREA)
  • Dispersion Chemistry (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
  • Soft Magnetic Materials (AREA)
  • Treatment Of Steel In Its Molten State (AREA)

Description

一种改善无取向硅钢表面粗晶的方法 发明领域
本发明涉及无取向硅钢的制造工艺，特别涉及一种改善无取向硅钢表 面粗晶的方法。 背景技术
现有无取向硅钢产品的成分含量为： C≤0.005%， Si: 0.1%~1.80%, Mn: 0.10%~0.80%, P: 0.04%以下， Ah 0.20%~0.80%, S≤0.005%以下， N≤0.005%以下，余为 Fe以及不可避免的夹杂物。上述钢水的成分经转炉、 RH精炼处理而获得， 钢水浇注成坯后， 经过热轧， 常化， 酸洗， 冷轧， 退火， 涂层后得到的无取向硅钢产品。 其产品的表面质量非常差， 如图 1 所示， 存在严重的表面粗晶问题。
目前， 解决钢铁产品粗晶问题的方案主要有以下几种：
中国专利 CN1073982公开的一种锻压件 "双重预热正火" 预处理工 艺， 克服了已有工艺不能充分使晶粒细化和不能明显改善粗晶和混晶问 题。 它包括预热和正火工序， 其特征在于正火前， 对锻压件进行预热， 预 热温度为 600~710 °C， 其特点： 1、 细化了晶粒； 2、 改善了粗晶和混晶，达 到了技术要求； 3、 利用已有设备可实现。 但是， 该工艺可应用于对大型 锻压件的预先热处理。如果无取向钢卷采用此工艺处理， 增加了一次热处 理工序， 成本上升。
中国专利 CN1804056公开了 "一种变形高温合金低倍粗晶粒的预防 方法" ， 它包括两套措施， 第一套是锻造工艺预防措施， 主要是用 DEFORM2D商业模拟软件进行计算机模拟， 确定高温合金锻件最小变形 部位的变形量， 并严格控制单火次有效变形部位产生再结晶的变形量。第 二套是预备热处理预防措施， 主要是严格掌握锻造加热温度低于 1160 °C， 当使用第一套措施不能完全奏效或产生意外时， 采用第二套措施。此发明 制定的生产工艺可以使变形高温合金制件的低倍粗晶达到合格水平，主要 用于普通高温合金的液压和锤锻变形， 不适用无取向硅钢的常化处理工 艺， 因为无取向硅钢卷在常化处理不能同时进行锻压变形热加工。
中国专利 CN1733946公开了 "一种亚临界汽轮机螺栓钢细晶粒处理 工艺方法"， 其特征是在材料调质处理前增加一次热处理， 其歩骤是： 第 一歩， 将材料加热至 920°C±20°C， 保温 0.5~2小时； 第二歩， 以每小时 100°C±20°C的冷却速度缓冷至 750°C±30°C， 保温 0.5~2小时； 第三歩， 空冷至室温。 但是， 此发明是在 20CrlMolVNbTiB钢调质处理前增加一 次热处理， 使材料在热处理调质前组织均衡化， 材料在调质处理后可得到 全部细晶组织， 从而解决了 20CrlMolVNbTiB 钢的粗晶缺陷， 不能解决 所遇到的无取向硅钢常化工艺产生的粗晶问题。
上述三种方法归结为两种思路： 一种是通过通两次热处理工艺， 使晶 粒细化，改善粗晶问题。另一种是在热处理的同时， 附加以临界锻压变形， 控制再结晶， 使低倍粗晶的问题得到有效解决。
但是， 上述三种方法不适用于经过常化的无取向硅钢产品， 主要原因 是无取向硅钢产品在常化热处理的同时不能进行热变形加工处理；如果采 用两次热处理细化晶粒的晶粒尺寸， 会增加成本。 发明概述
本发明的目的在于提供一种改善无取向硅钢表面粗晶的方法，在现有 的客观条件下， 不增加热处理工序， 也不进行并行的热加工情况下， 解决 无取向硅钢表面粗晶问题， 在不影响产品的电磁性能的前提下， 满足无取 向硅钢的表面质量要求。
为达到上述目的， 本发明的技术方案是：
一种改善无取向硅钢表面粗晶的方法， 其包括如下歩骤：
1) 冶炼、 浇铸
无取向硅钢的成分重量百分比为： C 0.001-0.005% , Si : 0.1%~1.80%, Mn: 0.10%~0.80%, P<0.04%, Ah 0.20%~0.80%, S<0.005%, N<0.005%, 余量为 Fe以及不可避免的夹杂物；
按上述成分经冶炼、 RH精炼处理， 钢水浇铸成坯；
2) 热轧成钢板；
3) 常化
常化温度控制在 800°C~900°C，常化均热时间控制在 15S -30S; 常化炉内的氧含量控制在 0.5%以下； 常化后钢板中的最大晶粒与 平均晶粒尺寸之比控制在 3以下； 4) 酸洗、 冷轧、 退火、 涂层， 得到无取向硅钢产品。
进一歩， 常化后钢板中的最大晶粒与平均晶粒尺寸之比控制在 2 以 下。
本发明针对无取向硅钢产品产品存在表面粗晶问题，对钢板采用常化 处理， 常化温度控制在 800°C~900 °C， 常化均热时间控制在 15S ~30S。 常 化温度过高， 时间过长， 导致晶粒组织异常长大， 经冷轧和退火后产生严 重的粗晶问题。 常化温度过低， 时间过短， 热轧后的轧制变形组织不能达 到常化再结晶的效果， 出现瓦楞状缺陷， 同时磁感劣化。 即上述成分和工 艺途径的无取向硅钢在常化处理过程中存在临界常化温度和时间区域，超 过或未达到这个临界常化温度和时间区域， 必然导致晶粒异常长大， 发生 表面粗晶的质量问题。
常化后钢板中的最大晶粒与平均晶粒尺寸之比控制在 3以下，常化处 理的晶粒尺寸之比过大， 容易产生表面粗晶问题， 优选控制在 2以下。
对于常化炉内的氧含量控制在 0.5%以下。 氧含量过高， 导致表面氧 化层变大， 酸洗困难， 影响表面质量。
本发明的有益效果
1、 本发明不采用两次热处理工艺， 工艺操作实施简便， 制造过程能 耗降低。
2、 本发明通过常化处理， 无取向硅钢板表面质量得到明显改善， 有 效解决了无取向硅钢成品的表面粗晶缺陷。 附图说明
图 1为比较例成品的表面粗晶金相照片。
图 2为本发明实施例成品表面金相照片。 发明的详细说明
下面结合附图和实施例对本发明作更详细的描述。
本发明实施例和比较例钢的化学成分见表 1， 常化工艺参见表 2。 将 钢水经转炉、 RH精炼处理、 浇注成坯后， 经过热轧， 常化， 酸洗， 冷轧， 退火， 涂层后得到无取向电工钢产品。 其中， 板坯经热轧轧成 2.6mm 的 带钢； 然后将 2.6mm 的热轧带钢进行常化处理； 常化处理后的带钢通过 冷轧成 0.5mm 的带钢， 再进行最终退火和涂层， 冷轧后的最终退火的板 温为 820°C， 退火时间控制在 13~15S， 得到冷轧电磁钢板。 比较例与实施 例所得冷轧无取向硅钢板的表面金相见图 1和图 2。 表 1 单位:
Figure imgf000006_0001
表 2
常化温度 常化时间 常化钢板的最大晶粒
(°C) (S) 与平均晶粒之比
实施例 1 900 20 1.86
实施例 2 880 20 1.49 实施例 3 850 20 1.25 实施例 4 830 20 1.10
实施例 5 900 30 2.15
实施例 6 880 30 1.94
实施例 7 850 30 1.41 实施例 8 830 30 1.13
比较例 1 1000 60 8.5
比较例 2 980 60 8.3
比较例 3 970 40 7.8
比较例 4 950 40 6.3
比较例 5 980 50 7.2
比较例 6 990 50 6.1
由表 2、 图 1和图 2可以看出， 实施例所得钢板的表面质量明显 比较例所得钢板的表面质量， 成品的表面粗晶缺陷得到了完全解决。

Claims

权 利 要 求 书
1. 一种改善无取向硅钢表面粗晶的方法， 其包括如下歩骤：
5) 冶炼、 浇铸
无取向硅钢的成分重量百分比为： C 0.001-0.005% , Si :
0.1%~1.80%, Mn: 0.10%~0.80% , P<0.04%, Ah 0.20%~0.80% , S<0.005%, N<0.005%, 余量为 Fe以及不可避免的夹杂物；
按上述成分经冶炼、 RH精炼处理， 钢水浇铸成坯；
6) 热轧成钢板；
7) 常化
常化温度控制在 800°C~900 °C，常化均热时间控制在 15S -30S ; 常化炉内的氧含量控制在 0.5%以下； 常化后钢板中的最大晶粒与 平均晶粒尺寸之比控制在 3以下；
8) 酸洗、 冷轧、 退火、 涂层， 得到无取向硅钢产品。
2. 如权利要求 1 所述的改善无取向硅钢表面粗晶的方法， 其特征在于， 常化后钢板中的最大晶粒与平均晶粒尺寸之比控制在 2以下。
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