WO2012055224A1 - 一种磁性优良的高效无取向硅钢制造方法 - Google Patents

一种磁性优良的高效无取向硅钢制造方法 Download PDF

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Publication number
WO2012055224A1
WO2012055224A1 PCT/CN2011/073373 CN2011073373W WO2012055224A1 WO 2012055224 A1 WO2012055224 A1 WO 2012055224A1 CN 2011073373 W CN2011073373 W CN 2011073373W WO 2012055224 A1 WO2012055224 A1 WO 2012055224A1
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rolling
temperature
silicon steel
oriented silicon
steel
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English (en)
French (fr)
Inventor
马爱华
王波
谢世殊
胡瞻源
邹亮
王子涛
朱雨华
黄杰
金冰忠
刘献东
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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 US13/637,611 priority Critical patent/US9816152B2/en
Priority to KR1020127020188A priority patent/KR101407009B1/ko
Priority to EP11835498.4A priority patent/EP2532758B1/en
Priority to JP2013500326A priority patent/JP5675950B2/ja
Priority to RU2012142297/02A priority patent/RU2532786C2/ru
Priority to MX2012010529A priority patent/MX346804B/es
Publication of WO2012055224A1 publication Critical patent/WO2012055224A1/zh
Anticipated expiration legal-status Critical
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    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment
    • C21D8/1261—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment following 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment
    • 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
    • C22C38/001—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
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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

Definitions

  • the invention relates to a method for manufacturing non-oriented electrical steel, in particular to a method for manufacturing high-efficiency non-oriented silicon steel with excellent magnetic properties, and solving the problems of high cost of normalization and long manufacturing cycle of high-efficiency non-oriented electrical steel produced by a conventional process. Background technique
  • the main feature of high-efficiency non-oriented silicon steel is its high magnetic induction.
  • Traditionally it is characterized by the use of hot-rolled sheets after hot rolling to make the hot-rolled sheet structure more uniform, increase the recrystallized grains, prevent corrugated defects, and at the same time coarsen and strengthen the grains and precipitates ( The 1 10 ) and (100 ) components reduce the (1 1 1 ) component and significantly improve the magnetic properties.
  • the normalizing temperature is above 950 °C.
  • the problems caused by the use of hot-rolled sheets are that the manufacturing cost is high and the manufacturing cycle is long.
  • Chinese patent CN1288070 discloses a non-oriented silicon steel whose composition is: C ⁇ 0.008%, Si 0.2 ⁇ 2.50%, Mn 0.15 ⁇ 0.8%, Als residual amount ⁇ 1.50%, B residual amount ⁇ 0.0035%, P+Sn /Sb0.08 ⁇ 0.45%, S ⁇ 0.0030%, N ⁇ 0.003%, and the balance is Fe and unavoidable inclusions.
  • High-efficiency motor cores are produced by low-temperature hot rolling, primary cold rolling, dry gas or moisture annealing.
  • Japanese Patent Laid-Open No. 2004-169141 mentions that the composition is 1.8% ⁇ (Si + 2A1 ) ⁇ 5% high-grade hot-rolled sheet free of normal production, requiring one or two of REM, Mg and Ca in the steelmaking process Above, while strictly controlling Ti ⁇ 0.003%, hot rolling requires final rolling above 950 °C and coiling below 700 °C.
  • the shortcomings are that the hot rolling production process conditions are harsh, the finish rolling temperature is high, and the actual production operation and control are very difficult.
  • the patent for annealing the hot-rolled sheet is also disclosed in Japanese Patent Laid-Open No. 2008-260980, which claims that the component system still belongs to a higher Si-containing steel type, which requires a Si content of 1.5% to 3.5%, (%Si + %).
  • the slab heating temperature is very high, 1230 ⁇ 1320 °C, the finishing temperature is also above 1050 °C, and the coiling is required below 700 °C.
  • the disadvantage is heat.
  • Rolling slab heating The temperature is high, and MnS and A1N are easily dispersed in the hot rolling process, which deteriorates the magnetic properties and makes it difficult to descale. Summary of invention
  • the object of the present invention is to provide a high-efficiency non-oriented silicon steel manufacturing method with excellent magnetic properties, which is advantageous for the addition of texture elements, component control of harmful elements, and air-cooling time control during hot rolling process under the premise of ensuring magnetic properties. Cooperating with high-temperature coiling to achieve low-cost and efficient electrical steel production.
  • a method for manufacturing high-efficiency non-oriented silicon steel with excellent magnetic properties comprising the following steps:
  • the chemical composition weight percentage of the non-oriented silicon steel is: C ⁇ 0.0040%, Si: 0.1% to 0.8%, Ah 0.002 to 1.0%, Mn: 0.10% to 1.50%, P ⁇ 0.2%, Sb: 0.04% to 0.08%, S ⁇ 0.0030%, N ⁇ 0.0020%, Ti ⁇ 0.0020%, residual iron and unavoidable impurities; smelting and casting into slab according to the above components;
  • the cold-rolled sheet is heated to 800 ⁇ 1000 °C at a heating rate of ⁇ 15 ° (/8, and the holding time is 10s ⁇ 25s).
  • the annealing atmosphere is (volume ratio 30% to 70%) 3 ⁇ 4+ (volume ratio 70% ⁇ 30%) N 2 , and the dew point is controlled at -25 °C to -40 °C.
  • composition design of the present invention is a composition design of the present invention:
  • Si It is soluble in ferrite to form a replacement solid solution, which increases the resistivity of the matrix and reduces the iron loss. It is the most important alloying element of electrical steel, but Si deteriorates the magnetic induction. When the Si content reaches a certain level, its content continues to increase. The effect of reducing the iron loss is weakened, and the Si content of the present invention is 0.1 to 0.8%, more than 0.8%, and it is difficult for B50 to achieve high magnetic induction.
  • A1 soluble in ferrite increases matrix resistivity, coarsens grains, reduces iron loss, and also Deoxidation and nitrogen fixation, but it is easy to cause oxidation in the surface layer of the finished steel sheet.
  • A1 content exceeds 1.5%, smelting and casting is difficult, the magnetic induction is lowered, and processing is difficult.
  • Mn Compared with Si and A1, it can increase the electrical resistivity of steel, reduce iron loss, form stable MnS with unavoidable inclusions S, eliminate the magnetic damage of S, and prevent hot brittleness. It is also soluble in ferrite. The body forms a replacement solid solution and has the effect of reducing iron loss. Therefore, it is necessary to add 0.1% or more.
  • the Mn of the present invention is 0.10% to 1.50%, and the Mn content is less than 0.1%. The effect is not obvious, higher than 1.50%, the temperature of ACl is lowered, the recrystallization temperature is lowered, the ⁇ - ⁇ phase transformation occurs during heat treatment, and the deterioration is favorable for texture.
  • S It is harmful to both processing and magnetic properties. It forms fine MnS particles with Mn, hinders the grain growth of the finished product, severely deteriorates the magnetic properties, and forms low-melting FeS and FeS2 or eutectic with Fe, which is easy to cause hot work brittleness.
  • S ⁇ 0.003% or less, and more than 0.003% will greatly increase the amount of precipitation of the S compound such as MnS, and strongly inhibit the growth of crystal grains and deteriorate the iron loss.
  • the optimum control range of the present invention is S ⁇ 0.002%.
  • C Harmful to magnetic properties, it is an element that strongly hinders grain growth. At the same time, C is an element that expands the ⁇ phase region. Excessive C increases the amount of transformation between the ⁇ and ⁇ phases in the normalization process, greatly reducing the Acl point. The crystal structure acts as a refinement, causing an increase in iron loss.
  • the present invention has C ⁇ 0.004%, and the optimum range C ⁇ 0.0020%.
  • N It is easy to form fine dispersion nitride such as A1N, which strongly inhibits grain growth and deteriorates iron loss. N ⁇ 0.002% or less in the present invention, and more than 0.002% will greatly increase the precipitation amount of N compound such as A1N, and strongly hinder grain growth. The iron loss is degraded.
  • Sb Activated element, when it is segregated at the surface layer or surface grain boundary, it can reduce the oxidation in the surface layer, prevent the active oxygen from penetrating into the steel base along the grain boundary, improve the texture, and promote the (100) and (110) components.
  • the (111) component is reduced, and the B50 effect is very remarkable.
  • the present invention studies that Sb has the most significant effect in improving magnetic properties in the range of 0.04 to 0.08%.
  • metal Sb when added to electrical steel, it can improve the (100 ⁇ ⁇ uvw> texture component and is an effective element for improving the magnetic properties of electrical steel. Since metal Sb isolates grain boundaries and has a choice The ground influences the growth of recrystallized ferrite grains and weakens the rate of (111) grain growth. With the addition of Sb, the number of (111) grains in the rolled material gradually disappears.
  • the invention deeply studies the influence of the hot rolling process on the Sb grain boundary segregation, and finds that the Sb is improved.
  • the effect of the favorable texture is inseparable from the cooling process after hot rolling.
  • it should be slowly cooled at about 700 °C or kept at a temperature near 700 °C for a certain period of time.
  • Near 700 °C is the temperature at which Sb undergoes strong grain boundary segregation in non-oriented electrical steel.
  • the coiling temperature of the hot rolled sheet is closely related to the magnetic properties.
  • the high temperature coiling can reduce the fiber structure at the center of the hot rolled sheet and thicken the edge recrystallized layer.
  • the present inventors have found that a hot rolled sheet having a Si content of 0.1 to 0.8% is wound up at 720 ° C or higher, and the fibrous structure in the middle of the hot rolled sheet substantially disappears.
  • the present invention adopts a method in which the hot-rolled sheet is not normalized, and can obtain magnetic properties comparable to those of the conventional process.
  • the iron loss can reach 4.5W/kg or less, and the magnetic induction can reach 1.78T or more.
  • the segregation element Sb is added, and the production is carried out according to (2+30x Sb%;) s ⁇ t ⁇ 7s after rolling, which greatly reduces the amount of hot-rolled laminar cooling water.
  • the application of the present invention not only shortens the manufacturing cycle of steel grades, but also reduces the cost of high-efficiency electrical steel.
  • the high-efficiency motor steel produced by the method has stable performance.
  • the addition of Sn is not involved in the composition of the present invention, and the iron loss of the similar steel of the present invention is 0.2 to 1.5 lower than the magnetic property in the patent.
  • W/Kg the magnetic induction is at least 20 ⁇ 100 Gauss.
  • the iron loss is 0.1 ⁇ 0.2W/kg, and the magnetic induction is 0.1T higher than the corresponding.
  • Figure 1 shows the relationship between air cooling time and magnetic properties after hot rolling of 0.26% Si and 0.055% Sb.
  • Figure 2 shows the relationship between air cooling time and magnetic properties after hot rolling of 0.26% Si and 0.055% Sb.
  • Figure 3 is the metallographic structure of 0.26% Si, 0.055% Sb hot-rolled sheet at a coiling temperature of 650 °C.
  • Figure 4 is 0.26% Si, 0.055% Sb hot-rolled sheet at a coiling temperature of 720 °C.
  • Table 1 shows the results of the chemical composition steels in Table 1 using the production method of the present invention and the finished Espresso square.
  • Example 1 in Table 1 were subjected to magnetic measurement according to the process shown in Table 4, and the results of magnetic detection are shown in Table 4.
  • Table 4 Example Production Method and Magnetic Results
  • the control of the air cooling time after rolling is an important indicator affecting the magnetic properties of the finished product.
  • the short or too long air cooling time is unfavorable to the magnetic properties of the finished product.
  • the air cooling time after rolling in the present invention is controlled within the range of (2+30 X Sb%:) s t 7s, and the magnetic properties of the finished product are optimal.
  • the present invention relates to a method for producing high-efficiency non-oriented electrical steel with excellent magnetic properties, characterized in that a certain amount of grain boundary segregation element Sb is added during steel making, and 2+30x Sb is taken according to air cooling time after hot rolling. %:) s ⁇ t ⁇ 7s to control the air-cooling process of hot-rolled sheet, and at the same time use high-temperature coiling instead of hot-rolled sheet to obtain high-efficiency motor steel with excellent performance, thus solving the conventional process for producing high-efficiency non-oriented electrical steel. High, long manufacturing cycle and other issues.

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Description

一种磁性优良的高效无取向硅钢制造方法 发明领域
本发明涉及无取向电工钢的制造方法，特别涉及一种磁性优良的高效 无取向硅钢制造方法， 解决传统工艺生产高效无取向电工钢常化成本高、 制造周期长等问题。 背景技术
随着电力、 电器行业的进歩， 机电产品正朝着小型化、 高精度化、 高 效率化方向发展， 用普通冷轧硅钢片制造的铁芯难以满足要求， 开发低铁 损、高磁感的高效无取向系列电工钢产品替代现行普通冷轧硅钢片是机电 产品减小体积、 减轻重量、 节约铜铁消耗、 提高效率的主要途径。
高效无取向硅钢其磁性的主要特点是磁感高。传统上其制造特点是热 轧后， 利用热轧板常化， 使热轧板组织更均匀， 使再结晶晶粒增多， 防止 瓦垅状缺陷， 同时使晶粒和析出物粗化， 加强 （1 10 ) 和 （100 ) 组分， 减 少（1 1 1 )组分， 使磁性能明显提高。 为提高磁感， 一般常化温度在 950 °C 以上。 采用热轧板常化带来的问题一是制造成本高， 二是制造周期长。
中国专利 CN1288070公开一种无取向硅钢， 其成分为： C≤0.008%、 Si 0.2〜2.50%、 Mn 0.15〜0.8%、 Als残量〜 1 .50%、 B残量〜 0.0035%、 P+Sn/Sb0.08〜0.45%、 S≤0.0030%、 N≤0.003%， 余量为 Fe 以及不可避免 的夹杂。低温热轧、一次冷轧、干气或湿气退火的方法生产高效电机铁芯。
日本专利特开 2004- 169141提到成分为 1 .8%< ( Si + 2A1 ) ≤5%高牌号 热轧板免常化生产， 要求炼钢过程添加 REM、 Mg和 Ca的一种或两种以 上， 同时严格控制 Ti≤0.003%， 热轧时要求在 950 °C以上终轧， 700 °C以下 卷取。 其不足之处在于热轧生产工艺条件苛刻， 终轧温度高， 实际生产操 作和控制难度很大。
热轧板省略退火的专利还有日本专利特开 2008-260980， 该专利要求 成分体系，仍旧属于含 Si较高钢种，其要求 Si含量在 1 .5%〜3.5%， ( %Si + %A1)>1 .9% , 热轧时， 板坯加热温度很高， 1230〜1320 °C， 终轧温度也 在 1050 °C以上， 同时要求 700 °C以下卷取， 其不足之处在于热轧板坯加热 温度高， 在热轧过程中 MnS和 A1N易细小弥散析出， 恶化磁性能， 难以 除鳞。 发明概述
本发明的目的在于提供一种磁性优良的高效无取向硅钢制造方法，在 保证磁性能的前提下， 通过炼钢过程有利织构元素的添加、有害元素的成 分控制， 以及热轧过程空冷时间控制和高温卷取的配合， 实现低成本的高 效电工钢的生产。
为达到上述目的， 本发明的技术方案是：
一种磁性优良的高效无取向硅钢制造方法， 其包括如下歩骤：
1) 冶炼、 浇铸
无取向硅钢的化学成分重量百分比为： C≤0.0040%， Si: 0.1%〜 0.8%, Ah 0.002〜1.0%， Mn: 0.10%〜1.50%， P<0.2%, Sb: 0.04%〜 0.08%, S≤0.0030%， N<0.0020%, Ti<0.0020%, 余铁和不可避免杂 质； 按上述成分冶炼、 浇铸成铸坯；
2) 热轧、 酸洗
板坯加热温度 1100°C〜1150°C， 终轧温度 860°C〜920°C ; 轧 后空冷， 空冷时间： （2+30xSb%：) s≤t≤7s; 在≥720 条件下进行卷取；
3) 冷轧
以 70〜78%压下率轧制成目标厚度的冷轧板；
4) 退火
冷轧板以≥15 °( /8 的加热速度升温到 800〜1000°C， 保温时间 10s〜25s。
进一歩， 退火气氛为 （体积比 30%〜70%) ¾+ (体积比 70%〜30%) N2， 露点控制在 -25 °C〜- 40°C。
在本发明的成分设计中：
Si: 能溶于铁素体中形成置换固溶体， 提高基体电阻率， 降低铁损， 是电工钢最重要的合金元素， 但是 Si恶化磁感， 当 Si含量达到一定水平 时， 其含量继续增加， 降低铁损作用减弱， 本发明 Si含量为 0.1〜0.8%， 大于 0.8%， B50难以达到高磁感要求。
A1: 可溶于铁素体提高基体电阻率， 粗化晶粒， 降低铁损， 同时还可 以脱氧固氮， 但容易造成成品钢板表层内氧化。 A1含量超过 1.5%将使冶 炼浇注困难， 磁感降低， 且加工困难。
Mn: 与 Si、 A1—样可以增加钢的电阻率， 降低铁损， 可与不可避免 夹杂物 S形成稳定的 MnS， 消除 S对磁性的危害， 还可防止热脆， 其也 溶于铁素体形成置换固溶体， 有降低铁损的作用。 因此有必要添加 0.1% 以上的含量。 本发明 Mn为 0.10%〜1.50%， Mn含量低于 0.1%有利作用 不明显， 高于 1.50%， Acl温度降低， 再结晶温度降低， 热处理时发生 α 一 γ相变， 劣化有利织构。
Ρ: 0.2%以下， 在钢中添加一定的磷可以改善钢板的加工性， 但超过 0.2%时反而使钢板冷轧加工性劣化。
S: 对加工及磁性均有害， 其与 Mn形成细小的 MnS质点， 阻碍成品 退火晶粒长大， 严重恶化磁性， 与 Fe形成低熔点 FeS及 FeS2或共晶体， 易造成热加工脆性。 本发明 S≤0.003%以下， 超过 0.003%将使 MnS等 S 化物析出量大大增加， 强烈阻碍晶粒长大， 铁损劣化。 本发明最佳控制范 围 S≤0.002%。
C: 对磁性有害， 是强烈阻碍晶粒长大的元素， 同时 C是扩大 γ相区 的元素， 过量的 C使常化处理时 α与 γ两相区转变量增加， 大大降低 Acl 点， 对结晶组织起细化作用， 引起铁损增加。 本发明 C≤0.004%， 最佳范 围 C≤0.0020%。
N: 易形成 A1N等细小弥散氮化物， 强烈阻碍晶粒长大， 铁损劣化， 本发明 N≤0.002%以下， 超过 0.002%将使 A1N等 N化物析出量大大增加， 强烈阻碍晶粒长大， 铁损劣化。
Sb: 活化元素， 在表层或表层晶界处偏聚时， 可以减少表层内氧化， 防止活性氧沿晶界向钢基渗透， 改善织构， 促使 （100) 和 （110) 组分增 力口， （111)组分减少， 提高 B50效果十分显著。 本发明研究 Sb在 0.04〜 0.08%范围改善磁性能效果最显著。
在高效电机钢的研究中发现， 将金属 Sb 加入电工钢时， 它能提高 (100} <uvw>织构组分， 是提高电工钢磁性的有效元素。 由于金属 Sb将 晶界隔离并且有选择地影响再结晶铁素体晶粒长大， 削弱 (111)晶粒长大 的速度， 随着 Sb的加入， 轧材中的 (111)晶粒数逐渐消失。
本发明深入研究了热轧工艺对 Sb晶界偏析的影响， 研究发现 Sb改善 有利织构的作用与热轧后的冷却过程密不可分，为了充分发挥 Sb的有益作 用，应在 700 °C左右进行缓冷，或者在 700°C附近某一温度下保温一段时间。 而 700 °C附近正是 Sb在无取向电工钢中发生强烈晶界偏聚的温度。
参见图 1、 图 2， 基本成分为 0.26%Si、 0.52%A1、 0.65%Mn、 0.08%P、 0.055%Sb、 <0.0030% C、 <0.0020% N的钢坯， 经过热轧、 采用不同的空 冷时间， 然后 720 °C高温卷取， 冷轧， 860 °C退火， 可以看到， 空冷时间的 范围在 3.5〜7S之间， 磁性能处于较好水平。
参见图 3、 图 4， 热轧板卷取温度与磁性能密切相关， 高温卷取可以使 得热轧板中心部纤维组织减少， 边部再结晶层增厚。 本发明发现 Si含量为 0.1~0.8%的热轧板， 经过 720 °C以上的卷取， 热轧板中间的纤维状组织基 本消失。
本发明的有益效果
与传统无取向高效硅钢制造工艺相比，本发明采用热轧板不常化的方 法， 能够获得与传统工艺相当的磁性能。 铁损可以达到 4.5W/kg以下， 磁 感可以达到 1.78T 以上。 同时添加偏析元素 Sb， 按照 (2+30x Sb%；) s≤t≤7s 的轧后空冷时间进行生产， 大量减少了热轧层流冷却水的用量。本发明的 应用不仅能够做到缩短钢种的制造周期，同时还可以减少高效电工钢的制 造成本。
利用本方法生产的高效电机钢性能稳定， 与中国专利 CN1288070相 比， 本发明成分中不涉及 Sn的添加， 与其专利中的磁性能相比本发明类 似钢种的铁损比其低 0.2〜1.5W/Kg， 磁感比其高至少 20~100高斯。 与现 行的普通冷轧无取向电工钢类似成分相比铁损低 0.1~0.2W/kg， 磁感则比 对应高 0.1T以上。 附图说明
图 1为 0.26%Si， 0.055%Sb 热轧后空冷时间与磁性能的关系。
图 2为 0.26%Si， 0.055%Sb 热轧后空冷时间与磁性能的关系。
图 3为 0.26%Si， 0.055%Sb热轧板在卷取温度 650 °C下的金相组织照 图 4为 0.26%Si， 0.055%Sb热轧板在卷取温度 720 °C下的金相组织照 发明的详细说明
下面结合实施例对本发明做进一歩说明。
按表 1的组分冶炼，铸坯经加热、粗轧、精轧、高温卷取、酸洗、 70〜 78%压下率一次冷轧到 0.5mm的成品厚度、冷轧带钢经不同温度的最终退 火至成品。表 2为表 1中化学成份钢种采用本发明生产方法及成品爱泼斯 坦方圈测量的结果。
表 1 实施例化学成份
Figure imgf000007_0001
表 2实施例生产方法及磁性结果
终轧 热轧后空 卷取 再结晶
P15/50 B50 温度 冷时间 温度 退火
FDT ( °C ) s V °C S W/Kg T 实施例 1 880 4 720 820 4.38 1.796 实施例 2 860 5.5 720 820 3.62 1.787 实施例 3 920 6 720 880 4.07 1.793 实施例 4 900 6.5 720 860 3.43 1.782 实施例 5 870 7 720 880 3.82 1.794 比较例 1 880 0 720 820 4.63 1.765 比较例 2 860 0 720 820 3.79 1.759 比较例 3 920 0 720 880 4.46 1.776 比较例 4 900 0 720 860 3.84 1.753 比较例 5 870 0 720 880 4.24 1.768 从表 2可以看出： 在相同的终轧温度、 卷取温度和退火温度下， 与没 有添加 Sb且不进行轧后空冷的比较例钢种相比， 实施例中各成分的磁性 能优良， 铁损明显要其比低 0.1〜0.4W/Kg， B50要比其高 0.2T以上。
将实施例中表 1成分按照表 3所示的工艺处理进行磁性测量，磁性检 测结果如表 3所示。
表 3实施例生产方法及磁性结果
Figure imgf000008_0001
从上表可以看出，没有采用高温卷取的比较例 1〜4的成品磁性能要 显著低于经高温卷取的实施钢种。
将表 1中实施例 1成分按照表 4所示的工艺处理进行磁性测量， 磁 性检测结果如表 4所示。 表 4实施例生产方法及磁性结果
Figure imgf000009_0001
从上表中可以看出，轧后空冷时间的控制是影响成品磁性能的一个重 要指标， 空冷时间过短或者过长对成品的磁性能均不利。本发明轧后空冷 时间控制在 (2+30 X Sb%：) s t 7s这个范围内， 成品磁性能发挥最佳。
综上所述，本发明涉及一种优良磁性能的高效无取向电工钢的制造方 法， 其特点是炼钢过程中添加一定含量的晶界偏析元素 Sb、 热轧后按照 空冷时间 2+30x Sb%：) s≤t≤7s控制热轧板的空冷过程，同时利用高温卷取替 代热轧板常化， 获得性能优良的高效电机钢， 从而解决了传统工艺生产高 效无取向电工钢常化成本高、 制造周期长等问题。

Claims

权 利 要 求 书
1. 一种磁性优良的高效无取向硅钢制造方法， 其包括如下歩骤：
5) 冶炼、 浇铸
无取向硅钢的化学成分重量百分比为： C≤0.0040%， Si: 0.1%〜 0.8%, Ah 0.002〜1.0%， Mn: 0.10%〜1.50%， P<0.2%, Sb: 0.04%〜 0.08%, S≤0.0030%， N<0.0020%, Ti<0.0020%, 余铁和不可避免杂 质； 按上述成分冶炼、 浇铸成铸坯；
6) 热轧、 酸洗
板坯加热温度 1100°C〜1150 °C， 终轧温度 860 °C〜920 °C ; 轧 后空冷， 空冷时间： （2+30xSb%：) s≤t≤7s; 在≥720 条件下进行卷取；
7) 冷轧
以 70〜78%压下率轧制成目标厚度的冷轧板；
8) 退火
冷轧板以≥15 °( /8 的加热速度升温到 800〜1000 °C， 保温时间 10s〜25s。
2. 如权利要求 1所述的磁性优良的高效无取向硅钢制造方法， 其特征是， 退火气氛为 （体积比 30%〜70%) ¾+ (体积比 70%〜30%) N2， 露点控制 在 -25 °C〜- 40 °C。
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CN102453844B (zh) 2013-09-04
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JP2013525596A (ja) 2013-06-20
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MX2012010529A (es) 2012-10-05
KR101407009B1 (ko) 2014-06-13
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