WO2013134897A1 - 热轧硅钢的制造方法 - Google Patents

热轧硅钢的制造方法 Download PDF

Info

Publication number
WO2013134897A1
WO2013134897A1 PCT/CN2012/000401 CN2012000401W WO2013134897A1 WO 2013134897 A1 WO2013134897 A1 WO 2013134897A1 CN 2012000401 W CN2012000401 W CN 2012000401W WO 2013134897 A1 WO2013134897 A1 WO 2013134897A1
Authority
WO
WIPO (PCT)
Prior art keywords
heating
silicon steel
section
slab
furnace
Prior art date
Application number
PCT/CN2012/000401
Other languages
English (en)
French (fr)
Inventor
张华伟
吴亚萍
龚羽
孙业中
黑红旭
Original Assignee
宝山钢铁股份有限公司
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
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 US14/372,689 priority Critical patent/US9496078B2/en
Priority to EP12871183.5A priority patent/EP2826871B1/en
Priority to IN1793MUN2014 priority patent/IN2014MN01793A/en
Priority to MX2014010516A priority patent/MX357221B/es
Priority to KR1020147025196A priority patent/KR101609174B1/ko
Priority to RU2014132737/02A priority patent/RU2591788C2/ru
Priority to JP2014561247A priority patent/JP6283617B2/ja
Publication of WO2013134897A1 publication Critical patent/WO2013134897A1/zh

Links

Classifications

    • 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
    • H01F1/147—Alloys characterised by their composition
    • H01F1/14766—Fe-Si based alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/041—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing involving a particular fabrication or treatment of ingot or slab
    • 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
    • C21D8/1205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular fabrication or treatment of ingot or slab
    • 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
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/70—Furnaces for ingots, i.e. soaking pits
    • 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
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic 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
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/05—Grain orientation

Definitions

  • the present invention relates to a method for producing hot rolled silicon steel, and more particularly to a method for improving the quality defects of silicon steel edges in the manufacture of hot rolled silicon steel. . Background technique
  • the edge of silicon steel with severe stress concentration and temperature change is prone to various defects during the rolling process, which affects the overall quality of silicon steel, reduces the product yield, and reduces production efficiency.
  • the edge linear defect is one of the common edge defects of hot rolled silicon steel. Studies have shown that the corners of the slab are always in a low temperature and high stress state during the rolling process. During the rolling, the inward friction of the rolling stock causes the corner metal to be strongly tensile and finally flows to the rolling.
  • Patent Document 1 discloses a continuous casting mold by setting the side walls of the crystallizer short plate into a circular arc shape, and the four corners are rounded to obtain a curved rounded side of the casting blank, so that the slab is No edge curling occurs during hot rolling, and excessive cooling of the corner portions is avoided to eliminate longitudinal strip black lines and warp defects.
  • Patent Document 2 discloses a method for obtaining a good surface quality of silicon steel by controlling a temperature gradient of a surface of a slab and a position of a certain depth at the time of rough rolling and finish rolling of silicon steel.
  • Document 3 uses a hole-shaped roll and a convex pressure widening machine (SSP) module to form a concave shape on the side of the slab to avoid the occurrence of defects. It has certain disadvantages: the grooved roll is prone to severe scratches, and the convex SSP module Causes instability of the press resulting in unstable rolling.
  • SSP convex pressure widening machine
  • the inventors conducted repeated and extensive experiments and found that in the method of manufacturing hot-rolled silicon steel, by changing the heating process, the defect occurrence rate of the edge portion of the silicon steel can be well reduced, and further, the rough rolling process is changed. The incidence of defects in the edge of the silicon steel can be further reduced.
  • the inventors completed the present invention based on the above findings.
  • the present invention aims to provide a method for producing hot-rolled silicon steel, which can achieve the purpose of improving the edge defects of silicon steel by changing the heating process and the rough rolling process, and can produce heat with good surface quality by the manufacturing method of the present invention.
  • Rolled silicon steel is a method for producing hot-rolled silicon steel, which can achieve the purpose of improving the edge defects of silicon steel by changing the heating process and the rough rolling process, and can produce heat with good surface quality by the manufacturing method of the present invention.
  • a method for producing hot-rolled silicon steel comprising: a heating step, a rough rolling step, and a finishing rolling step for a silicon steel slab, wherein the heating step is performed in a heating furnace, and the heating furnace is divided into a preheating section, a heating section, and Soaking section,
  • the preheating section satisfies the following formula (1),
  • the soaking section satisfies the following formula. (2-1) or (2-2),
  • T s the heating amount of the soaking section, that is, the temperature difference between the temperature at which the entire slab is just discharged and the end of the heating section, unit: . C;
  • the heating section heating amount satisfies the following formula (3):
  • Heating section heating amount (the temperature of the whole slab just out of the furnace - the heating section of the soaking section) - the temperature of the preheating section (3)
  • the preheating section refers to the distance from the furnace to the 1/6 of the furnace ⁇ 1/3 of the length of the furnace;
  • the soaking section refers to a distance from the furnace to a furnace length of 1/6 to 1/3 of the furnace;
  • the heating section refers to a portion between the preheating section and the soaking section.
  • the rough rolling is performed under a horizontal pressure of 3-8 passes, and the cumulative reduction ratio is 70-90%.
  • the time from the completion of the entire slab to the completion of the rough rolling is not more than 360 seconds.
  • the incidence of edge defects in the production of hot-rolled silicon steel can be reduced, so that hot-rolled silicon steel having a good surface quality can be produced.
  • Figure 1 shows the metal flow pattern of the rough rolled corners of the slab.
  • Fig. 2 is a view showing the cross-sectional temperature distribution of the slab obtained by the heating process of the present invention.
  • Fig. 3 shows a rough-rolled intermediate blank having a concave side surface obtained by the heating method of the present invention.
  • FIG. 4 and 5 are photographs showing linear crack defects in the edge of hot rolled silicon steel (Fig. 4 is an in-line inspection photograph, and Fig. 5 is a physical photograph).
  • Fig. 6 is a photograph showing a side portion of a silicon steel manufactured by the heating method of the present invention.
  • Figure 7 is a schematic view showing the manufacturing process of hot rolled silicon steel. The best way to implement the invention
  • the method for producing hot-rolled silicon steel mainly includes a heating step of the silicon steel slab, a rough rolling step, and a finish rolling step, and further, it may be rolled up into a silicon steel coil, that is, a silicon steel hot coil, by a winding process as needed.
  • the inventor based on the actual temperature measurement, observation, and simulation calculations, and concluded that for hot-rolled silicon steel, the edge defects are generated because the upper and lower edges of the slab are in the horizontal rolling and vertical rolling processes of rough rolling.
  • the parts are respectively turned over to the upper and lower surfaces to form (as shown in Fig. 1).
  • the edge of the slab is most affected by air cooling and has the lowest temperature. After rolling to the surface of silicon steel, defects are formed. Since the edge temperature is low, the deformation resistance is inconsistent with the surrounding structure after the inversion, so that cracks occur during the rolling extension, and welding cannot be performed in the subsequent rolling to form defects in the rolling direction.
  • the slab edge metal is in the two-phase region during rough rolling. Since the deformation stress of ferrite is 1/4 lower than the austenite phase, the deformation is concentrated in the ferrite. The bulk phase is likely to cause an increase in local deformation during the subsequent rolling process, resulting in a final fracture of the ferrite phase to form a defect.
  • edges of the slabs and the side surfaces are formed by burns and defects are left on the edges of the steel sheet to become edge-line defects.
  • the slab edge oxide layer is difficult to remove and remains on the edge of the steel sheet surface to become a linear defect in the edge.
  • the quality of the edge portion of the hot-rolled silicon steel is improved, and only the heating step and the rough rolling step are involved.
  • the finishing rolling step is not particularly limited, and the finishing step in the current method for producing hot-rolled silicon steel may be used.
  • the heating step is carried out in a heating furnace.
  • the heating furnace is not particularly limited, and a step beam type heating furnace commonly used in hot rolled silicon steel may be used, and the burner type may be a conventional burner or a regenerative burner.
  • the hot-rolled silicon steel heating furnace is generally divided into three sections: a preheating section, a heating section and a soaking section. But some new hot rolling heating
  • the furnace does not have strict above-mentioned sections (such as a pulse heating furnace), and the sections described in the present invention are defined by the following principles:
  • the preheating section means from the household to the distance of the furnace 1/6 ⁇ 1 /3 furnace length;
  • the soaking section refers to a distance from the furnace to a furnace length of 1/6 to 1/3 of the furnace;
  • the heating section refers to a portion between the preheating section and the soaking section.
  • the heating characteristics of the existing heating system are that the temperature of the preheating section is low and the temperature of the heating section is high, and the temperature of the soaking section is equivalent to the temperature of the tapping section, so that the heat absorbed by the slab in the heating section continues to be transmitted to the core to reach the slab.
  • the purpose of homogenizing the cross-section temperature is that the silicon steel with a specific steel grade produced by this heating system has a high incidence of edge-line defects, which is severely more than 80%, and it is often necessary to remove the defects by trimming.
  • the requirements for the heating process are as follows:
  • the purpose is to obtain the cross-sectional temperature distribution of the slab shown in Fig. 2, that is, to obtain a higher slab surface temperature, in particular to obtain a higher slab edge temperature.
  • Fig. 2 The purpose is to obtain the cross-sectional temperature distribution of the slab shown in Fig. 2, that is, to obtain a higher slab surface temperature, in particular to obtain a higher slab edge temperature.
  • Fig. 3 is a rough-rolled intermediate blank having a concave side obtained after the heating process is adjusted.
  • the soaking section satisfies the following formula (2-1) or (2-2),
  • ⁇ 5 represents the heating amount of the soaking section, that is, the difference between the temperature at which the entire slab is discharged and the temperature of the entire slab at the end of the heating section, in units of: . C.
  • the temperature of the preheating section is increased because the temperature is lowered in the heating section to be described later, in order to ensure the same production.
  • Rhythm without increasing the slab in the furnace time, it is necessary to increase the heating temperature of other sections to compensate for the effect of the temperature drop of the heating section on the heat absorption of the slab.
  • the preheating section satisfies the following formula (1),
  • V Tn xx 25°C7 mm ( 1 )
  • Reducing the temperature of the heating section can prevent the edge of the slab from being over-fired, avoiding the linear defects caused by the above reasons (3.); at the same time, the oxidation process is accelerated due to the high heating temperature, and the composition of the oxide also increases with temperature. It is easy to form a layered iron sheet when it is baked, and it is difficult to remove it. Therefore, lowering the temperature of the heating section can also avoid edge line defects caused by the above reason (4).
  • the furnace gas temperature setting is not specified, and can be determined according to the preheating section temperature and the heating section of the soaking section.
  • the heating section temperature is determined according to actual production, specifically: the heating section slab heating amount satisfies the following formula (3):
  • Heating section slab heating amount (outlet temperature - soaking section heating amount) - preheating section end temperature (3)
  • the tapping temperature refers to the temperature at which the entire slab is just discharged, that is, the target temperature at which the slab is heated;
  • the heating amount of the soaking section is as described above, and refers to the difference between the temperature of the entire slab and the temperature of the entire slab at the end of the heating section, and the unit is °C;
  • the temperature at the end of the preheating section refers to the temperature at which the entire slab just leaves the preheating section.
  • the heating section furnace temperature is set in combination with the actual production rhythm (the slab travels in the furnace).
  • the amount of side pressure refers to the amount of actual width reduction caused by the slab receiving a deformation force in the width direction.
  • Deformation force can come from The vertical roller can also come from a pressure widening machine.
  • the vertical roll side pressure refers to the actual reduction of the vertical roll to the slab, that is, the amount of reduction of the slab after passing through the vertical roll;
  • Each reduction amount refers to the amount of reduction of the slab after each vertical roll rolling
  • Horizontal pressing means that the slab is deformed by the pressure of the horizontal roller.
  • the cumulative reduction ratio refers to the percentage of the thickness of the slab rolling final exit and the thickness of the rolling start inlet.
  • the side pressure of the SSP refers to the amount of slab reduced by SSP
  • the rough rolling process can be carried out using the rough rolling equipment commonly used in the conventional hot rolled silicon steel manufacturing method.
  • the rough rolling equipment can use a two-roll mill or a four-roll mill.
  • the 1-6 passes vertical roll side pressure is used, and the amount of each press is 10-40 cm, preferably 3 passes of the vertical roll side pressure, and the amount of each press is 30 cm;
  • the cumulative reduction ratio is 70-90% using 3-8 passes of horizontal roll.
  • the slab is taken out from the heating furnace to the intermediate roller table, and the number of water passages in the rough rolling zone is not more than four.
  • the rough rolling In order to prevent the surface temperature drop from being too large, the rough rolling should be produced quickly, and the time from the completion of the entire slab to the end of the rough rolling is not more than 360 seconds.
  • the SSP can also be used in the rough rolling process as needed.
  • the SSP module with a concave profile helps to reduce the distance between the edges of the edge defects, so that the amount of trimming in the post-process can be reduced, thereby increasing the yield. If SSP is used, the side pressure is required to be in the range of 10-180 cm.
  • the improvement of the edge quality of the hot-rolled silicon steel does not involve an improvement of the finish rolling process, and therefore there is no particular limitation on the finish rolling process, and the finishing rolling equipment commonly used in the current hot-rolled silicon steel manufacturing method is used. Yes, usually 5-7 rack 4 roll mill. 4. Winding process
  • the hot rolled silicon steel of the present invention can also be rolled up into a hot rolled silicon steel coil, that is, a silicon steel hot coil, as needed.
  • a hot rolled silicon steel coil that is, a silicon steel hot coil
  • the raw materials and equipment used in production are as follows:
  • Slab material The present invention uses a silicon steel slab of different silicon contents produced by Baoshan Iron and Steel Co., Ltd., and a commercially available product can also be used.
  • Heating furnace walking beam type heating furnace, regenerative burner
  • SSP Pressure widening machine
  • Rough rolling equipment double-stand, the first frame is a two-roll mill, there is no vertical roll, and the second frame is a reversible rolling four-high mill with vertical rolls;
  • Finishing equipment 7-stand four-roll mill; Example 1 ⁇ 5
  • Silicon steel slab A (silicon content: 2.1% by weight) The hot rolled silicon steel was produced in the following steps.
  • the slabs of Examples 1 to 5 were respectively placed in a heating furnace, and were sequentially discharged through a heating process of three stages of a preheating section, a heating section, and a soaking section.
  • the side steel pressure, the horizontal reduction amount, the number of water passages in the rough rolling zone in the descaling water step, and the rough rolling time are set, and the silicon steel slab after the completion of the heating process is sent to the rough rolling equipment. Rough rolling process.
  • a pressure widening machine was used in the embodiment 5, and the pressure widening machine was not used in the examples 1 to 4.
  • the rough rolled slab is sent to a finishing rolling mill for a finish rolling process.
  • the belt speed is 9-l lm/s and the target thickness is 2.0-2.6 mm. Then, each of the obtained hot-rolled silicon steels was evaluated for the incidence of edge defects.
  • the silicon steel slab A (the silicon content was 2.1% by weight) in Examples 1 to 5 was used, and the examples 6 to 10 were produced in the same manner as in Examples 1 to 5 except that the rough rolling step was carried out as shown in Table 2. Silicon steel.
  • the heating process uses the method of the present invention, and the rough rolling process is still performed using the prior art Example 6-10, and the edge defect occurrence rate is 3.5% to 5.0%, which is slightly higher than the heating process and the rough rolling process.
  • Silicon steels of Examples 1 to 5 which were all produced in accordance with the method of the present invention.
  • Example 1 1 ⁇ 15
  • a silicon steel slab B having a silicon content of 0.5% by weight was used, and the silicon steel of Examples 1 to 15 was produced in the same manner as in Example 1 5 except that the heating process was as shown in Table 3, and according to Example 1 ⁇ 5 The same method was used to evaluate the incidence of edge defects.
  • Comparative Examples 1 to 3 were made of silicon steel slab A (silicon content: 2.1% by weight), and Comparative Examples 4 to 5 were made of silicon steel slab B (silicon content: 0.5% by weight), and Comparative Examples 1 to 5 were respectively shown in Table 4.
  • silicon steels of Comparative Examples 1 to 5 were produced, and the incidence of edge defects was evaluated in the same manner as in Examples 1 to 5, except that the heating step and the rough rolling step were sequentially performed. .
  • the hot rolled silicon steel produced according to the current manufacturing method that is, Comparative Examples 1 to 5
  • the edge defect occurrence rates were 11%, 8%, 7%, 8%, and 6%, respectively, which were significantly larger than the present invention.
  • the use of the heating crucible of the present invention can significantly reduce the incidence of edge defects, and the heating step and the rough rolling step of the present invention can be employed. Better reduce the incidence of edge defects. Therefore, it is desirable to simultaneously employ the heating process and the rough rolling process of the present invention.
  • the manufacturing method of the present invention can effectively reduce the edge defects of the hot rolled silicon steel, and can produce hot rolled silicon steel having a good surface quality, and therefore can be widely applied to the production of silicon steel hot coil.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Mechanical Engineering (AREA)
  • Organic Chemistry (AREA)
  • Metallurgy (AREA)
  • Materials Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Manufacturing & Machinery (AREA)
  • Electromagnetism (AREA)
  • Power Engineering (AREA)
  • Dispersion Chemistry (AREA)
  • Metal Rolling (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)

Abstract

一种热轧硅钢的制造方法，包括，对硅钢板坯的加热工序、粗轧工序和精轧工序、所述加热工序分为预热段、加热段和均热段，其中预热段满足下述式（1）。式中，VTp为预热段升温速率，单位为°C/min，t为板坯在加热炉内的总加热时间，t=180-240min，Tc为板坯入炉的初始温度，单位为°C；通过上述公式改变加热工序和粗轧工序，能够降低热轧硅钢制造中的边部缺陷发生率，生产具有良好表面质量的热轧硅钢。

Description

热轧硅钢的制造方法 技术领域
本发明涉及热轧硅钢的制造方法， 具体地， 涉及热轧硅钢制造中的硅钢边部质量缺陷 的改善方法。 . 背景技术
在热轧硅钢生产过程中， 应力集中和温度变化剧烈的硅钢边部， 易在轧制过程中产生 各种缺陷， 从而影响硅钢的整体质量， 降低产品的成材率， 进而降低生产效益。 其中， 边 部线状缺陷是热轧硅钢常见的边部缺陷之一。 有研究表明， 板坯边角部在轧制过程中始终 处于低温和高应力应变状态， 平轧时轧辊对轧件向内的摩擦力造成角部金属受到强烈的拉 应力作用并最终流动到轧件上表面， 随着平轧后道次的进行， 新生成的边界推动着原始的 边界向远离板坯边部方向移动， 而同时强烈的拉应力状态有可能诱发"黑线"缺陷的产生。 目前， 已有各种改善上述边部缺陷的报道。例如，专利文献 1公布了一种连铸结晶器， 通过将结晶器短板侧壁设置成圆弧形， 四个角设置成圆角， 获得弧形圆角的铸坯侧面， 使 板坯在热轧过程中不出现棱角翻边， 避免边角部分的过快冷却来消除纵向条状黑线、 翘皮 缺陷。 专利文献 2公布了通过控制硅钢粗轧、 精轧时的板坯表面与一定深度位置的温度梯 度来获得良好硅钢表面质量的方法。 文献 3 使用孔型辊和凸形压力调宽机 （SSP ) 模块对 板坯侧面进行凹形成形来避免缺陷的产生，具有一定的缺点：孔型辊容易产生严重的划伤， 凸形 SSP模块造成压下不稳定从而导致轧制不稳定。 文献 4、 5是通过数值模拟计算的方 式研究粗轧时板坯边角部金属在立一平轧制过程中的基本流动规律， 对不同立辊形状对轧 件边角部金属流动的影响规律作了计算。 但该研究结果没有经过生产验证， 且同样是属于 粗轧立辊压下的改进方法。 文献 6是为了消除其生产过程中的机械损伤而对粗轧机立辊进 行了改进设计和改造。 另外， 生产实践中也有人尝试对所使用的压力调宽机 （SSP ) 模块 进行改造， 以对板坯侧面进行凹形成形，但由于凸面 SSP模块在轧制时与板坯接触不稳定， 造成两侧金属流动不对称， 在其后的粗轧过程中板形控制困难。 但， 至目前为止的文献中， 均是研究粗轧立辊和轧件形状对缺陷距边部距离 （边距） 的模拟计算和实际改进， 目前尚无通过改变轧件温度， 特别是改变轧件横断面温度分布来 消除、 改善缺陷的报道。 现有技术文献：
1.中国实用新型专利 ZL200720067413.7
2.美国专利 US5572892A
3.山口晴生,草场芳昭，山田建夫. 不锈钢钢板边缘裂纹缺陷控制技术. 国外钢 铁, 1996(12):48-52.
4. Xiong Shangwu, J. M. C. Rodrigues, P. A. F. Martins. Threedimensional modelling of the vertical-horizontal rolling process [J], Finite Elements in Analysis and Design, 2003, 39： 1023-1037.
5. Xiong Shangwu , Liu Xianghua ， Wang Guodong ， et al . Three-dimensional thermo-mechanical finite element simulation of the vertical-horizontal rolling process[J] . Journal of Materials Processing Technology . 2001 , 11： 89 -97.
6. 高文芳， 颜正国， 宋 平， 饶克伟， 陈方武， 孔勇江. 荫罩框架钢冷轧薄板边部线状 缺陷研究 [J], 炼钢， 2003, 19(1). 发明的公开
鉴于上述技术问题， 本发明人进行了反复大量的试验， 发现， 在热轧硅钢的制造方法 中， 通过改变加热工序， 可以很好地降低硅钢边部的缺陷发生率， 进而， 改***轧工序可 以进一步降低硅钢边部的缺陷发生率。 发明人基于上述发现， 完成了本发明。
艮 P， 本发明旨在提供一种热轧硅钢的制造方法， 通过改变加热工序和粗轧工序， 达到 改善硅钢边部缺陷的目的， 通过本发明的制造方法， 能够生产具有良好表面质量的热轧硅 钢。
具体地， 本发明的技术方案如下：
1.一种热轧硅钢的制造方法， 包括： 对硅钢板坯的加热工序、 粗轧工序和精轧工序， 所述加热工序在加热炉内进行， 加热炉分为预热段、 加热段和均热段，
其特征在于，
预热段满足下述式 （1 )，
220min 100°C r。〜 . ,八
Τρ— > χ X 25°C / mm ( 1 )
τΓ + 200°c ·' 预热段升温速率， 单位： °C/min，
t : 板坯在加热炉内的总加热时间， t=180~240min， '板坯入炉初始温度， 单位： °c ;
均热段满足下述式. (2-1 ) 或 （2-2 )，
当硅钢中的硅含量≥1.5重量％时， 满足 - 10°C≤rs≤30°C (2-1 ) 当硅钢中的硅含量 < 1.5重量％时， 满足 10°C≤rs≤80°C (2-2 ) 其中， Ts： 均热段升温量，即整个板坯刚出炉的温度与加热段末的温度差，单位： 。C； 加热段升温量满足下述式 （3 ):
加热段升温量 = (整个板坯刚出炉的温度-均热段升温量） - 预热段末温度 （3 ) 所述预热段是指从入炉处起至距离该入炉处 1/6〜1/3炉长的距离；
所述均热段是指从出炉处起至距离该出炉处 1/6〜1/3炉长的距离；
所述加热段是指预热段与均热段之间的部分。
2.根据 （1 ) 所述的热轧硅钢的制造方法， 在所述粗轧工序中， 使用 1-6 道次立辊侧 压。
3. 根据 （2 ) 所述的热轧硅钢的制造方法， 所述立辊侧压的每次压下量为 10-40cm。
4. 根据 （2 ) 所述的热轧硅钢的制造方法， 粗轧使用 3-8 道次水平压下， 累计压下率 70-90%。
5. 根据 （2 ) 所述的热轧硅钢的制造方法， 自整个板坯刚出炉至粗轧末道次轧制完毕 的时间不超过 360秒。
6. 根据 （2 ) 所述的热轧硅钢的制造方法， 在粗轧工序中使用压力调宽机， 压力调宽 机的侧压量在 10〜180cm的范围内。
发明效果
根据本发明的热轧硅钢的制造方法， 能够降低热轧硅钢制造中的边部缺陷发生率， 从 而能够生产具有良好表面质量的热轧硅钢。 附图说明
图 1表示板坯粗轧边角部金属流动规律。
图 2表示本发明的加热工序获得的铸坯断面温度分布。
图 3表示通过本发明的加热方法获得的粗轧后的具有凹形侧面的中间坯。
图 4、 图 5是显示热轧硅钢边部线状裂纹缺陷的照片 （图 4为在线检测照片， 图 5为 实物照片）。 图 6表示通过本发明的加热方法制造出的硅钢边部照片。
图 7是热轧硅钢的制造过程示意图。 实现本发明的最佳方式
热轧硅钢的制造方法主要包括硅钢板坯的加热工序、 粗轧工序和精轧工序， 进而， 还 可以根据需要通过卷取工序将其卷起制成硅钢卷， 即硅钢热卷。
发明人根据生产实际测温、 观察、 模拟计算， 得出结论， 对于热轧硅钢， 边部缺陷的 产生是因为在粗轧的水平轧制和立辊轧制过程中， 板坯侧面上下棱边部分别翻转至上下表 面而形成 （如图 1所示）。 对于不同钢种， 棱边翻转至表面后， 有 4种可能的形成机理。
原因 （1 )
对于热导率低、 塑性差的钢种： 板坯棱边受空冷影响最大， 温度最低， 经轧制翻转到 硅钢表面后形成缺陷。 由于棱边温度低， 翻转后与周围组织变形抗力不一致， 因而在轧制 延展时产生裂纹， 且在随后的轧制中不能焊合， 形成沿轧制方向的缺陷。
原因 （2 )
对于 Y - α 相变温度较高的钢种： 板坯棱边部金属在粗轧时处于两相区， 由于铁素体 的变形应力比奥氏体相低 1 / 4， 变形集中在铁素体相， 在后续的轧制过程中易造成局部变 形增加， 导致铁素体相最终断裂而形成缺陷。
原因 （3 )
易发生过烧钢种： 板坯棱边、 侧面因过烧而形成缺陷遗留在钢板表面边部成为边部线 状缺陷。
原因 （4 )
铁皮难去除的钢种： 板坯棱边氧化层难以去除而遗留在钢板表面边部成为边部线状缺 陷。
本发明中， 改善热轧硅钢边部质量， 仅涉及加热工序和粗轧工序， 对于精轧工序没有 特别限制， 使用目前的热轧硅钢的制造方法中的精轧工序即可。
以下对本发明所涉及的各个工序进行详细说明。 ' 1.加热工序
加热工序在加热炉内进行， 对于加热炉没有特别限定， 可以使用热轧硅钢中常用的步 进梁式加热炉， 烧嘴类型可以是常规烧嘴或蓄热式烧嘴。
热轧硅钢的加热炉一般分为三个段： 预热段、 加热段和均热段。 但某些新式热轧加热 炉没有严格的上述分段 （比如脉冲式加热炉）， 本发明中所述的各段按以下原则定义： 所述预热段是指从 户处起至距离该入炉处 1/6〜1/3炉长的距离；
所述均热段是指从出炉处起至距离该出炉处 1/6〜1/3炉长的距离；
所述加热段是指预热段与均热段之间的部分。
现有的加热制度的加热特点是预热段温度较低而加热段温度高， 同时均热段温度和出 炉温度相当， 以使板坯在加热段吸收的热量继续向芯部传导， 达到板坯横断面温度均匀化 的目的。 但使用这种加热制度生产的特定钢种的硅钢的边部线状缺陷发生率很高， 严重的 可达 80%以上， 往往需要通过切边来去除缺陷。
本发明中， 对加热工序的要求如下：
( 1 )提高均热段温度
目的是为了获得图 2所示的板坯横断面温度分布， 即获得较高的板坯表面温度， 特别 是获得了较高的板坯棱边部温度。 其目的有 3个。
① 消除因上述原因 （1 ) 而产生的缺陷： 较高的板坯棱边部 （温度） 提高了其在粗轧 时的塑形， 降低了翻边后的棱边与其周边结构的延展性差异， 降低缺陷程度或避免了缺陷 的产生。
② 消除因上述原因（2 )而产生的缺陷: 由于板坯棱边部在加热时获得了较高的温度， 粗轧过程中处于相变点以上 （或到粗轧最后道次时才发生相变）， 避免了由于相变而产生 缺陷。
③ 粗轧时表面横向延展大， 减少缺陷距离边部距离： 上下表面由于温度高而具有较 小的变形抗力， 轧制时获得较大延展， 减少了棱边部翻边至表面的边距。 该结果已经为实 际生产所证实， 图 3就是加热工艺调整后获得的粗轧后的具有凹形侧面的中间坯。
因此， 在本发明中， 均热段满足下述式 （2-1 ) 或 （2-2 )，
当硅钢中的硅含量≥1.5重量％时， 满足- 10°C≤rs≤30°C (2-1 ) 当硅钢中的硅含量 < 1.5重量％时， 满足 10°C≤7 ≤80°C (2-2) 其中， Γ5 表示均热段升温量， 即整个板坯出炉时的温度与整个板坯在加热段末的温 度的差， 单位： 。C。
通过提高均热段温度， 可以消除由于上述原因 （1 )、 ( 2 ) 而产生的缺陷。
(2 ) 提高预热段温度
在本发明中， 提高预热段温度是由于在后述的加热段中降低了温度， 为保证同样生产 节奏， 不增加板坯在炉时间， 必须提高其它段的加热温度才可以弥补因加热段温度降低对 板坯吸热的影响。
因此， 预热段满足下述式 （1 )，
T 220min 100°C - ςο„. . . . .
VTn > x x 25°C7 mm ( 1 )
Tp t Tc + 200°C 其中， VTP : 预热段升温速率， 单位： °C7min，
t 板坯在加热炉内的总加热时间， t=180~240min， :板坯入炉初始温度， 单位： 。C ;
( 3 ) 降低加热段温度
降低加热段温度可以防止板坯棱边部过烧， 避免因上述原因（3.)而产生的线状缺陷； 同时由于加热温度高时氧化过程加快， 氧化物的成分也随温度的升高而改变， 出炉时易形 成层状铁皮， 难以去除， 因此降低加热段温度还可以避免由于上述原因 （4 ) 而产生的边 部线状缺陷。
但实际上， 加热段由于在炉时间不同、 出炉温度不同， 因此炉气温度设定不做具体要 求， 可以根据预热段温度与均热段升温量来确定。
由于本技术已经对预热段和均热段加热方法进行了限定， 因此加热段温度根据实际生 产时确定， 具体而言： 加热段板坯升温量满足下述式 （3 ) :
加热段板坯升温量 = (出炉温度-均热段升温量） - 预热段末温度 （3 ) 所述出炉温度是指整个板坯刚出炉时的温度， 也即板坯加热的目标温度；
所述均热段升温量如前所述， 是指整个板坯刚出炉的温度与整个板坯在加热段末的温 度的差， 单位： °C ;
所述预热段末温度是指整个板坯刚离开预热段时的温度。
根据以上计算的加热段升温量， 结合实际生产节奏 （板坯在炉内行进速度） 设定加热 段炉气温度。
2.粗轧工序
本发明中， 对粗轧工序中的各个术语定义如下：
侧压量是指板坯收到宽度方向上的变形力而导致的实际宽度减小量。 变形力可以来自 立辊， 也可以来自压力调宽机。
立辊侧压是指立辊对板坯的实际压下量， 即板坯经立辊后的减宽量；
每次压下量是指板坯每次经过立辊轧制后的减宽量；
水平压下是指板坯在受到水平辊的压力而产生变形。
累计压下率是指板坯轧制终了出口厚度与轧制开始入口厚度的百分比。
SSP的侧压量是指板坯经过 SSP压下后的减宽量；
本发明中， 可以使用现有的热轧硅钢制造方法中常用的粗轧设备进行粗轧工序。 粗轧 设备可以使用两辊轧机或四辊轧机。
关于粗轧工序中各个参数的设定， 可以参照目前通用的参数。 但是， 如果将粗轧工序 中的部分参数设定如下， 可以进一步消除热轧硅钢的边部缺陷发生率。
( 1 ) 侧压量
本发明中， 使用 1-6道次立辊侧压， 每次压下量为 10-40cm， 优选 3道次立辊侧压,， 每 次压下量为 30cm;
(2 ) 水平压下
本发明中， 使用 3-8道次水平辊压下， 累计压下率为 70-90%。
( 3 ) 除鳞水
为防止表面温降过大， 板坯自加热炉抽出至中间辊道， 粗轧区域使用水道次数不多于 4 道。
(4 ) 粗轧时间
为防止表面温降过大， 粗轧应快速生产， 自整个板坯刚出炉至粗轧末道次轧制完毕的 时间不超过 360秒。
( 5 ) 压力调宽机 ( SSP)
根据需要， 在粗轧工序中也可以使用 SSP。 使用凹面轮廓的 SSP模块有助于缩小边部 缺陷距边部距离， 因此可以减少后工序的切边量， 从而提高成材率。 若使用 SSP， 其侧压 量要求在 10-180cm的范围。
3.精轧工序
本发明的热轧硅钢的制造方法中， 改善热轧硅钢边部质量并不涉及精轧工序的改进， 因此对于精轧工序没有特别限制， 使用目前热轧硅钢的制造方法中常用的精轧设备即可， 一般为 5-7机架 4辊轧机。 4.卷取工序
根据需要， 还可以将本发明的热轧硅钢卷起制成热轧硅钢卷， 即硅钢热卷。 实施例
以下， 结合实施例和比较例详细说明本发明的技术方案， 但本发明并不局限于这些实 施例。―
生产中使用的原材料和设备如下所示：
板坯材料： 本发明使用宝山钢铁股份有限公司生产的不同硅含量的硅钢板坯， 也可以 使用市售品。
加热炉： 步进梁式加热炉， 蓄热烧嘴；
压力调宽机 （SSP): 含入口侧导板、 出入口夹送辊、 压紧辊的调宽机；
粗轧设备： 双机架， 第 1机架为两辊轧机， 无立辊， 第二机架为可逆轧制的四辊轧机， 含立辊；
精轧设备： 7机架四辊轧机； 实施例 1〜5
硅钢板坯 A (硅含量为 2.1重量％) 依次经过如下工序制造热轧硅钢。
( 1 ) 加热工序
按照表 1所示的加热条件，分别将实施例 1~5的板坯投入加热炉中，依次经过预热段、 加热段和均热段三个阶段的加热工序后出炉。
(2) 粗轧工序
按照表 1所示， 设定侧压量、 水平压下量、 除鳞水步骤中的粗轧区域使用水道次数、 以及粗轧时间， 将完成加热工序后的硅钢板坯送入粗轧设备进行粗轧工序。
实施例 5中使用了压力调宽机， 实施例 1~4不使用压力调宽机。
(3 ) 精轧工序
将粗轧后的板坯送入精轧设备进行精轧工序。
参数设定如下：
穿带速度 9-l lm/s， 目标厚度为 2.0-2.6mm。 然后， 对获得的各热轧硅钢分别进行边部缺陷发生率的评价。
使用带钢表面质量在线检测仪对热轧硅钢上下表面全长范围进行全覆盖式拍照， 然后 通过人工检査上下表面两侧 4个部位全长范围的表面质量， 以距离边部 15mm为标准， 以 上范围出现连续 5米， 或超出 10个边部线状缺陷即为该热轧硅钢不合格。 试验时生产多 卷带钢， 贝 IJ :
缺陷发生率 = 不合格硅钢数量 /硅钢生产卷数 X % 表 1 :
Figure imgf000010_0001
由表 1可知， 加热工序和粗轧工序都按照本发明的方法制造的实施例 1~5， 边部缺陷 发生率均在 3.0%以下。 实施例 6~10 ,
使用实施例 1〜5中的硅钢板坯 A (硅含量为 2.1重量％)， 除了粗轧工序按照表 2所示 进行之外， 其余都与实施例 1~5同样地制造实施例 6~10的硅钢。
采用与实施例 1〜5同样的评价方法， 对实施例 6~10的硅钢进行边部缺陷发生率的评 表 2 :
Figure imgf000011_0001
由表 2可知， 加热工序使用本发明的方法而粗轧工序仍然使用现有技术制造的实施例 6-10 , 边部缺陷发生率为 3.5%-5.0%, 略高于加热工序和粗轧工序都按照本发明的方法制 造的实施例 1~5的硅钢.。 实施例 1 1~15
使用硅含量为 0.5重量％的硅钢板坯 B， 除了加热工序采用表 3所示之外， 其余都和 实施例 1^5同样， 制造实施例 1 1~15的硅钢， 并按照与实施例 1~5同样的方法评价边部缺 陷发生率。
表 3:
Figure imgf000011_0002
由表 3可知， 对于硅含量为 0.5重量％的硅钢板坯， 按照本发明的加热方法和粗轧方 法， 同样能够将边部缺陷发生率控制在较低的水平。 比较例 1~5
比较例 1~3采用硅钢板坯 A (硅含量为 2.1重量％)、 比较例 4~5采用硅钢板坯 B (硅 含量为 0.5重量％)， 比较例 1~5分别按照表 4所示的参数依次进行加热工序和粗轧工序， 除此之外， 与实施例 1~5—样， 制造比较例 1~5的硅钢， 并按照与实施例 1~5同样的方法 评价边部缺陷发生率。
表 4:
Figure imgf000012_0001
由表 4可知， 按照目前的制造方法生产的热轧硅钢， 即比较例 1~5， 边部缺陷发生率 分别为 11%、 8%、 7%、 8%、 6%， 明显大于本发明的实施例 1〜15的热轧硅钢的边部缺陷发 生率。 由上述实施例 1〜15以及比较例 1~5可知， 制造热轧硅钢时， 使用本发明的加热 Π1序 可以明显地降低边部缺陷发生率， 同时采用本发明的加热工序和粗轧工序可以更好地降低 边部缺陷发生率。 因此， 理想的是同时采用本发明的加热工序和粗轧工序。 工业实用性
本发明的制造方法可以有效降低热轧硅钢的边部缺陷， 能够生产出具有良好表面质量 的热轧硅钢， 因此， 可广泛应用于硅钢热卷的生产。

Claims

权利 要 求书
1.一种热轧硅钢的制造方法， 包括： 对硅钢板坯的加热工序、 粗轧工序和精轧工序， 所述加热工序在加热炉内进行， 加热炉分为预热段、 加热段和均热段，
其特征在于，
预热段满足下述式 （1)，
Figure imgf000014_0001
V，
其中: T": 预热段升温速率， 单位： °C7min，
： 板坯在加热炉内的总加热时间， t=180~240min， c '板坯入炉初始温度， 单位： 。C ;
均热段满足下述式 （2-1) 或 （2-2)，
当硅钢中的硅含量≥1.5重量％时， 满足- 10°C≤7 ≤30°C (2-1) 当硅钢中的硅含量 < 1.5重量％时， 满足 10°C≤7;≤80°C (2-2) 其中， TS： 均热段升温量，即整个板坯刚出炉的温度与加热段末的温度差，单位： °C ; 加热段升温量满足下述式 （3):
加热段升温量 = (整个板坯刚出炉的温度 -均热段升温量） - 预热段末温度 （3) 所述预热段是指从入炉处起至距离该入炉处 1/6〜1/3炉长的距离；
所述均热段是指从出炉处起至距离该出炉处 1/6〜1/3炉长的距离；
所述加热段是指预热段与均热段之间的部分。
2. 根据权利要求 1所述的热轧硅钢的制造方法， 在所述粗轧工序中， 使用 1-6道次立 辊侧压。
3. 根据权利要求 2 所述的热轧硅钢的制造方法， 所述立辊侧压的每次压下量为 10-40cm。
4. 根据权利要求 2所述的热轧硅钢的制造方法， 粗轧使用 3-8道次水平压下， 累计压 下率 70-90%。
5. 根据权利要求 2所述的热轧硅钢的制造方法， 自整个板坯刚出炉至粗轧末道次轧制 完毕的时间不超过 360秒。
6. 根据权利要求 2所述的热轧硅钢的制造方法， 在粗轧工序中使用压力调宽机， 压力 调宽机的侧压量在 10~180cm的范围内。
PCT/CN2012/000401 2012-03-13 2012-03-29 热轧硅钢的制造方法 WO2013134897A1 (zh)

Priority Applications (7)

Application Number Priority Date Filing Date Title
US14/372,689 US9496078B2 (en) 2012-03-13 2012-03-29 Hot rolled silicon steel producing method
EP12871183.5A EP2826871B1 (en) 2012-03-13 2012-03-29 Hot rolled silicon steel producing method
IN1793MUN2014 IN2014MN01793A (zh) 2012-03-13 2012-03-29
MX2014010516A MX357221B (es) 2012-03-13 2012-03-29 Metodo de produccion de acero al silicio laminado en caliente.
KR1020147025196A KR101609174B1 (ko) 2012-03-13 2012-03-29 열연 규소강 생산방법
RU2014132737/02A RU2591788C2 (ru) 2012-03-13 2012-03-29 Способ изготовления горячекатаной кремнистой стали
JP2014561247A JP6283617B2 (ja) 2012-03-13 2012-03-29 熱延ケイ素鋼の製造方法

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN201210065610.0 2012-03-13
CN201210065610.0A CN103302104B (zh) 2012-03-13 2012-03-13 热轧硅钢的制造方法

Publications (1)

Publication Number Publication Date
WO2013134897A1 true WO2013134897A1 (zh) 2013-09-19

Family

ID=49128073

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2012/000401 WO2013134897A1 (zh) 2012-03-13 2012-03-29 热轧硅钢的制造方法

Country Status (9)

Country Link
US (1) US9496078B2 (zh)
EP (1) EP2826871B1 (zh)
JP (1) JP6283617B2 (zh)
KR (1) KR101609174B1 (zh)
CN (1) CN103302104B (zh)
IN (1) IN2014MN01793A (zh)
MX (1) MX357221B (zh)
RU (1) RU2591788C2 (zh)
WO (1) WO2013134897A1 (zh)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20170012318A (ko) * 2014-05-30 2017-02-02 바오샨 아이론 앤 스틸 유한공사 산화물층을 구비하는 용융도금 제품, 그 제조방법 및 그 응용
CN114378114A (zh) * 2021-12-10 2022-04-22 天津市新天钢钢铁集团有限公司 一种利用缺陷连铸坯生产质量优良中厚板的方法
CN114472518A (zh) * 2021-12-24 2022-05-13 安阳钢铁股份有限公司 一种提高热连轧无取向硅钢厚度精度的方法

Families Citing this family (18)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103551398B (zh) * 2013-11-06 2015-09-30 北京首钢股份有限公司 一种无取向硅钢热轧卷楔形控制方法
JP6748375B2 (ja) * 2016-10-19 2020-09-02 Ｊｆｅスチール株式会社 Ｓｉ含有熱延鋼板の脱スケール方法
CN108237148B (zh) * 2017-10-16 2019-10-08 首钢集团有限公司 一种用于消除目标钢毛刺链缺陷的方法
CN108246812B (zh) * 2017-12-22 2019-06-04 包头钢铁（集团）有限责任公司 一种热轧钢板边部翘皮的控制方法
CN109513753B (zh) * 2018-10-10 2020-12-11 北京首钢股份有限公司 测试板坯角部金属流动性的方法
ES2927557T3 (es) 2019-04-20 2022-11-08 Tata Steel Ijmuiden Bv Método para producir una tira de acero que contiene silicio de alta resistencia con excelente calidad superficial y dicha tira de acero producida por el mismo
CN110055391A (zh) * 2019-04-24 2019-07-26 首钢集团有限公司 一种消除精冲钢热卷边部裂纹缺陷的方法
CN110180895B (zh) * 2019-05-28 2021-05-14 北京首钢股份有限公司 一种解决热轧高碳合金钢边部线状缺陷的方法
CN111349778B (zh) * 2020-03-20 2021-12-21 首钢京唐钢铁联合有限责任公司 一种板坯装炉间距的控制方法及装置
CN111443666B (zh) * 2020-03-25 2022-08-09 唐山钢铁集团有限责任公司 一种基于数据库模型的钢卷质量判定参数智能跟踪的方法
CN112296102B (zh) * 2020-09-30 2022-08-19 首钢集团有限公司 无取向硅钢板坯低温加热的控制方法及控制装置
CN112575156A (zh) * 2020-11-06 2021-03-30 邢台钢铁有限责任公司 一种改善中碳合金钢铸坯偏析的开坯方法
CN112605122B (zh) * 2020-12-15 2023-01-10 首钢智新迁安电磁材料有限公司 一种改善硅钢热轧板边部质量的加工方法
CN113198866B (zh) * 2021-05-07 2023-03-17 新余钢铁股份有限公司 一种薄规格中高牌号无取向硅钢酸轧生产工艺
CN113393753B (zh) * 2021-05-24 2022-08-16 攀钢集团攀枝花钢钒有限公司 钢轨半万能轧制金属流动平面演示控制方法
CN113539653B (zh) * 2021-09-16 2021-12-10 西安钢研功能材料股份有限公司 一种软磁合金棒材的制备方法
CN114535315B (zh) * 2022-02-08 2023-10-20 山西太钢不锈钢股份有限公司 一种防止高磁感取向硅钢热轧边裂工艺
CN114632818B (zh) * 2022-03-14 2023-12-05 安阳钢铁股份有限公司 一种减少取向硅钢热轧边裂的工艺方法

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4204891A (en) * 1978-11-27 1980-05-27 Nippon Steel Corporation Method for preventing the edge crack in a grain oriented silicon steel sheet produced from a continuously cast steel slab
JPS61243118A (ja) * 1985-04-18 1986-10-29 Sumitomo Metal Ind Ltd ２相ステンレス鋼熱間圧延鋼帯の製造方法
US5572892A (en) 1992-12-28 1996-11-12 Kawasaki Steel Corporation Method of producing silicon steel hot rolled sheets having excellent surface properties
CN101245435A (zh) * 2007-02-16 2008-08-20 宝山钢铁股份有限公司 一种热轧铁素体不锈钢带钢的生产方法
CN101607266A (zh) * 2009-07-20 2009-12-23 山东泰山钢铁集团有限公司 一种适用于炉卷轧机生产铁素体不锈钢热轧钢带的方法
CN101947549A (zh) * 2010-09-10 2011-01-19 山东泰山钢铁集团有限公司 一种抑制节镍奥氏体不锈钢热轧板边裂的生产工艺

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR100273094B1 (ko) * 1996-06-17 2000-12-01 이구택 열연판의 에지크랙을 감소시키는 방향성 전기강판의 슬라브 가열방법
JPH11123404A (ja) * 1997-10-23 1999-05-11 Nippon Steel Corp 形鋼製造用矩形鋼片の加熱方法並びに形鋼の粗圧延方法
RU2133283C1 (ru) * 1998-07-06 1999-07-20 Открытое акционерное общество Верхнесалдинское металлургическое производственное объединение Способ нагрева слитков
KR100419641B1 (ko) * 1999-04-15 2004-02-25 주식회사 포스코 방향성 전기강판의 열연판 엣지크랙 방지방법
CN1258608C (zh) * 2003-10-27 2006-06-07 宝山钢铁股份有限公司 冷轧无取向电工钢的制造方法
JP2005152953A (ja) * 2003-11-26 2005-06-16 Jfe Steel Kk 高シリコン鋼材の先端反り抑制方法
CN100467625C (zh) * 2005-10-31 2009-03-11 宝山钢铁股份有限公司 一种生产取向硅钢的方法
RU2403293C1 (ru) * 2009-08-03 2010-11-10 Открытое акционерное общество "Новолипецкий металлургический комбинат" Способ производства анизотропной электротехнической стали

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4204891A (en) * 1978-11-27 1980-05-27 Nippon Steel Corporation Method for preventing the edge crack in a grain oriented silicon steel sheet produced from a continuously cast steel slab
JPS61243118A (ja) * 1985-04-18 1986-10-29 Sumitomo Metal Ind Ltd ２相ステンレス鋼熱間圧延鋼帯の製造方法
US5572892A (en) 1992-12-28 1996-11-12 Kawasaki Steel Corporation Method of producing silicon steel hot rolled sheets having excellent surface properties
CN101245435A (zh) * 2007-02-16 2008-08-20 宝山钢铁股份有限公司 一种热轧铁素体不锈钢带钢的生产方法
CN101607266A (zh) * 2009-07-20 2009-12-23 山东泰山钢铁集团有限公司 一种适用于炉卷轧机生产铁素体不锈钢热轧钢带的方法
CN101947549A (zh) * 2010-09-10 2011-01-19 山东泰山钢铁集团有限公司 一种抑制节镍奥氏体不锈钢热轧板边裂的生产工艺

Non-Patent Citations (5)

* Cited by examiner, † Cited by third party
Title
GAO WENFANG; YAN ZHENGGUO; SONG PING; RAO KEWEI; CHEN FANGWU; KONG YONGJIANG: "Research on the Linear Defects along the Edges of Shadow Mask and Chassis Cold-rolled Sheets [J", STEELMAKING, vol. 19, no. 1, 2003
See also references of EP2826871A4
XIONG SHANGWU; J.M.C. RODRIGUES; P.A.F. MARTINS: "Three-dimensional modelling of the vertical-horizontal rolling process [J", FINITE ELEMENTS IN ANALYSIS AND DESIGN, vol. 39, 2003, pages 1023 - 1037
XIONG SHANGWU; LIU XIANGHUA; WANG GUODONG ET AL.: "Three-dimensional thermo-mechanical finite element simulation of the vertical-horizontal rolling process [J", JOURNAL OF MATERIALS PROCESSING TECHNOLOGY, vol. 11, 2011, pages 89 - 97
YAMAGUCHI HARUO; KUSABA YOSHIAKI; YAMADA TAKEO: "Techniques for the Control of Edge Crack Defects of Stainless Steel Sheets", FOREIGN STEEL, 1996, pages 48 - 52

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20170012318A (ko) * 2014-05-30 2017-02-02 바오샨 아이론 앤 스틸 유한공사 산화물층을 구비하는 용융도금 제품, 그 제조방법 및 그 응용
KR102333168B1 (ko) * 2014-05-30 2021-12-01 바오샨 아이론 앤 스틸 유한공사 산화물층을 구비하는 용융도금 제품, 그 제조방법 및 그 응용
CN114378114A (zh) * 2021-12-10 2022-04-22 天津市新天钢钢铁集团有限公司 一种利用缺陷连铸坯生产质量优良中厚板的方法
CN114472518A (zh) * 2021-12-24 2022-05-13 安阳钢铁股份有限公司 一种提高热连轧无取向硅钢厚度精度的方法
CN114472518B (zh) * 2021-12-24 2023-12-29 安阳钢铁股份有限公司 一种提高热连轧无取向硅钢厚度精度的方法

Also Published As

Publication number Publication date
KR101609174B1 (ko) 2016-04-05
EP2826871A1 (en) 2015-01-21
EP2826871A4 (en) 2015-11-18
CN103302104A (zh) 2013-09-18
RU2591788C2 (ru) 2016-07-20
EP2826871B1 (en) 2018-10-17
JP6283617B2 (ja) 2018-02-21
CN103302104B (zh) 2015-07-22
US9496078B2 (en) 2016-11-15
MX357221B (es) 2018-06-29
RU2014132737A (ru) 2016-05-10
MX2014010516A (es) 2014-10-14
KR20140131952A (ko) 2014-11-14
US20150243418A1 (en) 2015-08-27
IN2014MN01793A (zh) 2015-07-03
JP2015511533A (ja) 2015-04-20

Similar Documents

Publication Publication Date Title
WO2013134897A1 (zh) 热轧硅钢的制造方法
CN110819877B (zh) 一种采用炉卷轧机生产装饰用超纯铁素体不锈钢的方法
CN109465295B (zh) 一种防止热连轧钢板在冷轧中边裂断带的方法
CN104525588B (zh) 一种提高厚规格钢板热轧过程变形渗透性的方法
CN109234495B (zh) 一种低圧缩比高探伤要求SM4Gr2MnNi模具钢板的连铸生产工艺
JP5220115B2 (ja) 熱間圧延用チタンスラブ、その溶製方法および圧延方法
JP2014521517A (ja) 熱間圧延中間スラブの頭部および尾部の切断量を減少させるための、連続鋳造スラブの頭部および尾部の形状を予め制御する方法
US9833823B2 (en) Method for producing a metal strip
CN105521996A (zh) 一种镁合金带材热辊加热轧制装置及方法
CN109772898A (zh) 消除热连轧带钢边部翘皮缺陷的方法及该方法生产的带钢
CN106636747A (zh) 一种采用中厚板轧机二次退火生产工业纯钛板的制造方法
KR20110113195A (ko) 전자빔 용해로에서 용제된 열간 압연용 티탄 슬래브와 그 용제 방법 및 열간 압연용 티탄 슬래브의 압연 방법
CN109772883A (zh) 一种if钢的生产方法
CN113953479B (zh) 一种改善薄带钢钢卷翻边的方法
CN105951016B (zh) 一种舰船用ta5钛合金中厚板材的短流程制备方法
JP4923650B2 (ja) 連続鋳造鋳片の表面割れ防止方法
CN109550793A (zh) 一种减少中高铬超纯铁素体不锈钢热轧粘辊缺陷的方法
CN103276172B (zh) 基于临界温度的低合金钢节能型轧制方法
CN104475450B (zh) 一种旋压坩埚用宽幅钼板带的轧制方法
KR101795871B1 (ko) 쌍롤식 박판 주조기를 이용한 고Cu 스테인리스강의 제조방법
JP2004237291A (ja) 連続鋳造鋳片の製造方法及びその鋳片を加工した鋼材
JPH11267755A (ja) 厚鋼板の製造方法およびそれに用いる矯正装置
JP2000233266A (ja) 表面性状の良好な鋼板の製造方法
JP2018034197A (ja) 鋼の連続鋳造鋳片及び連続鋳造方法
KR100920580B1 (ko) 표면품질이 우수한 고탄소 열연강판의 제조방법

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 12871183

Country of ref document: EP

Kind code of ref document: A1

WWE Wipo information: entry into national phase

Ref document number: 14372689

Country of ref document: US

WWE Wipo information: entry into national phase

Ref document number: MX/A/2014/010516

Country of ref document: MX

WWE Wipo information: entry into national phase

Ref document number: 2012871183

Country of ref document: EP

ENP Entry into the national phase

Ref document number: 20147025196

Country of ref document: KR

Kind code of ref document: A

ENP Entry into the national phase

Ref document number: 2014561247

Country of ref document: JP

Kind code of ref document: A

NENP Non-entry into the national phase

Ref country code: DE

ENP Entry into the national phase

Ref document number: 2014132737

Country of ref document: RU

Kind code of ref document: A