US20120285584A1 - Manufacture Process Of Non-Oriented Silicon Steel With High Magnetic Induction - Google Patents

Manufacture Process Of Non-Oriented Silicon Steel With High Magnetic Induction Download PDF

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US20120285584A1
US20120285584A1 US13/492,984 US201213492984A US2012285584A1 US 20120285584 A1 US20120285584 A1 US 20120285584A1 US 201213492984 A US201213492984 A US 201213492984A US 2012285584 A1 US2012285584 A1 US 2012285584A1
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temperature
cold
steel
rolled
silicon steel
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English (en)
Inventor
Zitao Wang
Bo Wang
Shishu Xie
Bingzhong Jin
Aihua Ma
Liang Zou
Yuhua Zhu
Zhanyuan Hu
Xiao Chen
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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Assigned to BAOSHAN IRON & STEEL CO., LTD. reassignment BAOSHAN IRON & STEEL CO., LTD. ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: CHEN, XIAO, HU, ZHANYUAN, JIN, BINGZHONG, MA, AIHUA, WANG, BO, WANG, ZITAO, XIE, SHISHU, ZHU, YUHUA, ZOU, Liang
Publication of US20120285584A1 publication Critical patent/US20120285584A1/en
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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
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • 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
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • 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

  • This invention relates generally to a manufacture process of non-oriented silicon Steel, and particularly, to a manufacture process of non-oriented silicon Steel with high magnetic induction.
  • Non-oriented silicon Steel is an important magnetic material and widely used in manufacture of various electric machines, compressors and so on. In general, it contains silicon of less than 6.5%, aluminum of less than 3%, carbon of less than 0.1%, and other trace elements. Manufacture process of silicon Steel includes the procedures of hot-rolling, normalization, cold-rolling, finish-annealing and coating with insulation film.
  • non-oriented silicon Steel main property indexes of include iron loss, magnetic induction and magnetic anisotropy.
  • the magnetic properties of non-oriented silicon Steel are very prone to be affected by various factors such as material compositions, thickness, heat treatment procedure, and so on.
  • anneal procedure is also a critical factor to affect on magnetic induction of silicon Steel.
  • a common practice is to employ an appropriate soakage temperature and an appropriate soakage period. If soakage temperature is too high and soakage period is too long, the crystal grains of annealed silicon Steel will be rather coarse, the surface texture ⁇ 111 ⁇ will be intensified, and magnetic induction of the sheet will be weakened; contrarily, if diameters of the grains are on the small side, the hysteresis loss of material will be on the large side, which will increase electric loss in end use.
  • heating at a higher temperature rise rate will bring about quite intensive Gauss texture.
  • heating at a lower temperature rise rate will result in that the texture of the finished silicon Steel product is composed of more component ⁇ 111 ⁇ [112] and less components ⁇ 110 ⁇ [114], ⁇ 001 ⁇ [120] and ⁇ 111 ⁇ [110].
  • Jong-Tae PARK, Jerzy A.SZPUNAR Sang-Yun CHA Effect of heating Rate on the development of Annealing Texture in Non-oriented Electrical steels ISIJ International, Vol. 43(2003), No. 10, pp. 1611-1614 Therefore, in anneal procedure, heating at a higher temperature rise rate can depress recovery and give a surface texture with ⁇ 110 ⁇ and ⁇ 100 ⁇ in core, and so that effectively improve magnetic induction of the finished silicon Steel product.
  • the objective of the invention is to provide a manufacture process of non-oriented silicon Steel with high magnetic induction, the manufacture process is characteristic of including the measures: to roll the hot-rolled plate lightly and to heat the cold-rolled sheet quickly to an anneal temperature so as to get non-oriented silicon Steel with high magnetic induction under the precondition of not increasing iron loss of the sheet.
  • the invention's manufacture process of non-oriented silicon Steel with high magnetic induction comprises the following procedures:
  • the steel billet is heated to a temperature between 1150 ⁇ 1200° C., and soaked at the temperature for a certain time, and then hot-rolled into a steel plate at finish-rolling temperature of 830 ⁇ 900° C.; when being cooled to a temperature ⁇ 570° C., the hot-rolled plate is coiled;
  • the hot-rolled plate is cold-rolled at rolling compression ratio of 2 ⁇ 5%;
  • the hot-rolled plate After being cold-rolled, the hot-rolled plate is continuously normalized at one time at a temperature not below 950° C., and maintained at the temperature for 30 ⁇ 180s;
  • the normalized plate is pickled, and then is successively cold-rolled several times at a progressive or total rolling compression ratio of 70 ⁇ 80% finally into a cold-rolled silicon steel sheet with the thickness of its finished product;
  • the cold-rolled sheet is quickly heated to a temperature between 800 ⁇ 1000° C. at a temperature rise rate of not below 10° C./s, and maintained at the temperature for 5 ⁇ 60s, thereafter, cooled slowly to 600 ⁇ 750° C. at a cooling rate of 3 ⁇ 15° C./s.
  • the atmosphere of the Annealing is H 2 of 30% ⁇ 70%+N 2 of 70% ⁇ 30%, the dew point ⁇ 25° C.
  • the main factors to have effect on magnetic induction intensity B 25 and B 50 of non-oriented silicon Steel are chemical compositions and crystal grain texture. Higher contents of silicon, aluminum and manganese will result in a higher current resistivity and lower magnetic properties B 25 and B 50 .
  • the ideal crystal texture is surface texture (100) [uvw] because it is isotropic and the hard-magnetized direction is not on the rolled surface. In practice, it is impossible to get a single surface texture of this kind.
  • texture component (100) [011], (111) [112], (110) [001], (112) [011] and so on, of them texture component (100) only amounts to 20% or so and largely belongs in non-oriented disordered texture, i. e. magnetic anisotropic one.
  • to change chemical compositions of material and to improve manufacture process so as to intensify component (100) and to weaken component (111) is an important approach to raise magnetic induction intensity B 25 and B 50 .
  • composition design of the invention the following points are primarily taken into account:
  • Si it is soluble in ferrite to form substitution solid solution so as to increase material resistivity and reduce iron loss, and thus, is the most important alloying element of electric steel, but it is adverse to magnetic induction.
  • the invention is aimed at non-oriented silicon Steel with high magnetic induction, therefore, Si content is determined as low as 0.1 ⁇ 1%.
  • Al it is also an element to increase resistivity, and is soluble in ferrite to increase material resistivity and to make crystal grains coarse and to reduce iron loss, but it will also reduce magnetic induction. Al content of more than 1.5% will cause smelting, casting and machining to be difficult and will reduce magnetic induction.
  • Mn like Si and Al, it will increase steel's resistivity and reduce magnetic induction, but it is advantageous to reduce iron loss, and it will react with composition S to generate stable MnS so as to eliminate the adverse influence of S on magnetic property. Therefore, it is necessary to have Mn content of over 0.1% in the silicon Steel. In the invention, Mn content is controlled within 0.10 ⁇ 1.50%.
  • P to add P of a certain content in steel's compositions can improve manufacturability of silicon Steel, but P content shall be below 0.2%.
  • C, N, Nb, V and Ti they are all elements adverse to magnetic property.
  • it is controlled that C ⁇ 0.004%, S ⁇ 0.005%, N ⁇ 0.002, Nb+V+Ti ⁇ 0.006% so as to minimize their adverse effect on magnetic property.
  • Temperature of heated billet or slab shall be below the solid solution temperature of inclusions MnS and AlN in the steel.
  • heating temperature is set at 1150 ⁇ 1200° C.
  • finish rolling temperature is set at 830 ⁇ 900° C.
  • coiling temperature is set not below 570° C., these temperatures can impede solid solution of the inclusions and make the hot-rolled plate have coarse grains.
  • the invention to flatten the hot-rolled plate appropriately is a key factor to attain superhigh-magnetic-induction non-oriented silicon Steel.
  • the invention aims at a manufacture process of superhigh-magnetic-induction non-oriented silicon Steel, therefore, the contents of silicon and aluminum in chemical compositions of the steel are controlled to be rather low.
  • too small contents of silicon and aluminum will give rise to such a case that crystal grains can not normally grow up in the procedure of normalization of the hot-rolled plate.
  • non-oriented silicon steel plate with a lower silicon content trends to generate re-crystallization in the course of being hot-rolled, which will lead to such a case that there are more fine equiaxed re-crystallized grains and less rolled fiber texture in the metallographic texture of the hot-rolled plate.
  • To flatten the hot-rolled plate at a rolling compression ratio of 2 ⁇ 5% before it is normalized can increase deformation stored energy so as to make the re-crystallized texture of the normalized plate be much coarser.
  • a too high rolling compression ratio in flattening procedure will cause the hot-rolled plate to have more internal defects so as to affect grain growth.
  • the intension to have the hot-rolled plate normalized and pre-annealed is to improve grain structure and texture.
  • a research on non-oriented silicon Steel indicates that to make grain structure become coarse prior to cold-rolling can weaken texture component ⁇ 111 ⁇ of the cold-rolled sheet and can intensify texture component ⁇ ok1 ⁇ of the cold-rolled sheet after it is finish-annealed, texture component ⁇ ok1 ⁇ is advantageous to magnetic property.
  • the incidental phenomenon of separated substance becoming coarser can make grains grow up even easier so as to improve magnetic induction and reduce iron loss.
  • normalization temperature of high-magnetic-induction non-oriented silicon steel plate is not below 950° C., soakage period is 30 ⁇ 180s.
  • the grains of ⁇ 110 ⁇ Gauss texture which are advantageous to magnetic property are usually to nucleate and grow up in the shear-deformed zone of the cold-rolled material. If temperature rise rate is too low, in the phase of temperature being lower, a recovery process in material will occur, which will reduce lattice distortion, thus, the probability of Gauss texture to nucleate will greatly fall down.
  • To use a high temperature rise rate in annealing procedure can rapidly go through the temperature range adverse to evolution of Gauss texture and can make the surface texture ⁇ ok1 ⁇ advantageous to magnetic property evolute even better, and thereby, can optimize magnetic induction and iron loss. To cool the annealed sheet slowly can improve its magnetic property.
  • the cold-rolled sheet is finish-annealed by quickly heating to a temperature between 800 ⁇ 1000° C. at a temperature rise rate of ⁇ 100° C./s and a soakage period of 5 ⁇ 60s, thereafter, is slowly cooled to 600 ⁇ 750° C. at cooling rate of 3 ⁇ 15° C./s.
  • the manufacture process of the invention can raise magnetic induction of non-oriented silicon Steel by at least 200 Gauss under the precondition to maintain the same iron loss.
  • FIG. 1 shows an interrelation between the compression ratio at which the hot-rolled plate is cold-rolled and the magnetic property of the finish-annealed Steel.
  • Hot-rolled non-oriented silicon steel plate with 2.6 mm thickness, its compositions and their contents are: Si 0.799%, Al 0.4282%, C 0.0016%, Mn 0.26%, P ⁇ 0.022%, S ⁇ 0.0033%, N ⁇ 0.0007%, Nb 0.0004%, V 0.0016%, Ti 0.0009%, the rest is Fe and unavoidable inclusions.
  • the hot-rolled plate is cold-rolled at a compression ratio of 1 ⁇ 10%.
  • the cold-rolled plate is normalized at normalization soakage temperature of 970° C. and maintained at the temperature for 60s, thereafter the normalized plate is pickled, and then, cold-rolled into a Steel of 0.5 mm thickness.
  • the cold-rolled sheet is annealed at a high heating rate in an electric annealing furnace in a laboratory, with temperature rise rate of 250° C./s, soakage temperature of 850° C. and soakage time of 13s.
  • the texture component ⁇ 111 ⁇ of the cold-rolled sheet after being finish-annealed is weakened, while the texture component ⁇ 110 ⁇ which is advantageous to magnetic property is intensified, thereby, the magnetic induction B50 of the finish-annealed sheet is optimized.
  • Hot-rolled non-oriented silicon steel plate with 2.6 mm thickness, its compositions and their contents are: Si 1%, Al 0.2989%, C 0.0015%, Mn 0.297%, P 0.0572%, S 0.0027%, N 0.0009%, Nb 0.0005%, V 0.0015%, Ti 0.0011%, the rest is Fe and unavoidable inclusions.
  • the hot-rolled plate is cold-rolled at rolling compression ratio of 4%.
  • the cold-rolled plate is normalized at normalization soakage temperature of 950° C. and maintained at the temperature for 60s, thereafter, the normalized plate is pickled, and then cold-rolled into a Steel of 0.5mm thickness.
  • the cold-rolled sheet is annealed at a high heating rate in an electric annealing furnace in a laboratory, with different temperature rise rates of 20° C. Is, 150° C./s and 250° C. Is, respectively, soakage temperature of 960° C. and soakage time of 13s.
  • the magnetic property of the finish-annealed sheet is shown in Table 3.
  • the iron loss and magnetic induction of the finish-annealed sheet is affected by temperature rise rate. As temperature rise rate is raised, iron loss is reduced and magnetic induction is increased.

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US13/492,984 2010-10-25 2012-06-11 Manufacture Process Of Non-Oriented Silicon Steel With High Magnetic Induction Abandoned US20120285584A1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
CN201010517872.7 2010-10-25
CN2010105178727A CN102453837B (zh) 2010-10-25 2010-10-25 一种高磁感无取向硅钢的制造方法
PCT/CN2011/072775 WO2012055215A1 (zh) 2010-10-25 2011-04-14 一种高磁感无取向硅钢的制造方法

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EP (1) EP2508629A4 (ru)
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KR (1) KR101404101B1 (ru)
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