Classifications

• • 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

• the present invention relates to a method for producing non-oriented silicon steel, and more particularly to a method for producing a high magnetic induction non-oriented silicon steel. Background technique
• Non-oriented silicon steel is an important magnetic material and is widely used in various fields such as motors and compressors.
• the silicon content is less than 6.5%
• the aluminum content is less than 3%
• C% is less than 0.1%
• the performance indicators mainly include material iron loss, magnetic induction and magnetic anisotropy.
• the magnetic properties of non-oriented silicon steel are affected by various factors such as material composition, thickness, and heat treatment process.
• a lower silicon content is generally used to lower the material resistivity, and at the same time, a high hot-rolled sheet is used to normalize the temperature, and the normalizing temperature is even as high as 1000 °C.
• the recrystallized structure of the non-oriented silicon steel normalized plate is fine. The fine normalized structure makes the texture of the Okl ⁇ surface in the final annealed sheet low and the corresponding magnetic induction is low.
• the annealing process is also a key factor affecting the magnetic induction of the material.
• Appropriate soaking temperatures and holding times are usually used to obtain annealed sheets of appropriate grain size. If the soaking temperature is high, the holding time is long, and the grain of the annealed sheet is coarse, the texture of the (111 ⁇ plane will be enhanced, resulting in a decrease in magnetic inductance; but if the grain diameter is small, the hysteresis loss of the material is too large. Increased motor losses in end use.
• the rapid heating annealing method can suppress the recovery process, and at the same time obtain the (110 ⁇ and (100 ⁇ surface texture cores to effectively improve the magnetic induction of the material.
• the object of the present invention is to provide a method for manufacturing high magnetic induction non-oriented silicon steel, which can produce high magnetic induction non-oriented electrical steel by using hot rolling plate light pressing measures and rapid heating annealing of cold rolled plate under the premise of ensuring iron loss. .
• a method for manufacturing a high magnetic induction non-oriented silicon steel comprising the following steps:
• Non-oriented silicon steel chemical composition weight percentage Si: 0.1 ⁇ 1%, A1: 0.005 ⁇ 1%, C ⁇ 0.004%, Mn: 0.10 ⁇ 1.50%, P ⁇ 0.2%, S ⁇ 0.005%, N ⁇ 0.002%,
• the billet heating temperature is 1150 ° C ⁇ 1200 ° C, after hot soaking, hot rolling, hot rolling finishing temperature 830 ⁇ 900 ° C, under ⁇ 570 temperature conditions;
• the normalized plate is pickled, and then subjected to cold rolling of a cumulative reduction of 70 to 80% in multiple passes, and rolled into a cold-rolled plate of a target thickness.
• Annealing rapid heating annealing of cold-rolled cold-rolled sheet, heating rate ⁇ 100° ⁇ /8, heating to 800 ⁇ 1000°C, holding time 5 ⁇ 60s, then 3 ⁇ 15°C/s The cooling rate is slowly cooled to 600 ⁇ 750 °C ;
• the annealing atmosphere is (volume ratio 30% ⁇ 70%) 3 ⁇ 4+ (volume ratio 70% ⁇ 30%)
• the main factors affecting the magnetic induction strength B 25 and B 5Q of non-oriented silicon steel are chemical composition and crystal texture.
• the amount of silicon, aluminum or manganese increases, the material resistivity increases, and B 25 and B 5Q decrease.
• the ideal crystal texture is (100) [uvw] surface texture because it is isotropic and the hard magnetization direction [111] is not on the rolling surface. This single face texture is not actually available.
• the texture is only about 20%, which is basically a non-oriented chaotic texture, that is, magnetic isotropic. Therefore, adjusting the composition and improving the manufacturing process to make the (100) component strengthening and the (111) component weakening are important ways to increase the magnetic induction B 25 and B 5Q .
• composition design of the present invention mainly considers the following points:
• Si soluble in ferrite to form a replacement solid solution, increase matrix resistivity, reduce iron loss, is the most important alloying element of electrical steel, but Si deteriorates magnetic induction.
• the present invention focuses on an ultra-high magnetic non-oriented silicon steel. Therefore, the Si content is low, 0.1 to 1%.
• A1 It is also a resistivity-increasing element. It is soluble in ferrite to increase the matrix resistivity, coarsen the grain, and reduce the iron loss, but it also reduces the magnetic inductance. A1 content exceeding 1.5% will make smelting casting difficult, magnetic induction is lowered, and processing is difficult.
• Mn Compared with Si and A1, it can increase the electrical resistivity of steel and reduce the magnetic induction. However, Mn can reduce the iron loss and form a stable MnS with the inevitable inclusion S to eliminate the magnetic damage of S. Therefore, it is necessary to add a content of 0.1% or more.
• the Mn of the present invention is from 0.10% to 1.50%.
• adding a certain amount of phosphorus to the steel can improve the workability of the steel sheet.
• C, N, Nb, V, Ti are all magnetic disadvantageous elements, and C ⁇ 0.004% is required in the present invention.
• the slab heating temperature should be lower than the solid solution temperature of the steel inclusions MnS and A1N.
• the heating temperature is set to 1150 ° C to 1200 ° C
• the hot rolling finishing temperature is 830 to 900 ° C
• the coiling temperature is ⁇ 570 ° C, which can ensure that the inclusions are not solid solution and obtain coarse hot rolled plate crystal. grain.
• the proper leveling of the hot rolled sheet is a key factor for obtaining ultra high magnetic induction non-oriented silicon steel in the invention.
• the present invention is directed to a method for producing a non-oriented silicon steel having an ultra-high magnetic sensation. Therefore, in the chemical component, the content of silicon and aluminum is low.
• the lack of grain growth elements such as silicon and aluminum leads to the inability of the grains to grow normally during the normalization of the hot rolled sheet.
• low-silicon non-oriented silicon steel is prone to recrystallization during hot rolling. Therefore, there are many fine equiaxed recrystallized grains in the hot-rolled sheet structure, and the rolled fiber structure is few.
• the main purpose of hot-rolled sheet normalization and pre-annealing is to improve the grain structure and texture of the finished product.
• the results of research on low-silicon non-oriented electrical steel show that the coarsening of grain structure before cold rolling will weaken the ⁇ 111 ⁇ texture component of the cold-rolled sheet after final annealing, and the ⁇ Okl ⁇ texture component favorable for magnetic properties. Enhanced while The coarsening of the precipitates makes the crystal grains easier to grow, so that the magnetic inductance and the iron loss are improved.
• the high magnetic induction non-oriented silicon steel has a normalization temperature of not lower than 950 ° C and a holding time of 30 to 180 s.
• the cold-rolled sheet is subjected to rapid heating annealing, and the annealing heating rate is ⁇ 100 °C/s. Warm up to 800 ⁇ 1000 °C, keep warm for 5 ⁇ 60s, then slowly cool to 600 ⁇ 750 °C at 3 ⁇ 15 °C/s.
• the present invention can improve the magnetic induction of the non-oriented silicon steel by at least 200 gauss under the premise of ensuring iron loss.
• Figure 1 shows the relationship between the amount of flattening of the hot rolled sheet and the magnetic properties of the final annealed sheet.
• Non-oriented silicon steel hot-rolled sheet thickness 2.6mm, composition: Si 0.799%, A1 0.4282%, C 0.0016%, Mn O.26%, P ⁇ 0.022%, S ⁇ 0.0033%, N ⁇ 0.0007%, Nb 0.0004%, V 0.0016%, Ti 0.0009%; the balance is iron and unavoidable impurities.
• Rapid thermal annealing using a laboratory electric heating annealing furnace The heating rate is 250 °C / s, the soaking temperature is 850 ° C, and the temperature is maintained for 13 s.
• the hot-rolled sheet After the hot-rolled sheet is lightly pressed by 1 to 10%, the recrystallized structure of the normalized sheet is obviously enlarged, but the microstructure of the finished sheet is not much different. When the reduction is 4 ⁇ 6%, the magnetic properties of the finished board are optimal, and the magnetic induction B50 reaches 1.83T. The performance is shown in Table 1. The flattening reduction of the hot rolled sheet is related to the magnetic properties of the final annealed sheet. As shown in Figure 1.
• the microstructures of the normalized and final annealed sheets after flattening at different reduction rates were examined. It was found that after the cold-rolled sheets were slightly cold-rolled, the grains of the normalized sheets were significantly enlarged, and the grain size of the final annealed sheets did not change significantly. .
• the average grain size of the normalized and annealed sheets is shown in Table 2. The results have a good correspondence with the magnetic properties of the finished plate. As the grain of the normalized plate becomes larger, the ⁇ 111 ⁇ texture component is weakened after the final annealing of the cold rolled plate, and the ⁇ 110 ⁇ texture component favorable for magnetic properties is enhanced. , the final annealed sheet magnetic induction B50 optimized.
• Non-oriented silicon steel hot-rolled sheet thickness 2.6mm, composition: Si 1%, A1 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 balance is iron and unavoidable impurities.
• the hot rolled sheet is cold rolled at a reduction ratio of 4%.

Landscapes

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

Priority Applications (6)

Applications Claiming Priority (2)

Related Child Applications (1)

Publications (1)

Family

ID=45993116

Family Applications (1)

Country Status (8)

Cited By (1)

Families Citing this family (40)

Citations (3)

Family Cites Families (15)

• 2010
  • 2010-10-25 CN CN2010105178727A patent/CN102453837B/zh active Active
• 2011
  • 2011-04-14 RU RU2012124187/02A patent/RU2527827C2/ru active
  • 2011-04-14 KR KR1020127015086A patent/KR101404101B1/ko active IP Right Grant
  • 2011-04-14 MX MX2012006680A patent/MX2012006680A/es not_active Application Discontinuation
  • 2011-04-14 JP JP2012542352A patent/JP2013513724A/ja active Pending
  • 2011-04-14 EP EP11835489.3A patent/EP2508629A4/en not_active Withdrawn
  • 2011-04-14 WO PCT/CN2011/072775 patent/WO2012055215A1/zh active Application Filing
• 2012
  • 2012-06-11 US US13/492,984 patent/US20120285584A1/en not_active Abandoned

Patent Citations (3)

Non-Patent Citations (2)

Also Published As

Similar Documents

Legal Events