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WO2008032483A1 - Procédé de fabrication de feuilles d'acier au silicium à grains orientés de haute densité de flux magnétique - Google Patents

Procédé de fabrication de feuilles d'acier au silicium à grains orientés de haute densité de flux magnétique Download PDF

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Publication number
WO2008032483A1
WO2008032483A1 PCT/JP2007/062183 JP2007062183W WO2008032483A1 WO 2008032483 A1 WO2008032483 A1 WO 2008032483A1 JP 2007062183 W JP2007062183 W JP 2007062183W WO 2008032483 A1 WO2008032483 A1 WO 2008032483A1
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hot
temperature
seconds
bar
rolling
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Japanese (ja)
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Akira Sakakura
Hiroshi Takechi
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Nippon Steel Corp
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Nippon Steel Corp
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Priority to EP07745437A priority Critical patent/EP2077164A1/fr
Priority to US12/310,769 priority patent/US20090199935A1/en
Publication of WO2008032483A1 publication Critical patent/WO2008032483A1/fr
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    • 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
    • H01F1/14775—Fe-Si based alloys in the form of sheets
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B3/02—Rolling special iron alloys, e.g. stainless steel
    • 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
    • C21D8/1205—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
    • C21D8/1211—Rapid solidification; Thin strip casting
    • 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
    • C21D8/1222—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 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
    • C21D8/1233—Cold 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 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
    • C21D8/1255—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 with diffusion of elements, e.g. decarburising, nitriding
    • 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
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/56—Continuous furnaces for strip or wire
    • 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
    • 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
    • C22C38/02—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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • B21B1/46—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 for rolling metal immediately subsequent to continuous casting
    • 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
    • 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
    • H01F41/02—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 for manufacturing cores, coils, or magnets
    • H01F41/0206—Manufacturing of magnetic cores by mechanical means
    • H01F41/0233—Manufacturing of magnetic circuits made from sheets

Definitions

  • the present invention relates to a method for producing a directional silicon steel sheet having excellent magnetic properties, particularly magnetic flux density, used for iron core materials for power transformers and iron core materials for rotating equipment.
  • NP Goss's two-stage cold rolling method has been developed for the production technology of grain-oriented silicon steel sheets, and the production principle is the presence of fine precipitates MnS.
  • the second secondary recrystallization phenomenon was revealed in 1958 by JE May & D. Turnbull (Trans. AIME., 212 (1958), 769).
  • the present inventors have developed a grain-oriented electrical steel sheet using the effectiveness of fine precipitate A1N in the one-stage strong cold rolling method containing A1 (Japanese Patent Publication No. 33-4710, US Pat. No. 3). 159, 511).
  • the manufacturing principle of the high magnetic flux density grain-oriented silicon steel sheet is determined by the present inventors. It was clarified by the effect on the secondary recrystallization of A1N (Feramu, Vol.9, No.2 (2004), 52)). That is, (110) [001] — Regarding the effect of A1N on the cold rolling and recrystallization phenomena of Goss-oriented single crystals, when the starting single crystal contains a small amount of extremely fine MN of 5 nm or less, ⁇ 111 ⁇ ⁇ 110> — C-oriented primary recrystallized growth structure.
  • the low temperature slab heating method (Material Science Forum, 204/206, No. P tl (1996), 143) is adopted as one manufacturing method.
  • JP-A-2-258922 the idea of adopting a thin-wall continuous manufacturing method with a thickness of several mm (JP-A-2-258922) has been announced.
  • the conventional method of once cooling a thick CC slab and then reheating the cold slab has problems in productivity and workability, and improvement is desired.
  • the effect of dispersion and precipitation of fine A1N is due to the fact that A1 N is once contained in silicon steel by high-temperature reheating work using a hot slab for thick slabs. This was achieved by the rapid cooling effect by hot rolling after the solid solution, but there was a problem due to the high temperature heating scale melting of the thick slab, and the problem of crystal orientation in the thin continuous manufacturing method of several mm thick There is a problem of brittleness of the structure, which is a big problem that hinders practical use.
  • the present invention produces a medium-thick slab by a continuous forging method, maintains the slab at a temperature that is at least the minimum that can be hot-rolled, and performs continuous hot rolling of A1N that is already solid solution in the molten steel state
  • the thick CC slab is once cooled by holding it in the steel without precipitation until it is finely precipitated by the rapid cooling effect during continuous hot rolling.
  • the configuration of the present invention is as follows.
  • Hot-rolled sheets with a thickness of 1.5 mm to 5 mm by hot rolling cool the cooling time to 600 ° C after hot-rolling at 150 seconds or less, then perform normal cold rolling, intermediate annealing, decarburization annealing
  • Figure 1 is a schematic diagram showing an example of continuous forging-hot rolling continuous equipment.
  • Fig. 2 is a schematic diagram showing another example of continuous forging-hot rolling continuous equipment.
  • Figure 3 shows the effect (3.20% Si) of the retention temperature and time on the magnetic properties after A1N solid solution treatment.
  • Fig. 4 shows a typical thermal history curve (3. 10% Si) in hot rolling after iN solid solution treatment.
  • Figure 5 shows the rapid cooling (tandem rolling) in hot rolling after A1N solid solution treatment
  • Figure 6 shows the cooling curve after A1N solid solution treatment and the effect of Si content on A1N precipitation.
  • C is necessary to cause a certain transformation during hot rolling depending on the amount of Si. It is an important element, and if it is less than 0.010%, secondary recrystallization cannot be generated stably. If it exceeds 0.075%, the decarburization annealing time becomes longer, which is not preferable for production, so the content was made 0.010 to 0.075%.
  • Si is less than 2.95%, an excellent iron loss value cannot be obtained as a high-grade high magnetic flux density grain-oriented silicon steel sheet. Further, if added over 4%, it is not preferable because cracks and the like occur during cold rolling due to brittleness, and its content was set to 2.95 to 4: 0%.
  • Oxidation-soluble A1 and N are elements necessary for producing an appropriate A1N as an inhibitor, and a sufficient amount for the purpose is 0.010 to 0.040% and 0.0010 to 0.0150%.
  • S and Se form Mn, MnS, and MnSe, and act as a precipitation dispersed phase for secondary recrystallization. Therefore, 0.005% to 015% of these are contained alone or both.
  • it is selected from the group of Sb: 0.005-0.2%, Nb: 0.005-0.2%, Mo: 0.003-0.1, Cu: 0.02-0.2%, Sn: 0.02-0.3% as necessary. At least one species can be included.
  • A1N of about 10 nm (5 to 50 nm) exists in the hot rolled sheet state.
  • a medium-thickness bar of 20 to 70 mm is manufactured, and the bar temperature is 1200C while maintaining the solid solution state of A1N by the heating means that prevents the heat held by this bar or temperature drop of the heat insulation furnace etc.
  • transfer to the hot rolling mill entrance within 150 seconds at the maximum after extraction from the heat-retaining furnace, and within 500 seconds at the maximum in the case of 1250 ° C or more, and 1.5 mm to 5 mm by hot rolling.
  • Thick A1N is deposited in the vicinity of lOim (5 to 500 nm) by using a thick hot-rolled sheet and setting the cooling time to 600 ° C after hot-rolling to 150 seconds or less.
  • the thickness of the bar is limited to a medium thickness of 20 to 70 mm. If it is less than 70 mm, large equipment is required for heat retention, and if it exceeds 70 mm, it is not possible to obtain hot-rolled sheets with only a finish rolling mill, and a rough rolling mill is required, so that economical production cannot be achieved.
  • the means for producing and rolling a 20 to 70 mm thick bar is not particularly limited.
  • An example of the known continuous forging-hot rolling continuous equipment is shown schematically in Figs.
  • Figure 1 shows the continuous slab 2 extracted from the mold 1 and the cut slab 3 placed in the heat-retaining furnace 4 to maintain a constant temperature.
  • Fig. 2 shows the continuous production of the medium slab 2 and then winding it into a coil 7. After the coil is placed in the coil box 8 to equalize the temperature, the continuous finishing hot rolling machine 5 is used. This is a rolling and winding device.
  • This hot-rolled sheet is cold-rolled, decarburized, and finally annealed to obtain the final product.
  • Fig. 4 (B) shows the B10 characteristics, and the magnetic properties when hot-rolled after holding at 1000 ° C for 20 seconds are short, although the holding time is short as shown by the white circle 2 in Fig. 3.
  • the B10 characteristic shows considerable deterioration, and if it exceeds 100 seconds, the secondary recrystallization itself becomes unstable.
  • Fig. 4 (C) shows the half-black circle 3 in Fig. 3, the magnetic characteristics are slightly improved due to the long holding time but high temperature.
  • the black circle 4 in Fig. 3 the magnetic properties when holding for 120 seconds above 1200 ° C in Fig. 4 (D) are shown in Fig. 3. Shows a value close to the best value.
  • Iron loss values are regarded as important for high magnetic flux density grain-oriented silicon steel plates.3.0-4.0% Si has a lower Si content of less than 3%.
  • the processing conditions are rather strict and the time allowed for production operations is relatively short. The reason is that in the case of low Si, precipitation can be prevented because the solid solubility of A1N is increased by the transformation. Therefore, when the amount of Si is high, the only way to prevent precipitation is to use temperature. The meaning is that the higher the temperature of A1N precipitation, the more rapidly it delays. Therefore, if it takes time to reach the inlet of the finishing hot rolling machine, it is sufficient to consider increasing the holding temperature.
  • the bar may be passed through a heating furnace for maintaining the bar at a temperature of 1250 to 1350 ° C., and when the bar temperature is as low as 1000 ° C. Precipitation of A1N can be prevented by means such as passing through a heating furnace to keep the temperature at ⁇ 1350 ° C.
  • Figure 5 shows a 0.040% C, 3.10% S i, 0.029% AK balance silicon steel ingot consisting of Fe and unavoidable impurities rolled into a 40mm thick bar at 1350 ° C for 30 minutes Immediately after heating, it is rolled into a 3.5-thick hot-rolled sheet at approximately 1000 ° C, and this is water-cooled from the cooling process immediately after the end of hot-rolling to create five types of hot-rolled sheets.
  • the figure shows the relationship between the magnetic properties and the thermal history when decarburized and finish-annealed into the final product.
  • the thick line in the figure indicates the starting point of cooling (water cooling) after hot rolling, and the thin line indicates the magnetic properties (B10).
  • the material after hot rolling is rapidly Cooling treatment, that is, within a range not exceeding 150 seconds after the end of hot rolling, can be done from a high temperature such as b.c.d.e instead of slow cooling like (a). Cooling at the fastest possible speed is necessary to obtain magnetic properties.
  • a b.c.d.e
  • Cooling at the fastest possible speed is necessary to obtain magnetic properties.
  • the temperature for cooling in a range not exceeding 150 seconds shall be at least 600 ° C. Normally, hot-rolled steel sheets are wound up at 600 ° C or lower and are slowly cooled, so A1N does not precipitate.
  • Figure 6 shows the relationship between the hot rolling cooling cycle and the amount of A1N precipitation.
  • the precipitation curves for low Si (1.12% Si, 2.17% Si) are also shown.
  • the Si content is 3.10%
  • the A1N starts from around 1250 ° C.
  • Precipitation starts and proceeds rapidly below 1200 ° C, whereas in the case of 1% Si, A1N deposition hardly progresses up to 1000 ° C, and it begins for the first time below 1000 ° C. This is because the ⁇ -a transformation region of the material varies depending on the amount of C and Si contained, and the precipitation behavior of A1N is closely related to the amount of this transformation.
  • the hot rolling conditions for producing an excellent high magnetic flux density grain-oriented silicon steel sheet using the crystal growth suppression effect of A1N are as follows.
  • the holding temperature after the bar is forged or extracted in a heating furnace If the temperature is 1250 ° C or higher, the hot rolling should reach the inlet of the hot finishing mill within 150 seconds at the longest, and if it exceeds 1200 ° C, preferably within 150 seconds. To start.
  • Cooling after the end of hot rolling should not exceed 150 seconds at the maximum to 600 ° C.
  • A1N precipitates due to cooling from a high temperature, but if it is gradually cooled over time, A1N becomes coarser with time and becomes about 1 m in extreme cases. It becomes a completely meaningless form.
  • the precipitation size becomes approximately 10 ⁇ m, which is a preferable state for the present invention.
  • Mass steel, 0.045% C, 3.05% Si, 0.032% A1 and the remainder Fe and unavoidable impurities in silicon steel molten steel is made into a 60-thick bar with a continuous forging machine (hereinafter referred to as CC machine) and immediately finished with heat
  • the thickness was 3.0mm.
  • the finishing heat inlet temperature was 1210 ° C for the bar head and 1205 ° C for the bottom.
  • the amount of C in the hot-rolled sheet is 0.041%, and decarburization is slightly occurring. This was first cold-rolled at a rolling reduction of 30% to a thickness of 2.1 mm, then annealed at 1100 ° C for 2 minutes in nitrogen, and then cooled by blowing a jet stream.
  • the cooling rate was about 18 seconds from 1100 ° C to 850 ° C, and about 27 seconds from 850 ° C to 400 ° C.
  • the A1N after this annealing was analyzed as 0.0055% (NasAIN).
  • this was cooled at a rolling rate of 83.3% to a thickness of 0.35 mm, decarburized at 800 ° C for 3 minutes in hydrogen, and then annealed at 1200 ° C for 20 hours.
  • the B 10 characteristics in the rolling direction of the product were 1.93T and W17 / 50 was 1.15W / kg.
  • Example 2 A bar having the same composition as in Example 1 was allowed to stand for about 40 seconds in front of the finishing hot rolling machine inlet, and then finishing hot rolling was started.
  • the finishing rolling temperature of the bar at that time was 1150 ° C for the bar head and 1120 ° C for the bottom.
  • the same treatment as in Example 1 was carried out, and the occurrence rate of secondary recrystallization in the final product was examined. As a result, it was almost 50% and did not become a product.
  • the hot-rolled sheet was pickled, cold-rolled at a rolling rate of 87.5% to a final gauge of 0.35 mm thickness, decarburized at 850 for 3 minutes in wet hydrogen, and then annealed at 1200 ° C in hydrogen for 15 hours.
  • the B10 characteristics in the rolling direction of the product were 1.92T and 1.05WZkg, respectively.
  • Example 3 A bar having the same composition as in Example 3 was allowed to stand for about 150 seconds in front of the finishing hot rolling machine inlet, and then finishing hot rolling was started. At that time, the finish rolling start temperature of the bar was 950 ° C at the bar head and 930 ° C at the bottom. After that, as a result of processing up to the final product under the same conditions as in Example 3 above, secondary reconstitution When the crystallinity generation rate was examined, it was 20%, which was not a product.
  • A1 containing the balance Fe and unavoidable impurities made of molten steel is made into a 60 mm thick bar with the CC machine and finished immediately. Hot rolled to 2.3mm thick.
  • the finishing hot rolling inlet temperature was 1230 ° C at the top of the bar and 1205 ° C at the bottom, and the hot rolling was finished after 12 seconds and 45 seconds, respectively.
  • the temperatures at that time were 1010 ° C and 995 ° C, respectively.
  • the winding was completed after about 85 seconds.
  • This hot-rolled sheet is continuously annealed at 1150 ° C for 2 minutes, then rapidly cooled, pickled, and cold-rolled to a final sheet thickness of 0.27mm, and then decarburized and annealed in hydrogen at 850 ° C, 1200 ° C was finally annealed.
  • the same pass schedule (1.6 mm, 1.2 mm, 1.0 mm, 0.8 mm, 0.6 mmni, 0.45 mm) was applied while aging treatment was performed at five different temperatures. 6 passes). That is, the relationship between the conditions and magnetic properties is as shown in Table 2.
  • the molten steel was made into a 60mm thick bar with the CC machine and immediately finished hot rolled to 2.
  • the finished hot rolling inlet temperature was 1220 ° C at the head and 1201 at the bottom, after 15 seconds each. After 55 seconds, the hot rolling was finished, and the temperatures at that time were 990 ° C and 985 ° C, respectively.
  • This hot-rolled sheet was continuously annealed at 1130 ° C for 2 minutes, then rapidly cooled in hot water at 100 ° C, subjected to precipitation heat treatment, pickled, and then subjected to aging treatment between passes at 250 ° C for 5 minutes. However, it was cold-rolled to a final thickness of 0.22. Then in 2 minutes Graced- NH 3 in 850 ° C, have rows decarburization annealing in an atmosphere of a dew point of 62 ° C, and final baking blunt with further MgO and Ti0 2 was coated with an annealing separating agent mixture 1200 ° C . Tension coating was applied after final annealing.
  • This hot-rolled sheet was continuously annealed at 1130 ° C for 3 minutes, then forced-cooled to immerse the bath containing boiling water at the furnace outlet, then pickled, and rolled at a rolling reduction of 90% to obtain 0.3
  • the thickness was mm. This was decarburized and annealed at 1200 ° C for about 20 hours in H 2 .
  • Example 8 As a comparative example, after forging a bar having the same components as in Example 8 above, the temperature was lowered to 1100 ° C when transported to the finishing hot rolling machine without holding the temperature by the heating device.
  • the hot-rolled sheet that was immediately hot-rolled was processed to the final product under the same conditions as in Example 3 above, and when the secondary recrystallized grain ratio occurrence rate was examined, it was 30% or less for the entire coil, resulting in a product. I could n’t.
  • a molten steel containing 0.055% C, 3.20% Si, 0.025% S, 0.30% acid-soluble Al, and the balance Fe and unavoidable impurities in a mass% was forged as a 30 mm thick bar with the CC machine. After fabrication, the bar temperature was 1150 ° C when cut into a single bar. This bar was immediately put into a heating furnace heated to 1330 ° C to dissolve the side A1N, then extracted from the furnace, allowed to reach the inlet of the finishing hot rolling mill for about 120 seconds, and immediately started hot rolling The thickness was 25mm.
  • the finishing hot rolling inlet temperature was 1210-1220 ° C, and the hot rolling was completed after 16 seconds and 50 seconds at the leading edge and trailing edge of the hot rolled sheet, respectively. The temperature at that time is They were 1010 ° C and 998 ° C, respectively, and the winding was completed after about 70 seconds.
  • Example 8 the bar having the same composition as in Example 8 was immediately transported to the finishing hot rolling machine inlet, and the temperature further decreased to 1080 ° C.
  • the hot rolled sheet that was immediately finished and hot rolled was processed to the final product under the same conditions as in Example 3 above, and when the secondary recrystallization rate occurrence rate was examined, it was found that only 20% was generated, which could be a product. There wasn't. Industrial applicability
  • A.1N obtained by rapid cooling in a hot rolling finish rolling mill (tandem mill) from a state in which it is completely dissolved in a medium-sized piece produced by continuous forging is uniform and It is finely dispersed and sufficient to generate primary recrystallization nuclei with excellent crystal orientation, and at the same time, it has a sufficient effect of suppressing crystal growth, and the crystal structure obtained by fabrication is hot rolled. Therefore, there is no adverse effect of abnormally grown grains of the slab by conventional high-temperature heating, and uniform and complete secondary recrystallized grains are formed by final annealing, and the magnetic flux density B 10 ⁇ 1.90T is excellent. It is possible to obtain a high magnetic flux density directional silicon steel sheet having excellent characteristics.

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Abstract

L'invention concerne un procédé comprenant le coulage d'une barre d'épaisseur intermédiaire par l'utilisation d'un équipement de coulage-laminage à chaud continu ; l'opération consistant à amener la barre à atteindre une entrée de laminage à chaud de finition tout en conservant un température dépassant 1200 °C à laquelle la barre reste en son état où elle contient AlN en solution solide ; et la réalisation d'un laminage à chaud et d'une trempe de la barre de façon à effectuer une précipitation d'AlN fin, accomplissant ainsi la production efficace d'une feuille d'acier au silicium à grains orientés de haute densité de flux magnétique à faible coût sans avoir besoin d'effectuer un chauffage à haute température de la barre.
PCT/JP2007/062183 2006-09-13 2007-06-11 Procédé de fabrication de feuilles d'acier au silicium à grains orientés de haute densité de flux magnétique Ceased WO2008032483A1 (fr)

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EP07745437A EP2077164A1 (fr) 2006-09-13 2007-06-11 Procédé de fabrication de feuilles d'acier au silicium à grains orientés de haute densité de flux magnétique
US12/310,769 US20090199935A1 (en) 2006-09-13 2007-06-11 Method of production of high flux density grain-oriented silicon steel sheet

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JP2006247674A JP5001611B2 (ja) 2006-09-13 2006-09-13 高磁束密度方向性珪素鋼板の製造方法
JP2006-247674 2006-09-13

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CN102725078B (zh) * 2010-01-29 2015-04-01 东芝三菱电机产业系统株式会社 轧制线上的注水控制装置、注水控制方法、注水控制程序
WO2012089696A1 (fr) * 2011-01-01 2012-07-05 Tata Steel Nederland Technology Bv Procédé pour la fabrication de bande d'acier électrique à grains orientés et acier électrique à grains orientés produit de cette manière
WO2014020369A1 (fr) 2012-07-31 2014-02-06 Arcelormittal Investigación Y Desarrollo Sl Procédé de production d'une tôle d'acier au silicium à grains orientés, tôle d'acier électrique à grains orientés et son utilisation
CN103805918B (zh) * 2012-11-15 2016-01-27 宝山钢铁股份有限公司 一种高磁感取向硅钢及其生产方法
WO2016139818A1 (fr) 2015-03-05 2016-09-09 Ｊｆｅスチール株式会社 Tôle d'acier magnétique à grains orientés et procédé pour la production de cette dernière
WO2018084203A1 (fr) * 2016-11-01 2018-05-11 Ｊｆｅスチール株式会社 Procédé de production de tôle d'acier électrique à grains orientés
CN109906277B (zh) * 2016-11-01 2021-01-15 杰富意钢铁株式会社 取向性电磁钢板的制造方法
WO2018151296A1 (fr) * 2017-02-20 2018-08-23 Ｊｆｅスチール株式会社 Procédé de fabrication de tôle d'acier électrique à grains orientés
CN112391512B (zh) * 2019-08-13 2022-03-18 宝山钢铁股份有限公司 一种高磁感取向硅钢及其制造方法
WO2024204818A1 (fr) 2023-03-29 2024-10-03 Ｊｆｅスチール株式会社 Procédé de production d'une feuille d'acier électrique à grains orientés, chaîne d'installation de production pour feuille d'acier électrique à grains orientés, et feuille laminée à chaud pour feuille d'acier électrique à grains orientés

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US20090199935A1 (en) 2009-08-13
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KR20090057010A (ko) 2009-06-03
JP5001611B2 (ja) 2012-08-15
JP2008069391A (ja) 2008-03-27

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