Classifications

• • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
  • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • 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
  • 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
  • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
• • 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
  • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
• • 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
  • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
• • 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
  • C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
• • 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
• • 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
  • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
• • 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
  • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
  • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
  • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
• • H—ELECTRICITY
  • H01—ELECTRIC ELEMENTS
  • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
  • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
  • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
  • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
  • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
  • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
  • H01F1/147—Alloys characterised by their composition
  • H01F1/14766—Fe-Si based alloys
  • H01F1/14775—Fe-Si based alloys in the form of sheets
• • 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
  • H01F1/14791—Fe-Si-Al based alloys, e.g. Sendust
• • 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
  • C21D2261/00—Machining or cutting being involved

Definitions

• the present invention relates to a non-oriented electrical steel sheet with low iron losses and excellent blanking property.
• a laminated iron core which is formed by laminating steel sheets with core shapes (i.e., core materials)
• an iron core i.e., core
• stamping is commonly used as a method of obtaining the core materials from a non-oriented electrical steel sheet.
• the magnetic properties of the iron core will degrade due to strain introduced into a region around a cut portion during stamping, or due to changes in the shape of a cut end surface, such as shear droops and burrs.
• Patent Literature 2 discloses non-oriented electrical steel that contains steel components including C: 0.003 mass% or less, Si: in the range of 1.0 mass% to 3.0 mass%, Al: in the range of 0.1 mass% to 3.0 mass%, and Mn: in the range of 0.1 mass% to 1.0 mass%, with the balance being Fe and unavoidable impurities, in which the Al content and the Si content satisfy the relationship of 0.2 ⁇ Al/(Si+Al) ⁇ 0.6, the yield ratio represented by (yield strength/ tensile strength) is 0.6 or greater, and the Vickers hardness is 200 or less, thus exhibiting excellent in magnetic properties and blanking property.
• the electrical steel sheet described in Patent Literature 1 above has a Si content of 1.5 mass% or less, and is not directly applicable to a non-oriented electrical steel sheet with a higher Si content.
• the electrical steel sheet disclosed in Patent Literature 2 requires a Vickers hardness of 200 or less. Thus, such an electrical steel sheet is not applicable to a non-oriented electrical steel sheet with a high Si content, either.
• the non-oriented electrical steel sheet described in Patent Literature 1 relates to a technology for improving blanking property by controlling the crystal grain size
• the non-oriented electrical steel sheet described in Patent Literature 2 relates to a technology for improving blanking property by controlling the mechanical characteristics of a parent phase, it is difficult to achieve a further improvement in blanking property using such these methods alone.
• the present invention has been made in view of the foregoing problems posed by the conventional technologies, and an object of the present invention is to provide a high-Si non-oriented electrical steel sheet having blanking property improved with a method different from the conventional technologies, without degradation in iron loss properties.
• the hot-rolled sheet was subjected to hot-band annealing at 1000°C ⁇ 30 seconds, and was then pickled before being cold-rolled to obtain a cold-rolled sheet with a final thickness of 0.25 mm.
• the cold-rolled sheet was then subjected to finishing annealing at 1000°C ⁇ 10 seconds.
• each steel sheet was stamped with a new die. With respect to each of disk-like specimens obtained through 1,000,000 times of stamping, the heights of burrs generated on two cut end portions at opposite ends of the steel sheet in the rolling direction were measured. Then, the blanking property of the steel sheet was evaluated from the mean value thereof.
• Pb is not dissolved as a solid solution in steel, but is dispersed as fine granular particles (i.e., metal inclusions) in the steel.
• metal inclusions fine granular particles
• the steel ingot was hot-rolled to obtain a hot-rolled sheet with a thickness of 1.5 mm. Then, the hot-rolled sheet was subjected to hot-band annealing at 1020°C ⁇ 30 seconds, and was then pickled before being cold-rolled to obtain a cold-rolled sheet with a final thickness of 0.25 mm. The cold-rolled sheet was then subjected to finishing annealing at 1000°C ⁇ 10 seconds.
• the secondary-phase particles refer to inclusions or precipitates forming a phase other than a ferrite phase that is a parent phase.
• the secondary-phase particles refer to oxide-base inclusions, carbonitride, sulfide, boride, and their compounds.
• the particle size of each secondary-phase particle refers to the mean value of the Feret's diameter in the rolling direction and the Feret's diameter in the thickness direction.
• secondary-phase particles for the measurement of the particle size, secondary-phase particles with a particle size of 0.10 ⁇ m or greater were selected. This is because particles with a particle size of less than 0.10 ⁇ m have a low level of interaction with magnetic domain walls, and thus have little effect of pinning the magnetic domain walls. Meanwhile, particles with a particle size of 5.00 ⁇ m or greater are also excluded from the measurement target because such particles likewise have a low level of interaction with magnetic domain walls.
• a SEM was used to measure the particle sizes of the secondary-phase particles in the present invention, any method may be used as long as the observation of particles with a particle size of 0.10 ⁇ m or greater is possible. However, the use of a SEM is preferable from the perspective that the adjustment of samples is easy and wide-range observation is possible.
• the particle size (i.e., class value) of the secondary-phase particles in each section was regarded as the center value of the section (for example, the particle size of particles in a section corresponding to a particle size of 0.10 ⁇ m or greater but less than 0.20 ⁇ m was regarded as 0.15 ⁇ m), and a histogram was created where each class represents the particle size of secondary-phase particles, the frequency represents the number density N si of the secondary-phase particles, and the class interval is 0.10 ⁇ m.
• Fig. 2 illustrates the relationship between the foregoing force of pinning magnetic domain walls and the Zn content. From the graph, it is found that the force of pinning magnetic domain walls will decrease as the Zn content increases. In particular, it is found that when the Zn content is 0.0005 mass% or greater, the force of pinning magnetic domain walls will decrease down to 0.0015 particles ⁇ m -1 or less.
• Fig. 3 illustrates the relationship between the foregoing force of pinning magnetic domain walls and the iron loss W 10/400 . From the graph, it is found that the iron loss W 10/400 will also decrease as the force of pinning magnetic domain walls decreases.
• the present invention has been developed based on such new findings with further studies conducted thereon.
• the C content in the steel material is limited to 0.0050 mass% or less.
• the C content is set to 0.0040 mass% or less.
• the lower limit of the C content is not particularly specified, but it is preferably set to about 0.0001 mass% from the perspective of reducing the decarburization cost of a refining step.
• Mn is an element useful in increasing the specific resistance and strength of steel. Mn is also an element that forms sulfide to improve hot workability. Thus, in the present invention, the Mn content is set to 0.05 mass% or greater. Meanwhile, if the Mn content is over 2.0 mass%, cracking of the slab will occur, for example, which will decrease operability in the steelmaking step. Thus, the upper limit of the Mn content is set to 2.0 mass%. Preferably, the Mn content is set in the range of 0.1 to 1.5 mass%.
• P is an element having a great effect of increasing the specific resistance of steel, and thus reducing eddy current losses. P also has the effect of increasing the hardness of steel, and thus improving blanking property. Thus, P may be added in an appropriate amount. However, if P is added excessively, cold-rolling performance will degrade.
• the upper limit of the P content is set to 0.10 mass%. Preferably, the P content is set to 0.05 mass% or less.
• the S content is preferably minimized.
• the upper limit of the S content is set to 0.0050 mass%.
• the S content is set to 0.0030 mass% or less.
• Al is an element having the effect of reducing iron losses by increasing the specific resistance of steel, and the effect of increasing the strength of steel.
• the upper limit of the Al content is set to 2.0 mass%.
• the Al content is less than 0.30 mass%, fine nitride will form and precipitate, which will rather degrade the iron loss properties.
• the lower limit of the Al content is set to 0.30 mass%.
• the Al content is set in the range of 0.4 to 1.5 mass%.
• N is a detrimental element that will form nitride as such nitride will precipitate and degrade the magnetic properties.
• the N content is limited to 0.010 mass% or less.
• the N content is set to 0.0060 mass% or less.
• Pb is dispersed as fine granular metal inclusions in steel, and will remain in the steel even after finishing annealing. Accordingly, as Pb becomes the starting point of cracking or promotes the propagation of cracking when stress concentrates thereon during stamping, Pb has the effect of improving blanking property and suppressing the wear of a die. However, if the Pb content is less than 0.00010 mass%, such an effect will not be obtained sufficiently. Meanwhile, if the Pb content is over 0.010 mass%, grain growth will be hindered, which makes it impossible to achieve excellent iron loss properties. Accordingly, the Pb content is set in the range of 0.00010 to 0.010 mass%. Preferably, the Pb content is set in the range of 0.0003 to 0.0050 mass%.
• Zn forms stable and coarse sulfide or oxide. That is, Zn has the effect of suppressing an increase in iron losses due to the addition of Pb described above by coarsening secondary-phase particles in steel and thus weakening the force of pinning magnetic domain walls with the secondary-phase particles. To obtain such an effect, Zn needs to be added in an amount of 0.0005 mass% or greater. However, if the Zn content is over 0.020 mass%, such an effect will saturate. Accordingly, the Zn content is set in the range of 0.0005 to 0.020 mass%. Preferably, the Zn content is set in the range of 0.001 to 0.010 mass%.
• Ti 0.0050 mass% or less
• Nb 0.0050 mass% or less
• V 0.0050 mass% or less
• Each of Ti, Nb, and V is a detrimental element that will form fine carbonitride as such fine carbonitride will precipitate and increase iron losses.
• the content of each of these elements is over 0.0050 mass%, such an adverse effect will become significant.
• the upper limit of the content of each element is limited to 0.0050 mass%.
• the content of each element is set to 0.0030 mass% or less.
• the non-oriented electrical steel sheet of the present invention contains Pb and Zn in the foregoing ranges. Further, provided that the Pb content (mass%) and the Zn content (mass%) are respectively represented by [Zn] and [Pb], it is necessary that [Zn] and [Pb] satisfy Expression (1) below: Zn / Pb ⁇ 1.58
• the Zn and Pb contents satisfy [Zn]/[Pb] ⁇ 2.5.
• At least one of Sn and Sb a total of 0.005 to 0.20 mass%
• each of Sn and Sb has the effect of improving the recrystallization texture, and thus improving the magnetic flux density and iron loss properties.
• at least one of such components needs to be added in an amount of 0.005 mass% or greater in total.
• the total content of such a component(s) is over 0.20 mass%, the foregoing effect will saturate.
• the total content of at least one of them is preferably set in the range of 0.005 to 0.20 mass%. More preferably, the total content of at least one of them is set in the range of 0.010 to 0.10 mass%.
• Each of Ca, Mg, and REM has the effect of decreasing the force of pinning magnetic domain walls with the secondary-phase particles by forming stable and coarse sulfide or oxide.
• at least one of Ca, Mg, and REM needs to be added in an amount of 0.0005 mass% or greater in total.
• the total content of such an element(s) is over 0.020 mass%, the foregoing effect will saturate.
• the total content of at least one of them is preferably set in the range of 0.0005 to 0.020 mass%. More preferably, the total content of at least one of them is set in the range of 0.0010 to 0.010 mass%.
• At least one of Cu, Ni, and Cr a total of 0.01 to 1.0 mass%
• Each of Cu, Ni, and Cr has the effect of reducing iron losses by increasing the specific resistance of steel.
• at least one of Cu, Ni, and Cr is preferably added in an amount of 0.01 mass% or greater in total.
• the total content of such an element(s) is over 1.0 mass%, the cost of the raw materials will increase. Accordingly, the total content of at least one of such elements is preferably set in the range of 0.01 to 1.0 mass%. More preferably, the total content of at least one of such elements is set in the range of 0.03 to 0.8 mass%.
• Co has the effect of suppressing nitridation during finishing annealing.
• Co is preferably added in an amount of 0.0005 mass% or greater. Meanwhile, if the Co content is over 0.0200 mass%, such an effect will saturate, resulting in an increased cost of alloying. Accordingly, when Co is added, the Co content is preferably set in the range of 0.0005 to 0.0200 mass%. More preferably, the Co content is set in the range of 0.001 to 0.010 mass%.
• the force of pinning magnetic domain walls determined with Expression (3) below from the particle size and the number density of secondary-phase particles in the particle size range of 0.10 ⁇ m or greater but less than 5.00 ⁇ m in the steel sheet needs to be 0.0015 particles ⁇ m -1 or less.
• ⁇ i 1 n ⁇ d i N Si
• d i represents the class value ( ⁇ m) of a class i
• N si represents the frequency (number/ ⁇ m 2 ) of the class i.
• the force of pinning magnetic domain walls is 0.0012 particles ⁇ m -1 or less.
• the non-oriented electrical steel sheet of the present invention may be produced with a known method, and the production method is not limited to a particular one. An example of a preferable production method will be described below.
• steel with the foregoing composition of components which matches the present invention, is smelted through a known refining process that involves the use of a converter or an electric furnace, or a vacuum degassing apparatus, for example. Then, the steel is subjected to a known continuous casting process or ingot making-blooming process so that a steel material (i.e., a slab) is produced. If an electric furnace, for which iron scraps generated as wastes or in factories are used as a raw material, is used in the smelting process, it is possible to utilize as an iron source inexpensive scraps containing Pb and Zn as impurities, which contributes to reducing the cost of the raw materials. To produce the slab, it is also possible to produce a thin slab with a thickness of 200 mm or less with a view to reducing the rolling reduction in a subsequent cold-rolling step, and thus increasing the magnetic flux density.
• a known refining process that involves the use of a converter or an electric furnace, or a vacuum degassing apparatus,
• the cooling rate during solidification is high, finer inclusions will form, which will hinder grain growth, or increase the force of pinning magnetic domain walls.
• the steel sheet i.e., the product sheet
• the stamping die was replaced with a new one for each steel sheet.
• the heights of burrs in the rolling direction on two stamping end portions at opposite ends of the specimen were measured, and the mean value thereof was calculated.

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• 2023
  • 2023-10-30 JP JP2024504964A patent/JP7552952B1/ja active Active
  • 2023-10-30 KR KR1020257019007A patent/KR20250096858A/ko active Pending
  • 2023-10-30 CN CN202380080245.7A patent/CN120187883A/zh active Pending
  • 2023-10-30 WO PCT/JP2023/039033 patent/WO2024142579A1/fr not_active Ceased
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