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WO2020111640A1 - Tôle d'acier électrique non orientée ayant une faible perte dans le fer et une excellente qualité de surface, et son procédé de fabrication - Google Patents

Tôle d'acier électrique non orientée ayant une faible perte dans le fer et une excellente qualité de surface, et son procédé de fabrication Download PDF

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WO2020111640A1
WO2020111640A1 PCT/KR2019/015937 KR2019015937W WO2020111640A1 WO 2020111640 A1 WO2020111640 A1 WO 2020111640A1 KR 2019015937 W KR2019015937 W KR 2019015937W WO 2020111640 A1 WO2020111640 A1 WO 2020111640A1
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steel sheet
electrical steel
iron loss
surface quality
excellent surface
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Korean (ko)
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공종판
차경세
이세일
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Posco Holdings Inc
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Posco Co Ltd
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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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • 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
    • B21B1/463—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 in a continuous process, i.e. the cast not being cut before rolling
    • 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
    • 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
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • 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
    • C21D9/0062—Heat-treating apparatus with a cooling or quenching zone
    • 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
    • C22C38/008—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
    • C22C38/04—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
    • H01F1/147—Alloys characterised by their composition
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/14766—Fe-Si based alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C2202/00—Physical properties
    • C22C2202/02—Magnetic

Definitions

  • the present invention relates to a non-oriented electrical steel sheet having excellent iron loss and surface quality, and a method for manufacturing the same.
  • Patent Document 1 discloses a non-oriented electrical steel sheet in which 0.1 to 5% of Co is added to steel having Si of 4% or less. It is.
  • Patent Document 2 the content of P is 0.07 to 0.20%, the content of Si is 0.17 to 3.0%, hot-rolled sheet annealing is performed by box annealing with a slow cooling rate, and the aggregate structure is formed at the time of finish annealing.
  • Patent Document 3 proposes a method for achieving a high magnetic flux density by setting the Al content to 0.017% or less.
  • Patent Document 4 proposes a technique for adding a Sb or Sn as an element other than the above to increase the magnetic flux density.
  • Patent Document 5 proposes a technique for improving magnetic properties by precisely controlling Ti, Nb, V, and B. As described above, in the case of the non-oriented electrical steel sheet, most of the techniques for improving the magnetic properties by precisely controlling the alloy component, and the research related to the control of the microstructure (unrecrystallized structure fraction, etc.) and scale quality of the hot-rolled material is very small.
  • a new steel manufacturing process which has recently attracted attention, is a manufacturing process using a so-called thin slab (mini-mill process), in particular, the direct-to-rolling direct process has a temperature deviation in the width and length of the strip due to the isothermal isothermal process characteristics. Because of its small size, it has attracted attention as a process with excellent material deviation and the potential to produce thin hot-rolled electrical steel sheets. This reason is different from the existing process that is rolled in batch form for every coil. In the case of the performance-rolling diameter process, only the first coil has a top part, so it is inserted, and only the final coil has a tail part.
  • Patent Document 1 Japanese Patent Publication No. 2000-129410
  • Patent Document 2 Japanese Patent Registration No. 3870893
  • Patent Document 3 Japanese Patent Registration No. 4126479
  • Patent Document 4 Japanese Patent Registration No. 2500033
  • Patent Document 5 Korean Patent Publication No. 10-2016-0078183
  • One aspect of the present invention is to provide a non-oriented electrical steel sheet having excellent iron loss and surface quality and a method of manufacturing the same, using a high-speed casting and continuous-rolling manufacturing process in a direct-rolling direct connection process.
  • One embodiment of the present invention in weight percent, C: 0.0005 to 0.0060%, Si: 2.6 to 3.8%, Mn: 0.05 to 2.0%, Al: 0.05 to 2.0%, Sn: 0.005 to 0.20%, P: 0.002 to 0.30%, S: 0.0002 ⁇ 0.005%, Ti: 0.0002 ⁇ 0.01%, Nb: 0.0002 ⁇ 0.01%, V: 0.0002 ⁇ 0.01%, N: 0.0005 ⁇ 0.006%, including balance Fe and other unavoidable impurities, and the following relationship It provides a non-oriented hot-rolled electrical steel sheet that satisfies 1 to 5 and has a low iron loss and excellent surface quality with an unrecrystallized structure of 30 to 80 area%.
  • the present invention it is possible to produce a thin-walled electrical steel sheet having a uniform microstructure and excellent scale quality through a high-speed casting and a continuous rolling process in a direct-rolling process.
  • the electric steel sheet manufactured through the continuous rolling process of the present invention can manufacture thin-walled hot-rolled materials of 1.6 mm or less compared to the existing hot-rolled electrical steel sheet manufactured through the batch process, thereby reducing the rolling reduction during the final cold rolling, thereby causing high-frequency iron loss.
  • the reduction performance is excellent.
  • FIG. 1 is a schematic diagram of a facility for a continuous casting-rolling direct connection process applicable to the production of hot rolled steel sheet of the present invention.
  • FIG. 2 is another schematic view of a facility for a continuous casting-rolling direct connection process applicable to the production of a hot rolled steel sheet of the present invention.
  • Figure 3 is a transmission micrograph (Replica specimen) of the composite precipitate for invention example 1 (cold rolled electrical steel sheet) according to an embodiment of the present invention.
  • FIG. 5 is an optical microscope organization photograph of Inventive Example 9 (hot-rolled electrical steel sheet) according to an embodiment of the present invention.
  • Comparative Example 16 hot rolled electrical steel sheet according to an embodiment of the present invention.
  • Example 7 is an electron microscope (SEM) organizational photograph of a scale cross-section for Inventive Example 10 (hot-rolled electrical steel sheet) according to an embodiment of the present invention.
  • the lower limit is preferably 0.0005%. Therefore, the C content is preferably 0.0005 to 0.0060%.
  • the lower limit of the C content is more preferably 0.0010%, and even more preferably 0.0015%.
  • the upper limit of the C content is more preferably 0.0050%, and even more preferably 0.0035%.
  • Silicon (Si) is generally added as a deoxidizing agent for steel, but is an important element because it has the effect of increasing the electrical resistance and reducing iron loss at high frequencies in an electric steel sheet, and it is necessary to add 2.6% or more to obtain such an effect. However, if it exceeds 3.8%, the strength of the steel sheet becomes too high, and thus, during cold rolling, a shape defect may occur due to an increase in the rolling load, so the upper limit is preferably 3.8%. Therefore, the Si content is preferably 2.6 to 3.8%.
  • the lower limit of the Si content is more preferably 2.9%, and even more preferably 3.1%.
  • the upper limit of the Si content is more preferably 3.7%, and even more preferably 3.5%.
  • manganese (Mn) is an element that can increase iron resistivity and lower iron loss, it is preferable to add 0.05% or more. However, if it exceeds 2.0%, the effect of reducing iron loss is reduced because it inhibits grain growth by forming coarse MnS precipitates in combination with S in steel. Therefore, it is preferable that the content of the Mn has a range of 0.05 to 2.0%.
  • the lower limit of the Mn content is more preferably 0.1%, and even more preferably 0.3%.
  • the upper limit of the Mn content is more preferably 1.6%, and even more preferably 1.2%.
  • Aluminum (Al) is generally used as a deoxidizing agent for steel in the same way as Si, and it is preferable to add 0.05% or more because it is an element having a large effect of reducing iron loss by increasing electrical resistance in electric steel sheets. However, if it exceeds 2.0%, it is picked up to the mold flux during continuous casting to change the physical properties of the mold flux, thereby deteriorating lubricity, which may result in interruption of casting. In addition, since the strength of the steel sheet is too high, shape defects may occur as the rolling load increases during cold rolling. Therefore, the Al content is preferably in the range of 0.05 to 2.0%. The lower limit of the Al content is more preferably 0.1%, and even more preferably 0.3%. The upper limit of the Al content is more preferably 1.6%, and even more preferably 1.2%.
  • Tin (Sn) is a grain boundary segregation element that suppresses the diffusion of nitrogen through grain boundaries, inhibits the formation of ⁇ 111 ⁇ , ⁇ 112 ⁇ aggregates that are harmful to magnetism, and ⁇ 100 ⁇ and ⁇ 110 ⁇ aggregates that are advantageous for magnetism. Increase to improve magnetic properties. In order to secure the above effect, it is preferable to add 0.005% or more. However, if it is added in excess of 0.20%, there is a disadvantage in that the grain growth is suppressed, the magnetism is reduced, and the rollability is inferior. Therefore, it is preferable that the amount of Sn added has a range of 0.005 to 0.20%.
  • the lower limit of the Sn content is more preferably 0.02%, and even more preferably 0.03%.
  • the upper limit of the Sn content is more preferably 0.15%, and even more preferably 0.10%.
  • Phosphorus (P) is an element that can increase the specific resistance in steel to lower iron loss, and is an element that can improve the magnetic flux density when added as a magnetic material, and it is preferable to add 0.002% or more for the above effect.
  • P is a segregation element that induces rolling plate fracture in ferrite at normal temperature rolling, and it is not preferable to exceed 0.30% because it segregates in grain boundaries in the steel and greatly weakens the bonding force between grain boundaries. Therefore, it is preferable that the P has a range of 0.002 to 0.30%.
  • the lower limit of the P content is more preferably 0.005%, and even more preferably 0.006%.
  • the upper limit of the P content is more preferably 0.10%, and even more preferably 0.05%.
  • S Sulfur
  • the lower limit is preferably 0.0002%. Therefore, the content of S is preferably in the range of 0.0002 ⁇ 0.005%.
  • the lower limit of the S content is more preferably 0.0004%, and even more preferably 0.0005%.
  • the upper limit of the S content is more preferably 0.004%, and even more preferably 0.003%.
  • Titanium (Ti) exacerbates iron loss by forming carbides or nitrides and interfering with grain growth, and promotes the development of ⁇ 111 ⁇ aggregates, which is undesirable for magnetism, so it is preferable to add it to 0.01% or less.
  • the content of Ti is preferably 0.0002 to 0.01%.
  • the lower limit of the Ti content is more preferably 0.0004%, and even more preferably 0.0005%.
  • the upper limit of the Ti content is more preferably 0.005%, and even more preferably 0.0035%.
  • Niobium (Nb) forms carbides or nitrides to interfere with grain growth, thereby exacerbating iron loss, and it is desirable to add less than 0.01% since it promotes the development of ⁇ 111 ⁇ aggregates that are undesirable for magnetism.
  • the Nb is preferably as small as possible, so it is not particularly limited, but it is preferable to limit the lower limit to 0.0002% in consideration of pickup from alloy iron. Therefore, the content of Nb is preferably 0.0002 to 0.01%.
  • the lower limit of the Nb content is more preferably 0.0004%, and even more preferably 0.0005%.
  • the upper limit of the Nb content is more preferably 0.005%, and even more preferably 0.0035%.
  • Vanadium (Nb) is preferably added to 0.01% or less since it forms carbides or nitrides and interferes with grain growth, thereby exacerbating iron loss and promoting the development of ⁇ 111 ⁇ aggregates that are undesirable for magnetism.
  • the lower limit of the V content is more preferably 0.0004%, and even more preferably 0.0005%.
  • the upper limit of the V content is more preferably 0.005%, and even more preferably 0.0035%.
  • Nitrogen (N) is preferably added in an amount of 0.006% or less because it deteriorates the magnetic properties in the same manner as C described above.
  • the lower limit is preferably 0.0005%. Therefore, the N content is preferably 0.0005 to 0.006%.
  • the lower limit of the N content is more preferably 0.0008%, and even more preferably 0.0010%.
  • the upper limit of the N content is more preferably 0.004%, and even more preferably 0.003%.
  • the remaining component of the invention is iron (Fe).
  • impurities that are not intended from the raw material or the surrounding environment may be inevitably mixed, and therefore cannot be excluded. Since these impurities are known to anyone skilled in the ordinary manufacturing process, they are not specifically mentioned in this specification.
  • Si, Al, Mn, Sn, P, Ti, Nb, V, C and N among the above-described alloy components satisfy the following relations 1 to 5, respectively.
  • the contents of Si, Al, Mn, Sn, P, Ti, Nb, V, C and N described in relations 1 to 3 below are weight%.
  • the value of the relational expression 1 has a range of 3.5 to 6.0.
  • the lower limit of the value of the relational expression 1 is more preferably 3.7, and even more preferably 3.8.
  • the upper limit of the value of the relational expression 1 is more preferably 5.8, and even more preferably 5.6.
  • the value of [(Ti/48+Nb/93+V/51)(C/12+N/14)] ⁇ 10 8 in the relational expression 2 exceeds 5.0, precipitates are excessively precipitated, and crystal grain growth is not sufficiently achieved. Because iron loss can be inferior.
  • the lower limit of the value of the relational expression 2 is more preferably 1.1, and even more preferably 1.2.
  • the upper limit of the value of the relational expression 2 is more preferably 4.9, and even more preferably 4.8.
  • the value of [Si+Al+(Mn+Sn)/2+5P]/[(Ti/48+Nb/93+V/51)(C/12+N/14) ⁇ 10 8 ] is 4.5 If it exceeds, the yield strength of the hot rolled material is too high, and thus the appearance shape quality of the final product may be inferior due to poor mailability due to the increase in rolling load during cold rolling. On the other hand, when the value of the relational expression 3 is less than 0.85, precipitates are excessively precipitated, and crystal grain growth is not sufficiently performed, so that iron loss may be inferior. Therefore, it is preferable that the value of the relational expression 3 has a range of 0.85 to 4.5.
  • the lower limit of the value of the relational expression 3 is more preferably 0.90, and even more preferably 0.95.
  • the upper limit of the value of the relational expression 3 is more preferably 4.0, and even more preferably 3.5.
  • the relational expression (4) is a formula related to magnetic properties and cold rolling properties.
  • the value of the relational expression (4) exceeds 8.0, the yield strength of the hot rolled material is too high, and plate breakage may occur due to poor mailability due to an increase in rolling load during cold rolling.
  • the value of the relational expression 4 is less than 3.8, the target iron loss may not be obtained. Therefore, it is preferable that the value of the relational expression 4 has a range of 3.8 to 8.0.
  • the lower limit of the value of the relational expression 4 is more preferably 4.0, and even more preferably 4.2.
  • the upper limit of the value of the relational expression 4 is more preferably 7.8, and even more preferably 7.6.
  • the relational expression 5 is a component relational formula for producing a material having low iron loss and excellent cold rolling properties.
  • the value of the relational expression 5 exceeds 1.35, the component content of Mn, Al, etc. is high, so that the playability and rollability may be inferior, and if it is less than 0.55, the P content is high, and the mailing property due to the increase in rolling load during cold rolling Failure can lead to plate breakage.
  • the electrical steel sheet of the present invention is one or more selected from the group consisting of Mo, Cu, Cr, Ni, Zn, Se, Sb, Zr, W, Ga, Ge, Ca and Mg as a tramp element in addition to the alloy composition described above. It may be included so that the total is 0.2% or less.
  • the tramp element is an impurity element originating from scrap, ladle, and tundish refractory material used as a raw material in the steelmaking process, and when the sum exceeds 0.2%, it is liquefied at high temperature to deteriorate performance. , It may worsen the iron loss by forming a precipitate.
  • the hot rolled electrical steel sheet of the present invention is preferably a non-recrystallized structure is 30 to 80 area%.
  • the fraction of the non-recrystallized structure exceeds 80 area%, it is difficult to obtain a sufficient recrystallized structure during cold rolling/annealing, and it is difficult to obtain a targeted iron loss reduction effect because grain growth is not smooth.
  • the fraction of the non-recrystallized structure in the microstructure of the hot-rolled electrical steel sheet is preferably 30 to 80 area%.
  • the lower limit of the fraction of the non-recrystallized structure is more preferably 35 area%, and more preferably 40 area%.
  • the upper limit of the fraction of the non-recrystallized structure is more preferably 75 area%, and even more preferably 70 area%.
  • the aforementioned non-recrystallized structure means a structure stretched in the rolling direction, and may be, for example, a structure in which the ratio of the long axis and the short axis is 5 or more.
  • the hot-rolled electrical steel sheet of the present invention may have a scale thickness of 7 ⁇ m or less. As described above, by reducing the thickness of the scale, good pickling properties can be secured to improve the surface quality of the finally obtained product.
  • the scale thickness of the hot-rolled electrical steel sheet is more preferably 6 ⁇ m or less, and even more preferably 5 ⁇ m or less.
  • the hot-rolled electrical steel sheet of the present invention may have a Si thickening layer thickness between the scale and the base iron of 1.4 ⁇ m or less. As described above, by controlling the thickness of the Si thickening layer, good pickling properties can be secured, thereby improving the surface quality of the finally obtained product.
  • the Si thickening layer thickness is more preferably 1.2 ⁇ m or less, and even more preferably 1.0 ⁇ m or less.
  • Fe 2 O 3 in the scale may be 75 area% or less.
  • the Fe 2 O 3 is generally known to have poor acidity.
  • by controlling the fraction of Fe 2 O 3 to 75 area% or less it is possible to secure a better pickling property and secure a good surface quality.
  • the fraction of Fe 2 O 3 in the scale is more preferably 70 area% or less, and even more preferably 65 area% or less.
  • the hot rolled electrical steel sheet of the present invention is preferably 0.6 to 1.6 mm thick.
  • the recrystallized aggregate structure increases to ensure a uniform structure after annealing, and also, the cold rolling reduction rate can be reduced, thereby reducing the crystal orientation of ⁇ -fiber and improving magnetic properties. And thickness variation can also be reduced.
  • the thickness of the hot-rolled electrical steel sheet exceeds 1.6 mm, the above effect may not be sufficient.
  • the thickness of the hot-rolled electrical steel sheet is less than 0.6 mm, the applicable cold rolling reduction rate is too low, which may make it difficult to sufficiently obtain a recrystallized structure.
  • the thickness of the hot-rolled electrical steel sheet is 0.6 to 1.6 mm.
  • the lower limit of the thickness of the hot-rolled electrical steel sheet is more preferably 0.7 mm, and even more preferably 0.8 mm.
  • the upper limit of the thickness of the hot-rolled electrical steel sheet is more preferably 1.5 mm, and even more preferably 1.4 mm.
  • the above-described hot-rolled electrical steel sheet may be made of cold-rolled electrical steel sheet through cold rolling and annealing processes.
  • the cold-rolled electrical steel sheet of the present invention preferably has an average ferrite grain size of 70-100 ⁇ m. If the average grain size of the ferrite grains (FGS, Ferrite Grain Size) is less than 70 ⁇ m, the iron grains are inferior because the grains do not grow sufficiently, and if it exceeds 100 ⁇ m, the magnetic flux density may decrease, so the average grain size of the ferrite grains is 70-100 ⁇ m It is preferred to have a range of.
  • the lower limit of the average size of the ferrite grains is more preferably 72 ⁇ m, and even more preferably 74 ⁇ m.
  • the upper limit of the average size of the ferrite grains is more preferably 98 ⁇ m, and even more preferably 96 ⁇ m.
  • the cold-rolled electrical steel sheet preferably has a thickness of 0.10 to 0.32 mm.
  • the thickness of the cold-rolled electrical steel sheet is preferably 0.10 ⁇ 0.32mm.
  • the lower limit of the thickness of the cold-rolled electrical steel sheet is more preferably 0.15 mm, and even more preferably 0.20 mm.
  • the upper limit of the thickness of the cold rolled electrical steel sheet is more preferably 0.30 mm, and even more preferably 0.28 mm.
  • the cold rolled electrical steel sheet provided by the present invention may have a high frequency iron loss (W10/400) of 10.5 to 13.5 W/kg, more preferably 10.7 to 13.4 W/kg, and even more preferably 10.9 to 13.3 W. It can be /kg.
  • the high-frequency iron loss (W10/400) means the average iron loss in the rolling direction and the direction perpendicular to the rolling direction when a magnetic flux density of 1.0 Tesla is induced at a frequency of 400 Hz.
  • the cold-rolled electrical steel sheet of the present invention may have a width direction gloss deviation of 8 or less, more preferably 7 or less, and even more preferably 6 or less.
  • the deviation in glossiness means a difference between a maximum value and a minimum value in the width direction.
  • FIG. 1 is a schematic diagram of a facility for a continuous casting-rolling direct connection process applicable to the production of a thin electric steel sheet of the present invention.
  • the non-oriented electrical steel sheet having low iron loss and excellent surface quality according to an embodiment of the present invention can be produced by applying a continuous casting-rolling direct connection facility as shown in FIG. 1.
  • the continuous casting-rolling direct connection facility is largely composed of a continuous casting machine 100, a rough rolling machine 400, and a finishing rolling machine 600.
  • the continuous casting-rolling direct connection facility is a high-speed continuous casting machine 100 producing a thin slab (a) having a first thickness, and a bar having a second thickness thinner than the first thickness (Bar) ) (b) includes a rough rolling mill (400), a finishing mill for rolling the bar having the second thickness into a strip (c) having a third thickness, and a winding machine (900) for winding the strip. can do.
  • the rough rolling mill breaker 300 in front of the rough rolling mill 400 (Roughing Mill Scale Breaker, hereinafter'RSB') and the finishing rolling scale breaker 500 in front of the finishing mill 600 (Fishing Mill Scale Breaker, hereinafter ' FSB') can be additionally included, and it is easy to remove the surface scale, making it possible to produce non-oriented electrical steel sheets with excellent surface quality when pickling hot rolled steel sheets in a later process.
  • FIG. 2 is another schematic view of a facility for a continuous casting-rolling direct connection process applicable to the production of a thin electric steel sheet of the present invention.
  • the continuous casting-rolling direct connection facility disclosed in FIG. 2 is mostly the same in configuration as the facility disclosed in FIG. 1, but is equipped with a heater 200' that additionally heats the slab in front of the rough rolling mill 400 and the rough rolling scale breaker 300.
  • a heater 200' that additionally heats the slab in front of the rough rolling mill 400 and the rough rolling scale breaker 300.
  • the slab edge temperature the occurrence of edge defects is low, which is advantageous for securing the surface quality.
  • batch type rolling is possible.
  • a molten slab having the above-described alloy composition is continuously cast to obtain a thin slab.
  • the continuous casting is preferably performed at a casting speed of 4.0 to 7.5mpm (m/min) or less.
  • the reason why the casting speed is 4.0MPm or more is that a high-speed casting and a rolling process are connected, and a casting speed of a predetermined or higher is required to secure a target rolling temperature.
  • the casting speed is slow, as the amount of Al picked up to the mold flux increases, the properties of the mold flux change, and lubrication decreases, which may lead to casting interruption.
  • the casting speed is preferably in the range of 4.0 to 7.5mpm.
  • the lower limit of the casting speed is more preferably 4.5mpm, and even more preferably 5.0mpm.
  • the upper limit of the casting speed is more preferably 7.0mpm, and even more preferably 6.5mpm.
  • the thickness of the thin slab is preferably 75 ⁇ 125mm.
  • the thickness of the thin slab exceeds 125mm, not only high-speed casting is difficult, but also the rolling load increases during rough rolling, and if it is less than 75mm, the temperature of the cast slab rapidly decreases and it is difficult to form a uniform structure.
  • the lower limit of the thickness of the thin slab is more preferably 80 mm, and even more preferably 85 mm.
  • the upper limit of the thickness of the thin slab is more preferably 120 mm, and even more preferably 115 mm.
  • the coolant is sprayed on the thin slab to remove the scale.
  • the surface scale of the thin slab can be removed to a thickness of 200 ⁇ m or less by spraying coolant at 50° C. or less at a pressure of 50 to 350 bar from a roughing mill scale breaker (hereinafter referred to as'RSB').
  • a roughing mill scale breaker hereinafter referred to as'RSB'.
  • the pressure is less than 50 bar, a large amount of arithmetic scale or the like remains on the surface of the thin slab, and the surface quality may deteriorate after pickling.
  • the edge temperature of the thin slab sharply decreases and edge cracking may occur. Therefore, when cooling water is injected into the thin slab, the cooling water injection pressure is preferably 50 to 350 bar.
  • the lower limit of the cooling water injection pressure is more preferably 100 bar, and even more preferably 150 bar.
  • the upper limit of the cooling water injection pressure is more preferably 300 bar, and even more preferably 250 bar.
  • the thin slab from which the scale has been removed is rough-rolled to obtain a bar.
  • the rough rolling inlet temperature may be 1000 to 1200°C, and a bar having a thickness of 10 to 30 mm may be obtained through the rough rolling.
  • the rough rolling entry temperature is less than 1000°C, the rough rolling load may increase, and cracks may occur at the edge of the thin slab.
  • the temperature exceeds 1200°C the hot rolled scale remains and the surface quality of the hot rolled electrical steel sheet may deteriorate.
  • the temperature at the rough rolling side may be 900°C or higher.
  • the exit temperature of the rough rolling if the exit temperature of the rough rolling is less than 900°C, it may be difficult to secure a finish rolling temperature.
  • the upper limit of the temperature at the exit side of the rough rolling may be less than 1000°C, and when it is higher than 1000°C, the surface quality of the hot-rolled electrical steel sheet may deteriorate because a hot-rolled scale remains.
  • the heating of the bar can be performed for 0.1 to 1.2 seconds in a range of 1000 to 1200°C, for example.
  • the reason for controlling the heating temperature of the bar is to stably produce a hot rolled electrical steel sheet and to secure the surface quality.
  • the heating is to ensure a sufficient temperature during the finish rolling, wherein the heating time of the bar is related to scale growth and diffusion of the Si thickening layer.
  • the heating temperature of the bar is preferably 1000 ⁇ 1200 °C.
  • the lower limit of the heating temperature of the bar is more preferably 1020°C, and even more preferably 1040°C.
  • the upper limit of the heating temperature of the bar is more preferably 1160°C, and even more preferably 1120°C.
  • the heating time of the bar exceeds 1.2 seconds, the scale may be overgrown, and the Si thickening layer may be thickly formed between the scale and the small iron to remain uneven after pickling, resulting in poor surface quality, and less than 0.1 seconds.
  • the bar may not be sufficiently heated, and the rolling load may rise rapidly during finish rolling, and thus the mailing property may be inferior. Therefore, the heating time of the bar is preferably 0.1 to 1.2 seconds.
  • the lower limit of the heating time of the bar is more preferably 0.2 seconds, and even more preferably 0.3 seconds.
  • the upper limit of the heating time of the bar is more preferably 1.0 seconds, and even more preferably 0.8 seconds.
  • cooling water is sprayed on the heated bar to remove the scale.
  • the surface scale may be removed to a thickness of 7 ⁇ m or less by spraying cooling water at 50° C. or less at a pressure of 50 to 250 bar in a finishing mill scale breaker (hereinafter referred to as'FSB').
  • 'FSB' finishing mill scale breaker
  • the cooling water injection pressure is less than 50 bar, the scale is insufficiently removed, resulting in a large amount of spindle- and scale-like scales on the surface of the steel sheet after finish rolling, resulting in poor surface quality after pickling.
  • the cooling water injection pressure exceeds 250 bar, it is difficult to secure the target finish rolling temperature, and as the rolling load increases, the mailing property decreases and operation stoppage may occur.
  • the coolant injection pressure is preferably 50 to 250 bar.
  • the lower limit of the cooling water injection pressure is more preferably 60 bar, and even more preferably 70 bar.
  • the upper limit of the cooling water injection pressure is more preferably 230 bar, and even more preferably 210 bar.
  • lubricating oil injection reduces the friction coefficient between the rolls of the first rolling mill, which has a very large rolling load among the bars and the finish rolling mill, and applies a strain to the central layer as well as the surface layer of the strip to reduce the fraction of the unrecrystallized structure and cold it. This is to promote grain growth after rolling/annealing.
  • amount of the lubricating oil is less than 10 l/min per 1 m2 of the surface of the bar, the effect is negligible.
  • the injection amount of the lubricating oil is preferably 10 ⁇ 60l / min per 1m2.
  • the lower limit of the injection amount of the lubricant is more preferably 15 l/min per 1 m2 of the surface of the bar, and more preferably 20 l/min per 1 m2 of the surface of the bar.
  • the upper limit of the injection amount of the lubricant is more preferably 55 l/min per 1 m2 of the surface of the bar, and even more preferably 50 l/min per 1 m2 of the surface of the bar.
  • the lubricating oil may be sprayed from the mouth of the first rolling mill before finishing rolling.
  • the hot-rolled steel sheet is obtained by finishing rolling (FM) the bar onto which the lubricant is sprayed.
  • the finishing rolling can be performed on a bar made by a rough rolling mill in a finishing mill consisting of 3 to 6 stands.
  • the entry temperature of the first rolling mill is 900 to 1200°C. If the temperature of the first rolling mill exceeds 1200°C, the surface quality may be inferior due to excessive scale, and if it is less than 900°C, the temperature is too low during the finish rolling, so that recrystallization does not occur sufficiently and the strip has a high recrystallization fraction, so it is cold. When rolling/annealing, grain growth may not occur sufficiently. Therefore, it is preferable that the entry temperature of the first rolling mill is 900 to 1200°C. The lower limit of the entry temperature of the first rolling mill is more preferably 940°C, and even more preferably 980°C. The upper limit of the entry temperature of the first rolling mill is more preferably 1160°C, and even more preferably 1120°C.
  • the reduction rate in the first rolling mill may be 35 to 70%.
  • the rolling reduction rate in the first rolling mill exceeds 70%, the mailing properties may be unstable due to the increase in rolling load, and if it is less than 35%, the strain may be low and recrystallization may not occur well.
  • the lower limit of the rolling reduction in the first rolling mill is more preferably 40%, and even more preferably 45%.
  • the upper limit of the rolling reduction in the first rolling mill is more preferably 65%, even more preferably 60%.
  • the temperature of the entrance of the last rolling mill is preferably 700 to 900°C.
  • the inlet temperature of the last mill exceeds 900°C, the scale may grow after finishing rolling, and the surface quality may be inferior. If it is less than 700°C, the mailing property may be unstable due to the increase in rolling load, and recrystallization may not occur sufficiently. Can be. Therefore, it is preferable that the entry temperature of the last rolling mill is 700 to 900°C.
  • the lower limit of the entry temperature of the last mill is more preferably 720°C, and even more preferably 740°C.
  • the upper limit of the entry temperature of the last mill is more preferably 880°C, and even more preferably 860°C.
  • the rolling reduction in the last rolling mill may be 8 to 24%.
  • the rolling reduction rate in the last rolling mill exceeds 24%, the rolling load may increase, resulting in poor mailability, and if it is less than 12%, the strain may be low and sufficient recrystallization may not occur.
  • the lower limit of the rolling reduction in the last mill is more preferably 10%, and even more preferably 12%.
  • the upper limit of the rolling reduction in the last mill is more preferably 22%, and even more preferably 20%.
  • the average sheet speed in the last mill may be 250 to 750mpm (m/min).
  • the plate speed in the final rolling machine may be directly related to the casting speed and the thickness of the final hot rolled product. If the average sheet speed in the last mill is more than 750mpm, an operation accident such as plate breakage may occur, and uniform temperature may not be secured due to difficulty in isothermal constant velocity rolling, resulting in material and thickness variations. On the other hand, if it is less than 250mpm, the rolling speed is too slow, which may cause problems in mass balance and heat balance, and it may be difficult to perform continuous rolling.
  • the hot rolled steel sheet is wound.
  • the winding can be performed at 500 to 660°C.
  • the coiling temperature is less than 500°C, the yield strength is too high, and the rolling load increases during cold rolling, which may lead to poor thickness variation due to poor mailability, and when exceeding 660°C, the yield strength is low and cold rolling.
  • the coiling temperature is preferably 500 to 660°C.
  • the lower limit of the coiling temperature is more preferably 520°C, and even more preferably 540°C.
  • the upper limit of the coiling temperature is more preferably 640°C, and even more preferably 620°C.
  • the hot rolled electrical steel sheet obtained as described above may be pickled/cold rolled/annealed to produce a cold rolled electrical steel sheet.
  • the pickling can use any method commonly used in the art, and the present invention is not particularly limited to the pickling method.
  • the cold rolling method is not particularly limited.
  • the annealed cold rolled steel sheet is annealed and cracked at the following [Relational Formula 6] +30°C or higher and 1160°C or lower.
  • the following relational expression 6 is a (Ti,Nb,V)(C) precipitation temperature prediction formula.
  • the annealing crack temperature is less than (Ti,Nb,V)(C) precipitation temperature +30°C, precipitates are not dissolved and excessively precipitated, which may interfere with grain growth and deteriorate iron loss, and when it exceeds 1160°C
  • the grain size may be too coarse and the magnetic flux density may be inferior.
  • the annealing crack zone temperature has a range of [Relational Formula 6] +30°C or higher and 1160°C or lower.
  • the lower limit of the annealing crack zone temperature is more preferably [Relational Formula 6]+35°C, and more preferably [Relational Formula 6]+40°C.
  • the upper limit of the annealing crack zone temperature is more preferably 1140°C, and more preferably 1100°C.
  • the line speed may be about 120mpm.
  • the microstructure was observed using an optical microscope, and the area fraction of the non-recrystallized structure means the proportion of the unrecrystallized structure in the cross section of the strip.
  • the scale thickness was measured using a GDS (glow discharge spectrometer), and the depth of the Si thickening layer was processed using a focused ion beam processing observing equipment (FIB) to process the scale cross-section and photographed the tissue with a scanning electron microscope (SEM). Confirmed. And the Fe 2 O 3 fraction on the scale was measured using X-ray diffraction analysis (XRD).
  • GDS low discharge spectrometer
  • FIB focused ion beam processing observing equipment
  • SEM scanning electron microscope
  • XRD X-ray diffraction analysis
  • the average grain size of the ferrite was photographed at random 10 (Random) at 25 times magnification using an optical microscope, and the average value measured by the line-intercept method was described.
  • the high-frequency iron loss was obtained by measuring the specimens of 3 sheets in the rolling direction and 3 sheets in the rolling vertical direction with a size of 305 mm ⁇ 30 mm, and measuring them with an Epstein tester.
  • the high frequency iron loss (W10/400) represents the average loss (W/kg) in the rolling direction and in the direction perpendicular to the rolling direction when a magnetic flux density of 1.0 Tesla is induced at a frequency of 400 Hz.
  • the glossiness is a numerical representation of the glossiness of the surface of a steel sheet, measured using a Rhopoint IQ TM device, and the glossiness deviation means the difference between the minimum and maximum glossiness in the width direction.
  • FIG. 3 is a transmission micrograph (Replica specimen) of the composite precipitate for Inventive Example 1 (cold rolled electrical steel sheet), and FIG. 4 is a transmission microscope (Replica Specimen) of the composite precipitate for Comparative Example 10 (Cold Rolled Electric Steel Sheet).
  • (Ti,Nb,V)C precipitates are present in the grain boundaries.
  • Comparative Example 10 does not satisfy relations 2 and 3, and thus it can be confirmed that a large amount of (Ti,Nb,V)C precipitates are present in the grain boundaries, which can be expected to adversely affect grain growth.
  • FIG. 5 is an optical microscope tissue picture for Inventive Example 9 (hot rolled electrical steel sheet)
  • FIG. 6 is an optical microscope tissue picture for Comparative Example 16 (hot rolled electrical steel sheet).
  • Figures 5 and 6 in the case of Inventive Example 9, it can be seen that less unrecrystallized structure is formed than Comparative Example 16, and through this, Inventive Example 9 has smooth grain growth compared to Comparative Example 16. Therefore, it can be predicted that it will have a relatively high iron loss reduction effect.
  • the alloy compositions proposed by the present invention, relations 1 to 5, and Inventive Examples 10 and 11 satisfying the manufacturing conditions not only satisfy the scale conditions of the present invention, but also have a deviation in glossiness. It can be seen that it is excellent.
  • FIG. 7 is an electron microscope (SEM) organization photograph of a scale cross-section for Inventive Example 10 (hot-rolled electrical steel sheet)
  • FIG. 8 is an electron microscope (SEM) organization photograph of a scale cross-section for Comparative Example 20 (hot-rolled electrical steel sheet).
  • SEM electron microscope

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Abstract

Un mode de réalisation de la présente invention concerne une tôle d'acier électrique non orientée ayant une faible perte dans le fer et une excellente qualité de surface, la tôle d'acier électrique non orientée comprenant, en % en poids, 0,0005 à 0,0060 % de C, 2,6 à 3,8 % de Si, 0,05 à 2,0 % de Mn, 0,05 à 2,0 % d'Al, 0,005 à 0,20 % de Sn, 0,002 à 0,30 % de P, 0,0002 à 0,005 % de S, 0,0002 à 0,01 % de Ti, 0,0002 à 0,01 % de Nb, 0,0002 à 0,01 % de V, 0,0005 à 0,006 % de N, et le reste de Fe et d'autres impuretés inévitables, satisfaisant ainsi les relations suivantes 1 à 5, et ayant 30 à 80 % en surface d'une structure de région non recristallisée. [Relation 1] 3,5 ≤ [Si+Al+(Mn+Sn)/2+5P] ≤ 6,0 [Relation 2] 1,0 ≤ [(Ti/48+Nb/93+V/51)(C/12+N/14)]×108≤ 5,0 [Relation 3] 0,85 ≤ [Si+Al+(Mn+Sn)/2+5P]/[(Ti/48+Nb/93+V/51)(C/12+N/14)×108] ≤ 4,5 [Relation 4] 3,8 ≤ [Si+100P] ≤ 8,0 [Relation 5] 0,55 ≤ [Si+Al+(Mn+Sn)/2+5P]/[Si+100P] ≤ 1,35 (Dans les relations 1 à 5, la quantité de Si, Al, Mn, Sn, P, Ti, Nb, V, C et N est exprimée en % en poids.)
PCT/KR2019/015937 2018-11-29 2019-11-20 Tôle d'acier électrique non orientée ayant une faible perte dans le fer et une excellente qualité de surface, et son procédé de fabrication Ceased WO2020111640A1 (fr)

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KR20250093723A (ko) * 2023-12-15 2025-06-25 주식회사 포스코 무방향성 전기강판 및 그 제조방법
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WO2021258578A1 (fr) * 2020-06-23 2021-12-30 中冶赛迪工程技术股份有限公司 Procédé de production de bande mince utilisant une coulée continue et un laminage
EP4265749A4 (fr) * 2020-12-21 2025-07-30 Posco Co Ltd Feuille d'acier électrique non orientée et son procédé de fabrication
EP4407051A4 (fr) * 2021-11-25 2025-08-27 Jfe Steel Corp Procédé de production de tôle d'acier laminée à chaud pour tôle d'acier électromagnétique non orientée et procédé de production de tôle d'acier électromagnétique non orientée
EP4455347A4 (fr) * 2021-12-21 2025-11-12 Posco Co Ltd Feuille d'acier électrique non orientée et son procédé de fabrication
CN119187486A (zh) * 2024-05-27 2024-12-27 吉林建龙钢铁有限责任公司 一种控制高硅电工钢边裂的方法

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