EP2520681A2 - Nichtkornorientiertes elektrisches stahlblech mit hervorragenden magnetismuseigenschaften und herstellungsverfahren dafür - Google Patents

Nichtkornorientiertes elektrisches stahlblech mit hervorragenden magnetismuseigenschaften und herstellungsverfahren dafür Download PDF

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EP2520681A2
EP2520681A2 EP10841218A EP10841218A EP2520681A2 EP 2520681 A2 EP2520681 A2 EP 2520681A2 EP 10841218 A EP10841218 A EP 10841218A EP 10841218 A EP10841218 A EP 10841218A EP 2520681 A2 EP2520681 A2 EP 2520681A2
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Prior art keywords
steel sheet
oriented electrical
electrical steel
slab
condition
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EP10841218A
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English (en)
French (fr)
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EP2520681B1 (de
EP2520681A4 (de
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Jae-Hoon Kim
Jae-Kwan Kim
Yong-Soo Kim
Won-Seog Bong
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Posco Holdings Inc
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Posco Co Ltd
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Priority claimed from KR1020090131990A external-priority patent/KR101286243B1/ko
Priority claimed from KR1020090131992A external-priority patent/KR101296114B1/ko
Priority claimed from KR1020100135004A external-priority patent/KR101296117B1/ko
Priority claimed from KR1020100135003A external-priority patent/KR101296116B1/ko
Priority claimed from KR1020100135943A external-priority patent/KR101296124B1/ko
Application filed by Posco Co Ltd filed Critical Posco Co Ltd
Publication of EP2520681A2 publication Critical patent/EP2520681A2/de
Publication of EP2520681A4 publication Critical patent/EP2520681A4/de
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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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/008—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
    • C22C38/14—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
    • C22C38/60—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
    • H01F1/16—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys in the form of sheets
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations

Definitions

  • the present invention relates to the production of a non-oriented electrical steel sheet, and particularly to a non-oriented electrical steel sheet of the highest quality, wherein the components of steel are optimally designed to increase the distribution density of coarse inclusions in steel and to improve growth of grains and mobility of domain walls, so that magnetic properties are enhanced, and low hardness is ensured, thus improving productivity and punchability, and to a method of producing the same.
  • the present invention pertains to the production of a non-oriented electrical steel sheet useful as a material for iron cores of rotation devices.
  • This non-oriented electrical steel sheet is essential in terms of converting electrical energy into mechanical energy, and thus the magnetic properties thereof are regarded as very important.
  • the magnetic properties mainly include core loss and magnetic flux density. Because the core loss is energy that disappears in the form of heat in the course of converting energy, it is good for it to be as low as possible.
  • the magnetic flux density is a power source of a rotator. The higher the magnetic flux density, the more favorable the energy efficiency.
  • a non-oriented electrical steel sheet is composed mainly of Si in order to reduce core loss.
  • Si the magnetic flux density decreases. If the amount of Si is excessively increased, processability is decreased making it difficult to perform cold rolling. Furthermore, the lifetime of a mold may decrease upon punching by the customer. Hence, attempts are made to decrease the amount of Si and increase the amount of Al so as to improve magnetic properties and mechanical properties.
  • the magnetic properties of non-oriented electrical steel sheet of the highest quality are not obtained, and such sheets have not yet been actually produced because of difficulties in mass producing them.
  • impurities including C, S, N, Ti and so on such as fine inclusions present in steel are controlled to be minimal and thus the growth of grains needs to be increased.
  • the control of impurities to the minimum is not easy in a typical production process of electrical steel sheets, and the cost of a steel making process may undesirably increase.
  • the impurities which were not removed in the steel making process are present in the form of nitrides or sulfides in a slab upon continuous casting.
  • inclusions such as nitrides or sulfides may be re-dissolved and then finely precipitated again upon termination of hot rolling.
  • the inclusions that are precipitated in typical non-oriented electrical steel sheets include MnS and AlN, which are observed to have a small average size of about 50 nm, and such fine inclusions may hinder the growth of grains upon annealing thus increasing hysteresis loss and obstructing the movement of domain walls upon magnetization, undesirably lowering permeability.
  • impurities are appropriately controlled from the steel making process so that such fine inclusions are not present, and the residual inclusions should be prevented from being more finely precipitated via redissolution upon hot rolling.
  • an object of the present invention is to provide a non-oriented electrical steel sheet of the highest quality, wherein the proportions of Al, Si and Mn which are alloy elements of steel and N and S which are impurity elements of steel are optimally controlled so that the distribution density of coarse inclusions in steel is increased and the formation of fine inclusions is decreased, thus enhancing the growth of grains and the mobility of domain walls to thereby manifest excellent magnetic properties, and also superior productivity and punchability because of low hardness.
  • an aspect of the present invention provides a non-oriented electrical steel sheet having superior magnetic properties, comprising 0.7 ⁇ 3.0% of Al, 0.2 ⁇ 3.5% of Si, 0.2 ⁇ 2.0% of Mn, 0.001 ⁇ 0.004% of N, 0.0005 ⁇ 0.004% of S, and a balance of Fe and other inevitable impurities by wt%, and satisfying at least one of Conditions (1), (2) and (3) below: Condition (1): 0.7 ⁇ [Al] ⁇ 2.7, 0.2 ⁇ [Si] ⁇ 1.0, 0.2 ⁇ [Mn] ⁇ 1.7, ⁇ [Al]+[Mn] ⁇ 2.0, 0.002 ⁇ [N]+[S] ⁇ 0.006, 230 ⁇ ([Al]+[Mn])/([N]+[S]) ⁇ 1,000; Condition (2): 1.0 ⁇ [Al] ⁇ 3.0, 0.5 ⁇ [Si] ⁇ 2.5, 0.5 ⁇ [Mn] ⁇ 2.0, ⁇ [Al]+[Mn] ⁇ 3.5, 0.002 ⁇ [N]
  • the amounts of Al, Si and Mn may satisfy Relations (1) and (2) below, and a cross-sectional Vickers hardness (Hv1) may be 140 or less.
  • Hv1 cross-sectional Vickers hardness
  • the amounts of Al, Si and Mn may satisfy Relation (2) and the following Relations (3) and (4), and a cross-sectional Vickers hardness (Hv1) may be 190 or less.
  • Hv1 cross-sectional Vickers hardness
  • the non-oriented electrical steel sheet which satisfies at least one of Conditions (1) to (3) may have inclusions comprising nitrides and sulfides alone or combinations thereof formed in the steel sheet, and the distribution density of the inclusions having an average size of 300 nm or more may be equal to or greater than 0.02 number/mm 2 .
  • the non-oriented electrical steel sheet may further comprise 0.2% or less of P.
  • the non-oriented electrical steel sheet may further comprise at least one of 0.005 ⁇ 0.2% of Sn and 0.005 ⁇ 0.1% of Sb.
  • Another aspect of the present invention provides a method of producing the non-oriented electrical steel sheet having superior magnetic properties, comprising subjecting a slab comprising 0.7 ⁇ 3.0% of Al, 0.2 ⁇ 3.5% of Si, 0.2 ⁇ 2.0% of Mn, 0.001 ⁇ 0.004% of N, 0.0005 ⁇ 0.004% of S, and a balance of Fe and other inevitable impurities by wt% and satisfying at least one of Conditions (1), (2) and (3) to heating, hot rolling, cold rolling, and final annealing at 750 ⁇ 1100°C.
  • inclusions comprising nitrides and sulfides alone or combinations thereof may be formed in the steel sheet subjected to final annealing, and the distribution density of the inclusions having an average size of 300 nm or more may be equal to or greater than 0.02 number/mm 2 .
  • the slab may be prepared by adding 0.3 ⁇ 0.5% of Al to perform deoxidation, adding remaining alloy elements, and maintaining a temperature at 1,500 ⁇ 1,600°C.
  • a further aspect of the present invention provides a non-oriented electrical steel sheet slab, comprising 0.7 ⁇ 3.0% of Al, 0.2 ⁇ 3.5% of Si, 0.2 ⁇ 2.0% of Mn, 0.001 ⁇ 0.004% of N, 0.0005 ⁇ 0.004% of S, and a balance of Fe and other inevitable impurities by wt%, and satisfying at least one of Conditions (1), (2) and (3).
  • the non-oriented electrical steel sheet slab which satisfies at least one of Conditions (1), (2) and (3), may further comprise 0.2% or less of P.
  • the non-oriented electrical steel sheet slab may further comprise at least one of 0.005 ⁇ 0.2% of Sn and 0.005 ⁇ 0.1% of Sb.
  • Still a further aspect of the present invention provides a method of producing the non-oriented electrical steel sheet slab, comprising adding 0.3 ⁇ 0.5% of Al to molten steel to perform deoxidation, adding a remainder of Al and Si and Mn, and maintaining the temperature of the molten steel at 1,500 ⁇ 1,600°C, thus obtaining the slab comprising 0.7 ⁇ 3.0% of Al, 0.2 ⁇ 3.5% of Si, 0.2 ⁇ 2.0% of Mn, 0.001 ⁇ 0.004% of N, 0.0005 ⁇ 0.004% of S, and a balance of Fe and other inevitable impurities by wt%, and satisfying at least one of Conditions (1), (2) and (3).
  • the proportions of alloy elements such as Al, Si and Mn and of impurity elements such as N and S can be appropriately controlled so as to increase the distribution density of coarse inclusions, thus enhancing the growth of grains and the mobility of domain walls.
  • a non-oriented electrical steel sheet of the highest quality having excellent magnetic properties and very low hardness can be stably produced. Also customer workability and productivity are superior, and the unit cost of production of products can be decreased, thus reducing the cost.
  • the present inventors have examined the effects of alloy elements and impurity elements in steel and of the relation between respective elements on forming the inclusions and also the effects thereof on magnetic properties and processability, resulted in the finding that among alloy elements of steel, the amounts of Al, Si and Mn and the amounts of impurity elements such as N and S may be appropriately adjusted and Al/Si and Al/Mn, Al+Si+Mn/2, Al+Mn, N+S and (Al+Mn)/(N+S) may be optimally controlled so that the hardness of a steel sheet is decreased and the distribution density of coarse composite inclusions having an average size of 300 nm or more in the steel sheet is increased, thereby drastically enhancing magnetic properties and improving productivity and punchability, which culminates in the present invention.
  • the present invention is directed to a non-oriented electrical steel sheet of the highest quality, comprising 0.7 ⁇ 3.0% of Al, 0.2 ⁇ 3.5% of Si, 0.2 ⁇ 2.0% of Mn, 0.001 ⁇ 0.004% of N, 0.0005 ⁇ 0.004% of S, and a balance of Fe and other inevitable impurities by wt%, wherein Al, Si, Mn, N and S are contained so as to satisfy at least one of the following Conditions (1), (2) and (3), and thus the distribution density of 300 nm or more sized coarse inclusions having combinations of nitrides and sulfides is increased to be equal to or greater than 0.02 number/mm 2 , resulting in high magnetic properties and low hardness.
  • [Al], [Si], [Mn], [N] and [S] indicate the amounts (wt%) of Al, Si, Mn, N and S, respectively.
  • the present invention is directed to the production of the non-oriented electrical steel sheet which is superior in both magnetic properties and processability, by adding 0.3 ⁇ 0.5% of Al to molten steel to perform deoxidation in a steel making process, adding remaining alloy elements, and then maintaining the temperature of the molten steel at 1,500 ⁇ 1,600°C thus manufacturing a slab having the composition that satisfies at least one of Conditions (1), (2) and (3), followed by heating the slab to 1,100 ⁇ 1,250°C and then performing hot rolling wherein finish hot rolling is conducted at 800°C or higher, carrying out cold rolling, and then finally annealing the cold rolled sheet at 750 ⁇ 1,100°C.
  • the alloy elements of steel namely, Al, Si and Mn are described below. These alloy elements are added to reduce the core loss of an electrical steel sheet. As the amounts thereof increase, the magnetic flux density may decrease and the processability of a material may deteriorate. Hence, the amounts of such alloy components are appropriately designed to improve not only the core loss but also the magnetic flux density, and also hardness needs to be maintained to an appropriate level or less.
  • Al and Mn combine with N and S which are impurity elements to form inclusions such as nitrides or sulfides.
  • inclusions greatly affect magnetic properties and thus the formation of inclusions that minimize the deterioration of magnetic properties should be increased.
  • the present inventors were the first to discover that coarse composite inclusions comprising combinations of nitrides or sulfides may be formed when the amounts of Al, Mn, Si, N and S are adapted for specific conditions, and have found the fact that the distribution density of such composite inclusions to a predetermined level or more is ensured, and thereby magnetic properties may be drastically improved despite the addition of minimum amounts of alloy elements that deteriorate processability, and thus devised the present invention.
  • Al functions to increase resistivity of a material to reduce core loss and to form a nitride, and is added in an amount of 0.7 ⁇ 3.0% so as to form a coarse nitride. If the amount of Al is less than 0.7%, inclusions may not be sufficiently grown. In contrast, if the amount thereof exceeds 3.0%, processability may deteriorate and all processes including steel making, continuous casting and so on may be problematic, making it impossible to produce a steel sheet in the typical manner.
  • Si functions to increase resistivity of a material to reduce core loss. If the amount of Si is less than 0.2%, it is difficult to expect reduction effects of core loss. In contrast, if the amount thereof exceeds 3.5%, the hardness of a material may increase, undesirably deteriorating productivity and punchability.
  • Mn functions to increase resistivity of a material to reduce core loss and to form a sulfide, and is added in an amount of 0.2% or more. If the amount thereof exceeds 2.0%, the formation of [111] texture that is unfavorable for magnetic properties may be facilitated. Hence, the amount of Mn is preferably limited to 0.5 ⁇ 2.0%.
  • Sn is preferentially segregated on the surface and the grain boundaries and may reduce accumulated strain energy upon hot rolling and cold rolling, so that the strength in ⁇ 100 ⁇ orientation that is favorable for magnetic properties may increase whereas the strength in ⁇ 111 ⁇ orientation that is unfavorable for magnetic properties may decrease, thus achieving improvements in texture.
  • Sn is added in the range of 0.2% or less.
  • Sn is preferentially formed on the surface during welding to thus suppress surface oxidation and enhance the weld properties thereby increasing productivity of continuous lines.
  • the formation of Al-based oxides and nitrides on the surface or the layer under the surface may be suppressed during heat treatment, thus enhancing magnetic properties. Upon punching by a customer, the increase in hardness of the layer under the surface due to nitrides may be inhibited to improve punchability.
  • Sn is preferably added in the range of 0.005% or more.
  • the amount of Sn exceeds 0.2%, improvements in magnetic properties based on such an additional use thereof are insignificant, and fine inclusions and deposits may be formed in steel, rather than preferential segregation on the surface and the grain boundaries, negatively affecting the magnetic properties.
  • cold rollability and punchability may decrease and the Erichsen number that represents the weld properties is 5 mm or less, making it impossible to perform welding of the same species.
  • a low-graded material having the sum of Si and Al of less than 2 should be undesirably used as a connection material for continuous line working.
  • the amount of Sn is preferably limited to 0.005 ⁇ 0.2%.
  • Sb is preferentially segregated on the surface and the grain boundaries and may reduce accumulated strain energy upon hot rolling and cold rolling, so that the strength in ⁇ 100 ⁇ orientation that is favorable for magnetic properties may increase and the strength in ⁇ 111 ⁇ orientation that is unfavorable for magnetic properties may decrease, thus attaining improvements in texture.
  • Sb is added in the range of 0.1% or less.
  • Sb is preferentially formed on the surface during welding to thus suppress surface oxidation and enhance weld properties thereby increasing productivity of continuous lines.
  • the formation of Al-based oxides and nitrides on the surface or the layer under the surface may be suppressed during heat treatment, thus improving magnetic properties. Upon punching by the customer, the increase in hardness of the layer under the surface due to nitrides may be inhibited to improve punchability.
  • Sb is preferably added in the range of 0.005% or more.
  • the amount of Sb exceeds 0.1%, improvements in magnetic properties based on such an additional use thereof are insignificant, and fine inclusions and deposits may be formed in steel, rather than preferential segregation on the surface and the grain boundaries, undesirably aggravating the magnetic properties.
  • cold rollability and punchability may decrease and the Erichsen number that represents the weld properties is 5mm or less, making it impossible to perform welding of the same species.
  • a low-graded material having the sum of Si and Al of less than 2 should be undesirably used as a connection material for continuous line working.
  • the amount of Sb is preferably limited to 0.005 ⁇ 0.1%.
  • N is an impurity element, and may form a fine nitride during the production process to suppress the growth of grains undesirably deteriorating core loss. Although the formation of nitrides is suppressed, an additional high cost and long process time are required, and thus monetary benefits are negatively affected. Therefore, it is preferred that an element having high affinity for the impurity element N is positively utilized to coarsely grow inclusions so as to reduce an influence on the growth of grains. To coarsely grow the inclusions in this way, the amount of N is essentially controlled in the range of 0.001 ⁇ 0.004%. If the amount of N exceeds 0.004%, the inclusions may not be coarsely formed undesirably increasing core loss. More preferably, the amount of N is limited to 0.003% or less.
  • S is an impurity element, and may form a fine sulfide during the production process to thus suppress the growth of grains and deteriorate core loss. Although the formation of sulfides is suppressed, an additional high cost and long process time are required, and thus monetary benefits are negatively affected. Thus, it is preferred that an element having high affinity for the impurity element S is positively utilized to coarsely grow inclusions so as to reduce the influence on the growth of grains. To coarsely grow the inclusions in this way, the amount of S is essentially controlled in the range of 0.0005 ⁇ 0.004%. If the amount of S exceeds 0.004%, the inclusions may not be coarsely formed undesirably increasing core loss. More preferably, the amount of S is limited to 0.003% or less.
  • C may cause magnetic aging, and the amount thereof is thus limited in the range of 0.004% or less, and more preferably 0.003% or less.
  • Ti may promote the growth of [111] texture that is unfavorable for a non-oriented electrical steel sheet, and the amount thereof is thus limited in the range of 0.004% or less, and preferably 0.002% or less.
  • the sum ([Al]+[Mn]) of Al and Mn by wt% is limited to 2.0% or less. If the sum of Al and Mn exceeds 2.0% in steel comprising 0.7 ⁇ 2.7% of Al, 0.2 ⁇ 1.0% of Si and 0.2 ⁇ 1.7% of Mn, the fraction of [111] texture that is unfavorable for magnetic properties may increase, undesirably deteriorating the magnetic properties. In the case of the non-oriented electrical steel sheet that satisfies Condition (1), if the sum of Al and Mn is less than 0.9%, nitrides, sulfides or composite inclusions of these two are not coarsely formed, thus deteriorating the magnetic properties.
  • Al is contained in an amount of 0.7% or more and Mn is contained in an amount of 0.2% or more, so that the sum of Al and Mn is 0.9% or more, thereby preventing the deterioration of the magnetic properties.
  • the sum ([Al]+[Mn]) of Al and Mn by wt% is limited to 3.5% or less. If the sum of Al and Mn exceeds 3.5% in steel comprising 1.0 ⁇ 3.0% of Al, 0.5 ⁇ 3.5% of Si and 0.5 ⁇ 2.0% of Mn, the fraction of [111] texture that is unfavorable for magnetic properties may increase undesirably deteriorating the magnetic properties. In the non-oriented electrical steel sheet that satisfies Condition (2) or (3), if the sum of Al and Mn is less than 1.5%, nitrides, sulfides or composite inclusions of these two are not coarsely formed, thus deteriorating the magnetic properties.
  • Al is contained in an amount of 1.0% or more and Mn is contained in an amount of 0.5% or more, so that the sum of Al and Mn is 1.5% or more, thereby preventing the deterioration of the magnetic properties.
  • the sum ([N]+[S]) of N and S is limited to 0.002 ⁇ 0.006%. This is because inclusions are coarsely formed in the above range. If the sum of N and S exceeds 0.006%, the fraction of fine inclusions may be increased, undesirably deteriorating the magnetic properties.
  • the ratio of the sum ([Al]+[Mn]) of Al and Mn by wt% to the sum ([N]+[S]) of N and S by wt% is regarded as important.
  • FIG. 1 shows composite inclusions which are present in the non-oriented electrical steel sheet according to the present invention.
  • inclusions are grown several times or more compared to when using typical materials, thus increasing the formation of coarse composite inclusions having an average size of 300 nm or more. Accordingly, the formation of fine inclusions having an average size of about 50 nm may decrease, thereby improving magnetic properties.
  • the present inventors have appreciated that, when the distribution density of coarse composite inclusions as shown in FIG. 1 is equal to or greater than 0.02 number/mm 2 , the magnetic properties of the non-oriented electrical steel sheet may be remarkably improved.
  • Al-based oxides and nitrides may be formed due to deoxidation, and in the composition that additionally includes the alloy elements such as Al and Mn and satisfies the amounts of Al, Mn, Si, N and S as designed in the present invention upon bubbling, Al-based oxides and nitrides are grown and Mn-based sulfides may also be precipitated thereon.
  • FIG. 2 is a graph showing whether the distribution density of coarse composite inclusions having an average size of 300 nm or more is equal to or greater than 0.02 number/mm 2 in the non-oriented electrical steel sheet containing 0.5 ⁇ 2.5% of Si wherein [N]+[S] is represented on a horizontal axis and [Al]+[Mn] is represented on a vertical axis.
  • FIG. 3 is a graph showing whether the distribution density of coarse composite inclusions having an average size of 300 nm or more is equal to or greater than 0.02 number/mm 2 in the non-oriented electrical steel sheet containing 0.2 ⁇ 1.0% of Si wherein [N]+[S] is represented on a horizontal axis and [Al]+[Mn] is represented on a vertical axis.
  • FIG. 4 is a graph showing whether the distribution density of coarse composite inclusions having an average size of 300 nm or more is equal to or greater than 0.02 number/mm 2 in the non-oriented electrical steel sheet containing 2.3 ⁇ 3.5% of Si wherein [N]+[S] is represented on a horizontal axis and [Al]+[Mn] is represented on a vertical axis.
  • the coarse inclusions are mainly observed to be combinations of nitrides and sulfides having an average size of 300 nm or more
  • the examples thereof may include combinations of a plurality of nitrides or combinations of a plurality of sulfides having an average size of 300 nm or more, and those having nitrides or sulfides alone having a size of 300 nm or more.
  • the average size of the inclusions is determined by measuring the longest length and the shortest length of the inclusions when viewed in the cross-section of the steel sheet and averaging the measured values.
  • the amount ratio of Al to Si ([Al]/[Si]) is limited to 0.6 ⁇ 4.0.
  • the grains may effectively grow and the hardness of a material may decrease thus improving productivity and punchability.
  • the ratio of [Al]/[Si] is less than 0.6, inclusions do not greatly grow undesirably decreasing the growth of grains and deteriorating magnetic properties.
  • the amount of Si may increase, undesirably enhancing hardness. If the ratio of [Al]/[Si] exceeds 4.0, texture of a material may become poor undesirably deteriorating the magnetic flux density.
  • the ratio of Al to Mn ([Al]/[Mn]) is preferably limited to 1 ⁇ 8.
  • the ratio of Al to Mn is 1 ⁇ 8
  • the inclusions may effectively grow thus exhibiting superior core loss properties.
  • the growth of inclusions may decrease and the fraction of texture that is favorable for magnetic properties may decrease.
  • the limited ratio of alloy components related to resistivity is described below. Recently, as the demand for environmentally friendly automobiles drastically increases, there is a high need for non-oriented electrical steel sheets usable for highly rotatable motors.
  • the motors used in the environmentally friendly automobiles should greatly increase their number of rotations. When the number of rotations of the motor is increased, the fraction of eddy current loss in the inner core loss may be drastically increased. To reduce such eddy current loss, resistivity should increase.
  • [Al]+[Si]+[Mn]/2 is limited to 3.0 or more so as to ensure resistivity of 47 or more.
  • the resistivity exceeds 87 may increase the amounts of alloy elements and may deteriorate processability. Because the production of steel sheets is impossible via typical cold rolling, the resistivity should be set to 87 or less.
  • [Al]+[Si]+[Mn]/2 is limited to 1.7 or more so as to ensure the resistivity of 32 or more. Furthermore, in the present invention that satisfies Condition (2), [Al]+[Si]+[Mn]/2 is controlled to 5.5% or less so that resistivity (intrinsic resistance) is maintained to 75 or less and Vickers hardness (Hv1) is 190 or less.
  • resistivity intrinsic resistance
  • the resistivity should be controlled to at least 25.
  • the method of producing the non-oriented electrical steel sheet preferably includes adding 0.3 ⁇ 0.5% of Al, corresponding to a portion of the total amount of added Al, in the steel making process, so that deoxidation of steel sufficiently occurs, and adding the remaining alloy elements. Subsequently, the temperature of molten steel is maintained at 1,500 ⁇ 1,600°C so that inclusions in steel are sufficiently grown, after which the resultant steel is solidified in a continuous casting process thus manufacturing a slab.
  • the slab is placed in a furnace so that it is re-heated to 1,100 ⁇ 1,250°C. If the slab is heated to a temperature exceeding 1,250°C, deposits that negatively affect the magnetic properties may be re-dissolved, hot rolled and then finely deposited, and thus the slab is heated to 1,250°C or less.
  • the heated slab is hot rolled.
  • finish hot rolling is preferably carried out at 800°C or more.
  • the hot rolled sheet is annealed at 850 ⁇ 1,100°C. If the annealing temperature of the hot rolled sheet is lower than 850°C, texture does not grow or finally grows, and thus the extent of increasing the magnetic flux density is low. In contrast, if the annealing temperature of the hot rolled sheet is higher than 1,100°C, magnetic properties may deteriorate instead, and rolling workability may decrease due to plate transformation. Hence, the temperature range thereof is limited to 850 ⁇ 1,100°C. More preferably the annealing temperature of the hot rolled sheet is 950 ⁇ 1,100°C. The annealing of the hot rolled sheet may be carried out to increase the grain orientation favorable for magnetic properties, as necessary, but may be omitted.
  • the hot rolled sheet which was annealed or not is pickled, and cold rolled to a reduction of 70 ⁇ 95% to obtain a predetermined sheet thickness.
  • one cold rolling makes it possible to form a thin sheet having a thickness of about 0.15 mm.
  • two cold rolling operations including intermediate annealing may be conducted, as necessary, or two annealing operations may be applied.
  • final annealing is preferably conducted at 750 ⁇ 1,100°C.
  • the finally annealed steel sheet is subjected to insulation coating treatment using typical methods and is then discharged to customers.
  • insulation coating the application of a typical coating material is possible, and either Cr-type or Cr-free type may be used without limitation.
  • Vacuum melting was performed in a laboratory, thus preparing steel ingots having the components shown in Table 1 below.
  • the amount of each of impurity elements C, S, N, Ti was controlled to 0.002%, and 0.3 ⁇ 0.5% of Al was added to molten steel to facilitate the formation of inclusions, after which the remainder of Al, and Si and Mn were added thus making steel ingots.
  • Each of the ingots was heated to 1,150°C, and finish hot rolled at 850°C thus manufacturing a hot rolled sheet having a thickness of 2.0 mm.
  • the hot rolled sheet was annealed at 1,050°C for 4 min and then pickled. Subsequently, cold rolling was conducted so that the thickness of the sheet was 0.35 mm, followed by carrying out final annealing at 1,050°C for 38 sec.
  • the size and distribution density of inclusions of respective sheets, the core loss, the magnetic flux density and hardness were measured. The results are shown in Table 2 below.
  • a sample for use in observing the inclusions was manufactured using a replica method that is typical in the steel industry, and a transmission electron microscope was used therefor. As such, the acceleration voltage of 200 kV was applied.
  • steels A3, A5, A6, A9, A10, A12 and A14 were inventive examples that satisfy Condition (2), wherein coarse composite inclusions having a size of 300 nm or more were observed, and the distribution density thereof was greater than 0.02(1/mm 2 ) thus exhibiting superior magnetic properties.
  • the Vickers hardness (Hv1) was as low as 190 or less thus obtaining superior productivity and customer punchability.
  • the ratio of Al/Si and Al+Mn did not satisfy Condition (2), and thus inclusions having a size of 300 nm or more were not observed, and core loss and magnetic flux density were deteriorated.
  • the ratio of Al/Si did not satisfy Condition (2), and thus inclusions having a size of 300 nm or more were not observed, and core loss and magnetic flux density were deteriorated.
  • the ratio of Al/Si and the ratio of Al/Mn did not satisfy Condition (2), and thus inclusions having a size of 300 nm or more were not observed, and core loss and magnetic flux density were deteriorated.
  • Vacuum melting was performed in a laboratory, thus preparing steel ingots having the components shown in Table 3 below. As such, the components of steel were controlled while variously adjusting the amounts of impurity elements N and S, and 0.3 ⁇ 0.5% of Al was added to molten steel to facilitate the formation of inclusions, after which the remainder of Al, and Si and Mn were added thus making steel ingots.
  • Each of the ingots was heated to 1,150°C, and finish hot rolled at 850°C thus manufacturing a hot rolled sheet having a thickness of 2.0 mm. The hot rolled sheet was annealed at 1,050°C for 4 min and then pickled. Subsequently, cold rolling was conducted so that the thickness of the sheet was 0.35 mm, followed by carrying out final annealing at 1,050°C for 38 sec.
  • the size and distribution density of inclusions of respective sheets, the core loss, the magnetic flux density and hardness were measured. The results are shown in Table 4 below.
  • a sample for observing the inclusions was manufactured using a replica method that is typical in the steel industry, and a transmission electron microscope was used therefor. As such, the acceleration voltage of 200 kV was applied.
  • steels B1, B4, B5, B7, B9, B10, B13 and B14 were inventive examples that satisfy Condition (2), wherein coarse composite inclusions having a size of 300 nm or more were observed, and the distribution density thereof was greater than 0.02(1/mm 2 ) thus manifesting excellent magnetic properties.
  • the hardness was low thus obtaining superior productivity and customer punchability.
  • N+S fell outside Condition (2) N+S fell outside Condition (2), and thus inclusions having a size of 300 nm or more were not observed, and core loss and magnetic flux density were deteriorated.
  • Al+Mn fell outside Condition (2) and in steels B2 and B12, the ratio of (Al+Mn)/(N+S) fell outside Condition (2), and thus inclusions having a size of 300 nm or more were not observed, and core loss and magnetic flux density were deteriorated.
  • Vacuum melting was performed in a laboratory, thus preparing steel ingots having the components shown in Table 5 below. As such, 0.3 ⁇ 0.5% of Al was added to molten steel to facilitate the formation of inclusions, after which the remainder of Al, and Si, Mn and P were added thus making steel ingots. Each of the ingots was heated to 1,150°C, and finish hot rolled at 850°C thus manufacturing a hot rolled sheet having a thickness of 2.0 mm. The hot rolled sheet was annealed at 1,050°C for 4 min and then pickled.
  • steels C2 ⁇ C7 were inventive examples that satisfy Condition (2), wherein the magnetic flux density was high and the core loss was low. This is considered to be because the composition according to the present invention had coarsely grown inclusions and the distribution density of coarse composite inclusions was greater than 0.02(1/mm 2 ), and also the texture was stable.
  • the radio-frequency core loss (W10/400) is surely correlated with the thickness of steel sheet. Specifically, as the thickness of the steel sheet decreases, the properties thereof may be improved. Compared to the steel sheet having a thickness of 0.35 mm, the core loss of the steel sheet having a thickness of 0.15 mm was improved by about 50%. In steel C1, Al+Mn and Al/Si did not satisfy Condition (2), and thus core loss (W10/400) and magnetic flux density (B50) were deteriorated.
  • Vacuum melting was performed in a laboratory, thus preparing steel ingots having the components shown in Table 7 below.
  • 0.3 ⁇ 0.5% of Al was added to molten steel to facilitate the formation of inclusions, after which the remainder of Al, and Si, Mn and P were added thus making steel ingots.
  • Each of the ingots was heated to 1,150°C, and finish hot rolled at 850°C thus manufacturing a hot rolled sheet having a thickness of 2.0 mm.
  • the hot rolled sheet was annealed at 1,050°C for 4 min and then pickled. Subsequently, cold rolling was conducted so that the thickness of the sheet was 0.35 mm, followed by carrying out final annealing at 1,050°C for 38 sec.
  • the size and distribution density of inclusions of respective sheets, the core loss, the magnetic flux density, the Erichsen number and hardness were measured. The results are shown in Table 8 below.
  • a sample for observing the inclusions was manufactured using a replica method that is typical in the steel industry, and a transmission electron microscope was used therefor. As such, the acceleration voltage of 200 kV was applied.
  • the height until the sheet broken was determined, which is referred to as the Erichsen number.
  • steels D2 ⁇ 6, D8 ⁇ 12, D14, D15 and D17 were inventive examples which satisfy Condition (2) and in which 0.005 ⁇ 0.2% of Sn or 0.005 ⁇ 0.1% of Sb is added, and thus, the distribution density of coarse inclusions having a size of 300 nm or more was greater than 0.02(1/mm 2 ), and upon final annealing, the oxide layer and the nitride layer of the surface were reduced thus improving core loss and magnetic flux density. Also, the Erichsen number was high and the Vickers hardness (Hv1) was low, thus exhibiting superior weldability, productivity and customer punchability.
  • Hv1 Vickers hardness
  • Vacuum melting was performed in a laboratory, thus preparing steel ingots having the components shown in Table 9 below.
  • 0.3 ⁇ 0.5% of Al was added to molten steel to facilitate the formation of inclusions, after which the remainder of Al, and Si and Mn were added thus making steel ingots.
  • Each of the ingots was heated to 1,150°C, and finish hot rolled at 850°C thus manufacturing a hot rolled sheet having a thickness of 2.3 mm.
  • the hot rolled sheet was annealed at 1,050°C for 4 min and then pickled. Subsequently, cold rolling was conducted so that the thickness of the sheet was 0.50 mm, followed by carrying out final annealing at 900°C for 30 sec.
  • the size and distribution density of inclusions of respective sheets, the core loss, the magnetic flux density and hardness were measured. The results are shown in Table 10 below.
  • a sample for observing the inclusions was manufactured using a replica method that is typical in the steel industry, and a transmission electron microscope was used therefor. As such, the acceleration voltage of 200 kV was applied.
  • steels E1 ⁇ E3, E6, E10, E12, E13, E16, E20 and E21 were inventive examples that satisfy Condition (1), wherein the coarse inclusions having a size of 300 nm or more were observed, and the distribution density thereof was greater than 0.02(1/mm 2 ) thus exhibiting superior magnetic properties, and the Vickers hardness (Hv1) was 140 or less, resulting in good productivity and customer punchability.
  • Vacuum melting was performed in a laboratory, thus preparing steel ingots having the components shown in Table 11 below. As such, 0.3 ⁇ 0.5% of Al was added to molten steel to facilitate the formation of inclusions, after which the remainder of Al, and Si and Mn were added thus making steel ingots.
  • Each of the ingots was heated to 1,150°C, and finish hot rolled at 850°C thus manufacturing a hot rolled sheet having a thickness of 2.3 mm.
  • the hot rolled sheet was annealed at 1,050°C for 4 min and then pickled. Subsequently, cold rolling was conducted so that the thickness of the sheet was 0.50 mm, followed by carrying out final annealing at 900°C for 30 sec.
  • the size and distribution density of inclusions of respective sheets, the core loss, the magnetic flux density and hardness were measured. The results are shown in Table 12 below.
  • a sample for observing the inclusions was manufactured using a replica method that is typical in the steel industry, and a transmission electron microscope was used therefor. As such, the acceleration voltage of 200 kV was applied.
  • steels F1, F3, F4, F6, F8, F9, F11 and F12 were inventive examples that satisfy Condition (1), wherein the coarse inclusions having a size of 300 nm or more were observed, and the distribution density thereof was greater than 0.02(1/mm 2 ) thus exhibiting superior magnetic properties, and hardness was low, resulting in good productivity and customer punchability.
  • Vacuum melting was performed in a laboratory, thus preparing steel ingots having the components shown in Table 13 below. As such, 0.3 ⁇ 0.5% of Al was added to molten steel to facilitate the formation of inclusions, after which the remainder of Al, and Si and Mn were added thus making steel ingots.
  • Each of the ingots was heated to 1,150°C, and finish hot rolled at 850°C thus manufacturing a hot rolled sheet having a thickness of 2.0 mm.
  • the hot rolled sheet was annealed at 1,050°C for 4 min and then pickled. Subsequently, cold rolling was conducted so that the thickness of the sheet was 0.35 mm, followed by carrying out final annealing at 1,050°C for 38 sec.
  • the size and distribution density of inclusions of respective sheets, the core loss, the magnetic flux density and hardness were measured. The results are shown in Table 14 below.
  • a sample for observing the inclusions was manufactured using a replica method that is typical in the steel industry, and a transmission electron microscope was used therefor. As such, the acceleration voltage of 200 kV was applied.
  • steels G3 ⁇ G6, G9, G10, G12, G14 and G15 were inventive examples that satisfy Condition (3), wherein the coarse inclusions having a size of 300 nm or more were observed, and the distribution density thereof was greater than 0.02(1/mm 2 ) thus exhibiting superior magnetic properties, and the Vickers hardness was as low as 225 or less.
  • Vacuum melting was performed in a laboratory, thus preparing steel ingots having the components shown in Table 15 below. As such, 0.3 ⁇ 0.5% of Al was added to molten steel to facilitate the formation of inclusions, after which the remainder of Al, and Si and Mn were added thus making steel ingots.
  • Each of the ingots was heated to 1,150°C, and finish hot rolled at 850°C thus manufacturing a hot rolled sheet having a thickness of 2.0 mm.
  • the hot rolled sheet was annealed at 1,050°C for 4 min and then pickled. Subsequently, cold rolling was conducted so that the thickness of the sheet was 0.35 mm, followed by carrying out final annealing at 1,050°C for 38 sec.
  • the size and distribution density of inclusions of respective sheets, the core loss, the magnetic flux density and hardness were measured. The results are shown in Table 16 below.
  • a sample for observing the inclusions was manufactured using a replica method that is typical in the steel industry, and a transmission electron microscope was used therefor. As such, the acceleration voltage of 200 kV was applied.
  • steels H1, H3, H4, H6, H8, H9, H11 and H12 were inventive examples that satisfy Condition (3), wherein the coarse inclusions having a size of 300 nm or more were observed, and the distribution density thereof was greater than 0.02(1/mm 2 ) thus exhibiting superior magnetic properties.

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Title
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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3239309A4 (de) * 2014-12-24 2017-12-20 Posco Nicht-orientiertes elektrisches stahlblech und verfahren zur herstellung davon
US10941457B2 (en) 2014-12-24 2021-03-09 Posco Non-oriented electrical steel sheet and method for manufacturing the same

Also Published As

Publication number Publication date
EP2520681B1 (de) 2018-10-24
EP2520681A4 (de) 2014-11-19
JP2013515170A (ja) 2013-05-02
US20120267015A1 (en) 2012-10-25
WO2011081386A3 (ko) 2011-12-01
WO2011081386A2 (ko) 2011-07-07
CN102906289A (zh) 2013-01-30
CN102906289B (zh) 2016-03-23
JP5642195B2 (ja) 2014-12-17

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