WO2019132315A1 - Tôle d'acier électrique non orientée possédant une excellente propriété de forme et procédé de fabrication s'y rapportant - Google Patents

Tôle d'acier électrique non orientée possédant une excellente propriété de forme et procédé de fabrication s'y rapportant Download PDF

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Publication number
WO2019132315A1
WO2019132315A1 PCT/KR2018/015593 KR2018015593W WO2019132315A1 WO 2019132315 A1 WO2019132315 A1 WO 2019132315A1 KR 2018015593 W KR2018015593 W KR 2018015593W WO 2019132315 A1 WO2019132315 A1 WO 2019132315A1
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WIPO (PCT)
Prior art keywords
steel sheet
rolling
thickness
hot
rolled steel
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PCT/KR2018/015593
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English (en)
Korean (ko)
Inventor
공종판
이세일
정제숙
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주식회사 포스코
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Publication of WO2019132315A1 publication Critical patent/WO2019132315A1/fr

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    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
    • C21D8/1233—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1277—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular surface treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

Definitions

  • Patent Document 1 Japanese Laid-Open Patent Publication No. 2000-129410
  • Patent Document 4 Japanese Patent Publication No. 2500033
  • FIG. 2 is another schematic diagram of a facility for a performance-rolling direct process that can be applied to the present invention.
  • Phosphorus (P) is an element capable of increasing iron specific resistance and lowering iron loss, and is an element capable of improving magnetic flux density when added as a magnetic material. It is preferable to add 0.002% or more for the above effect. However, if it exceeds 0.15%, there is a disadvantage that it is present as a segregation element which induces the fracture of the rolled plate in the ferrite grain boundary at the room temperature rolling, and weakens the bonding force between grain boundaries to a great extent. Therefore, the P content is preferably in the range of 0.002 to 0.15%, more preferably 0.004 to 0.10%, still more preferably 0.006 to 0.05%.
  • the remainder of the present invention is iron (Fe).
  • impurities which are not intended from the raw material or the surrounding environment may be inevitably incorporated, so that it can not be excluded. These impurities are not specifically mentioned in this specification, as they are known to any person skilled in the art of manufacturing.
  • the thickness variation ⁇ t CR in the width direction of the strip satisfies the following relational expression (2).
  • the following expression (2) it is possible to secure a superior appearance shape quality.
  • ⁇ t CR is the thickness deviation ( ⁇ m) in the width direction of the strip
  • S is the thickness measurement position (mm) at a distance from the edge in the strip width direction
  • t is the thickness box.
  • FIG. 1 is a schematic view of a facility for a performance-to-rolling direct process that can be applied to the present invention, and is a schematic diagram of a performance-to-rolling direct process facility applicable to the manufacture of hot rolled steel sheets for obtaining a final electrical steel sheet.
  • the steel slabs of excellent shape quality according to one embodiment of the present invention can be manufactured from the hot-rolled steel sheets produced by applying the direct rolling-to-rolling direct connection equipment as shown in Fig.
  • the performance-to-rolling direct connection facility consists largely of a continuous casting machine 100, a roughing mill 400, and a finishing mill 600.
  • the performance-to-rolling direct connection plant comprises a high-speed continuous casting machine (100) producing a thin slab (a) of a first thickness and a rolling bar (b) of a second thickness thinner than the first thickness
  • a roughing scale breaker 300 and a finishing mill scale breaker 500 are placed in front of the roughing mill 400 and before the finishing mill 600, FSB '), and it is possible to produce an electrical steel sheet having excellent surface quality in the post-process because of easy removal of the surface scale.
  • FIG. 2 is another schematic diagram of a facility for a performance-rolling direct process that can be applied to the present invention.
  • the apparatus for direct rolling-to-rolling process disclosed in FIG. 2 is substantially identical in construction to the apparatus disclosed in FIG. 1, but includes a heater 200 'for further heating a slab in front of the rough rolling mill 400, It is possible to lower the occurrence of edge defects and is advantageous in securing the surface quality. In addition, a space of at least one slab length is secured before the roughing mill, and batch rolling is possible.
  • the hot rolled steel sheet having excellent magnetic properties and shapes of the present invention can be produced in all of the performance-rolling direct connection facilities disclosed in Figs. 1 and 2.
  • the continuous casting is preferably performed at a casting speed of 3.5 to 8.0 mpm (m / min).
  • the reason why the casting speed is set to 3.5 mpm or more is that a high speed casting and a rolling process are connected and a casting speed higher than a certain level is required to secure the target rolling temperature.
  • the casting speed is less than 3.5 mpm, Al may increase the amount of pick-up in the mold flux, thereby changing the physical properties of the mold flux, resulting in reduced lubricity and casting failure.
  • it exceeds 8.0 mpm the operation success rate may be reduced due to instability of the molten steel bath surface. Therefore, the casting speed is preferably in the range of 3.5 to 8.0 mpm, more preferably 4.0 to 7.5 mpm , And more preferably in the range of 4.5 to 6.5 mpm.
  • the thickness of the bar is preferably 10 to 30 mm. If the thickness of the bar exceeds 30 mm, the rolling load due to the increase in the reduction rate during the finish rolling may increase sharply and the thickness variation in the width direction in the strip may be worsened. If the thickness is less than 10 mm, the resistance to rolling deformation becomes large, And it is difficult to secure the temperature during finish rolling.
  • the thickness of the bar is preferably in the range of 10 to 30 mm, more preferably in the range of 12 to 28 mm, and even more preferably in the range of 14 to 26 mm.
  • the bar is then heated.
  • the heating temperature of the bar is preferably 1000 to 1200 ° C.
  • the reason for controlling the heating temperature of the bar is to stably produce the hot rolled steel sheet and to secure the surface quality. If the temperature is less than 1000 ° C, the finish rolling rolling temperature is lowered and the rolling load is rapidly increased, Plate breakage may occur. If the temperature exceeds 1200 ° C, the scale may be excessively generated and the surface quality may be deteriorated.
  • the heating temperature of the bar is preferably in the range of 1000 to 1200 ° C, more preferably in the range of 1020 to 1180 ° C, and even more preferably in the range of 1040 to 1160 ° C.
  • the average passing speed during the final rolling at the time of the hot rolling is 250 to 750 mpm.
  • the passing speed in the last rolling mill can be directly connected to the casting speed and the thickness of the hot rolled product. If the rolling speed in the last rolling mill is more than 750 mPm, it is possible to cause an accident such as a plate rupture, and since a uniform temperature is not secured due to difficulty in isothermal constant rolling, a material and thickness variation may occur . On the other hand, in the case of less than 250 mpm, the final rolling speed is too slow, which may cause problems in mass balance and heat balance, and it may be difficult to carry out continuous continuous rolling.
  • the average passing speed during the final rolling in the hot rolling is preferably in the range of 250 to 750 mpm, more preferably 270 to 730 mpm, and even more preferably 290 to 710 mpm.
  • lubricating oil is applied to the surface of the bar to decrease the friction coefficient between the bar and the rolling roll, thereby reducing the rolling load, thereby reducing the thickness deviation.
  • the lubricating oil is applied in the first rolling mill having a very high rolling load during the hot finishing rolling. It is preferable that the lubricating oil is applied to the surface of the bar at a rate of 5 to 40 L / min per 1 m2. When the application of the lubricating oil is less than 5 L / min, the effect described above is insignificant. If the lubricating oil is more than 40 L / min, the manufacturing cost may be increased due to excessive use of the lubricant.
  • the lubricating oil is preferably applied to the surface of the bar at a rate of 5 to 40 L / min per 1 m2 of the surface of the bar, more preferably at 7 to 38 L / min per 1 m2 of the surface of the bar , And more preferably 9 to 36 L / min per 1 m < 2 > on the surface of the bar.
  • the hot-rolled steel sheet preferably has a thickness of 1.8 mm or less. As the thickness of the steel sheet is reduced, the recrystallized texture increases, uniform structure after annealing can be secured, the crystal orientation of the? -Fiber can be reduced by decreasing the cold rolling reduction and the magnetic property can be improved, Can also be reduced. However, if it exceeds 1.8 mm, the above effect may not be sufficient. Therefore, the thickness of the hot-rolled steel sheet is preferably 1.8 mm or less, more preferably 1.6 mm or less.
  • JIS 5 specimens were used for the yield strength and specimens were taken from the vertical direction (C direction) and horizontal direction (L direction) of the rolled steel sheet, and the results were averaged. The final product was measured in the horizontal direction The results are shown in Table 3 below. ≪ tb > < TABLE >
  • Comparative Example 1 does not satisfy the amount of lubricating oil applied in the first rolling mill at the finish rolling proposed in the present invention, so that the rolling load is high and it can be understood that the target thickness deviation in the width direction is not satisfied.
  • FIG. 5 is a graph examining the correlation between the S / t and the thermal gradient widthwise thickness deviation for Inventive Examples 1 to 19, Comparative Examples 1 to 8, and Conventional Example 1.
  • FIG. 5 the S / t and thickness-direction thickness deviations of inventive steels (Inventive Examples 1 to 19) have the relationship as shown in Equation 1, and the comparative steels (Comparative Examples 2 to 5) And Conventional Example 1 has the same relationship as Equation 3.
  • Fig. 6 is a graph examining the correlation between the S / t and the thickness deviation in the width direction of the final product for Inventive Examples 1 to 19, Comparative Examples 1 to 8 and Conventional Example 1. Fig. From these results, it can be understood that the S / t and the lateral thickness deviation of the inventive steel (Inventive Examples 1 to 19) have the relationship as shown in Equation 4, the comparative steels (Comparative Examples 2 to 5) It can be seen that Conventional Example 1 has the same relationship as Equation 6.
  • Inventive Samples 20 to 25 which satisfy both the alloy composition, the component relation and the manufacturing conditions proposed in the present invention, satisfy both the thickness variation in the width direction and the yield strength , And the thickness deviation and the yield strength in the width direction of the final product are all satisfied.
  • the comparative examples 9 and 10 do not satisfy the velocity deviation in the final rolling mill proposed in the present invention, and it can be seen that the widthwise thickness deviation of the thermal laminate and the final product is severe.

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

Abstract

La présente invention concerne une tôle d'acier électrique non orientée possédant une excellente propriété de forme et un procédé de fabrication s'y rapportant. Un mode de réalisation de la présente invention concerne une tôle d'acier électrique non orientée possédant une excellente propriété de forme et un procédé pour sa fabrication, la tôle d'acier électrique non orientée comprenant Si : 2,8 à 4,0 % en poids, Al : 0,1 à 1,5 % en poids, Mn : 0,05 à 1,5 % en poids, Sn : 0,005 à 0,20 % en poids, P : 0,002 à 0,15 % en poids et le reste étant du Fe et d'autres impuretés inévitables, lesdits Si, Al, Mn, Sn et P satisfaisant à l'expression relationnelle 1 ci-dessous et une variation d'épaisseur dans le sens de la largeur (△tCR) d'une bande satisfaisant à l'expression relationnelle 2 ci-dessous. [Expression relationnelle 1] 3,8 ≤ Si+Al+0,5Mn+0,8Sn+5P ≤ 5,4 [Expression relationnelle 2] △tCR ≤ 36*(S/t)-0,48 (dans l'expression relationnelle 1 ci-dessus, Si, Al, Mn, Sn et P représentent leurs quantités respectives (% en poids correspondantes et, dans l'expression relationnelle 2, △tCR est une variation d'épaisseur dans le sens de la largeur (µm) d'une bande, S est une position de mesure d'épaisseur (mm) d'un point qui est séparé d'un bord de bande dans le sens de la largeur d'une certaine distance et t est l'épaisseur (mm) de la bande.)
PCT/KR2018/015593 2017-12-26 2018-12-10 Tôle d'acier électrique non orientée possédant une excellente propriété de forme et procédé de fabrication s'y rapportant WO2019132315A1 (fr)

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KR1020170180275A KR102109241B1 (ko) 2017-12-26 2017-12-26 형상 품질이 우수한 무방향성 전기강판 및 그 제조방법
KR10-2017-0180275 2017-12-26

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KR102325008B1 (ko) * 2019-12-20 2021-11-10 주식회사 포스코 무방향성 전기강판 및 그 제조방법
KR102493776B1 (ko) * 2020-12-21 2023-01-31 주식회사 포스코 무방향성 전기강판 및 그 제조방법

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JPH1161256A (ja) * 1997-08-08 1999-03-05 Nkk Corp 表面性状が優れ且つ鉄損の低い無方向性電磁鋼板の製造方法
KR20050044499A (ko) * 2001-11-16 2005-05-12 티센크루프 일렉트리컬 스틸 게엠베하 무방향성 전기 강판 제조 방법
JP2009149993A (ja) * 1999-07-05 2009-07-09 Thyssenkrupp Stahl Ag 無方向性電磁鋼板の製造方法
KR100951462B1 (ko) * 2001-10-31 2010-04-07 티센크루프 스틸 유럽 악티엔게젤샤프트 무방향성 전기 강판 제조용 열연 강대 및 이를 제조하는방법
JP2012036455A (ja) * 2010-08-09 2012-02-23 Sumitomo Metal Ind Ltd 無方向性電磁鋼板およびその製造方法
KR20160078172A (ko) * 2014-12-24 2016-07-04 주식회사 포스코 무방향성 전기강판 및 그 제조방법

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JP2500033Y2 (ja) 1991-02-28 1996-06-05 株式会社大井製作所 ドアロック装置の取付け構造
JP2000129410A (ja) 1998-10-30 2000-05-09 Nkk Corp 磁束密度の高い無方向性電磁鋼板
JP4126479B2 (ja) 2000-04-28 2008-07-30 Ｊｆｅスチール株式会社 無方向性電磁鋼板の製造方法
JP3870893B2 (ja) 2002-11-29 2007-01-24 住友金属工業株式会社 無方向性電磁鋼板およびその製造方法
KR101664097B1 (ko) 2014-12-24 2016-10-10 주식회사 포스코 무방향성 전기강판 및 그 제조방법

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH1161256A (ja) * 1997-08-08 1999-03-05 Nkk Corp 表面性状が優れ且つ鉄損の低い無方向性電磁鋼板の製造方法
JP2009149993A (ja) * 1999-07-05 2009-07-09 Thyssenkrupp Stahl Ag 無方向性電磁鋼板の製造方法
KR100951462B1 (ko) * 2001-10-31 2010-04-07 티센크루프 스틸 유럽 악티엔게젤샤프트 무방향성 전기 강판 제조용 열연 강대 및 이를 제조하는방법
KR20050044499A (ko) * 2001-11-16 2005-05-12 티센크루프 일렉트리컬 스틸 게엠베하 무방향성 전기 강판 제조 방법
JP2012036455A (ja) * 2010-08-09 2012-02-23 Sumitomo Metal Ind Ltd 無方向性電磁鋼板およびその製造方法
KR20160078172A (ko) * 2014-12-24 2016-07-04 주식회사 포스코 무방향성 전기강판 및 그 제조방법

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