US20230287543A1 - Method for producing ultra-low carbon steel product - Google Patents

Method for producing ultra-low carbon steel product Download PDF

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US20230287543A1
US20230287543A1 US18/013,326 US202118013326A US2023287543A1 US 20230287543 A1 US20230287543 A1 US 20230287543A1 US 202118013326 A US202118013326 A US 202118013326A US 2023287543 A1 US2023287543 A1 US 2023287543A1
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slab
hot
rolling
steel sheet
low carbon
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Keisuke Sano
Masatoshi Ishiwari
Masaru Miyake
Kenji TSUZUMI
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JFE Steel Corp
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JFE Steel Corp
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Assigned to JFE STEEL CORPORATION reassignment JFE STEEL CORPORATION ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: ISHIWARI, MASATOSHI, MIYAKE, MASARU, SANO, KEISUKE, TSUZUMI, Kenji
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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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • 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%
    • 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
    • B21B1/02—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 heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D1/00—Treatment of fused masses in the ladle or the supply runners before casting
    • B22D1/002—Treatment with gases
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/10—Supplying or treating molten metal
    • B22D11/11—Treating the molten metal
    • B22D11/116—Refining the metal
    • B22D11/117—Refining the metal by treating with gases
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/12—Accessories for subsequent treating or working cast stock in situ
    • B22D11/1206—Accessories for subsequent treating or working cast stock in situ for plastic shaping of strands
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/12—Accessories for subsequent treating or working cast stock in situ
    • B22D11/128—Accessories for subsequent treating or working cast stock in situ for removing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/04—Removing impurities by adding a treating agent
    • C21C7/068—Decarburising
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—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
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese

Definitions

  • the present invention relates to a method for producing an ultra-low carbon steel product having a small number of blister defects.
  • Blister defects in cold-rolled steel sheets are, as disclosed in Non Patent Literature 1, blister-like surface defects which occur when hydrogen that has entered a steel sheet during pickling after hot rolling is retained in bubbles in the steel sheet, the volume thereof expands with heating during annealing after cold rolling, and the pressure raised by this deforms the surface of the steel sheet that has been softened by heating.
  • Patent Literature 1 discloses a method in which, by a continuous casting machine including a mold having upper magnetic poles and lower magnetic poles and a nozzle having exit ports of molten steel positioned between the magnetic field peak position of the upper magnetic poles and the magnetic field peak position of the lower magnetic poles, a slab is cast while the flow of molten steel being controlled, so that bubbles are suppressed from being captured in a solidified shell, and thus, occurrence of blisters can be suppressed.
  • Patent Literature 1 is a technique in which bubbles which may cause blister defects are suppressed from being captured in the solidified shell mainly at the casting stage.
  • inert gas is introduced into the immersion nozzle. Accordingly, it is difficult to completely prevent bubbles from being captured in a solidified shell.
  • aspects of the present invention have been made in consideration of the problem of the existing technique, and it is an object according to aspects of the invention to provide a method for producing an ultra-low carbon steel product in which, even if bubbles are captured in a solidified shell, occurrence of blister defects can be suppressed in a hot rolling step and subsequent steps.
  • a method for producing an ultra-low carbon steel product having a carbon concentration of 0.005% by mass or less including, at least, a refining step of adjusting a carbon concentration of molten iron to obtain molten steel, a casting step of casting the molten steel into a slab, and a hot rolling step of hot rolling the slab to obtain a hot-rolled steel sheet, in which the method further includes a width reduction step of performing width reduction on the slab to be subjected to the hot rolling step with a reduction amount which is predetermined in accordance with the slab width in a direction orthogonal to the rolling direction of the slab.
  • a method for producing an ultra-low carbon steel product having a carbon concentration of 0.005% by mass or less including, at least, a refining step of adjusting a carbon concentration of molten iron to obtain molten steel, a casting step of casting the molten steel into a slab, a hot rolling step of hot rolling the slab to obtain a hot-rolled steel sheet, and a cold rolling step of cold rolling the hot-rolled steel sheet to obtain a cold-rolled steel sheet, in which in the cold rolling step, cold rolling is performed at a rolling reduction ratio which is predetermined in accordance with the thickness of the hot-rolled steel sheet.
  • FIG. 1 is a graph showing the relationship between the width reduction amount and the blister defect occurrence rate.
  • FIG. 2 is a graph showing the relationship between the rolling reduction ratio of cold rolling and the blister defect occurrence rate.
  • blister defects occur when hydrogen that has entered a steel sheet during pickling after hot rolling is retained in bubbles and the like in the steel sheet, the volume thereof expands with heating during annealing after cold rolling, and the pressure raised by this deforms the surface of the steel sheet that has been softened by heating.
  • the present inventors have found that by performing width reduction on a slab to be subjected to hot rolling with a reduction amount which is predetermined in accordance with the slab width (size) in a direction orthogonal to the rolling direction of the slab so as to deform bubbles contained in the slab, occurrence of blister defects can be suppressed, and thus aspects of the present invention have been made. Aspects of the present invention will be described below by way of an exemplary embodiment.
  • a method for producing an ultra-low carbon steel product includes, at least, a refining step of adjusting a carbon concentration of molten iron to obtain molten steel, a casting step of casting the molten steel into a slab, a width reduction step of performing width reduction on the slab, and a hot rolling step of hot rolling the slab subjected to width reduction. Furthermore, in some cases, the method may include, after the hot rolling step, a cold rolling step of cold rolling the hot-rolled steel sheet.
  • Molten steel of ultra-low carbon steel is obtained by steelmaking in such a manner that molten steel which has been subjected to a primary refining process in a refining apparatus, such as a converter, in advance is further subjected to a degassing and decarburization process using an RH type degassing apparatus or the like.
  • the step including these processes is an example of the refining step of adjusting a carbon concentration of molten iron to obtain molten steel.
  • molten steel of ultra-low carbon steel having a carbon concentration of 0.005% by mass or less is obtained.
  • the molten steel of ultra-low carbon steel is continuously cast into a slab using a continuous casting machine equipped with a tundish, a mold, foot rolls, guide rolls, pinch rolls, a secondary cooling device, and the like.
  • the step of continuously casting molten steel into a slab using the continuous casting machine is an example of the casting step of casting the molten steel into a slab.
  • the slab is subjected to hot rolling to obtain a hot-rolled steel sheet, and by pickling the hot-rolled steel sheet, a hot-rolled steel sheet is produced.
  • the hot-rolled steel sheet may be further subjected to cold rolling, annealing, and other processes to obtain a cold-rolled steel sheet.
  • the cold-rolled steel sheet may be subjected to hot-dip galvannealing treatment to obtain a hot-dip galvannealed steel sheet.
  • the step of subjecting the slab to hot rolling including the pickling process to obtain a hot-rolled steel sheet is an example of the step of hot rolling the slab, and the step of subjecting the hot-rolled steel sheet to cold rolling, annealing, and other processes to obtain a cold-rolled steel sheet is an example of the cold rolling step of cold rolling the hot-rolled slab.
  • molten steel in a tundish is poured into a mold through an immersion nozzle.
  • the ultra-low carbon steel having a carbon concentration of 0.005% by mass or less contains alumina generated during the degassing and decarburization process using an RH-degassing apparatus.
  • inert gas such as Ar gas
  • Bubbles of the inert gas are discharged, together with the molten steel, from molten steel exit ports of the immersion nozzle into the mold.
  • the method for producing an ultra-low carbon steel product according to the embodiment further includes a width reduction step of performing width reduction on the slab to be subjected to hot rolling with a reduction amount which is predetermined in accordance with the slab width in a direction orthogonal to the rolling direction of the slab. Specifically, using a sizing press, width reduction is performed on the slab to be subjected to hot rolling. In this way, occurrence of blister defects during annealing after cold rolling can be suppressed.
  • ⁇ is the expansion amount (m)
  • W is the stress (N)
  • L is the bubble width (m)
  • E is the Young's modulus (MPa)
  • I is the moment of inertia of area (m 4 ).
  • the bubble width is narrowed, and L in the formula (1) decreases.
  • L decreases, the expansion amount ( ⁇ ) at the center of the beam also decreases. Because of this effect, expansion of bubbles is suppressed, and thus it is considered that occurrence of blister defects is suppressed.
  • the resulting cold-rolled steel sheet was subjected to hot-dip galvannealing treatment, and surface defects of the resulting hot-dip galvannealed steel sheet were continuously measured with an on-line surface defect meter.
  • surface defects of the resulting hot-dip galvannealed steel sheet were continuously measured with an on-line surface defect meter.
  • SEM analysis, ICP analysis, or the like it was visually confirmed whether or not the surface defects were blister defects.
  • a value obtained by dividing the mass coils in which blister defects occurred by the total coil mass was multiplied by 100 to calculate the blister defect occurrence rate.
  • the rolling reduction ratio of cold rolling was calculated in accordance with formula (2) below.
  • Rolling reduction ratio (steel sheet thickness at entry of cold rolling-steel sheet thickness at exit of cold rolling)/steel sheet thickness at entry of cold rolling (2)
  • the blister defect occurrence rate was confirmed using an ultra-low carbon steel 1 whose standard component concentrations were C concentration: 0.0000 to 0.0020 by mass, Si concentration: 0.00 to 0.03% by mass, Mn concentration: 0.10 to 0.25% by mass, P concentration: 0.010 to 0.020% by mass, S concentration: 0.003 to 0.010% by mass, and N concentration: 0.0000 to 0.0035% by mass, and an ultra-low carbon steel 2 whose standard component concentrations were C concentration: 0.0000 to 0.0015 by mass, Si concentration: 0.00 to 0.03% by mass, Mn concentration: 0.05 to 0.18% by mass, P concentration: 0.000 to 0.010% by mass, S concentration: 0.003 to 0.009% by mass, and N concentration: 0.0000 to 0.0030% by mass.
  • FIG. 1 is a graph showing the relationship between the width reduction amount by the sizing press and the blister defect occurrence rate.
  • the horizontal axis represents the slab width reduction amount (mm)
  • the vertical axis represents the blister defect occurrence rate (%).
  • the blister defect occurrence rate slightly increases when the width reduction amount is increased from 100 to 150 mm to 150 to 200 mm, as a whole, the blister defect occurrence rate tends to decrease as the slab width reduction amount is increased. This result shows that by performing width reduction on the slab to be subjected to hot rolling with a reduction amount which is predetermined in accordance with the slab width in a direction orthogonal to the rolling direction of the slab, occurrence of blister defects can be suppressed.
  • the proper width reduction amount in accordance with the slab width can be predetermined by grasping the relationship between the width reduction amount and the blister defect occurrence rate shown in FIG. 1 by an experiment or the like. That is, in the example shown in FIG. 1 , it is clear that by subjecting a slab with a width of 1,100 to 2,100 mm to width reduction by a sizing press, with a reduction amount of 200 to 250 mm or more, the blister defect occurrence rate can be greatly decreased.
  • cold rolling may be performed at a rolling reduction ratio which is predetermined in accordance with the thickness of the hot-rolled steel sheet.
  • a rolling reduction ratio which is predetermined in accordance with the thickness of the hot-rolled steel sheet.
  • FIG. 2 is a graph showing the relationship between the rolling reduction ratio of cold rolling and the blister defect occurrence rate.
  • the horizontal axis represents cold rolling reduction ratio ( ⁇ )
  • the vertical axis represents the blister defect occurrence rate (%).
  • the rolling reduction ratio of cold rolling also correlates with the blister defect occurrence rate, and the blister defect occurrence rate tends to decrease as the rolling reduction ratio of cold rolling is increased. This result shows that instead of width reduction of the slab, or together with width reduction of the slab, cold rolling may be performed at a rolling reduction ratio which is predetermined in accordance with the thickness of the hot-rolled steel sheet, and thereby, occurrence of blister defects can be suppressed.
  • the proper rolling reduction ratio in accordance with the thickness of the hot-rolled steel sheet can be predetermined by grasping the relationship between the rolling reduction ratio of cold rolling and the blister defect occurrence rate shown in FIG. 2 by an experiment or the like. That is, in the example shown in FIG. 2 , it is clear that by performing cold rolling at a rolling reduction ratio of 0.76 or more on a hot-rolled steel sheet with a thickness of 2.6 to 4.0 mm, the blister occurrence rate can be greatly decreased.
  • the mechanism of suppression of occurrence of blister defects by slab width reduction is different from the mechanism of suppression of occurrence of blister defects by cold rolling, it is clear that by using these techniques together, the occurrence of blister defects can be further suppressed.
  • slab width reduction and cold rolling are used together, slabs subjected to width reduction with different reduction amounts are prepared, and regarding hot-rolled steel sheets produced from the slabs prepared, the relationship between the cold rolling reduction ratio and the blister defect occurrence rate is grasped in advance by an experiment or the like. In this way, the width reduction amount in accordance with the slab width and the rolling reduction ratio in accordance with the thickness of the hot-rolled steel sheet can be predetermined.
  • an ultra-low carbon steel product produced by the method for producing an ultra-low carbon steel product according to the embodiment is a hot-rolled steel sheet obtained by subjecting an ultra-low carbon steel slab with 0.005% by mass or less to width reduction with a predetermined width reduction amount, followed by hot rolling and pickling.
  • an ultra-low carbon steel product produced by the method for producing an ultra-low carbon steel product according to the embodiment may be a cold-rolled steel sheet obtained by subjecting an ultra-low carbon steel slab with 0.005% by mass or less to hot rolling, followed by pickling and cold rolling, or may be a hot-dip galvannealed steel sheet obtained by subjecting the cold-rolled steel sheet to hot-dip galvannealing treatment.
  • the method for producing an ultra-low carbon steel according to the embodiment can be applied not only to the ultra-low carbon steels 1 and 2 described above, but also to an ultra-low carbon steel 3 whose standard component concentrations are C concentration: 0.0000 to 0.0030 by mass, Si concentration: 0.00 to 0.03% by mass, Mn concentration: 0.10 to 0.25% by mass, P concentration: 0.015 to 0.030% by mass, S concentration: 0.005 to 0.012% by mass, and N concentration: 0.0000 to 0.0035% by mass, and an ultra-low carbon steel 4 whose standard component concentrations are C concentration: 0.0000 to 0.0020 by mass, Si concentration: 0.00 to 0.04% by mass, Mn concentration: 0.10 to 0.25% by mass, P concentration: 0.000 to 0.010% by mass, S concentration: 0.004 to 0.012% by mass, and N concentration: 0.0000 to 0.0030% by mass.

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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)
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  • Crystallography & Structural Chemistry (AREA)
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US18/013,326 2020-07-08 2021-07-05 Method for producing ultra-low carbon steel product Pending US20230287543A1 (en)

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JP2020-117921 2020-07-08
JP2020117921 2020-07-08
PCT/JP2021/025374 WO2022009849A1 (ja) 2020-07-08 2021-07-05 極低炭素鋼製品の製造方法

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EP (1) EP4151755A4 (enrdf_load_stackoverflow)
JP (1) JP7452656B2 (enrdf_load_stackoverflow)
KR (1) KR20230022213A (enrdf_load_stackoverflow)
CN (1) CN115803126A (enrdf_load_stackoverflow)
TW (1) TWI778702B (enrdf_load_stackoverflow)
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JPH04247827A (ja) * 1991-01-23 1992-09-03 Nkk Corp プレス成形性に優れた高強度冷延鋼板の製造方法
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JPH1046243A (ja) * 1996-07-29 1998-02-17 Kawasaki Steel Corp 缶用鋼板の製造方法
JP2001279331A (ja) * 2000-03-30 2001-10-10 Kawasaki Steel Corp 耐フクレ欠陥特性に優れたほうろう用冷延鋼板の製造方法
US20150252456A1 (en) * 2012-10-11 2015-09-10 Jfe Steel Corporation Cold-rolled steel sheet with excellent shape fixability and method of manufacturing the same

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