CN109477192B - Method for producing a hot-rolled coil and method for shape correction of a hot-rolled coil - Google Patents

Method for producing a hot-rolled coil and method for shape correction of a hot-rolled coil Download PDF

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CN109477192B
CN109477192B CN201780045377.0A CN201780045377A CN109477192B CN 109477192 B CN109477192 B CN 109477192B CN 201780045377 A CN201780045377 A CN 201780045377A CN 109477192 B CN109477192 B CN 109477192B
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hot rolled
rolled coil
hot
manganese
steel slab
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CN109477192A (en
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赵昇汉
黄至成
金泰冏
金贤洙
金炯辰
朴铭洙
朴永洙
李麒杓
李丞夏
林钟协
林埈锡
林熙重
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Hyundai Steel Co
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    • 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
    • B21B1/22—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 plates, strips, bands or sheets of indefinite length
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B3/02—Rolling special iron alloys, e.g. stainless steel
    • 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
    • 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
    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following 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
    • C22C38/001—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
    • C22C38/02—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • 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
    • B21B1/22—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 plates, strips, bands or sheets of indefinite length
    • B21B2001/225—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 plates, strips, bands or sheets of indefinite length by hot-rolling

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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)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

The present invention relates to a method for manufacturing a hot rolled coil and a method for modifying the shape of a hot rolled coil. In one embodiment, a method for making a hot rolled coil comprises the steps of: reheating a steel slab including 0.18 to 0.56 wt% of carbon (C), 0.1 to 0.5 wt% of silicon (Si), 0.7 to 6.5 wt% of manganese (Mn), more than 0 wt% but not more than 0.02 wt% of phosphorus (P), more than 0 wt% but not more than 0.02 wt% of sulfur (S), more than 0 wt% but not more than 0.3 wt% of chromium (Cr), more than 0 wt% but not more than 0.004 wt% of boron (B), 0.01 to 0.04 wt% of titanium (Ti), and the balance of iron (Fe) and other unavoidable impurities; hot rolling the steel slab at a finishing mill delivery temperature of 850 ℃ to 950 ℃ to form a hot rolled plate; and cooling the hot rolled sheet and then coiling at a coiling temperature of 700 ℃ or higher.

Description

Method for producing a hot-rolled coil and method for shape correction of a hot-rolled coil
Technical Field
The present invention relates to a method for manufacturing a hot rolled coil and a method for modifying the shape of a hot rolled coil. More particularly, the present invention relates to a method for manufacturing a hot rolled coil for preventing shape defects, which can prevent shape defects due to self weight during the manufacturing of the hot rolled coil, and a method for correcting the shape of the hot rolled coil.
Background
In recent years, ensuring weight reduction is considered to be an important factor in the development of automotive materials. This is intended to replace existing components with high strength materials, ultimately improving fuel efficiency. For this reason, materials as automobile structural materials have been developed to improve performance by adding alloying elements including manganese (Mn), nickel (Ni), chromium (Cr), molybdenum (Mo), titanium (Ti), etc., and cold rolling and heat treatment processes are employed to secure the strength of steel.
In Korean patent application laid-open No.1995-
Figure BDA0001952928280000011
Figure BDA0001952928280000012
) The background art related to the present invention is disclosed in the specification.
Disclosure of Invention
Technical problem
An embodiment of the present invention is directed to providing a method for manufacturing a hot rolled coil having an excellent effect of preventing deformation of the hot rolled coil.
Another embodiment of the present invention is directed to providing a method for modifying the shape of a hot rolled coil, which can prevent deterioration of the material and physical properties of the hot rolled coil.
Still another embodiment of the present invention is directed to providing a method for correcting a shape of a hot rolled coil, which can prevent surface defects of the hot rolled coil from being generated when the shape is corrected by applying an external force.
Yet another embodiment of the present invention is directed to providing a method for modifying the shape of a hot rolled coil, which has excellent economic efficiency.
Technical scheme
One aspect of the present invention relates to a method for manufacturing a hot rolled coil. In one embodiment, a method for manufacturing a hot rolled coil comprises the steps of: reheating a steel slab including 0.18 to 0.56 wt% of carbon (C), 0.1 to 0.5 wt% of silicon (Si), 0.7 to 6.5 wt% of manganese (Mn), greater than 0 but not more than 0.02 wt% of phosphorus (P), greater than 0 but not more than 0.02 wt% of sulfur (S), greater than 0 but not more than 0.3 wt% of chromium (Cr), greater than 0 but not more than 0.004 wt% of boron (B), 0.01 to 0.04 wt% of titanium (Ti), and the balance of iron (Fe) and other unavoidable impurities; hot rolling the steel slab at a finishing mill delivery temperature of 850 ℃ to 950 ℃ to form a hot rolled plate; and cooling the hot rolled sheet and then coiling at a coiling temperature of 700 ℃ or higher.
In one embodiment, a steel slab may include 0.21 to 0.37 wt% of carbon (C), 0.1 to 0.4 wt% of silicon (Si), 1.1 to 1.5 wt% of manganese (Mn), more than 0 wt% but not more than 0.02 wt% of phosphorus (P), more than 0 wt% but not more than 0.02 wt% of sulfur (S), 0.1 to 0.3 wt% of chromium (Cr), 0.001 to 0.004 wt% of boron (B), 0.01 to 0.04 wt% of titanium (Ti), and the balance of iron (Fe) and other unavoidable impurities.
In one embodiment, a steel slab may include 0.18 to 0.25 wt% of carbon (C), 0.3 to 0.5 wt% of silicon (Si), 2 to 6.5 wt% of manganese (Mn), more than 0 wt% but not more than 0.02 wt% of phosphorus (P), more than 0 wt% but not more than 0.01 wt% of sulfur (S), more than 0 wt% but not more than 0.1 wt% of chromium (Cr), more than 0 wt% but not more than 0.001 wt% of boron (B), 0.01 to 0.04 wt% of titanium (Ti), and the balance of iron (Fe) and other unavoidable impurities.
In one embodiment, a steel slab may include 0.5 to 0.56 wt% of carbon (C), 0.1 to 0.3 wt% of silicon (Si), 0.7 to 1 wt% of manganese (Mn), more than 0 wt% but not more than 0.02 wt% of phosphorus (P), more than 0 wt% but not more than 0.01 wt% of sulfur (S), 0.1 to 0.3 wt% of chromium (Cr), more than 0 wt% but not more than 0.001 wt% of boron (B), 0.01 to 0.02 wt% of titanium (Ti), and the balance of iron (Fe) and other unavoidable impurities.
Another aspect of the invention relates to a method for modifying the shape of a hot rolled coil. In one embodiment, a method for modifying the shape of a hot rolled coil comprises the steps of: mounting the hot rolled coil on a hook forming the lower part of the C-shaped hook; measuring the longest diameter of the hot rolled coil using an outer diameter measuring device disposed at an upper portion of the C-shaped hook; adjusting the longest diameter of the hot-rolled coil to be perpendicular to the C-shaped hook through a driving roller arranged on the hook; the C-shaped hook with the hot rolled coil mounted thereon is placed on a stand and then lifted, thereby correcting the shape of the hot rolled coil by its own weight.
Yet another aspect of the present invention relates to a method for modifying the shape of a hot rolled coil. In one embodiment, a method for modifying the shape of a hot rolled coil comprises the steps of: mounting the hot rolled coil on a hook forming the lower part of the C-shaped hook; measuring the longest diameter of the hot rolled coil using an outer diameter measuring device disposed at an upper portion of the C-shaped hook; adjusting the longest diameter of the hot rolled coil to be perpendicular to the C-shaped hook by a driving roller arranged on the lower hook; placing the C-shaped hook, on which the hot rolled coil is mounted, on a stand and then lifting up to modify the shape of the hot rolled coil by its own weight, wherein the hot rolled coil is manufactured by a method comprising the steps of; reheating a steel slab including 0.18 to 0.56 wt% of carbon (C), 0.1 to 0.5 wt% of silicon (Si), 0.7 to 6.5 wt% of manganese (Mn), more than 0 wt% but not more than 0.02 wt% of phosphorus (P), more than 0 wt% but not more than 0.02 wt% of sulfur (S), more than 0 wt% but not more than 0.3 wt% of chromium (Cr), more than 0 wt% but not more than 0.004 wt% of boron (B), 0.01 to 0.04 wt% of titanium (Ti), and the balance of iron (Fe) and other unavoidable impurities; hot rolling the steel slab at a finishing mill delivery temperature of 850 ℃ to 950 ℃ to form a hot rolled plate; and cooling the hot rolled sheet and then coiling at a coiling temperature of 700 ℃ or higher.
In one embodiment, the hot rolled coil may include 0.21 to 0.37 wt% of carbon (C), 0.1 to 0.4 wt% of silicon (Si), 1.1 to 1.5 wt% of manganese (Mn), greater than 0 wt% but not more than 0.02 wt% of phosphorus (P), greater than 0 wt% but not more than 0.02 wt% of sulfur (S), 0.1 to 0.3 wt% of chromium (Cr), 0.001 to 0.004 wt% of boron (B), 0.01 to 0.04 wt% of titanium (Ti), and the balance of iron (Fe) and other unavoidable impurities.
In one embodiment, the hot rolled sheet may be cooled and then coiled at a coiling temperature of 700 ℃ to 900 ℃.
Advantageous effects
When the shape correction is performed on the hot rolled coil manufactured by the method for manufacturing a hot rolled coil according to the present invention, the phase change of steel during cooling after hot rolling can be delayed, thereby preventing deterioration of the material and physical properties of the hot rolled coil while exhibiting an excellent effect of preventing deformation of the hot rolled coil. In addition, the use of the correction by the self-weight and the gravity makes it possible to prevent surface defects (e.g., scratches) of the hot rolled coil generated when the correction is used using an external force. In addition, it can reduce the revision cost and provide excellent economic efficiency.
Drawings
Fig. 1 illustrates a method for manufacturing a hot rolled coil according to one embodiment of the present invention.
Fig. 2 illustrates a method for modifying the shape of a hot rolled coil according to one embodiment of the present invention.
Fig. 3 schematically illustrates a method for modifying the shape of a hot rolled coil according to one embodiment of the present invention.
Fig. 4(a) is a photograph showing a hot rolled coil immediately after being wound according to an embodiment of the present invention, and fig. 4(b) is a photograph showing a hot rolled coil after being air-cooled.
Fig. 5(a) is a photograph showing a hot rolled coil immediately after being wound according to another embodiment of the present invention, and fig. 5(b) is a photograph showing a hot rolled coil after being air-cooled.
Fig. 6(a) is a photograph showing a hot rolled coil of a comparative example of the present invention immediately after being wound, and fig. 6(b) is a photograph showing a hot rolled coil after being air-cooled.
FIG. 7 is a graph comparing phase change curves of hot rolled coils according to manufacturing time and shape correction time of the hot rolled coils in the example of the present invention and the comparative example of the present invention.
Detailed Description
Hereinafter, the present invention will be described in detail. In the following description of the present invention, a detailed description of related known technologies or configurations will be omitted when it may unnecessarily obscure the subject matter of the present invention.
In addition, terms used in the following description are defined in consideration of their roles in the present invention, and may vary according to the intention of a user or an operator or general practice. Therefore, the definition should be made based on the contents of the specification describing the present invention.
Method for producing hot-rolled coils
One aspect of the present invention relates to a method for manufacturing a hot rolled coil. Fig. 1 illustrates a method for manufacturing a hot rolled coil according to one embodiment of the present invention. In one embodiment, a method for manufacturing a hot rolled coil comprises the steps of: (S10) reheating the slab; (S20) hot rolling; and (S30) winding. More specifically, the method for manufacturing a hot-rolled coil comprises the steps of: (S10) reheating a steel slab including 0.18 to 0.56 wt% of carbon (C), 0.1 to 0.5 wt% of silicon (Si), 0.7 to 6.5 wt% of manganese (Mn), more than 0 wt% but not more than 0.02 wt% of phosphorus (P), more than 0 wt% but not more than 0.02 wt% of sulfur (S), more than 0 wt% but not more than 0.3 wt% of chromium (Cr), more than 0 wt% but not more than 0.004 wt% of boron (B), 0.01 to 0.04 wt% of titanium (Ti), and the balance of iron (Fe) and other unavoidable impurities; (S20) hot rolling the steel slab at a finish rolling delivery temperature of 850 to 950 ℃, thereby forming a hot-rolled sheet; and (S30) cooling the hot rolled sheet, followed by coiling at a coiling temperature of 700 ℃ or higher.
Hereinafter, each step of the method for manufacturing a hot rolled coil according to the present invention will be described in detail.
(S10) billet reheating step
This step is a step of reheating a steel slab including 0.18 to 0.56 wt% of carbon (C), 0.1 to 0.5 wt% of silicon (Si), 0.7 to 6.5 wt% of manganese (Mn), more than 0 wt% but not more than 0.02 wt% of phosphorus (P), more than 0 wt% but not more than 0.02 wt% of sulfur (S), more than 0 wt% but not more than 0.3 wt% of chromium (Cr), more than 0 wt% but not more than 0.004 wt% of boron (B), 0.01 to 0.04 wt% of titanium (Ti), and the balance of iron (Fe) and other unavoidable impurities.
Hereinafter, the components contained in the steel billet will be described in detail.
Carbon (C)
Carbon (C) is added to ensure strength. The carbon content is 0.18 wt% to 0.56 wt% based on the total weight of the steel slab. If the content of carbon is less than 0.18 wt%, it may be difficult to secure sufficient strength. On the other hand, if the content of carbon is more than 0.56 wt%, toughness may be reduced.
Silicon (Si)
Silicon (Si) is used as a deoxidizer for removing oxygen from steel, and is added for solid solution strengthening. In one embodiment, the silicon is present in an amount of 0.1 to 0.5 wt.%, based on the total weight of the steel slab. If the content of silicon is less than 0.1 wt%, the effect of adding silicon is insufficient, and if the content of silicon is more than 0.5 wt%, weldability may be reduced and red rust may be generated during reheating and hot rolling, thus adversely affecting surface quality. In addition, it may adversely affect the properties of the coating after welding.
Manganese (Mn)
Manganese (Mn) is a solid-solution strengthening element that effectively secures strength by increasing hardenability of steel. In addition, manganese is an austenite stabilizing element that contributes to ferrite grain refinement by delaying ferrite and pearlite transformation.
In one embodiment, the manganese is present in an amount of 0.7 wt.% to 6.5 wt.%, based on the total weight of the steel slab. If the content of manganese is less than 0.7 wt%, the solid solution strengthening effect may be insufficient. On the other hand, if the content of manganese is more than 6.5 wt%, weldability may be greatly reduced. In addition, there may be a problem in that ductility of the steel sheet is greatly reduced due to formation of MnS inclusions and occurrence of center segregation.
Phosphorus (P)
Phosphorus (P) is added to inhibit the formation of cementite and increase strength. However, phosphorus deteriorates weldability and causes a difference in final properties by center segregation of the slab. Therefore, in the present invention, the content of phosphorus (P) is limited to more than 0 wt% but not more than 0.02 wt% based on the total weight of the steel slab.
Sulfur (S)
Sulfur (S) is an element that reduces toughness and weldability of steel and forms non-metallic inclusions (MnS) in combination with manganese, which cause cracks during processing of steel. Therefore, the content of sulfur (S) is limited to more than 0 wt% but not more than 0.02 wt% based on the total weight of the steel slab.
Chromium (Cr)
Chromium is added to increase the hardenability and strength of the steel. In one embodiment, the chromium content is greater than 0 wt% but not greater than 0.3 wt% based on the total weight of the steel slab. If the content of chromium is more than 0.3 wt%, the toughness of the hot rolled coil may be reduced.
Boron (B)
Boron (B) is added to compensate hardenability by replacing the expensive hardening element molybdenum, and has the effect of refining grains by increasing the austenite grain growth temperature.
In one embodiment, the boron content is greater than 0 wt% but not greater than 0.004 wt% based on the total weight of the steel slab. If the content of boron is more than 0.004 wt%, the risk of decreasing the elongation may be increased.
Titanium (Ti)
Titanium (Ti) is added to improve hardenability and to improve properties by forming precipitates. In addition, austenite grain refinement is effectively promoted by forming a precipitation phase such as Ti (C, N) at high temperature.
In one embodiment, the titanium is present in an amount of 0.01 wt.% to 0.04 wt.%, based on the total weight of the steel slab. If the content of titanium is less than 0.01 wt%, the effect of adding titanium may be insufficient, and if the content of titanium is more than 0.04 wt%, continuous casting defects may be generated, it may be difficult to secure physical properties of a hot rolled coil, and cracks may be generated on the surface of the hot rolled coil.
The remainder other than the above components consists essentially of iron (Fe). As used herein, the expression "the remainder substantially consists of iron (Fe)" means that a substance containing other trace elements including inevitable impurities may be included in the present invention as long as it does not impair the effects of the present invention.
In one embodiment, the steel slab may be applied to a medium carbon hot rolled coil. For example, the steel slab may include 0.21 to 0.37 wt% of carbon (C), 0.1 to 0.4 wt% of silicon (Si), 1.1 to 1.5 wt% of manganese (Mn), more than 0 wt% but not more than 0.02 wt% of phosphorus (P), more than 0 wt% but not more than 0.02 wt% of sulfur (S), 0.1 to 0.3 wt% of chromium (Cr), 0.001 to 0.004 wt% of boron (B), 0.01 to 0.04 wt% of titanium (Ti), and the balance of iron (Fe) and other unavoidable impurities.
In another embodiment, the steel slab may be applied to a high manganese hot rolled coil. For example, the steel slab may include 0.18 to 0.25 wt% of carbon (C), 0.3 to 0.5 wt% of silicon (Si), 2 to 6.5 wt% of manganese (Mn), more than 0 wt% but not more than 0.02 wt% of phosphorus (P), more than 0 wt% but not more than 0.01 wt% of sulfur (S), more than 0 wt% but not more than 0.1 wt% of chromium (Cr), more than 0 wt% but not more than 0.001 wt% of boron (B), 0.01 to 0.04 wt% of titanium (Ti), and the balance of iron (Fe) and other unavoidable impurities.
In yet another embodiment, the steel blank may be applied to a high carbon hot rolled coil. For example, the steel slab may include 0.5 to 0.56 wt% of carbon (C), 0.1 to 0.3 wt% of silicon (Si), 0.7 to 1 wt% of manganese (Mn), more than 0 wt% but not more than 0.02 wt% of phosphorus (P), more than 0 wt% but not more than 0.01 wt% of sulfur (S), 0.1 to 0.3 wt% of chromium (Cr), more than 0 wt% but not more than 0.001 wt% of boron (B), 0.01 to 0.02 wt% of titanium (Ti), and the balance of iron (Fe) and other unavoidable impurities.
In one embodiment, the steel slab may be heated at a Slab Reheating Temperature (SRT) of 1,150 ℃ to 1,250 ℃. At this slab reheating temperature, the effect of homogenizing the alloying elements can be excellent.
(S20) Hot Rolling step
The step is a step of hot rolling the steel slab at a finish rolling mill delivery temperature of 850 ℃ to 950 ℃ to form a hot rolled plate. When hot rolling is performed at the finish rolling mill conveyance temperature, the hot rolled coil may have excellent rigidity and excellent formability and is excellent in coiling workability, and the effect of preventing deformation of the hot rolled coil may be excellent.
(S30) winding step
This step is a step of cooling the hot rolled sheet and then performing coiling at a coiling temperature of 700 ℃ or higher. In one embodiment, the hot rolled sheet may be cooled to a coiling temperature and then coiled at that temperature. In one embodiment, the cooling may be performed by air cooling without using cooling water. When cooling is performed under the above-described conditions, the occurrence of the bulge defect on the hot rolled coil can be effectively reduced. As used herein, "bulging defect" may refer to a shape deformation defect of a hot rolled coil. Specifically, the "bulging defect" may refer to a shape deformation defect caused by the inner and outer diameters of the hot rolled coil becoming elliptical rather than circular due to the deformation of the hot rolled coil in the gravity direction, among shape defects generated on the hot rolled coil.
After the hot rolling of the sheet including the alloy composition of the present invention, cooling control may be performed such that coiling is completed at a temperature equal to or higher than the transformation start temperature. When coiling is performed at the above coiling temperature, ferrite phase transformation starts after a certain time after coiling, and therefore, due to slow cooling (air cooling) of the coil after coiling, the time required to complete the phase transformation may rapidly increase, thereby advantageously preventing shape deformation. That is, one embodiment of the present invention can provide a treatment condition that delays the time point at which the phase transition after winding occurs as much as possible.
If the hot rolled sheet is coiled at a coiling temperature lower than 700 ℃, the phase transformation of the hot rolled sheet may be performed during cooling and additional phase transformation may occur after the hot rolled coil is formed, resulting in an increase in coil volume, and then the hot rolled coil may shrink as the temperature decreases and its shape is deformed into an ellipse by its own weight, resulting in a protrusion defect. In one embodiment, the hot rolled sheet may be cooled and then coiled at a coiling temperature of 700 ℃ to 900 ℃. For example, the coiling may be performed at a coiling temperature of 730 ℃ to 820 ℃. The resulting hot rolled coil may include a ferrite and bainite microstructure.
Method for modifying the shape of a hot-rolled coil
Another aspect of the invention relates to a method for modifying the shape of a hot rolled coil. Fig. 2 illustrates a method for modifying the shape of a hot rolled coil according to one embodiment of the present invention. Referring to fig. 2, the method for modifying the shape of a hot rolled coil includes the steps of: (S101) installing a hot-rolled coil; (S102) measuring the longest diameter of the hot rolled coil; (S103) adjusting the position of the hot rolled coil; and (S104) lifting.
Fig. 3 schematically illustrates a method for modifying the shape of a hot rolled coil according to another embodiment of the present invention. Referring to fig. 3, the method for modifying the shape of a hot rolled coil includes the steps of: (S101) mounting the hot-rolled coil on a hook forming a lower portion of the C-shaped hook; (S102) measuring the longest diameter of the hot rolled coil using an outer diameter measuring device disposed at an upper portion of the C-shaped hook; (S103) adjusting the longest diameter of the hot rolled coil to be perpendicular to the C-shaped hook by means of the driving roller provided on the lower hook; (S104) placing the C-shaped hook, on which the hot rolled coil is mounted, on the stand and then lifting, thereby correcting the shape of the hot rolled coil by its own weight.
For example, as shown in fig. 3(a), the hot rolled coil 100 is mounted on a hook 201 forming a lower portion of a C-shaped hook 200. As shown in FIG. 3(b), the longest diameter of the hot rolled coil 100 is measured using an outer diameter measuring device 210 provided at the upper portion 202 of the C-hook. Next, as shown in fig. 3(C), the longest diameter of the hot rolled coil 100 is adjusted to be perpendicular to the C-shaped hook using the driving roller 220 provided on the hook 201 forming the lower portion. As shown in fig. 3(e), the C-shaped hook 200 with the hot rolled coil mounted thereon is placed on the support 300 and then lifted, whereby the shape of the hot rolled coil deformed into an oval shape can be corrected into a circular shape by its own weight as shown in fig. 3 (f).
The hot rolled coil is manufactured by a method comprising the steps of: reheating a steel slab including 0.18 to 0.56 wt% of carbon (C), 0.1 to 0.5 wt% of silicon (Si), 0.7 to 6.5 wt% of manganese (Mn), more than 0 wt% but not more than 0.02 wt% of phosphorus (P), more than 0 wt% but not more than 0.02 wt% of sulfur (S), more than 0 wt% but not more than 0.3 wt% of chromium (Cr), more than 0 wt% but not more than 0.004 wt% of boron (B), 0.01 to 0.04 wt% of titanium (Ti), and the balance of iron (Fe) and other unavoidable impurities; hot rolling the steel slab at a finishing mill delivery temperature of 850 ℃ to 950 ℃ to form a hot rolled plate; and cooling the hot rolled sheet and then coiling at a coiling temperature of 700 ℃ or higher. In one embodiment, the hot rolled coil may be manufactured by cooling a hot rolled sheet and then coiling at a coiling temperature of 700 ℃ to 900 ℃. The resulting hot rolled coil may include a ferrite and bainite microstructure.
The method for manufacturing the hot rolled coil may be performed using the same steel slab as that used in the above-described method for manufacturing the hot rolled coil, and thus a detailed description thereof is omitted.
In one embodiment, the hot rolled coil may be a medium carbon hot rolled material. It may include 0.21 to 0.37 wt% of carbon (C), 0.1 to 0.4 wt% of silicon (Si), 1.1 to 1.5 wt% of manganese (Mn), more than 0 wt% but not more than 0.02 wt% of phosphorus (P), more than 0 wt% but not more than 0.02 wt% of sulfur (S), 0.1 to 0.3 wt% of chromium (Cr), 0.001 to 0.004 wt% of boron (B), 0.01 to 0.04 wt% of titanium (Ti), and the balance of iron (Fe) and other unavoidable impurities.
In another embodiment, the hot rolled coil may be a high manganese hot rolled material. It may include 0.18 to 0.25 wt% of carbon (C), 0.3 to 0.5 wt% of silicon (Si), 2 to 6.5 wt% of manganese (Mn), more than 0 wt% but not more than 0.02 wt% of phosphorus (P), more than 0 wt% but not more than 0.01 wt% of sulfur (S), more than 0 wt% but not more than 0.1 wt% of chromium (Cr), more than 0 wt% but not more than 0.001 wt% of boron (B), 0.01 to 0.04 wt% of titanium (Ti), and the balance of iron (Fe) and other unavoidable impurities.
In yet another embodiment, the hot rolled coil may be a high carbon hot rolled material. It may include 0.5 to 0.56 wt% of carbon (C), 0.1 to 0.3 wt% of silicon (Si), 0.7 to 1 wt% of manganese (Mn), more than 0 wt% but not more than 0.02 wt% of phosphorus (P), more than 0 wt% but not more than 0.01 wt% of sulfur (S), 0.1 to 0.3 wt% of chromium (Cr), more than 0 wt% but not more than 0.001 wt% of boron (B), 0.01 to 0.02 wt% of titanium (Ti), and the balance of iron (Fe) and other unavoidable impurities.
When the shape correction is performed on the hot rolled coil manufactured by the method for manufacturing a hot rolled coil according to the present invention, it is possible to prevent the phase transformation of steel during cooling after hot rolling, thereby preventing deterioration of the material and physical properties of the hot rolled coil, while exhibiting an excellent effect of preventing deformation of the hot rolled coil. In addition, the use of the correction by the self-weight and the gravity makes it possible to prevent surface defects (e.g., scratches) of the hot rolled coil generated when the correction is used using an external force. In addition, it can eliminate the existing correction device using an external force, thereby reducing the correction cost and providing excellent economic efficiency.
Hereinafter, the constitution and effect of the present invention will be described in more detail with reference to preferred embodiments. However, these examples are only for illustrating the present invention and should not be construed as limiting the scope of the present invention in any way.
Examples and comparative examples
Example 1
As a medium carbon material, a steel slab comprising 0.23 wt% of carbon (C), 0.2 wt% of silicon (Si), 1.2 wt% of manganese (Mn), 0.015 wt% of phosphorus (P), 0.01 wt% of sulfur (S), 0.2 wt% of chromium (Cr), 0.003 wt% of boron (B), 0.02 wt% of titanium (Ti), and the balance of iron (Fe) and other unavoidable impurities was reheated at 1200 ℃, and the steel slab was hot-rolled at a finish rolling mill delivery temperature of 880 ℃, thereby forming a hot-rolled plate. Then, the hot-rolled sheet was cooled and coiled at a coiling temperature of 700 ℃, thereby manufacturing a hot-rolled coil.
Example 2
As a high manganese material, a slab comprising 0.2 wt% of carbon (C), 0.4 wt% of silicon (Si), 6 wt% of manganese (Mn), 0.015 wt% of phosphorus (P), 0.01 wt% of sulfur (S), 0.05 wt% of chromium (Cr), 0.001 wt% of boron (B), 0.02 wt% of titanium (Ti), and the balance of iron (Fe) and other unavoidable impurities was reheated at 1200 ℃, and the slab was hot-rolled at a finish rolling mill delivery temperature of 940 ℃ to form a hot-rolled plate. Then, the hot-rolled sheet was cooled and coiled at a coiling temperature of 700 ℃, thereby manufacturing a hot-rolled coil.
Example 3
As a high carbon material, a steel slab comprising 0.55 wt% of carbon (C), 0.2 wt% of silicon (Si), 0.8 wt% of manganese (Mn), 0.015 wt% of phosphorus (P), 0.01 wt% of sulfur (S), 0.2 wt% of chromium (Cr), 0.001 wt% of boron (B), 0.01 wt% of titanium (Ti), and the balance of iron (Fe) and other unavoidable impurities was reheated at 1200 ℃, and the steel slab was hot-rolled at a finish rolling mill delivery temperature of 890 ℃, thereby forming a hot-rolled plate. Then, the hot-rolled sheet was cooled and coiled at a coiling temperature of 730 ℃, thereby manufacturing a hot-rolled coil.
Comparative example 1
A hot rolled coil was manufactured in the same manner as described in example 1, except that the hot rolled sheet was coiled at a coiling temperature of 560 ℃.
Comparative example 2
A hot rolled coil was manufactured in the same manner as described in example 1, except that the hot rolled sheet was coiled at a coiling temperature of 600 ℃.
Comparative example 3
A hot rolled coil was manufactured in the same manner as described in example 1, except that the hot rolled sheet was coiled at a coiling temperature of 620 ℃.
Comparative example 4
A hot rolled coil was manufactured in the same manner as described in example 1, except that the hot rolled sheet was coiled at a coiling temperature of 650 ℃.
Fig. 4(a) is a photograph showing a hot rolled coil according to example 1 of the present invention immediately after being wound, and fig. 4(b) is a photograph showing a hot rolled coil after being air-cooled. Fig. 5(a) is a photograph showing a hot rolled coil according to example 1 of the present invention immediately after being wound, and fig. 5(b) is a photograph showing a hot rolled coil after being air-cooled. Fig. 6(a) is a photograph showing a hot rolled coil according to a comparative example of the present invention immediately after being wound, and fig. 6(b) is a photograph showing a hot rolled coil after being air-cooled. Referring to fig. 4(a) and 4(b), in example 1, no convex defect was observed immediately after coiling of the hot rolled coil, but convex defect was observed after air cooling. However, it can be seen that the degree of the projected defect is smaller than that in the comparative example. Referring to fig. 5(a) and 5(b), in example 2, no convex defect was observed immediately after coiling of the hot rolled coil and immediately after air cooling. Referring to fig. 6(a) and 6(b), in the comparative example, the projected defects were observed immediately after the coiling of the hot rolled coil, and it can be seen that the degree of projected defects became more serious as the air cooling proceeded.
Correction of shape of hot-rolled coil
For the hot rolled coils of example 1 to example 3 and comparative example 1 to comparative example 4, shape correction was performed. Each hot rolled coil was mounted on a hook forming a lower portion of the C-hook, and then the longest diameter of the hot rolled coil was measured using an outer diameter measuring device disposed at an upper portion of the C-hook. Thereafter, the longest diameter of the hot rolled coil was adjusted to be perpendicular to the C-hook using a driving roller provided on the hook. The C-shaped hook with the hot rolled coil mounted thereon is placed on a support and then lifted, thereby correcting the shape of the hot rolled coil by its own weight.
For examples 1 to 3 and comparative examples 1 to 4, the inner diameter of the roll and whether the bulging defect was corrected after the shape correction were observed, and the observation results are shown in table 1 below.
TABLE 1
Figure BDA0001952928280000131
Referring to table 1 above, it can be seen that in the case of examples 1 to 3, no protrusion defect occurred after correction, whereas in the case of comparative examples 1 to 4, which exceeded the coiling temperature of the present invention, the protrusion defect was not properly corrected even after correction.
Fig. 7 is a graph of phase transition curves of the hot rolled coil in comparative example 1 and comparative example 1 with the lapse of the manufacturing time and the shape correcting time of the hot rolled coil. Referring to fig. 7, in the case of example 1 of the present invention, in which a specific alloy element system is applied and coiling is performed at a temperature (700 ℃) equal to or higher than the transformation temperature, and thus, transformation into ferrite is performed after a certain time after the hot rolled coil is manufactured, it can be seen that the time required to complete the transformation rapidly increases due to slow cooling (air cooling) of the coil after coiling, which indicates that example 1 is advantageous for shape correction. However, in the case of comparative example 1 in which coiling was performed at a temperature lower than the transformation temperature of the hot-rolled sheet, it can be seen that transformation into ferrite occurred earlier than in example 1, making it difficult to secure the time for transformation start of the present invention, which indicates that comparative example 1 is disadvantageous in shape correction.
In addition, according to the method for manufacturing a hot rolled coil and the method for modifying the shape of a hot rolled coil of the present invention, it is possible to reduce the occurrence of bulging of a hot rolled coil, thereby reducing additional operations caused by breakage of an inner wrap portion, delayed operation time, equipment breakage, and the like, which may occur due to a bulging coil in a subsequent modification process, thereby providing the following effects: including increased work efficiency, increased material quality, decreased production of defective products that are disposed of as waste, and the like.
Simple modifications or changes may be easily made by those skilled in the art and are considered to be included in the scope of the present invention.

Claims (6)

1. A method for manufacturing a hot rolled coil, the method comprising the steps of:
reheating a steel slab including 0.18 to 0.56 wt% of carbon (C), 0.1 to 0.5 wt% of silicon (Si), 0.7 to 6.5 wt% of manganese (Mn), more than 0 wt% but not more than 0.02 wt% of phosphorus (P), more than 0 wt% but not more than 0.02 wt% of sulfur (S), more than 0 wt% but not more than 0.3 wt% of chromium (Cr), more than 0 wt% but not more than 0.004 wt% of boron (B), 0.01 to 0.04 wt% of titanium (Ti), and the balance of iron (Fe) and other unavoidable impurities;
hot rolling the reheated slab at a finish-rolling-mill delivery temperature of 850 ℃ to 950 ℃ to form a hot-rolled sheet; and
the hot rolled sheet is cooled and then coiled at a coiling temperature of 730 ℃ to 900 ℃.
2. The method of claim 1 wherein the steel slab comprises 0.21 to 0.37 wt.% carbon (C), 0.1 to 0.4 wt.% silicon (Si), 1.1 to 1.5 wt.% manganese (Mn), greater than 0 but not more than 0.02 wt.% phosphorus (P), greater than 0 but not more than 0.02 wt.% sulfur (S), 0.1 to 0.3 wt.% chromium (Cr), 0.001 to 0.004 wt.% boron (B), 0.01 to 0.04 wt.% titanium (Ti), and the balance iron (Fe) and other unavoidable impurities.
3. The method of claim 1 wherein the steel slab comprises 0.18 to 0.25 wt.% carbon (C), 0.3 to 0.5 wt.% silicon (Si), 2 to 6.5 wt.% manganese (Mn), greater than 0 but not more than 0.02 wt.% phosphorus (P), greater than 0 but not more than 0.01 wt.% sulfur (S), greater than 0 but not more than 0.1 wt.% chromium (Cr), greater than 0 but not more than 0.001 wt.% boron (B), 0.01 to 0.04 wt.% titanium (Ti), and the balance iron (Fe) and other unavoidable impurities.
4. The method of claim 1 wherein the steel slab comprises 0.5 to 0.56 weight percent carbon (C), 0.1 to 0.3 weight percent silicon (Si), 0.7 to 1 weight percent manganese (Mn), greater than 0 but not greater than 0.02 weight percent phosphorus (P), greater than 0 but not greater than 0.01 weight percent sulfur (S), 0.1 to 0.3 weight percent chromium (Cr), greater than 0 but not greater than 0.001 weight percent boron (B), 0.01 to 0.02 weight percent titanium (Ti), and the balance iron (Fe) and other unavoidable impurities.
5. A method for modifying the shape of a hot rolled coil, the method comprising the steps of:
mounting the hot rolled coil on a hook forming the lower part of the C-shaped hook;
measuring the longest diameter of the hot rolled coil using an outer diameter measuring device disposed at an upper portion of the C-shaped hook;
adjusting the longest diameter of the hot-rolled coil to be perpendicular to the C-shaped hook through a driving roller arranged on the hook; and
the C-shaped hook with the hot rolled coil mounted thereon is placed on a support and then lifted, thereby correcting the shape of the hot rolled coil by self-weight,
wherein the hot rolled coil is manufactured by a method comprising the steps of:
reheating a steel slab including 0.18 to 0.56 wt% of carbon (C), 0.1 to 0.5 wt% of silicon (Si), 0.7 to 6.5 wt% of manganese (Mn), more than 0 wt% but not more than 0.02 wt% of phosphorus (P), more than 0 wt% but not more than 0.02 wt% of sulfur (S), more than 0 wt% but not more than 0.3 wt% of chromium (Cr), more than 0 wt% but not more than 0.004 wt% of boron (B), 0.01 to 0.04 wt% of titanium (Ti), and the balance of iron (Fe) and other unavoidable impurities;
hot rolling the steel slab at a finishing mill delivery temperature of 850 ℃ to 950 ℃ to form a hot rolled plate; and
the hot rolled sheet is cooled and then coiled at a coiling temperature of 730 ℃ to 900 ℃.
6. The method of claim 5, wherein the hot rolled coil comprises 0.21 to 0.37 wt% of carbon (C), 0.1 to 0.4 wt% of silicon (Si), 1.1 to 1.5 wt% of manganese (Mn), greater than 0 but not more than 0.02 wt% of phosphorus (P), greater than 0 but not more than 0.02 wt% of sulfur (S), 0.1 to 0.3 wt% of chromium (Cr), 0.001 to 0.004 wt% of boron (B), 0.01 to 0.04 wt% of titanium (Ti), and the balance iron (Fe) and other unavoidable impurities.
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