US20230033491A1 - Steel plate having excellent wear resistance and composite corrosion resistance and method for manufacturing same - Google Patents

Steel plate having excellent wear resistance and composite corrosion resistance and method for manufacturing same Download PDF

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US20230033491A1
US20230033491A1 US17/785,846 US202017785846A US2023033491A1 US 20230033491 A1 US20230033491 A1 US 20230033491A1 US 202017785846 A US202017785846 A US 202017785846A US 2023033491 A1 US2023033491 A1 US 2023033491A1
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steel sheet
corrosion
resistant steel
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Byoung Ho LEE
Young-Kwang HONG
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Posco Holdings Inc
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Posco Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • 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
    • C21D8/0205—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
    • 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
    • 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
    • C21D8/0273—Final recrystallisation annealing
    • 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
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips 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
    • 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
    • C21D8/1277—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
    • C21D8/1283—Application of a separating or insulating coating
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations

Definitions

  • the present invention relates to a steel sheet having excellent wear resistance and composite corrosion resistance and a method for manufacturing the same. More particularly, the present invention relates to a steel sheet having corrosion resistance to a phenomenon in which a steel sheet corrodes, due to sulfate acid/hydrochloric acid composite condensate water and sulfuric acid condensate water produced by SO x , Cl, and the like present in exhaust gas after fossil fuel combustion when an exhaust gas temperature is lowered, high strength, and excellent wear resistance, and a method for manufacturing the same.
  • Fossil fuel includes various impurity elements such as S and Cl. Since combustion is performed using the fossil fuel, there is always a problem in that piping which is a passage through which combustion gas passes and equipment are deteriorated by corrosion. The corrosion phenomenon is referred to as condensate water corrosion, and representative uses where piping and equipment are exposed to the corrosion environment are exhaust gas piping and environmental facilities of thermal power plants, automobile exhaust system, and the like.
  • the present invention has been made in an effort to provide a steel sheet having excellent wear resistance and composite corrosion resistance, and a method for manufacturing the same.
  • a steel sheet having corrosion resistance to a phenomenon in which a steel sheet corrodes, due to sulfate acid/hydrochloric acid composite condensate water and sulfuric acid condensate water produced by SO x , Cl, and the like present in exhaust gas after fossil fuel combustion when an exhaust gas temperature is lowered, high strength, and excellent wear resistance, and a method for manufacturing the same are provided.
  • An exemplary embodiment of the present invention provides a corrosion-resistant steel sheet including, by weight: 0.04 to 0.10% of carbon (C), 0.1% or less (excluding 0%) of silicon (Si), 0.20 to 0.35% of copper (Cu), 0.1 to 0.2% of nickel (Ni), 0.05 to 0.15% of antimony (Sb), 0.07 to 0.22% of tin (Sn), 0.05 to 0.15% of titanium (Ti), 0.01% or less (excluding 0%) of sulfur (S), and 0.005% or less (excluding 0%) of nitrogen (N), with a remainder of iron (Fe) and unavoidable impurities, the corrosion-resistant steel sheet satisfying the following Formulae 1 and 2:
  • the corrosion-resistant steel sheet includes a TiC precipitate, and the TiC precipitate and an aggregate formed of the TiC precipitate may be included at 10 16 per 1 cm 3 .
  • the TiC precipitate may have a particle diameter of 1 to 10 nm.
  • the corrosion-resistant steel sheet may further satisfy the following Formula 3:
  • [Sn], [Sb], and [Cu] represent contents (wt %) of Sn, Sb, and Cu in the steel sheet, respectively.
  • a concentrated layer may be formed on the surface of the steel sheet.
  • the concentrated layer may include Cu, Sb, and Sn.
  • the concentrated layer may have a concentrated amount of 15 wt % or more.
  • the concentrated amount refers to the sum of the contents (wt %) of concentrating elements Mo, Cu, Sb, and Sn, at a boundary point at which the wt % of Fe and O are the same.
  • the concentrated layer may have a thickness of 10 nm or more.
  • the hot rolled steel sheet may have a tensile strength of 550 MPa or more and a surface hardness of 85 or more based on HRB.
  • the cold rolled steel sheet may have a tensile strength of 500 MPa or more and a surface hardness of 80 or more based on HRB.
  • winding the hot rolled steel sheet at 450 to 750° C.; cold rolling the wound hot rolled steel sheet to a reduction rate of 54 to 70% to manufacture a cold rolled steel sheet; and subjecting the cold rolled steel sheet to an annealing heat treatment at 750 to 880° C. may be further included.
  • a residence time may be 150 minutes or more.
  • FIG. 2 is photographs in which (a) a crack occurrence tendency in a hot rolled edge portion after hot rolling Inventive Example 4 under Condition 1 and (b) a crack occurrence tendency in a hot rolled edge portion after hot rolling Inventive Example 4 under Condition 2 are compared.
  • the part when it is mentioned that a part is present “on” the other part, the part may be present directly on the other part, or another part may be involved between them. In contrast, when it is mentioned that a part is present “directly on” the other part, there is no part interposed between them.
  • the inventors of the present invention confirmed that when an element to form precipitates such as Ti is added to a common medium-low carbon steel sheet, in the case of using appropriate manufacturing conditions in the manufacturing process, the hardness and the strength of a hot rolled material which is an intermediate material and a cold rolled material which is a final material may be greatly increased.
  • the corrosion-resistant steel sheet may further satisfy the following Formula 3:
  • [Sn], [Sb], and [Cu] represent contents (wt %) of Sn, Sb, and Cu in the steel sheet, respectively.
  • a carbon content in a low-carbon steel sheet may be 0.04 to 0.10 wt %.
  • a silicon content in the low-carbon steel sheet may be 0.1 wt % or less.
  • the Si content in a steel is too high, a large amount of red scale may be caused by a composite phase shape of SiO 2 and Fe oxides on the surface. Therefore, the Si content may be in the range above for overcoming the surface defects. More specifically, it may be 0.05 wt % or less. More specifically, it may be 0.01 to 0.05 wt %.
  • Cu is a representative element which is, in the case of corrosion in an acid immersion environment, concentrated between the surface of a steel material and a corrosion product to prevent further corrosion. In order to show the effect, an appropriate amount of Cu may be added. However, when added too much, cracks may be caused in the manufacture due to the low melting point of Cu.
  • Nickel(Ni) 0.1% to 0.2 wt %
  • Ni is added for the purpose of raising the melting point with the addition to limit occurrence of cracks.
  • a Ni content is too low, it does not sufficiently serve to raise the melting point of Cu, and on the contrary, when the Ni content is too high, surface defects due to Ni may occur. More specifically, the Ni content may be 0.11 to 0.19 wt %.
  • Sb is added for forming a stable concentrated layer on the surface, like Cu.
  • a sufficient concentrated layer may not be formed.
  • surface cracks may be caused.
  • Sn is added for forming a stable concentrated layer on the surface like Cu and Sb.
  • Sn is first dissolved in an acid immersion environment such as sulfuric acid to serve to greatly improve steel type corrosion resistance. More specifically, though it is not clear, it is considered that Sn improves steel type corrosion resistance by the following mechanism.
  • Sn and Cu are dissolved, and Sn is dissolved before Cu.
  • Sn is dissociated in the solution. The dissociated Sn lowers corrosion potential of the solution, thereby partially delaying a corrosion phenomenon of the steel sheet.
  • a corrosion potential refers to a potential to a combination electrode (reference electrode) of metal undergoing corrosion.
  • a corrosion delay layer may be formed in a process in which dissolved Sn is fused again on the surface of the steel sheet, and it is considered that the corrosion delay layer may delay corrosion of the steel sheet.
  • Sn is included too little, a sufficient concentrated layer may not be formed.
  • Sn is added too much, serious surface cracks may be caused in the production process. More specifically, the Sn content may be 0.073 to 0.22 wt %.
  • Cu, Sb, and Sn are elements which form a concentrated layer on the surface of the steel sheet under a sulfuric acid/hydrochloric acid composite condensation atmosphere or a sulfuric acid condensation atmosphere, and the relationship of Formula 3 as well as appropriate contents of each element may be satisfied. When the value of Formula 3 is too low, a sufficient concentrated layer may not be formed.
  • [Sn], [Sb], and [Cu] represent contents (wt %) of Sn, Sb, and Cu in the steel sheet, respectively. More specifically, Formula 3 may be 15 to 26. More specifically, Formula 3 may be 15.2 to 23.44.
  • Ti acts as an element which forms precipitates and is added for increasing the strength and the wear resistance of the steel sheet. That is, Ti is bonded to C to form a TiC precipitate. TiC is a fine precipitate, may improve the hardness and the wear resistance of a steel sheet due to precipitation strengthening, and also, may increase strength. In this regard, the details of TiC will be described later.
  • a Ti content is too low, precipitates are not sufficiently formed to show no strength increase effect.
  • Ti content is too high, TiC is excessively formed to cause cracks in rolling, and Ti and Al-based composite oxides are formed in a steelmaking step to block a tundish nozzle to cause manufacturing defects and surface defects. Therefore, Ti may be included, more specifically, at 0.05 to 0.145 wt %. More specifically, Ti may be included at 0.052 to 0.145 wt %.
  • the present invention is characterized by increasing wear resistance by precipitation hardening by TiC precipitate formation, but since TiS is formed before TiC is formed, the more S content interferes with the formation of TiC. Therefore, the maximum component range may be the range described above. More specifically, it may be 0.0097 wt % or less. More specifically, it may be 0.001 to 0.0097 wt %.
  • N may cause a reverse effect of limiting a Ti content effective for forming a Ti carbide.
  • the present invention is characterized by increasing wear resistance by precipitation hardening by TiC precipitate formation, but since TiN is formed before TiC is formed, the more N content interferes with the formation of TiC.
  • the range of the maximum component may be in the above range. More specifically, it may be 0.004 wt % or less. More specifically, it may be 0.001 to 0.004 wt %.
  • the effective Ti(Ti*) content may be calculated by Formula 2. Even in the case in which the component ranges of S and N are satisfied, when the range of Formula 2 is not satisfied, sufficient TiC may not be formed to cause drop in strength.
  • [Ti], [S], and [N] represent contents (wt %) of Ti, S, and N in the steel sheet, respectively. More specifically, the range of Formula 2 may be 0.04 to 0.12.
  • steel sheet may further include manganese (Mn) and aluminum (Al).
  • Mn serves to improve strength by solid solution strengthening in a steel, but when the content is too excessive, coarse MnS is formed to rather deteriorate strength. Therefore, it is preferred that the Mn content in the present invention is limited to 0.5 to 1.5 wt %.
  • Al is an element which is inevitably added in the manufacture of an aluminum-killed steel, and it is preferred to add Al in an appropriate content for a deoxidation effect.
  • the Al content is more than 0.02 wt %, surface defects of the steel sheet are more likely to be caused, and weldability may be reduced. Therefore, in the present invention, it is preferred to limit the Al content to 0.02 to 0.05 wt %.
  • the present invention includes Fe and unavoidable impurities. Since the unavoidable impurities are well known in the art, detailed description thereof will be omitted. In an exemplary embodiment of the present invention, addition of effective components other than the above components is not excluded, and when an additional component is further included, it is included by replacing the remainder Fe.
  • the corrosion-resistant steel sheet according to an exemplary embodiment of the present invention is characterized by having excellent wear resistance, and may include a TiC precipitate in this regard.
  • the TiC precipitate and the aggregate formed of the TiC precipitate are fine precipitates and may improve the hardness and the wear resistance of a steel sheet due to precipitation strengthening, and also, may increase strength.
  • the TiC precipitate and the aggregate formed of a plurality of TiC precipitate may be included at 10 16 per 1 cm 3 .
  • the strength and the wear resistance to be desired may not be secured. More specifically, they may be included at 10 16 to 10 18 per 1 cm 3 .
  • the TiC precipitate may have a spherical shape.
  • the TiC precipitate may have a particle diameter of 1 to 10 nm.
  • the precipitates interfere with movement of potential inside a steel material and form a potential band to increase strength, and when the particle diameter of the precipitates is too small, potential may easily move so that there is no effect of strength increase, but when the particle diameter of the precipitates is too large, potential cuts and passes through the precipitates to facilitate movement, and thus, the effect of strength increase is also deteriorated.
  • the particle diameter of the TiC precipitate may be 2 to 10 nm. More specifically, it may be 2 to 8 nm.
  • a particle diameter refers to a diameter of a sphere, when the sphere having the same volume as the particle is assumed.
  • the TiC precipitate may be uniformly distributed in the steel sheet.
  • Cu, Sb, Sn, and the like form a concentrated layer under a sulfuric acid/hydrochloric acid composite condensate atmosphere or a sulfuric acid condensation atmosphere, which suppresses additional corrosion.
  • the concentrated layer may be produced on the surface of the steel sheet.
  • the concentrated layer may be produced on the surface of the steel sheet. More specifically, when the steel sheet is immersed therein for 4 to 8 hours, the concentrated layer may be produced.
  • the concentrated layer refers to a layer in which Cu, Sb, and Sn start to be concentrated, and on the other hand, it is generally similar to the point at which oxidation starts.
  • the concentrated layer in the present invention refers to a layer in which the total amount of Cu, Sb, and Sn is more than 4 times the total amount of Cu, Sb, and Sn of the steel sheet.
  • the concentrated layer may be an amorphous concentrated layer.
  • the concentrated layer is produced with the formation of a corrosive layer when immersed in an acid.
  • the corrosive layer refers to a layer in which Fe is oxidized by O.
  • Fe is oxidized before Cu and Sb, and when immersed in an acid, Fe is dissociated into a Fe ion and escapes into an acid solution, but Cu and Sb are stable in a solid state and remain on the surface. Therefore, though the acid reaction continues and a Fe content reduction continuously occurs on the surface of the steel sheet, Cu and Sb remain on the surface to form a high concentration layer. This is produced on the surface in the form of a concentrated layer after a certain reaction time, and the concentrated layer prevents a direct contact between an acid and interior iron to suppress further corrosion.
  • the concentrated layer may include Cu, Sb, and Sn, and the concentrated amount of the concentrated layer may be 15 wt % or more.
  • the concentrated amount refers to the sum of the contents (wt %) of concentrating element Mo, Cu, Sb, and Sn, at a boundary point at which the wt % of Fe and O are the same. That is, it refers to the sum of the contents (wt %) of concentrating elements Cu, Sb, and Sn, at a boundary point at which the contents (wt %) of Fe and O are the same.
  • the concentrated amount is too small, the concentrated layer is not sufficiently formed to increase a corrosion weight loss ratio. More specifically, it may be 15% to 22%.
  • the content of each concentrating element at the point at which the contents (wt %) of Fe and O are the same in the concentrated layer may be 10 to 15 wt % of Cu, 1 to 3 wt % of Sb, and 1 to 3 wt % of Sn.
  • the concentrated layer may have a thickness of 10 nm or more. More specifically, the concentrated layer may be formed at a thickness of 10 to 500 nm. When the concentrated layer is too thin, it is difficult to serve to prevent corrosion as described above. When the concentrated layer is formed to be too thick, cracks occur inside the concentrated layer, so that an acid may penetrate along the cracks to cause corrosion. More specifically, the concentrated layer may be formed at a thickness of 12 to 100 nm.
  • the corrosion-resistant steel sheet according to an exemplary embodiment of the present invention may be a hot rolled steel sheet or a cold rolled steel sheet.
  • the steel sheet may have a thickness of 2.5 to 5.5 mm. More specifically, the thickness may be 3.5 to 5.5 mm.
  • the steel sheet may have a thickness of 1.0 to 2.5 mm. More specifically, the thickness may be 1.0 to 2.0 mm.
  • a recrystallization fraction after subjecting the steel sheet to an annealing heat treatment may be 80% or more. More specifically, the recrystallization fraction may be 100%.
  • the recrystallization fraction refers to an area of grains which is recrystallized based on the total steel sheet area.
  • a corrosion weight loss ratio may be 1.0 mg/cm 2 /hr or less.
  • the corrosion weight loss ratio may be 25 mg/cm 2 /hr or less.
  • the corrosion-resistant steel sheet according to an exemplary embodiment of the present invention is a hot rolled steel sheet
  • the hot rolled steel sheet may have a tensile strength of 550 MPa or more and a surface hardness of 85 or more based on HRB.
  • the corrosion-resistant steel sheet according to an exemplary embodiment of the present invention is a cold rolled steel sheet
  • the cold rolled steel sheet may have a tensile strength of 500 MPa or more and a surface hardness of 80 or more based on HRB.
  • a method for manufacturing a corrosion-resistant steel sheet includes: preparing a steel slab which includes, by weight: 0.04 to 0.10% of carbon (C), 0.1% or less (excluding 0%) of silicon (Si), 0.20 to 0.35% of copper (Cu), 0.1 to 0.2% of nickel (Ni), 0.05 to 0.15% of antimony (Sb), 0.07 to 0.22% of tin (Sn), 0.05 to 0.15% of titanium (Ti), 0.01% or less (excluding 0%) of sulfur (S), and 0.005% or less (excluding 0%) of nitrogen (N), with a remainder of iron (Fe) and unavoidable impurities, and satisfies the following Formulae 1 and 2; heating the slab at 1,200° C. or higher; and hot rolling the heated slab at a finish rolling temperature of 850 to 1000° C. to manufacture a hot rolled steel sheet:
  • winding the hot rolled steel sheet at 450 to 750° C.; cold rolling the wound hot rolled steel sheet to a reduction rate of 54 to 70% to manufacture a cold rolled steel sheet, and subjecting the cold rolled steel sheet to an annealing heat treatment at 750 to 880° C. may be further included.
  • a slab satisfying the composition described above is heated. Since the reason that the addition ratio of each composition in the slab is limited is the same as the reason of limiting the composition of the steel sheet described above, repeated description will be omitted. Since the composition of the slab is substantially not changed in the manufacturing process such as hot rolling, winding, pickling, cold rolling, and annealing, as described later, the composition of the slab and the composition of the finally manufactured corrosion-resistant steel sheet is substantially the same.
  • the slab By heating the slab, a subsequent hot rolling process is performed well, and the slab may be homogenized. More specifically, the heating may refer to reheating.
  • a slab heating temperature may be 1,200° C. or higher. The reason that the heating temperature of the slab is in the above range is for sufficient Ti re-solid solution. When Ti is sufficiently re-solid solubilized, the TiC precipitate is precipitated later.
  • a residence time in the slab heating may be 150 minutes or more. When the residence time is too short, re-solid solution of Ti may not sufficiently occur.
  • a finish rolling temperature of the hot rolling may be 850 to 1000° C.
  • the hot rolled plate may have a thickness of 2.5 to 5.5 mm.
  • a step of winding the hot rolled steel sheet may be included.
  • the step of winding the hot rolled steel sheet may be performed at 450 to 750° C.
  • the winding temperature is too low, final cold rolling may be difficult due to an increase of the initial strength of the hot rolled material, and on the contrary, when the winding temperature is too high, buckling may occur and strength may be lowered due to the phase transformation in a winding section.
  • a step of pickling the wound hot rolled steel sheet may be included.
  • a step of cold rolling the wound hot rolled steel sheet at a reduction rate of 54 to 70% to manufacture a cold rolled steel sheet may be included.
  • the reduction rate is too low, it may be difficult to secure complete recrystallization in the cold rolling, which causes a decrease in elongation of materials, and cracks in later customer processing.
  • rolling may not be performed by a motor load in the rolling process.
  • a step of subjecting the cold rolled steel sheet to an annealing heat treatment at 750 to 880° C. may be included.
  • the annealing heat treatment temperature is too low, it may be difficult to secure complete recrystallization, which causes a decrease in elongation of materials, and cracks in later customer processing.
  • the annealing heat treatment temperature is too high, it is difficult to secure the strength of the steel sheet.
  • the slab was heated at 1250° C. for 200 minutes, and then hot rolled to a thickness of 3.5 mm, thereby manufacturing a hot rolled plate.
  • a finish rolling temperature (FDT) was 920° C., and winding was performed at 650° C.
  • an immersion test was performed by the method described in the standard of ASTM G31.
  • the immersion test was performed by a method of preparing 50 wt % of an aqueous sulfuric acid solution and performing immersion at 70° C. for 6 hours. After the immersion, the steel sheet was washed by the specimen surface washing method of ASTM G1, and a weight loss was measured to measure weight losses per unit time and per unit surface.
  • a mixed aqueous solution of 28.5 wt % of a sulfuric acid solution and 0.5 wt % of a hydrochloric acid solution was prepared, and a test of immersion at 60° C. for 6 hours was performed. After the immersion, as described above, a weight loss after washing was measured by a specimen surface washing method of ASTM G1, and weight losses per unit time and per unit surface were measured.
  • the hot rolled plates of each of the inventive examples and the comparative examples were immersed in 50 wt % of a sulfuric acid solution at 70° C. for 24 hours, and then the specimen was measured for an element distribution from the surface to the inside by GDS measurement.
  • the thickness of the concentrated layer measured therefrom and the concentrated amount of the surface concentrating elements were measured and are shown in the following Table 2.
  • the concentrated layer refers to a layer in which Cu, Sb, and Sn starts to be concentrated, and on the other hand, is generally similar to the point at which oxidation starts.
  • the thickness of the concentrated layer was measured as the thickness of the layer in which the combined amount of Cu, Sb, and Sn is more than 4 times the combined amount of Cu, Sb, and Sn in the steel sheet.
  • FIG. 1 is a graph showing an element concentration degree of a surface portion of a steel sheet, by measuring an element distribution from the surface to the inside by GDS measurement, after the steel sheet of Inventive Example 2 was immersed in 50 wt % of a sulfuric acid solution for 24 hours.
  • the sum of the contents of Cu, Sb, and Sn of Inventive Example 2 was (0.26+0.1+0.15) and 0.51 wt %, and in the depth of 14 nm, the sum of the amounts of Cu, Sb, and Sn was more than 2.04 wt %, which is 4 times 0.51 wt %. Therefore, the depth, 14 nm was the thickness of the concentrated layer. (Red dotted line)
  • a boundary point at which Fe and O meets that is, the point at which the contents of Fe and O are the same corresponds to the blue dotted line (left) of FIG. 1 , and the concentrated amount which is the sum of Cu, Sb, and Sn in the layer was 17 wt %.
  • the concentrated amount refers to the sum of the contents (wt %) of concentrating elements Cu, Sb, and Sn at a point at which the contents (wt %) of Fe and O are the same.
  • Comparative Example 1 having a low C content, due to the reduced content of the TiC precipitate by the low C content, the tensile strength of the hot rolled material was lower than 550 MPa, and the surface hardness was low, and thus, strength and abrasiveness were not able to be secured.
  • the C content was excessively high as in Comparative Example 2, a phenomenon in which composite corrosion resistance was reduced due to the increased TiC precipitate was observed.
  • the content of Si was greatly lowered, and the reason is that it was confirmed that as the Si content was higher as in Comparative Example 3, red scale excessively occurred on the surface of the hot rolled material, leading to cracks.
  • Comparative Example 4 having a low Cu content, in particular, the corrosion resistance to a sulfuric acid alone was reduced, and in Comparative Example 5 in which the Cu content was excessively high, cracks in cast iron due to the liquefaction of Cu in the continuous casting process was confirmed.
  • the active addition of Ni serves to raise the melting point of Cu, and thus, it was confirmed that when a Ni/Cu ratio does not satisfy a certain ratio as in Comparative Example 6, cracks in cast iron occurred.
  • Condition 2 in which a hot finish rolling temperature (EDT) was high, edge cracks occurred in the hot rolling production process, and this was the same in Condition 4 having a low winding temperature (CT)
  • FIG. 2 is photographs in which (a) a crack occurrence tendency in a hot rolled edge portion after hot rolling Inventive Example 4 under Condition 1 and (b) a crack occurrence tendency in a hot rolled edge portion after hot rolling Inventive Example 4 under Condition 2 are compared
  • Condition 3 having a high hot finish rolling temperature (FDT) of 1050° C.
  • FDT hot finish rolling temperature
  • CT winding temperature
  • the steel type of the present invention has high contents of C and Ti and is characterized by a high recrystallization temperature after cold rolling, and under Condition 6 having a cold reduction rate of 53%, the recrystallization fraction of the final cold rolled material was about 70%, which did not form complete recrystallization, and in Condition 8 having an annealing temperature was 740° C. which was low also, the recrystallization fraction was 65%, which did not form complete recrystallization.
  • the material which did not undergo complete recrystallization may cause cracks in the customer processing due to a lowered elongation, and thus, in the present invention, when it is used as a cold rolling material, the reduction rate was limited to 54% or more and the annealing temperature was limited to 750° C. or higher.
  • Condition 4 and Condition 7 in which the strength of the hot rolled material was high or the cold reduction rate was high, rolling was not performed by a motor loading in the rolling process, and thus, the final product was not able to be obtained.
  • the present invention is not limited to the implementations and/or the exemplary embodiments, but may be produced in various forms different from each other.
  • a person with ordinary skill in the art to which the present invention pertains will understand that the present invention may be carried out in other specific forms without changing the technical idea or the essential feature of the present invention. Therefore, the implementations and/or the exemplary embodiments described above should be understood to be illustrative in all respects, and not to be restrictive.

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Abstract

The present invention provides a steel sheet having excellent wear resistance and composite corrosion resistance, and a method for manufacturing same.
A corrosion-resistant steel sheet according to an embodiment of the present invention comprises, in wt %: 0.04 to 0.10% of carbon (C); 0.1% or less (excluding 0%) of silicon (Si); 0.20 to 0.35% of copper (Cu); 0.1% to 0.2% of nickel (Ni); 0.05 to 0.15% of antimony (Sb); 0.07 to 0.22% of tin (Sn); 0.05 to 0.15% of titanium (Ti); 0.01% or less (excluding 0%) of sulfur (S); 0.005% or less (excluding 0%) of nitrogen (N); the remainder iron (Fe); and unavoidable impurities, and satisfies formulas 1 and 2 below:

[Ni]/[Cu]≥0.5  [Formula 1]

48×([Ti]/48−[S]/32−[N]/14)≥0.04  [Formula 2]
    • wherein, in formulas 1 and 2, [Ni], [Cu], [Ti], [S], and [N] represent contents (wt %) of Ni, Cu, Ti, S, and N contained in the steel sheet, respectively.

Description

    TECHNICAL FIELD
  • The present invention relates to a steel sheet having excellent wear resistance and composite corrosion resistance and a method for manufacturing the same. More particularly, the present invention relates to a steel sheet having corrosion resistance to a phenomenon in which a steel sheet corrodes, due to sulfate acid/hydrochloric acid composite condensate water and sulfuric acid condensate water produced by SOx, Cl, and the like present in exhaust gas after fossil fuel combustion when an exhaust gas temperature is lowered, high strength, and excellent wear resistance, and a method for manufacturing the same.
    • BACKGROUND ART
  • Fossil fuel includes various impurity elements such as S and Cl. Since combustion is performed using the fossil fuel, there is always a problem in that piping which is a passage through which combustion gas passes and equipment are deteriorated by corrosion. The corrosion phenomenon is referred to as condensate water corrosion, and representative uses where piping and equipment are exposed to the corrosion environment are exhaust gas piping and environmental facilities of thermal power plants, automobile exhaust system, and the like. The kinds of condensate corrosion includes sulfuric acid condensate water corrosion in which S included in exhaust gas burns to form SOx, and in particular, SO3 meets moisture in the exhaust gas to form sulfuric acid, corrosion by hydrochloric acid condensate water in which chlorine included in exhaust gas or industrial water produces hydrochloric acid by various reactions, sulfuric acid/hydrochloric acid composite condensate water corrosion occurring when the sulfuric acid and the hydrochloric acid are mixed in combination, and the like. A starting temperature of the acid condensation is related to the temperature of the exhaust gas itself, contents of SOx and C in the exhaust gas, and a water vapor content.
  • In recent years, for the purpose of utilizing power generation efficiency or waste heat discharged to the outside in uses such as power plants, a demand to lower the exhaust gas temperature itself continues. In general, when the exhaust temperature is lowered to the temperature at which sulfuric acid starts to condense, sulfuric acid gas formed in the exhaust gas is liquefied and condensed on the surface of steel material to increase an amount to cause corrosion, and when the exhaust gas temperature is lowered to a lower temperature at which hydrochloric acid may be condensed, a composite corrosion phenomenon in which sulfuric acid and hydrochloric acid are condensed in combination occurs.
  • In addition, a study related to facility change for increasing desulfurization efficiency in thermal power plant environmental equipment continues. As a representative example, Gas Gas Heater (GGH) type which is a heat exchange device at a front/rear end of the desulfurization equipment is being changed. Conventional GGH is disposed at a rear end of an electrostatic precipitator (EP), and development of a steel material used herein was studied with a focus on corrosion resistance, but recently, in GGH, since a part of desulfurization equipment was disposed at a front end of the electrostatic precipitator, corrosion by steel material erosion by dusts which have not been removed, and also, corrosion from wear occur, and thus, for the steel material used in the equipment, a wear resistance problem should be solved in addition to a corrosion resistance problem.
  • As an example of a solution to the problem, there are a method of using a high alloy-based high corrosion-resistant steel such as Duplex-based stainless steel (STS) or a method of raising an exhaust gas temperature, but the methods cause high costs and a decrease in power generation efficiency. In addition, there was a movement to adopt a high-strength steel material, and this solves a strength problem, but may cause a problem of deterioration of other facilities due to the corrosion resistance problem.
  • Meanwhile, when a Cu-added corrosion-resistant steel known as a sulfuric acid-resistant condensed corrosion steel is used, a Cu concentrated layer produced on the surface of steel exhibits corrosion resistance to sulfuric acid condensation to form a corrosion suppression layer to suppress corrosion, and an effect of greatly improving an equipment life is exhibited, for the preparation of the case of using a general steel. However, a lower temperature of the exhaust gas, complexity of the corrosion environment, and requirement of wear resistance, as mentioned above lower the corrosion resistance characteristics to sulfuric acid-resistant condensed corrosion steel, and thus, there has been a demand for a corrosion-resistant steel having better performance.
  • Further, there has been a problem in that its original performance was not exhibited under complex and harsh corrosion-resistant environments with a conventional sulfuric acid-resistant condensed corrosion steel or a high-alloy stainless steel.
    • DISCLOSURE
  • The present invention has been made in an effort to provide a steel sheet having excellent wear resistance and composite corrosion resistance, and a method for manufacturing the same.
  • More specifically, a steel sheet having corrosion resistance to a phenomenon in which a steel sheet corrodes, due to sulfate acid/hydrochloric acid composite condensate water and sulfuric acid condensate water produced by SOx, Cl, and the like present in exhaust gas after fossil fuel combustion when an exhaust gas temperature is lowered, high strength, and excellent wear resistance, and a method for manufacturing the same are provided.
  • An exemplary embodiment of the present invention provides a corrosion-resistant steel sheet including, by weight: 0.04 to 0.10% of carbon (C), 0.1% or less (excluding 0%) of silicon (Si), 0.20 to 0.35% of copper (Cu), 0.1 to 0.2% of nickel (Ni), 0.05 to 0.15% of antimony (Sb), 0.07 to 0.22% of tin (Sn), 0.05 to 0.15% of titanium (Ti), 0.01% or less (excluding 0%) of sulfur (S), and 0.005% or less (excluding 0%) of nitrogen (N), with a remainder of iron (Fe) and unavoidable impurities, the corrosion-resistant steel sheet satisfying the following Formulae 1 and 2:

  • [Ni]/[Cu]≥0.5  [Formula 1]

  • 48×([Ti]/48−[S]/32−[N]/14)≥0.04  [Formula 2]
  • wherein [Ni], [Cu], [Ti], [S], and [N] represent contents (wt %) of Ni, Cu, Ti, S, and N in the steel sheet, respectively.
  • The corrosion-resistant steel sheet includes a TiC precipitate, and the TiC precipitate and an aggregate formed of the TiC precipitate may be included at 1016 per 1 cm3.
  • The TiC precipitate may have a particle diameter of 1 to 10 nm.
  • The corrosion-resistant steel sheet may further satisfy the following Formula 3:

  • 12×[Sn]+22×[Sb]+50×[Cu]≥15  [Formula 3]
  • wherein [Sn], [Sb], and [Cu] represent contents (wt %) of Sn, Sb, and Cu in the steel sheet, respectively.
  • When the steel sheet is immersed in a mixed solution of 28.5 wt % of a sulfuric acid solution and 0.5 wt % of a hydrochloric acid solution at 40 to 80° C., a concentrated layer may be formed on the surface of the steel sheet.
  • When the steel sheet is immersed in 50 wt % of a sulfuric acid solution at 50 to 90° C., a concentrated layer may be produced on the surface of the steel sheet.
  • The concentrated layer may include Cu, Sb, and Sn.
  • The concentrated layer may have a concentrated amount of 15 wt % or more.
  • Here, the concentrated amount refers to the sum of the contents (wt %) of concentrating elements Mo, Cu, Sb, and Sn, at a boundary point at which the wt % of Fe and O are the same.
  • The concentrated layer may have a thickness of 10 nm or more.
  • A recrystallization fraction after subjecting the steel sheet to an annealing heat treatment may be 80% or more.
  • When the steel sheet is immersed in a mixed solution of 28.5 wt % of a sulfuric acid solution and 0.5 wt % of a hydrochloric acid solution at 60° C. for 6 hours, a corrosion weight loss ratio may be 1.0 mg/cm2/hr or less.
  • When the steel sheet is immersed in 50 wt % of a sulfuric acid solution at 70° C. for 6 hours, a corrosion weight loss ratio may be 25 mg/cm2/hr or less.
  • When the steel sheet is a hot rolled steel sheet, the hot rolled steel sheet may have a tensile strength of 550 MPa or more and a surface hardness of 85 or more based on HRB.
  • When the steel sheet is a cold rolled steel sheet, the cold rolled steel sheet may have a tensile strength of 500 MPa or more and a surface hardness of 80 or more based on HRB.
  • Another embodiment of the present invention provides a method for manufacturing a corrosion-resistant steel sheet including: preparing a steel slab which includes, by weight: 0.04 to 0.10% of carbon (C), 0.1% or less (excluding 0%) of silicon (Si), 0.20 to 0.35% of copper (Cu), 0.1 to 0.2% of nickel (Ni), 0.05 to 0.15% of antimony (Sb), 0.07 to 0.22% of tin (Sn), 0.05 to 0.15% of titanium (Ti), 0.01% or less (excluding 0%) of sulfur (S), and 0.005% or less (excluding 0%) of nitrogen (N), with a remainder of iron (Fe) and unavoidable impurities, and satisfies the following Formulae 1 and 2; heating the slab at 1,200° C. or higher; and hot rolling the heated slab at a finish rolling temperature of 850 to 1000° C. to manufacture a hot rolled steel sheet:

  • [Ni]/[Cu]≥0.5  [Formula 1]

  • 48×([Ti]/48−[S]/32−[N]/14)≥0.04  [Formula 2]
  • wherein [Ni], [Cu], [Ti], [S], and [N] represent contents (wt %) of Ni, Cu, Ti, S, and N in the steel sheet, respectively.
  • Meanwhile, after the step of manufacturing the hot rolled steel sheet, winding the hot rolled steel sheet at 450 to 750° C.; cold rolling the wound hot rolled steel sheet to a reduction rate of 54 to 70% to manufacture a cold rolled steel sheet; and subjecting the cold rolled steel sheet to an annealing heat treatment at 750 to 880° C., may be further included.
  • In addition, in the step of heating the slab at 1,200° C. or higher, a residence time may be 150 minutes or more.
  • The corrosion-resistant steel sheet according to an exemplary embodiment of the present invention may be useful for piping through which exhaust gas passes after combustion of fossil fuel, hot rolled products for fossil fuel combustion equipment, and raw materials of cold rolled products.
  • When the corrosion-resistant steel sheet according to an exemplary embodiment of the present invention is applied to Gas Gas heater (GGH) equipment, both wear resistance and composite corrosion resistance requirements may be met in spite of a large difference in environmental changes, regardless of whether the GGH equipment which is a heat exchange device used in a desulfurization equipment for thermal power plants is installed at a front end or a rear end of an electrostatic precipitator (EP).
    • DESCRIPTION OF THE DRAWINGS
  • FIG. 1 is a graph showing an element concentration degree of a surface portion of a steel sheet, by measuring an element distribution from the surface to the inside by GDS measurement, after the steel sheet of Inventive Example 2 was immersed in 50 wt % of a sulfuric acid solution for 24 hours.
  • FIG. 2 is photographs in which (a) a crack occurrence tendency in a hot rolled edge portion after hot rolling Inventive Example 4 under Condition 1 and (b) a crack occurrence tendency in a hot rolled edge portion after hot rolling Inventive Example 4 under Condition 2 are compared.
    •  MODE FOR INVENTION
  • In the present specification, the terms such as first, second, and third are used for describing various parts, components, areas, layers, and/or sections, but are not limited thereto. These terms are used only for distinguishing one part, component, area, layer, or section from other parts, components, areas, layers, or sections. Therefore, a first part, component, area, layer, or section described below may be mentioned as a second part, component, area, layer, or section without departing from the scope of the present invention.
  • In the present specification, when it is said that a portion “comprises” a constituent element, it means that other constituent elements may be further comprised rather than other constituent elements are excluded, unless otherwise stated to the contrary.
  • In the present specification, the terminology used herein is only for mentioning a certain example, and is not intended to limit the present invention. Singular forms used herein also include plural forms unless otherwise stated clearly to the contrary. The meaning of “comprising” used in the specification is embodying certain characteristics, regions, integers, steps, operations, and/or components, but is not excluding the presence or addition of other characteristics, regions, integers, steps, operations, and/or components.
  • In the present specification, the term “combination thereof” included in a Markush-type expression refers to a mixture or a combination of one or more selected from the group consisting of constituent elements described in a Markush-type expression, and refers to inclusion of one or more selected from the group consisting of the constituent elements.
  • In the present specification, when it is mentioned that a part is present “on” the other part, the part may be present directly on the other part, or another part may be involved between them. In contrast, when it is mentioned that a part is present “directly on” the other part, there is no part interposed between them.
  • Though not defined otherwise, all terms including technical terms and scientific terms used herein have the same meaning as commonly understood by a person with ordinary skill in the art to which the present invention pertain. Terms defined in commonly used dictionaries are further interpreted as having a meaning consistent with the related technical literatures and the currently disclosed description, and unless otherwise defined, they are not interpreted as having an ideal or very formal meaning.
  • In addition, unless otherwise particularly stated, % means wt %, and 1 ppm is 0.0001 wt %.
  • The meaning of further including an additional element in an exemplary embodiment of the present invention is including an additional element in place of iron (Fe) as a balance at the added amount of the additional element.
  • Hereinafter, an exemplary embodiment of the present invention will be described in detail so that a person with ordinary skill in the art to which the present invention pertains may easily practice the invention. However, the present invention may be implemented in various forms, and is not limited to the exemplary embodiments described herein.
  • The inventors of the present invention confirmed that when an element to form precipitates such as Ti is added to a common medium-low carbon steel sheet, in the case of using appropriate manufacturing conditions in the manufacturing process, the hardness and the strength of a hot rolled material which is an intermediate material and a cold rolled material which is a final material may be greatly increased.
  • That is, the inventors of the present invention confirmed that when the steel sheet is subjected to a sulfuric acid or a sulfuric acid/hydrochloric acid composite corrosive environment, precipitates are formed by a corrosive product produced depending on the kind and the contents of the element contained in the steel sheet, and a composite relation, but additional corrosion is inhibited.
  • Here, when two or more of Cu, Sb, Sn, and the like which are special component element are added in combination to the steel sheet, corrosion resistance both in high-concentration sulfuric acid and sulfuric acid/hydrochloric acid component condensation environments may be greatly improved, and thus, it was concluded that equipment corrosion resistance performance in a condensate water corrosion environment may be significantly increased.
  • When a corrosion reaction is performed on a low-carbon steel sheet using the principle, it was confirmed that a concentrated layer containing corrosion-resistant elements produced between a steel material and a corrosion product may be densely formed, and thus, it was found that the steel sheet manufactured therefrom has excellent corrosion resistance in an immersion corrosive environment.
  • Hereinafter, as an exemplary embodiment of the present invention, a steel sheet having excellent wear resistance and composite corrosion resistance, and a method for manufacturing the same will be described in detail.
  • A corrosion-resistant steel sheet according to an exemplary embodiment of the present invention includes, by weight: 0.04 to 0.10% of carbon (C), 0.1% or less (excluding 0%) of silicon (Si), 0.20 to 0.35% of copper (Cu), 0.1 to 0.2% of nickel (Ni), 0.05 to 0.15% of antimony (Sb), 0.07 to 0.22% of tin (Sn), 0.05 to 0.15% of titanium (Ti), 0.01% or less (excluding 0%) of sulfur (S), and 0.005% or less (excluding 0%) of nitrogen (N), with a remainder of iron (Fe) and unavoidable impurities, and satisfies the following Formulae 1 and 2:

  • [Ni]/[Cu]≥0.5  [Formula 1]

  • 48×([Ti]/48−[S]/32−[N]/14)≥0.04  [Formula 2]
  • wherein [Ni], [Cu], [Ti], [S], and [N] represent contents (wt %) of Ni, Cu, Ti, S, and N in the steel sheet, respectively.
  • Meanwhile, the corrosion-resistant steel sheet may further satisfy the following Formula 3:

  • 12×[Sn]+22×[Sb]+50×[Cu]≥15  [Formula 3]
  • wherein [Sn], [Sb], and [Cu] represent contents (wt %) of Sn, Sb, and Cu in the steel sheet, respectively.
  • First, the reasons why the components of the steel sheet, and Formulae 1, 2, and 3 are limited will be described.
  • Carbon (C): 0.04 to 0.10 wt %
  • A carbon content in a low-carbon steel sheet may be 0.04 to 0.10 wt %.
  • When a carbon content in a steel is too high, deterioration of corrosion resistance, in particular, deterioration of sulfuric acid/hydrochloric acid composite corrosion resistance may occur by excessive TiC formation and carbide formation. On the contrary, when the carbon content is too low, it may be impossible to secure the strength to be desired in the present invention. More specifically, it may be 0.042 to 0.10 wt %.
  • Silicon (Si): 0.1 wt % or Less (Excluding 0 wt %)
  • A silicon content in the low-carbon steel sheet may be 0.1 wt % or less. When the silicon content in a steel is too high, a large amount of red scale may be caused by a composite phase shape of SiO2 and Fe oxides on the surface. Therefore, the Si content may be in the range above for overcoming the surface defects. More specifically, it may be 0.05 wt % or less. More specifically, it may be 0.01 to 0.05 wt %.
  • Copper (Cu): 0.20 to 0.35 wt %
  • Cu is a representative element which is, in the case of corrosion in an acid immersion environment, concentrated between the surface of a steel material and a corrosion product to prevent further corrosion. In order to show the effect, an appropriate amount of Cu may be added. However, when added too much, cracks may be caused in the manufacture due to the low melting point of Cu.
  • Nickel(Ni): 0.1% to 0.2 wt %
  • When only Cu is added to a steel without Ni, liquid Cu may penetrate to a grain boundary due to the low melting point of Cu to cause cracks. Ni is added for the purpose of raising the melting point with the addition to limit occurrence of cracks. When a Ni content is too low, it does not sufficiently serve to raise the melting point of Cu, and on the contrary, when the Ni content is too high, surface defects due to Ni may occur. More specifically, the Ni content may be 0.11 to 0.19 wt %.

  • [Ni]/[Cu]≥0.5  [Formula 1]
  • For the same reason as adding Ni with Cu, Ni and Cu may be added in the above range, in order to appropriately increase a melting point and not to cause surface defects due to Ni. When the value of Formula 1 is too high, surface defects due to Ni may occur, and when the value of Formula 1 is too low, an effect of raising a melting point by Ni may be insignificant. In Formula 1, [Ni] and [Cu] represent contents (wt %) of Ni and Cu in the steel sheet, respectively.
  • Antimony (Sb): 0.05 to 0.15 wt %
  • Sb is added for forming a stable concentrated layer on the surface, like Cu. When the Sb content is too low, a sufficient concentrated layer may not be formed. On the contrary, when the Sb content is too high, surface cracks may be caused.
  • Tin (Sn): 0.07 to 0.22 wt %
  • Sn is added for forming a stable concentrated layer on the surface like Cu and Sb. In particular, it was confirmed that Sn is first dissolved in an acid immersion environment such as sulfuric acid to serve to greatly improve steel type corrosion resistance. More specifically, though it is not clear, it is considered that Sn improves steel type corrosion resistance by the following mechanism. When the steel sheet is under an immersion environment of sulfuric acid or composite acid, Sn and Cu are dissolved, and Sn is dissolved before Cu. As Sn is dissolved before Cu, Sn is dissociated in the solution. The dissociated Sn lowers corrosion potential of the solution, thereby partially delaying a corrosion phenomenon of the steel sheet. Here, a corrosion potential refers to a potential to a combination electrode (reference electrode) of metal undergoing corrosion. In addition, a corrosion delay layer may be formed in a process in which dissolved Sn is fused again on the surface of the steel sheet, and it is considered that the corrosion delay layer may delay corrosion of the steel sheet. When Sn is included too little, a sufficient concentrated layer may not be formed. When Sn is added too much, serious surface cracks may be caused in the production process. More specifically, the Sn content may be 0.073 to 0.22 wt %.

  • 12×[Sn]+22×[Sb]+50×[Cu]≥15  [Formula 3]
  • Cu, Sb, and Sn are elements which form a concentrated layer on the surface of the steel sheet under a sulfuric acid/hydrochloric acid composite condensation atmosphere or a sulfuric acid condensation atmosphere, and the relationship of Formula 3 as well as appropriate contents of each element may be satisfied. When the value of Formula 3 is too low, a sufficient concentrated layer may not be formed. In Formula 3, [Sn], [Sb], and [Cu] represent contents (wt %) of Sn, Sb, and Cu in the steel sheet, respectively. More specifically, Formula 3 may be 15 to 26. More specifically, Formula 3 may be 15.2 to 23.44.
  • Titanium (Ti): 0.05 to 0.15 wt %
  • Ti acts as an element which forms precipitates and is added for increasing the strength and the wear resistance of the steel sheet. That is, Ti is bonded to C to form a TiC precipitate. TiC is a fine precipitate, may improve the hardness and the wear resistance of a steel sheet due to precipitation strengthening, and also, may increase strength. In this regard, the details of TiC will be described later. Here, a Ti content is too low, precipitates are not sufficiently formed to show no strength increase effect. However, when the Ti content is too high, TiC is excessively formed to cause cracks in rolling, and Ti and Al-based composite oxides are formed in a steelmaking step to block a tundish nozzle to cause manufacturing defects and surface defects. Therefore, Ti may be included, more specifically, at 0.05 to 0.145 wt %. More specifically, Ti may be included at 0.052 to 0.145 wt %.
  • Sulfur (S): 0.01 wt % or Less (Excluding 0%)
  • S may cause a reverse effect of limiting a Ti content effective for forming a Ti carbide. The reason is that the present invention is characterized by increasing wear resistance by precipitation hardening by TiC precipitate formation, but since TiS is formed before TiC is formed, the more S content interferes with the formation of TiC. Therefore, the maximum component range may be the range described above. More specifically, it may be 0.0097 wt % or less. More specifically, it may be 0.001 to 0.0097 wt %.
  • Nitrogen (N): 0.005 wt % or Less (Excluding 0%)
  • N may cause a reverse effect of limiting a Ti content effective for forming a Ti carbide. The reason is that the present invention is characterized by increasing wear resistance by precipitation hardening by TiC precipitate formation, but since TiN is formed before TiC is formed, the more N content interferes with the formation of TiC. For reference, when Ti forms precipitates, they are formed in the order of TiN, TiS, and TiC. Therefore, the range of the maximum component may be in the above range. More specifically, it may be 0.004 wt % or less. More specifically, it may be 0.001 to 0.004 wt %.

  • 48×([Ti]/48−[S]/32−[N]/14)≥0.04  [Formula 2]
  • The effective Ti(Ti*) content may be calculated by Formula 2. Even in the case in which the component ranges of S and N are satisfied, when the range of Formula 2 is not satisfied, sufficient TiC may not be formed to cause drop in strength. Here, in Formula 2, [Ti], [S], and [N] represent contents (wt %) of Ti, S, and N in the steel sheet, respectively. More specifically, the range of Formula 2 may be 0.04 to 0.12.
  • In addition, the steel sheet may further include manganese (Mn) and aluminum (Al).
  • Manganese (Mn): 0.5 to 1.5 wt %
  • Mn serves to improve strength by solid solution strengthening in a steel, but when the content is too excessive, coarse MnS is formed to rather deteriorate strength. Therefore, it is preferred that the Mn content in the present invention is limited to 0.5 to 1.5 wt %.
  • Aluminum (Al): 0.02 to 0.05 wt %
  • Al is an element which is inevitably added in the manufacture of an aluminum-killed steel, and it is preferred to add Al in an appropriate content for a deoxidation effect. However, the Al content is more than 0.02 wt %, surface defects of the steel sheet are more likely to be caused, and weldability may be reduced. Therefore, in the present invention, it is preferred to limit the Al content to 0.02 to 0.05 wt %.
  • In addition to the components, the present invention includes Fe and unavoidable impurities. Since the unavoidable impurities are well known in the art, detailed description thereof will be omitted. In an exemplary embodiment of the present invention, addition of effective components other than the above components is not excluded, and when an additional component is further included, it is included by replacing the remainder Fe.
  • Meanwhile, the corrosion-resistant steel sheet according to an exemplary embodiment of the present invention is characterized by having excellent wear resistance, and may include a TiC precipitate in this regard. The TiC precipitate and the aggregate formed of the TiC precipitate are fine precipitates and may improve the hardness and the wear resistance of a steel sheet due to precipitation strengthening, and also, may increase strength.
  • The TiC precipitate and the aggregate formed of a plurality of TiC precipitate may be included at 1016 per 1 cm3. When the precipitate content is too low, the strength and the wear resistance to be desired may not be secured. More specifically, they may be included at 1016 to 1018 per 1 cm3.
  • The TiC precipitate may have a spherical shape.
  • The TiC precipitate may have a particle diameter of 1 to 10 nm. The precipitates interfere with movement of potential inside a steel material and form a potential band to increase strength, and when the particle diameter of the precipitates is too small, potential may easily move so that there is no effect of strength increase, but when the particle diameter of the precipitates is too large, potential cuts and passes through the precipitates to facilitate movement, and thus, the effect of strength increase is also deteriorated. More specifically, the particle diameter of the TiC precipitate may be 2 to 10 nm. More specifically, it may be 2 to 8 nm. Here, a particle diameter refers to a diameter of a sphere, when the sphere having the same volume as the particle is assumed.
  • In addition, the TiC precipitate may be uniformly distributed in the steel sheet.
  • Meanwhile, on the corrosion-resistant steel sheet according to an exemplary embodiment of the present invention, Cu, Sb, Sn, and the like form a concentrated layer under a sulfuric acid/hydrochloric acid composite condensate atmosphere or a sulfuric acid condensation atmosphere, which suppresses additional corrosion. More specifically, when the steel sheet is immersed in a mixed solution of 28.5 wt % of a sulfuric acid solution and 0.5 wt % of a hydrochloric acid solution at 40 to 80° C., the concentrated layer may be produced on the surface of the steel sheet. In addition, when the steel sheet is immersed in 50 wt % of a sulfuric acid solution at 50 to 90° C., the concentrated layer may be produced on the surface of the steel sheet. More specifically, when the steel sheet is immersed therein for 4 to 8 hours, the concentrated layer may be produced.
  • Here, the concentrated layer refers to a layer in which Cu, Sb, and Sn start to be concentrated, and on the other hand, it is generally similar to the point at which oxidation starts. The concentrated layer in the present invention refers to a layer in which the total amount of Cu, Sb, and Sn is more than 4 times the total amount of Cu, Sb, and Sn of the steel sheet.
  • In addition, the concentrated layer may be an amorphous concentrated layer.
  • The concentrated layer is produced with the formation of a corrosive layer when immersed in an acid. Here, the corrosive layer refers to a layer in which Fe is oxidized by O. In general, Fe is oxidized before Cu and Sb, and when immersed in an acid, Fe is dissociated into a Fe ion and escapes into an acid solution, but Cu and Sb are stable in a solid state and remain on the surface. Therefore, though the acid reaction continues and a Fe content reduction continuously occurs on the surface of the steel sheet, Cu and Sb remain on the surface to form a high concentration layer. This is produced on the surface in the form of a concentrated layer after a certain reaction time, and the concentrated layer prevents a direct contact between an acid and interior iron to suppress further corrosion.
  • The concentrated layer may include Cu, Sb, and Sn, and the concentrated amount of the concentrated layer may be 15 wt % or more. Here, the concentrated amount refers to the sum of the contents (wt %) of concentrating element Mo, Cu, Sb, and Sn, at a boundary point at which the wt % of Fe and O are the same. That is, it refers to the sum of the contents (wt %) of concentrating elements Cu, Sb, and Sn, at a boundary point at which the contents (wt %) of Fe and O are the same. When the concentrated amount is too small, the concentrated layer is not sufficiently formed to increase a corrosion weight loss ratio. More specifically, it may be 15% to 22%.
  • The content of each concentrating element at the point at which the contents (wt %) of Fe and O are the same in the concentrated layer may be 10 to 15 wt % of Cu, 1 to 3 wt % of Sb, and 1 to 3 wt % of Sn.
  • The concentrated layer may have a thickness of 10 nm or more. More specifically, the concentrated layer may be formed at a thickness of 10 to 500 nm. When the concentrated layer is too thin, it is difficult to serve to prevent corrosion as described above. When the concentrated layer is formed to be too thick, cracks occur inside the concentrated layer, so that an acid may penetrate along the cracks to cause corrosion. More specifically, the concentrated layer may be formed at a thickness of 12 to 100 nm.
  • The corrosion-resistant steel sheet according to an exemplary embodiment of the present invention may be a hot rolled steel sheet or a cold rolled steel sheet.
  • In the case of the hot rolled steel sheet, the steel sheet may have a thickness of 2.5 to 5.5 mm. More specifically, the thickness may be 3.5 to 5.5 mm.
  • In the case of the cold rolled steel sheet, the steel sheet may have a thickness of 1.0 to 2.5 mm. More specifically, the thickness may be 1.0 to 2.0 mm.
  • When the corrosion-resistant steel sheet according to an exemplary embodiment of the present invention is a cold rolled steel sheet, a recrystallization fraction after subjecting the steel sheet to an annealing heat treatment may be 80% or more. More specifically, the recrystallization fraction may be 100%. When the recrystallization fraction is too low, the strength is increased, but ductility is rapidly decreased, and thus, defects are formed in the customer processing. Here, the recrystallization fraction refers to an area of grains which is recrystallized based on the total steel sheet area.
  • When the corrosion-resistant steel sheet according to an exemplary embodiment of the present invention is immersed in a mixed solution of 28.5 wt % of a sulfuric acid solution and 0.5 wt % of a hydrochloric acid at 60° C. for 6 hours, a corrosion weight loss ratio may be 1.0 mg/cm2/hr or less.
  • When the corrosion-resistant steel sheet according to an exemplary embodiment of the present invention is immersed in 50 wt % of a sulfuric acid solution at 70° C. for 6 hours, the corrosion weight loss ratio may be 25 mg/cm2/hr or less.
  • When the corrosion-resistant steel sheet according to an exemplary embodiment of the present invention is a hot rolled steel sheet, the hot rolled steel sheet may have a tensile strength of 550 MPa or more and a surface hardness of 85 or more based on HRB.
  • When the corrosion-resistant steel sheet according to an exemplary embodiment of the present invention is a cold rolled steel sheet, the cold rolled steel sheet may have a tensile strength of 500 MPa or more and a surface hardness of 80 or more based on HRB.
  • A method for manufacturing a corrosion-resistant steel sheet according to an exemplary embodiment of the present invention includes: preparing a steel slab which includes, by weight: 0.04 to 0.10% of carbon (C), 0.1% or less (excluding 0%) of silicon (Si), 0.20 to 0.35% of copper (Cu), 0.1 to 0.2% of nickel (Ni), 0.05 to 0.15% of antimony (Sb), 0.07 to 0.22% of tin (Sn), 0.05 to 0.15% of titanium (Ti), 0.01% or less (excluding 0%) of sulfur (S), and 0.005% or less (excluding 0%) of nitrogen (N), with a remainder of iron (Fe) and unavoidable impurities, and satisfies the following Formulae 1 and 2; heating the slab at 1,200° C. or higher; and hot rolling the heated slab at a finish rolling temperature of 850 to 1000° C. to manufacture a hot rolled steel sheet:

  • [Ni]/[Cu]≥0.5  [Formula 1]

  • 48×([Ti]/48−[S]/32−[N]/14)≥0.04  [Formula 2]
  • wherein [Ni], [Cu], [Ti], [S], and [N] represent contents (wt %) of Ni, Cu, Ti, S, and N in the steel sheet, respectively.
  • In addition, after the step of manufacturing the hot rolled steel sheet, winding the hot rolled steel sheet at 450 to 750° C.; cold rolling the wound hot rolled steel sheet to a reduction rate of 54 to 70% to manufacture a cold rolled steel sheet, and subjecting the cold rolled steel sheet to an annealing heat treatment at 750 to 880° C., may be further included.
  • Hereinafter, each step will be described in detail.
  • First, a slab satisfying the composition described above is heated. Since the reason that the addition ratio of each composition in the slab is limited is the same as the reason of limiting the composition of the steel sheet described above, repeated description will be omitted. Since the composition of the slab is substantially not changed in the manufacturing process such as hot rolling, winding, pickling, cold rolling, and annealing, as described later, the composition of the slab and the composition of the finally manufactured corrosion-resistant steel sheet is substantially the same.
  • By heating the slab, a subsequent hot rolling process is performed well, and the slab may be homogenized. More specifically, the heating may refer to reheating. Here, a slab heating temperature may be 1,200° C. or higher. The reason that the heating temperature of the slab is in the above range is for sufficient Ti re-solid solution. When Ti is sufficiently re-solid solubilized, the TiC precipitate is precipitated later.
  • Meanwhile, a residence time in the slab heating may be 150 minutes or more. When the residence time is too short, re-solid solution of Ti may not sufficiently occur.
  • Next, the heated slab is hot rolled to manufacture a hot rolled steel sheet. A finish rolling temperature of the hot rolling may be 850 to 1000° C. When the finish rolling temperature is too low, sufficiently rolling ability may not be exhibited, and on the contrary, when the finish rolling temperature is too high, it may be difficult to secure the strength of the steel sheet. Here, the hot rolled plate may have a thickness of 2.5 to 5.5 mm.
  • Next, a step of winding the hot rolled steel sheet may be included. The step of winding the hot rolled steel sheet may be performed at 450 to 750° C. When the winding temperature is too low, final cold rolling may be difficult due to an increase of the initial strength of the hot rolled material, and on the contrary, when the winding temperature is too high, buckling may occur and strength may be lowered due to the phase transformation in a winding section.
  • Thereafter, a step of pickling the wound hot rolled steel sheet may be included.
  • Next, a step of cold rolling the wound hot rolled steel sheet at a reduction rate of 54 to 70% to manufacture a cold rolled steel sheet may be included. When the reduction rate is too low, it may be difficult to secure complete recrystallization in the cold rolling, which causes a decrease in elongation of materials, and cracks in later customer processing. However, when the reduction rate is too high, rolling may not be performed by a motor load in the rolling process.
  • Next, a step of subjecting the cold rolled steel sheet to an annealing heat treatment at 750 to 880° C. may be included. When the annealing heat treatment temperature is too low, it may be difficult to secure complete recrystallization, which causes a decrease in elongation of materials, and cracks in later customer processing. However, when the annealing heat treatment temperature is too high, it is difficult to secure the strength of the steel sheet.
  • Hereinafter, the present invention will be described in more detail by the examples. However, the examples are only for illustrating the present invention, and the present invention is not limited thereto.
    • Examples
  • First, a low-carbon steel slab including the alloy components summarized in the following Table 1 was manufactured.
  • The slab was heated at 1250° C. for 200 minutes, and then hot rolled to a thickness of 3.5 mm, thereby manufacturing a hot rolled plate. A finish rolling temperature (FDT) was 920° C., and winding was performed at 650° C.
  • TABLE 1
    Com- For- For- For-
    ponent mula mula mula
    system C Si Cu Ni Sb Ti Sn S N 1 2 (Ti*) 3
    Inven- 0.043 0.015 0.28 0.14 0.11 0.072 0.18 0.005 0.0018 0.50 0.0583 18.58
    tive
    Ex-
    ample
    1
    Inven- 0.1 0.035 0.26 0.13 0.1 0.07 0.15 0.007 0.0023 0.50 0.0516 17.00
    tive
    Ex-
    ample
    2
    Inven- 0.072 0.035 0.21 0.11 0.12 0.068 0.18 0.005 0.0021 0.52 0.0533 15.30
    tive
    Ex-
    ample
    3
    Inven- 0.072 0.032 0.34 0.19 0.1 0.065 0.13 0.005 0.0022 0.56 0.0500 20.76
    tive
    Ex-
    ample
    4
    Inven- 0.078 0.044 0.28 0.15 0.052 0.075 0.22 0.005 0.0032 0.54 0.0565 17.78
    tive
    Ex-
    ample
    5
    Inven- 0.075 0.035 0.32 0.16 0.145 0.078 0.15 0.005 0.0038 0.50 0.0575 20.99
    tive
    Ex-
    ample
    6
    Inven- 0.076 0.032 0.22 0.11 0.11 0.053 0.15 0.003 0.0018 0.50 0.0423 15.22
    tive
    Ex-
    ample
    7
    Inven- 0.071 0.022 0.24 0.13 0.11 0.143 0.16 0.0085 0.0028 0.54 0.1207 16.34
    tive
    Ex-
    ample
    8
    Inven- 0.073 0.028 0.26 0.14 0.12 0.12 0.075 0.0065 0.0018 0.54 0.1041 16.54
    tive
    Ex-
    ample
    9
    Inven- 0.076 0.026 0.28 0.14 0.09 0.09 0.21 0.0095 0.0023 0.50 0.0679 18.50
    tive
    Ex-
    ample
    10
    Inven- 0.07 0.055 0.3 0.15 0.1 0.07 0.2 0.005 0.0032 0.50 0.0515 19.60
    tive
    Ex-
    ample
    11
    Com- 0.035 0.032 0.22 0.15 0.09 0.068 0.15 0.005 0.0021 0.68 0.0533 14.78
    para-
    tive
    Ex-
    ample
    1
    Com- 0.12 0.022 0.3 0.15 0.1 0.07 0.2 0.007 0.0022 0.50 0.0520 19.60
    para-
    tive
    Ex-
    ample
    2
    Com- 0.07 0.11 0.3 0.15 0.1 0.07 0.2 0.005 0.0032 0.50 0.0515 19.60
    para-
    tive
    Ex-
    ample
    3
    Com- 0.072 0.035 0.15 0.14 0.12 0.068 0.18 0.005 0.0038 0.93 0.0475 12.30
    para-
    tive
    Ex-
    ample
    4
    Com- 0.072 0.032 0.45 0.15 0.09 0.07 0.15 0.005 0.0036 0.33 0.0502 26.28
    para-
    tive
    Ex-
    ample
    5
    Com- 0.078 0.044 0.34 0.1 0.09 0.12 0.09 0.005 0.0028 0.29 0.1029 20.06
    para-
    tive
    Ex-
    ample
    6
    Com- 0.075 0.035 0.32 0.22 0.1 0.09 0.13 0.005 0.0018 0.69 0.0763 19.76
    para-
    tive
    Ex-
    ample
    7
    Com- 0.076 0.032 0.22 0.16 0.045 0.068 0.22 0.0085 0.0023 0.73 0.0474 14.63
    para-
    tive
    Ex-
    ample
    8
    Com- 0.071 0.022 0.24 0.11 0.155 0.07 0.15 0.0065 0.0021 0.46 0.0531 17.21
    para-
    tive
    Ex-
    ample
    9
    Com- 0.073 0.028 0.26 0.13 0.12 0.045 0.15 0.0095 0.0022 0.50 0.0232 17.44
    para-
    tive
    Ex-
    ample
    10
    Com- 0.076 0.026 0.28 0.14 0.09 0.155 0.16 0.005 0.0032 0.50 0.1365 17.90
    para-
    tive
    Ex-
    ample
    11
    Com- 0.075 0.032 0.22 0.14 0.09 0.068 0.06 0.007 0.0038 0.64 0.0445 13.70
    para-
    tive
    Ex-
    ample
    12
    Com- 0.076 0.022 0.3 0.15 0.1 0.07 0.23 0.005 0.0045 0.50 0.0471 19.96
    para-
    tive
    Ex-
    ample
    13
    Com- 0.075 0.035 0.32 0.16 0.11 0.05 0.15 0.012 0.002 0.50 0.0251 20.22
    para-
    tive
    Ex-
    ample
    14
    Com- 0.075 0.035 0.32 0.16 0.11 0.065 0.15 0.005 0.0055 0.50 0.0386 20.22
    para-
    tive
    Ex-
    ample
    15
    Com- 0.075 0.035 0.32 0.16 0.11 0.06 0.15 0.01 0.0049 0.50 0.0282 20.22
    para-
    tive
    Ex-
    ample
    16
  • After the low-carbon steel sheet was manufactured, an immersion test was performed by the method described in the standard of ASTM G31. The immersion test was performed by a method of preparing 50 wt % of an aqueous sulfuric acid solution and performing immersion at 70° C. for 6 hours. After the immersion, the steel sheet was washed by the specimen surface washing method of ASTM G1, and a weight loss was measured to measure weight losses per unit time and per unit surface.
  • In addition, in order to simulate sulfuric acid/hydrochloric acid composite condensation occurring in low-temperature condensation in the Korean-style thermal power plant, a mixed aqueous solution of 28.5 wt % of a sulfuric acid solution and 0.5 wt % of a hydrochloric acid solution was prepared, and a test of immersion at 60° C. for 6 hours was performed. After the immersion, as described above, a weight loss after washing was measured by a specimen surface washing method of ASTM G1, and weight losses per unit time and per unit surface were measured.
  • The results are shown in the following Table 2. The unit was mg/cm2/hr.
  • Meanwhile, in order to reveal the relationship between a corrosion-resistant element and a surface concentrated layer, the hot rolled plates of each of the inventive examples and the comparative examples were immersed in 50 wt % of a sulfuric acid solution at 70° C. for 24 hours, and then the specimen was measured for an element distribution from the surface to the inside by GDS measurement. The thickness of the concentrated layer measured therefrom and the concentrated amount of the surface concentrating elements were measured and are shown in the following Table 2.
  • Herein, the concentrated layer refers to a layer in which Cu, Sb, and Sn starts to be concentrated, and on the other hand, is generally similar to the point at which oxidation starts. Empirically, the thickness of the concentrated layer was measured as the thickness of the layer in which the combined amount of Cu, Sb, and Sn is more than 4 times the combined amount of Cu, Sb, and Sn in the steel sheet. Herein, in the boundary point at which the contents (wt %) of Fe and O are the same in wt %, it was confirmed that Cu and the like was concentrated at most, and the concentrated amount was calculated as the sum of the contents (wt %) of concentrating elements Cu, Sb, and Sn, at a point at which the contents (wt %) of Fe and O are the same. It was confirmed that the concentrated layer formed of Sb, Sn, and Cu was present at about 20 wt % on the surfaces of the steel material and the corrosion product. It was found that the thickness of the concentrated layer and the concentrated amount determine the corrosion resistance in immersion.
  • In this regard, FIG. 1 is a graph showing an element concentration degree of a surface portion of a steel sheet, by measuring an element distribution from the surface to the inside by GDS measurement, after the steel sheet of Inventive Example 2 was immersed in 50 wt % of a sulfuric acid solution for 24 hours. The sum of the contents of Cu, Sb, and Sn of Inventive Example 2 was (0.26+0.1+0.15) and 0.51 wt %, and in the depth of 14 nm, the sum of the amounts of Cu, Sb, and Sn was more than 2.04 wt %, which is 4 times 0.51 wt %. Therefore, the depth, 14 nm was the thickness of the concentrated layer. (Red dotted line)
  • In addition, a boundary point at which Fe and O meets, that is, the point at which the contents of Fe and O are the same corresponds to the blue dotted line (left) of FIG. 1 , and the concentrated amount which is the sum of Cu, Sb, and Sn in the layer was 17 wt %.
  • In addition, for the manufactured steel sheet, strength, hardness, and crack occurrence were confirmed before acid immersion. The hot rolled materials of the inventive examples and the comparative examples were processed into a tensile specimen conforming to the standards of JIS13B, a tensile test was performed at length in a rolling direction, and the results of measuring HRB surface hardness based on Rockwell hardness are shown in the following Table 2.
  • In addition, whether cracks occurred in cast iron in the continuous casting process in manufacturing the hot rolled plate, or whether cracks occurred in a hot rolled material edge in the process of hot rolling is also shown in the following Table 2. Herein, the concentrated amount refers to the sum of the contents (wt %) of concentrating elements Cu, Sb, and Sn at a point at which the contents (wt %) of Fe and O are the same.
  • TABLE 2
    Corrosion Corrosion
    reduction reduction Thick-
    ratio of ration of ness of Hot
    sulfuric composite concen- Concen- TiC rolling Cracks in
    Com- acid alone acid mg/ trated trated TiC particle Tensile hard- soft
    ponent mg/ (cm2 × layer amount density diameter strength ness casting,
    system (cm2 × hr.) hr.) (nm) (wt %) (/cm3) (nm) (MPa) (HRB) hot rolling
    Inven- 18 0.82 15 18.6 2.9E+16 3.7 630 93 X
    tive
    Ex-
    ample
    1
    Inven- 22 0.94 14 17.0 2.0E+16 3.0 668 96 X
    tive
    Ex-
    ample
    2
    Inven- 24.5 0.74 16 15.3 2.2E+16 3.2 652 95.5 X
    tive
    Ex-
    ample
    3
    Inven- 23 0.85 12 20.8 1.8E+16 2.8 650 95.5 X
    tive
    Ex-
    ample
    4
    Inven- 23.5 0.95 14 17.8 2.6E+16 3.5 654 93.5 X
    tive
    Ex-
    ample
    5
    Inven- 20.8 0.74 15 21.0 2.7E+16 3.6 665 94.5 X
    tive
    Ex-
    ample
    6
    Inven- 21.9 0.88 14 15.2 1.1E+16 2.1 550 85 X
    tive
    Ex-
    ample
    7
    Inven- 21.6 0.98 14 16.3 1.0E+18 9.6 920 106 X
    tive
    Ex-
    ample
    8
    Inven- 24.6 0.95 12 16.5 4.0E+17 8.1 725 101 X
    tive
    Ex-
    ample
    9
    Inven- 20.8 0.65 14 18.5 5.0E+16 4.6 690 97 X
    tive
    Ex-
    ample
    10
    Inven- 23.5 0.85 14 19.6 2.2E+16 3.2 635 91 X
    tive
    Ex-
    ample
    11
    Com- 25.8 0.85 9 14.8 1.7E+16 2.8 510 82 X
    parative
    Ex-
    ample
    1
    Com- 22.9 1.03 12 19.6 1.7E+16 2.8 640 91.6 X
    parative
    Ex-
    ample
    2
    Com- 22.5 0.75 14 18.5 2.1E+16 3.1 639 91.5 ◯
    parative (Crack
    Ex- occurrence
    ample in hot
    3 rolling)
    Com- 48.5 2.35 7.5 12.3 2.0E+16 3.0 615 90.2 X
    parative
    Ex-
    ample
    4
    Com- 20.5 0.68 15 26.3 1.9E+16 3.0 580 90 ◯
    parative (Crack
    Ex- occurrence
    ample in cast
    5 iron)
    Com- 21 0.72 15 20.1 1.5E+16 2.6 910 102 ◯
    parative (Crack
    Ex- occurrence
    ample in cast
    6 iron)
    Com- 20.6 1.52 13 19.8 1.8E+16 2.9 685 94 X
    parative
    Ex-
    ample
    7
    Com- 56.9 2.65 8.9 14.6 3.7E+17 7.9 590 90 X
    parative
    Ex-
    ample
    8
    Com- 18 0.68 11 17.2 8.1E+16 5.4 610 90 ◯
    parative (Crack
    Ex- occurrence
    ample in hot
    9 rolling)
    Com- 19.5 0.55 13 17.4 1.5E+16 2.6 460 73 X
    parative
    Ex-
    ample
    10
    Com- 22.5 2.31 14 17.9 2.1E+16 3.1 930 108 ◯
    parative (Crack
    Ex- occurrence
    ample in cast
    11 iron)
    Com- 85.5 8.95 6.8 13.7 3.8E+15 0.3 608 90 X
    parative
    Ex-
    ample
    12
    Com- 24.5 0.56 14 20.0 2.6E+18 11.2 605 90 ◯
    parative (Crack
    Ex- occurrence
    ample in hot
    13 rolling)
    Com- 22.3 1.55 13 18.0 1.3E+16 2.3 480 76 X
    parative
    Ex-
    ample
    14
    Com- 21.5 2.36 12 18.0 1.5E+16 2.6 520 83 X
    parative
    Ex-
    ample
    15
    Com- 20.8 2.08 13 18.0 4.3E+15 0.5 490 79 X
    parative
    Ex-
    ample
    16
  • In Comparative Example 1 having a low C content, due to the reduced content of the TiC precipitate by the low C content, the tensile strength of the hot rolled material was lower than 550 MPa, and the surface hardness was low, and thus, strength and abrasiveness were not able to be secured. However, when the C content was excessively high as in Comparative Example 2, a phenomenon in which composite corrosion resistance was reduced due to the increased TiC precipitate was observed.
  • In the present invention, characteristically, the content of Si was greatly lowered, and the reason is that it was confirmed that as the Si content was higher as in Comparative Example 3, red scale excessively occurred on the surface of the hot rolled material, leading to cracks.
  • In Comparative Example 4 having a low Cu content, in particular, the corrosion resistance to a sulfuric acid alone was reduced, and in Comparative Example 5 in which the Cu content was excessively high, cracks in cast iron due to the liquefaction of Cu in the continuous casting process was confirmed.
  • As in Formula 1, the active addition of Ni serves to raise the melting point of Cu, and thus, it was confirmed that when a Ni/Cu ratio does not satisfy a certain ratio as in Comparative Example 6, cracks in cast iron occurred.
  • The most important elements in corrosion resistance are Cu, Sb, and Sn, and it was confirmed that in Comparative Example 8 having a low Sb content and in Comparative Example 12 having a low Sn content, corrosion resistance was greatly deteriorated, and in Comparative Example 9 having an excessively high Sb content and in Comparative Example 13 having an excessively high Sn content, defects and cracks on the surface of the hot rolled material were caused.
  • In the present invention, Ti was actively added for forming precipitates for securing strength and surface hardness, and it was confirmed that when the Ti content was low as in Comparative Example 10, the tensile strength and the surface hardness of the hot rolled material were rapidly lowered. Meanwhile, in Comparative Example 11 having a high Ti content, in particular, in the case of the Ti content of 0.15 wt % or more, nozzle clogging may be caused in the continuous casting process, and extreme nozzle clogging was confirmed even in the real test process of the comparative example.
  • For forming TiC, not only C and Ti adjustment and temperature adjustment, but also an effective Ti content capable of precipitating carbide is important. The excessive addition of nitrogen and sulfur as in Comparative Examples 14 and 15 lowered the effective Ti content to offset the strength increase effect.
  • In addition, even in the case in which the composition was within the contents of S and N described in the inventive examples as in Comparative Example 16, when the effective Ti(Ti) content of Formula 2 was not 0.04 or more, it is difficult to obtain the effects of high strength and high wear resistance. Meanwhile, in Comparative Example 16 having a low effective Ti content, TiC density was small, a TiC particle diameter was also too small, and thus, a precipitation hardening effect to be desired was not able to be obtained.
  • In order to examine the influence of the manufacturing conditions on the productivity and the strength of the hot rolled material and the cold rolled material, the manufacturing conditions were modified under the component system of Inventive Example 4 to perform manufacture, and the characteristics were evaluated and are shown in Table 3.
  • TABLE 3
    Re- Cold Anneal- Tensile Tensile
    heating re- ing strength strength Cold Occur-
    Manu- temper- duction temper- of hot of cold Recrys- rolling rence
    facturing ature FDT CT rate ature rolled rolled tallization possi- of edge
    conditions (° C.) (° C.) (° C.) (%) (° C.) material material fraction bility Crack
    Condition 1250 920 650 64 810 650 550 100% ◯ X
    1
    Condition 1250 800 650 64 810 680 594 100% ◯ ◯
    2
    Condition 1250 1050 650 64 810 540 485 100% ◯ X
    3
    Condition 1250 920 440 64 — 690 — 100% X ◯
    4
    Condition 1250 920 755 64 810 530 490 100% ◯ X
    5
    Condition 1250 920 650 53 810 650 650  70% ◯ X
    6
    Condition 1250 920 650 72 — 650 — 100% X X
    7
    Condition 1250 920 650 64 740 650 670  65% ◯ X
    8
    Condition 1250 920 650 64 890 650 450 100% ◯ X
    9
    Condition 1180 920 650 64 810 530 480 100% ◯ X
    10
  • In the results of Table 3, in Condition 10 in which the reheating temperature was lower than 1200° C., it was confirmed that the tensile strengths of the hot rolled material and the cold rolled material were decreased even in the case of using the inventive component system, and this is because Ti formed as a precipitate in the slab processing was not sufficiently re-solid solubilized in the reheating process.
  • In Condition 2 in which a hot finish rolling temperature (EDT) was high, edge cracks occurred in the hot rolling production process, and this was the same in Condition 4 having a low winding temperature (CT)
  • In this regard, FIG. 2 is photographs in which (a) a crack occurrence tendency in a hot rolled edge portion after hot rolling Inventive Example 4 under Condition 1 and (b) a crack occurrence tendency in a hot rolled edge portion after hot rolling Inventive Example 4 under Condition 2 are compared
  • However, under Condition 3 having a high hot finish rolling temperature (FDT) of 1050° C., the tensile strength of the hot rolled material and the cold rolled material, so that a material to be desired was not able to be secured, and this was the same also in Condition 5 having a high winding temperature (CT).
  • The steel type of the present invention has high contents of C and Ti and is characterized by a high recrystallization temperature after cold rolling, and under Condition 6 having a cold reduction rate of 53%, the recrystallization fraction of the final cold rolled material was about 70%, which did not form complete recrystallization, and in Condition 8 having an annealing temperature was 740° C. which was low also, the recrystallization fraction was 65%, which did not form complete recrystallization. The material which did not undergo complete recrystallization may cause cracks in the customer processing due to a lowered elongation, and thus, in the present invention, when it is used as a cold rolling material, the reduction rate was limited to 54% or more and the annealing temperature was limited to 750° C. or higher.
  • Further, in Condition 4 and Condition 7 in which the strength of the hot rolled material was high or the cold reduction rate was high, rolling was not performed by a motor loading in the rolling process, and thus, the final product was not able to be obtained.
  • The present invention is not limited to the implementations and/or the exemplary embodiments, but may be produced in various forms different from each other. A person with ordinary skill in the art to which the present invention pertains will understand that the present invention may be carried out in other specific forms without changing the technical idea or the essential feature of the present invention. Therefore, the implementations and/or the exemplary embodiments described above should be understood to be illustrative in all respects, and not to be restrictive.

Claims (17)

1. A corrosion-resistant steel sheet comprising, by weight: 0.04 to 0.10% of carbon (C), 0.1% or less (excluding 0%) of silicon (Si), 0.20 to 0.35% of copper (Cu), 0.1 to 0.2% of nickel (Ni), 0.05 to 0.15% of antimony (Sb), 0.05 to 0.15% of titanium (Ti), 0.07 to 0.22% of tin (Sn), 0.01% or less (excluding 0%) of sulfur (S), and 0.005% or less (excluding 0%) of nitrogen (N), with a remainder of iron (Fe) and unavoidable impurities,
the corrosion-resistant steel sheet satisfying the following Formulae 1 and 2:

[Ni]/[Cu]≥0.5  [Formula 1]

48×([Ti]/48−[S]/32−[N]/14)≥0.04  [Formula 2]
wherein [Ni], [Cu], [Ti], [S], and [N] represent contents (wt %) of Ni, Cu, Ti, S, and N in the steel sheet, respectively.
2. The corrosion-resistant steel sheet of claim 1, wherein:
the corrosion-resistant steel sheet includes a TiC precipitate, and
the TiC precipitate and an aggregate formed of the TiC precipitate are included at 1016 or more per 1 cm3.
3. The corrosion-resistant steel sheet of claim 2, wherein:
the TiC precipitate has a particle diameter of 1 to 10 nm.
4. The corrosion-resistant steel sheet of claim 1, wherein:
the corrosion-resistant steel sheet satisfies the following Formula 3.

12×[Sn]+22×[Sb]+50×[Cu]≥15  [Formula 3]
wherein [Sn], [Sb], and [Cu] represent contents (wt %) of Sn, Sb, and Cu in the steel sheet, respectively.
5. The corrosion-resistant steel sheet of claim 2, wherein:
when the steel sheet is immersed in a mixed solution of 28.5 wt % of a sulfuric acid solution and 0.5 wt % of a hydrochloric acid solution at 40 to 80° C., a concentrated layer is produced on a surface of the steel sheet.
6. The corrosion-resistant steel sheet of claim 2, wherein:
when the steel sheet is immersed in 50 wt % of a sulfuric acid solution at 50 to 90° C., a concentrated layer is produced on a surface of the steel sheet.
7. The corrosion-resistant steel sheet of claim 5, wherein:
the concentrated layer includes Cu, Sb, and Sn.
8. The corrosion-resistant steel sheet of claim 7, wherein:
the concentrated layer has a concentrated amount of 15 wt % or more,
wherein the concentrated amount refers to a sum of the contents (wt %) of concentrating elements Mo, Cu, Sb, and Sn, at a boundary point at which wt % of Fe and O are the same.
9. The corrosion-resistant steel sheet of claim 5, wherein:
the concentrated layer has a thickness of 10 nm or more.
10. The corrosion-resistant steel sheet of claim 1, wherein:
a recrystallization fraction after subjecting the steel sheet to an annealing heat treatment is 80% or more.
11. The corrosion-resistant steel sheet of claim 5, wherein:
when the steel sheet is immersed in the mixed solution of 28.5 wt % of the sulfuric acid solution and 0.5 wt % of the hydrochloric acid solution at 60° C. for 6 hours, a corrosion weight loss ratio is 1.0 mg/cm2/hr or less.
12. The corrosion-resistant steel sheet of claim 6, wherein:
when the steel sheet is immersed in 50 wt % of the sulfuric acid solution at 70° C. for 6 hours, a corrosion weight loss ratio is 25 mg/cm2/hr or less.
13. The corrosion-resistant steel sheet of claim 2, wherein:
when the steel sheet is a hot rolled steel sheet, the hot rolled steel sheet has a tensile strength of 550 MPa or more and a surface hardness of 85 or more based on HRB.
14. The corrosion-resistant steel sheet of claim 2, wherein:
when the steel sheet is a cold rolled steel sheet, the cold rolled steel sheet has a tensile strength of 500 MPa or more and a surface hardness of 80 or more based on HRB.
15. A method for manufacturing a corrosion-resistant steel sheet, the method comprising: preparing a steel slab which includes, by weight: 0.04 to 0.10% of carbon (C), 0.1% or less (excluding 0%) of silicon (Si), 0.20 to 0.35% of copper (Cu), 0.1 to 0.2% of nickel (Ni), 0.05 to 0.15% of antimony (Sb), 0.07 to 0.22% of tin (Sn), 0.05 to 0.15% of titanium (Ti), 0.01% or less (excluding 0%) of sulfur (S), and 0.005% or less (excluding 0%) of nitrogen (N), with a remainder of iron (Fe) and unavoidable impurities, and
satisfies the following Formulae 1 and 2;
heating the slab at 1,200° C. or higher; and
hot rolling the heated slab at a finish rolling temperature of 850 to 1000° C. to manufacture a hot rolled steel sheet.

[Ni]/[Cu]≥0.5  [Formula 1]

48×([Ti]/48−[S]/32−[N]/14)≥0.04  [Formula 2]
wherein [Ni], [Cu], [Ti], [S], and [N] represent contents (wt %) of Ni, Cu, Ti, S, and N in the steel sheet, respectively.
16. The method for manufacturing a corrosion-resistant steel sheet of claim 15, further comprising:
after the manufacturing of a hot rolled steel sheet,
winding the hot rolled steel sheet at 450 to 750° C.;
cold rolling the wound hot rolled steel sheet at a reduction ratio of 54 to 70% to manufacture a cold rolled steel sheet; and
subjecting the cold rolled steel sheet to an annealing heat treatment at 750 to 880° C.
17. The method for manufacturing a corrosion-resistant steel sheet of claim 15, wherein:
in the heating of a slab at 1,200° C. or higher,
a residence time is 150 minutes or more.
US17/785,846 2019-12-19 2020-12-14 Steel plate having excellent wear resistance and composite corrosion resistance and method for manufacturing same Pending US20230033491A1 (en)

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