EP3305936B1 - Warmgewalztes stahlblech mit hervorragender kombinierterkorrosionsbeständigkeit gegen schwefelsäure und salzsäure und herstellungsverfahren dafür - Google Patents

Warmgewalztes stahlblech mit hervorragender kombinierterkorrosionsbeständigkeit gegen schwefelsäure und salzsäure und herstellungsverfahren dafür Download PDF

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EP3305936B1
EP3305936B1 EP15893419.0A EP15893419A EP3305936B1 EP 3305936 B1 EP3305936 B1 EP 3305936B1 EP 15893419 A EP15893419 A EP 15893419A EP 3305936 B1 EP3305936 B1 EP 3305936B1
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Prior art keywords
hot
steel sheet
rolled steel
sulfuric acid
hydrochloric acid
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French (fr)
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EP3305936A4 (de
EP3305936A1 (de
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Jeong-Bong Yoon
Byoung-Ho Lee
Jong-Hwa Kim
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Posco Holdings Inc
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Posco Co Ltd
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Classifications

    • 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
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/84—Controlled slow cooling
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

Definitions

  • the present disclosure relates to a hot-rolled steel sheet having high composite corrosion resistance to sulfuric acid and hydrochloric acid and applicable as a material for thermal power plant equipment such as desulfurization equipment, denitrification equipment, preheaters, or parts thereof, and a method for manufacturing the hot-rolled steel sheet.
  • Steels having resistance to sulfuric acid corrosion or sulfuric acid-hydrochloric acid composite corrosion are used as materials for desulfurization equipment and denitrification equipment in thermal power plants in which sulfuric acid corrosion or sulfuric acid-hydrochloric acid composite corrosion is serious, due to sulfuric acid and hydrochloric acid produced by a reaction between moisture and exhaust gas containing sulfurous acid gas and chlorine gas generated when fossil fuels such as coal or petroleum are combusted, pipes of combined cycle power plants, and gas-gas heater (GGH) heat elements required to be made of relatively thick steel sheets, etc.
  • GGH gas-gas heater
  • Cu copper
  • elements such as phosphorus in a range of 0.03 to 0.15 wt%, nickel in a range of 0.1 to 0.4 wt% and cobalt in a range of 0.03 to 0.1 wt% has been added to a steel sheet for resistance to composite corrosion from sulfuric acid and hydrochloric acid as described in patent document KR 2015 0029468 A .
  • copper (Cu) is a relatively expensive alloying element, and thus production costs may be increased in proportion to the amount of copper (Cu).
  • copper (Cu) having a low melting point, may be segregated or easily cause cracks, even if only a small amount of deformation occurs in copper-rich regions. Therefore, cracks may be easily formed in portions such as slab corners undergoing a large amount of processing during a continuous casting process, and thus, surface defects undergoing corrosion earlier that other portions may remain after a hot rolling process.
  • aspects of the present disclosure may provide a hot-rolled steel sheet having high corrosion resistance in a composite corrosive environment containing sulfuric acid and hydrochloric acid, and a method for manufacturing the hot-rolled steel sheet.
  • a hot-rolled steel sheet having high composite corrosion resistance to sulfuric acid and hydrochloric acid comprises, by wt%, carbon (C) : 0.05% to 0.1%, manganese (Mn) : 0.5% to 1.5%, phosphorus (P): 0.02% or less, sulfur (S): 0.02% to less, aluminum (Al): 0.01% to 0.1%, copper (Cu): 0.2% to 0.6%, antimony (Sb): 0.05% to 0.1%, and a balance of iron (Fe) and inevitable impurities, wherein copper (Cu) and antimony (Sb) may be concentrated in a region from a surface to a 500-nm position in a thickness direction of the hot-rolled steel sheet, and the hot-rolled steel sheet may have a corrosion loss of 2.0 mg/cm 2 /hr in 6 hours or less in a solution of 16.9 volume% sulfuric acid and 0.35 volume% hydrochloric acid having a temperature of 60°C.
  • a method for manufacturing a hot-rolled steel sheet having high composite corrosion resistance to sulfuric acid and hydrochloric acid may include: reheating a steel slab to 1100°C to 1300°C, the steel slab including, by wt%, carbon (C): 0.05% to 0.1%, manganese (Mn): 0.5% to 1.5%, phosphorus (P): 0.02% or less, sulfur (S): 0.02% or less, aluminum (Al): 0.01% to 0.1%, copper (Cu): 0.2% to 0.6%, antimony (Sb): 0.05% to 0.1%, and a balance of iron (Fe) and inevitable impurities; obtaining a hot-rolled steel sheet by hot rolling the reheated steel slab and finish hot rolling the steel slab at a temperature of 850°C to 950°C; rapidly cooling the hot-rolled steel sheet at a rate of 120°C/s to 150°C/s; coiling the cooled hot-rolled steel sheet at a temperature of 650°C to 750
  • the present disclosure may provide a hot-rolled steel sheet having high composite corrosion resistance even though the hot-rolled steel sheet has lower amounts of alloying elements than steel sheets of the related art having composite corrosion resistance to sulfuric acid and hydrochloric acid.
  • the hot-rolled steel sheet of the present disclosure may be used as a material, required to have a relatively thick thickness, for denitrification equipment and desulfurization equipment of power plants, exhaust gas pipes of boilers, and preheaters, and may markedly increase the lifespans of such facilities and apparatuses.
  • the inventors have repeatedly conducted research into compositions of steel sheets and methods of manufacturing steel sheets in order to provide a method of imparting high composite corrosion resistance to steel resistant to sulfuric acid-hydrochloric acid composite corrosion while minimizing the content of copper (Cu) in the steel.
  • Cu copper
  • the inventors have found that if antimony (Sb) is added to a steel sheet as an alloying element, and cooling conditions after a hot rolling process and a coiling process are properly controlled, a Cu-Sb rich layer, guaranteeing high composite corrosion resistance, is formed on the steel sheet to an appropriate thickness in a corrosive environment containing sulfuric acid and hydrochloric acid. Based on this knowledge, the inventors have invented the present invention.
  • Carbon (C) is effective in increasing the strength of a steel sheet. If the content of carbon (C) is less than 0.05 wt%, it is difficult to obtain a desired degree of strength, and wear resistance reduces. Conversely, if the content of carbon (C) is greater than 0.1 wt%, the weldability of the steel sheet markedly reduces, thereby markedly increasing the possibility of defects during welding and decreasing the corrosion resistance of the steel sheet.
  • Manganese (Mn) dissolves in steel and precipitates sulfur (S) in the form of manganese sulfide, thereby preventing hot shortness caused by dissolved sulfur (S) and having a solid-solution strengthening effect. If the content of manganese (Mn) is less than 0.5 wt%, manganese sulfide is not sufficiently precipitated. Thus, hot shortness may be caused by dissolved sulfur (S), and it may be difficult to obtain a desired degree of strength. Conversely, if the content of manganese (Mn) is greater than 1.5 wt%, the above-described effects are saturated, and product cost markedly increases.
  • Phosphorus (P) 0.02 wt% or less
  • Phosphorus (P) is an element inevitably added to steel, and if the content of phosphorus (P) is greater than 0.02 wt%, composite corrosion resistance may markedly decrease from a desired value.
  • Sulfur (S) is an element dissolved in steel causing hot shortness, and thus, the content of sulfur (S) is adjusted to be as low as possible. If the content of sulfur (S) is greater than 0.02 wt%, there is a high possibility that defects will be formed due to hot shortness.
  • Aluminum (Al) is an element inevitably added to Alkilled steel, and it may be preferable that the content of aluminum (Al) be within the range of 0.01 wt% or greater for the effect of deoxidation. However, if the content of aluminum (Al) is greater than 0.1 wt%, surface defects may very likely be formed on the steel sheet, and the weldability of the steel sheet may be decreased.
  • Copper (Cu) is an element added for composite corrosion resistance to sulfuric acid and hydrochloric acid. If the content of copper (Cu) is excessively low, it may be difficult to obtain desired composite corrosion resistance. Thus, preferably, copper (Cu) may be added in an amount of 0.3% or greater. Although composite corrosion resistance increases in proportion to the content of copper (Cu), if the content of copper (Cu) is excessively high, the increase of corrosion resistance is markedly lowered, and production costs may be markedly increased. In addition, surface defects known as star cracks may be formed. Therefore, according to the present disclosure, preferably, the upper limit of the content of copper (Cu) may be set to be 0.5 wt%.
  • antimony (Sb) is a key element for improving composite corrosion resistance.
  • antimony (Sb) forms a Cu-Sb composite oxide in a corrosive environment, thereby effectively improving composite corrosion resistance. If the content of antimony (Sb) is less than 0.05 wt%, it is difficult to obtain the above-described effects. Conversely, if the content of antimony (Sb) is greater than 0.1 wt%, the above-described effects are saturated, and production costs markedly increase.
  • the steel sheet includes iron (Fe) and inevitable impurities in addition to the above-described alloying elements.
  • Fe iron
  • the addition of elements other than the above-described elements is not excluded, it may be preferable that the total content of tungsten (W), molybdenum (Mo), cobalt (Co), and nickel (Ni) be adjusted to be less than 10 ppm. The reason for this is that these elements may deteriorate the properties of the hot-rolled steel sheet, for example, ductility.
  • copper (Cu) and antimony (Sb) may be concentrated in a region from the surface to a 500-nm position in the thickness direction of the hot-rolled steel sheet. These elements are concentrated in the surface of the hot-rolled steel sheet during manufacturing processes, and if the hot-rolled steel sheet is exposed to a corrosive environment containing sulfuric acid and hydrochloric acid, the elements change into a Cu-Sb composite oxide, thereby markedly improving the corrosion resistance of the hot-rolled steel sheet.
  • the contents of concentrated copper (Cu) and antimony (Sb) are not particularly limited. As described below, the contents of concentrated copper (Cu) and antimony (Sb) may be adjusted such that an oxide layer having a thickness of 400 nm or greater from the surface of the hot-rolled steel sheet may be formed in a corrosive environment containing sulfuric acid and hydrochloric acid. If the thickness of the oxide layer is less than 400 nm, it may be difficult to obtain a degree of corrosion resistance intended in the present disclosure. Since corrosion resistance increases as the thickness of the oxide layer increases, the upper limit of the thickness of the oxide layer is not particularly set in the present disclosure.
  • the thickness of the oxide layer is greater than 500 nm, the effect of improving corrosion resistance is relatively low when the addition of large amounts of alloying elements is considered, and production costs may be excessively increased.
  • the thickness of the oxide layer it may be more preferable that the thickness of the oxide layer be within the range of 400 nm to 500 nm.
  • the hot-rolled steel sheet of the present disclosure has a corrosion loss of 2.0 mg/cm 2 /hr or less in a solution of 16.9 volume% sulfuric acid and 0.35 volume% hydrochloric acid.
  • a steel slab having the above-described composition is prepared and reheated to a temperature of 1100°C to 1300°C. If the reheating temperature is lower than 1100°C, it is difficult to secure a temperature for a subsequent hot rolling process. Conversely, if the reheating temperature is higher than 1300°C, copper (Cu) having a relatively low melting point may melt out, and thus cracks may very likely be formed in the surface of the steel slab.
  • Cu copper
  • the reheated steel slab is subjected to hot rolling, and is then subjected to finish hot rolling at a temperature of 850°C to 950°C, to obtain a hot-rolled steel sheet.
  • finish hot rolling temperature is lower than 850°C, the elongation of the hot-rolled steel sheet is markedly decreased due to elongated grains, and properties of the hot-rolled steel sheet have directional deviations.
  • finish hot rolling temperature is higher than 950°C, austenite grains become coarse, and thus hardenability markedly increases.
  • the hot-rolled steel sheet is rapidly cooled at a rate of 120°C/s to 150°C/s, based on the surface temperature of the hot-rolled steel sheet.
  • the rapid cooling may provide driving force such that alloying elements improving corrosion resistance may move to the surface of the hot-rolled steel sheet after a coiling process. If the cooling rate is less than 120°C/s, the surface temperature of the hot-rolled steel sheet may be too high to sufficiently drive oxide-forming elements from the interior to the surface of the hot-rolled steel sheet, and thus when the hot-rolled steel sheet is exposed to a composite corrosive environment, oxides may not be sufficiently formed.
  • the cooling rate may be set to be within the range of 120°C/s to 150°C/s.
  • the cooled hot-rolled steel sheet is coiled at a temperature of 650°C to 750°C. If the coiling temperature is lower than 650°C, atoms may not easily move during the coiling process. As a result, a rich layer may not be easily formed, and thus an oxide layer may not be formed in a corrosive environment. That is, corrosion resistance may not be sufficiently guaranteed. If the coiling temperature is higher than 750°C, heat recuperation occurs to an excessively high temperature, and thus, defects such as dents may be formed on the coiled hot-rolled steel sheet. Therefore, the coiling temperature may preferably be set to be within the range of 650°C to 750°C.
  • the surface of the hot-rolled steel sheet may have a temperature of 720°C to 750°C owing to a heat recuperation phenomenon.
  • the interior temperature of the hot-rolled steel sheet is adjusted to be within the range of 650°C to 750°C through the cooling process, the surface temperature of the hot-rolled steel sheet is lower than the range because of rapid cooling. Therefore, the hot-rolled steel sheet may be allowed to undergo heat recuperation so as to activate the movement of alloying elements effective in forming an oxide layer and thus to form a rich layer having a sufficient thickness.
  • the surface temperature of the hot-rolled steel sheet may preferably be 720°C or higher after heat recuperation. However, the surface temperature of the hot-rolled steel sheet will not exceed 750°C even if the heat recuperation is sufficient.
  • the coiled hot-rolled steel sheet is slowly cooled to a cooling finish temperature of 350°C to 400°C at a rate of 30°C/hr to 40°C/hr. If the slow cooling rate is excessively high, copper (Cu) forming a rich layer may not sufficiently move, and thus it may be difficult to form a rich layer having a sufficient thickness. Therefore, it may be preferable that the slow cooling rate be within the range of 40°C/hr or less. However, if the slow cooling rate is less than 30°C/hr, the size of grains may increase excessively, and thus, the strength of the hot-rolled steel sheet may decrease. Thus, the slow cooling rate may preferably be within the range of 30°C/hr to 40°C/hr.
  • the cooling finish temperature may preferably be within the range of 350°C to 400°C.
  • Inventive Examples 1 to 3 satisfying the alloying composition and manufacturing conditions proposed in the present disclosure had a corrosion loss of 2.0 mg/cm 2 /hr or less in the sulfuric acid-hydrochloric acid corrosive environment owing to the formation of oxide layers having a thickness of 400 nm or greater. That is, Inventive Examples 1 to 3 had high corrosion resistance.
  • Comparative Example 1 satisfied the alloying composition of the present disclosure, the coiling temperature of Comparative Example 1 was low, 500°C. Thus, an oxide layer was not sufficiently formed, resulting in corrosion loss of 4.5 mg/cm 2 /hr. That is, Comparative Example 1 had poor corrosion resistance.
  • Comparative Examples 2 to 4 satisfied the alloying composition of the present disclosure, the cooling rate of Comparative Example 2 to 4 was low, 10°C/s. Thus, oxide layers were not sufficiently formed, resulting in a corrosion loss of 3.2 mg/cm 2 /hr or greater. That is, Comparative Examples 2 to 4 had poor corrosion resistance.
  • Comparative Example 5 satisfied the manufacturing conditions of the present disclosure, antimony (Sb) was not added to Comparative Example 5, resulting in a corrosion loss of 8.8 mg/cm 2 /hr in the sulfuric acid-hydrochloric acid corrosive environment. That is, Comparative Example 5 had poor corrosion resistance. The reason for this is that a Cu-Sb composite oxide having high corrosion resistance was not formed in an oxide layer.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
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  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
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Claims (6)

  1. Warmgewalztes Stahlblech mit hoher kombinierter Korrosionsbeständigkeit gegen Schwefelsäure und Salzsäure, wobei das warmgewalzte Stahlblech in Gew.-% umfasst, Kohlenstoff (C): 0,05 % bis 0,1 %, Mangan (Mn): 0,5 % bis 1,5 %, Phosphor (P): 0,02 % oder weniger, Schwefel (S): 0,02 % oder weniger, Aluminium (AI): 0,01 % bis 0,1 %, Kupfer (Cu): 0,2 % bis 0,6 %, Antimon (Sb): 0,05 % bis 0,1 %, und einen Rest aus Eisen (Fe) und unvermeidlichen Verunreinigungen, wobei Kupfer (Cu) und Antimon (Sb) in einem Bereich ausgehend von einer Oberfläche zu einer 500 nm-Position in einer Dickenrichtung des warmgewalzten Stahlblechs konzentriert sind, und das warmgewalzte Stahlblech einen Korrosionsverlust von 2,0 mg/cm2/h in 6 Stunden oder weniger in einer Lösung aus 16,9 Volumen-% Schwefelsäure und 0,35 Volumen-% Salzsäure mit einer Temperatur von 60° C hat.
  2. Warmgewalztes Stahlblech nach Anspruch 1, wobei die unvermeidlichen Verunreinigungen Wolfram (W), Molybdän (Mo), Cobalt (Co) und Nickel (Ni) in einer Gesamtmenge von weniger als 10 ppm umfassen.
  3. Warmgewalztes Stahlblech nach Anspruch 1, wobei das konzentrierte Kupfer (Cu) und Antimon (Sb) eine ein Cu-Sb-Verbundoxid umfassende Oxidschicht in einer Schwefelsäure und Salzsäure enthaltenden korrosiven Umgebung bilden.
  4. Warmgewalztes Stahlblech nach Anspruch 3, wobei die Oxidschicht eine Dicke von 400 nm bis 500 nm ausgehend von der Oberfläche des warmgewalzten Stahlblechs in der Dickenrichtung des warmgewalzten Stahlblechs hat.
  5. Verfahren zum Herstellen eines warmgewalzten Stahlblechs mit hoher kombinierter Korrosionsbeständigkeit gegen Schwefelsäure und Salzsäure, wobei das Verfahren umfasst:
    Wiedererwärmen einer Stahlbramme auf 1100° C bis 1300 ° C, wobei die Stahlbramme in Gew.-% umfasst, Kohlenstoff (C): 0,05 % bis 0,1 %, Mangan (Mn): 0,5 % bis 1,5 %, Phosphor (P): 0,02 % oder weniger, Schwefel (S): 0,02 % oder weniger, Aluminium (AI): 0,01 % bis 0,1 %, Kupfer (Cu): 0,2 % bis 0,6 %, Antimon (Sb): 0,05 % bis 0,1 %, und einen Rest aus Eisen (Fe) und unvermeidlichen Verunreinigungen;
    Erlangen eines warmgewalzten Stahlblechs durch Warmwalzen der wiedererwärmten Stahlbramme und Endwarmwalzen der Stahlbramme bei einer Temperatur von 850° C bis 950° C;
    schnelles Abkühlen des warmgewalzten Stahlblechs mit einer Rate von 120° C/s bis 150° C/s;
    Aufwickeln des warmgewalzten Stahlblechs bei einer Temperatur von 650° C bis 750° C; und
    langsames Abkühlen des aufgewickelten warmgewalzten Stahlblechs mit einer Rate von 30° C/h bis 40° C/h auf eine Abkühlendtemperatur von 350° C bis 400° C.
  6. Verfahren nach Anspruch 5, wobei eine Oberfläche des warmgewalzten Stahlblechs während des Aufwickelns des abgekühlten warmgewalzten Stahlblechs durch ein Wärmerückgewinnungsphänomen eine Temperatur von 720° C bis 750° C erreicht.
EP15893419.0A 2015-05-28 2015-05-28 Warmgewalztes stahlblech mit hervorragender kombinierterkorrosionsbeständigkeit gegen schwefelsäure und salzsäure und herstellungsverfahren dafür Active EP3305936B1 (de)

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PCT/KR2015/005381 WO2016190467A1 (ko) 2015-05-28 2015-05-28 황산 및 염산 복합내식성이 우수한 열연강판 및 그 제조방법

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US (1) US20180148811A1 (de)
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JP (1) JP6549254B2 (de)
KR (1) KR102098511B1 (de)
CN (1) CN107614721B (de)
WO (1) WO2016190467A1 (de)

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CN110629124B (zh) * 2018-06-25 2021-09-17 宝山钢铁股份有限公司 一种耐稀硫酸腐蚀的微合金化钢及其钢板/钢管的热处理方法
KR20200065990A (ko) * 2018-11-30 2020-06-09 주식회사 포스코 황산 및 황산/염산 복합 응축 환경에서 내식성을 갖는 강판 및 그 제조방법
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EP3305936A4 (de) 2018-04-11
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KR20180027534A (ko) 2018-03-14
WO2016190467A1 (ko) 2016-12-01
CN107614721B (zh) 2019-08-13
JP6549254B2 (ja) 2019-07-24
US20180148811A1 (en) 2018-05-31
CN107614721A (zh) 2018-01-19
KR102098511B1 (ko) 2020-04-07

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