WO2016190467A1 - Tôle d'acier laminée à chaud ayant une excellente résistance combinée à la corrosion par l'acide sulfurique et l'acide chlorhydrique et son procédé de fabrication - Google Patents

Tôle d'acier laminée à chaud ayant une excellente résistance combinée à la corrosion par l'acide sulfurique et l'acide chlorhydrique et son procédé de fabrication Download PDF

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Publication number
WO2016190467A1
WO2016190467A1 PCT/KR2015/005381 KR2015005381W WO2016190467A1 WO 2016190467 A1 WO2016190467 A1 WO 2016190467A1 KR 2015005381 W KR2015005381 W KR 2015005381W WO 2016190467 A1 WO2016190467 A1 WO 2016190467A1
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WIPO (PCT)
Prior art keywords
steel sheet
rolled steel
sulfuric acid
hydrochloric acid
corrosion resistance
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PCT/KR2015/005381
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English (en)
Korean (ko)
Inventor
윤정봉
이병호
김종화
Original Assignee
주식회사 포스코
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Application filed by 주식회사 포스코 filed Critical 주식회사 포스코
Priority to US15/577,228 priority Critical patent/US20180148811A1/en
Priority to PCT/KR2015/005381 priority patent/WO2016190467A1/fr
Priority to KR1020187003152A priority patent/KR102098511B1/ko
Priority to CN201580080459.XA priority patent/CN107614721B/zh
Priority to EP15893419.0A priority patent/EP3305936B1/fr
Priority to JP2017561739A priority patent/JP6549254B2/ja
Publication of WO2016190467A1 publication Critical patent/WO2016190467A1/fr

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Classifications

    • 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
    • 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

Definitions

  • the present invention relates to a hot rolled steel sheet excellent in complex corrosion resistance to sulfuric acid and hydrochloric acid that can be preferably applied to materials such as desulfurization of a thermal power plant, denitrification equipment, preheater, and parts thereof, and a manufacturing method thereof.
  • Sulfuric acid or sulfuric acid-hydrochloric acid corrosion resistant steels produce sulfuric acid and hydrochloric acid by producing sulfuric acid and hydrochloric acid by the reaction of sulfur dioxide and chlorine gas exhaust gas generated by burning fossil fuels such as coal or petroleum with water. It is used as a desulfurization and denitrification facility for a serious thermal power plant, or as a heat element material that requires the use of a relatively thick thickness steel plate of a gas gas heater (GGH).
  • GGH gas gas heater
  • Copper (Cu) has a great effect of significantly delaying the corrosion rate of sulfuric acid compared to other additive elements, but if a large amount of copper is added, an appropriate amount of copper (Cu) is added while adding a proper amount of copper (Cu).
  • Steels having a complex addition Japanese Patent Laid-Open No. 1997-025536, Japanese Laid-Open Patent Publication No. 1998-110237, Korean Laid-open Patent Publication No. 2009-0070249, etc. have been developed.
  • One aspect of the present invention is to provide a hot rolled steel sheet having excellent corrosion resistance in a corrosive environment in which sulfuric acid and hydrochloric acid are present in combination and a method of manufacturing the same.
  • C 0.05 ⁇ 0.1%
  • Mn 0.5 ⁇ 1.5%
  • P 0.02% or less
  • S 0.02% or less
  • Al 0.01% ⁇ 0.1%
  • Cu 0.2 ⁇ 0.6 %
  • Sb 0.05-0.1%
  • Cu and Sb are concentrated within 500 nm in the thickness direction from the surface, and the loss of corrosion for the solution of sulfuric acid 16.9% by volume + 0.35% by volume hydrochloric acid is 2.0mg It provides a hot rolled steel sheet having excellent corrosion resistance of sulfuric acid and hydrochloric acid of less than / cm 2 / hr.
  • C 0.05 ⁇ 0.1%
  • Mn 0.5 ⁇ 1.5%
  • P 0.02% or less
  • S 0.02% or less
  • Al 0.01% ⁇ 0.1%
  • Cu 0.2 ⁇
  • Sb 0.05-0.1%
  • balance Fe and other unavoidable impurities at 1100-1300 ° C .
  • the hot rolled steel sheet of the present invention can be suitably applied to materials requiring relatively thick thicknesses of power plant denitrification, desulfurization equipment, flue gas piping of boilers, and preheaters in which complex corrosion of sulfuric acid and hydrochloric acid occurs. It has the effect of greatly extending the life of the.
  • the inventors of the present invention have repeatedly studied in both aspects of the composition and manufacturing method of the steel sheet to minimize the content of copper (Cu) in the sulfuric acid-hydrochloric acid corrosion resistant steel, while ensuring a high composite corrosion resistance,
  • Cu copper
  • Sb is added as a composition and the cooling conditions after hot rolling and the cooling conditions after winding are appropriately controlled, the Cu and Sb concentration layers are formed on the surface of the steel sheet in a sulfuric acid and hydrochloric acid corrosion environment to have an appropriate thickness, thereby providing excellent composite corrosion resistance. It was confirmed that it could be ensured and came to complete this invention.
  • Carbon (C) is an advantageous element for securing the strength of the steel sheet, when the content is less than 0.05% by weight, it is difficult to secure the target strength and there is a problem that the wear resistance is lowered. On the other hand, if the content exceeds 0.1% by weight, weldability is greatly degraded during welding of the steel sheet, so that defects are likely to occur, and corrosion resistance is also greatly reduced. Therefore, in the present invention, the content of carbon is preferably limited to 0.05 to 0.1% by weight.
  • Manganese (Mn) is an element that serves to prevent hot shortness caused by solid solution sulfur by precipitating sulfur dissolved in steel as manganese sulfide and expressing a solid solution strengthening effect.
  • the content of manganese is less than 0.5% by weight, manganese sulfide may not be sufficiently precipitated, causing red brittleness due to solid solution sulfur, and it is difficult to secure a target strength.
  • the content of the manganese is preferably limited to 0.5 to 1.5% by weight.
  • Phosphorus (P) 0.02 wt% or less
  • Phosphorus (P) is an element that is inevitably added in steel, and if its content exceeds 0.02% by weight, there is a problem in that the target composite corrosion resistance is greatly reduced. Therefore, it is desirable to manage the content of P to 0.02% by weight or less.
  • S Sulfur
  • S is an element that is solid-solubilized in steel to cause red-brittle brittleness, so it is desirable to control the content as low as possible. If the content exceeds 0.02% by weight, there is a problem that the possibility of defects due to red-hot brittleness increases, so it is preferable to manage the content of S to 0.02% by weight or less.
  • Aluminum (Al) is an element that is inevitably added during the production of aluminum-killed steel, and preferably 0.01 wt% or more for the deoxidation effect.
  • the content of aluminum exceeds 0.1% by weight, the possibility of causing surface defects of the steel sheet is not only increased, but there is a problem in that weldability is lowered. Therefore, in the present invention, it is preferable to limit the content of Al to 0.01 to 0.1% by weight.
  • Copper (Cu) is an element added in consideration of the complex corrosion characteristics of sulfuric acid and hydrochloric acid, and if the content is too low, it is difficult to secure the target complex corrosion resistance, so it is preferably added at 0.2% or more. It is more preferable to add more than%. Complex corrosion resistance is improved as the content of Cu increases, but if the content is too high, the corrosion resistance increase greatly decreases, the manufacturing cost increases rapidly, and there is a problem of causing surface defects such as radial cracking. Therefore, in this invention, it is preferable that the upper limit of content of Cu is 0.6 weight%, and it is more preferable that it is 0.5 weight%.
  • Antimony (Sb) is an element which is essentially added together with Cu to improve complex corrosion resistance, and is an element that can effectively improve complex corrosion resistance by forming a Cu-Sb composite oxide in a corrosive environment. If the content of the antimony is less than 0.05% by weight it is difficult to obtain the above-described effect, whereas if the content of more than 0.1% by weight not only saturation of the above-described effect, there is a problem that the manufacturing cost rises sharply, in consideration of this, 0.1% by weight or less It is preferable to add by.
  • the remainder consists of Fe and unavoidable impurities.
  • the sum of the content of W, Mo, Co and Ni is more preferably controlled to less than 10ppm. This is because these elements may deteriorate the material properties of the hot rolled steel sheet, such as ductility.
  • the hot-rolled steel sheet of the present invention it is preferable that Cu and Sb are concentrated within 500 nm from the surface thereof. These elements are concentrated on the surface during the production of the steel sheet, but when exposed to the corrosive environment by sulfuric acid and hydrochloric acid, the elements are changed to the form of Cu-Sb composite oxide, thereby improving the corrosion resistance of the hot-rolled steel sheet to a very good level.
  • the content of the concentrated Cu and Sb is not particularly limited, and as described below, it may be sufficient to form an oxide layer having a thickness of 400 nm or more from the surface of the hot-rolled steel sheet in a corrosive environment by sulfuric acid and hydrochloric acid. .
  • the thickness of the oxide layer is less than 400 nm, it is difficult to secure the corrosion resistance targeted by the present invention.
  • the corrosion resistance improves more as the thickness of the said oxide layer becomes thick, in this invention, it does not specifically limit about the upper limit of the thickness of the said oxide layer.
  • the thickness of the oxide layer is more preferably 400 to 500 nm.
  • the hot rolled steel sheet of the present invention has a very good composite corrosion resistance with a loss of corrosion of 16.9% by volume sulfuric acid + 0.35% by volume hydrochloric acid solution of 2.0 mg / cm 2 / hr or less.
  • the reheating temperature is less than 1100 °C, there is a problem that it is difficult to ensure the temperature during the subsequent hot rolling, whereas, if the reheating temperature exceeds 1300 °C, the low melting point Cu is eluted and cracks (crack) on the surface of the slab There is a problem that is likely to occur.
  • the reheated steel slab is hot rolled and finished hot rolled at 850 to 950 ° C. to obtain a hot rolled steel sheet.
  • finish hot rolling temperature is less than 850 °C, there is a problem that the elongation is greatly reduced due to the formation of the drawn grains, the material deviation in each direction is non-uniform, whereas if the finish hot rolling temperature exceeds 950 °C, the austenite grains are coarse to increase the hardenability There is a growing problem.
  • the hot rolled steel sheet is quenched to 120 ⁇ 150 °C / s based on the surface temperature of the steel sheet.
  • the cooling rate is less than 120 °C / s, the surface temperature of the hot-rolled steel sheet is too high, the driving force for the oxide-forming elements existing in the steel to move to the surface, the final oxide is formed when the steel sheet is exposed to the complex corrosive environment There is a difficult problem.
  • the cooling rate is preferably 120 ⁇ 150 °C / s.
  • the cooled hot rolled steel sheet is wound at 650 ⁇ 750 °C. If the coiling temperature is less than 650 °C it may be difficult to ensure the sufficient corrosion resistance since the movement of atoms in the winding process is not easy to form a concentrated layer is difficult to form an oxide layer in a corrosive environment. When the coiling temperature exceeds 750 ° C, defects may occur such that the coiled steel sheet is so high that the reheating temperature is so high that the coiling temperature is preferably in the range of 650 to 750 ° C.
  • the surface of the steel sheet is 720 ⁇ 750 °C by the recuperation phenomenon. Even though the temperature inside the steel sheet is in the range of 650 to 750 ° C. through the cooling process, the surface of the steel sheet has a temperature lower than the temperature range by quenching. Therefore, by going through the recuperation process, the movement of the alloying elements advantageous for forming the oxide layer may be activated, and through this, the concentration layer may be formed to a sufficient thickness. In order to fully acquire the said effect, it is preferable that the surface temperature of the steel plate which passed through this reheating is 720 degreeC or more. However, even after a sufficient recuperation process, the surface temperature of the steel sheet is difficult to exceed 750 °C.
  • the wound steel sheet is slowly cooled to a cooling stop temperature of 350 to 400 ° C. at a rate of 30 to 40 ° C./hr.
  • the cooling rate is preferably in the range of 40 ° C / hr or less. .
  • the cooling rate is preferably in the range of 30 ⁇ 40 °C / hr.
  • the cooling stop temperature is less than 350 °C there is a problem that the material properties of the hot-rolled steel sheet, for example, ductility is deteriorated, productivity is lowered, while if the cooling stop temperature is higher than 400 °C, the thickness of the concentrated layer is not enough to provide corrosion resistance There may be an inferior problem. Therefore, the cooling stop temperature is preferably in the range of 350 ⁇ 400 °C.
  • the steel ingots prepared by dissolving them in the composition of compositions as shown in Table 1 were maintained at 1200 ° C. for 1 hour and then hot rolled. At this time, the finish hot rolling was carried out at 900 °C, to produce a hot rolled steel sheet having a final thickness of 4.5mm. Then, it was maintained after cooling and winding up under the conditions shown in Table 2 below. Then, slow cooling was performed to a cooling end temperature of 380 ° C. at a rate of 35 ° C./h to prepare a final hot rolled steel sheet.
  • each specimen was immersed in a solution of 16.9% sulfuric acid + 0.35% hydrochloric acid at 60 ° C. for 6 hours, and then the corrosion loss of each specimen was measured. Is shown in Table 2 below.
  • the thickness of the oxide layer (corrosion layer) formed on the surface of the steel sheet after the completion of deposition under sulfuric acid-hydrochloric acid complex corrosion conditions was measured and shown in Table 2.
  • Comparative Example 1 satisfies the alloy composition of the present invention, but the coiling temperature is low to 500 ° C, the oxide layer was not sufficiently formed, it can be seen that the corrosion loss is 4.5mg / cm2 / hr very low corrosion resistance.
  • Comparative Examples 2 to 4 satisfy the alloy composition of the present invention, but because the cooling rate is low as 10 °C / s, the oxide layer was not formed sufficiently, which results in corrosion loss of 3.2 mg / cm2 / hr or more as corrosion resistance It can be seen that it is very low.

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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)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

La présente invention concerne : une tôle d'acier laminée à chaud ayant une excellente résistance combinée à l'acide sulfurique et à l'acide chlorhydrique ; et un procédé pour la fabriquer. Sous un aspect, la présente invention concerne une tôle d'acier laminée à chaud ayant une excellente résistance combinée à la corrosion par l'acide sulfurique et l'acide chlorhydrique, la tôle d'acier laminée à chaud contenant, en % poids, de 0,05 à 0,1 % de C, de 0,5 à 1,5 % de Mn, 0,02 % ou moins de P, 0,02 % ou moins de S, de 0,01 à 0,1 % d'Al, de 0,2 à 0,6 % de Cu, de 0,05 à 0,1 % de Sb, le reste étant constitué de Fe et des impuretés inévitables, un enrichissement en Cu et Sb étant effectué à l'intérieur sur 500 nm à partir de la surface dans le sens de l'épaisseur, et la perte de masse en présence d'une solution comprenant 16,9 % en volume d'acide sulfurique + 0,35 % en volume d'acide chlorhydrique étant de 2,0 mg/cm2/h.
PCT/KR2015/005381 2015-05-28 2015-05-28 Tôle d'acier laminée à chaud ayant une excellente résistance combinée à la corrosion par l'acide sulfurique et l'acide chlorhydrique et son procédé de fabrication WO2016190467A1 (fr)

Priority Applications (6)

Application Number Priority Date Filing Date Title
US15/577,228 US20180148811A1 (en) 2015-05-28 2015-05-28 Hot-rolled steel sheet having excellent composite corrosion resistance to sulfuric acid and hydrochloric acid and manufacturing method therefor
PCT/KR2015/005381 WO2016190467A1 (fr) 2015-05-28 2015-05-28 Tôle d'acier laminée à chaud ayant une excellente résistance combinée à la corrosion par l'acide sulfurique et l'acide chlorhydrique et son procédé de fabrication
KR1020187003152A KR102098511B1 (ko) 2015-05-28 2015-05-28 황산 및 염산 복합내식성이 우수한 열연강판 및 그 제조방법
CN201580080459.XA CN107614721B (zh) 2015-05-28 2015-05-28 硫酸及盐酸复合耐蚀性优异的热轧钢板及其制造方法
EP15893419.0A EP3305936B1 (fr) 2015-05-28 2015-05-28 Tôle d'acier laminée à chaud ayant une excellente résistance combinée à la corrosion par l'acide sulfurique et l'acide chlorhydrique et son procédé de fabrication
JP2017561739A JP6549254B2 (ja) 2015-05-28 2015-05-28 硫酸及び塩酸複合耐食性に優れた熱延鋼板及びその製造方法

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/KR2015/005381 WO2016190467A1 (fr) 2015-05-28 2015-05-28 Tôle d'acier laminée à chaud ayant une excellente résistance combinée à la corrosion par l'acide sulfurique et l'acide chlorhydrique et son procédé de fabrication

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Publication Number Publication Date
WO2016190467A1 true WO2016190467A1 (fr) 2016-12-01

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Country Status (6)

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US (1) US20180148811A1 (fr)
EP (1) EP3305936B1 (fr)
JP (1) JP6549254B2 (fr)
KR (1) KR102098511B1 (fr)
CN (1) CN107614721B (fr)
WO (1) WO2016190467A1 (fr)

Cited By (1)

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CN115161547A (zh) * 2022-04-27 2022-10-11 日照钢铁控股集团有限公司 一种耐大气腐蚀花纹板的制造方法

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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
KR102709606B1 (ko) * 2019-11-13 2024-09-26 닛폰세이테츠 가부시키가이샤 열간 압연 강재
CN114599804B (zh) * 2019-11-13 2024-03-29 日本制铁株式会社 钢材
KR102326323B1 (ko) * 2019-12-19 2021-11-12 주식회사 포스코 내마모성과 복합내식성이 우수한 강판 및 그 제조방법
KR102468054B1 (ko) 2020-11-19 2022-11-17 주식회사 포스코 내마모성과 내식성이 우수한 용접이음부
KR102352601B1 (ko) 2020-11-19 2022-01-18 주식회사 포스코 피복 아크 용접재료

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JP2018519422A (ja) 2018-07-19
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