US20200071800A1 - High-carbon hot-rolled steel sheet having excellent surface quality and manufacturing method therefor - Google Patents

High-carbon hot-rolled steel sheet having excellent surface quality and manufacturing method therefor Download PDF

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US20200071800A1
US20200071800A1 US16/468,114 US201716468114A US2020071800A1 US 20200071800 A1 US20200071800 A1 US 20200071800A1 US 201716468114 A US201716468114 A US 201716468114A US 2020071800 A1 US2020071800 A1 US 2020071800A1
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steel sheet
rolled steel
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surface quality
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Deuk-Jung Kim
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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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • 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
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/009—Pearlite

Definitions

  • the present invention relates to a hot-rolled steel sheet suitable for construction, tools, vehicle parts, and the like and, more particularly, to a high-carbon hot-rolled steel sheet having an excellent surface quality and a manufacturing method therefor.
  • a high-carbon hot-rolled steel sheet used variously in construction, tools, vehicle parts, and the like, is pickled and cold-rolled at a secondary customer company, and then the steel sheet is heat-treated and molded to form a component according to intended purpose at a final customer company.
  • grain boundary oxidation may easily occur.
  • additional processes are required at the secondary customer company in order to remove this, which may mainly increase manufacturing costs.
  • Patent Document 1 Korean Patent Laid-Open Publication No. 2016-0018805
  • An aspect of the present disclosure may provide a high-carbon hot-rolled steel sheet having an excellent surface quality by significantly reducing the grain boundary oxidation of the high-carbon hot-rolled steel sheet by optimizing an alloy composition and manufacturing conditions, and a method for manufacturing the same.
  • a high-carbon hot-rolled steel sheet having an excellent surface quality includes: carbon (C): 0.3 wt % to 1.3 wt %, silicon (Si): 0.01 wt % to 0.5 wt %, manganese (Mn): 0.3 wt % to 2.0 wt %, aluminum (Al): 0.1 wt % or less, excluding 0 wt %, chromium (Cr): 5.0 wt % or less, excluding 0 wt %, further includes: one or more selected from the group consisting of molybdenum (Mo): 2.0 wt % or less, antimony (Sb): 0.005 wt % to 0.1 wt %, vanadium (V): 0.5 wt % or less, copper (Cu): 0.5 wt % or less, and nickel (Ni): 2.0 wt % or less, and includes:
  • the content of each element means weight %.
  • a method for manufacturing a high-carbon hot-rolled steel sheet having an excellent surface quality includes: reheating a steel slab, satisfying the alloy composition and Relations 1 and 2, described above, in a temperature range of 1100° C. to 1300° C.; producing a hot-rolled steel sheet by rough rolling and finish rolling the reheated steel slab; and coiling the hot-rolled steel sheet in a temperature range of 500° C. to 710° C. after cooling.
  • a high-carbon hot-rolled steel sheet having an excellent surface quality, in which grain boundary oxidation is significantly reduced may be provided.
  • FIG. 1 is an image illustrating cross sections of Comparative Example 6(a) and Inventive Example 7(b) in an embodiment.
  • the inventor of the present disclosure has studied in detail a method for significantly reducing grain boundary oxidation, in providing a high carbon steel hot-rolled steel sheet. As a result, it has been confirmed that grain boundary oxidation on a surface of a hot-rolled steel sheet could be significantly reduced, by thoroughly controlling an alloy composition of the hot-rolled steel sheet while optimizing coiling conditions among manufacturing conditions, thereby resulting in completion of the present disclosure.
  • a high-carbon hot-rolled steel sheet having an excellent surface quality preferably includes C: 0.3% to 1.3%, Si: 0.01% to 0.5%, Mn: 0.3% to 2.0%, Al: 0.1% or less, Cr: 5.0% or less (excluding 0%).
  • Carbon (C) is the most effective element for securing strength. In order to obtain excellent hardness in the present disclosure, it is preferable to add 0.3% or more of C. However, if the content of C exceeds 1.3%, it may cause a defect in a process due to significant hardness during hot rolling.
  • the content of C is preferably controlled to be 0.3% to 1.3%. More preferably, the content of C is controlled to be 0.35% to 1.25%.
  • Si is an element effective for the deoxidation effect.
  • Si is preferably contained in an amount of 0.01% or more. However, if the content of Si exceeds 0.5%, it is not preferable since the possibility of causing grain boundary oxidation on a surface of a hot-rolled steel sheet is increased.
  • the content of Si is preferably controlled to be 0.01% to 0.5%. More preferably, the content of Si is controlled to be 0.1% to 0.4%.
  • Manganese (Mn) is an element effective for securing strength together with the C. If the content of Mn is less than 0.3%, iron sulfide (FeS) may be formed, which may cause grain boundary brittleness at high temperature. On the other hand, if the content of Mn exceeds 2.0%, a quality of a hot-rolled steel sheet may be degraded due to grain boundary oxidation along with center segregation and inclusion formation.
  • FeS iron sulfide
  • the content of Mn is preferably controlled to be 0.3% to 2.0%. More preferably, the content of Mn is controlled to be 0.4% to 1.5%.
  • Aluminum (Al) is an element added for not only the deoxidation effect but also the solid solution strengthening effect. If the content of Al is significant, for example, more than 0.1%, slab cracking may be caused in continuous casting, and grain boundary oxidation may be caused in a final product.
  • the content of Al is preferably controlled to be 0.1% or less, and 0% is excluded.
  • Chromium (Cr) is an element added to enhance the hardenability of steel, and has the effect of inhibiting the generation of rust of iron by forming a passive film in the atmosphere. However, if the content of Cr exceeds 5.0%, it is not preferable since cracking at an edge of a hot-rolled sheet may be caused during cooling.
  • the content of Cr is preferably controlled to be 5.0% or less, and 0% is excluded. More preferably, the content of Cr is controlled to be 3.5% or less.
  • the hot-rolled steel sheet of the present disclosure may further include the following elements to improve physical properties in addition to the alloy composition described above.
  • Mo molybdenum
  • Sb antimony
  • V vanadium
  • Cu copper
  • Ni nickel
  • Molybdenum (Mo) is an element effective for improving hardenability of steel, and may be added for imparting thermal stability of a precipitation strengthening element. However, since Mo is a relatively expensive element, if the content of Mo exceeds 2.0%, manufacturing costs may be increased significantly.
  • the content of Mo is preferably controlled to be 2.0% or less.
  • Antimony (Sb) is an effective element concentrated at grain boundaries at high temperature to inhibit grain boundary oxidation.
  • Sb is an element effectively suppressing the grain boundary oxidation.
  • Sb is preferably added in an amount of 0.005% or more. However, if the content of Sb exceeds 0.1%, it is not preferably since grain boundary embrittlement may be rather caused.
  • the content of Sb is preferably controlled to be 0.005% to 0.1%.
  • V Vanadium (V): 0.5% or less
  • V Vanadium
  • the content of V is preferably controlled to be 0.5% or less.
  • Copper (Cu) is an element added to increase strength and improve corrosion resistance. However, if the content of Cu exceeds 0.5%, it is not preferable since grain boundary brittleness may be caused at high temperature.
  • the content of Cu is preferably controlled to be 0.5% or less.
  • Nickel (Ni) is also an element added to increase the strength and to improve the corrosion resistance, and has an effect of preventing grain boundary embrittlement, caused by Cu, at high-temperature when added together with Cu. However, if the content of Ni exceeds 2.0%, an interface may be non-uniform and thus the descaling properties of the scale may be deteriorated at high temperature.
  • the content of Ni is preferably controlled to be 2.0% or less.
  • the remaining elements of the present disclosure are iron (Fe).
  • Fe iron
  • unintended impurities maybe inevitably mixed from surroundings, and thus, this may not be excluded. Since these impurities are known to a person having skill in the common manufacturing process, all contents will not be particularly described in the present specification, but P, S and N are preferably controlled as follows.
  • Phosphorus (P) is an element which is inevitably added during a steel making process. Since P may cause brittleness due to segregation, the content of P is preferably controlled as low as possible.
  • the content of P may be increased by adding scrap iron or the like in the production of molten iron, the content of P is preferably controlled up to 0.03%, more preferably 0.02% or less.
  • S Sulfur
  • FeS iron sulfide
  • the content of S is preferably controlled as low as possible, and the content of S is preferably controlled up to 0.02% since the content of S may be increased by the addition of scrap iron or the like in the production of molten iron. More preferably, the content of S is controlled to be 0.01% or less.
  • N Nitrogen
  • N has a solid solution strengthening effect.
  • a solid solution element may cause the yield point elongation to lower a surface quality.
  • nitride is precipitated to deteriorate the workability.
  • the content of N is preferably controlled to be 0.01% or less, and 0% is excluded.
  • the relationship among elements may preferably satisfy Relations 1 and 2.
  • the content of each element means weight %.
  • the grain boundary oxidation may not occur. However, if the HI value is 0 or more, the grain boundary oxidation may significantly occur. In this regard, in the present disclosure, when the HI value is 0 or more, the relationship among alloy elements (Mo, Sb, and Cr) is controlled by Relation 2, thereby significantly suppressing the grain boundary oxidation.
  • the hot-rolled steel sheet of the present disclosure satisfying the alloy composition and element relationship preferably includes a ferrite and pearlite composite structure as a microstructure.
  • the hot-rolled steel sheet includes the ferrite in an area fraction of 2% to 70%, and the balance of pearlite. In this case, if the ferrite fraction is less than 2%, it is not preferable since a small amount of elements such as Cr for securing hardenability is contained.
  • the transformation speed is fast or the transformation speed is significantly slow as the case in which a hardenability strengthening element such as Cr, Mo, or the like is excessively added.
  • an area fraction of an oxide located within 10 ⁇ m in a thickness direction from a surface is 5% or less, and the grain boundary oxidation suppressing effect is excellent.
  • a grain boundary oxidation thickness (a depth) formed on the surface of the steel sheet is thin.
  • a thickness of the grain boundary oxidation could be obtained to 2 ⁇ m or less.
  • the high-carbon hot-rolled steel sheet of the present disclosure may be manufactured through a process of [steel slab reheating—hot rolling—cooling and coiling], and conditions for each process will be described in detail below.
  • a steel slab according to the present disclosure satisfying the alloy composition and component relationship (Relations 1 and 2) described above, is prepared, and then the steel slab is reheated in a temperature range of 1100° C. to 1300° C.
  • the reheating process is a process for homogenization of a slab. If a temperature of the reheating process is less than 1100° C., rolling load may be significantly increased during hot rolling, a subsequent process. On the other hand, if the temperature of the reheating process exceeds 1300° C., a surface defect maybe caused during rolling since a surface temperature is high during finish rolling of subsequent hot rolling and thus high temperature oxidation scale grows thicker on a surface, or a defect, in which scale is separated from a surface when a wound coil is uncoiling, may be caused.
  • the steel slab, reheated as described above, is hot rolled to produce a hot-rolled steel sheet, and the hot rolling may include rough rolling and finish rolling.
  • the finish rolling is preferably performed in a temperature range in which an inlet temperature is 900° C. to 1100° C. and an outlet temperature is 800° C. to 950° C.
  • outlet temperature is less than 800° C.
  • rolling load may be significantly increased.
  • a pro-eutectoid ferrite phase is generated and a material may be non-uniform in a width direction.
  • the outlet temperature exceeds 950° C., a structure of a steel sheet may be coarsened, and scale may be thickened and a surface quality may be degraded.
  • the hot-rolled steel sheet, manufactured as described above, is preferably coiled after cooling.
  • the cooling is preferably performed at an average cooling rate of 30° C./s to 60° C./s using water cooling in a run-out table (ROT), by way of example.
  • ROT run-out table
  • the coiling is preferably performed in a temperature range of 500° C. to 710° C. If a temperature during the coiling is less than 500° C., it is not preferable since a shape defect may occur. On the other hand, if the temperature during the coiling exceeds 710° C., it is not preferable since a surface quality may be degraded due to scale peeling.
  • the steel slab having an alloy composition, illustrated in Table 1, was reheated in a temperature range of 1100° C. to 1300° C., and was then hot-rolled to manufacture a hot-rolled steel sheet.
  • finish rolling was performed in a temperature range in which an outlet temperature is 800° C. to 950° C.
  • cooling was performed to perform coiling at a coiling temperature illustrated in Table 2.
  • a cross section was measured using the scanning electron microscopy (SEM), a fraction of an oxide was measured using the oxide picture and image analysis, and a thickness of the grain boundary oxidation was measured.
  • SEM scanning electron microscopy
  • Contrast Example in which an HI value, represented by Relation 1, is less than 0, it was confirmed that occurrence of the grain boundary oxidation is not significant.
  • FIG. 1 is an image illustrating a cross-section of each of Comparative Example 6(a) and Inventive Example 7(b).

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
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  • Metallurgy (AREA)
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  • Physics & Mathematics (AREA)
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  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
US16/468,114 2016-12-14 2017-12-08 High-carbon hot-rolled steel sheet having excellent surface quality and manufacturing method therefor Abandoned US20200071800A1 (en)

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KR1020160170370A KR101830551B1 (ko) 2016-12-14 2016-12-14 표면품질이 우수한 고탄소 열연강판 및 이의 제조방법
KR10-2016-0170370 2016-12-14
PCT/KR2017/014362 WO2018110906A1 (ko) 2016-12-14 2017-12-08 표면품질이 우수한 고탄소 열연강판 및 이의 제조방법

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EP4108798A4 (en) * 2020-02-18 2023-07-26 Posco HIGH CARBON STEEL SHEET HAVING GOOD SURFACE QUALITY, AND METHOD OF MANUFACTURING THEREOF
CN112126850B (zh) * 2020-08-24 2022-02-22 上海衍衡新材料科技有限公司 一种耐蚀针布钢及制备方法
JP7334700B2 (ja) * 2020-09-28 2023-08-29 Ｊｆｅスチール株式会社 厚鋼板およびその製造方法

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JPH02194145A (ja) * 1989-01-20 1990-07-31 Sumitomo Metal Ind Ltd 高炭素薄鋼板
JPH0344422A (ja) * 1989-07-10 1991-02-26 Sumitomo Metal Ind Ltd 高炭素薄鋼板の製造方法
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JP5050433B2 (ja) * 2005-10-05 2012-10-17 Ｊｆｅスチール株式会社 極軟質高炭素熱延鋼板の製造方法
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