WO2022131535A1 - High-hardness bullet-proof steel with excellent low-temperature impact toughness and method for manufacturing same - Google Patents
High-hardness bullet-proof steel with excellent low-temperature impact toughness and method for manufacturing same Download PDFInfo
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
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- C21D1/26—Methods of annealing
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- 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
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- 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
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- 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
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- 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
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- 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
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- 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
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- 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
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- 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
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- 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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- 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
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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- 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
- C21D2211/001—Austenite
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- 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
- C21D2211/008—Martensite
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- 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
Definitions
- the present invention relates to a material suitable for an armored vehicle and an explosion-proof structure, and more particularly, to a bulletproof steel having excellent low-temperature impact toughness and high hardness, and a method for manufacturing the same.
- Bulletproof steel is a material with a very hard surface for the main function of blocking bullets.
- Non-ferrous materials have the advantage of weight reduction compared to steel materials, but are relatively expensive and have poor workability.
- steel materials are widely used as materials for self-propelled guns and wheeled armored vehicles because they are relatively inexpensive and can change properties such as hardness relatively easily.
- Hardness is one of the important properties for securing the performance of bulletproof steel, but simply because the hardness is high does not guarantee bulletproof performance.
- the high hardness property is a factor that increases the resistance that prevents bullets from penetrating the material, but the material having the high hardness property cannot be said to necessarily provide excellent bulletproof performance because it can be broken relatively easily. Therefore, rather than simply increasing the hardness of the material, development of a material capable of securing not only high hardness but also brittle fracture resistance against external impact is required.
- Patent Document Korean Patent Publication No. 10-2018-0043788 (published on April 30, 2018)
- An object of the present invention is to provide a bulletproof steel having high hardness characteristics as well as excellent low-temperature impact toughness and a method for manufacturing the same.
- the subject of the present invention is not limited to the above.
- the subject of the present invention will be understood from the overall content of the present specification, and those of ordinary skill in the art to which the present invention pertains will have no difficulty in understanding the additional subject of the present invention.
- High-hardness bulletproof steel excellent in low-temperature impact toughness by weight, carbon (C): 0.18 to 0.25%, silicon (Si): 1.0 to 2.0%, manganese (Mn): 0.5 to 1.6 %, Nickel (Ni): 0.5 to 1.2%, Chromium (Cr): 0.4 to 1.5%, Phosphorus (P): 0.05% or less, Sulfur (S): 0.02% or less, Nitrogen (N): 0.006% or less, Aluminum (Al): 0.07% or less (excluding 0%), molybdenum (Mo): 0.1 to 0.5%, niobium (Nb): 0.01 to 0.05%, boron (B): 0.0002 to 0.005%, calcium (Ca): 0.0005 ⁇ 0.004%, including the remaining Fe and unavoidable impurities, satisfying the following [Relational Expression 1], may include a complex structure containing retained austenite in the tempered martensite matrix structure
- [C] and [Si] mean the contents (wt%) of carbon (C) and silicon (Si) contained in the steel sheet, and 0 is substituted if the corresponding components are not intentionally added.
- the bulletproof steel may further include one or more of titanium (Ti): 0.005 to 0.025% and vanadium (V): 0.2% or less by weight%.
- the fraction of tempered martensite may be 90 area% or more, and the fraction of retained austenite may be 0.5 area% to 5 area%.
- the bullet-proof steel may have a surface hardness of 360 to 440HB, and an impact absorption energy at -40°C of 27J or more.
- the bulletproof steel may have a thickness of 6 to 40 mm.
- the method for manufacturing high-hardness ballistic steel having excellent low-temperature impact toughness is, in weight %, carbon (C): 0.18 to 0.25%, silicon (Si): 1.0 to 2.0%, manganese (Mn): 0.5 ⁇ 1.6%, Nickel (Ni): 0.5 to 1.2%, Chromium (Cr): 0.4 to 1.5%, Phosphorus (P): 0.05% or less, Sulfur (S): 0.02% or less, Nitrogen (N): 0.006% or less , Aluminum (Al): 0.07% or less (excluding 0%), Molybdenum (Mo): 0.1 to 0.5%, Niobium (Nb): 0.01 to 0.05%, Boron (B): 0.0002 to 0.005%, Calcium (Ca) : 0.0005 to 0.004%, including the remaining Fe and unavoidable impurities, preparing a steel slab that satisfies the following [Relational Expression 1]; heating the steel
- [C] and [Si] mean the content (wt%) of carbon (C) and silicon (Si) contained in the steel slab, and 0 is substituted if the component is not intentionally added. .
- the steel slab may further include one or more of titanium (Ti): 0.005 to 0.025% and vanadium (V): 0.2% or less by weight%.
- the re-heating time may be 1.3t+10 minutes (t: plate thickness (mm)) or more.
- the holding time may be 1.9t+10 minutes (t: plate thickness (mm)) or more.
- the bulletproof steel excellent in low-temperature toughness while having high hardness can be provided.
- the present invention can provide a bulletproof steel having a target level of physical properties without additional heat treatment from the optimization of the alloy composition and manufacturing conditions, and there is an economically advantageous effect.
- the present invention relates to a high-hardness bulletproof steel having excellent low-temperature impact toughness and a method for manufacturing the same, and preferred embodiments of the present invention will be described below. Embodiments of the present invention may be modified in various forms, and the scope of the present invention should not be construed as being limited to the embodiments described below. The present embodiments are provided in order to further detailed the present invention to those of ordinary skill in the art to which the present invention pertains.
- the present inventors have studied in depth to provide a steel material that can be suitably applied to track-type armored vehicles and explosion-proof structures, and has excellent properties such as high hardness properties and low-temperature impact toughness, which are core properties required.
- Carbon (C) is effective for improving strength and hardness in steel having a low-temperature transformation phase such as martensite or bainite phase, and is an effective element for improving hardenability.
- the present invention may contain 0.18% or more of carbon (C).
- a preferable lower limit of the carbon (C) content may be 0.19%, and a more preferable lower limit of the carbon (C) content may be 0.20%.
- the present invention may limit the upper limit of the carbon (C) content to 0.25%.
- the upper limit of the preferred carbon (C) content may be 0.24%.
- Silicon (Si) is an element effective for strength improvement due to solid solution strengthening along with deoxidation effect, and is an element that promotes the formation of retained austenite by suppressing the formation of carbides such as cementite in steels containing a certain amount of carbon (C) or more It is also In particular, retained austenite homogeneously distributed in steel having low-temperature transformation phases such as martensite and bainite can effectively contribute to the improvement of impact toughness without reducing strength. Therefore, in order to obtain the above-described effect, the present invention may contain 1.0% or more of silicon (Si). A preferable lower limit of the silicon (Si) content may be 1.1%, and a more preferable lower limit of the silicon (Si) content may be 1.2%.
- the present invention may limit the upper limit of the silicon (Si) content to 2.0%.
- a preferable upper limit of the silicon (Si) content may be 1.9%, and a more preferable upper limit of the silicon (Si) content may be 1.8%.
- Manganese (Mn) is an advantageous element for suppressing the formation of ferrite and improving the hardenability of steel by lowering the Ar3 temperature to increase strength and toughness.
- 0.5% or more of manganese (Mn) may be included in order to secure a desired level of hardness.
- a preferred lower limit of the manganese (Mn) content may be 0.6%, and a more preferred lower limit of the manganese (Mn) content may be 0.7%.
- the present invention may limit the upper limit of the manganese (Mn) content to 1.6%.
- the upper limit of the preferable manganese (Mn) content may be 1.5%, and the upper limit of the more preferable manganese (Mn) content may be 1.45%.
- Nickel (Ni) is an element advantageous for simultaneously improving the strength and toughness of steel.
- the present invention may contain 0.5% or more of nickel (Ni).
- a preferred lower limit of the nickel (Ni) content may be 0.6%, and a more preferred lower limit of the nickel (Ni) content may be 0.7%.
- the present invention may limit the upper limit of the nickel (Ni) content to 1.2%.
- a preferable upper limit of the nickel (Ni) content may be 1.17%, and a more preferable upper limit of the nickel (Ni) content may be 1.15%.
- Chromium (Cr) is an element that improves the strength by increasing the hardenability of steel, and effectively contributes to securing the hardness of the surface and the center of the steel.
- Cr chromium
- the present invention may include chromium (Cr) of 0.4% or more.
- a preferred lower limit of the chromium (Cr) content may be 0.45%.
- the present invention may limit the upper limit of the chromium (Cr) content to 1.5%.
- a preferable upper limit of the chromium (Cr) content may be 1.4%, and a more preferable upper limit of the chromium (Cr) content may be 1.3%.
- Phosphorus (P) is an element that is unavoidably contained in steel, and is also an element that inhibits the toughness of steel. Therefore, it is desirable to lower the content as much as possible.
- the upper limit of the phosphorus (P) content can be limited to 0.05%. More advantageously, it can be limited to 0.03% or less. However, 0% may be excluded in consideration of the unavoidable content level.
- Sulfur (S) is an element that is unavoidably contained in steel, and is also an element that forms MnS inclusions and impairs the toughness of steel. Therefore, it is desirable to lower the content as much as possible.
- the sulfur (S) is contained at a maximum of 0.02%, there is no significant effect on the physical properties of the steel, so the upper limit of the sulfur (S) content can be limited to 0.02%. More advantageously, it can be limited to 0.01% or less. However, 0% may be excluded in consideration of the unavoidable content level.
- Nitrogen (N) is an advantageous component for improving the strength of steel by forming precipitates in steel, but when its content is above a certain level, it may rather cause a decrease in the toughness of the steel.
- the present invention may limit the upper limit of the nitrogen (N) content to 0.006%. However, 0% may be excluded in consideration of the unavoidable content level.
- Aluminum (Al) is an effective element for lowering the oxygen content in molten steel as a deoxidizer of steel. However, if the aluminum (Al) content is excessive, the cleanliness of the steel may be impaired, and the present invention may limit the upper limit of the aluminum (Al) content to 0.07%.
- 0% may be excluded from the lower limit of the aluminum (Al) content, The lower limit may be 0.01%.
- Molybdenum (Mo) is an element advantageous to increase the hardenability of steel and, in particular, to improve the hardness of a thick material having a thickness greater than or equal to a certain level.
- the present invention may contain 0.1% or more of molybdenum (Mo).
- a preferred lower limit of the molybdenum (Mo) content may be 0.11%, and a more preferred lower limit of the molybdenum (Mo) content may be 0.12%.
- the present invention may limit the upper limit of the molybdenum (Mo) content to 0.5%.
- the upper limit of the preferable molybdenum (Mo) content may be 0.48%, and the upper limit of the more preferable molybdenum (Mo) content may be 0.45%.
- Niobium (Nb) is dissolved in austenite to increase the hardenability of austenite, and is an effective component for increasing the strength of steel and suppressing austenite grain growth by forming carbonitrides such as Nb(C,N).
- the present invention may include 0.01% or more of niobium (Nb).
- the present invention may limit the upper limit of the niobium (Nb) content to 0.05%.
- a preferable upper limit of the niobium (Nb) content may be 0.04%, and a more preferable upper limit of the niobium (Nb) content may be 0.03%.
- Boron (B) is an element that effectively contributes to strength improvement by increasing the hardenability of steel even with a small amount of addition.
- the present invention may contain 0.0002% or more of boron (B).
- a preferable lower limit of the content of boron (B) may be 0.0005%, and a more preferable lower limit of the content of boron (B) may be 0.001%.
- the present invention may limit the upper limit of the boron (B) content to 0.005%.
- a preferable upper limit of the content of boron (B) may be 0.004%, and a more preferable upper limit of the content of boron (B) may be 0.003%.
- Calcium (Ca) has good bonding strength with sulfur (S), so it generates CaS around (perimeter) MnS to suppress elongation of MnS, and is an advantageous element for improving toughness in a direction perpendicular to the rolling direction.
- CaS generated by the addition of calcium (Ca) may increase corrosion resistance under a humid external environment.
- the present invention may include calcium (Ca) of 0.0005% or more.
- a preferred lower limit of the calcium (Ca) content may be 0.001%.
- the present invention may limit the upper limit of the calcium (Ca) content to 0.004%.
- the upper limit of the preferable calcium (Ca) content may be 0.003%.
- the bulletproof steel of the present invention may further include the following elements for the purpose of advantageously securing target physical properties.
- the bulletproof steel of the present invention may further include one or more of titanium (Ti) and vanadium (V).
- Titanium (Ti) is an element that maximizes the effect of boron (B), which is an element beneficial to improving hardenability of steel. That is, since the titanium (Ti) combines with nitrogen (N) in the steel to precipitate TiN, the content of dissolved nitrogen (N) is reduced, and the formation of BN is suppressed to increase boron (B) in solid solution to improve hardenability. can be maximized. In order to sufficiently obtain the above-described effects, titanium (Ti) of 0.005% or more may be contained. However, when the content is excessive, coarse TiN precipitates are formed, which may cause a decrease in the toughness of the steel, so the present invention may limit the upper limit of the titanium (Ti) content to 0.025%.
- V Vanadium (V): 0.2% or less (including 0%)
- Vanadium (V) forms VC carbide upon reheating after hot rolling, suppressing the growth of austenite grains, improving hardenability of steel, and is an advantageous element for securing strength and toughness.
- vanadium (V) is a relatively expensive element, the upper limit of the amount may be limited to 0.2% in consideration of the manufacturing cost.
- the bulletproof steel according to an aspect of the present invention may include the remaining Fe and other unavoidable impurities in addition to the above-described components.
- unintended impurities from raw materials or the surrounding environment may inevitably be mixed in the normal manufacturing process, it cannot be entirely excluded. Since these impurities are known to those of ordinary skill in the art, all contents thereof are not specifically mentioned in the present specification.
- additional addition of effective ingredients other than the above-mentioned ingredients is not entirely excluded.
- the bulletproof steel according to an aspect of the present invention may satisfy the following [Relational Expression 1].
- [C] and [Si] mean the contents (wt%) of carbon (C) and silicon (Si) contained in the steel sheet, and 0 is substituted if the corresponding components are not intentionally added.
- the inventor of the present invention has conducted an in-depth study on a method to simultaneously secure high hardness characteristics and excellent low-temperature impact toughness of a steel sheet, It was derived that it is effective to control the relative content range.
- the present invention not only controls the content range of individual alloy compositions included in the steel sheet to a certain range, but also controls the relative content range of carbon (C) and silicon (Si) to a certain range as shown in [Relational Expression 1], so that high hardness Characteristics and excellent low-temperature impact toughness can be effectively reconciled.
- 10*[C]*[Si] defined by Relation 1 may be 2.9 or more.
- the bulletproof steel of the present invention having the above-described alloy composition may have a complex structure including retained austenite in the tempered martensite matrix structure as a microstructure, and may further include other unavoidable structures.
- the preferred fraction of retained austenite may be 1 area% to 10 area%, and the fraction of tempered martensite may be 90 area% or more.
- Retained austenite is a structure that remains in a state that does not completely transform into martensite during rapid cooling heat treatment, and has relatively low hardness compared to martensite, but has excellent toughness.
- the ballistic steel of the present invention may contain 1 area% or more of retained austenite for this effect, and more preferably 2 area% or more of retained austenite.
- the retained austenite is excessively formed, the low-temperature impact toughness is greatly increased, while it is difficult to secure a target hardness property.
- the upper limit of the retained austenite fraction may be 5 area%, and the lower limit of the tempered martensite fraction may be 95 area%.
- the bulletproof steel of the present invention may have the above-described microstructure configuration over the entire thickness.
- the bullet-proof steel of the present invention having the proposed microstructure in addition to the alloy composition described above may have a thickness of 6 to 40 mm, and the surface hardness of such bullet-proof steel is 360-440 HB, which is ultra-high hardness, and the shock absorption energy at -40 ° C. 27J or more may have excellent low-temperature toughness.
- the surface hardness refers to the average value of three measurements of the surface of the bulletproof steel in the thickness direction after milling in the thickness direction using a Brinell hardness tester (load 3000kgf, 10mm tungsten indentation hole).
- the steel slab of the present invention has an alloy composition corresponding to the alloy composition (including [Relational Expression 1]) of the hot-rolled steel sheet described above, the description of the alloy composition of the steel slab is replaced by the description of the alloy composition of the hot-rolled steel sheet. .
- the steel slab may be manufactured through a process of [heating - rolling - primary heat treatment (quenching) - secondary heat treatment (tempering)].
- a process of [heating - rolling - primary heat treatment (quenching) - secondary heat treatment (tempering)] a process of [heating - rolling - primary heat treatment (quenching) - secondary heat treatment (tempering)].
- the heating temperature is less than 1050 °C, the deformation resistance of the steel becomes large, so that the subsequent rolling process cannot be effectively performed, whereas when the temperature exceeds 1250 °C, the austenite grains become coarse and there is a risk of forming a non-uniform structure.
- the heating of the steel slab can be performed in a temperature range of 1050 ⁇ 1250 °C.
- the heated steel slab can be rolled according to the above, and in this case, it can be manufactured into a hot-rolled steel sheet through the processes of rough rolling and finish hot rolling.
- the heated steel slab is rough-rolled in a temperature range of 950 to 1150° C. to produce a bar, and then finish hot rolling can be performed in a temperature range of 850 to 950° C.
- the rough rolling temperature is less than 950° C.
- the pressure is relatively weak
- the deformation cannot be sufficiently transmitted to the center of the slab thickness direction, and as a result, there is a fear that defects such as voids may not be removed.
- the temperature exceeds 1150° C.
- the recrystallized grain size becomes too coarse, which may be harmful to toughness.
- the temperature during the finish hot rolling is less than 850 ° C, two-phase rolling is performed and there is a fear that ferrite is generated in the microstructure, whereas when the temperature exceeds 950 ° C, the grain size of the final structure becomes coarse and the low-temperature toughness is inferior there is a problem.
- the hot-rolled steel sheet manufactured through the above-described rolling process is air-cooled to room temperature, it is heated in a temperature range of 880 to 930° C. for a re-heating time of 1.3t+10 minutes (t: plate thickness (mm)) or more.
- the heating is for reverse transformation of a hot-rolled steel sheet composed of ferrite and pearlite into austenite single phase, and when the heating temperature is less than 880 ° C, austenitization is not sufficiently achieved, so coarse soft ferrite is mixed, and accordingly, the hardness of the final product may be lowered.
- the temperature exceeds 930 °C, the austenite grains become coarse and hardenability is increased, but there is a disadvantage in terms of thermal efficiency in mass production. Therefore, it is preferable to perform heating during the primary heat treatment in the range of 880 to 930 °C.
- the lower limit of the heating temperature is more preferably 885°C, still more preferably 890°C, and most preferably 895°C.
- the upper limit of the heating temperature is more preferably 925°C, even more preferably 920°C, and most preferably 915°C.
- the heating time of the primary heat treatment is less than 1.3t + 10 minutes (t: plate thickness (mm))
- austenitization does not occur sufficiently, so that a phase transformation by subsequent rapid cooling, that is, a martensitic structure can be sufficiently obtained.
- the heating time is preferably 1.3t + 10 minutes (t: plate thickness (mm)) or more.
- the heating time is more preferably 1.3t+12 minutes (t: plate thickness (mm)) or more, even more preferably 1.3t+13 minutes (t: plate thickness (mm)) or more, and 1.3t+ Most preferably, it is 15 minutes (t: plate thickness (mm)) or longer.
- the heating time is preferably 1.3t + 60 minutes (t: plate thickness (mm)) or less.
- the heating time is more preferably 1.3t+50 minutes (t: plate thickness (mm)) or less, more preferably 1.3t+40 minutes (t: plate thickness (mm)) or less, and more preferably 1.3t+ Most preferably, it is 30 minutes (t: plate thickness (mm)) or less.
- the heated hot-rolled steel sheet may be cooled to 120° C. or less at a cooling rate of 10° C./s or more based on the central plate thickness (eg, 1/2t point, t: plate thickness (mm)).
- the cooling is rapid cooling through water cooling.
- the cooling rate is less than 10°C/s or when the cooling end temperature exceeds 120°C, there is a risk that a ferrite phase is formed during cooling or a bainite phase is excessively formed.
- the cooling is preferably performed to 120° C. or less at a cooling rate of 10° C./s or more. The faster the cooling rate is, the more advantageous it is to form the microstructure to be obtained in the present invention.
- the upper limit of the cooling rate is not particularly limited, and a person skilled in the art may appropriately set the upper limit in consideration of the equipment limit.
- the cooling end temperature is more preferably 100° C. or less, still more preferably 80° C. or less, and most preferably 50° C. or less.
- the hot-rolled steel sheet manufactured through the above-described primary heat treatment can be heated to a temperature range of 350° C. or less to maintain 1.9 t+10 minutes (t: plate thickness (mm)) or more.
- the reheating is to release the internal stress of the hot-rolled steel sheet fully composed of martensite after quenching.
- the hardness may be slightly reduced, but toughness can be secured.
- bulletproof steel not only high hardness but also excellent low-temperature impact toughness is essential.
- the tempering temperature exceeds 350° C., the dislocation density inside the martensite is excessively reduced, and thus the hardness of the final product may be reduced.
- the tempering temperature is too low, it is possible to prevent hardness decrease, but the dislocation density is too high, which is disadvantageous in terms of securing impact toughness.
- the lower limit of the tempering temperature is not separately specified, but it is preferably 100° C. or higher in order to obtain the above-described effect. More preferably, tempering is performed at a temperature of 125°C or higher, and still more preferably 150°C or higher.
- the lower limit of the holding time during the tempering is not particularly limited.
- the holding time during the tempering is less than 1.9t + 10 minutes (t: plate thickness (mm))
- heat treatment is performed at a relatively low temperature for a short time, so that the central portion of the thickness compared to the surface may not be sufficiently heated. Therefore, the holding time during the tempering is preferably 1.9t + 10 minutes (t: plate thickness (mm)) or more.
- the holding time during the tempering is more preferably 1.9t+12 minutes (t: plate thickness (mm)) or more, more preferably 1.9t+15 minutes (t: plate thickness (mm)) or less, and more preferably 1.9t+ It is most preferably 20 minutes (t: plate thickness (mm)) or longer.
- the hot-rolled steel sheet according to an aspect of the present invention may be provided with a tempered martensite matrix structure that has been softened.
- the hot-rolled steel sheet obtained through the above-described series of manufacturing processes is a steel material having a thickness of 6 to 40 mm, and can provide excellent ballistic resistance by securing high hardness and high toughness.
- each hot-rolled steel sheet is cut to an arbitrary size to produce a mirror surface, corroded using a nital etchant, and then used an optical microscope and a scanning electron microscope (SEM) to form a 1/ The 2t point was observed. At this time, the microstructure fraction was measured using electron back-scattered diffraction (EBSD) analysis.
- EBSD electron back-scattered diffraction
- each hot-rolled steel sheet was measured using a Brinell hardness tester (load 3000kgf, 10mm tungsten indentation hole) and a Charpy impact tester, respectively.
- a Brinell hardness tester load 3000kgf, 10mm tungsten indentation hole
- a Charpy impact tester a Charpy impact tester
- the specimens satisfying the alloy composition and process conditions of the present invention satisfy the surface hardness of 360 to 440HB and the shock absorption energy of -40°C or more of 27J, while the alloy composition or process of the present invention It can be seen that the specimens that do not satisfy any one or more of the conditions do not simultaneously satisfy the surface hardness of 360 ⁇ 440HB or the -40°C shock absorption energy of 27J or more.
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Abstract
Description
강종steel grade | 합금조성(중량%)Alloy composition (wt%) | 관계식 1Relation 1 | ||||||||||||||
CC | SiSi | MnMn | P*P* | S*S* | NiNi | CrCr | MoMo | NbNb | VV | AlAl | Ca*Ca* | TiTi | B*B* | N*N* | ||
AA | 0.360.36 | 1.371.37 | 1.451.45 | 7676 | 1919 | 1.131.13 | 0.680.68 | 0.280.28 | 0.030.03 | -- | 0.040.04 | 1616 | 0.0120.012 | 2121 | 4545 | 4.934.93 |
BB | 0.160.16 | 0.290.29 | 1.081.08 | 7272 | 2020 | 0.420.42 | 0.460.46 | 0.130.13 | 0.010.01 | 0.020.02 | 0.030.03 | 1818 | 0.0170.017 | 2323 | 4848 | 0.460.46 |
CC | 0.240.24 | 1.391.39 | 1.121.12 | 7373 | 1818 | 0.960.96 | 0.550.55 | 0.390.39 | 0.020.02 | -- | 0.030.03 | 2222 | -- | 2121 | 4444 | 3.343.34 |
DD | 0.200.20 | 1.651.65 | 1.21.2 | 7676 | 1919 | 1.141.14 | 0.810.81 | 0.440.44 | 0.030.03 | 0.040.04 | 0.030.03 | 2121 | -- | 1919 | 4646 | 3.303.30 |
EE | 0.230.23 | 1.261.26 | 0.960.96 | 7777 | 1717 | 1.061.06 | 0.730.73 | 0.420.42 | 0.030.03 | -- | 0.030.03 | 1919 | 0.0150.015 | 1818 | 4646 | 2.902.90 |
FF | 0.180.18 | 1.121.12 | 0.630.63 | 8080 | 1818 | 0.710.71 | 0.620.62 | 0.270.27 | 0.020.02 | -- | 0.030.03 | 2020 | 0.0140.014 | 2020 | 4343 | 2.022.02 |
P*, S*, Ca*, B*, N*은 ppm 단위로 기재한 것을 의미함P*, S*, Ca*, B*, N* means what is written in ppm |
시편 No.Psalter No. |
강종steel grade |
두께 (mm)thickness (mm) |
슬라브 가열 (℃)Slavic heating (℃) |
압연rolled |
1차 열처리(퀜칭)Primary Heat treatment (quenching) |
2차 열처리(템퍼링)Secondary Heat treatment (tempering) |
|||||
조압연 (℃)rough rolling (℃) |
마무리 열간 압연 (℃)Wrap-up hot rolled (℃) |
가열 온도 (℃)heating temperature (℃) |
재로 시간 (분)with ashes hour (minute) |
냉각 종료 온도 (℃)Cooling end temperature (℃) |
냉각 속도 (℃/s)Cooling speed (℃/s) |
가열 온도 (℃)heating temperature (℃) |
유지 시간 (분)maintain hour (minute) |
||||
1One | AA | 1010 | 11471147 | 10551055 | 861861 | 909909 | 3636 | 3030 | 65.265.2 | 208208 | 3939 |
22 | AA | 2525 | 11491149 | 10291029 | 928928 | 913913 | 5454 | 3737 | 45.945.9 | 227227 | 6060 |
33 | AA | 5050 | 11551155 | 10441044 | 910910 | 904904 | 8585 | 2323 | 12.512.5 | 212212 | 9595 |
44 | BB | 1515 | 11621162 | 10251025 | 899899 | 907907 | 4343 | 2424 | 44.144.1 | 301301 | 3939 |
55 | BB | 3030 | 11481148 | 10351035 | 923923 | 905905 | 6060 | 3232 | 31.931.9 | 254254 | 7575 |
66 | BB | 6060 | 11531153 | 980980 | 915915 | 904904 | 8989 | 4343 | 7.67.6 | 203203 | 114114 |
77 | CC | 88 | 11851185 | 10591059 | 886886 | 913913 | 3232 | 1919 | 62.262.2 | 215215 | 3636 |
88 | CC | 2525 | 11291129 | 10331033 | 925925 | 916916 | 5454 | 2525 | 43.343.3 | 391391 | 6060 |
99 | CC | 5050 | 11311131 | 965965 | 911911 | 907907 | 8686 | 2121 | 9.49.4 | 224224 | 116116 |
1010 | DD | 1212 | 11451145 | 10461046 | 924924 | 905905 | 4040 | 1818 | 50.550.5 | 209209 | 4545 |
1111 | DD | 2525 | 11381138 | 10301030 | 922922 | 914914 | 5555 | 1919 | 40.740.7 | - - | - - |
1212 | DD | 4040 | 11491149 | 991991 | 916916 | 900900 | 7272 | 2020 | 2525 | 216216 | 9393 |
1313 | DD | 6060 | 11421142 | 984984 | 900900 | 912912 | 9393 | 285285 | 7.77.7 | 200200 | 127127 |
1414 | EE | 2020 | 11631163 | 10301030 | 934934 | 917917 | 4747 | 3030 | 43.843.8 | 209209 | 5959 |
1515 | EE | 4040 | 11541154 | 10041004 | 927927 | 903903 | 7575 | 2525 | 20.620.6 | 231231 | 9797 |
1616 | EE | 4040 | 11521152 | 10181018 | 923923 | 912912 | 7474 | 2929 | 21.921.9 | 208208 | 1515 |
1717 | EE | 6060 | 11201120 | 977977 | 909909 | 906906 | 100100 | 1616 | 7.17.1 | 220220 | 140140 |
1818 | FF | 4040 | 11451145 | 982982 | 914914 | 908908 | 8585 | 4141 | 9.09.0 | 256256 | 118118 |
시편 No.Psalter No. |
강종steel grade |
미세조직 (면적%)microstructure (area%) |
표면경도 (HB)surface hardness (HB) |
충격인성 (J,@-40℃)impact toughness (J,@-40℃) |
||
TMTM | BB | R-γ R-γ | ||||
1One | AA | 9898 | -- | 22 | 526526 | 2424 |
22 | AA | 9797 | -- | 33 | 493493 | 2828 |
33 | AA | 9898 | -- | 22 | 511511 | 2626 |
44 | BB | 9999 | -- | 1One | 329329 | 2929 |
55 | BB | 9797 | -- | 33 | 337337 | 3434 |
66 | BB | 9898 | -- | 22 | 355355 | 3131 |
77 | CC | 9696 | -- | 44 | 424424 | 4545 |
88 | CC | 100100 | -- | 00 | 308308 | 6363 |
99 | CC | 9797 | -- | 33 | 417417 | 3737 |
1010 | DD | 9696 | -- | 44 | 379379 | 5858 |
1111 | DD | 100100 | -- | 00 | 470470 | 2020 |
1212 | DD | 9797 | -- | 33 | 409409 | 3333 |
1313 | EE | 5353 | B: 47B: 47 | 00 | 302302 | 7777 |
1414 | EE | 9797 | -- | 33 | 435435 | 3232 |
1515 | EE | 9797 | -- | 33 | 414414 | 3434 |
1616 | EE | 100100 | -- | 00 | 461461 | 2424 |
1717 | EE | 9696 | -- | 44 | 416416 | 4040 |
1818 | FF | 9898 | -- | 22 | 347347 | 3030 |
TM은 템퍼드 마르텐사이트, B는 베이나이트, R-γ는 잔류 오스테나이트를 의미함TM stands for tempered martensite, B stands for bainite, and R-γ stands for retained austenite. |
Claims (9)
- 중량%로, 탄소(C): 0.18~0.25%, 실리콘(Si): 1.0~2.0%, 망간(Mn): 0.5~1.6%, 니켈(Ni): 0.5~1.2%, 크롬(Cr): 0.4~1.5%, 인(P): 0.05% 이하, 황(S): 0.02% 이하, 질소(N): 0.006% 이하, 알루미늄(Al): 0.07% 이하(0%는 제외), 몰리브덴(Mo): 0.1~0.5%, 니오븀(Nb): 0.01~0.05%, 보론(B): 0.0002~0.005%, 칼슘(Ca): 0.0005~0.004%, 나머지 Fe 및 불가피한 불순물을 포함하고,By weight%, carbon (C): 0.18 to 0.25%, silicon (Si): 1.0 to 2.0%, manganese (Mn): 0.5 to 1.6%, nickel (Ni): 0.5 to 1.2%, chromium (Cr): 0.4 ~1.5%, Phosphorus (P): 0.05% or less, Sulfur (S): 0.02% or less, Nitrogen (N): 0.006% or less, Aluminum (Al): 0.07% or less (excluding 0%), Molybdenum (Mo) : 0.1 to 0.5%, niobium (Nb): 0.01 to 0.05%, boron (B): 0.0002 to 0.005%, calcium (Ca): 0.0005 to 0.004%, remaining Fe and unavoidable impurities,하기의 [관계식 1]을 만족하며, It satisfies the following [Relational Expression 1],템퍼드 마르텐사이트 기지조직에 잔류 오스테나이트가 포함된 복합조직을 미세조직으로 포함하는, 저온 충격인성이 우수한 고경도 방탄강.High-hardness bulletproof steel with excellent low-temperature impact toughness, including a complex structure containing retained austenite in a tempered martensite matrix structure as a microstructure.[관계식 1][Relational Expression 1]10*[C]*[Si] ≥ 2.510*[C]*[Si] ≥ 2.5상기 관계식 1에서 [C] 및 [Si]은 상기 강판에 포함된 탄소(C) 및 실리콘(Si)의 함량(중량%)을 의미하며, 해당 성분이 의도적으로 첨가되지 않은 경우 0을 대입한다.In Relation 1, [C] and [Si] mean the contents (wt%) of carbon (C) and silicon (Si) contained in the steel sheet, and 0 is substituted if the corresponding components are not intentionally added.
- 제1항에 있어서,According to claim 1,상기 방탄강은 중량%로, 티타늄(Ti): 0.005~0.025% 및 바나듐(V): 0.2% 이하 중 1종 이상을 더 포함하는, 저온 충격인성이 우수한 고경도 방탄강.The bulletproof steel is, by weight%, titanium (Ti): 0.005 to 0.025% and vanadium (V): high hardness bulletproof steel excellent in low-temperature impact toughness, further comprising at least one of 0.2% or less.
- 제1항에 있어서,According to claim 1,상기 템퍼드 마르텐사이트의 분율은 90면적% 이상이고, 상기 잔류 오스테나이트의 분율은 0.5면적% 내지 5면적%인, 저온 충격인성이 우수한 고경도 방탄강.The high hardness ballistic steel excellent in low-temperature impact toughness, wherein the fraction of the tempered martensite is 90 area% or more, and the fraction of the retained austenite is 0.5 area% to 5 area%.
- 제1항에 있어서,According to claim 1,상기 방탄강은 표면 경도가 360~440HB 이고, -40℃에서의 충격 흡수 에너지가 27J 이상인, 저온 충격인성이 우수한 고경도 방탄강.The bullet-proof steel has a surface hardness of 360-440HB, and the shock absorption energy at -40°C is 27J or more, high-hardness bulletproof steel excellent in low-temperature impact toughness.
- 제1항에 있어서,According to claim 1,상기 방탄강은 6~40mm의 두께를 가지는 저온 충격인성이 우수한 고경도 방탄강.The bullet-proof steel is a high-hardness bullet-proof steel excellent in low-temperature impact toughness having a thickness of 6-40 mm.
- 중량%로, 탄소(C): 0.18~0.25%, 실리콘(Si): 1.0~2.0%, 망간(Mn): 0.5~1.6%, 니켈(Ni): 0.5~1.2%, 크롬(Cr): 0.4~1.5%, 인(P): 0.05% 이하, 황(S): 0.02% 이하, 질소(N): 0.006% 이하, 알루미늄(Al): 0.07% 이하(0%는 제외), 몰리브덴(Mo): 0.1~0.5%, 니오븀(Nb): 0.01~0.05%, 보론(B): 0.0002~0.005%, 칼슘(Ca): 0.0005~0.004%, 나머지 Fe 및 불가피한 불순물을 포함하고, 하기의 [관계식 1]을 만족하는 강 슬라브를 준비하는 단계;By weight%, carbon (C): 0.18 to 0.25%, silicon (Si): 1.0 to 2.0%, manganese (Mn): 0.5 to 1.6%, nickel (Ni): 0.5 to 1.2%, chromium (Cr): 0.4 ~1.5%, Phosphorus (P): 0.05% or less, Sulfur (S): 0.02% or less, Nitrogen (N): 0.006% or less, Aluminum (Al): 0.07% or less (excluding 0%), Molybdenum (Mo) : 0.1 to 0.5%, niobium (Nb): 0.01 to 0.05%, boron (B): 0.0002 to 0.005%, calcium (Ca): 0.0005 to 0.004%, including the remaining Fe and unavoidable impurities, the following [Relational Expression 1] ] to prepare a steel slab that satisfies;상기 강 슬라브를 1050~1250℃의 온도범위에서 가열하는 단계;heating the steel slab in a temperature range of 1050 to 1250 °C;상기 가열된 강 슬라브를 950~1150℃의 온도범위에서 조압연하는 단계;rough rolling the heated steel slab in a temperature range of 950 to 1150 °C;상기 조압연 후 850~950℃의 온도범위에서 마무리 열간압연하여 열연강판을 제조하는 단계;manufacturing a hot-rolled steel sheet by finishing hot rolling in a temperature range of 850 to 950° C. after the rough rolling;상기 열연강판을 880~930℃의 온도범위로 가열 한 후 10℃/s 이상의 냉각속도로 150℃ 이하의 냉각종료온도까지 냉각하는 1차 열처리 단계; 및a first heat treatment step of heating the hot-rolled steel sheet to a temperature range of 880 to 930° C. and then cooling it to a cooling end temperature of 150° C. or less at a cooling rate of 10° C./s or more; and상기 1차 열처리된 열연강판을 350℃ 이하의 온도범위로 가열하여 유지하는 2차 열처리 단계를 포함하는, 저온 충격인성이 우수한 고경도 방탄강의 제조방법.A method for producing high-hardness bullet-proof steel having excellent low-temperature impact toughness, comprising a secondary heat treatment step of heating and maintaining the first heat-treated hot-rolled steel sheet to a temperature range of 350° C. or less.[관계식 1][Relational Expression 1]10*[C]*[Si] ≥ 2.510*[C]*[Si] ≥ 2.5상기 관계식 1에서 [C] 및 [Si]은 상기 강 슬라브에 포함된 탄소(C) 및 실리콘(Si)의 함량(중량%)을 의미하며, 해당 성분이 의도적으로 첨가되지 않은 경우 0을 대입한다.In Relation 1, [C] and [Si] mean the content (wt%) of carbon (C) and silicon (Si) contained in the steel slab, and 0 is substituted if the component is not intentionally added. .
- 제6항에 있어서,7. The method of claim 6,상기 강 슬라브는 중량%로, 티타늄(Ti): 0.005~0.025% 및 바나듐(V): 0.2% 이하 중 1종 이상을 더 포함하는 저온 충격인성이 우수한 고경도 방탄강의 제조방법.The steel slab is a method for producing high-hardness bullet-proof steel excellent in low-temperature impact toughness, further comprising at least one of 0.005 to 0.025% and vanadium (V): 0.2% or less in weight % of the steel slab.
- 제6항에 있어서,7. The method of claim 6,상기 1차 열처리시 재로시간은 1.3t+10분(t: 판 두께(mm)) 이상인, 저온 충격인성이 우수한 고경도 방탄강의 제조방법.The primary heat treatment time is 1.3t + 10 minutes (t: plate thickness (mm)) or more, a method of manufacturing high-hardness bulletproof steel excellent in low-temperature impact toughness.
- 제6항에 있어서,7. The method of claim 6,상기 2차 열처리시 유지시간은 1.9t+10분(t: 판 두께(mm)) 이상인, 저온 충격인성이 우수한 고경도 방탄강의 제조방법.The holding time during the secondary heat treatment is 1.9t + 10 minutes (t: plate thickness (mm)) or more, a method of manufacturing a high-hardness bulletproof steel excellent in low-temperature impact toughness.
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Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR20100116608A (en) * | 2008-01-31 | 2010-11-01 | 제이에프이 스틸 가부시키가이샤 | High-strength steel sheet and process for production therof |
KR20140074981A (en) * | 2011-10-07 | 2014-06-18 | 제이에프이 스틸 가부시키가이샤 | High-strength hot-dipped galvanized steel sheet having excellent formability and impact resistance, and method for producing same |
KR20150064223A (en) * | 2013-03-28 | 2015-06-10 | 바오샨 아이론 앤 스틸 유한공사 | Low-alloy high-hardness wear-resistant steel plate and manufacturing method therefor |
KR20180043788A (en) | 2015-08-28 | 2018-04-30 | 바오샨 아이론 앤 스틸 유한공사 | 2000 MPa class bulletproof steel sheet with tensile strength and manufacturing method thereof |
KR20190076790A (en) * | 2017-12-22 | 2019-07-02 | 주식회사 포스코 | Wear resistant steel having excellent hardness and impact toughness and method of manufacturing the same |
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CN103205627B (en) * | 2013-03-28 | 2015-08-26 | 宝山钢铁股份有限公司 | A kind of Low-alloy high-performance wear-resistant steel plate and manufacture method thereof |
KR102119959B1 (en) * | 2018-09-27 | 2020-06-05 | 주식회사 포스코 | Wear resistant steel having excellent hardness and impact toughness and method of manufacturing the same |
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KR20100116608A (en) * | 2008-01-31 | 2010-11-01 | 제이에프이 스틸 가부시키가이샤 | High-strength steel sheet and process for production therof |
KR20140074981A (en) * | 2011-10-07 | 2014-06-18 | 제이에프이 스틸 가부시키가이샤 | High-strength hot-dipped galvanized steel sheet having excellent formability and impact resistance, and method for producing same |
KR20150064223A (en) * | 2013-03-28 | 2015-06-10 | 바오샨 아이론 앤 스틸 유한공사 | Low-alloy high-hardness wear-resistant steel plate and manufacturing method therefor |
KR20180043788A (en) | 2015-08-28 | 2018-04-30 | 바오샨 아이론 앤 스틸 유한공사 | 2000 MPa class bulletproof steel sheet with tensile strength and manufacturing method thereof |
KR20190076790A (en) * | 2017-12-22 | 2019-07-02 | 주식회사 포스코 | Wear resistant steel having excellent hardness and impact toughness and method of manufacturing the same |
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EP4265785A1 (en) | 2023-10-25 |
AU2021400778A9 (en) | 2024-06-20 |
KR102498147B1 (en) | 2023-02-08 |
AU2021400778A1 (en) | 2023-07-06 |
KR20220088239A (en) | 2022-06-27 |
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