CA3226779A1 - Hot-rolled steel plate and steel tube having excellent abrasion resistance, and manufacturing method thereof - Google Patents
Hot-rolled steel plate and steel tube having excellent abrasion resistance, and manufacturing method thereof Download PDFInfo
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- CA3226779A1 CA3226779A1 CA3226779A CA3226779A CA3226779A1 CA 3226779 A1 CA3226779 A1 CA 3226779A1 CA 3226779 A CA3226779 A CA 3226779A CA 3226779 A CA3226779 A CA 3226779A CA 3226779 A1 CA3226779 A1 CA 3226779A1
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 134
- 239000010959 steel Substances 0.000 title claims abstract description 134
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 29
- 238000005299 abrasion Methods 0.000 title abstract description 20
- 239000011572 manganese Substances 0.000 claims abstract description 33
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 17
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims abstract description 15
- 239000011651 chromium Substances 0.000 claims description 31
- 229910001566 austenite Inorganic materials 0.000 claims description 29
- 229910052799 carbon Inorganic materials 0.000 claims description 18
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 16
- 229910052804 chromium Inorganic materials 0.000 claims description 16
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 15
- 238000001816 cooling Methods 0.000 claims description 15
- 239000002244 precipitate Substances 0.000 claims description 15
- 238000005098 hot rolling Methods 0.000 claims description 13
- 229910052782 aluminium Inorganic materials 0.000 claims description 12
- 239000012535 impurity Substances 0.000 claims description 12
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 10
- 229910052698 phosphorus Inorganic materials 0.000 claims description 10
- 229910052710 silicon Inorganic materials 0.000 claims description 10
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims description 9
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 9
- 239000011574 phosphorus Substances 0.000 claims description 9
- 238000003303 reheating Methods 0.000 claims description 9
- 239000010703 silicon Substances 0.000 claims description 9
- 229910052717 sulfur Inorganic materials 0.000 claims description 9
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims description 8
- 238000005482 strain hardening Methods 0.000 claims description 8
- 239000011593 sulfur Substances 0.000 claims description 8
- 238000000034 method Methods 0.000 abstract description 3
- 150000001247 metal acetylides Chemical class 0.000 description 13
- 239000000463 material Substances 0.000 description 10
- 239000000203 mixture Substances 0.000 description 8
- 229910045601 alloy Inorganic materials 0.000 description 5
- 239000000956 alloy Substances 0.000 description 5
- 230000015572 biosynthetic process Effects 0.000 description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 5
- 230000006866 deterioration Effects 0.000 description 4
- 230000000704 physical effect Effects 0.000 description 4
- 238000003466 welding Methods 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 3
- 230000003287 optical effect Effects 0.000 description 3
- 229910000617 Mangalloy Inorganic materials 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 229910052500 inorganic mineral Inorganic materials 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 239000011707 mineral Substances 0.000 description 2
- 230000002028 premature Effects 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 230000000087 stabilizing effect Effects 0.000 description 2
- 238000009628 steelmaking Methods 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- 238000007545 Vickers hardness test Methods 0.000 description 1
- 239000008186 active pharmaceutical agent Substances 0.000 description 1
- 239000010962 carbon steel Substances 0.000 description 1
- 239000002826 coolant Substances 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000000605 extraction Methods 0.000 description 1
- 150000002500 ions Chemical class 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000005065 mining Methods 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 239000004576 sand Substances 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C47/00—Winding-up, coiling or winding-off metal wire, metal band or other flexible metal material characterised by features relevant to metal processing only
- B21C47/02—Winding-up or coiling
-
- 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
- C21D8/0221—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
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
Abstract
The present invention pertains to: a hot-rolled steel plate; a steel tube; and methods for manufacturing the steel plate and steel tube. More specifically, the present invention pertains to: a high manganese hot-rolled steel plate having excellent abrasion resistance; a steel tube manufactured using the hot-rolled steel plate; and methods for manufacturing the steel plate and steel tube.
Description
Description Title of Invention: HOT-ROLLED STEEL PLATE AND STEEL TUBE
HAVING EXCELLENT ABRASION RESISTANCE, AND MANUFACTURING
METHOD THEREOF
Technical Field [0001] The present disclosure relates to a hot-rolled steel plate, a steel tube, and a manufacturing method thereof, and more specifically, to a high-manganese hot-rolled steel plate having excellent abrasion resistance, a steel tube manufactured using the hot-rolled steel plate, and a manufacturing method thereof.
Background Art
HAVING EXCELLENT ABRASION RESISTANCE, AND MANUFACTURING
METHOD THEREOF
Technical Field [0001] The present disclosure relates to a hot-rolled steel plate, a steel tube, and a manufacturing method thereof, and more specifically, to a high-manganese hot-rolled steel plate having excellent abrasion resistance, a steel tube manufactured using the hot-rolled steel plate, and a manufacturing method thereof.
Background Art
[0002] When dredging a route to secure a water depth and water area of a sailing vessel or dredging landfill to create a hinterland, a steel tube used for dredging is required to have excellent abrasion resistance against gravel, sand, or the like. In addition, in the case of a steel tube used in the mining industry to extract and transport resources such as minerals, abrasion resistance characteristics are closely related to production costs, so excellent abrasion resistance characteristics are required for efficient production costs.
[0003] In the case of carbon steel of which a main structure is ferrite or martensite, which is used as an abrasion-resistant steel tube, there is a need for substitute materials that can overcome these disadvantages as limitations in abrasion resistance have recently appeared.
[0004] Meanwhile, an austenitic steel material has excellent abrasion resistance due to work hardenability characteristics, which is used as abrasion-resistant parts in various industries. In order to increase abrasion resistance, high manganese steel contains a high content of carbon and a large amount of manganese, and efforts have been made to increase an austenite structure and resistance.
[0005] In addition, in the case of steel tubes for dredging and mineral extraction/transport, as well as small and medium-diameter steel tubes, ERW steel tubes are manufactured and used using hot-rolled materials, and in the case of large diameter steel tubes, spiral steel tubes using hot-rolled materials and submerged arc welding (SAW) steel tubes using thick plates are manufactured and used. In the case of high manganese steel, much development has been performed on steel tubes using thick plates, but the development of high manganese hot-rolled steel and steel tubes using the same is required.
Summary of Invention Technical Problem
Summary of Invention Technical Problem
[0006] An aspect of the present disclosure is to provide a hot-rolled steel plate, a steel tube, having excellent abrasion resistance, and a manufacturing method thereof.
[0007] The object of the present disclosure is not limited to the above. A person skilled in the art would have no difficulty in understanding the further subject matter of the present disclosure from the general content of this specification.
Solution to Problem
Solution to Problem
[0008] According to an aspect of the present disclosure, provided is a hot-rolled steel plate, the hot-rolled steel plate including, by weight: manganese (Mn): 10 to 20%, carbon (C): 0.6 to 2.0%, chromium (Cr): 5.0% or less, aluminum (Al):
0.5% or less, silicon (Si): 1.0% or less, phosphorus (P):
0.1% or less, sulfur (S): 0.02% or less, with a remainder of Fe, and other unavoidable impurities,
0.5% or less, silicon (Si): 1.0% or less, phosphorus (P):
0.1% or less, sulfur (S): 0.02% or less, with a remainder of Fe, and other unavoidable impurities,
[0009] wherein the hot-rolled steel plate has a microstructure with austenite as a main phase, and includes film-shaped precipitates formed along austenite grain boundaries,
[0010] wherein hardness of the hot-rolled steel plate increases by 1.1 times or more by work hardening after piping.
[0011] The precipitate may have a thickness of 0.1 to 2.0 um.
[0012] The steel plate may have a tensile strength of 800 MPa or more and elongation of 30% or more.
[0013] The steel plate may have a Vickers hardness of 220Hv or more.
[0014] The steel plate may have a thickness of 4 to 20 mm.
[0015]
[0016] According to another aspect of the present disclosure, provided is a steel tube, the steel tube including, by weight:
manganese (Mn): 10 to 20%, carbon (C): 0.6 to 2.0%, chromium (Cr): 5.0% or less, aluminum (Al): 0.5% or less, silicon (Si): 1.0% or less, phosphorus (P): 0.1% or less, sulfur (S):
0.02% or less, with a remainder of Fe, and other unavoidable impurities,
manganese (Mn): 10 to 20%, carbon (C): 0.6 to 2.0%, chromium (Cr): 5.0% or less, aluminum (Al): 0.5% or less, silicon (Si): 1.0% or less, phosphorus (P): 0.1% or less, sulfur (S):
0.02% or less, with a remainder of Fe, and other unavoidable impurities,
[0017] wherein the steel tube has a microstructure with austenite as a main phase, and includes film-shaped precipitates formed along austenite grain boundaries,
[0018] wherein hardness of the steel tube, as compared to that of the steel plate, is 1.1 times or more.
[0019] The steel tube may have a Vickers hardness of 250Hv or more.
[0020]
[0021] According to an aspect of the present disclosure, provided is a manufacturing method of a hot-rolled steel plate, the manufacturing method including operations of:
reheating a steel slab including, by weight: manganese (Mn):
to 20%, carbon (C): 0.6 to 2.0%, chromium (Cr): 5.0% or less, aluminum (Al): 0.5% or less, silicon (Si): 1.0% or less, phosphorus (P): 0.1% or less, sulfur (S): 0.02% or less, with a remainder of Fe, and other unavoidable 5 impurities,
reheating a steel slab including, by weight: manganese (Mn):
to 20%, carbon (C): 0.6 to 2.0%, chromium (Cr): 5.0% or less, aluminum (Al): 0.5% or less, silicon (Si): 1.0% or less, phosphorus (P): 0.1% or less, sulfur (S): 0.02% or less, with a remainder of Fe, and other unavoidable 5 impurities,
[0022] hot rolling the reheated steel slab to obtain a hot-rolled steel plate; and
[0023] cooling the hot-rolled steel plate to a temperature range of less than 500 C and then coiled, 10 [0024] wherein a coiling start temperature is 500 C or lower, and an average coiling temperature is less than 300 C.
[0025] The reheating may be performed at a temperature within a range of 1000 to 1250 C.
[0026] The hot rolling may be performed at a finishing temperature of 800 C or higher, [0027] During the cooling, a cooling rate may be 5 C/s or more.
[0028] The steel plate after the hot rolling may have a thickness of 4 to 20 mm.
[0029]
[0030] Another aspect of the present disclosure may provide a manufacturing method of a steel tube including the operation of piping the hot-rolled steel plate to obtain a steel tube.
Advantageous Effects of Invention [0031] As set forth above, according an aspect of the present disclosure, a hot-rolled steel plate and a steel tube having excellent abrasion resistance, and a manufacturing method thereof may be provided.
Brief description of drawings [0032] FIG. 1 is a photograph of a microstructure of Inventive Example 1 according to an aspect of the present disclosure observed with an optical microscope (200x magnification).
Best Mode for Invention [0033] Hereinafter, the present disclosure will be described in detail. Embodiments of the present disclosure may be modified in various forms, and the scope of the present disclosure should not be construed as limited to the embodiments described below. These embodiments are provided to explain the present disclosure in more detail to those skilled in the art.
[0034]
[0035] Hereinafter, the present disclosure will be described in detail.
[0036]
[0037] Hereinafter, a steel composition of the present disclosure will be described in detail.
[0038] In the present disclosure, unless other specified, %
indicating a content of each element is based on weight.
[0039]
[0040] A hot-rolled steel plate may include, by weight:
manganese (Mn): 10 to 20%, carbon (C): 0.6 to 2.0%, chromium (Cr): 5.0% or less, aluminum (Al): 0.5% or less, silicon (Si): 1.0 % or less, phosphorus (P): 0.1% or less, sulfur (S): 0.02% or less, with a remainder of Fe and other unavoidable impurities.
[0041]
[0042] Manganese (Mn): 10 to 20%
[0043] Manganese (Mn) is a very important element that plays a role in stabilizing austenite and may improve uniform elongation. Manganese (Mn) is preferably included in an amount of 10% or more in order to secure austenite as a main structure. If a content of manganese (Mn) is less than 10%, austenite stability may decrease and a martensite structure may be formed during a rolling process in a manufacturing process. As a result, an austenite structure may not be sufficiently secured, making it difficult to secure sufficiently uniform elongation. On the other hand, if the content of manganese (Mn) exceeds 20%, manufacturing costs may increase significantly, corrosion resistance may be reduced due to excessive addition of manganese (Mn), and internal oxidation may occur severely when heated in the manufacturing process, which may cause a problem such as deterioration in surface quality. A more preferable lower limit of the manganese (Mn) content may be 11.5%, and a more preferable upper limit may be 19.5%.
[0044]
[0045] Carbon (C): 0.6 to 2.0%
[0046] Carbon (C) is an austenite stabilizing element that only plays a role in improving uniform elongation, but is also a very advantageous element in improving strength and a work hardening rate. If a carbon (C) content is less than 0.6%, it may be difficult to form stable austenite at room temperature, causing a problem in that it may be difficult to secure sufficient strength and work hardening rate.
Meanwhile, if the carbon (C) content exceeds 2.0%, a large amount of carbides are precipitated and the uniform elongation is reduced, making it difficult to secure excellent elongation, and premature fracturing may occur. In order to increase abrasion resistance, it is advantageous to increase the carbon (C) content as much as possible, but even if precipitation of carbides is suppressed through heat treatment, there is a limitation in solid solutioning of carbon (C), since there are concerns about deterioration in physical properties of the steel material, an upper limit of the carbon (C) content is preferably limited to 2.0%. A more preferable lower limit of the carbon (C) content may be 0.75%, and a more preferable upper limit of the carbon (C) content may be 1.85%.
[0047]
[0048] Chromium (Cr): 5.0% or less [0049] Chromium (Cr) may serve to increase strength of a steel material by being dissolved in austenite. In addition, chromium (Cr) is an element for improving corrosion resistance of the steel material, but it may reduce toughness by forming carbides at austenite grain boundaries. Therefore, a chromium (Cr) content added in the present disclosure is preferably determined considering the relationship with C
and other elements added together, and in order to prevent formation of carbides, chromium (Cr) is preferably included in an amount of 5% or less. More preferably, chromium (Cr) is preferably included in an amount of 4% or less. If the chromium (Cr) content exceeds 5%, it may be difficult to effectively suppress formation of chromium-based carbides at austenite grain boundaries, which may reduce impact toughness. In the present disclosure, the chromium (Cr) content may be controlled as needed, and 0% may be included.
[0050]
[0051] Aluminum (Al): 0.5% or less [0052] Aluminum (Al) is a component included as a deoxidizer during a steelmaking process, and in the present disclosure, aluminum (Al) may be included in an amount of 0.5% or less.
In the present disclosure, 0% can be excluded as an aluminum (Al) content.
[0053]
[0054] Silicon (Si): 1.0% or less [0055] Silicon (Si) is a component included as a deoxidizer during a steelmaking process along with Al, and in the present disclosure, silicon (Si) may be included in an amount of 1.0% or less, and 0% may be excluded.
[0056]
[0057] Phosphorus (P): 0.1% or less [0058] Phosphorus (P) is a representative impurity that is inevitably added to steel. If phosphorus (P) is added excessively, it can cause quality deterioration, so an upper limit thereof may be limited to 0.1%.
[0059]
[0060] Sulfur (S): 0.02% or less [0061] Sulfur (S) is an impurity that is inevitably added to steel along with P, and an upper limit thereof may be limited to 0.02%.
[0062]
[0063] The steel of the present disclosure may include remaining iron (Fe) and unavoidable impurities in addition to the above-described composition. Since unavoidable impurities may be unintentionally incorporated in a common manufacturing process, the component may not be excluded.
Since these impurities are known to any person skilled in the common manufacturing process, the entire contents thereof are not particularly mentioned in the present specification.
[0064]
[0065] Hereinafter, a microstructure of steel of the present disclosure will be described in detail.
[0066] In the present disclosure, unless specifically stated otherwise, % indicating a fraction of microstructure is based on area.
[0067]
[0068] The hot-rolled steel plate according to an aspect of the present disclosure may have a microstructure with austenite as a main phase.
[0069] In the present invention, the hot-rolled steel plate may have a microstructure with austenite as the main phase in order to secure abrasion resistance by increasing hardness due to excellent work hardening of the material itself in an abrasive environment. More preferably, the microstructure may include 97 area% or more of austenite.
[0070]
[0071] A steel according to an aspect of the present disclosure may include film-shaped precipitates formed along austenite grain boundaries, and a thickness of the precipitates may be 0.1 to 2.0 pm.
[0072] In the present disclosure, it is intended to secure sufficient strength and abrasion resistance by forming film-shaped precipitates at austenite grain boundaries. The precipitate according to the present disclosure may include carbides, and may include carbides in which Cr is formed together with C. If the thickness of the precipitates is less than 0.1 pm, sufficient strength may not be secured, causing a problem in that abrasion resistance may be reduced, and if the thickness of the precipitates exceeds 2.0 pm, there is a problem in that ductility and toughness are reduced.
[0073]
[0074] A steel tube formed by piping a hot-rolled steel plate according to an aspect of the present disclosure may have a microstructure with austenite as a main phase, may include film-shaped precipitates at grain boundaries, and a thickness of the precipitates may be 0.1 to 2.0 pm.
[0075]
[0076] Hereinafter, a method of manufacturing steel of the present disclosure will be described in detail.
[0077] The steel according to an aspect of the present disclosure can be manufactured by reheating, hot rolling, cooling, and coiling a steel slab satisfying the above-described alloy composition.
[0078]
[0079] Reheating [0080] A steel slab satisfying the alloy composition of the present disclosure may be reheated to a temperature within a range of 1000 to 125000.
[0081] The slab maybe reheated before performing hot rolling.
In the slab operation, the slab may be reheated to solidify and homonize a casting structure, segregation, and secondary phases of the slab. If the reheating temperature is less than 1000 C, it may be difficult to sufficiently secure the reheating effect, and a heating furnace temperature may become too low, causing a problem of increased deformation resistance during hot rolling. On the other hand, if the temperature exceeds 1250 C, partial melting and deterioration of surface quality may occur in a segregation zone within the casting structure.
[0082]
[0083] Hot rolling [0084] The reheated slab can be hot rolled at a finishing temperature of 800 C or higher to obtain a hot-rolled steel plate with a thickness of 4 to 20 mm.
[0085] In the present disclosure, hot rolling may be performed to produce a hot rolled steel plate with a thickness of 4 to 20 mm. A finishing temperature is preferably limited to be 800 C or higher for productivity, and more preferably, hot rolling can be performed at a finishing temperature at a non-recrystallization temperature (Tnr) or lower.
[0086]
[0087] Cooling and coiling [0088] The hot-rolled steel plate may be cooled to a temperature range of 500 C or lower at a cooling rate of 5 C/s or higher and then coiled. A coiling start temperature may be 500 C or lower, and an average coiling temperature may be 300 C or lower.
[0089] In the present disclosure, cooling may be performed to a temperature within a range of less than 500 C to prevent formation of coarse carbides. If a cooling end temperature exceeds 500 C, coarse carbides may be formed during cooling to room temperature after coiling to reduce uniform elongation, and it may be difficult to secure excellent elongation, and there may be a risk of premature fracturing.
A lower limit of the coiling temperature is not particularly limited, and there is no problem even if the coiling is performed at room temperature.
[0090] If a cooling rate is less than 5 C/s, coarse carbides may be formed, which may cause a problem of a decrease in strength and elongation. An upper limit of the average cooling rate is not particularly limited, but may be appropriately selected depending on equipment specifications.
[0091] In addition, in the present invention, by controlling the coiling start temperature and the average coiling temperature, the formation of coarse carbides can be prevented and the excellent strength and elongation, which is unique to an austenite-based steel material can be secured, and a work hardening rate may be improved to ensure excellent abrasion resistance.
[0092] In the present disclosure, the coiling start temperature represents the temperature of the steel plate when coiling begins using a coiling equipment, and the average coiling temperature refers to the average value of the coiling temperature of an entire length of a coil. If the coiling start temperature exceeds 500 C or the average coiling temperature exceeds 300 C, there may be a problem of reduced ductility and toughness due to excessive formation of carbides.
[0093]
[0094] A steel tube according to an aspect of the present disclosure may be manufactured by manufacturing the hot-rolled steel plate satisfying the alloy composition and manufacturing method described above.
[0095]
[0096] Piping [0097] A steel tube can be obtained by piping a steel plate according to an aspect of the present disclosure.
[0098] In the present disclosure, the method of manufacturing a welded steel tube is not particularly limited, and a typical ERW steel tube manufacturing method can be used. However, due to a high Mn content, intrusion defects may occur during ERW welding due to oxides generated during a process of melting and solidifying a steel material. To prevent this, molten metal and oxides in a narrow gap may be completely discharged before entering a welding point, and additional devices may be installed to prevent exposure from the atmosphere and a coolant.
[0099]
[00100] The steel plate of the present disclosure manufactured in this manner may have a thickness of 4 to 20 mm, a tensile strength of 800 MPa or more, an elongation of 30% or more, and a hardness after piping into a steel tube of 1.1 times or more that of a hot-rolled steel plate, and may have characteristics of excellent work hardening rate and abrasion resistance.
[00101] In addition, the steel plate of the present disclosure may have a hardness of 220Hv or more, and the steel tube may have a hardness of 250Hv or more.
[00102]
[00103] Hereinafter, the present disclosure will be specifically described through the following Examples.
However, it should be noted that the following examples are only for describing the present disclosure by illustration, and not intended to limit the scope of rights of the present disclosure.
Mode for Invention [00104] (Example) [00105] A steel slab having the alloy composition shown in Table 1 below was manufactured to form a hot-rolled steel plate according to the conditions shown in Table 2 below, and a steel plate was manufactured with the thickness shown in Table 3. In this case, the same reheating temperature of 1150 C was applied.
[00106]
[00107] [Table 1]
Steel Alloy composition (wt%) type Mn C Cr Al Si P
A 13.2 1.09 0 0.002 0.370 0.0127 B 14.2 1.13 3.9 0.002 0.365 0.0125 C 10.4 1.82 2.4 0.003 0.358 0.0128 D 15.3 1.93 1.5 0.002 0.376 0.0124 E 11.7 1.31 3.1 0.003 0.367 0.0123 F 18.1 0.79 0 0.003 0.006 0.0126 G 12.1 0.3 2.9 0.002 0.008 0.0128 H 1.1 0.12 0 0.003 0.007 0.0127 I 11.1 1.14 1.4 0.003 0.328 0.0124 [00108]
[00109] [Table 2]
Sampl Steel Hot rolling Cooling Coiling e No. type Finishing Temperat Rate Start Average temperature( C) ure ( C/s) temperature temperature ( C) ( C) ( C) 1 A 950 454 7.3 430 180 2 B 950 478 6.5 370 180 3 C 910 493 8.4 460 160 4 D 970 467 7.8 380 160 E 890 484 5.6 370 170 9 I 890 490 17.1 560 420 [00110]
[00111] In Table 3 below, a microstructure and mechanical properties were measured for the manufactured steel plate and illustrated, and ERW welding steel tube was manufactured 5 from the steel plate, and then physical properties of the steel tube were also shown. The microstructure was shown by observing a 1/4 portion of a thickness of the steel plate with an optical microscope at 200x magnification, and the tensile strength and elongation were obtained by taking a sample of API 5L standard from the 1/4 portion of the thickness of the steel plate and performing a tensile test and the results thereof were shown. In this case, if the microstructure had 97% or more of austenite, it was indicated as 0. In addition, when precipitates with a thickness of 0.1 to 2.0 pm were formed at austenite grain boundaries, 0 was indicated. Regarding the mechanical properties, a hardness of the steel plate was measured using a Vickers hardness test, and after piping, the hardness was measured and the ratio thereof was calculated and shown.
[00112]
[00113] [Table 3]
Sam St Thic Microstructure of Physical property of Physical Hardne Divis pie ee knes steel plate steel plate property ss ion No. 1 s of steel ratio ty (mm) tube pe Austenite Precipit Tensile Elonga Hardne Hardness ate strengt tion ss (Hv) (%) (Hv) (MPa) 1 A 8 0 0 1097 52 229.3 264.8 1.15 Inven tive Examp le 1 2 B 8 0 0 1086 52 231.5 269.4 1.16 Inven tive Examp le 2 3 C 10 0 0 1133 58 232.3 267.5 1.15 'riven tive Examp le 3 4 D 10 0 0 1159 51 233.9 271.4 1.14 Maven tive Examp le 4 5 E 12 0 0 1140 57 236.1 269.3 1.14 Maven tive Examp le 5 226.2 258.3 1.14 Inven tive Examp le 6 216.2 234.1 1.08 Compa rativ e Examp le 1 168.7 171.5 1.01 Compa rativ e Examp le 2 239.1 261.1 1.09 Compa rativ e Examp le 3 [00114]
[00115] As shown in Table 3, in the case of the Invention Example satisfying the alloy composition and manufacturing conditions of the present disclosure, the microstructure characteristics proposed in the present disclosure were satisfied and the physical properties desired in the present disclosure were secured.
[00116] FIG. 1 is a photograph of the microstructure of Inventive Example 1 according to an aspect of the present disclosure observed with an optical microscope (200x magnification).
[00117]
[00118] On the other hand, in Comparative Example 1 in which a C content was below the range proposed in the present disclosure, and compared to Invention Example, the strength was insufficient and a work hardening rate after manufacturing a steel tube was also insufficient.
[00119] In Comparative Example 2 in which contents of Mn and C were outside of the range proposed in the present disclosure, and the strength of the steel plate was inferior, and the elongation was also not secured due to the inferior austenite stability due to a lack of the Mn content.
[00120] In Comparative Example 3 in which a coiling start temperature and average temperature exceeded the range of the present disclosure, and coarse carbides were excessively formed, resulting in poor ductility.
[00121]
[00122] While example embodiments have been illustrated and described above, it will be apparent to those skilled in the art that modifications and variations could be made without departing from the scope of the present disclosure as defined by the appended claims.
[0025] The reheating may be performed at a temperature within a range of 1000 to 1250 C.
[0026] The hot rolling may be performed at a finishing temperature of 800 C or higher, [0027] During the cooling, a cooling rate may be 5 C/s or more.
[0028] The steel plate after the hot rolling may have a thickness of 4 to 20 mm.
[0029]
[0030] Another aspect of the present disclosure may provide a manufacturing method of a steel tube including the operation of piping the hot-rolled steel plate to obtain a steel tube.
Advantageous Effects of Invention [0031] As set forth above, according an aspect of the present disclosure, a hot-rolled steel plate and a steel tube having excellent abrasion resistance, and a manufacturing method thereof may be provided.
Brief description of drawings [0032] FIG. 1 is a photograph of a microstructure of Inventive Example 1 according to an aspect of the present disclosure observed with an optical microscope (200x magnification).
Best Mode for Invention [0033] Hereinafter, the present disclosure will be described in detail. Embodiments of the present disclosure may be modified in various forms, and the scope of the present disclosure should not be construed as limited to the embodiments described below. These embodiments are provided to explain the present disclosure in more detail to those skilled in the art.
[0034]
[0035] Hereinafter, the present disclosure will be described in detail.
[0036]
[0037] Hereinafter, a steel composition of the present disclosure will be described in detail.
[0038] In the present disclosure, unless other specified, %
indicating a content of each element is based on weight.
[0039]
[0040] A hot-rolled steel plate may include, by weight:
manganese (Mn): 10 to 20%, carbon (C): 0.6 to 2.0%, chromium (Cr): 5.0% or less, aluminum (Al): 0.5% or less, silicon (Si): 1.0 % or less, phosphorus (P): 0.1% or less, sulfur (S): 0.02% or less, with a remainder of Fe and other unavoidable impurities.
[0041]
[0042] Manganese (Mn): 10 to 20%
[0043] Manganese (Mn) is a very important element that plays a role in stabilizing austenite and may improve uniform elongation. Manganese (Mn) is preferably included in an amount of 10% or more in order to secure austenite as a main structure. If a content of manganese (Mn) is less than 10%, austenite stability may decrease and a martensite structure may be formed during a rolling process in a manufacturing process. As a result, an austenite structure may not be sufficiently secured, making it difficult to secure sufficiently uniform elongation. On the other hand, if the content of manganese (Mn) exceeds 20%, manufacturing costs may increase significantly, corrosion resistance may be reduced due to excessive addition of manganese (Mn), and internal oxidation may occur severely when heated in the manufacturing process, which may cause a problem such as deterioration in surface quality. A more preferable lower limit of the manganese (Mn) content may be 11.5%, and a more preferable upper limit may be 19.5%.
[0044]
[0045] Carbon (C): 0.6 to 2.0%
[0046] Carbon (C) is an austenite stabilizing element that only plays a role in improving uniform elongation, but is also a very advantageous element in improving strength and a work hardening rate. If a carbon (C) content is less than 0.6%, it may be difficult to form stable austenite at room temperature, causing a problem in that it may be difficult to secure sufficient strength and work hardening rate.
Meanwhile, if the carbon (C) content exceeds 2.0%, a large amount of carbides are precipitated and the uniform elongation is reduced, making it difficult to secure excellent elongation, and premature fracturing may occur. In order to increase abrasion resistance, it is advantageous to increase the carbon (C) content as much as possible, but even if precipitation of carbides is suppressed through heat treatment, there is a limitation in solid solutioning of carbon (C), since there are concerns about deterioration in physical properties of the steel material, an upper limit of the carbon (C) content is preferably limited to 2.0%. A more preferable lower limit of the carbon (C) content may be 0.75%, and a more preferable upper limit of the carbon (C) content may be 1.85%.
[0047]
[0048] Chromium (Cr): 5.0% or less [0049] Chromium (Cr) may serve to increase strength of a steel material by being dissolved in austenite. In addition, chromium (Cr) is an element for improving corrosion resistance of the steel material, but it may reduce toughness by forming carbides at austenite grain boundaries. Therefore, a chromium (Cr) content added in the present disclosure is preferably determined considering the relationship with C
and other elements added together, and in order to prevent formation of carbides, chromium (Cr) is preferably included in an amount of 5% or less. More preferably, chromium (Cr) is preferably included in an amount of 4% or less. If the chromium (Cr) content exceeds 5%, it may be difficult to effectively suppress formation of chromium-based carbides at austenite grain boundaries, which may reduce impact toughness. In the present disclosure, the chromium (Cr) content may be controlled as needed, and 0% may be included.
[0050]
[0051] Aluminum (Al): 0.5% or less [0052] Aluminum (Al) is a component included as a deoxidizer during a steelmaking process, and in the present disclosure, aluminum (Al) may be included in an amount of 0.5% or less.
In the present disclosure, 0% can be excluded as an aluminum (Al) content.
[0053]
[0054] Silicon (Si): 1.0% or less [0055] Silicon (Si) is a component included as a deoxidizer during a steelmaking process along with Al, and in the present disclosure, silicon (Si) may be included in an amount of 1.0% or less, and 0% may be excluded.
[0056]
[0057] Phosphorus (P): 0.1% or less [0058] Phosphorus (P) is a representative impurity that is inevitably added to steel. If phosphorus (P) is added excessively, it can cause quality deterioration, so an upper limit thereof may be limited to 0.1%.
[0059]
[0060] Sulfur (S): 0.02% or less [0061] Sulfur (S) is an impurity that is inevitably added to steel along with P, and an upper limit thereof may be limited to 0.02%.
[0062]
[0063] The steel of the present disclosure may include remaining iron (Fe) and unavoidable impurities in addition to the above-described composition. Since unavoidable impurities may be unintentionally incorporated in a common manufacturing process, the component may not be excluded.
Since these impurities are known to any person skilled in the common manufacturing process, the entire contents thereof are not particularly mentioned in the present specification.
[0064]
[0065] Hereinafter, a microstructure of steel of the present disclosure will be described in detail.
[0066] In the present disclosure, unless specifically stated otherwise, % indicating a fraction of microstructure is based on area.
[0067]
[0068] The hot-rolled steel plate according to an aspect of the present disclosure may have a microstructure with austenite as a main phase.
[0069] In the present invention, the hot-rolled steel plate may have a microstructure with austenite as the main phase in order to secure abrasion resistance by increasing hardness due to excellent work hardening of the material itself in an abrasive environment. More preferably, the microstructure may include 97 area% or more of austenite.
[0070]
[0071] A steel according to an aspect of the present disclosure may include film-shaped precipitates formed along austenite grain boundaries, and a thickness of the precipitates may be 0.1 to 2.0 pm.
[0072] In the present disclosure, it is intended to secure sufficient strength and abrasion resistance by forming film-shaped precipitates at austenite grain boundaries. The precipitate according to the present disclosure may include carbides, and may include carbides in which Cr is formed together with C. If the thickness of the precipitates is less than 0.1 pm, sufficient strength may not be secured, causing a problem in that abrasion resistance may be reduced, and if the thickness of the precipitates exceeds 2.0 pm, there is a problem in that ductility and toughness are reduced.
[0073]
[0074] A steel tube formed by piping a hot-rolled steel plate according to an aspect of the present disclosure may have a microstructure with austenite as a main phase, may include film-shaped precipitates at grain boundaries, and a thickness of the precipitates may be 0.1 to 2.0 pm.
[0075]
[0076] Hereinafter, a method of manufacturing steel of the present disclosure will be described in detail.
[0077] The steel according to an aspect of the present disclosure can be manufactured by reheating, hot rolling, cooling, and coiling a steel slab satisfying the above-described alloy composition.
[0078]
[0079] Reheating [0080] A steel slab satisfying the alloy composition of the present disclosure may be reheated to a temperature within a range of 1000 to 125000.
[0081] The slab maybe reheated before performing hot rolling.
In the slab operation, the slab may be reheated to solidify and homonize a casting structure, segregation, and secondary phases of the slab. If the reheating temperature is less than 1000 C, it may be difficult to sufficiently secure the reheating effect, and a heating furnace temperature may become too low, causing a problem of increased deformation resistance during hot rolling. On the other hand, if the temperature exceeds 1250 C, partial melting and deterioration of surface quality may occur in a segregation zone within the casting structure.
[0082]
[0083] Hot rolling [0084] The reheated slab can be hot rolled at a finishing temperature of 800 C or higher to obtain a hot-rolled steel plate with a thickness of 4 to 20 mm.
[0085] In the present disclosure, hot rolling may be performed to produce a hot rolled steel plate with a thickness of 4 to 20 mm. A finishing temperature is preferably limited to be 800 C or higher for productivity, and more preferably, hot rolling can be performed at a finishing temperature at a non-recrystallization temperature (Tnr) or lower.
[0086]
[0087] Cooling and coiling [0088] The hot-rolled steel plate may be cooled to a temperature range of 500 C or lower at a cooling rate of 5 C/s or higher and then coiled. A coiling start temperature may be 500 C or lower, and an average coiling temperature may be 300 C or lower.
[0089] In the present disclosure, cooling may be performed to a temperature within a range of less than 500 C to prevent formation of coarse carbides. If a cooling end temperature exceeds 500 C, coarse carbides may be formed during cooling to room temperature after coiling to reduce uniform elongation, and it may be difficult to secure excellent elongation, and there may be a risk of premature fracturing.
A lower limit of the coiling temperature is not particularly limited, and there is no problem even if the coiling is performed at room temperature.
[0090] If a cooling rate is less than 5 C/s, coarse carbides may be formed, which may cause a problem of a decrease in strength and elongation. An upper limit of the average cooling rate is not particularly limited, but may be appropriately selected depending on equipment specifications.
[0091] In addition, in the present invention, by controlling the coiling start temperature and the average coiling temperature, the formation of coarse carbides can be prevented and the excellent strength and elongation, which is unique to an austenite-based steel material can be secured, and a work hardening rate may be improved to ensure excellent abrasion resistance.
[0092] In the present disclosure, the coiling start temperature represents the temperature of the steel plate when coiling begins using a coiling equipment, and the average coiling temperature refers to the average value of the coiling temperature of an entire length of a coil. If the coiling start temperature exceeds 500 C or the average coiling temperature exceeds 300 C, there may be a problem of reduced ductility and toughness due to excessive formation of carbides.
[0093]
[0094] A steel tube according to an aspect of the present disclosure may be manufactured by manufacturing the hot-rolled steel plate satisfying the alloy composition and manufacturing method described above.
[0095]
[0096] Piping [0097] A steel tube can be obtained by piping a steel plate according to an aspect of the present disclosure.
[0098] In the present disclosure, the method of manufacturing a welded steel tube is not particularly limited, and a typical ERW steel tube manufacturing method can be used. However, due to a high Mn content, intrusion defects may occur during ERW welding due to oxides generated during a process of melting and solidifying a steel material. To prevent this, molten metal and oxides in a narrow gap may be completely discharged before entering a welding point, and additional devices may be installed to prevent exposure from the atmosphere and a coolant.
[0099]
[00100] The steel plate of the present disclosure manufactured in this manner may have a thickness of 4 to 20 mm, a tensile strength of 800 MPa or more, an elongation of 30% or more, and a hardness after piping into a steel tube of 1.1 times or more that of a hot-rolled steel plate, and may have characteristics of excellent work hardening rate and abrasion resistance.
[00101] In addition, the steel plate of the present disclosure may have a hardness of 220Hv or more, and the steel tube may have a hardness of 250Hv or more.
[00102]
[00103] Hereinafter, the present disclosure will be specifically described through the following Examples.
However, it should be noted that the following examples are only for describing the present disclosure by illustration, and not intended to limit the scope of rights of the present disclosure.
Mode for Invention [00104] (Example) [00105] A steel slab having the alloy composition shown in Table 1 below was manufactured to form a hot-rolled steel plate according to the conditions shown in Table 2 below, and a steel plate was manufactured with the thickness shown in Table 3. In this case, the same reheating temperature of 1150 C was applied.
[00106]
[00107] [Table 1]
Steel Alloy composition (wt%) type Mn C Cr Al Si P
A 13.2 1.09 0 0.002 0.370 0.0127 B 14.2 1.13 3.9 0.002 0.365 0.0125 C 10.4 1.82 2.4 0.003 0.358 0.0128 D 15.3 1.93 1.5 0.002 0.376 0.0124 E 11.7 1.31 3.1 0.003 0.367 0.0123 F 18.1 0.79 0 0.003 0.006 0.0126 G 12.1 0.3 2.9 0.002 0.008 0.0128 H 1.1 0.12 0 0.003 0.007 0.0127 I 11.1 1.14 1.4 0.003 0.328 0.0124 [00108]
[00109] [Table 2]
Sampl Steel Hot rolling Cooling Coiling e No. type Finishing Temperat Rate Start Average temperature( C) ure ( C/s) temperature temperature ( C) ( C) ( C) 1 A 950 454 7.3 430 180 2 B 950 478 6.5 370 180 3 C 910 493 8.4 460 160 4 D 970 467 7.8 380 160 E 890 484 5.6 370 170 9 I 890 490 17.1 560 420 [00110]
[00111] In Table 3 below, a microstructure and mechanical properties were measured for the manufactured steel plate and illustrated, and ERW welding steel tube was manufactured 5 from the steel plate, and then physical properties of the steel tube were also shown. The microstructure was shown by observing a 1/4 portion of a thickness of the steel plate with an optical microscope at 200x magnification, and the tensile strength and elongation were obtained by taking a sample of API 5L standard from the 1/4 portion of the thickness of the steel plate and performing a tensile test and the results thereof were shown. In this case, if the microstructure had 97% or more of austenite, it was indicated as 0. In addition, when precipitates with a thickness of 0.1 to 2.0 pm were formed at austenite grain boundaries, 0 was indicated. Regarding the mechanical properties, a hardness of the steel plate was measured using a Vickers hardness test, and after piping, the hardness was measured and the ratio thereof was calculated and shown.
[00112]
[00113] [Table 3]
Sam St Thic Microstructure of Physical property of Physical Hardne Divis pie ee knes steel plate steel plate property ss ion No. 1 s of steel ratio ty (mm) tube pe Austenite Precipit Tensile Elonga Hardne Hardness ate strengt tion ss (Hv) (%) (Hv) (MPa) 1 A 8 0 0 1097 52 229.3 264.8 1.15 Inven tive Examp le 1 2 B 8 0 0 1086 52 231.5 269.4 1.16 Inven tive Examp le 2 3 C 10 0 0 1133 58 232.3 267.5 1.15 'riven tive Examp le 3 4 D 10 0 0 1159 51 233.9 271.4 1.14 Maven tive Examp le 4 5 E 12 0 0 1140 57 236.1 269.3 1.14 Maven tive Examp le 5 226.2 258.3 1.14 Inven tive Examp le 6 216.2 234.1 1.08 Compa rativ e Examp le 1 168.7 171.5 1.01 Compa rativ e Examp le 2 239.1 261.1 1.09 Compa rativ e Examp le 3 [00114]
[00115] As shown in Table 3, in the case of the Invention Example satisfying the alloy composition and manufacturing conditions of the present disclosure, the microstructure characteristics proposed in the present disclosure were satisfied and the physical properties desired in the present disclosure were secured.
[00116] FIG. 1 is a photograph of the microstructure of Inventive Example 1 according to an aspect of the present disclosure observed with an optical microscope (200x magnification).
[00117]
[00118] On the other hand, in Comparative Example 1 in which a C content was below the range proposed in the present disclosure, and compared to Invention Example, the strength was insufficient and a work hardening rate after manufacturing a steel tube was also insufficient.
[00119] In Comparative Example 2 in which contents of Mn and C were outside of the range proposed in the present disclosure, and the strength of the steel plate was inferior, and the elongation was also not secured due to the inferior austenite stability due to a lack of the Mn content.
[00120] In Comparative Example 3 in which a coiling start temperature and average temperature exceeded the range of the present disclosure, and coarse carbides were excessively formed, resulting in poor ductility.
[00121]
[00122] While example embodiments have been illustrated and described above, it will be apparent to those skilled in the art that modifications and variations could be made without departing from the scope of the present disclosure as defined by the appended claims.
Claims (11)
1. A hot-rolled steel plate, comprising, by weight:
manganese (Mn): 10 to 20%, carbon (C): 0.6 to 2.0%, chromium (Cr): 5.0% or less, aluminum (Al): 0.5% or less, silicon (Si): 1.0% or less, phosphorus (P): 0.1% or less, sulfur (S): 0.02% or less, with a remainder of Fe, and other unavoidable impurities, wherein the hot-rolled steel plate has a microstructure with austenite as a main phase, and includes film-shaped precipitates formed along austenite grain boundaries, wherein hardness of the hot-rolled steel plate increases by 1.1 times or more by work hardening after piping.
manganese (Mn): 10 to 20%, carbon (C): 0.6 to 2.0%, chromium (Cr): 5.0% or less, aluminum (Al): 0.5% or less, silicon (Si): 1.0% or less, phosphorus (P): 0.1% or less, sulfur (S): 0.02% or less, with a remainder of Fe, and other unavoidable impurities, wherein the hot-rolled steel plate has a microstructure with austenite as a main phase, and includes film-shaped precipitates formed along austenite grain boundaries, wherein hardness of the hot-rolled steel plate increases by 1.1 times or more by work hardening after piping.
2. The hot-rolled steel plate of claim 1, wherein the precipitate has a thickness of 0.1 to 2.0 pm.
3. The hot-rolled steel plate of claim 1, wherein the steel plate has a tensile strength of 800MPa or more and elongation of 30% or more.
4. The hot-rolled steel plate of claim 1, wherein the steel plate has a Vickers hardness of 220Hv or more.
5. The hot-rolled steel plate of claim 1, wherein the steel plate has a thickness of 4 to 20 mm.
6. A steel tube, comprising, by weight:
manganese (Mn): 10 to 20%, carbon (C): 0.6 to 2.0%, chromium (Cr): 5.0% or less, aluminum (Al): 0.5% or less, silicon (Si): 1.0% or less, phosphorus (P): 0.1% or less, sulfur (S): 0.02% or less, with a remainder of Fe, and other unavoidable impurities, wherein the steel tube has a microstructure with austenite as a main phase, and includes film-shaped precipitates formed along austenite grain boundaries, wherein hardness of the steel tube, as compared to that of the steel plate is 1.1 times or more.
manganese (Mn): 10 to 20%, carbon (C): 0.6 to 2.0%, chromium (Cr): 5.0% or less, aluminum (Al): 0.5% or less, silicon (Si): 1.0% or less, phosphorus (P): 0.1% or less, sulfur (S): 0.02% or less, with a remainder of Fe, and other unavoidable impurities, wherein the steel tube has a microstructure with austenite as a main phase, and includes film-shaped precipitates formed along austenite grain boundaries, wherein hardness of the steel tube, as compared to that of the steel plate is 1.1 times or more.
7. The steel tube of claim 6, wherein the steel tube has a Vickers hardness of 250Hv or more.
8. A manufacturing method of a high-rolled steel plate, comprising operations of:
reheating a steel slab including, by weight: Mn: 10 to 20%, C: 0.6 to 2.0%, Cr: 5.0% or less, Al: 0.5% or less, Si:
1.0% or less, P: 0.1% or less, S: 0.02% or less, with a remainder of Fe, and other unavoidable impurities;
hot rolling the reheated steel slab to obtain a hot-rolled steel plate; and cooling the hot-rolled steel plate to a temperature range of less than 500 C and then coiled, wherein a coiling start temperature is 500 C or lower, and an average coiling temperature is less than 300 C.
reheating a steel slab including, by weight: Mn: 10 to 20%, C: 0.6 to 2.0%, Cr: 5.0% or less, Al: 0.5% or less, Si:
1.0% or less, P: 0.1% or less, S: 0.02% or less, with a remainder of Fe, and other unavoidable impurities;
hot rolling the reheated steel slab to obtain a hot-rolled steel plate; and cooling the hot-rolled steel plate to a temperature range of less than 500 C and then coiled, wherein a coiling start temperature is 500 C or lower, and an average coiling temperature is less than 300 C.
9.
The manufacturing method of a hot-rolled steel plate of claim 8, wherein the reheating is performed at a temperature within a range of 1000 to 1250 C, the hot rolling is performed at a finishing temperature of 800 C or higher, and during the cooling, a cooling rate is 5 C/s or more.
The manufacturing method of a hot-rolled steel plate of claim 8, wherein the reheating is performed at a temperature within a range of 1000 to 1250 C, the hot rolling is performed at a finishing temperature of 800 C or higher, and during the cooling, a cooling rate is 5 C/s or more.
10. The manufacturing method of a hot-rolled steel plate of claim 8, wherein after the hot rolling, the steel plate has a thickness of 4 to 20 mm.
11. A manufacturing method of a steel tube of one of claims 8 to 10, comprising:
an operation of obtaining a steel tube by piping the hot-rolled steel plate.
an operation of obtaining a steel tube by piping the hot-rolled steel plate.
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| KR10-2021-0159256 | 2021-11-18 | ||
| KR1020210159256A KR20230072727A (en) | 2021-11-18 | 2021-11-18 | Hot rolled steel plate and steel tube having excellent abrasion resistance and manufacturing method thereof |
| PCT/KR2022/018212 WO2023090897A1 (en) | 2021-11-18 | 2022-11-17 | Hot-rolled steel plate and steel tube having excellent abrasion resistance, and manufacturing method thereof |
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| KR100851158B1 (en) * | 2006-12-27 | 2008-08-08 | 주식회사 포스코 | High Manganese High Strength Steel Sheets With Excellent Crashworthiness, And Method For Manufacturing Of It |
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| KR101714929B1 (en) * | 2015-12-22 | 2017-03-23 | 주식회사 포스코 | Austenitic steel having excellent wear resistance and method for manufacturing the same |
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