WO2011081331A9 - 쌍롤식 박판 주조공정에 의해 제조된 마르텐사이트계 스테인리스강 및 그 제조방법 - Google Patents
쌍롤식 박판 주조공정에 의해 제조된 마르텐사이트계 스테인리스강 및 그 제조방법 Download PDFInfo
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- WO2011081331A9 WO2011081331A9 PCT/KR2010/009004 KR2010009004W WO2011081331A9 WO 2011081331 A9 WO2011081331 A9 WO 2011081331A9 KR 2010009004 W KR2010009004 W KR 2010009004W WO 2011081331 A9 WO2011081331 A9 WO 2011081331A9
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/46—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/02—Hardening by precipitation
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- 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
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- 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
- C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
- C21D8/0215—Rapid solidification; Thin strip casting
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- 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
- C21D9/18—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for knives, scythes, scissors, or like hand cutting tools
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- 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
- C21D9/22—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for drills; for milling cutters; for machine cutting tools
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—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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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—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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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
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- 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
- C21D2211/008—Martensite
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- 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
- C21D2221/00—Treating localised areas of an article
- C21D2221/02—Edge parts
Definitions
- the present invention relates to a martensitic stainless steel produced by a twin roll type sheet casting process, and a method of manufacturing the same, and more particularly, to secure casting stability by suppressing central segregation, cracking, and plate breakage during casting, and to refine the casting structure. It relates to a martensitic stainless steel and a method of manufacturing the same that can produce a product having high hardness and excellent edge quality through.
- martensitic stainless steel is used in the manufacture of various tools and ceramics because of its excellent corrosion resistance, hardness and abrasion resistance.
- the present invention has been made to solve the above problems, by applying a twin-roll thin plate casting process and adding grain boundary strengthening element is suppressed central segregation, cracks and plate breakage martensite-based excellent cracking resistance to ensure casting stability
- a twin-roll thin plate casting process and adding grain boundary strengthening element is suppressed central segregation, cracks and plate breakage martensite-based excellent cracking resistance to ensure casting stability
- stainless steel hot rolled steel sheet and its manufacturing method and high hardness martensitic stainless steel cold rolled steel sheet having high hardness and excellent edge quality when forming ceramics or tools by forming microstructure uniformly distributed in steel and its manufacturing method For the purpose.
- the present invention is produced by a twin roll sheet metal casting process, by weight% C: 0.1 ⁇ 1.5%, Cr: 12 ⁇ 15%, Ni: 1% or less, Ti: 0.005 ⁇ 0.1%, balance Fe and other unavoidable addition It provides a martensite stainless steel hot rolled steel sheet having excellent crack resistance, characterized in that the impurity is made, and the primary chromium compound precipitated at the grain boundary is segmented and refined.
- the martensitic stainless steel hot-rolled steel sheet is characterized in that the Mo: 0.005 ⁇ 0.1%, V: 0.005 ⁇ 1.0% is further added alone or in combination by weight.
- the primary chromium carbide is characterized in that the thickness is 0.5 ⁇ m or less.
- martensitic stainless steel hot rolled steel sheet is characterized in that the central pores are removed.
- the equiaxed crystallinity in the cross-sectional structure of the martensitic stainless steel hot rolled steel sheet is 5 to 30%.
- the present invention is produced by a twin roll sheet metal casting process, by weight% C: 0.1 ⁇ 1.5%, Cr: 12 ⁇ 15%, Ni: 1% or less, Ti: 0.005 ⁇ 0.1%, balance Fe and other unavoidable It provides a high hardness martensitic stainless steel cold rolled steel sheet consisting of impurities are added to the spherical, and the spherical secondary chromium carbide is finely distributed.
- the martensitic stainless steel cold-rolled steel sheet is characterized in that the Mo: 0.005 ⁇ 0.1%, V: 0.005 ⁇ 1.0% is further added alone or in combination by weight.
- the secondary chromium carbide has a characteristic of having a size of 5 ⁇ m or less and having more than 30 chromium carbides having an area of 100 ⁇ m 2 .
- the martensitic stainless steel cold rolled steel sheet is characterized in that the hardness is 100 ⁇ 300Hv.
- the present invention is C: 0.1 ⁇ 1.5%, Cr: 12 ⁇ 15%, Ni: 1% or less, Ti: 0.005 ⁇ 0.1%, remainder Fe and other unavoidable impurities in weight% in twin roll sheet casting process
- Cold rolling is performed after the annealing treatment at a temperature, the cold rolling is repeated several times, the method of manufacturing a high hardness martensitic stainless steel cold rolled steel sheet characterized in that the intermediate annealing between the cold rolling To provide.
- the molten steel is also characterized in that Mo: 0.005 to 0.1% and V: 0.005 to 1.0% are further added alone or in combination.
- 1 is a configuration diagram of a twin roll thin plate casting process.
- Figure 2 is a photograph of the crack generation of martensitic stainless steel during casting.
- Figure 3 is a crack fracture surface photograph of martensitic stainless steel during casting.
- Figure 4 is a photograph of the primary chromium carbide deposited on the grain boundaries of martensitic stainless steel.
- 6 is a graph showing equiaxed crystallization and cracking according to Ti content of martensitic stainless steel.
- FIG. 7 is a photograph of the central pore in the cross-sectional structure of the martensitic stainless steel according to the rolling rate of hot rolling, (a) is a picture when not hot rolled, (b) is a picture when the hot rolling rate 25% applied.
- FIG. 9 is a photograph of the primary chromium carbide precipitated at the grain boundaries according to the Ti content of martensitic stainless steel hot rolled steel sheet.
- FIG. 10 is a distribution photograph of secondary chromium carbide of the martensitic stainless steel cold rolled steel sheet according to the present invention.
- IRM Inline rolling mill
- twin roll thin plate casting process is a pair of casting rolls that rotate (3) It is a facility for supplying molten steel (4) in between to continuously manufacture a sheet product of several mm thickness directly from the molten steel.
- the molten steel 4 having a predetermined component injected through the nozzle 2 between the casting rolls 3 cooled while rotating in the opposite direction is solidified to form a solidification shell, which is pressed down on the roll chuck to form a thin plate 7. Is generated.
- the thin plate 7 thus produced is guided by the pinch roll 10 and rolled by a rolling roll in the in-line rolling mill IRM 11 to produce a martensitic stainless steel hot rolled steel sheet.
- the martensitic stainless steel produced by the twin roll type sheet casting process has a central segregation removed as compared to the conventional casting method, and fine chromium carbide is precipitated at the grain boundary as shown in FIG. 2 and 3, the primary chromium carbide may act as a cause of cracking and plate breakage during casting, and thus, the influence of the primary chromium carbide should be suppressed as much as possible by adding grain boundary strengthening elements.
- the martensitic stainless steel of the present invention is composed of C: 0.1 to 1.5% by weight, Cr: 12 to 15%, Ni: 1% or less, Ti: 0.005 to 0.1%, balance Fe and other inevitable impurities. do. At this time, Mo: 0.005 ⁇ 0.1%, V: 0.005 ⁇ 1.0% by weight may be further added alone or in combination.
- the C is a very effective element for improving the hardness of stainless steel, when the content of C is less than 0.1% by weight, the hardness required for martensitic stainless steel cannot be secured, and when the content of C exceeds 1.5% by weight, it is relatively coarse. Since the formation of primary chromium carbide increases the crack sensitivity and reduces the corrosion resistance, the content of C is limited to 0.1 to 1.5% by weight.
- the Cr is added to improve the corrosion resistance, when the content of Cr is less than 12% by weight, the effect of improving the corrosion resistance is insignificant, and when the content of Cr is more than 15% by weight, the corrosion resistance is improved, but the strength is high and the elongation is low, the workability is reduced. And because the cost is relatively high, the Cr content is limited to 12 to 15% by weight.
- Ni is added as a gamma ( ⁇ ) phase generating element
- the ⁇ phase increases, and when the coil is air-cooled after hot rolling, martensite phase is promoted to increase strength and hardness, while elongation decreases. It is preferable to limit it to 1 weight% or less.
- the primary chromium carbide of the grain boundary is segmented or finely precipitated to suppress cracking and delamination.
- the Ti content is less than 0.005% by weight, the effect of inhibiting cracking and delamination of the steel sheet is insignificant. If the content of Ti exceeds 0.1% by weight, the clogging phenomenon of clogging of the stopper of the tundish due to the Ti-based oxide occurs, which causes problems in casting. Therefore, the content of Ti is 0.005 to 0.1% by weight. It is limited.
- the Mo and V may be contained alone or in combination, and the content of Mo and V is preferably 0.005% by weight or more for strengthening the grain boundary and improving the corrosion resistance. However, since the toughness is lowered when the content exceeds 0.1% by weight, the content of Mo and V is 0.005. It is limited to 0.1 weight%.
- the martensitic stainless steel hot rolled steel sheet having the composition prepared by rolling a thin plate cast by a twin roll type sheet casting process in an in-line rolling mill is a band-shaped primary chromium carbide precipitated at the grain boundary
- the grains are finely divided and are intermittently distributed so that the grain boundaries are strengthened, thereby suppressing cracks and plate breaks during casting, thereby improving completion rate.
- the primary chromium carbide has a thickness of 0.5 ⁇ m or less, and is mainly distributed as a band-shaped fine grains having a size of 0.05 ⁇ 0.30 ⁇ m.
- the martensitic stainless steel hot rolled steel sheet is rolled at a rolling rate of 5 to 50% during hot rolling in an in-line rolling mill to remove central pores as shown in FIG. 7 (b), thereby suppressing embrittlement due to pores and ensuring elongation. Can be.
- the present invention is characterized by the high hardness martensitic stainless steel cold rolled steel sheet produced by cold rolling after the annealing treatment of the crack-resistant martensitic stainless steel hot-rolled steel bar, Mo: 0.005 ⁇ 0.1%, V: 0.005-1.0% may further be added individually or in combination.
- the martensitic stainless steel cold rolled steel sheet has a spherical secondary chromium carbide formed in a spherical shape and is finely uniformly distributed to provide a high hardness martensitic stainless steel cold rolled steel sheet. It is possible to produce products with good edge quality during manufacturing.
- the secondary chromium carbide is 5 ⁇ m or less in size, most of the diameter is uniformly distributed in the size of 0.1 ⁇ 3.0 ⁇ m.
- the chromium carbide having a size of 5 ⁇ m or less has a high hardness of 100 to 300 Hv by forming 30 or more microstructures per 100 ⁇ m 2 , and martensitic stainless steel cold rolled steel having excellent edge quality when manufacturing tools or ceramics. Steel sheet can be produced.
- the thin plate 7 thus produced is guided by a pinch roll 10 and hot rolled by a rolling roll in the inline rolling mill IRM 11 to produce a martensitic stainless steel hot rolled steel sheet.
- a pinch roll 10 hot rolled by a rolling roll in the inline rolling mill IRM 11 to produce a martensitic stainless steel hot rolled steel sheet.
- the hot rolling is not applied, since the elongation is not secured after the annealing, it is embrittled to the extent that it is difficult to perform the pickling and cold rolling processes, which are post-processes, and thus hot rolling is essentially performed in the manufacturing method according to the present invention.
- FIG. 7 is a comparison of the central pore picture in the cross-sectional structure according to the rolling rate of hot rolling of martensitic stainless steel, pores are generated in the equiaxed crystal region when the hot rolling is not applied as shown in FIG. 7 (b) applying a rolling rate of 25% can confirm that all pores are removed in the equiaxed crystal region.
- the hot rolled steel sheet manufactured by the twin roll thin sheet casting process is subjected to an annealing (BAF) process to stabilize the solid solution of chromium carbide.
- BAF annealing
- the steel structure is a mixture of martensite phase, tempered martensite phase, and ferrite phase, but the ferrite and chromium are martensite phase in which high strength carbon is supersaturated through the above annealing process. Decomposition into carbides to soften the material to improve workability.
- the phase annealing process is gradually heated and maintained at an annealing temperature of 650 ⁇ 950 °C in a reducing gas atmosphere, and is slowly cooled in a batch form furnace again.
- the annealing temperature is less than 650 °C, the heat treatment effect is not so small that ductility is not secured, there is a possibility that cracks or plate breakage may occur in the post-process, and when the annealing temperature exceeds 950 °C, precipitation of reused chromium carbide is excessive
- the annealing temperature was limited to 650 to 950 ° C. because the size of precipitates was locally increased and the material was excessively softened to control chromium carbide.
- the steel sheet which has been heat treated in the above annealing process is transformed into martensitic stainless steel by performing cold rolling after pickling treatment.
- the cold rolling may be repeated several times, and the intermediate annealing may be performed between the cold rolling to distribute finely and uniformly disassembled spherical secondary chromium carbide to produce martensitic stainless steel cold rolled steel sheets of high hardness. have.
- the martensitic stainless steels composed of the components shown in Table 1, balance Fe, and other impurities were cast into thin plates of 100 ton, each having a casting width of 1,300 mm and a casting thickness of 2 mm, and hot rolled with an inline rolling mill to have a thickness of 1 to 2 mm. Was prepared continuously. And the results were investigated and shown in Table 2.
- the inventive steels 1 to 8 wherein the content of the steel components, including components such as Ti, which are grain boundary strengthening elements, fall within the scope of the present invention, the thickness of the primary chromium carbide is 0.5 ⁇ m or less. It was finely precipitated at the grain boundary, and the equiaxed crystallinity secured 5 ⁇ 30% so that no cracks or cracks were found, and the tundish stopper was not clogged.
- the martensitic stainless steel hot rolled steel sheet thus prepared was subjected to pickling treatment and then subjected to annealing for a long time at 650 to 950 ° C., and then repeatedly subjected to intermediate annealing between cold rolling and the cold rolling.
- chromium carbide was spherically precipitated and was distributed finely and uniformly. No chromium carbide was observed, and the martensitic stainless steel having the microstructure was very excellent in hardness of 100 to 300 Hv, thereby producing a product having excellent edge quality when manufacturing tools or ceramics.
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Abstract
Description
Claims (11)
- 쌍롤식 박판 주조공정에 의해 제조되고, 중량%로 C:0.1~1.5%, Cr:12~15%, Ni:1%이하, Ti:0.005~0.1%, 잔부 Fe 및 기타 불가피하게 첨가되는 불순물로 이루어지며,입계에 석출된 1차 크롬 탄화물이 분절 및 미세화되어 있는 것을 특징으로 하는 내크랙성이 우수한 마르텐사이트계 스테인리스 열연강판.
- 제1항에 있어서,상기 마르텐사이트계 스테인리스 열연강판은 중량%로 Mo:0.005~0.1%, V:0.005~1.0%가 단독 또는 복합으로 더 첨가되는 것을 특징으로 하는 내크랙성이 우수한 마르텐사이트계 스테인리스 열연강판.
- 제1항에 있어서,상기 1차 크롬 탄화물은 두께는 0.5㎛ 이하인 것을 특징으로 하는 내크랙성이 우수한 마르텐사이트계 스테인리스 열연강판.
- 제1항에 있어서,상기 마르텐사이트계 스테인리스 열연강판은 중심 기공이 제거된 것을 특징으로 하는 내크랙성이 우수한 마르텐사이트계 스테인리스 열연강판.
- 제1항에 있어서,상기 마르텐사이트계 스테인리스 열연강판의 단면 조직에서의 등축정율은 5~30%인 것을 특징으로 하는 내크랙성이 우수한 마르텐사이트계 스테인리스 열연강판.
- 쌍롤식 박판 주조공정에 의해 제조되고, 중량%로 C:0.1~1.5%, Cr:12~15%, Ni:1%이하, Ti:0.005~0.1%, 잔부 Fe 및 기타 불가피하게 첨가되는 불순물로 이루어지며,구상의 2차 크롬 탄화물이 미세하게 분포되어 있는 것을 특징으로 하는 고경도 마르텐사이트계 스테인리스 냉연강판.
- 제6항에 있어서,상기 마르텐사이트계 스테인리스 냉연강판은 중량%로 Mo:0.005~0.1%, V:0.005~1.0%가 단독 또는 복합으로 더 첨가되는 것을 특징으로 하는 고경도 마르텐사이트계 스테인리스 냉연강판.
- 제6항에 있어서,상기 2차 크롬 탄화물은 크기가 5㎛ 이하이고, 상기 크기를 갖는 크롬 탄화물이 100㎛2의 면적당 30개 이상 존재하는 것을 특징으로 하는 고경도 마르텐사이트계 스테인리스 냉연강판.
- 제6항에 있어서,상기 마르텐사이트계 스테인리스 냉연강판의 경도는 100~300Hv인 것을 특징으로 하는 고경도 마르텐사이트계 스테인리스 냉연강판.
- 쌍롤식 박판 주조공정에서 중량%로 C:0.1~1.5%, Cr:12~15%, Ni:1%이하, Ti:0.005~0.1%, 잔부 Fe 및 기타 불가피하게 첨가되는 불순물로 조성된 용강을 주입하여 박판을 주조하는 단계와,상기 박판을 인라인 압연기에서 압연율 5~50%로 압연하여 열연강판을 제조하는 단계와,상기 열연강판을 환원성 가스 분위기에서 650~950℃의 온도에서 상소둔 처리후 냉간압연을 실시하는 단계를 포함하되,상기 냉간압연은 수회 반복 실시하고, 상기 냉간압연 사이에 중간 소둔을 실시하는 것을 특징으로 하는 고경도 마르텐사이트계 스테인리스 냉연강판의 제조방법.
- 제10항에 있어서,상기 용강에 중량%로 Mo:0.005~0.1%, V:0.005~1.0%가 단독 또는 복합으로 더 첨가되는 것을 특징으로 하는 고경도 마르텐사이트계 스테인리스 냉연강판의 제조방법.
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AU2010339154A AU2010339154B2 (en) | 2009-12-28 | 2010-12-16 | Martensitic stainless steel produced by a twin roll strip casting process and method for manufacturing same |
US13/514,003 US20120237390A1 (en) | 2009-12-28 | 2010-12-16 | Martensitic Stainless Steel Produced by a Twin Roll Strip Casting Process and Method for Manufacturing Same |
JP2012541964A JP5531109B2 (ja) | 2009-12-28 | 2010-12-16 | 双ロール式薄板鋳造工程により製造されたマルテンサイト系ステンレス鋼及びその製造方法 |
EP10841163.8A EP2520685A4 (en) | 2009-12-28 | 2010-12-16 | MARTENSITIC STAINLESS STEEL OBTAINED USING A TWO CYLINDER TAPE BANDING PROCESS AND METHOD OF MANUFACTURING THE SAME |
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KR101403286B1 (ko) * | 2011-12-27 | 2014-06-02 | 주식회사 포스코 | 마르텐사이트계 스테인리스 강판 및 그 제조방법 |
KR101423826B1 (ko) * | 2012-07-16 | 2014-07-25 | 주식회사 포스코 | 마르텐사이트계 스테인리스강 및 그 제조방법 |
WO2014162997A1 (ja) * | 2013-04-01 | 2014-10-09 | 日立金属株式会社 | 刃物用鋼の製造方法 |
CN105102660B (zh) * | 2013-04-01 | 2017-03-08 | 日立金属株式会社 | 刀具用钢及其生产方法 |
KR101543867B1 (ko) * | 2013-11-14 | 2015-08-11 | 주식회사 포스코 | 쌍롤식 박판주조기를 사용한 마르텐사이트계 스테인리스 강판의 제조 방법 |
KR20150055788A (ko) * | 2013-11-14 | 2015-05-22 | 주식회사 포스코 | 쌍롤식 박판주조기의 주조롤 및 그 제조 방법 |
DE102014217369A1 (de) | 2014-09-01 | 2016-03-03 | Leibniz-Institut Für Festkörper- Und Werkstoffforschung Dresden E.V. | Hochfeste, mechanische energie absorbierende und korrosionsbeständige formkörper aus eisenlegierungen und verfahren zu deren herstellung |
WO2016174500A1 (fr) * | 2015-04-30 | 2016-11-03 | Aperam | Acier inoxydable martensitique, procédé de fabrication d'un demi-produit en cet acier et outil de coupe réalisé à partir de ce demi-produit |
CN106676379B (zh) * | 2016-12-29 | 2018-07-17 | 马鞍山市中桥金属材料有限公司 | 一种耐腐蚀410不锈钢的制备方法 |
CN107186184A (zh) * | 2017-04-27 | 2017-09-22 | 酒泉钢铁(集团)有限责任公司 | 一种马氏体不锈钢双辊薄带铸轧生产工艺 |
CN107794357B (zh) | 2017-10-26 | 2018-09-14 | 北京科技大学 | 超快速加热工艺生产超高强度马氏体冷轧钢板的方法 |
KR20190074074A (ko) * | 2017-12-19 | 2019-06-27 | 주식회사 포스코 | 표면 품질이 우수한 마르텐사이트계 스테인리스 강의 제조방법 |
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2009
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2010
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AU2010339154B2 (en) | 2014-01-23 |
EP2520685A4 (en) | 2015-01-21 |
EP2520685A2 (en) | 2012-11-07 |
CN102666902B (zh) | 2014-10-22 |
WO2011081331A3 (ko) | 2011-12-01 |
KR20110075387A (ko) | 2011-07-06 |
AU2010339154A1 (en) | 2012-07-19 |
KR101318274B1 (ko) | 2013-10-15 |
JP2013512347A (ja) | 2013-04-11 |
US20120237390A1 (en) | 2012-09-20 |
CN102666902A (zh) | 2012-09-12 |
JP5531109B2 (ja) | 2014-06-25 |
WO2011081331A2 (ko) | 2011-07-07 |
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