Classifications

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  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
  • C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
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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
• • 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
  • B21B1/22—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 plates, strips, bands or sheets of indefinite length
  • B21B1/24—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 plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21B—ROLLING OF METAL
  • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
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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
  • 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
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
  • C21D1/18—Hardening; Quenching with or without subsequent tempering
  • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
  • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
  • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
  • C21D1/60—Aqueous agents
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
  • C21D1/84—Controlled slow cooling
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D6/00—Heat treatment of ferrous alloys
  • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D6/00—Heat treatment of ferrous alloys
  • C21D6/005—Heat treatment of ferrous alloys containing Mn
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D6/00—Heat treatment of ferrous alloys
  • C21D6/008—Heat treatment of ferrous alloys containing Si
• • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
  • C21D8/0226—Hot rolling
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
  • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
  • C21D9/54—Furnaces for treating strips or wire
  • C21D9/68—Furnace coilers; Hot coilers
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
  • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
  • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
  • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
• • 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
• • 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
  • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D2211/00—Microstructure comprising significant phases
  • C21D2211/005—Ferrite
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D2211/00—Microstructure comprising significant phases
  • C21D2211/009—Pearlite

Definitions

• the present disclosure relates to a steel material having properties that are particularly suitable for a vacuum tube that is provided for a high-speed vacuum tube train, and a method of manufacturing the steel material.
• a high-speed vacuum tube train is a means of transportation that fundamentally moves a train within a vacuum tube. That is, it is a means of transportation utilizing a concept in which it is possible to operate a train at a super high speeds because air resistance is minimized by maintaining the inside of a tube in a vacuum state.
• Patent Document 1 A section of tubing for manufacturing a vacuum tube that may be used for a high-speed train vacuum tube is disclosed in Patent Document 1; however, the material of the tube is not specifically stated therein.
• Patent Document 1 US 2019/0170276 A1 (published on 2019.06.06 )
• a steel material having properties that are particularly suitable for a vacuum tube that is provided for a high-speed vacuum tube train, and a method of manufacturing the steel material may be provided.
• a steel material for a vacuum tube may include C: 0.1 ⁇ 0.2%, Si: 0.05 ⁇ 0.5%, Mn: 1.0 ⁇ 1.6%, Ni: 0.5 ⁇ 1.0%, Cr: 1.5 ⁇ 4.0%, and the balance of Fe and unavoidable impurities in percentage by weight, and may have a complex structure of ferrite and pearlite as a microstructure, may have complex structure of ferrite and pearlite as a microstructure, and may have an outgassing rate of 1.0*10 -10 mbar ⁇ l ⁇ s -1 ⁇ cm -2 or less.
• a total content of Ti, Nb, and V of the impurities included in the steel material may be less than 0.01% (including 0%).
• a fraction of the ferrite may be 60 ⁇ 90 percent by area and a fraction of the pearlite may be 10 ⁇ 40 percent by area.
• a fraction of martensite or bainite included in the steel material may less than 1 percent by area (including 0%).
• the steel material may have yield strength (YS) of 400 ⁇ 600MPa, a yield ratio (YR) of 0.8 or less, and elongation (El) of 19 ⁇ 30%.
• the steel material may have Charpy impact energy of 30 ⁇ 50J at -20°C.
• a thickness of the steel material may be 15 ⁇ 30mm.
• a method of controlling a steel material for a vacuum tube may include: providing a steel material by reheating a slab including C: 0.1 ⁇ 0.2%, Si: 0.05 ⁇ 0.5%, Mn: 1.0 ⁇ 1.6%, Ni: 0.5 ⁇ 1.0%, Cr: 1.5 ⁇ 4.0%, and the balance of Fe and unavoidable impurities in percentage by weight, and then by hot-rolling the slab at a finishing rolling temperature of 900 ⁇ 1000°C; primarily cooling the hot-rolled steel material up to 550-650°C at a first cooling speed of 5 ⁇ 50°C/s; coiling the steel material into a coil at a primary cooling end temperature after the primary cooling; and secondarily cooling the coil to room temperature at a secondary cooling speed of 0.005 ⁇ 0.05°C/s.
• a total content of Ti, Nb, and V of the impurities included in the slab may be less than 0.01% (including 0%).
• a thickness of the hot-rolled steel material may be 15 ⁇ 30mm.
• a cooling type of the primary cooling may be water cooling and a cooling type of the secondary cooling may be discharge of cold.
• the present disclosure relates to a steel material for a vacuum tube and a method of manufacturing the steel material.
• preferred embodiments of the present disclosure are described.
• Embodiments of the present disclosure may be modified in various ways and the scope of the present disclosure should not be construed as being limited to the embodiments to be described below.
• the embodiments are provided to describe the present disclosure in detail to those skilled in the art.
• a steel material for a vacuum tube may include, in percentage by weight, C: 0.1 ⁇ 0.2%, Si: 0.05 ⁇ 0.5%, Mn: 1.0 ⁇ 1.6%, Ni: 0.5 ⁇ 1.0%, Cr: 1.5 ⁇ 4.0%, and the balance of Fe and unavoidable impurities, may have a complex structure of ferrite and pearlite as a microstructure, and may have an outgassing rate of 1.0*10 -10 mbar ⁇ l ⁇ s -1 ⁇ cm -2 or less.
• a steel material for a vacuum tube may include, in percentage by weight, C: 0.1 ⁇ 0.2%, Si: 0.05 ⁇ 0.5%, Mn: 1.0 ⁇ 1.6%, Ni: 0.5 ⁇ 1.0%, Cr: 1.5 ⁇ 4.0%, and the balance of Fe and unavoidable impurities, in which the total content of Ni, Nb, Nd, and V of the impurities can be suppressed under 0.01% (including 0%).
• Carbon (C) which is a representative hardenability improvement element, is an element that most effectively contributes to securing strength of a steel material. Accordingly, the present disclosure may include carbon (C) of 0.1% or more in order to secure strength of a vacuum tube structure.
• a preferred content of carbon (C) may exceed 0.1%, and a more preferable content of carbon (C) may be 0.12% or more.
• the upper limit of the content of carbon (C) may be limited at 2.0%.
• a preferred content of carbon (C) may be less than 0.2%, and a more preferable content of carbon (C) may be 0.18% or less.
• Silicon (Si) is an element that contributes to deoxidization of steel. Accordingly, the present disclosure may include silicon (Si) of 0.05% or more to secure the degree of purity of steel. A preferred content of silicon (Si) may be 0.06% or more, and a more preferable content of silicon (Si) may be 0.08%. However, when silicon (Si) is excessively added, it may interfere with detachment of surface scale, so not only the surface quality of a product may be deteriorated, but extraction of carbides may be interfered with, whereby formation of a target microstructure may be interfered with. Accordingly, the present disclosure may limit the upper limit of the content of silicon (Si) at 0.5%. A preferred content of silicon (Si) may be 0.4% or less, and a more preferable content of silicon (Si) may be 0.3% or less.
• Manganese (Mn) is an element that contributes to improving hardenability of steel, so the present disclosure may include manganese (Mn) of 1.0% or more to secure strength of a steel material.
• a preferred content of manganese (Mn) may be 1.1% or more, and a more preferable content of silicon (Si) may be 1.2% or more.
• manganese (Mn) is excessive added, the roughness of steel decreases and crack resistance is deteriorated, and additionally, material deviation may be caused due to molding segregation, so the present disclosure may limit the upper limit of the content of manganese (Mn) at 1.6%.
• a preferred content of manganese (Mn) may be 1.5% or less, and a more preferable content of silicon (Si) may be 1.4% or less.
• Nickel (Ni) is not only an element that contributes to increasing the strength of a steel material, but an element that effectively contributes to increasing the shock toughness of a steel material. Accordingly, the present disclosure may include nickel (Ni) of 0.5% or more for this effect. A preferred content of nickel (Ni) may exceed 0.5%, and a more preferable content of nickel (Ni) may be 0.6% or more. However, the content of nickel (Ni) exceeds a predetermined level, the effects described above are saturated, but it is not preferable in terms of economical efficiency, so the present disclosure may limit the upper limit of the content of nickel (Ni) at 1.0%. A preferred content of nickel (Ni) may be less 1.0%, and a more preferable content of nickel (Ni) may be 0.9% or less.
• Chrome (Cr) is an element that effectively contributes to reducing an outgassing rate intended in the present disclosure.
• Chrome (Cr) has reduction potential (-0.73V) lower than that of iron (-0.44V), so it is possible to form a very thin and dense chrome oxide film on the surface of a steel material.
• a dense oxide film acts as a barrier against gas that is discharged from a material, so it is possible to effectively reduce the outgassing rate of a material.
• the present disclosure may include chrome (Cr) of 1.5% or more for this effect.
• a preferred content of chrome (Cr) may exceed 1.5%, and a more preferable content of chrome (Cr) may be 1.7% or more.
• chrome (Cr) The higher the content of chrome (Cr), the more the effect of reducing an outgassing rate is improved.
• chrome (Cr) is an expensive element, it is not preferable in terms of economic that chrome (Cr) is added at a predetermined level or more.
• chrome (Cr) is excessively added, hardenability is excessively increased, so it may cause low-temperature microstructure formation in a surface layer, which is not preferable in terms of property material deviation. Accordingly, the present disclosure may limit the upper limit of the content of chrome (Cr) at 4.0%.
• a preferred content of chrome (Cr) may be 3.6% or less, and a more preferable content of chrome (Cr) may be 3.3% or less.
• the steel material for a vacuum tube may include the balance of Fe and other unavoidable impurities other than the components described above.
• unintended impurities may be unavoidably mixed from a raw material or a surrounding environment in a common manufacturing process, such impurities cannot be completely excluded. Since anyone of those skilled in the art can know such impurities, all impurities are not specifically stated in the specification. Further, addition of effective components other than the composition described above is not excluded.
• Titanium (Ti), niobium (Nb), and vanadium (V), which are representative precipitation strengthening elements, are elements that effectively contribute to improving the strength of a steel material by forming micro carbonitrides even though only a small mount of them is added. Since the target to which the steel material of the present disclosure is applied is a vacuum tube for a high-speed vacuum tube train that is a large structure, an increase of a yield ratio is not advantageous in terms of constructability.
• the present disclosure in order to achieve a target yield ratio, actively restricts intentional addition of titanium (Ti), niobium (Nb), and vanadium (V), and even if these components are unavoidably mixed, it is possible to limit the total content less than 0.01% (including 0%).
• the steel material for a vacuum tube may have a complex structure of ferrite and pearlite as a microstructure and can actively suppress formation of a hard phase.
• the fraction of ferrite may be 60 ⁇ 90 percent by area
• the fraction of pearlite may be 10 ⁇ 40 percent by area
• the total fraction of martensite or bainite that is a hard phase may be less than 1 percent by area (including 0%).
• low-temperature microstructures such as martensite or bainite have high strength and a low yield ratio, they show excellent characteristics as a material for structures.
• the thickness of the steel material for a vacuum tube of the present disclosure is about 5 ⁇ 30mm, there is a high possibility that a hard phase is introduced only on the surface of the steel material even through control under a cooling condition. That is, a hard phase is not formed at the center portion of the steel material, but a hard phase is intensively formed only at the surface portion of the steel material, so there is a high possibility of material deviation in the thickness direction of the steel material. Accordingly, the present disclosure can actively control the total fraction of martensite or bainite to reduce such material deviation.
• the outgassing rate of the steel material for a vacuum tube may be 1.0*10 -10 mbar ⁇ ls -1 ⁇ cm -2 or less.
• Equation 1 q is an outgassing rate (mbar ⁇ l ⁇ s -1 ⁇ cm -2 ), V is the volume (liter) of a chamber, A is the surface area (cm 2 ) of the chamber, P is internal pressure (mbar) of the chamber, and t is time (s).
• the steel material for a vacuum tube may have yield strength (YS) of 400 ⁇ 600MPa, a yield ratio (YR) of 0.8 or less, elongation (El) of 19 ⁇ 30%, and Charpy impact energy at -20°C can satisfy the range of 30-50J.
• the steel material according to an aspect of the present disclosure has the characteristics of a low outgassing rate and a low yield ratio, the steel material can provide properties specifically appropriate as a vacuum tube for a high-speed vacuum train that is a large vacuum structure.
• a vacuum tube manufactured using the steel material according to an embodiment of the present disclosure has a low outgassing rate, it is possible not only to effectively maintain the vacuum state in the vacuum tube, but to have an excellent earthquake-proof characteristic because it has a low yield ratio.
• the steel material for a vacuum tube may have a thickness of 5-30mm, and thickness of the steel material that is applied to a vacuum tube to be applied may be selectively determined in accordance with the diameter of the vacuum tube.
• thickness of the steel material that is applied to a vacuum tube to be applied may be selectively determined in accordance with the diameter of the vacuum tube.
• a steel material having a thickness of 5 ⁇ 15mm may be applied
• a steel material having a thickness of 15 ⁇ 30mm may be applied.
• the method of manufacturing the steel material for a vacuum tube may include: providing a steel material by reheating a slab including, in percentage by weight, C: 0.1 ⁇ 0.2%, Si: 0.05 ⁇ 0.5%, Mn: 1.0 ⁇ 1.6%, Ni: 0.5 ⁇ 1.0%, Cr: 1.5 ⁇ 4.0%, and the balance of Fe and unavoidable impurities and then by hot-rolling the slab at a finishing hot-rolling temperature of 900 ⁇ 1000°C; primarily cooling the hot-rolled steel material up to 550 ⁇ 650°C at a primary cooling speed of 5 ⁇ 50°C/s; coiling the steel material into a coil at a primary cooling stop temperature after finishing the primary cooling; and secondarily cooling the coil to room temperature at a secondary cooling speed of 0.005 ⁇ 0.05°C/s.
• a slab having predetermined components can be prepared and reheated. Since the alloy composition of the slab of the present disclosure correspond to the alloy composition of the steel material described above, the description of the alloy composition of the slab of the present disclosure refers to the description of the alloy composition of the steel material described above.
• the common slab heating condition may be applied as the slab heating condition of the present disclosure, but, as a non-limiting example, reheating of the slab may be performed in a temperature range of 1200 ⁇ 1350°C.
• a hot-rolled steel material can be provided by hot-rolling the reheated slab. Finishing hot-rolling may be performed in a temperature range of 900 ⁇ 1000°C. Finishing hot-rolling may be performed in a temperature range of 900°C or more to prevent deterioration of the low yield ratio characteristic due to structure refinement. Further, it is preferable that finishing hot-rolling is performed in a temperature range of 1000°C or less to prevent an excessive scale.
• the hot-rolled steel material after hot rolling is finished is cooled up to 550 ⁇ 650°C at a primary cooling speed of 5 ⁇ 50°C/s and then can be wound into a hot-rolled coil.
• the present disclosure may perform primary cooling at a cooling speed of 5°C/s or more.
• the primary cooling speed is excessively high, there is a possibility that the shape of a product is deteriorated or a low-temperature microstructure is generated, so the present disclosure may limit the upper limit of the primary cooling speed at 50°C/s.
• the steel material having the alloy composition of the present disclosure shows the highest transformation speed at around 600°C, it is preferable to finish cooling in a temperature range of 550 ⁇ 650°C and then perform coiling in the temperature range in order to introduce all microstructures of the final steel material into a complex structure of ferrite and pearlite.
• the wound coil can be cooled up to room temperature at a secondary cooling speed of 0.005 ⁇ 0.05°C/s.
• the steel material of the present disclosure finishes ferrite and pearlite transformation at around 600°C, but it is preferable to perform secondary cooling under a low cooling condition in order to prevent some non-transformed structures from changing into low-temperature microstructures. Further, when the wound coil is cooled at a high cooling speed, poor shapes such as twisting and bending of a product may be generated, so the present disclosure may limit the upper limit of the secondary cooling speed at 0.05°C/s.
• the present disclosure does not specifically limit the lower limit of the secondary cooling speed, it is possible to limit the lower limit of the secondary cooling speed at 0.005°C/s in a meaning of excluding a cooling speed of 0°C/s.
• the cooling condition of the secondary cooling may be discharge of cold.
• the steel material manufactured through the manufacturing method described above not only have a complex structure of ferrite and pearlite, but can actively suppress formation of a hard phase such as martensite and bainite.
• a hard phase such as martensite and bainite.
• the fraction of ferrite may be 60 ⁇ 90%
• the fraction of pearlite may be 10 ⁇ 40 percent by area
• the fraction of a hard phase may be less than 1 percentage by weight (including 0%).
• the steel material manufactured through the manufacturing method may have an outgassing rate of 1.0*10 -10 mbar ⁇ l ⁇ s -1 ⁇ cm -2 or less, a yield strength (YS) of 400 ⁇ 600MPa, a yield ratio (YR) of 0.8 or less, elongation (El) of 19-30%, and Charpy impact energy of 30 ⁇ 50J at -20°C.
• a hot-rolled steel material having a thickness of 25mm was manufactured by heating a slab having the composition of Table 1 in a temperature range of 1250°C and then performing finishing hot rolling in a temperature range of 950°C. Thereafter, the hot-rolled steel material was cooled up to 600°C at a cooling speed of 25°C/s, and after cooling, the hot-rolled steel material was coiled at the cooling end temperature. Thereafter, the hot-rolled steel material was cooled up to room temperature at a cooling speed of 0.03°C/s, and then a microstructure, a yield ratio, and an outgassing rate were measured for each sample and described in Table 1.
• the microstructure was measured by etching each sample through Nital etching and using an optical microscope having a magnification of 500.
• F is ferrite and P is pearlite.
• Samples of JIS5 were taken and a tension test was performed on the samples in the rolling direction, and a yield ratio was obtained by dividing a 0.2% off-set yield strength by tensile strength.
• An outgassing rate was measured through [Equation 1] described above after configuring a vacuum chamber having a 500m length, a 150mm diameter, and a 20mm thickness. [Table 1] Samp le No.
• samples 1 and 2 that satisfy the conditions limited in the present disclosure satisfy both an outgassing ratio of 1.0*10 -10 mbar ⁇ l ⁇ s -1 ⁇ cm -2 or less and a yield ratio of 0.8 or less.
• samples 3 and 4 that did not satisfy the conditions limited in the present disclosure did not satisfy both the yield ratio and the outgassing rate intended in the present disclosure.
• the steel material according to an aspect of the present disclosure has the characteristics of both a low outgassing rate and a low yield ratio, the steel material has properties specifically appropriate as a vacuum tube for a high-speed vacuum train that is a large vacuum structure.

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• 2019
  • 2019-12-18 KR KR1020190169644A patent/KR102348664B1/ko active Active
• 2020
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