WO2015099402A1 - 스트립의 연속소둔 장치 및 그 연속소둔 방법 - Google Patents
스트립의 연속소둔 장치 및 그 연속소둔 방법 Download PDFInfo
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- WO2015099402A1 WO2015099402A1 PCT/KR2014/012705 KR2014012705W WO2015099402A1 WO 2015099402 A1 WO2015099402 A1 WO 2015099402A1 KR 2014012705 W KR2014012705 W KR 2014012705W WO 2015099402 A1 WO2015099402 A1 WO 2015099402A1
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- C—CHEMISTRY; METALLURGY
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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
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
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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
- C21D1/26—Methods of annealing
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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
- C21D1/34—Methods of heating
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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
- C21D1/34—Methods of heating
- C21D1/40—Direct resistance heating
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- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/34—Methods of heating
- C21D1/42—Induction heating
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- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/34—Methods of heating
- C21D1/52—Methods of heating with flames
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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
- C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
- C21D1/60—Aqueous agents
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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
- C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
- C21D1/613—Gases; Liquefied or solidified normally gaseous material
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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
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
- C21D1/773—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material under reduced pressure or vacuum
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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
- C21D9/52—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
- C21D9/56—Continuous furnaces for strip or wire
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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
- C21D9/52—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
- C21D9/56—Continuous furnaces for strip or wire
- C21D9/561—Continuous furnaces for strip or wire with a controlled atmosphere or vacuum
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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
- C21D9/52—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
- C21D9/56—Continuous furnaces for strip or wire
- C21D9/573—Continuous furnaces for strip or wire with cooling
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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
- C21D9/52—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
- C21D9/56—Continuous furnaces for strip or wire
- C21D9/573—Continuous furnaces for strip or wire with cooling
- C21D9/5735—Details
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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
- C21D9/52—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
- C21D9/56—Continuous furnaces for strip or wire
- C21D9/60—Continuous furnaces for strip or wire with induction heating
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- 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
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing 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
- C21D2211/005—Ferrite
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
Definitions
- the present invention relates to a continuous annealing apparatus for strips and a continuous annealing method for producing a high strength, high ductility cold rolled steel sheet having excellent strength and ductility, and more particularly, to an apparatus for continuously annealing a strip and the apparatus. It relates to a method of continuous annealing using.
- Conventional annealing apparatus for manufacturing a conventional cold rolled coil includes a heating and cracking zone and a cooling zone, while heating the strip of room temperature to a predetermined temperature in the heating and cracking zone, and maintained at the same temperature for a certain time Then, it consists of cooling to room temperature in the cooling zone.
- the over-aging treatment in the over-aging stage or maintained at a temperature of 600 °C or less in the constant temperature holding and then cooled to room temperature Osstem or mar tempering is carried out.
- the heating and cracking zone recrystallizes the cold rolled strip and heats it to a temperature with the desired phase. At this time, carbide dissolution and recrystallization nucleation and growth of ferrite tissue are achieved, and austenite appears when the temperature is higher than A 3 . All of these tissues have a polygonal structure. Then, a constant temperature is maintained for a predetermined time for the purpose of obtaining an equilibrium suitable for the temperature, and the grains are grown and homogenized.
- the cooling zone is composed of a device for slow cooling and quenching, the ferrite single phase is quenched to supersaturate carbon, and the composite steel is quenched to contain a tissue containing martensite, bainite or residual austenite in the ferrite matrix. Quick-cool to obtain.
- overaging zone supersaturated carbon of ferrite single phase steel is precipitated to significantly reduce the solid solution in a short time, thereby improving workability.
- the martensite is tempered in the over-aging zone, or bainite containing bainite or residual austenite is formed through constant temperature bainite heat treatment to control strength and ductility. Excessive age can be removed depending on the purpose.
- the conventional continuous annealing heat treatment apparatus has a polygonal structure obtained by recrystallization from a heating step, and thus, the method of controlling the steel component to refine the structure, which does not effectively control even when a large amount of alloying elements are added.
- Japanese Patent Laid-Open No. 2003-328039 and Japanese Patent Laid-Open No. 1984-133329 Japanese Patent Laid-Open No. 2003-328039 and Japanese Patent Laid-Open No. 1984-133329.
- the present invention is to provide a continuous annealing apparatus of the strip capable of producing a high strength high ductility cold rolled steel sheet and galvanized steel sheet excellent in both strength and ductility.
- the present invention is to provide a method of continuous annealing using a continuous annealing device of the strip capable of producing a high strength and high ductility cold rolled steel sheet and galvanized steel sheet excellent in both strength and ductility.
- the present invention provides an apparatus for manufacturing a heating apparatus comprising: a first heating zone configured to primary heat a strip; A first cooling or constant temperature holder configured to cool or constant temperature the primary heated strip in the first heating zone; A second heating and cracking zone configured to secondary heat and crack the strip cooled or constant temperatured in the first cooling or constant temperature holding stand; And a second cooling zone configured to cool the heated and cracked strip in the second heating and cracking zone.
- an overaging and constant temperature holder configured to overage or maintain the temperature of the strip; And a final cooling zone for cooling the overaged or incubated strips in the overaging and constant temperature support.
- the present invention also provides a method of continuously annealing a strip using the continuous annealing apparatus of the strip, the method comprising: first heating the strip on a first heating table; Primary cooling or constant temperature of the first heated strip in a first cooling or constant temperature holder; Secondary heating and cracking the primary cooled or constant temperature strip at a second heating and cracking zone; And secondary cooling the secondary heated and cracked strip in a second cooling zone.
- FIG. 1 is a conceptual diagram showing a schematic configuration of an embodiment of a continuous annealing apparatus of the present invention.
- FIG. 2 is a conceptual diagram showing a schematic configuration of an embodiment of the first cooling or constant temperature holding apparatus of the continuous annealing apparatus of the present invention.
- Figure 3 is a conceptual diagram showing a schematic cross-section and operation of one embodiment of the hollow water-cooled roll of the continuous annealing apparatus of the present invention.
- Figure 4 is a conceptual diagram showing the schematic configuration and operation of one embodiment of a mobile water cooling tank of the continuous annealing apparatus of the present invention.
- Example 5 is a photograph of the microstructure of Comparative Example 2 annealed with a conventional continuous annealing device.
- FIG. 6 is a photograph of the microstructure of Inventive Example 3 annealed by the continuous annealing apparatus of an embodiment of the present invention.
- the present invention relates to a continuous annealing apparatus for a strip capable of producing a high strength, high ductility cold rolled steel sheet excellent in both strength and ductility, and a continuous annealing method thereof.
- the continuous annealing apparatus of the present invention can be subjected to continuous annealing by a method of cooling after heating and then heating again, unlike the conventional continuous annealing apparatus which performs heating only once and then cooling or overaging.
- the continuous annealing apparatus of the present invention is capable of firstly homogenizing or controlling the tissue to the desired tissue, and then performing another reheating heat treatment to control the stabilization or morphology of the tissue as desired.
- the present invention confirms that the physical properties deviating from the conventional physical properties can be obtained by diversifying the temperature raising method rather than the single heating method, and provide a new continuous annealing apparatus capable of realizing this.
- the continuous annealing apparatus of the strip of the present invention comprises: a first heating table (1) configured to primary heat the strip; A first cooling or constant temperature holder (2) configured to cool or constant temperature the primary heated strip in this first heating zone (1); A second heating and cracking zone (3) configured to secondaryly heat and crack the strip cooled or constant temperatured in the first cooling or constant temperature holder (2); And a second cooling zone 4 configured to cool the heated and cracked strips in the second heating and cracking zone 3.
- the structure of the strip in the first heating zone and in the first cooling or constant temperature support, can be controlled to homogenization or the desired structure, and in the second heating and cracking zone and in the second cooling zone the structure of the strip is controlled. It may be stabilized or controlled in the desired form. In this way, it is possible to first homogenize or control the tissue to the desired tissue, and then perform another reheating treatment to control the stabilization or shape of the tissue as desired. Not only can be prepared, but it is possible to control the thickness of the element and oxide concentrated on the surface of the strip (strip) to produce a galvanized strip excellent in the plating surface.
- the continuous annealing apparatus of the strip includes: an overaging and constant temperature holder (5) configured to overage or maintain the strip at the rear of the second cooling stand (4); And a final cooling zone 6 for cooling the overaged or incubated strips in the overaging and constant temperature holders.
- Continuous annealing heat treatment is carried out using the continuous annealing apparatus of the present invention, in which the first heating table 1 and the first cooling or constant temperature holding table 2 are added, and then cooled after heating to form martensite or bainite to refine the structure. Then, the reheating heat treatment can be performed, and high strength and high workability can be obtained even with a small amount of alloying elements. Further, by strengthening the recrystallized texture of the ultra low carbon steel, excellent deep drawing property can be obtained.
- the heating of the strip in the first heating table 1 is preferably performed by an induction heating method, a radiant tube heating method or a direct heating method.
- the first cooling or constant temperature support 2 includes a cooling device 23 by gas, a cooling device 24 by gas and mist, and a cooling device by gas, mist and water ( It is preferable to include at least one cooling device of 25). In order to adjust the cooling rate to 5 ⁇ 200 °C / s as needed, it can be provided with the above devices.
- the plating apparatus when the plating apparatus is provided behind the continuous annealing apparatus, it is preferable that all the cooling apparatuses 23, 24, and 25 which consist of 1-3 are the cooling apparatus 23 by gas. This is because when the plating is performed in the plating apparatus, if water is cooled by water and / or mist, an oxide film is formed on the mist or the surface and plating is difficult.
- the first cooling or constant temperature holder 2 is provided with a tension control roll 21 for each of the inlet and outlet. As shown in Fig. 2, by providing the tension control roll 21 at the inlet and outlet, it is possible to cope with the linear expansion of the strip for transformation during rapid cooling.
- the first cooling or constant temperature holder 2 includes at least one gas and vapor discharge device 22 for generating a negative pressure therein.
- the first cooling or constant temperature support (2) is to prevent the diffusion of the vapor to the device provided before and after, when the vapor inside the high vapor can be generated.
- the first cooling or constant temperature holder 2 includes a pair of hollow water cooling rolls 26 at the rear of the rearmost cooling device 25 in the advancing direction of the strip. and;
- the pair of hollow water-cooling rolls (26) are arranged such that the strips cooled in the cooling devices (23, 24, 25) are movable therebetween;
- the hollow water-cooling roll 26 is rotatable and preferably configured to flow the cooling water therein, more preferably, the hollow water-cooling roll 26 is configured to be movable in the left and right directions.
- the hollow water cooling roll 26 is installed to maximize the water cooling efficiency. Among the gas, mist and water generated in the cooling devices 23, 24 and 25, water falls downwardly by gravity, between the hollow water-cooling rolls 26, rotating at the same speed as the strip that proceeds. When the water is discharged through the gaps, water film is formed on the surface of the strip to prevent boiling and achieve uniform cooling.
- the hollow water cooling roll 26 preferably has a pupil structure in order to allow the cooling water to flow therein. By allowing the cooling water to flow into the hollow water cooling roll 26, the surface temperature of the hollow water cooling roll 26 can be prevented from rising, thereby preventing boiling of the cooling water flowing from the cooling device.
- the hollow water-cooling roll 26 is more preferably configured to be able to move in the left and right direction to adjust the cooling water flow rate.
- the cooling water stored between the hollow water cooling rolls 26 is cooling water flowing down from the cooling devices 23, 24, and 25 located above the hollow water cooling rolls 26.
- cooling devices 23, 24, 25 are all composed of the gas cooling device 23, it is not necessary to install the hollow water cooling roll 26, or the hollow water cooling roll 26 shown on the right side of FIG. It is desirable to open the bar completely left and right in the form of.
- the movable water cooling tank 27 is preferably configured to be movable in the vertical direction. When it is not necessary to cool below 80 ° C, open the hollow water cooling roll 26 and move the movable water cooling tank 27 down as shown on the right side of FIG. 4 so that water does not touch the traveling strip. .
- the circulation type fixed water cooling tank 28 located below the first cooling or constant temperature holding holder 2 has a structure in which cooling water at room temperature continues to circulate. Steam generated by the contact of the mobile water cooling tank 27 and the circulation fixed water cooling tank 28 with the hot strip is completely discharged from the gas and vapor discharge device 22 so as not to enter the second heating table 3.
- the cooling water outlet 29 located at the bottom of the circulation type fixed water cooling tank 28 has a good discharge of mist and water injected from the cooling devices 24 and 25, so that the cooling water of the circulation type fixed water cooling tank 28 is desired. Control the flow rate to the height.
- the cooling device 23, 24, 25 is stopped when the first cooling or constant temperature holding is to be performed in the constant temperature holding table, not cooling. What is necessary is just to open the type
- the processes in the second heating and cracking zone 3, the second cooling zone 4, the overaging and constant temperature holding zone 5, and the final cooling zone 6 are not particularly limited, and the conventional continuous annealing apparatus ( 7) can be used, but will be described briefly below.
- the second heating and cracking zone (3) can be heated up to 950 °C, constant temperature maintenance can be configured to maintain for more than 10 seconds.
- the second cooling stand 4 may be configured as a slow cooling stand by gas cooling, and a rapid cooling stand capable of cooling at 10 ° C / s or more.
- the optional aging and constant temperature holder (5) which can be selectively added, is used to keep the inside of the aging and constant temperature support (5) at a constant temperature by using the sensible heat of the strip after cooling, or to be actively equipped with heating facilities Can keep constant temperature.
- the final cooling stand (6) which can be optionally further configured, such as the overaging and constant temperature support (5), is configured to be cooled to room temperature, omitting the configuration of the final cooling stand (6) and attaching a plating apparatus. can do.
- the continuous annealing method of the strip according to the present invention comprises the steps of first heating the strip in a first heating zone using the continuous annealing apparatus of the strip of the present invention; Primary cooling or constant temperature of the first heated strip in a first cooling or constant temperature holder; Secondary heating and cracking the primary cooled or constant temperature strip at a second heating and cracking zone; And secondary cooling the secondary heated and cracked strip in a second cooling zone.
- the continuous annealing method of the strip after the secondary cooling step, the step of overaging or constant temperature holding the strip; And cooling the overaged or incubated strip.
- the heating of the strip is preferably performed by an induction heating method, a radiant tube heating method or a direct heating method, and by selecting the heating method as described above, the temperature increase rate is 3 to 150 ° C. It is preferable to heat up to 1000 ° C. in order to prevent the increase in energy cost, the reduction of the steel strength and the deterioration of the sheet flow.
- the first heating table (1) may be configured to be able to maintain a constant temperature, there is a problem that the line length is long, it is preferable to be configured to maintain within 10 seconds.
- the cooling or constant temperature holding in the first cooling or constant temperature holder (2) is carried out by at least one of a gas cooling method, a hydrogen cooling method, a mist cooling method of mixing water and gas and a water cooling method of directly spraying water. It is preferably made, by the cooling method as described above, the cooling rate can be adjusted to 5 ⁇ 200 °C / s, it is preferable to cool to at least 80 °C to improve the ductility.
- the cooling or constant temperature holding in the first cooling or constant temperature holder 2 is preferably performed by a gas cooling method.
- the first cooling or constant temperature holding step is preferably performed in a state in which a tension of 1/5 to 3/5 of the yield strength is applied to the strip.
- the tension control rolls 21 of the first cooling or constant temperature holder 2 are preferably provided at both ends of the first cooling or constant temperature holder 2, so that the linear expansion of the strip against transformation during rapid cooling is achieved. It is preferable that the tension control roll 21 gives the strip a tension of 1/5 to 3/5 of its yield strength.
- stepwise cooling and tension are artificially performed in order to prevent a case of plate bending due to linear expansion, and plate warping due to non-uniform cooling, resulting in transformation of bainite or martensite from austenite. To correct the plate shape.
- the first cooling or constant temperature maintaining step is preferably carried out in a state in which a negative pressure is formed.
- the steel sheet manufactured by the continuous annealing method of the present invention as described above is excellent in drawingability because the Rankford (r) value is higher than that of the usual heat treatment method in the case of ultra-low carbon steel, and the composite structure of the ferrite and the secondary phase is fine so that the strength and the High ductility cold rolled steel sheet and galvanized steel sheet excellent in both ductility can be produced.
- a steel slab prepared as shown in Table 1 was prepared by vacuum induction melting, and heated and extracted at a temperature of 1200 ° C., followed by hot rolling in a range of 900 ° C. or higher.
- the thickness of the hot rolled sheet is 3.2mm, which is maintained at a temperature of 500 to 700 ° C. for 1 hour, followed by cooling to room temperature, and then removing the scale to prepare a cold rolled steel sheet having a thickness of 1 mm.
- an infrared heating apparatus reproduced the conventional heat treatment method and the heat treatment method of the present invention, and the Rankford (r) value, which is an index indicating tensile test and plastic anisotropy, was measured at a strain of 15%.
- the texture was analyzed by EBSD (Electron Back Scattered Diffraction) analysis. The EBSD analysis was performed to remove the residual stress on the surface by polishing to 1 / 4t of the heat-treated specimen and then electrolytic polishing, and then measured the strength of the texture in the surface direction.
- Tensile test was processed in ASTM standard size to evaluate the yield strength (YS), tensile strength (TS) and elongation (El).
- Inventive Example 1 subjected to the heat treatment of the present invention as a steel having a composition of the ultra-low carbon steel of Table 1 is heated to 700 °C at 5 °C / s and then cooled to 620 °C at a cooling rate of 5 °C / s similar heat treatment
- Primary heating constant temperature heat treatment was carried out to become. Although it can hold
- Secondary heating and heat treatment is heated to 850 °C at 5 °C / s as usual, maintained at 850 °C for 60 seconds, then slowly cooled to 650 °C at 5 °C / s and then quenched to 400 °C at 15 °C / s and 400 °C After 120 seconds at the temperature was cooled to room temperature.
- Comparative Example 1 which was carried out by the conventional heat treatment method with the composition of the ultra low carbon steel, was heat treated in the same manner from the secondary heat treatment. That is, as usual, without primary heat treatment, heated to 850 °C at 5 °C / s and held at 850 °C for 60 seconds, then slowly cooled to 650 °C at 5 °C / s and then quenched to 400 °C at 15 °C / s 400 °C After 120 seconds at a temperature of air cooled to room temperature.
- the heat treatment of the present invention has a high strength of ⁇ 111 ⁇ aggregate structure, which is advantageous for workability.
- ⁇ 111 ⁇ ⁇ 110> ⁇ ⁇ 111 ⁇ ⁇ 112> Aggregates are called gamma textures.
- the ⁇ 100 ⁇ and ⁇ 110 ⁇ orientations develop but grow slowly.
- the temperature range of 600 ⁇ 750 °C the growth of the ⁇ 111 ⁇ aggregate tissue is actively developed and becomes more developed.
- a composite structure steel was manufactured using the steel having the composition of the alloy steel of Table 1 above.
- Inventive Examples 2 to 4 subjected to the heat treatment by the apparatus of the present invention is heated to 900 °C at 5 °C / s as shown in Table 3 and then cooled to 80 ⁇ 300 °C, the temperature below Ms at a cooling rate of 15 °C / s It is.
- the secondary heating and heat treatment is heated to 820 °C at 5 °C / s as usual, and maintained at 820 °C for 60 seconds and then to 650 °C at 5 °C / s
- the solution was quenched to 400 ° C. at 15 ° C./s and held at 400 ° C. for 120 seconds, followed by air cooling at room temperature.
- Comparative Example 2 subjected to heat treatment of the conventional apparatus using the steel having the composition of the alloy steel of Table 1 was heat treated in the same manner from the secondary heat treatment. That is, as usual, without the first heat treatment, heated to 820 °C at 5 °C / s and held at 820 °C for 60 seconds, then slowly cooled to 650 °C at 5 °C / s and then quenched to 400 °C at 15 °C / s 400 °C After 120 seconds at a temperature of air cooled to room temperature.
- Inventive Example 3 the whole is transformed into coarse polygonal austenite, and after rapid cooling to 200 ° C., a substantial part is transformed into martensite to have a structure of martensite and residual austenite.
- Martensite contains a large amount of dislocations, and the higher the temperature, the lower the dislocation density and the area fraction of martensite.
- the supersaturated carbon from martensite moves to austenite, so that the lattice constants of martensite have the same tetragonal structure and become ferrite, and the carbon enriched with austenite is austenite. Stabilize. This is called Reverse Transformation.
- the present invention is a core apparatus in which the tissue is refined by the secondary heat treatment. Subsequently, in slow cooling to 650 ° C., ferrite is formed of quasi-polygonal ferrite. Accordingly, in the heat treatment by the apparatus of the present invention, fine quasi-polygonal ferrite and fine austenite appear to obtain a ferrite structure that is four times finer than the conventional heat treatment method. Subsequently, the bainite constant temperature transformation at 400 ° C. results in the appearance of bainite from rod-shaped microdispersed austenite, and the austenite / benite is much finer than the polygonal austenite obtained from conventional heat treatment. Due to the wider area of austenite, the austenite stabilization is smooth and the amount of retained austenite is much increased, resulting in excellent ductility.
- the amount of martensite decreases slightly to the tensile strength, but the yield strength is increased by the refinement of the ferrite structure, and the residual austenite is more stabilized, thereby increasing the ductility.
- the yield strength can be controlled by adjusting the primary cooling temperature using the same alloy steel. The higher the primary cooling temperature, the higher the yield strength, the lower the amount of Athermal Martesite and the higher the austenite. This is because the ferrite structure is made finer by decreasing.
- the steel sheet manufactured by the apparatus of the present invention is not only excellent in drawing property because the r value is higher than that of the ordinary heat treatment method in the case of ultra low carbon steel, and the composite structure of ferrite and secondary phase There is an advantage that can produce a high strength high ductility cold rolled steel sheet and a galvanized steel sheet excellent in both strength and ductility.
- first heating table 2 first cooling or constant temperature support
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Abstract
Description
강종 | C | Mn | Si | P | S | Al | Ti | N |
극저탄소강 | 0.003 | 0.25 | Tr | 0.011 | 0.008 | 0.03 | 0.05 | 0.002 |
합금강 | 0.2 | 1.5 | 1.5 | 0.009 | 0.005 | 0.04 | Tr | 0.004 |
구분 | φ1 | φ2 | Φ | Texture | f(g) | YS | TS | El | r |
발명예 1 | 60 | 45 | 55 | {111}<110> | 13.1 | 18 | 29 | 48 | 2.69 |
90 | 45 | 55 | {111}<112> | 9.6 | |||||
비교예 1 | 60 | 45 | 55 | {111}<110> | 10.4 | 19 | 29 | 45 | 2.28 |
90 | 45 | 55 | {111}<112> | 6.2 |
구분 | 1 차소둔온도 | 1 차냉각온도 | 2 차소둔온도 | YS | TS | El |
발명예 2 | 900 | 80 | 820 | 615 | 1012 | 22 |
발명예 3 | 900 | 200 | 820 | 632 | 1008 | 26 |
발명예 4 | 900 | 300 | 820 | 658 | 998 | 26 |
비교예 2 | - | - | 820 | 420 | 1072 | 17 |
Claims (9)
- 스트립을 1 차 가열하도록 구성되는 제 1 가열대;상기 제 1 가열대에서 1 차 가열된 스트립을 냉각하거나 항온 유지하도록 구성되는 제 1 냉각 또는 항온 유지대;상기 제 1 냉각 또는 항온 유지대에서 냉각하거나 항온 유지된 스트립을 2 차 가열 및 균열하도록 구성되는 제 2 가열 및 균열대; 및상기 제 2 가열 및 균열대에서 가열 및 균열된 스트립을 냉각하도록 구성되는 제 2 냉각대를 포함하는 스트립의 연속소둔 장치.
- 제 1 항에 있어서, 상기 제 1 가열대 및 제 1 냉각 또는 항온 유지대에서는 스트립의 조직이 균질화 또는 원하는 조직으로 제어되고; 그리고 상기 제 2 가열 및 균열대, 및 제 2 냉각대에서는 스트립의 조직이 안정화되거나 원하는 형태로 제어되는 것을 특징으로 하는 스트립의 연속소둔 장치.
- 제 1 항에 있어서, 상기 제 2 냉각대 후방에, 스트립을 과시효 또는 항온유지 하도록 구성되는 과시효 또는 항온 유지대; 및상기 과시효 또는 항온 유지대에서 과시효 또는 항온유지된 스트립을 냉각하는 최종 냉각대를 추가로 포함하는 스트립의 연속소둔 장치.
- 제 1 항에 있어서, 상기 제 1 냉각 또는 항온 유지대는 내부에 음압을 발생시키는 가스 및 증기배출장치를 적어도 하나 이상 포함하는 스트립의 연속소둔 장치.
- 스트립을 연속소둔하는 방법에 있어서,스트립을 제 1 가열대에서 1 차 가열하는 단계;상기 1 차 가열된 스트립을 제 1 냉각 또는 항온 유지대에서 1 차 냉각하거나 항온 유지하는 단계;상기 1 차 냉각 또는 항온 유지된 스트립을 제 2 가열 및 균열대에서 2 차 가열 및 균열하는 단계; 및상기 2 차 가열 및 균열된 스트립을 제 2 냉각대에서 2 차 냉각하는 단계를 포함하는 스트립의 연속소둔 방법.
- 제 5 항에 있어서, 상기 2 차 냉각단계 후, 스트립을 과시효 또는 항온유지하는 단계; 및 상기 과시효 또는 항온유지된 스트립을 냉각하는 단계를 추가로 포함하는 스트립의 연속소둔 방법.
- 제 5 항에 있어서, 상기 제 1 가열대에서, 스트립의 가열은 유도가열방식, 라디안트 튜브 (Radiant Tube) 가열 방식 또는 직화 가열방식에 의해 이루어지고, 승온속도는 3~150℃/s이고, 가열온도는 최대 1000℃이고, 그리고 유지시간은 10초 이하인 것을 특징으로 하는 스트립의 연속소둔 방법.
- 제 5 항에 있어서, 제 1 냉각 또는 항온 유지대에서 냉각 또는 항온유지는 가스냉각방식, 수소냉각방식, 물과 가스를 혼합 분사하는 미스트 냉각방식 및 물을 직접 분사하는 수냉각 방식 중 적어도 하나의 방식에 의해 이루어지고, 냉각속도는 5~200℃/s 이고, 그리고 냉각온도는 최저 80℃인 것을 특징으로 하는 스트립의 연속소둔 방법.
- 제 5 항에 있어서, 상기 제 1 냉각 또는 항온 유지단계는 음압이 형성된 상태에서 실시하는 것을 특징으로 하는 스트립의 연속소둔 방법.
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Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US10407751B2 (en) | 2014-07-03 | 2019-09-10 | Arcelormittal | Multipurpose processing line for heat treating and hot dip coating a steel strip |
JP2019518876A (ja) * | 2016-05-10 | 2019-07-04 | ユナイテッド ステイツ スチール コーポレイションUnited States Steel Corporation | 高強度鋼製品及び該製品を製造するためのアニーリング工程 |
JP7186694B2 (ja) | 2016-05-10 | 2022-12-09 | ユナイテッド ステイツ スチール コーポレイション | 高強度鋼製品及び該製品を製造するためのアニーリング工程 |
Also Published As
Publication number | Publication date |
---|---|
US10358691B2 (en) | 2019-07-23 |
EP3088538B1 (en) | 2019-03-13 |
KR20150075311A (ko) | 2015-07-03 |
CN105849289B (zh) | 2018-08-28 |
US20190276913A1 (en) | 2019-09-12 |
JP2017504716A (ja) | 2017-02-09 |
US20160355903A1 (en) | 2016-12-08 |
JP6641279B2 (ja) | 2020-02-05 |
EP3088538A4 (en) | 2017-01-11 |
US10604820B2 (en) | 2020-03-31 |
EP3088538A1 (en) | 2016-11-02 |
CN105849289A (zh) | 2016-08-10 |
WO2015099402A8 (ko) | 2015-09-17 |
KR101568547B1 (ko) | 2015-11-11 |
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