Classifications

• • 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
• • 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
  • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
  • C21D8/0273—Final recrystallisation annealing
• • 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
• • 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
• • 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%
• • 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

Definitions

• the present invention relates to a method for manufacturing a blackplate for tinplate and tin-free steel (TFS) by continuous annealing, and particularly to a method for manufacturing arbitrary grades of blackplates having T1 to T6 temper degrees through a single rolling step without significantly changing the heat cycle after the first cooling step in a continuous annealing process.
• TFS tinplate and tin-free steel
• blackplates, tinplates and TFSs for steel cans are grouped depending on their temper degree expressed by Rockwell hardness (HR30T).
• HR30T Rockwell hardness
• the blackplates, tinplates and TFSs which are prepared by a single rolling step are grouped in T1 to T6 temper degrees.
• T1 to T3 groups are called soft materials
• T4 to T6 groups are called hard materials.
• the blackplates of soft materials are
• JP-A-70227(1982) discloses a method to prepare blackplates having T4 and T5 temper degrees separately in CAL by adjusting the cooling speed in a range of from 3 to 1000°C/sec.
• JP-B-45653(1993) discloses a method to prepare blackplates having T4 and T5 temper degrees separately in CAL by controlling the average cooling speed between 500 and 400°C in the cooling step to either not more than 55°C/sec or not less than 65°C/sec, and further adjusting the reduction rate in the temper rolling.
• JP-A-92425(1985) discloses a method for manufacturing hard materials by hot rolling low carbon steels containing 0.02 to 0.10% by weight P at temperatures of less than Ar 3 transformation point, coiling the hot rolled steel sheets at a low temperature, cold rolling thus coiled steel sheets, and continuous annealing the cold rolled steel sheet with a cooling speed not less than 30°C/sec.
• JP-A-80346(1992) discloses a method for manufacturing soft materials by applying rapid cooling and overaging in CAL.
• JP-A-197523(1990) discloses a method using very low C-Nb steels for preparing soft materials by CAL, followed by changing reduction rate of temper rolling
• JP-B-10801(1985) discloses a method of combination of with or without overaging in CAL and reduction rate in dry temper rolling using 300 mm or smaller size work rolls.
• manufacture of hard materials of T4 to T6 groups requires temper rolling at high reduction rate of from 10 to 30%, which condition degrades formability of products, particularly degrades ductility, and needs a temper rolling unit for high reduction rate.
• JP-B-10801(1985) it is necessary to have two kinds of cycles, with or without overaging treatment, to manufacture blackplates having different temper degrees separately. Accordingly, the consumption of above-described dummy coil increases and the productivity decreases. Furthermore, overaging for not less than one minute is required, which extends the overaging zone, and increases the investment. In addition, since the dry temper rolling with small size work rolls is conducted, if the manufacture of soft materials is performed at a low reduction rate of about 1 to 1.5%, the rolling load becomes excessively light, which results in difficulty to assure stable rolling.
• the present invention has been derived to solve the above-described problems in prior art, and an object of the present invention is to provide a method for manufacturing a blackplate for tinplate and TFS by continuous annealing, which method uses a compact and inexpensive single CAL facility, and manufactures blackplates having different temper degrees separately and stably covering all ranges of from soft materials to hard materials without degrading productivity and yield.
• a method for manufacturing a blackplate for tinplate and TFS by continuous annealing comprises the steps of: heating and soaking an as cold rolled steel sheet of low carbon aluminum-killed steel containing not more than 0.1% by weight C and 0.001 to 0.015% by weight N, at temperatures of not less than recrystallization point; applying a first cooling to thus heated and soaked steel sheet to temperatures of from 350 to 480°C at average cooling speeds of from more than 100°C/sec to less than 300°C/sec; applying overaging to thus cooled steel sheet without giving reheating thereto; applying final cooling to thus overaged steel sheet to conduct temper rolling; wherein the temperatures for soaking at not less than recrystallization point are varied depending on aimed temper degree, thus keeping a heat cycle in stages succeeding to the first cooling nearly unchanged independent of the temper degree.
• the carbon content if the carbon content exceeds 0.1% by weight, the steel sheet becomes excessively hard, which results in difficulty of controlling the shape thereof during cold rolling, and degrades the flatness and the accuracy of sheet thickness thereof.
• excess amount of carbon may induce poor travel of sheets in continuous annealing line. Consequently, the carbon content is limited to not more than 0.1% by weight.
• the carbon content is changed depending on the target temper degree. That is, further stable manufacture of blackplates is available by adjusting the carbon content to not more than 0.05% by weight for preparing soft materials of T1 to T3 temper degrees, and adjusting the carbon content to a range of from 0.03 to 0.1% by weight for preparing hard materials of T4 to T6 temper degrees.
• the nitrogen content is limited to a range of from 0.001 to 0.015% by weight.
• Contents of other elements such as Si, Mn, P. S, and sol.Al are not specifically limited, and they may be within a range found in low carbon aluminum-killed steels used for ordinary tinplates and TFSs.
• carbide/nitride-forming elements such as B and Nb may be added, at need.
• tinplates and TFSs for steel cans are manufactured by preparing a slab of low carbon aluminum-killed steel having compositions above-described, followed by hot rolling, pickling, cold rolling, and annealing.
• the method according to the present invention there is no specific limitation on the manufacturing conditions before the annealing in CAL, and the manufacturing conditions may be those of common practice. That is, the hot rolling may be conducted at slab heating temperatures of from 1050 to 1250°C, finishing temperatures of from 830 to 900°C, and coiling temperatures of from 500 to 700°C, and the cold rolling may be conducted at reduction rates of from 80 to 95%.
• the slab is hot rolled by a direct rolling method or a hot charge rolling method.
• the coiling temperature for manufacturing blackplates of T1 to T3 temper degrees is preferably specified to a range of from 600 to 700° C.
• the coiling temperature for manufacturing blackplates of T4 to T6 temper degrees is preferably specified to a range of from 520 to 620°C.
• the as cold rolled steel sheets are annealed in CAL at a heat cycle of: heating, soaking, first cooling, overaging, and final cooling.
• the core parts of the method according to the present invention are to change the soaking temperature depending on the aimed temper degree, then to keep the heat cycle to nearly fixed independent of the temper degree, and to apply the first cooling to temperatures ranging from 350 to 480°C at average cooling speeds of from more than 100°C/sec to less than 300°C/sec, then applying overaging without reheating.
• the overaging without reheating does not mean that positive heating is given to above the end point temperature of the first cooling step, but means that the treatment is given to a degree to keep the temperature of the steel sheet.
• a small scale heater is installed in the over aging zone of CAL to make the heater always working.
• the reason to specify the average cooling speed in the first cooling step to a range of from more than 100°C/sec to less than 300°C/sec is the following. If the average cooling speed is less than 100°C/sec, the rapid cooling effect cannot be fully attained, and the supersaturation of solid solution carbon before the overaging treatment becomes insufficient, so that the manufacture of soft materials becomes difficult, also the dispersion of characteristics of hard materials increases owing to a slight fluctuation of cooling speed. And, if the average cooling speed is set to not less than 300°C/sec, there is a need of cooling facility with large cooling capacity, and the investment increases.
• the reason to specify the end temperature of the first cooling step to a range of from 350 to 480°C is the following.
• the end temperature of the first cooling step is less than 350°C, the carbon diffusion becomes insufficient.
• the end temperature of the first cooling step exceeds 480°C, the supersaturation becomes insufficient, and fully softening becomes difficult in the overaging treatment, which results in not capable of manufacturing blackplates covering all ranges from soft materials to hard materials, separately.
• the method for cooling in the first cooling step according to the present invention may be gas jet cooling, air/water cooling, roll cooling, or the like, if only the method controls the cooling speed within the above-described range. Nevertheless, gas jet cooling is most preferable in terms of cooling capacity, stability of cooling, manufacturing cost, and quality of surface of steel sheet.
• the soaking temperature of CAL is preferably specified to a range of from 660 to 780°C.
• the soaking temperature of less than 600°C leaves unrecrystallized structure, which induces degradation of formability and dispersion of characteristics. If the soaking temperature exceeds 730°C, the steel sheet becomes soft to fail in obtaining specified temper degree. Consequently, the soaking temperature of CAL is preferably specified to a range of from 600 to 730°C.
• the soaking time As for the soaking time, less than 5 seconds of soaking time is short for grain growth, and is likely to induce mixed grain sizes, and to increase dispersion of characteristics. Therefore, it is preferable to assure 5 seconds or longer soaking time. However, unnecessarily long time of soaking only results in saturation of stability of characteristics, and in increased size of furnace to raise investment and production cost . Accordingly, the soaking time is preferably specified to not more than around 20 seconds.
• the overaging time becomes not less than 60 seconds, a very long overaging zone is necessary, which induces increase in investment and production cost. Consequently, the overaging time is preferably less than 60 seconds.
• the initiation temperature of the final cooling after overaging is less than 300°C, the diffusion of carbon becomes insufficient. If the initiation temperature of the final cooling after overaging exceeds 400°C, the supersaturation of carbon becomes insufficient, and it becomes difficult to fully soften the steel sheet by overaging. Therefore, the initiation temperature of the final cooling is preferably in a range of from 300 to 400°C. With the similar reason, the difference between the inlet and the outlet of the overaging treatment, or the difference between the end temperature of the first cooling and the initiation temperature of the final cooling is preferably not more than 100°C.
• the reduction rate in temper rolling after the final cooling is less than 1.0%, it is difficult to attain aimed surface roughness, flatness, and anti-aging performance. If the reduction rate becomes not less than 3.0%, the formability degrades and there occurs necessity of reducing the roll size and changing the lubrication conditions to secure good sheet thickness and flatness. Therefore, the reduction rate in temper rolling after final cooling is preferably in a range of from not less than 1.0% to less than 3.0%.
• the blackplates for tinplate and TFS which are manufactured by the method according to the present invention, are subjected to coating treatment in Electrical Tin plating Line (ETL) or TFS line, thus producing tinplates and TFSs for steel cans.
• ETL Electrical Tin plating Line
• the method according to the present invention is, however, also applicable to manufacture blackplates for Ni coating steel sheets or other metal coating steel sheets for steel cans.
• the blackplates of T3 and T4 temper degrees overlap the hardness to each other in a range of 58 ⁇ HR30T ⁇ 60.
• the method according to the present invention gives differentiation between T1 to T3 temper degrees and T4 to T6 temper degrees as HR30T ⁇ 59 and HR30T ⁇ 59, respectively.
• Low carbon aluminum-killed steels A to J having compositions given in Table 1 were prepared separately by melting in a converter, followed by continuously casting.
• the slabs thus obtained were hot rolled and pickled, and were cold rolled to a sheet thickness of 0.20 mm.
• the slab heating temperature was set to a range of from 1150 to 1230°C
• the finish temperature was set to a range of from 860 to 900°C
• the coiling temperature was changed as shown in Tables 2 and 3.
• the steel sheets were annealed by CAL under the conditions given in Tables 2 and 3, followed by temper rolling to obtain steel sheets Nos. 1 through 22.
• No. 5 which was treated by secondary rolling after annealed, and No. 17 which was soaked at a low temperature in CAL are the Comparative Examples. All the other steel sheets are Examples according to the present invention.

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• Chemical & Material Sciences (AREA)
• Engineering & Computer Science (AREA)
• Materials Engineering (AREA)
• Mechanical Engineering (AREA)
• Metallurgy (AREA)
• Organic Chemistry (AREA)
• Physics & Mathematics (AREA)
• Thermal Sciences (AREA)
• Crystallography & Structural Chemistry (AREA)
• Heat Treatment Of Sheet Steel (AREA)
• Heat Treatment Of Strip Materials And Filament Materials (AREA)
• Heat Treatment Of Steel (AREA)

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• 1998
  • 1998-07-09 JP JP10210394A patent/JP2000026921A/ja active Pending
• 1999
  • 1999-06-29 EP EP99926832A patent/EP1022347A4/de not_active Withdrawn
  • 1999-06-29 CN CN99801104A patent/CN1101857C/zh not_active Expired - Fee Related
  • 1999-06-29 TR TR2000/00567T patent/TR200000567T1/xx unknown
  • 1999-06-29 WO PCT/JP1999/003471 patent/WO2000003043A1/ja not_active Application Discontinuation

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