EP1002884A1 - Plaque d'acier laminee a froid possedant d'excellentes caracteristiques d'aptitude au moulage et de formabilite en panneaux, une bonne resistance a la constriction, plaque d'acier a placage en zinc moule et procede de fabrication de ces plaques - Google Patents

Plaque d'acier laminee a froid possedant d'excellentes caracteristiques d'aptitude au moulage et de formabilite en panneaux, une bonne resistance a la constriction, plaque d'acier a placage en zinc moule et procede de fabrication de ces plaques Download PDF

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Publication number
EP1002884A1
EP1002884A1 EP98944222A EP98944222A EP1002884A1 EP 1002884 A1 EP1002884 A1 EP 1002884A1 EP 98944222 A EP98944222 A EP 98944222A EP 98944222 A EP98944222 A EP 98944222A EP 1002884 A1 EP1002884 A1 EP 1002884A1
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European Patent Office
Prior art keywords
steel sheet
panel
weight
resistance
rolled steel
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP98944222A
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German (de)
English (en)
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EP1002884A4 (fr
EP1002884B1 (fr
Inventor
Fusato Kitano
Masaya Morita
Yoshihiro Hosoya
Takeshi Fujita
Tadashi Inoue
Masahiro Iwabuchi
Takeo Ishii
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JFE Engineering Corp
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NKK Corp
Nippon Kokan Ltd
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Priority to EP09150416A priority Critical patent/EP2172575A1/fr
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Publication of EP1002884A4 publication Critical patent/EP1002884A4/fr
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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
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C21D8/04—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 to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/0421—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 to produce plates or strips for drawing, e.g. for deep-drawing characterised by the working steps
    • C21D8/0426—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
    • C21D8/04—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 to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/0421—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 to produce plates or strips for drawing, e.g. for deep-drawing characterised by the working steps
    • C21D8/0436—Cold rolling
    • 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
    • C22C38/02—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
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/024—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by cleaning or etching

Definitions

  • the present invention relates to a cold-rolled steel sheet and a galvanized steel sheet, which are excellent in formability, panel shapeability, and dent-resistance required for an outer panel of a motor car, and a method of manufacturing the same.
  • An excellent formability, a satisfactory shape after a panel formation and a high dent-resistance (resistance to local depression) are required for a steel sheet for an outer panel of a motor car.
  • the panel formability is evaluated by indexes such as yield strength, elongation, and an n-value (work-hardening index) of the steel sheet.
  • the panel shapeability and the dent-resistance are evaluated in many cases by yield strength and the yield strength after the working and the coating-baking treatment. If the yield strength of the steel sheet is weakened, the press formability can be improved. However, the dent-resistance after the panel formation is rendered unsatisfactory.
  • a method of manufacturing a BH steel sheet having a excellent deep drawability which is a cold-rolled steel sheet prepared by adding elements capable of forming carbonitrides such as Nb and Ti to a steel having a very low carbon content of about 50 ppm, the addition amount of such an element being not larger than 1 in terms of the atomic ratio of carbon.
  • Japanese Patent Publication (Kokoku) No. 60-46166 teaches that a Nb or Ti added low-carbon steel is annealed at a high temperature close to 900°C for manufacturing the particular BH steel sheet.
  • Japanese Patent Disclosure (Kokai) No. 61-276928 teaches that an extra low carbon BH steel sheet is manufactured by annealing under a temperature region of about 700 to 850°C.
  • JP '166 The technology disclosed in JP '166 is certainly advantageous in that the BH properties and an r-value can be improved.
  • the annealing is performed at a high temperature, the rough surface derived from enlargement of the ferrite grains is worried about.
  • the steel sheet itself is softened, the yield strength after the press forming and the baking steps is not acceptably high, though high BH properties may be obtained.
  • the annealing temperature is relatively low, compared with that employed in JP '166, and, thus, is desirable in the required surface properties and the yield strength.
  • the cold-rolled sheet manufactured by the conventional method is not sufficiently satisfactory in the surface properties, the resistance to natural aging, and the dent-resistance, which are required for the steel sheet used for an outer panel of a motor car.
  • An object of the present invention is to provide a cold-rolled steel sheet and a galvanized steel sheet, which are satisfactory in any of the surface properties, the resistance to natural aging, and the dent-resistance, which are required for the steel sheet used for an outer panel of a motor car, and a method of manufacturing the same.
  • the present inventors have conducted an extensive research in an attempt to obtain a cold-rolled steel sheet and a galvanized steel sheet, which are excellent in the surface properties, the resistance to natural aging and the dent-resistance required for the steel used for an outer panel of a motor car, and a method of manufacturing the same.
  • the dent-resistance of a panel can be improved by an alloy design with an emphasis placed on the work-hardening behavior in a low strain region in the panel forming step, unlike the prior art in which the dent-resistance required for an outer panel of a motor car is improved by increasing the BH value. It has also been found that good surface properties and resistance to natural aging can be imparted to the steel sheet by positively suppressing the BH value.
  • % represents “% by weight”.
  • a carbide formed together with Nb affects the work-hardening in a low strain region in panel forming step and contributes to an improvement of the dent-resistance.
  • the particular effect cannot be obtained, if the C amount is less than 0.005%. Also, if the C amount exceeds 0.015%, the dent-resistance of the panel is certainly improved. However, the shape of the panel is impaired. It follows that the C amount should fall within a range of between 0.005 and 0.015%.
  • Silicon is effective for strengthening the steel. However, if the Si amount is smaller than 0.01%, it is impossible to obtain a capability of the solid solution strengthening. On the other hand, if the Si amount is larger than 0.2%, the surface properties of the steel sheet are impaired. In addition, striped surface defects are generated after galvanizing. Therefore, the Si amount should fall within a range of between 0.01 and 0.2%.
  • Manganese serves to precipitate sulfide and to suppress deterioration of the hot ductility. Also, Mn is effective for strengthening the steel. If the Mn amount is less than 0.2%, hot brittleness of the steel sheet is brought about, leading to a low yield. In addition, a high mechanical strength characterizing the steel sheet of the present invention cannot be obtained. Further, Mn, which relates to an improvement in the workability of the steel sheet, is necessary for controlling the morphology of the MnS in the hot rolling step. It should be noted that fine MnS particles are formed by the process of resolution and re-precipitation in the hot rolling step. These MnS particles impair the grain growth of the steel.
  • Mn amount should fall within a range of between 0.2% and 1.5%.
  • Phosphorus is most effective for the solid solution strengthening of steel. If the P amount is smaller than 0.01%, however, P fails to exhibit a sufficient strengthening capability. On the other hand, if the P amount exceeds 0.07%, the ductility of the steel sheet is deteriorated. Also, a defective coating is brought about in the step of the alloying treatment during the continuous galvanizing process. It follows that the P amount should fall within a range of between 0.01 and 0.07%.
  • Sulfur if added in an amount exceeding 0.015%, brings about hot brittleness of the steel. If the S amount is smaller than 0.006%, however, the peeling capability of the scale is impaired in the hot rolling step, and surface defects tend to be generated markedly. It follows that the S amount should fall within a range of between 0.006 and 0.015%.
  • Aluminum serves to deoxidize the steel and fix N as nitride. If the Al amount is smaller than 0.01%, however, the deoxidation and the fixation of N cannot be achieved sufficiently. On the other hand, if the Al amount is larger than 0.08%, the surface properties of the steel sheet are deteriorated. Therefore, the Al amount should fall within a range of between 0.01 and 0.08%.
  • Nitrogen is fixed in the form of AlN. If the N amount exceeds 0.004%, however, it is impossible to obtain a desired formability of the steel sheet. Naturally, the N amount should not exceed 0.004%.
  • Niobium is bonded to C to form fine carbide particles. These fine carbide particles affect the work-hardening behavior in the panel forming step so as to contribute to an improvement in the dent-resistance of the panel. If the Nb amount is smaller than 0.04%, however, it is impossible to obtain the particular effect. On the other hand, if the Nb amount exceeds 0.23%, the panel shapeability such as the spring back and the surface deflection is deteriorated, though the dent-resistance is certainly improved. Naturally, the Nb amount should fall within a range of between 0.04 and 0.23%.
  • the grain boundary is strengthened so as to improve the resistance to the secondary working brittleness.
  • the ferrite grains are diminished so as to ensure an absolute value of the yield strength and, thus, to improve the dent-resistance.
  • the B amount is smaller than 0.0001%.
  • the B amount exceeds 0.002%, the yield point is increased and, thus, the panel shapeability is impaired. It follows that the B amount should fall within a range of between 0.0001 and 0.002%.
  • a ratio of flow stress ⁇ obtained by a tensile test under the condition that a true strain ⁇ is larger than 0.002 and not larger than 0.096, i.e., 0.002 ⁇ ⁇ ⁇ 0.096, to a 0.2% proof stress ⁇ 0.2 , i.e., ⁇ / ⁇ 0.2 , should fall within a range of between exp( ⁇ ) ⁇ (5.29 ⁇ exp( ⁇ ) - 4.19) and exp( ⁇ ) ⁇ (5.64 ⁇ exp( ⁇ ) - 4.49) .
  • the dent-resistance load under the conditions of 2%P0.1, 4%P0.1, 8%P0.1 is as high as 160 to 190N as shown in FIGS. 3 to 5.
  • a steel sheet is formed to a model panel shown in FIG. 2 with strain of 2%, 4% or 8% imparted to the steel sheet, followed by applying a heat treatment at 170°C for 20 minutes. Then, measured is a load required for imparting a residual displacement of 0.1 mm to the model panel.
  • the spring back ⁇ (measured for a panel having a strain of 2%) is as large as 7 to 10% so as to impair the panel shapeability, if the ratio ⁇ / ⁇ 0.2 is lower than the lower limit noted above. On the other hand, if the ratio ⁇ / ⁇ 0.2 is higher than the upper limit noted above, the spring back ⁇ is as small as 2 to 5% to improve the panel shapeability.
  • the dent-resistance is as low as 140 to 175N. In other words, the dent-resistance cannot be improved.
  • the ratio ⁇ / ⁇ 0.2 should fall within a range of between exp( ⁇ ) ⁇ (5.29 ⁇ exp( ⁇ ) - 4.19) and exp( ⁇ ) ⁇ (5.64 ⁇ exp( ⁇ ) - 4.49) .
  • a cold-rolled steel sheet and a galvanized steel sheet excellent in the panel surface properties and the dent-resistance required for the steel used for an outer panel of a motor car can be obtained by controlling the additive components as described in item (1) above and the tensile characteristics as described in item (2) above.
  • the steel sheet exhibiting the particular properties can be manufactured as follows.
  • steel of the composition given in item (1) above is melted.
  • a converter method is generally employed for melting the steel composition, or an electric furnace method can also be employed.
  • the slab is heated immediately after the casting, or after the slab is once cooled, for applying a hot rolling.
  • the hot rolling is performed under the conditions that the finishing temperature is set at temperature not less than (Ar 3 -100)°C and that the coiling temperature is set at 500°C to 700°C. If the finishing temperature is lower than (Ar 3 -100)°C, 2%P0.1, i.e., the dent-resistance load of the panel imparted with 2% of strain) is as low as 140 to 150N, as shown in FIG. 6.
  • the dent-resistance of the panel cannot be improved.
  • the value of 2%P0.1 is high, i.e., 155 to 165N.
  • the value of ⁇ i.e., the spring back amount of the panel imparted with 2% of strain, is as large as 8% to 10%, leading to a poor shapeability.
  • the value of Wca i.e., Arithmetic Average Waviness Height; measuring length of 25 mm; average of the values measured at 10 optional points around the apex of the panel
  • Wca Arithmetic Average Waviness Height; measuring length of 25 mm; average of the values measured at 10 optional points around the apex of the panel
  • the finishing temperature should be not lower than (Ar 3 -100)°C and that the coiling temperature should fall within a range of between 500°C and 700°C.
  • the hot-rolled steel band is subjected to pickling, cold-rolling and, then, a continuous annealing.
  • galvanizing is applied after the continuous annealing.
  • the cold-rolling reduction should desirably be at least 70% in order to improve the deep drawability (r-value) of the steel sheet.
  • the annealing should desirably be carried out within a recrystallization temperature region of the ferrite phase.
  • the coating employed in the present invention is not limited to continuous galvanizing. Specifically, even if a surface treatment such as coating with zinc phosphate or an electrolytic galvanizing is applied to the steel sheet obtained by the continuous annealing, no problem is brought about in the characteristics of the resultant steel sheet.
  • % represents “% by weight”.
  • a carbide formed together with Nb or Ti affects the work-hardening in a low strain region in the panel forming step and contributes to an improvement of the dent-resistance.
  • the particular effect cannot be obtained, if the C amount is less than 0.004%. Also, if the C amount exceeds 0.015%, the dent-resistance of the panel is certainly improved. However, the shape of the panel is impaired. It follows that the C amount should fall within a range of between 0.004 and 0.015%.
  • Silicon is effective for strengthening the steel. However, if the Si amount is smaller than 0.01%, it is impossible to obtain a capability of strengthening. On the other hand, if the Si amount is larger than 0.2%, the surface properties of the steel sheet are impaired. In addition, striped surface defects are generated after galvanizing. Therefore, the Si amount should fall within a range of between 0.01 and 0.2%.
  • Manganese serves to precipitate sulfide and to suppress deterioration of the hot ductility. Also, Mn is effective for strengthening the steel. If the Mn amount is less than 0.1%, hot brittleness of the steel sheet is brought about. However, if the Mn amount exceeds 1.5%, the steel sheet is hardened and the panel shapeability of the steel sheet is deteriorated. It follows that Mn amount should fall within a range of between 0.1% and 1.5%.
  • Phosphorus is most effective for strengthening the steel. If the P amount is smaller than 0.01%, however, P fails to exhibit a sufficient strengthening capability. On the other hand, if the P amount exceeds 0.07%, the ductility of the steel sheet is deteriorated. Also, a defective coating is brought about in the step of the alloying treatment during the process of the continuous galvanizing. It follows that the P amount should fall within a range of between 0.01 and 0.07%.
  • Sulfur if added in an amount exceeding 0.015%, brings about hot brittleness of the steel.
  • the S amount smaller than 0.005% is undesirable in terms of the manufacturing cost of the desired steel sheet because a desulfurization treatment and a degassing treatment of the molten steel are required. It follows that the S amount should fall within a range of between 0.005 and 0.015%.
  • Aluminum serves to deoxidize the steel. If the Al amount is smaller than 0.01%, however, the deoxidation cannot be achieved sufficiently. On the other hand, if the Al amount is larger than 0.08%, the surface properties of the steel sheet are deteriorated. Therefore, the Al amount should fall within a range of between 0.01 and 0.08%.
  • Nitrogen is fixed in the form of TiN. If the N amount exceeds 0.005%, however, the resistance to natural aging is deteriorated. Naturally, the N amount should not exceed 0.005%.
  • Niobium is bonded to C to form fine carbide particles. These fine carbide particles affect the work-hardening behavior in the panel forming step so as to contribute to an improvement in the dent-resistance of the panel. If the Nb amount is smaller than 0.02%, however, it is impossible to obtain the particular effect. On the other hand, if the Nb amount exceeds 0.12%, the panel shapeability such as the spring back and the surface deflection is deteriorated, though the dent-resistance is certainly improved. Naturally, the Nb amount should fall within a range of between 0.02 and 0.12%.
  • the grain boundary is strengthened so as to improve the resistance to the secondary working brittleness.
  • the ferrite grains are diminished so as to ensure an absolute value of the yield strength and, thus, to improve the dent-resistance.
  • the B amount is smaller than 0.0001%.
  • the B amount exceeds 0.002%, the yield point is increased and, thus, the panel shapeability is impaired. It follows that the B amount should fall within a range of between 0.0001 and 0.002%.
  • a ratio of flow stress ⁇ obtained by a tensile test under the condition that a true strain ⁇ is larger than 0.002 and not larger than 0.096, i.e., 0.002 ⁇ ⁇ ⁇ 0.096, to a 0.2% proof stress ⁇ 0.2 , i.e., ⁇ / ⁇ 0.2 , should fall within a range of between exp( ⁇ ) ⁇ (5.29 ⁇ exp( ⁇ ) - 4.19) and exp( ⁇ ) ⁇ (5.64 ⁇ exp( ⁇ ) - 4.49) .
  • the dent-resistance load under the conditions of 2%P0.1, 4%P0.1, 8%P0.1 is as high as 160 to 210N as shown in FIGS. 8 to 10.
  • a steel sheet is shaped into a model panel shown in FIG. 1 with strain of 2%, 4% or 8% imparted to the steel sheet, followed by applying a heat treatment at 170°C for 20 minutes. Then, measured is a load required for imparting a residual displacement of 0.1 mm to the model panel.
  • the spring back ⁇ (measured for a panel having a strain of 2%) is as large as 7 to 11% so as to impair the panel shapeability, if the ratio ⁇ / ⁇ 0.2 is lower than the lower limit noted above. On the other hand, if the ratio ⁇ / ⁇ 0.2 is higher than the upper limit noted above, the spring back ⁇ is as small as 1 to 5%.
  • the dent-resistance is as low as 140 to 165N. In other words, the dent-resistance cannot be improved.
  • a cold-rolled steel sheet and a galvanizing steel sheet excellent in the panel surface properties, the resistance to natural aging and the dent-resistance required for the steel used for an outer panel of a motor car can be obtained by controlling the additive components as described in item (1) above and the tensile characteristics as described in item (2) above.
  • the steel sheet exhibiting the particular properties can be manufactured as follows.
  • steel of the composition given in item (1) above is melted.
  • a converter method is generally employed for melting the steel composition, or an electric furnace method can also be employed.
  • the slab is heated to 1050°C or higher immediately after the casting, or after the slab is once cooled, for applying a hot rolling.
  • the hot rolling is performed under the conditions that the finishing temperature is set at temperature not less than (Ar 3 -100)°C and that the coiling temperature is set at 500°C to 700°C.
  • the finishing temperature is lower than (Ar 3 -100)°C, 2%P0.1, i.e., the dent-resistance load of the panel imparted with 2% of strain) is as low as 140 to 155N, as shown in FIG. 11. In other words, the dent-resistance of the panel cannot be improved. Also, where the coiling temperature is lower than 500°C or higher than 700°C, the value of 2%P0.1 is high, i.e., 156 to 175N.
  • Wca i.e., Arithmetic Average Waviness Height;, measuring length of 25 mm; average of the values measured at 10 optional points around the apex of the panel
  • Wca Arithmetic Average Waviness Height;, measuring length of 25 mm; average of the values measured at 10 optional points around the apex of the panel
  • the hot-rolled steel band is subjected to a pickling, cold-rolling and, then, a continuous annealing.
  • galvanizing is applied after the continuous annealing step.
  • the cold-rolling reduction should desirably be at least 70% in order to improve the deep drawability of the steel sheet.
  • the annealing should desirably be carried out within a recrystallization temperature region of the ferrite phase and not higher than 930°C.
  • the coating employed in the present invention is not limited to galvanizing. Specifically, even if a surface treatment such as coating with zinc phosphate or an electrolytic zinc coating is applied to the steel sheet obtained by the continuous annealing, no problem is brought about in the characteristics of the resultant steel sheet.
  • Molten steel of the composition shown in Table 1 were prepared in a laboratory, followed by continuously casting the steel to prepare a slab having a thickness of 60 mm.
  • Samples Nos. 1 to 7 shown in Table 1 represent the steel of the composition specified in the present invention, with samples Nos. 8 to 15 denoting the steel for Comparative Examples.
  • the slab was treated by a blooming mill to reduce the thickness of the steel sheet to 30 mm, followed by heating the steel sheet at 1050°C for 1.5 hours under the atmosphere for the hot rolling treatment (by roughing mill). After the rough rolling, a finish rolling was applied at 900°C, followed by applying a coiling simulation at 630°C so as to obtain a hot rolled sheet having a thickness of 3 mm.
  • the hot rolled steel sheet was pickled, followed by applying a cold rolling to reduce the thickness of the steel sheet to 0.8 mm and subsequently applying a continuous annealing at 840°C for 90 seconds.
  • a galvanizing was applied at 460°C, followed by applying an alloying treatment at 530°C.
  • 1.0% of temper rolling was applied to the annealed steel sheet or the galvanized steel sheet so as to prepare samples for the experiments. These samples were used for the tensile test (test piece of JIS No.
  • the sample was formed into the model panel shown in FIG. 2 (formed at three levels of the forming strain of 2, 4 and 8%). After a heat treatment was applied at 170°C for 20 minutes, the dent-resistance of the panel and the shapeability of the panel were examined.
  • the dent-resistance was evaluated under a load of P0.1, in which 0.1 mm of residual displacement was imparted to the panel (in the following description, expressions of 2%P0.1, 4%P0.1 and 8%P0.1 are used for denoting the panel imparted with strain of 2, 4 and 8%, respectively).
  • the panel shapeability was evaluated by the spring back amount ⁇ and Wca: Arithmetic Average Waviness Height (JIS B 0610).
  • the spring back amount ⁇ was defined by using a curvature radius R' of the panel imparted with 2% of strain and a curvature radius R of the press mold, i.e., ⁇ was defined by (R'/R-1) ⁇ 100 .
  • ⁇ was not larger than 6%, i.e., ⁇ ⁇ 6%, the evaluation was marked by ⁇ .
  • ⁇ was larger than 10%, i.e., ⁇ > 10%, the evaluation was marked by x.
  • Wca was not larger than 0.2 ⁇ m, i.e., Wca ⁇ 0.2 ⁇ m, the evaluation was marked by ⁇ .
  • Wca was larger than 0.2 ⁇ m but not larger than 0.4 ⁇ m, i.e., 0.2 ⁇ m ⁇ Wca ⁇ 0.4 ⁇ m
  • the evaluation was marked by ⁇ .
  • Wca was larger than 0.4 ⁇ m and not larger than 0.6 ⁇ m, i.e., 0.4 ⁇ m ⁇ Wca ⁇ 0.6 ⁇ m
  • the evaluation was marked by x.
  • Table 2 shows the results of measurements and evaluations.
  • the value of the elongation El was as large as 41.6% to 45.0%.
  • the average r-value, i.e., (r0 + 2r45 + r90)/4 was as large as 1.80 to 2.20.
  • the value of ⁇ YPel was 0% in any of the samples of the present invention.
  • the spring back amount ⁇ and the Waviness Height Wca were small, i.e., 3% to 5% and 0.09 ⁇ m to 0.17 ⁇ m, respectively, supporting a good panel shapeability.
  • the dent-resistance P0.1 of the panel imparted with strains of 2%, 4% and 8% was as high as 158N to 193N.
  • the steel samples Nos. 8 to 15 each having a composition failing to fall within the range specified in the present invention, did not satisfy simultaneously the formability, the shapeability, and the dent-resistance.
  • each of Comparative Samples Nos. 8 and 9 exhibited a 2% BH as high as 33 MPa to 42 MPa and a ⁇ YPel of 0.9% to 2.2%, indicating that these samples were not satisfactory in the resistance to natural aging.
  • the dent-resistance P0.1 under strains of 2% to 8% was found to be 165N to 193N, supporting a high dent-resistance.
  • Comparative steel sample No. 10 was high in the elongation El and the r-value, and low in ⁇ and Wca, supporting that this sample was satisfactory in each of formability and shapeability.
  • the dent-resistance load P0.1 under strains of 2% to 8% was as low as 148 to 172N.
  • Comparative steel sample No. 11 was high in ⁇ 0.2 , which was 265 MPa to 270 MPa, supporting that this sample was satisfactory in dent-resistance.
  • a molten steel having a composition of steel sample No. 2 of the present invention shown in Table 1 was prepared by melting and casting in a laboratory, followed by casting the molten steel to prepare a slab having a thickness of 50 mm.
  • the slab was treated by a blooming mill to reduce the thickness of the steel sheet to 25 mm, followed by heating the steel sheet at 1250°C for 1 hour under the atmosphere and subsequently applying a hot rolling treatment to reduce the thickness of the steel sheet to 2.8 mm.
  • the finishing temperature and the coiling temperature in the hot rolling treatment were changed within ranges of 770°C to 930°C and 450°C to 750°C, respectively.
  • Example 1 The mechanical characteristics and the panel characteristics of the thin steel sheet thus prepared were examined as in Example 1. Table 3 shows the results.
  • the finishing temperature for each of steel samples Nos. 1 to 3 of the present invention was lower than (Ar 3 -100)°C.
  • each of these steel samples exhibited a low P0.1 under strains of 2% to 8%, i.e., 139N to 159N, and a high Wca, i.e., 0.35 ⁇ m to 0.40 ⁇ m, indicating that these steel samples were poor in the dent-resistance and in the shapeability. Further, the r-value for these steel samples was as low as 1.69 to 1.77.
  • the coiling temperature for each of steel samples Nos. 7 and 12 was lower than 500°C. Also, each of these steel samples exhibited a high ⁇ 0.2 value, i.e., 243 MPa and 248 MPa, respectively, supporting a good dent-resistance.
  • the ⁇ value was as high as 8% and the Wca value was as high as 0.30 ⁇ m, indicating that these steel samples were poor in the panel shape.
  • the coiling temperature for each of steel samples Nos. 11, 15 and 18 was higher than 700°C.
  • each of these steel samples exhibited a low ⁇ 0.2 value, i.e., 210 MPa to 216 MPa, and such a low ⁇ value of 2%.
  • the Wca value was as high as 0.42 ⁇ m to 0.43 ⁇ m.
  • the dent-resistance load was low in each of these steel samples.
  • each of steel samples Nos. 4-6, 8-10, 13, 14, 16 and 17, which fell within the scopes specified in the present invention in respect of the finishing temperature and the coiling temperature was found to be satisfactory in each of the formability, the dent-resistance and the shapeability.
  • Molten steel of the composition shown in Table 4 (steel samples Nos. 1 to 15 belonging to Examples of the present invention, with steel samples Nos. 16 to 29 belonging to Comparative Example) were prepared in a laboratory, followed by continuously casting the molten steel to prepare a slab having a thickness of 60 mm.
  • the slab was treated by a blooming mill to reduce the thickness of the steel sheet to 30 mm, followed by heating the steel sheet at 1100°C for 1 hour under the air atmosphere for the hot rolling process (by roughing mill). After the roughing, a finish rolling was applied at 890°C, followed by applying a coiling simulation at 600°C so as to obtain a hot rolled sheet having a thickness of 3 mm.
  • the hot rolled steel sheet was pickled, followed by applying a cold rolling to reduce the thickness of the steel sheet to 0.75 mm and subsequently applying a continuous annealing at 850°C for 90 seconds.
  • a galvanizing was applied at 460°C, followed by applying an alloying treatment at 500°C.
  • 1.0% of temper rolling was applied to the annealed steel sheet or the galvanized steel sheet so as to prepare samples for the experiments. These samples were used for the tensile test (test piece of JIS No.
  • the sample was formed into the model panel shown in FIG. 7 (molded at three levels of the strain of 2, 4 and 8%). After a heat treatment was applied at 170°C for 20 minutes, the dent-resistance of the panel and the shapeability of the panel were examined.
  • the dent-resistance was evaluated under a load of P0.1, in which 0.1 mm of residual displacement was imparted to the panel (in the following description, expressions of 2%P0.1, 4%P0.1 and 8%P0.1 are used for denoting the panel imparted with molding strain of 2, 4 and 8%, respectively).
  • the panel shapeability was evaluated by the spring back amount ⁇ and the Arithmetic Average Waviness Height Wca (JIS B 0610).
  • the spring back amount ⁇ was defined by using a curvature radius R' of the formed panel imparted with 2% of strain and a curvature radius R of the press mold, i.e., ⁇ was defined by (R'/R-1) ⁇ 100 .
  • ⁇ was not larger than 6%, i.e., ⁇ ⁇ 6%, the evaluation was marked by ⁇ .
  • ⁇ was larger than 10%, i.e., ⁇ > 10%, the evaluation was marked by x.
  • the surface waviness height each having a length of 25 mm were measured at optional 10 points in the vicinity of the apex of the panel in accordance with the method specified in JIS B 0610, and the average measured value is denoted by Wca.
  • Wca was not larger than 0.2 ⁇ m, i.e., Wca ⁇ 0.2 ⁇ m, the evaluation was marked by ⁇ .
  • Wca was larger than 0.2 ⁇ m but not larger than 0.4 ⁇ m, i.e., 0.2 ⁇ m ⁇ Wca ⁇ 0.4 ⁇ m
  • the evaluation was marked by ⁇ .
  • Wca was larger than 0.4 ⁇ m and not larger than 0.6 ⁇ m, i.e., 0.4 ⁇ m ⁇ Wca ⁇ 0.6 ⁇ m
  • the evaluation was marked by x.
  • Table 5 shows the results of measurements and evaluations.
  • the value of the 2% BH amount was 0 to 26 MPa and the ⁇ YPel was 0%.
  • the amount of C was 0.0025% and the 2% BH amount was 36 to 38 MPa
  • 2%P0.1, 4%P0.1, 8%0.1 of the steel samples of the present invention was high, i.e., 150 to 180N, 160 to 192N and 175 to 208N, supporting a high dent-resistance of the panel.
  • the steel samples of the present invention were satisfactory in the panel shapeability. Further, concerning ⁇ YPel, the restoring amount of the yield point elongation was measured for the samples (steel sample No. 6 for the present invention and steel sample 18 for Comparative Example) stored for 18 months at 25°C after the temper annealing, with the results as shown in FIG. 12. The value of ⁇ YPel after storage for 18 months for the steel sample No. 6 of the present invention was less than 0.2%, supporting an excellent resistance to natural aging. On the other hand, the value of ⁇ YPel for the steel sample of Comparative Example 18 was 2.2%, supporting a marked deterioration in the resistance to natural aging.
  • Molten steel having compositions of steel samples Nos. 2 and 14 of the present invention shown in Table 4 was prepared by melting and casting in a laboratory, followed by casting the steel to prepare a slab having a thickness of 50 mm.
  • the slab was treated by a blooming mill to reduce the thickness of the steel sheet to 20 mm, followed by heating the steel sheet at 1200°C for 1 hour under the atmosphere and subsequently applying a hot rolling treatment to reduce the thickness of the steel sheet to 2.8 mm.
  • the finishing temperature and the coiling temperature in the hot rolling treatment were changed within ranges of 750°C to 930°C and 440°C to 750°C, respectively.
  • the thin steel sheet thus prepared was shaped into a model panel shown in FIG. 7 with equivalent strains of 2%, 4% and 8%, followed by applying a heat treatment at 170°C for 20 minutes, said heat treatment corresponding to the coating-baking treatment.
  • Table 6 shows the results of evaluation of the dent-resistance of the panel (three levels of 2%, 4% and 8% of strains) and of the shapeability of the panel imparted with 2% of strain.
  • the finishing temperature for samples Nos. 1-3 and 23-26 for Comparative Examples was lower than (Ar 3 -100)°C, which does not fall within the scope defined in the present invention.
  • these samples for Comparative Examples exhibited a 2% to 8%P0.1 of 140N to 158N and 140N to 165N, and Wca values of 0.38 to 0.43 ⁇ m and 0.37 to 0.59 ⁇ m, respectively, resulting in failure to obtain a good dent-resistance of the panel and a good shapeability.
  • the coiling temperature for samples Nos. 13, 19, 22, 30, and 40 for Comparative Examples was higher than 700°C and, thus, each of these samples exhibited an undesirable dent-resistance, i.e., 2 to 8%P0.1 of 145N to 166N. Also, the Wca values were 0.33 to 0.42 ⁇ m, indicating a poor panel shapeability.
  • each of the finishing temperature and the coiling temperature for Nos. 4-7, 9-12, 15-18, 20, 21, 27-29, 32-34, and 36-39 of the present invention fell within the scope defined in the present invention.
  • 2 to 8%P0.1 was 153 to 188N, supporting a good dent-resistance of the panel.
  • the samples of the present invention were also satisfactory in the ⁇ value, i.e., ⁇ ⁇ 5%, and in the Wca value, i.e., Wca ⁇ 0.2 ⁇ m, supporting a good shapeability.
  • the present invention makes it possible to manufacture stably a cold-rolled steel sheet and a galvanized steel sheet satisfying the dent-resistance of a panel, the surface shapeability and resistance to natural aging and having a tensile strength of 340 MPa or more, which are required for steels used for an outer panel of a motor car, by specifying the steel composition, the tensile characteristics and the manufacturing conditions. It follows that the present invention is highly valuable in the steel industries and in the motor car industries.

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EP98944222A 1998-04-27 1998-09-24 Plaque d'acier laminee a froid possedant d'excellentes caracteristiques d'aptitude au moulage et de formabilite en panneaux, une bonne resistance a la constriction, plaque d'acier a placage en zinc moule et procede de fabrication de ces plaques Expired - Lifetime EP1002884B1 (fr)

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EP09150416A EP2172575A1 (fr) 1998-04-27 1998-09-24 Plaque d'acier laminée à froid possédant d'excellentes caractéristiques d'aptitude au moulage et de formabilité en panneaux, une bonne résistance à la constriction, plaque d'acier à placage de zinc moulé et procédé de fabrication de ces plaques

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JP11678898 1998-04-27
JP11678898A JP4177478B2 (ja) 1998-04-27 1998-04-27 成形性、パネル形状性、耐デント性に優れた冷延鋼板、溶融亜鉛めっき鋼板及びそれらの製造方法
PCT/JP1998/004283 WO1999055927A1 (fr) 1998-04-27 1998-09-24 Plaque d'acier laminee a froid possedant d'excellentes caracteristiques d'aptitude au moulage et de formabilite en panneaux, une bonne resistance a la constriction, plaque d'acier a placage en zinc moule et procede de fabrication de ces plaques

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EP98944222A Expired - Lifetime EP1002884B1 (fr) 1998-04-27 1998-09-24 Plaque d'acier laminee a froid possedant d'excellentes caracteristiques d'aptitude au moulage et de formabilite en panneaux, une bonne resistance a la constriction, plaque d'acier a placage en zinc moule et procede de fabrication de ces plaques

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EP1291448A4 (fr) * 2000-05-26 2004-06-30 Jfe Steel Corp Tole d'acier laminee a froid et tole d'acier galvanisee possedant des proprietes de durcissement par ecrouissage et par precipitation et procede de production associe
EP1209244A4 (fr) * 2000-04-24 2005-04-06 Jfe Steel Corp Acier de forme lineaire presentant d'excellentes caracteristiques de fatigue au niveau des joints, et procede de production correspondant
US7067023B2 (en) 2000-05-26 2006-06-27 Jfe Steel Corporation Cold rolled steel sheet and galvanized steel sheet having strain age hardenability and method of producing the same
CN100467651C (zh) * 2003-11-10 2009-03-11 Posco公司 具有抗老化性和极好的可成形性的冷轧薄钢板及其生产方法
EP2312010A1 (fr) * 2000-06-20 2011-04-20 JFE Steel Corporation Feuille d'acier et son procédé de fabrication
KR20190055150A (ko) * 2016-09-20 2019-05-22 티센크루프 스틸 유럽 악티엔게젤샤프트 평탄형 강 제품의 제조 방법 및 평탄형 강 제품
EP4079903A4 (fr) * 2019-12-19 2023-02-22 Posco Tôle d'acier laminée à froid présentant une excellente résistance thermique et une excellente aptitude au moulage et son procédé de fabrication

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JP4513434B2 (ja) * 2004-07-09 2010-07-28 Ｊｆｅスチール株式会社 コイル内材質均一性に優れた高強度冷延鋼板およびその製造方法
KR101042434B1 (ko) * 2007-10-29 2011-06-16 현대제철 주식회사 냉연강판 및 그의 제조방법
JP5056863B2 (ja) * 2010-01-15 2012-10-24 Ｊｆｅスチール株式会社 冷延鋼板およびその製造方法
CA3039083A1 (fr) * 2016-10-17 2018-04-26 Tata Steel Ijmuiden B.V. Substrat en acier pour pieces peintes
DE102017103308A1 (de) * 2017-02-17 2018-08-23 Voestalpine Stahl Gmbh Verfahren zum Herstellen von Stahlblechen
WO2021149810A1 (fr) * 2020-01-24 2021-07-29 日本製鉄株式会社 Panneau
KR102556444B1 (ko) * 2020-12-29 2023-07-18 현대제철 주식회사 우수한 내덴트 특성을 가지는 내덴트성 냉연강판, 내덴트성 도금강판 및 그 제조방법
CN117165845B (zh) * 2023-04-28 2024-04-16 鞍钢股份有限公司 新能源汽车用340MPa级合金化热镀锌板及其制备方法

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EP1209244A4 (fr) * 2000-04-24 2005-04-06 Jfe Steel Corp Acier de forme lineaire presentant d'excellentes caracteristiques de fatigue au niveau des joints, et procede de production correspondant
EP1291448A4 (fr) * 2000-05-26 2004-06-30 Jfe Steel Corp Tole d'acier laminee a froid et tole d'acier galvanisee possedant des proprietes de durcissement par ecrouissage et par precipitation et procede de production associe
EP1498507A1 (fr) * 2000-05-26 2005-01-19 JFE Steel Corporation Tole d'acier laminee a froid, galvanisee ayant excellent aptitude au durcissement au viellissement par ecruissage et son procede de fabrication
US7067023B2 (en) 2000-05-26 2006-06-27 Jfe Steel Corporation Cold rolled steel sheet and galvanized steel sheet having strain age hardenability and method of producing the same
US7101445B2 (en) 2000-05-26 2006-09-05 Jfe Steel Corporation Cold rolled steel sheet and galvanized steel sheet having strain age hardenability and method of producing the same
EP2312010A1 (fr) * 2000-06-20 2011-04-20 JFE Steel Corporation Feuille d'acier et son procédé de fabrication
EP2312009A1 (fr) * 2000-06-20 2011-04-20 JFE Steel Corporation Feuille d'acier et son procédé de fabrication
CN100467651C (zh) * 2003-11-10 2009-03-11 Posco公司 具有抗老化性和极好的可成形性的冷轧薄钢板及其生产方法
KR20190055150A (ko) * 2016-09-20 2019-05-22 티센크루프 스틸 유럽 악티엔게젤샤프트 평탄형 강 제품의 제조 방법 및 평탄형 강 제품
JP2019532172A (ja) * 2016-09-20 2019-11-07 ティッセンクルップ スチール ヨーロッパ アクチェンゲゼルシャフトＴｈｙｓｓｅｎＫｒｕｐｐ Ｓｔｅｅｌ Ｅｕｒｏｐｅ ＡＧ 平鋼製品の製造方法および平鋼製品
US11453923B2 (en) 2016-09-20 2022-09-27 Thyssenkrupp Steel Europe Ag Method for manufacturing flat steel products and flat steel product
EP4079903A4 (fr) * 2019-12-19 2023-02-22 Posco Tôle d'acier laminée à froid présentant une excellente résistance thermique et une excellente aptitude au moulage et son procédé de fabrication
US12584185B2 (en) 2019-12-19 2026-03-24 Posco Cold-rolled steel sheet having excellent thermal-resistance and moldability, and method for manufacturing same

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KR20010014238A (ko) 2001-02-26
CN1261408A (zh) 2000-07-26
EP1002884A4 (fr) 2006-04-05
EP1002884B1 (fr) 2009-02-25
BR9810485A (pt) 2000-09-12
DE69840595D1 (de) 2009-04-09
JPH11310849A (ja) 1999-11-09
KR100345012B1 (ko) 2002-07-20
CN1084797C (zh) 2002-05-15
CN1138016C (zh) 2004-02-11
CN1405352A (zh) 2003-03-26
EP2172575A1 (fr) 2010-04-07
WO1999055927A1 (fr) 1999-11-04
JP4177478B2 (ja) 2008-11-05

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