EP2371978B1 - Stahlblech und oberflächenbehandeltes stahlblech - Google Patents

Stahlblech und oberflächenbehandeltes stahlblech Download PDF

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Publication number
EP2371978B1
EP2371978B1 EP09827543.1A EP09827543A EP2371978B1 EP 2371978 B1 EP2371978 B1 EP 2371978B1 EP 09827543 A EP09827543 A EP 09827543A EP 2371978 B1 EP2371978 B1 EP 2371978B1
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EP
European Patent Office
Prior art keywords
steel sheet
bending
hot
rolling
strength
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Not-in-force
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EP09827543.1A
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English (en)
French (fr)
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EP2371978A4 (de
EP2371978A1 (de
Inventor
Koutarou Hayashi
Hideo Mizukami
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Nippon Steel Corp
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Nippon Steel and Sumitomo Metal Corp
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Publication date
Priority claimed from JP2008295900A external-priority patent/JP5206352B2/ja
Priority claimed from JP2008295899A external-priority patent/JP5206351B2/ja
Priority claimed from JP2008295898A external-priority patent/JP5206350B2/ja
Priority claimed from JP2008295897A external-priority patent/JP5206349B2/ja
Application filed by Nippon Steel and Sumitomo Metal Corp filed Critical Nippon Steel and Sumitomo Metal Corp
Priority to PL09827543T priority Critical patent/PL2371978T3/pl
Publication of EP2371978A1 publication Critical patent/EP2371978A1/de
Publication of EP2371978A4 publication Critical patent/EP2371978A4/de
Application granted granted Critical
Publication of EP2371978B1 publication Critical patent/EP2371978B1/de
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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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • C21D8/0215—Rapid solidification; Thin strip casting
    • 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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties 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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold 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 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
    • C22C38/002—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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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

Definitions

  • This invention relates to a steel sheet and a surface-treated steel sheet. More specifically, the present invention relates to a high-strength steel sheet and surface-treated steel sheet which are suitable as materials for members such as reinforcing members for automobiles or seat components for automobiles.
  • Patent Document 1 discloses a high-strength steel sheet in which the hardness of hard bainitic and martensitic phases is decreased so as to reduce the difference in hardness with respect to the low-hardness ferritic phase surrounding the bainitic phase and the martensitic phase.
  • Patent Documents 2 and Patent Document 3 disclose cold-rolled steel sheets and hot-dip galvanized steel sheets which have both a high strength and satisfactory stretch flange formability for which good local deformability is required as for bending properties.
  • High-strength steel sheets generally contain a large amount of Mn in order to increase strength. Mn tends to segregate in steel. Therefore, the chemical composition of high-strength steel sheets locally varies due to the segregation of Mn.
  • Figure 1 is an explanatory view showing the surface condition after bending deformation of a high-strength steel sheet.
  • Figure 1 if a nonuniform structure is formed in a high-strength steel sheet, marked surface irregularities which can be visually observed develop in the surface of worked portions of the high-strength steel sheet. These irregularities promote nonuniform deformation at the time of bending, thereby inducing the formation of cracks in worked portions and worsening bending properties. Even when cracks do not develop, surface irregularities present in worked portions remain in a member which is manufactured from the high-strength steel sheet and worsen the impact properties of the member.
  • Patent Documents 1 - 3 have a steel composition containing a large amount of Mn and Ni which easily segregate in steel, so for the above-described reasons, there is a concern of a deterioration in the bending properties and impact properties of members formed from the steel sheets.
  • Patent Document 4 discloses a high-strength cold-rolled steel sheet having improved bending properties due to having a martensitic single-phase structure which is an essentially uniform structure.
  • the steel structure is made a martensitic single-phase structure, the flatness of a high-strength steel sheet is worsened, and this makes it difficult to use the sheet as a material for automotive parts requiring high dimensional accuracy.
  • Patent Document 5 discloses a thin steel sheet having an increased hole expansion ratio with an increased strength by employing a matrix with a single-phase ferritic structure.
  • a high-strength cold-rolled steel sheet or a high-strength hot-dip galvanized steel sheet based on the technology disclosed in that document, it is necessary to perform cold rolling and annealing in order to improve the surface roughness and the accuracy of the sheet thickness of a product.
  • the steel composition which is disclosed in that document contains a large amount of carbonitride-forming elements, the steel has an increased recrystallization temperature, and it is necessary to carry out annealing at a high temperature of not lower than the Ac 3 point. Annealing at such a high temperature promotes coarsening of precipitates and makes it impossible to attain a high strength.
  • the grain diameter of the steel becomes nonuniform, and it is not possible to improve bending properties.
  • Patent Document 6 discloses a heat treatment method for steel in which segregation is diffused by performing homogenization in which a steel material is maintained at a high temperature of at least 1250° C for a long period of at least 10 hours.
  • that method cannot completely eliminate segregation.
  • segregation produces a nonuniform structure, and surface irregularities in worked portions are not removed, so bending properties cannot be adequately improved.
  • Patent Document 7 and Patent Document 8 disclose a hot-dip galvanized steel sheet having reduced segregation and excellent hole expendability manufactured by carrying out continuous casting under conditions in which cooling is performed from the liquidus temperature to the solidus temperature such that the average cooling rate is at least 100° C per minute at a depth of 1/4 of the slab thickness ts.
  • this cooling rate can only be achieved with a thin slab having a thickness of 30 - 70 mm, and this technique cannot be applied to continuous casting of a usual slab having a thickness of 200 - 300 mm.
  • the object of the present invention is to provide a steel sheet and a surface-treated steel sheet having a tensile strength of at least 590 MPa and excellent bending properties.
  • excellent bending properties mean that the smallest bending radius for which cracks do not develop in a 180° bending test in which the axis for bending is in the rolling direction is not greater than 1.0t and that surface irregularities cannot be visually observed in a portion which has been bent after 90° V bending with a bending radius of 1.0t in the same bending direction as above. Accordingly, unless otherwise specified, bending properties in this description are evaluated by the above-described properties of a steel sheet and by visual observation of a member manufactured by bending of such a steel sheet.
  • the smallest bending radius in a 180° bending test be not greater than 0.5t and that irregularities be not visually observed in the surface of the bent portion after 90° V bending with a bending radius of 0.5t.
  • the present invention is based on the finding that a desired distribution of the Mn concentration can be achieved by optimizing the chemical composition and the manufacturing conditions of a high-strength steel sheet. As a result, the formation of a nonuniform structure caused by Mn segregation can be suppressed to obtain a uniform structure, whereby a high-strength steel sheet having a tensile strength of at least 590 MPa and excellent bending properties can be manufactured.
  • the present invention is a steel sheet according to claim 1.
  • the above-described chemical composition includes at least one of the following (a) - (d):
  • the present invention is a surface-treated steel sheet characterized by having a plating layer formed on the surface of at least one side of the above-described steel sheet.
  • the present invention can provide a high-strength steel sheet having a strength of at least 590 MPa and excellent bending properties.
  • a steel sheet according to the present invention can be widely used in various industrial fields and particularly in the automotive field.
  • Figure 1 is an explanatory view showing the surface condition after bending deformation.
  • the chemical composition of a steel sheet according to the present invention is as follows.
  • the C contributes to increasing the strength of a steel sheet.
  • the C content is at least 0.03 % in order to make the tensile strength of a steel sheet at least 590 MPa. If the C content exceeds 0.20 %, weldability worsens. Therefore, the C content is 1 made at most 0.20 %.
  • the C content is preferably at least 0.05 % in order to easily obtain a tensile strength of at least 980 MPa.
  • the Si content is at least 0.005 %, it is possible to increase the strength of a steel sheet without significantly degrading bending properties. If the Si content exceeds 2.0 %, the ability of an unplated steel sheet to undergo chemical conversion treatment is degraded, and in the case of a hot-dip galvanized steel sheet, wettability at the time of plating, the ability to undergo alloying treatment, and plating adhesion deteriorate. Therefore, the Si content is at least 0.005 % and at most 2.0 %.
  • the Si content exceeds 1.5 %, Si-containing oxides may be formed on the surface of the steel sheet to such a degree that the surface condition worsens. Therefore, the Si content is preferably at most 1.5 %.
  • a tensile strength of at least 980 MPa can be easily obtained if the Si content is at least 0.4 %. Therefore, the Si content is preferably at least 0.4 %.
  • Mn contributes to increasing the strength of a steel sheet.
  • the Mn content In order to make the tensile strength of a steel sheet at least 590 MPa, it is necessary for the Mn content to be at least 1.2 %. If the Mn content exceeds 3.5 %, it not only becomes difficult to melt and refine steel in a converter, but weldability also worsens. Therefore, the Mn content is at least 1.2 % and at most 3.5 %. Mn promotes the formation of a nonuniform structure in steel, but as stated below, when Bi is contained in the steel, this adverse effect of Mn is alleviated and the structure becomes uniform, so a worsening of bending properties is suppressed and strength is increased. In order to achieve a tensile strength of at least 980 MPa, the Mn content is preferably at least 1.8 %.
  • P is typically contained as an unavoidable impurity.
  • P is a solid solution strengthening element, and it is effective for strengthening a steel sheet, so it may be deliberately contained. Weldability deteriorates if the P content exceeds 0.1 %. Therefore, the P content is at most 0.1 %. In order to strengthen a steel sheet with greater certainty, the P content is at least 0.003 %.
  • S is contained in steel as an unavoidable impurity.
  • the S content is preferably as low as possible from the standpoint of bending properties and weldability. Therefore, the S content is made at most 0.01 %.
  • the S content is preferably at most 0.005 % and more preferably at most 0.003 %.
  • Al is contained in steel for deoxidation of steel. Al is effective for increasing the yield of carbonitride-forming elements such as Ti.
  • the content of sol. Al which is necessary for this effect is at least 0.001 %. If the sol. Al content exceeds 1.0 %, weldability is degraded, and oxide inclusions in the steel increase, leading to a deterioration in the surface condition. Therefore, the sol. Al content is made at least 0.001 % and at most 1.0 %.
  • the sol. Al content is preferably at least 0.01 % and at most 0.2 %.
  • N is contained in steel as an unavoidable impurity. From the standpoint of bending properties, the N content is preferably as low as possible, so it is made at most 0.01 %. The N content is preferably at most 0.006 %.
  • Bi performs an important function in the present invention.
  • Ti, Nb, and V each contribute to increasing the strength of a steel sheet, so they are optional elements which can be contained in steel as necessary. Containing at least one of Ti, Nb, and V in steel is effective for guaranteeing a tensile strength of at least 980 MPa.
  • the content of at least one of Ti, Nb, and V is preferably at least 0.003 %. If the content of any of Ti, Nb, and V exceeds 0.3 %, inclusions containing Ti, Nb, or V increase and the surface condition of the steel sheet deteriorates. Therefore, when at least one of Ti, Nb, and V is contained, the content of each which is added is preferably at most 0.3 %.
  • Cr, Mo, Cu, and Ni each contribute to increasing the strength of a steel sheet, so they are optional elements which can be contained in the steel as necessary. Containing at least one of Cr, Mo and Ni in a steel is effective for guaranteeing a tensile strength of at least 980 MPa when manufacturing a cold-rolled steel sheet such that the temperature at the completion of cooling in continuous annealing is at least 300° C and at most 420° C or when manufacturing a hot-dip galvanized steel sheet. In order to obtain this effect with greater certainty, at least one of Cr, Mo and Ni is preferably contained in an amount of at least 0.01 %.
  • Each of Ca, Mg, REM, and Zr contributes to controlling inclusions in steel and particularly to finely dispersing inclusions, thereby further improving the bending properties of a steel sheet. Therefore, they are optional elements which can be contained in steel as necessary. However, if an excessive amount of Ca, Mg, REM, or Zr is contained, the surface condition of a steel sheet deteriorates. Therefore, when at least one of Ca, Mg, REM, and Zr is contained, the content of each which is added is at most 0.01 %. In order to obtain the above-described effect with certainty, the content of any of Ca, Mg, REM, and Zr which is added is preferably at least 0.0001 %.
  • the B not only contributes to improving the bending properties of a steel sheet, but it is effective at guaranteeing a tensile strength of at least 980 MPa when manufacturing a hot-dip galvanized steel sheet. Therefore, it is an optional element which can be contained in steel as necessary. However, if the B content exceeds 0.01 %, a hot-rolled steel sheet becomes hard, and it becomes difficult to carry out cold rolling on the hot-rolled steel sheet. Therefore, the B content is preferably at most 0.01 %. In order to obtain the above-described effect with greater certainty, the B content, when B is contained, is preferably at least 0.0003 %.
  • the remainder of the composition other than the above-described components is essentially Fe and impurities.
  • a steel sheet according to the present invention has a prescribed Mn distribution. Namely, the Mn distribution of the steel sheet satisfies the condition that the Mn segregation ratio (Mn max /Mn av ) is less than 1.30.
  • the Mn segregation ratio (Mn max /Mn av ) is determined by analysis with an EPMA (electron probe microanalyzer) at a depth of 1/20 of the sheet thickness from the surface of the steel sheet in a region which does not contain MnS.
  • the segregation ratio is calculated as the ratio of the maximum Mn concentration (Mn max ) to the average Mn concentration (Mn av ).
  • a Mn segregation ratio of less than 1.30 indicates that the structure is uniform, as a result of which the bending properties of the steel sheet are improved, and it becomes difficult for surface irregularities to develop in a portion which has undergone bending.
  • the Mn segregation ratio of a steel sheet can be made less than 1.30 by containing Bi in the chemical composition of the steel and, as described below, by satisfying prescribed conditions for the casting speed. In order to further improve bending properties, the Mn segregation ratio is preferably less than 1.20.
  • the bending properties of a steel sheet are affected by the Mn distribution in the surface layer of the steel sheet. Reformation during bending is larger in the surface layer of a steel sheet than in the center of the thickness of the steel sheet, and bending properties are controlled by the deformability in the surface layer of the steel sheet.
  • the Mn concentration is measured at the above-described depth near the surface of the steel sheet to determine the Mn segregation ratio.
  • Analysis by EPMA is preferably performed by measurement in an area sufficient to adequately evaluate local variations in the Mn distribution such as a rectangular region measuring 500 micrometers in the rolling direction by a total of 4 mm in a direction perpendicular to the rolling direction, as shown in the examples.
  • a steel sheet according to the present invention can also be used as a surface-treated steel sheet by forming a plating layer on the surface of one or both sides thereof with the object of increasing corrosion resistance or the like.
  • the plating layer which is formed may be an electroplated layer or a hot-dip plated layer.
  • an electroplated layer are an electroplated zinc layer and an electroplated Zn-Ni alloy layer.
  • a hot-dip plated layer are a hot-dip galvanized (zinc) layer, a galvannealed layer, a hot-dip aluminum plated layer, a hot-dip Zn-Al alloy plated layer, a hot-dip Zn-Al-Mg alloy plated layer, a hot-dip Zn-Al-Mg-Si alloy plated layer, and the like.
  • the coating weight (or thickness) of these plated layers may be that typically used for this type of plated steel sheet. If desired, there may be two or more plated layers.
  • Molten steel having the above-described chemical composition is prepared by a known melting method using a converter, an electric furnace, or the like.
  • the molten steel is contiguously cast to form a slab with a thickness of 200 - 300 mm under conditions such that the rate of solidification at a depth of 10 mm from the slab surface is 100 - 1000° C per minute.
  • Rate of solidification 100 - 1000° C per minute
  • the solidification rate at a depth of 10 mm from the slab surface in the continuous casting step is less than 100° C per minute, the primary dendrite arm spacing at a depth of 1/20 of the slab thickness from the slab surface cannot be refined, and segregation ofMn is not sufficiently prevented. As a result, it is sometimes not possible to improve the bending properties of a steel sheet. A solidification rate exceeding 1000° C per minute may induce surface cracking of the slab. Therefore, the solidification rate is at least 100° C per minute and at most 1000° C per minute.
  • the slab thickness is less than 200 mm, it becomes difficult to guarantee an overall rolling reduction of at least 99.0 % in the below-described hot rolling and cold rolling. If the slab thickness exceeds 300 mm, it becomes difficult to guarantee an Mn segregation ratio of less than 1.30 at a depth of 1/20 of the sheet thickness from the surface of the steel sheet. Therefore, the slab thickness is at least 200 mm and at most 300 mm.
  • a slab obtained by the above-described continuous casting step is subjected to hot rolling to prepare a hot-rolled steel sheet, and then the hot-rolled steel sheet is subjected to cold rolling to obtain a cold-rolled steel sheet.
  • a slab which is obtained by the continuous casting step is subjected to homogenization by holding in a temperature range of 1200 - 1350° C for at least 20 minutes and then to hot rolling with a finishing temperature of 800 - 950° C and a coiling temperature of 400 - 750° C to obtain a hot-rolled steel sheet.
  • the hot-rolled steel sheet is then cold rolled to obtain a cold-rolled steel sheet, with the overall rolling reduction in hot rolling and cold rolling being at least 99.0 %.
  • Homogenization Temperature 1200 - 1350° C, Duration of Homogenization: at least 20 minutes
  • the homogenization temperature is preferably at most 1350° C from the standpoints of suppressing scale loss, preventing damage to the heating furnace, and increasing productivity.
  • the duration of homogenization is more preferably at least 1.0 hours and at most 3 hours.
  • the Mn segregation ratio can be made less than 1.20 and the bending properties of the steel sheet can be further improved.
  • By making the duration of homogenization at most 3 hours scale loss is suppressed and productivity can be increased which leads to a decrease in manufacturing costs.
  • finishing temperature of hot rolling is at least 800° C, the resistance to deformation during hot rolling can be made small and operations can more easily be carried out. If the finishing temperature is at most 950° C, flaws due to scale can be suppressed with greater certainty, and a good surface condition can be guaranteed.
  • the coiling temperature in hot rolling is at least 400° C, the formation of hard bainite or martensite is suppressed, and subsequent cold rolling can be easily carried out.
  • the coiling temperature is at most 750° C, oxidation of the surface of a steel sheet is suppressed and a good surface condition can be guaranteed.
  • a rough bar after rough rolling and before finish rolling is preferably heated by induction heating or the like so as to allow the rough bar to have a uniform temperature over its entire length, whereby variations in the properties of the steel sheet can be suppressed.
  • the hot-rolled steel sheet which is obtained by the above-described hot rolling step usually undergoes descaling by a usual method such as pickling before it is subjected to cold rolling to obtain a cold-rolled steel sheet.
  • the overall rolling reduction in the hot rolling and cold rolling is preferably at least 99.0 %.
  • Mn concentrated bands are ribbon-shaped regions in which Mn segregated portions which developed by segregation during solidification are elongated in the rolling direction in the subsequent rolling step. Decreasing the thickness of these Mn concentrated bands can suppress surface irregularities after working with greater certainty, and as a result, the bending properties of a steel sheet can be improved. For this purpose, it is effective to make the overall reduction at least 99.0 %.
  • the reduction in cold rolling is preferably at least 30 % in order to make the structure of a steel sheet after continuous annealing uniform. It is preferable from the standpoint of guaranteeing the flatness of a steel sheet that light rolling with a reduction of at most 5 % be carried out before or after pickling to rectify the shape. Carrying out this light rolling before pickling improves the processability of pickling so as to promote removal of elements which concentrate at the surface. As a result, adhesion of a plated layer is improved in the case of a hot-dip galvanized sheet or the surface condition is improved in the case of a cold-rolled steel sheet.
  • a cold-rolled steel sheet obtained by the rolling step including the above-described hot rolling and cold rolling undergoes continuous annealing.
  • the annealing temperature is preferably at least 750° C and at most 950° C. From the standpoint of productivity, the rate of temperature increase up to the recrystallization annealing temperature is preferably at least 1° C per second.
  • the annealing temperature at least 750° C, the possibility that an unrecrystallized structure remains is suppressed and a uniform structure can be obtained with certainty, which results in further improvements in bending properties.
  • Making the annealing temperature at most 950° C suppresses damage to the annealing furnace and increases productivity.
  • the annealing time is preferably at least 10 seconds in order to completely remove an unrecrystallized structure and stably guarantee good bending properties. From the standpoint of productivity, the annealing time is preferably at most 300 seconds.
  • cooling after annealing is preferably carried out with an average cooling rate of at least 5° C per second in the region from 650° C to 550° C.
  • Temper rolling is preferably carried out on the steel sheet after annealing (after plating when hot-dip galvanizing has been carried out). Temper rolling can suppress the occurrence of yield elongation and present fouling and galling at the time of press forming.
  • the elongation in temper rolling is preferably at least 0.05 % and at most 1 %.
  • cooling after annealing in the annealing step be stopped at a temperature of at least 460° C and at most 550° C and that the annealed steel sheet be immediately immersed in a hot-dip plating bath to carry out continuous plating. If cooling after annealing is stopped at a temperature lower than 460° C, there is a large amount of heat dissipation at the time of immersion in the plating bath, as a result of which plating operation sometimes becomes difficult. If it is stopped at a temperature exceeding 550° C, plating operation sometimes becomes difficult.
  • Hot-dip galvanizing can be carried out by usual methods.
  • a steel sheet can be immersed in a hot-dip galvanizing bath at a temperature of at least 410° C and at most 490° C, and the coating weight of plating can be controlled with a gas swiping nozzle or the like immediately alter the steel sheet leaves the plating bath.
  • Alloying heat treatment to manufactured a galvannealed steel sheet may be carried out on the resulting galvanized steel sheet after immersion in the hot-dip galvanizing bath.
  • a preferable temperature for alloying heat treatment is at least 460° C and at most 600° C. If this temperature is less than 460° C, portions which have not undergone alloying may develop and it becomes easy for the surface condition of the steel sheet to deteriorate. If the temperature for alloying heat treatment exceeds 600° C, powdering of the plating easily develops.
  • conventional post-treatment such as chemical conversion treatment, lubricating treatment, or the like may be performed on the resulting plated steel sheet.
  • the slabs were subjected to hot rolling under the conditions shown in Table 2 followed by pickling and then cold rolling under the conditions shown in Table 2 to obtain cold-rolled steel sheets with a thickness of 1.2 mm.
  • Test specimens for heat treatment were taken from the resulting cold-rolled steel sheets, and as shown in Table 3, the test specimens underwent heat treatment corresponding to the heat pattern in a continuous annealing apparatus or a hot-dip galvanizing apparatus.
  • Table 3 Tell steel No. Continuous annealing step Heat treatment simulating continuous annealing equipment (cold rolled steel sheet) Heat treatment simulating hot dip galvanized equipment (hot dip galvanized steel sheet) Elongation in temper rolling (%) Heating rate (°C/min) Annealing temp. (°C) Annealing time (s) Slow cooling (°C/s) Temp. at start of rapid cooling (°C) Cooling rate (°C/s) Stopping temp. (°C) Holding temp.
  • Cooling time (s) Cooling rate after holding (°C/s) Stopping temp. (°C) Holding temp. Holding time (s) Immersion temp. (°C) Alloying temp. (°C) Cooling rate after heating (°C) 1 10 880 60 None 25 400 400 250 10 2 10 860 60 None 20 400 400 250 10 0.1 3 10 860 60 None 20 500 500 20 460 500 10 0.1 4 10 860 60 None 20 400 400 250 10 0.1 5 10 900 60 None 25 280 280 250 10 0.1 6 10 860 60 None 25 320 320 250 10 0.1 7 10 860 60 None 20 350 350 250 10 0.1 8 10 860 60 None 20 500 500 20 460 500 10 0.1 9 10 860 60 None 20 350 350 250 10 0.1 10 10 860 60 None 25 280 280 250 10 0.1 11 10 880 60 None 20 280 280 250 10 0.1 12 10 840 60 None 20 360 360 250 10 0.1 13 10 840 60 None 20 500 500 20 460 500 10 0.1 14 10 860 60 None 20 250 250
  • the Mn distribution in the resulting cold-rolled steel sheets for testing obtained under various manufacturing conditions was analyzed using an EPMA.
  • a tensile test and a bending test in which the axis for bending was the rolling direction were performed on the cold-rolled steel sheets for testing to evaluate mechanical properties.
  • a sample for analysis was prepared from each cold-rolled steel sheet for testing by grinding and buffing the rolled surface of the steel sheet so as to expose a surface to be analyzed located at a depth of 1/20 of the sheet thickness from the rolled surface, and the Mn distribution was examined using an EPMA.
  • a region which did not include MnS was selected, and using a beam diameter of 10 micrometers, the Mn concentration distribution was analyzed in an area which measured 500 micrometers in the rolling direction and a total of 4 mm in the direction perpendicular to the rolling direction and which was divided into sections with a width of 500 micrometers each in the direction perpendicular to the rolling direction by finding the average Mn concentration of each section.
  • the Mn segregation ratio (Mn max /Mn av ) was calculated from the average Mn concentration (Mn av ) and the maximum Mn concentration (Mn max ).
  • a JIS No. 5 tensile test piece was taken from each cold-rolled steel sheet for testing in a direction perpendicular to the rolling direction and the tensile strength (TS) was measured.
  • a bending test piece (40 mm wide x 100 mm long x 1.2 mm thick) in which the lengthwise direction was in the direction perpendicular to the rolling direction was taken from each cold-rolled steel sheet for testing so that the axis about which bending took place coincided with the rolling direction.
  • the test piece was subjected to a 180° bending test with a steel sheet having a thickness of 2.4 mm being disposed on the inside of the bend (to make a bend with a radius of 1.0t), and it was visually ascertained whether cracking occurred.
  • Cold-rolled steel sheets which did not undergo cracking were subjected to a 180° bending test with a steel sheet having a thickness of 1.2 mm being disposed on the inside of the bend (to make a bend with a radius of 0.5t) using a test piece which was taken in the same manner as described above, and visual observation for the occurrence of cracking was performed in the same manner.
  • Cold-rolled steel sheets which did not undergo cracking in this test were subjected to a 180° bending test without disposing a steel sheet on the inside of the bend (a bending test with intimate contact and a bending radius of 0t), and it was ascertained in the same manner whether cracking took place.
  • the bending radius expressed as a function of the sheet thickness (t) was found by dividing the sheet thickness of the steel sheet disposed on the inside of the bend by two times the thickness of the bending test piece (2.4 mm), and the smallest bending radius (R min shown in Table 4) for the cases in which cracking was not ascertained after the test was determined.
  • R min the smallest bending radius
  • a bending test piece (40 mm wide x 60 mm long x 1.2 mm thick) in which the lengthwise direction was in the direction perpendicular to the rolling direction was taken from each cold-rolled steel sheet for testing from each cold-rolled steel sheet for which the minimum bending radius in the above-described bending test was at most 1.0t so that the axis for bending coincided with the rolling direction.
  • Each test piece was subjected to a 90° V bending test by pressing a 90° punch having a radius of 1.2 mm at its end (to make a bend with a radius of 1.0t) against the test piece, and it was visually ascertained whether there were irregularities in the surface. The surface condition was evaluated as poor for samples having surface irregularities and good for samples with no surface irregularities.
  • Test steels Nos. 1 - 3, 7, 8, 10 - 17, 20 - 27, 29 - 31, 35 - 40, and 42 in Table 4 are examples of the present invention which satisfy all the conditions of the present invention.
  • test steels Nos. 4 and 18 had a solidification rate at a depth of 10 mm from the surface in the continuous annealing step which was below the lower limit prescribed by the present invention, so the Mn segregation ratio was greater than 1.30, and bending properties were poor or the surface condition after bending deformation was poor.
  • Test steels Nos. 6, 19, and 41 did not contain Bi, so the Mn segregation ratio was greater than 1.30, and bending properties were poor or the surface condition after bending deformation was poor.
  • Test steels Nos. 5, 9, 28, and 32 had a C content or an Mn content which was below the lower limit prescribed by the present invention, so a desired tensile strength was not obtained.
  • the steel sheets of the examples according to the present invention all had a tensile strength of at least 590 MPa, and the bending properties and the surface condition after bending deformation were good.
  • the Bi content was in the above-described preferred range of at least 0.0010 % to at most 0.05 %
  • the homogenization temperature and the duration of homogenization were in the above-described preferred ranges of at least 1200° C to at most 1350° C and at least 1.0 hours to at most 3 hours, respectively, and the Mn segregation ratio was less than 1.20, so the tensile strength was at least 590 MPa and the bending properties were further improved.

Claims (6)

  1. Stahlblech, dadurch gekennzeichnet, dass es eine chemische Zusammensetzung hat bestehend aus C, Si, Mn, P, S, sol. Al, N, Bi, Ti, Nb, V, Cr, Mo, Ni, Ca, Mg, REM, Zr und B, mit dem Gehalt in Masseprozent C: 0,03 - 0,20%, Si: 0,005 - 2,0%, Mn: 1,2 - 3,5%, P ist wenigstens 0,003% und P ≤ 0,1%, S: ≤ 0,01%, sol. Al: 0,001 - 1,0%, N: ≤ 0,01%, Bi: 0,0001 - 0,05%, Ti: 0 - 0,3%, Nb: 0 - 0,3%, V: 0 - 0,3%, Cr: 0 - 1%, Mo: 0 - 1%, Ni: 0 - 1%, Ca: 0 - 0,01%, Mg: 0 - 0,01%, REM: 0 - 0,01%, Zr: 0 - 0,01% und B: 0 - 0,01%, wobei es sich bei dem Rest um Fe und Verunreinigungen handelt, und dadurch, dass das Mn-Segregationsverhältnis (Mnmax/Mnav), das durch die mittlere Mn-Konzentration (Mnav) und die maximale Mn-Konzentration (Mnmax) bei einer Tiefe von 1/20 der Blechdicke von der Oberfläche des Stahlblechs berechnet wird, weniger als 1,30 beträgt.
  2. Stahlblech nach Anspruch 1, wobei die chemische Zusammensetzung, in Masseprozent, mindestens eines von Ti: 0,003 - 0,3%, Nb: 0,003 - 0,3% und V: 0,003 - 0,3% enthält.
  3. Stahlblech nach Anspruch 1 oder Anspruch 2, wobei die chemische Zusammensetzung, in Masseprozent, mindestens eines von Cr: 0,01 - 1%, Mo: 0,01 - 1 % und Ni: 0,01 - 1% enthält.
  4. Stahlblech nach einem der Ansprüche 1-3, wobei die chemische Zusammensetzung, in Masseprozent, mindestens eines von Ca: 0,0001 - 0,01%, Mg: 0,0001 - 0,01%, REM: 0,0001 - 0,01% und Zr: 0,0001 - 0,01% enthält.
  5. Stahlblech nach einem der Ansprüche 1-4, wobei die chemische Zusammensetzung, in Masseprozent, B: 0,0003 - 0,01% enthält.
  6. Oberflächenbehandeltes Stahlblech, dadurch gekennzeichnet, dass es eine auf der Oberfläche von mindestens einer Seite eines Stahlblechs nach einem der Ansprüche 1-5 gebildete Plattierungsschicht aufweist.
EP09827543.1A 2008-11-19 2009-11-17 Stahlblech und oberflächenbehandeltes stahlblech Not-in-force EP2371978B1 (de)

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JP2008295900A JP5206352B2 (ja) 2008-11-19 2008-11-19 鋼板およびその製造方法
JP2008295899A JP5206351B2 (ja) 2008-11-19 2008-11-19 鋼板およびその製造方法
JP2008295898A JP5206350B2 (ja) 2008-11-19 2008-11-19 溶融亜鉛めっき鋼板およびその製造方法
JP2008295897A JP5206349B2 (ja) 2008-11-19 2008-11-19 鋼板および表面処理鋼板ならびにそれらの製造方法
PCT/JP2009/069464 WO2010058762A1 (ja) 2008-11-19 2009-11-17 鋼板および表面処理鋼板ならびにそれらの製造方法

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JP5533629B2 (ja) * 2010-12-17 2014-06-25 新日鐵住金株式会社 高強度鋼板用の連続鋳造鋳片およびその連続鋳造方法、ならびに高強度鋼板
ES2437715B1 (es) * 2012-07-10 2014-10-24 Gerdau Investigación Y Desarrollo Europa, S.A. Procedimiento para la fabricación de acero
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MX2016007802A (es) 2013-12-27 2016-09-07 Nippon Steel & Sumitomo Metal Corp Miembro de hoja de acero prensado en caliente, metodo de manufactura del mismo, y hoja de acero para prensado en caliente.
WO2015102050A1 (ja) 2014-01-06 2015-07-09 新日鐵住金株式会社 鋼材およびその製造方法
EP3170912B1 (de) 2014-07-18 2019-05-29 Nippon Steel & Sumitomo Metal Corporation Stahlprodukt und verfahren zur herstellung davon
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KR101304009B1 (ko) 2013-09-04
PL2371978T3 (pl) 2018-09-28
EP2371978A4 (de) 2016-05-04
ES2672070T3 (es) 2018-06-12
EP2371978A1 (de) 2011-10-05
CN102282280A (zh) 2011-12-14
CN102282280B (zh) 2015-01-07
WO2010058762A1 (ja) 2010-05-27
KR20110084545A (ko) 2011-07-25

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