• 专利附录
  • 专利说明
  • 权利要求
  • 类似技术
  • 同族专利
  • 引用文献
  • 法律状态
  • 优先权
    • 专利摘要:
    steel sheet and steel sheet production method. The present invention relates to a steel sheet, including: as chemical components, by weight%, 0.05% to 0.35% c; 0.05% to 2.0% of itself; 0.8% to 3.0 mn; 0.01% s; equal to or less than 0.01% of n; and the balance including iron and unavoidable impurities, where an area ratio equal to or greater than 50% of the total ferrite phase, bainite phase, and temperate martensite phase is contained, an area ratio equal to or greater than 3%. % of a retained austenite phase is contained, and crystal grains of the retained austenite phase having a ratio number greater than or equal to 50% satisfy expression 1, assuming that the carbon concentration at a center of gravity position is cgc and The carbon concentration at the grain edge is cgb.
    公开号:BR112012018697B1
    申请号:R112012018697-3
    申请日:2011-01-31
    公开日:2018-11-21
    发明作者:Riki Okamoto；Natsuko Sugiura；Kohichi Sano；Chisato Wakabayashi；Naoki Yoshinaga；Kaoru Kawasaki
    申请人:Nippon Steel & Sumitomo Metal Corporation；
    IPC主号:
    专利说明:

    Report of the Invention Patent for "STEEL PLATE AND METHOD OF PRODUCTION OF STEEL PLATE".
    Technical Field The present invention relates to a steel plate and a method of producing the steel plate. Sheet steel is a high strength sheet steel that is suitable for vehicle structural material or the like used primarily for press work and has excellent elongation, V-folding capability and increased press forming stability.
    Priority is claimed over Japanese Patent Application No. 2010-019193, filed January 29, 2010, and Japanese Patent Application No. 2010-032667, filed February 17, 2010, the contents of which are incorporated herein by reference. Background Art Excellent elongation and V-bending in addition to high strength are required in a steel plate used in the body structure of a vehicle.
    It is known that a TRIP (transformation induced plasticity) steel plate containing a retained austenite phase has high strength and high elongation due to the TRIP effect.
    [005] In Patent Document 1, for the purpose of also increasing the elongation of retained austenite steel, a technique of ensuring a high fraction of a retained austenite is described thereby controlling two types of ferrite phases (bainitic ferrite and polygonal ferrite phase). ).
    [006] In Patent Document 2, for the purpose of ensuring elongation and shape-holding capability, the technique of specifying the shape of an austenite phase as an aspect ratio is described.
    [007] In Patent Document 3, for the purpose of also increasing elongation, the technique of optimizing the distribution of an austenite phase is described.
    In addition, in Patent Documents 4 and 5, the technique of increasing local ductility by uniformity of structure is described.
    Related Art Documents Patent Documents [009] Patent Document 1 Unexamined Japanese Patent Application, First Publication No. 2006-274418 [0010] Patent Document 2 Unexamined Japanese Patent Application, First Publication No. 2007-154283 [ Patent Document 3 Unexamined Japanese Patent Application, First Publication No. 2008-56993 [0012] Patent Document 4 Unexamined Japanese Patent Application, First Publication No. 2003-306746 [0013] Patent Document 5 Unexamined Japanese Patent, First Publication No. H04-88125 Non-Patent Document [0015] Non-Patent Document 1 M. Takahashi: IS3-2007, (2007), 47-50.
    Description of the Invention Technical Problem Retained austenite steel is a steel in which a retained austenite phase is contained in a steel structure by increasing the austenite C concentration through the control of ferrite transformation and the transformation of austenite. bainite during annealing. However, retained austenite steel has a mixed structure and thus may not have a high V-bending capacity (local bending capacity). Therefore, in the above-mentioned technique, obtaining both the greater elongation and the V-bending capacity required by a current high strength steel plate is not achieved.
    In addition, the TRIP effect is temperature dependent, and in actual pressing forming, the temperature of a mold changes during pressing forming. Therefore, in a case where a TRIP sheet steel is subjected to pressing forming, defects such as fractures may occur at an early stage of pressing forming at, for example, 25 ° C, and at a later stage of forming by pressing. pressing at, for example, about 150 ° C, and thus there is the problem with stability in pressing forming.
    Therefore, in addition to the high elongation and V-folding capability, achieving excellent stability in pressing forming without relying on temperature change during pressing forming is an objective in practice.
    An object of the present invention is to provide a steel sheet having high elongation and V-bending capability compared to those of the relative technique and also having excellent press forming stability, and a method of production thereof.
    Means for Solving the Problem The present invention employs the following measures to fulfill the above objective.
    According to a first aspect of the present invention, a steel plate is provided including, as chemical components, m% by weight, 0.05% to 0.35% C; 0.05% to 2.0% Si; 0.8% to 3.0% Mn; 0.01% to 2.0% Al; 0.1% or less of P; 0.05% or less of S; 0.01% or less of N; and the balance including iron and unavoidable impurities, where the steel plate containing by area 50% or more of the total ferrite phase, the bainite phase and the martenite phase, containing by area 3 % or more of the total retained austenite, and 50% or more of the retained austenite phase grains satisfy Expression 1, assuming that the carbon concentration at a center of gravity position is CGC and the carbon concentration at the grain boundary is Cgb.
    Cgb / Cgc> 1,2 (Expression 1) [0022] The steel plate described in item (1) may also include in the chemical components, by weight%, at least one element from: 0,01% to 0, 5% Mo; 0.005% to 0.1% Nb; 0.005% to 0.2% Ti; 0.005% to 0.5% V; 0.05% to 5.0% Cr; 0.05% to 5.0% W; 0.0005% to 0.05% Ca; 0.0005% to 0.05% Mg; 0.0005% to 0.05% Zr; 0.0005% to 0.05% REM; 0.02% to 2.0% Cu; 0.02% to 1.0% Ni; 0.0003% to 0.007% of B.
    In the steel plate described in item (1), the average grain size of the crystal grains may be equal to or less than 10 Pm, and the average carbon concentration in the retained austenite phase may be equal to or greater than 0.7% and less than or equal to 1.5%.
    In the steel plate described in item (1), 40% or more of the crystal grains may be small diameter grains having an average grain size equal to or greater than 1 Lim and equal to or less than 2 Pm, and 20% or more of the crystal grains may be large diameter crystal grains having an average grain size of 2 µm or greater.
    In the steel plate described in item (4), 50% or more of the small diameter crystal grains can satisfy Expression 2, assuming that the carbon concentration at the center of gravity position is CgcS and the carbon concentration grain boundary is CgbS, and 50% or more of large diameter crystal grains can satisfy Expression 3, assuming that the carbon concentration at the center of gravity position is CgcL and the carbon concentration at the grain boundary is CgbL .
    CgbS / CgcS> 1.3 (Expression 2) 1.3> CgbL / CgcL> 1.1 (Expression 3) [0026] The steel plate described in any of (1) to (5) may have a galvanized film supplied. on at least one surface.
    The steel plate described in any of items (1) to (5) may have a galvanized film provided on at least one surface.
    According to a second aspect of the present invention, there is provided a method of producing a steel sheet, including a hot rolling process of producing a hot rolled steel sheet by performing hot rolling of a plate having the chemical components described in (1) and (2) at a finishing temperature of 850 ° C or greater and 970 ° C or lower; an air cooling process of performing an air cooling on the hot-rolled steel plate for a time of 1 second or greater and less than or equal to 10 seconds, a cooling process for cooling the hot-rolled steel plate hot air-cooled to a temperature range equal to or less than 650 ° C at a cooling rate equal to or greater than 10 ° C / s and equal to or less than 200 ° C / s and subsequently coil the steel sheet in a temperature range equal to or less than 650 ° C; a cold rolling process of stripping the hot rolled coil steel sheet at a rolling reduction ratio equal to or greater than 40% and then cold rolling the steel sheet, thereby producing a hot rolled steel sheet. cold, an annealing process of annealing the cold-rolled steel sheet at a maximum temperature of 700 ° C or greater and less than 900 ° C; a retention process for cooling the cold-rolled annealed steel sheet in a temperature range of 350 ° C or greater and 480 ° C or lower at an average cooling rate of or greater than 0,1 ° C / s equal to or less than 200 ° C / s, and keep the steel plate in this temperature range for a time equal to or greater than 1 second and equal to or less than 1000 seconds; and a final cooling process of primarily cooling cold rolled steel sheet over a temperature range of 350 ° C to 220 ° C at an average cooling rate of 5 ° C / s or less than 25 ° C / s , and secondarily cool the steel sheet in a temperature range of 120 ° C to about room temperature at an average cooling rate of 100 ° C / s or greater or less than 5 ° C / s.
    In the steel plate production method described in item (8), the rolling can be performed with an amount of stress equal to or less than 20% in each of the two final passes of the hot rolling process.
    In the steel plate production method described in item (8), the plate which is reheated to 1100 ° C or more after being cooled to 1100 ° C or less can be used in the hot rolling process.
    The method of producing a steel plate described in item (8) may also include an immersion process of dipping the steel plate into a hot dip galvanizing bath after the retention process.
    The steel plate production method described in item (11) may also include an alloy forming process for performing an alloy forming process in a range equal to or greater than 500 ° C and equal to or less than 580 ° C after the soaking process. Advantageous Effects of the Invention According to the measures described above, the concentration gradient of C in the retained austenite phase is suitably controlled so that an extremely stable retained austenite phase can be obtained. As a result, due to the TRIP effect of retained austenite, extremely high elongation and high V-folding capability may be displayed despite the high strength. In addition, where the quantities of small diameter crystal grains and large diameter crystal grains are adequately controlled, the stability of the retained austenite TRIP function may be dispersed. Therefore, excellent stability in pressing forming that does not depend on a temperature change during pressing forming can be exhibited. In addition, in a case where the C concentration gradient of the small diameter crystal grains and the C concentration gradient of the large diameter crystal grains are adequately controlled, superior pressing conformation stability may be exhibited.
    BRIEF DESCRIPTION OF THE DRAWINGS Figure 1 is a diagram showing the relationship between tensile strength and elongation at 25 ° C of steel sheets according to Examples and Comparative Examples.
    [0035] Figure 2 is a diagram showing the relationship between tensile strength and minimum V-bending radius (V-bending capacity) of steel sheets as per Examples and Comparative Examples.
    Figure 3 is a diagram showing the relationship between tensile strength and elongation at 150 ° C according to Examples and Comparative Examples.
    Description of Configurations The inventors have found that in order to make the retained austenite's TRIP effect act not only on stretching but also on the V-folding capability, it is effective to increase the stability of a retained austenite phase to an equal degree. or greater than the current, and to make the TRIP effect to act over a wide range of press forming temperatures, it is effective to uniformly disperse the retained austenite phases with different stability.
    However, in a technique of increasing the C concentration in the retained austenite phases using bainitic transformation of the retained austenite steel according to the related technique, the C concentration may not be increased to a T0 concentration or greater described in Non-Patent Document 1 and the stability of the retained austenite phase may not be increased.
    Here, as a result of the inventors' intensive examination, it has been found that an extremely stable retained austenite phase can be obtained by properly controlling the gradient of C concentration in the retained austenite phase, and the austenite phases with different stability can be uniformly. dispersed by adequately controlling the grain size distribution of the aus-tenite grains in the retained austenite phase.
    Hereinafter, a steel plate will be described in detail in accordance with an embodiment of the present invention made on the basis of the discovery described above.
    Initially, in relation to steel according to this configuration and a plate (ingot plate) which is its raw material, the chemical components of the steel will be described. Here "%" represents the quantity of each element in% by mass. (Basic Elements) The chemical components of steel contain C, Si, Mn and Al as basic elements. (C: 0.05 to 0.35%) [0043] C is an extremely important element for increasing steel strength and ensuring retained austenite phase. When the C content is less than 0,05%. Sufficient resistance may not be guaranteed, and sufficient retained austenite phase may not be obtained. On the other hand, when the C content exceeds 0.35%, the ductility or spot welding capability is significantly deteriorated. In consideration of the characteristics described above, the C content may be specified as a narrower range.
    Therefore, with respect to the C content, its lower limit is specified as 0.05%, preferably 0.08%, more preferably 0.15%, and its upper limit is specified as 0.35%, preferably 0.26%, and more preferably 0.22%. (Si: 0.05 to 2.0%) [0045] Si is an important element in terms of ensuring strength. In a case where the Si content is equal to or greater than 0.05%, the effect of contributing to the generation of the retained austenite phase and ensuring ductility is obtained. On the other hand, in a case where the Si content exceeds 2.0%, such an effect is saturated and, moreover, the brittleness of the steel is more likely to occur. In a case where hot dip galvanizing and chemical conversion treatments need to be facilitated, their upper limit should be specified as 1.8%. In consideration of the characteristics described above, the Si content may be specified as a narrower range.
    Therefore, with respect to Si content, its lower limit is specified as 0.05%, preferably 0.1%, and more preferably 0.5%, and its upper limit is specified as 2.0%. preferably 1.8%, and more preferably 1.6%. (Mn: 0.8 to 3.0%) [0047] Mn is an important element in terms of ensuring strength. In a case where the Mn content is equal to or greater than 0.8%, the effect of contributing to retained austenite phase generation and ensuring ductility is obtained. On the other hand, in a case where the Mn content exceeds 3.0%, the hardening capacity is increased, the retained austenite phase is transformed into a martensite phase, and thus an excessive increase in strength is more likely to be caused. . As a result, products vary significantly and ductility becomes insufficient. In consideration of the characteristics described above, the Mn content may be specified in a narrower range.
    Therefore, with respect to the Mn content, its lower limit is specified as 0.8%, preferably 0.9%, and more preferably 1.2%, and its upper limit is specified as 3.0%. preferably 2.8%, and more preferably 2.6%. (Al: 0.01 to 2.0%) In a case where the Al content is equal to or greater than 0.01%, as with Si, the effect of contributing to the generation of retained austenite phase and ensure ductility. On the other hand, in a case where the Al content exceeds 2.0%, such an effect is saturated, and the steel becomes brittle. In consideration of the characteristics described above, Si content may be specified as a narrower range.
    Therefore, in relation to the Al content, its lower limit is specified as 0.01%, preferably 0.015%, and more preferably greater than 0.04%, and its upper limit is specified as 2.0%. preferably 1.8%, and more preferably less than 1.4%.
    In a case where hot dip galvanizing is performed, Al deteriorates the hot dip galvanizing properties, so it is preferable that its upper limit be 1.8%. In a case where a large amount of the above mentioned Si and Al having the same effect is added to the steel, the Si + Al content may be specified.
    In this case, in relation to the Si + Al content, its lower limit is specified as 0.8%, preferably 0.9%, and more preferably greater than 1.0%, and its upper limit. is specified as 4.0%, preferably 3.0%, and more preferably 2.0%. (Limited Elements) In the steel described above, the contents of P, S and N, which are limited elements, are limited as follows. (P: equal to or less than 0.1%) The P content is limited depending on the strength required of the steel sheet. When P content exceeds 0.1%, local ductility is deteriorated due to segregation in grain boundaries, and weldability is deteriorated. Therefore, the P content is limited to be equal to or less than 0.1%.
    P is inevitably contained in steel, and thus its lower limit exceeds 0%. However, an excessive cost is incurred to limit the P content to be extremely low. Therefore, your lower limit can be specified as 0.001% or 0.006%. In consideration of the characteristics described above, the P content may be specified as a narrower range.
    Therefore, the P content is limited to be equal to or less than 0.1%, preferably equal to or less than 0.05%, and more preferably equal to or less than 0.01%. In addition, your lower limit can be specified as greater than 0%, 0.001%, or 0.006%. (S: equal to or less than 0.05%) [0058] S is an element that generates MnS and thus deteriorates local ductility and weldability. Therefore, the S content is limited to equal to or less than 0.05%.
    S is inevitably contained in steel, and thus its lower limit exceeds 0%. However, an excessive cost is incurred to limit the S content to be extremely low. Therefore, your lower limit can be specified as 0.0005% or greater than 0.001%.
    In consideration of the characteristics described above, the S content may be specified as a narrower range.
    Therefore, the content of S is limited to being equal to or less than 0.05%, preferably equal to or less than 0.01%, and more preferably less than 0.004%. In addition, your lower limit can be specified as greater than 0%, 0.0005%, or greater than 0.001%. (N: equal to or less than 0.01%) When a large amount of N is contained, aging characteristics are deteriorated, the amount of AlN precipitation is increased, and thus the effect of the addition of Al is reduced. Therefore, the N content is limited to equal to or less than 0.01%.
    N is inevitably contained in steel, and thus its lower limit is specified as greater than 0%. However, an excessive cost is incurred to limit the N content to be extremely low, and thus its lower limit may be specified as 0.001% or greater than 0.002%, E, considering the characteristics described above, the N content may be be specified as a narrower range.
    Therefore, the N content is limited to be equal to or less than 0.01%, preferably equal to or less than 0.008%, and more preferably less than 0.005%. In addition, your lower limit can be specified as greater than 0%, 0.001%, or greater than 0.002%. (Fe and the inevitable impurities) The steel described above contains iron and the inevitable impurities as a balance. As unavoidable impurities, there are Sn, As, and built-in scrap scrapers. In addition, other elements may be contained in a range that does not disrupt the features of the present invention. (Selective Elements) The steel described above may contain at least one element between Mo, Nb, Ti, V, Cr, W, Ca, Mg, Zr, REM, Cu, Ni, and B as selective elements. (Mo: 0.01 to 0.5%) In a case where the Mo content is equal to or greater than 0.01%, the effect of suppressing the generation of a perlite phase in the steel is obtained. Therefore, Mo is an element that is important in a case where the cooling rate is slow during annealing or in a case where reheating is performed due to an alloying or similar coating process. However, in a case where the Mo content exceeds 0.5%, the ductility or chemical conversion treatment properties may be impaired. To obtain the balance between higher strength and ductility, it is preferable that the Mo content is equal to or less than 0.3%. In consideration of the characteristics described above, the Mo content may be specified as a narrower range.
    Therefore, in a case where Mo is contained in steel, its lower limit may be specified as 0.01%, and preferably 0.02%, and its upper limit may be specified as 0.5%, preferably 0.3%, and more preferably 0.2%. (Nb: 0.005 to 0.1%) (Ti: 0.005 to 0.2%) (V: 0.005 to 0.5%) (Cr: 0.05 to 5.0%) (W: 0.05 to 5 , 0%) [0068] Nb, Ti, V, Cr, and W are elements that generate carbides, nitrides or fine carbides, and are effective in ensuring strength. In terms of resistance, the lower limit of Nb may be specified as 0.005%, the lower limit of Ti may be specified as 0.005%, the lower limit of V may be specified as 0.005% and the lower limit of Cr may be specified as 0.05%, and the lower limit of W can be specified as 0.05%.
    On the other hand, when such elements are excessively added to steel, the strength of the steel is excessively increased and thus the ductility is degraded. In terms of ensuring ductility, the upper limit and Nb can be specified with 0.1%, the upper limit of Ti can be specified as 0.2%, the upper limit of V can be specified as 0.5%. , the upper limit of Cr can be specified as 5.0%, and the upper limit of W can be specified as 5.0%.
    In addition, in consideration of the characteristics described above the content of each of the elements may be specified as a narrower range.
    Therefore, in a case where Nb is contained in steel, its lower limit may be specified as 0.005%, and preferably 0.01%, and its upper limit may be specified as 0.1%, preferably 0. 0.05%, and more preferably 0.03%.
    In addition, in a case where Ti is contained in steel, its lower limit may be specified as 0.005%, and preferably 0.01%, and its upper limit may be specified as 0.2%, preferably 0.1%, and more preferably 0.07%.
    In addition, in a case where V is contained in steel, its lower limit may be specified as 0.005%, and preferably 0.01%, and its upper limit may be specified as 0.5%, preferably 0.3%, and more preferably 0.1%.
    In addition, in a case where Cr is contained in steel, its lower limit may be specified as 0.05%, and preferably 0.1%, and its upper limit may be specified as 5.0%, preferably 3.0%, and more preferably 1.0%.
    In addition, in a case where W is contained in steel, its lower limit may be specified as 0.05%, and preferably 0.1%, and its upper limit may be specified as 5.0. %, preferably 3.0%, and more preferably 1.0%. (Ca: 0.0005 at 0.05%) (Mg: 0.0005 at 0.05%) (Zr: 0.0005 at 0.05%) (REM: 0.0005 At 0.05%) [0076] Ca, Mg, Zr, and REM (rare earth elements) control the shapes of sulphides and oxides and increase local ductility and pipe expansion capacity. Therefore, the lower limit of each element can be specified as 0.0005%.
    On the other hand, in a case where steel excessively contains these elements, the working capacity is deteriorated. Therefore, the upper limit of each element can be specified as 0.05%.
    In addition, in consideration of the characteristics described above, the content of each of the elements may be specified in a narrower range.
    Therefore, in a case where Ca is contained in steel, its lower limit may be specified as 0.0005%, and preferably 0.001%, and its upper limit may be specified as 0.05%, preferably 0, 01%, and more preferably 0.005%.
    In addition, in a case where Mg is contained in steel, its lower limit may be specified as 0.0005%, and preferably 0.001%, and its upper limit may be specified as 0.05%, preferably 0.01%, and more preferably 0.005%.
    In addition, in a case where Zr is contained in steel, its lower limit may be specified as 0.0005%, and preferably 0.001%, and its upper limit may be specified as 0.05%, preferably 0.01%, and more preferably 0.005%.
    In addition, in a case where REM is contained in steel, its lower limit may be specified as 0.0005%, and preferably 0.001% and its upper limit may be specified as 0.05%, preferably 0, 01%, and more preferably 0.005%. (Cu: 0.02 to 2.0%) (Ni: 0.02 to 1.0%) (B: 0.0003 to 0.007%) Cu, Ni, and B can have a reducing effect on transformation speed and increase the strength of steel. Therefore, the lower limit of Cu can be specified as 0.02%, the lower limit of Ni can be specified as 0.02%, and the lower limit of B can be specified as 0.0003%.
    On the other hand, when each of the elements is excessively added, the hardening capacity is excessively increased, the ferrite transformation and the bainite transformation have their velocities reduced, and thus the concentration of C in the retained austenite phase. decreases. Therefore, the upper limit of Cu can be specified as 2.0%, the upper limit of Ni can be specified as 1.0%, and the upper limit of B can be specified as 0.007%.
    In addition, in consideration of the characteristics described above, the content of each of the elements may be specified as a narrower range.
    Therefore, in a case where Cu is contained in steel, its lower limit may be specified as 0.02%, and preferably 0.04% and its upper limit may be specified as 2.0%, preferably 1. , 5%, and more preferably 1.0%.
    In addition, in a case where Ni is contained in steel, its lower limit may be specified as 0.02%, and preferably 0.04%, and its upper limit may be specified as 1.0%. preferably 0.7%, and more preferably 0.5%.
    In addition, in a case where B is contained in steel, its lower limit may be specified as 0.0003%, and preferably 0.0005%, and its upper limit may be specified as 0.007%, preferably 0.005%, and more preferably 0.003%.
    The following describes the steel structure of the steel plate according to this configuration. Here "%" relative to the steel structure means an area ratio unless otherwise stated.
    The steel structure of the steel plate according to this configuration contains 50% or more, preferably 60%, and more preferably 70% or more of the total of a ferrite phase, a bainite phase, and a relative tempered martensite phase. the whole structure in terms of area ratio. In addition, the steel structure contains 3% or more, preferably more than 5%, and more preferably more than 10% of a retained austenite phase relative to the entire structure. The hardened martensite phase may be contained depending on the required strength of the steel plate, and 0% of it may be contained. In addition, when 5% or less of the perlite phase is contained, the perlite phase does not significantly deteriorate the material quality although it is contained in the steel structure, and thus the perlite phase may be contained within a range of 5% or less. .
    In a case where less than 50% of the total ferrite phase, bainite phase and tempered martensite phase are contained, the concentration of C in the retained austenite phase may not be increased, and thus it is difficult to guarantee the stability of the phases although the austenitic phase has a concentration gradient. Therefore, the V-folding capacity is deteriorated. On the other hand, when more than 95% of the total ferrite phase, bainite phase, and temperate martensite are contained, it is difficult to guarantee 3% or more of the retained austenite phase, resulting in elongation degradation. Therefore, 95% or less is preferable.
    In steel sheet according to this configuration, the C concentration distribution of the retained austenite phase crystal grains is adequately controlled. That is, the concentration of C (Cgb) at a phase interface in which the retained austenite phase crystal grains bound the ferrite phase, the bainite phase or the tempered martensite phase is controlled to be greater than the C (Cgc) concentration. ) at a position of the center of gravity of the crystal grains. Consequently, the stability of the austenite phase retained at the phase interface is increased, and thus excellent elongation and V-folding capability can be exhibited.
    More specifically, in a case where the retained austenite phase crystal grains having a number ratio of 50% or more, preferably 55% or more, and more preferably 60% or more satisfy Expression 1 below, an effect of increasing the stability of the entire retained austenite phase is obtained.
    Cgb / Cgc> 1.2 (Expression 1) [0094] Cgb and Cgc (and CgbS, CgcS, CgbL, and CgcL described later) can be measured by any measurement method while the measurement method ensures accuracy. For example, they can be obtained by measuring the C concentration at a peak of 0.5 Lim or month using an EPMA with attached FE-SEM.
    Here, the concentration of C (Cgb) at a phase interface is referred to as concentration of C at a measurement point that is closest to the grain boundaries of the crystal grain side. However, depending on the measurement conditions, there may be cases where Cgb is measured to be low due to an effect external to the crystal grains. In this case, the highest C concentration in the vicinity of grain boundaries is referred to as Cgb.
    Measurement of local C concentration in an interface is impossible in current technology. However, as a result of intensive examinations by the inventors, it has been determined that a sufficient effect is obtained when the condition of Expression 1 is met during the typical measurement.
    The average grain size of the crystal grains of the retained auspicious phase may be equal to or less than 10 µm, preferably 4 µm, and more preferably equal to or less than 2 µm. The "grain size" mentioned here means an average equivalent circle diameter, and the "average grain size" means its average number. When the average grain size exceeds 10 Pm, the dispersion of the retained austenite phase is brutalized, and thus the TRIP effect may not be sufficiently displayed. Therefore, excellent stretching may not be obtained. In addition, in a case where the average grain size of the retained austenite phase crystal grains is less than 1 Pm, it is difficult to obtain a phase interface having a predetermined C concentration gradient and excellent V-folding capability. not be obtained.
    An average carbon concentration in the retained austenite phase contributes significantly to the stability of retained austenite, such as the C concentration gradient. When the average concentration of C is less than 0.7%, the stability of retained austenite is extremely reduced, the TRIP effect may not be effectively achieved, and thus the stretching is degraded. On the other hand, when the average C concentration exceeds 1.5%, the elongation-enhancing effect is saturated, and thus the cost of production is increased. Therefore, with respect to the average carbon concentration in the retained austenite phase, its upper limit may be specified as 0.7%, preferably 0.8%, and more preferably 0.9% its lower limit may be specified as 1, 5%, preferably 1.4%, and more preferably 1.3%.
    In steel sheet according to this configuration, the retained austenite phases with different stability can be uniformly dispersed by the appropriate grain size distribution of the retained austenite crystal grains. In this case, the high stability retained austenitic phase contributes to the press forming capability in an initial press forming step at, for example, about 25 ° C, and the low stability retained austenitic phase contributes for the press forming capacity in a later step of pressing forming at, for example, about 150 ° C. Therefore, in addition to the high elongation and excellent V-folding capability, excellent press forming stability can also be presented.
    [00100] To ensure stability of the press forming, the retained austenite phase crystal grains need to be dispersed so that the TRIP effect is always displayed even though the mold temperature is changed during continuous pressing. Here, in the steel plate according to this configuration, it is possible to achieve excellent press forming capability which does not depend on the mold temperature by uniform dispersion of the retained austenite crystal grains having different stability.
    Specifically, it is preferred that the austenite phase crystal grains retained in the steel plate have 40% or more of the small diameter crystal grains and grain size equal to or greater than 1 Pm and less than 2 Pm, and 20% or more of large diameter crystal grains and grain size of 2 Pm or greater. In this case, austenite grains having different stabilities are uniformly arranged, and thus excellent press forming stability can be realized.
    Grains (crystal grains with extremely small diameters) having sizes of less than 0.5 Lim provide an extremely difficult C concentration gradient, become crystal grains of an extremely unstable retained austenite phase, and thus have a low contribution to the press forming capacity. Grains having a size equal to or greater than 0.5 Lim and less than 2 Lim (small diameter crystal grains) provide the possibility of maintaining a high concentration gradient in a shaped product because a large amount of carbon is incorporated from adjacent grains. . If 40% or more of the small diameter crystal grains are present, this effect can be exhibited. Grains having a size equal to or greater than 2 Lim (large diameter crystal grains) become retained austenite phase crystal grains having a relatively low stability in which the amount of carbon incorporated from the adjacent grains is small and the temperature gradient is small. Thus, the retained austenite phase is likely to cause the TRIP effect in a low pressing range. If the large diameter crystal grains are present in a ratio of 20% or more, this effect can be exhibited.
    In addition, in steel plate as per this configuration, a suitable C concentration gradient may be provided for each size of the retained austenite phase crystal grains. More specifically, it is preferable that 50%, preferably 55%, and more preferably 60% or more of the small diameter crystal grains satisfy Expression 2 assuming that the carbon concentration at a center of gravity position is CgcS and that the carbon concentration at a grain boundary position is CgbS, and 50% or more, preferably 55%, and more preferably 60% or more of the large diameter crystal grains satisfy Expression 3 assuming that the carbon concentration at one position of center of gravity is CgcL and the carbon concentration at the grain boundary position is CgbL.
    CgbS / CgcS> 1.3 (Expression 2) 1.3> CgbL / CgcL> 1.1 (Expression 3) [00104] As described above, providing an appropriate C concentration gradient for each phase crystal grain size retained austenite, a stable and high press forming capacity may be presented in a relatively low temperature state at, for example, about 25 ° C in a relatively high temperature state, for example, about 150 ° C.
    When 50% or more of small diameter crystal grains having a CgbS / CgcS value greater than 1.3 relative to total small diameter crystal grains, small diameter crystal grains have high stability, and thus the elongation at a low temperature state in an initial pressing forming step can be increased. On the other hand, such stable retained austenite has degraded elongation at a high temperature state at a later stage of pressing forming. To compensate for this, when 50% or more of the large diameter crystal grains having a CgbL / CgcL value of more than 1.1 and less than 1.3 in relation to the total large diameter crystal grains the Large diameter crystals have low stability, which is effective for improving elongation in the high temperature state at a later stage of pressing.
    Here, when the value of CgbL / CgcL is less than 1.1, the crystal grain acts on elongation at a higher temperature, resulting in deterioration of elongation at 150 ° C or less.
    When such a concentration ratio is guaranteed, a high press forming capacity can be guaranteed in a range from a low temperature to a high temperature. However, to ensure this effect for the entire structure, 50%, preferably 55%, and more preferably 60% of the small diameter crystal grains satisfying Expression 2 relative to the total small diameter crystal grains are required. When the percentage is less than the above value, its TRIP effect is low, and thus the low temperature forming capacity is deteriorated. On the other hand, when large diameter crystal grains satisfy Expression 3, the press forming capacity can be obtained in a high temperature region. Even for large diameter crystal grains, to ensure this effect for the entire structure, 50%, preferably 55%, and more preferably 60% of the large diameter grain sizes that satisfy Expression 3 for all grains of Crystal are required.
    The steel plate according to this configuration may have a galvanized film or a galvanized film on a minus surface.
    Hereinafter a method of producing a steel plate according to the embodiment of the present invention will be described.
    [00110] In the embodiment of the present invention, at least one hot rolling process, an air cooling process, a winding process, a cold rolling process, an annealing process, a retention process, and a process final cooling are included. Hereafter each process will be described in detail. . (Hot Rolling Process) [00111] In the hot rolling process, hot rolling is performed on a casting plate (plate) immediately after continuous casting or a reheated plate to 1100 ° C or more after being cooled to 1100 ° C or less, thereby producing a hot-rolled steel sheet. In a case where reheated slab is used, the homogenization treatment is insufficiently performed at a reheat temperature of less than 1100 ° C, and thus the strength and V-bending capacity are degraded. A higher finishing temperature in the hot rolling process is more preferable in terms of recrystallization and growth of austenite grains and thus is adjusted to be equal to or greater than 850 ° C and equal to or less than 970 ° C. When the hot rolling finish temperature is less than 850 ° C, the double phase lamination range (ferrit-austenite) is caused, resulting in ductility degradation. On the other hand, when the hot rolling finish temperature exceeds 970 ° C, the austenite grains become crude, the fraction of the ferrite phase is reduced, and thus the ductility is degraded.
    In the case where the C concentration gradient of the crystal grains in the retained austenite phase is uniformly dispersed, a lower amount of lamination reduction is more preferable to the two final passes (one step before the final step and the final step). ) during lamination, and thus the amount of lamination reduction at each step can be adjusted to be equal to or less than 20%. In addition, the lamination reduction ratio for a final pass (final pass) may be set to be less than or equal to 15% or less than or equal to 10%. Accordingly, the crystal grain sizes of the retained austenite phase may be dispersed, so that the stability of the press forming of the steel plate may be increased. When the amount of lamination reduction in each step exceeds 20%, recrystallization of austenite grains proceeds, and thus it becomes difficult to obtain crystal grains having a grain size (equivalent circle diameter) of equal to or greater than 2 Lim. final structure. (Air cooling process) [00113] In the air cooling process, cooling (air cooling) is performed on the hot rolled steel sheet obtained as described above for a time equal to or greater than 1 second and equal to or shorter than 10 seconds. When the air cooling time is shorter than 1 second, recrystallization and growth of austenite grains is insufficient, and thus crystal grains in the retained austenite phase of the final structure are reduced. On the other hand, when the air cooling time exceeds 10 seconds, the austenite grains become crude, uniformity is eliminated and thus elongation is deteriorated. The air cooling time is adjusted to preferably 5 seconds or less, and more preferably 3 seconds or less. (Winding Process) [00114] In the winding process, after the air-cooled hot-rolled steel plate is cooled to an average cooling rate of 10 ° C or greater or less than 200 ° C / s up to a temperature range of less than or equal to 650 ° C, the resultant is wound in a temperature range of or less than 650 ° C, preferably equal to or less than 600 ° C, and more preferably equal to at or below 400 ° C. When the average cooling rate is less than 10 ° C / s or the winding temperature exceeds 650 ° C, the perlite phase that deteriorates the V-folding capacity is generated. When the average cooling rate exceeds 200 ° C /s. The effect of suppressing the perlite is saturated, and variations in the temperature of the cooling end point become significant. Therefore, it is difficult to guarantee a stable material.
    Therefore, with respect to the average cooling rate, its lower limit is set to 10 ° C / s, preferably 30 ° C / s. and more preferably 40 ° C / s, and its upper limit is set to 200 ° C / s, preferably 150 ° C / s, and more preferably 120 ° C / s. In addition, with respect to the winding temperature, its lower limit is set to 600 ° C or 550 ° C. (Cold rolling process) [00116] In cold rolling process, the hot rolled coil is stripped, and then the resulting cold rolled at a rolling reduction ratio of 40% or more. thus producing a cold rolled steel sheet. At a lamination reduction ratio of less than 40%, recrystallization or reverse transformation during annealing is suppressed, resulting in elongation degradation. Here the upper limit of rolling reduction is not particularly specified and can be 90% or 70%. (Annealing Process) In the annealing process, annealing is performed on cold rolled steel sheet at a maximum temperature equal to or greater than 700 ° C and equal to or less than 900 ° C. When the maximum temperature is below 700 ° C, recrystallization of a ferrite phase during annealing slows, resulting in degradation of elongation. When the maximum temperature exceeds 900 ° C, the martensite fraction is increased, resulting in elongation degradation.
    Therefore, with respect to the maximum annealing temperature, its lower limit is set to 700 ° C, preferably 720 ° C, and more preferably 750 ° C, and its upper limit is set to 900 ° C, preferably 880 ° C. C, and more preferably less than 850 ° C.
    After the annealing process, for the purpose of suppressing the yield limit elongation, skin-pass lamination can be performed by about 1%. (Retention Process) [00120] In order to perform an aging treatment (hereinafter referred to as OA), in the retention process, the annealed cold rolled steel plate is cooled to a temperature range equal to or greater than 250 ° C and equal to or less than 480C at an average cooling rate equal to or greater than 0.1C / s and equal to or less than 200 ° C / s, and is maintained at that temperature for a time equal to or greater than 1 second and equal to or less than 1000 seconds. During cooling after annealing, to secure the structure and efficiently cause bainite transformation, the average cooling rate is set to be equal to or greater than 0.1C / s and equal to or less than 200 ° C / s. When the average cooling rate is less than 0.1 ° C / s, the transformation cannot be controlled. On the other hand, when the average cooling rate exceeds 200 ° C / s, the effect is saturated, and the ability to control the temperature of the cooling endpoint that is most important for generating retained austenite is significantly deteriorated. Therefore, with respect to the average cooling rate, its lower limit is set to 0.1 ° C / s, preferably 2 ° C / s, and more preferably 3 ° C / s, and its upper limit is set to 200 ° C / s. ° C / s, preferably 150 ° C / s, more preferably 120 ° C / s. Cooling endpoint temperature and subsequent retention are important for controlling bainite generation and determining the retained austenite C concentration. When the temperature of the cooling endpoint is below 350 ° C, a large amount of martensite is generated, and thus the strength of the steel is excessively increased. Also, it is difficult to make austenite be retained. Therefore, the degradation of stretching is greatly increased. When the temperature of the cooling endpoint exceeds 480 ° C, bainite transformation slows down and, in addition, the generation of cementite occurs during maintenance, degrading the increase in C concentration in retained austenite. Therefore, with respect to the cooling end point temperature and the holding temperature, its lower limit is set to 350 ° C, preferably 380 ° C, and more preferably 390C, and its upper limit is set to 480C, preferably 470 ° C, and more preferably 460 ° C.
    The retention time is set to be equal to or greater than 1 second and equal to or less than 1000 seconds. When the retention time is shorter than 1 second, insufficient bainite transformation occurs, and the increase in C concentration in retained austenite is insufficient. When the retention time exceeds 1000 seconds, cementite is generated in the austenite phase, and thus the reduction in C concentration is likely to occur. Therefore, with respect to retention time its lower limit is set to 1 second, preferably 10 seconds, and more preferably 40 seconds, and its upper limit is set to 1000 seconds, preferably 600 seconds, and more preferably 400 seconds. (Final Cooling Process) [00123] In the final cooling process, the cold rolled steel plate after retention is initially cooled over a temperature range of 350 ° C to 220 ° C at an average cooling rate equal to or greater than 5C / s and equal to or less than 25 ° C / s, and then cooled within a temperature range of 120 ° C to near room temperature at an average cooling rate equal to or greater than 100 ° C / s s or equal to or less than 5 ° C / s.
    A weak transformation that occurs during cooling after OA plays an important role in increasing the C concentration in the vicinity of grain boundaries in austenite. Therefore, the steel plate is cooled over a temperature range of 350 ° C to 220 ° C at an average cooling rate equal to or greater than 5 ° C / s and less than 25 ° C / s. When the cooling rate in the temperature range of 350 ° C to 220 ° C exceeds 25 ° C / s, transformation does not proceed, and the increase in C concentration in austenite does not occur. On the other hand, when the cooling rate in the temperature range of 350 ° C to 220 ° C / s is less than 5 ° C / s, the diffusion of C in the austenite continues and thus the concentration gradient of C is reduced. Therefore, with respect to the average cooling rate during primary cooling, its lower limit is set to 5 ° C / s, preferably 6 ° C / s, and more preferably 7 ° C / s, and its limit higher is set to 20 ° C / s, preferably 19 ° C / s, and more preferably 18 ° C / s.
    In addition, in a low temperature range equal to or lower than 120 ° C, diffusion of C is also restricted, and transformation is not likely to occur. Therefore, during secondary cooling, the steel plate is cooled at a temperature range of 120 ° C to near room temperature at an average cooling rate equal to or greater than 100 ° C / s, and a concentration gradient of C in the austenite phase from 350 ° C to 220 ° C is reached. On the other hand, during secondary cooling, the steel plate is cooled in a temperature range of 120 ° C to near room temperature at an average cooling rate of 5 ° C / s or less in order to do so. that the concentration gradient of C in the austenite phase becomes more significant. When the average cooling rate is greater than 5 ° C / s, and less than 100 ° C / s during secondary cooling, the transformation does not occur, and the concentration of C in the grain boundaries decreases.
    Therefore, the average cooling rate during secondary cooling is set to be equal to or less than 5 ° C / s, preferably 4 ° C / s, and more preferably 3 ° C / s or is adjusted to be equal to at or greater than 100 ° C / s, preferably 120 ° C / s, and more preferably 150 ° C / s.
    According to the method of producing a steel sheet according to this configuration described above, by controlling the cooling condition after the concentration of C in the retained austenite phase is increased by bainite transformation, it is possible to control the gradient of C concentration of the edge portion of the grains. In addition, by increasing the concentration of C in the auscultite phase during cooling after annealing, it is possible to increase the stability of the retained austenite phase.
    In addition, in a case where the C concentration gradient of the retained austenite phase is uniformly dispersed by the dispersion of the crystal grain sizes of the retained austenite phase, the press forming stability of the steel sheet may be increased. .
    [00130] This technique can be applied to the production of hot dip galvanized steel sheet. In this case, after the retention process described above, the steel plate is immersed in a hot dip galvanizing bath prior to the final cooling process. In addition, an alloying process can be added after dipping. The alloying process is performed within a temperature range of 500 ° C and 580 ° C or greater. At a temperature of less than 500 ° C, insufficient bonding occurs, and at a temperature greater than 580 ° C, superlinking occurs, and thus the corrosion resistance is significantly deteriorated.
    In addition, the present invention is not influenced by the casting conditions. For example, the influence of the casting method (continuous casting or conventional casting) and the difference in plate thickness is small, and a special casting such as thin plate and a hot rolling method can be used. In addition, electroplating can be performed on the steel plate.
    Examples The present invention will also be described on the basis of Examples. Example conditions are exemplary conditions that are employed to confirm the configurability and effects of the present invention, and the present invention is not limited to the example conditions. The present invention may employ various conditions without departing from the concept of the present invention provided that the object of the present invention is achieved.
    Initially, the ingot slabs A to V (steel components of the Examples) were produced having the chemical compositions shown in Table 1 and the ingot slabs to g (steel components of the Comparative Examples).
    Table 1 Hot rolled steel sheets were produced by performing hot rolling on these ingot plates. During hot rolling, the rolling reduction ratios in the sixth and seventh rolling stages corresponding to the two final passes and the finishing temperature were as shown in Table 2. Thereafter, the hot rolled steel plate that was subjected to cooling air for a predetermined time was cooled to about 550 ° C at an average cooling rate of 60C / s, and then coiled to about 540 ° C. The hot rolled coil sheet was stripped, and was then cold rolled at a 50% rolling reduction ratio, thereby producing a cold rolled sheet. In addition, an annealing treatment was performed at the maximum annealing temperature shown in Table 2. After re-cooking, with the purpose of suppressing yield limit elongation, skin-pass lamination hurts by about of 1%.
    Subsequently, to perform a medium treatment, the steel plate after annealing was cooled and maintained. The cooling rate, retention temperature, and retention time here are shown in Table 2. In addition, for some steel sheets, the steel sheets after retention were dipped into a hot dip galvanizing bath. hot, and were subjected to an alloying process at a given binding temperature.
    Finally, initial cooling (cooling at a range of 350 ° C to 220 ° C) and secondary cooling (cooling at a range of 120 ° C to 20 ° C) were performed on the cold rolled steel sheet. cold at a predetermined cooling rate, thus producing steel plates A1 to V1 and a1 to g1.
    Table 2 [00138] The steel structures of the steel sheets obtained as described above and the characteristics of the steel plate are shown in Tables 3 and 4. For steel structures, "ferrite + bainite + tempered martensite ratio" were measured. "," retained austenite ratio "," ratio of crystal grains meeting Expression (1) "," small diameter crystal grain ratio "," large diameter crystal grain ratio "," grain ratio diameter crystal beads satisfying the expression (2) "," proportion of large diameter crystal grains satisfying Expression (3) "," average crystal grain size ", and" average C concentration in the austenite phase retained ". In addition, in relation to the characteristics of the steel plate, "tensile strength", elongation at 25 ° C "," V-bending capacity "and" elongation at 150 ° C "were evaluated.
    Table 3 Table 4 [00139] For observing the identification of the structure and the positions and measurements of an average grain size (mean equivalent circle diameter) and occupancy ratio, the cross section in the rolling direction of a steel sheet or The cross-section perpendicular to the rolling direction was corroded by a Ni-tal reagent for quantification by observation using an optical microscope at 500x to 1000x magnification.
    Measurement of the "retained austenite phase ratio" was performed on a surface that was chemically polished to 1/4 of the thickness from the steel sheet surface layer, and the retained austenite was quantified and obtained from the integrated intensities. of the ferrite planes (200) and (211) and the integrated intensities of the MoKa monochromic ray austenite planes (200), (220) and (311).
    In addition, the "average concentration of C in the retained austenite phase" (Cy) was calculated by the following Expression A by obtaining a lattice constant (unit: Angstrom) from the reflection angles of the plane (200), from the plane (220) and the plane (311) of the austenite by radius analysis using Cu-Ka rays.
    Cy = (lattice constant-3,572) / 0,033 (Expression A) "Stretching at 25 ° C" and "Stretching at 150 ° C" were evaluated at temperatures of 25 ° C and 150 ° C by stretching in the C-direction of a specimen from JIS # 5.
    "V-folding capability" was evaluated by a minimum R at which no fracture occurred during the V-folding test. In the V-folding test, a 30 mm x 200 mm specimen was 90 degrees using V blocks having several R. The distance between the supports was 95 mm, and a bending pressing force (BHF) on the supports was 98 kN. Fracture determination was performed by visual observation or observation using a magnifying lens, and those with fractures or constrictions on the surface were determined as fracture. Among the aag steels of Table 1, steel a did not meet the upper limit of C that is specified by the present invention, and steel b did not meet the lower limit of C. Steels c, d and did not meet the upper limits of S, Si, and Mn, respectively. Steel f did not meet the lower limits of Si and Al. Steel g did not satisfy the lower limit of Si and the upper limit of Al.
    Sheet steel A3 and sheet steel A4 are sheet steel produced by adjusting the rolling reduction ratios at the two final passes to be high.
    [00145] Steel plate D3 is a steel plate produced by adjusting the maximum temperature during annealing to be low. [00146] Steel plate D4 is a steel plate produced by adjusting the final primary cooling speed to be high.
    [00147] Steel plate E3 is a steel plate produced by setting the final secondary cooling speed to 50 ° C / s. Steel plate F3 is a steel plate produced by adjusting the retention temperature to be low.
    [00149] Steel plate F4 is a steel cover produced by setting the retention temperature to be high.
    [00150] H3 sheet steel is a sheet steel produced by adjusting the retention time to be long.
    [00151] H4 steel sheet is a steel sheet produced by adjusting the final primary cooling speed to be low. [00152] Sheet steel J2 is a sheet steel produced by adjusting the air cooling time to be long.
    [00153] M2 steel sheet is a steel sheet produced by adjusting the air cooling time to be short.
    In steel plate a1, the ferrite + bainite fraction is out of range, and in steel plate b1, the austenite fraction is equal to or less than the range. Sheet steel e1 has a low average concentration of C in austenite. Steel plate f1 and steel plate g1 cannot guarantee austenite fractions.
    Figure 1 is a diagram showing the relationship between tensile strength and elongation at 25 ° C of steel sheets according to the Examples and Comparative Examples, and Figure 2 is a diagram showing the relationship between tensile strength tensile strength and V-folding capability relative to the same steel sheets. From figures 1 and 2, it can be seen that both high elongation and V-bending ability are obtained according to the steel plate and the method of production of the steel plate according to the present invention.
    In addition, Figure 3 is a diagram showing the relationship between tensile strength and elongation at 150 ° C according to the Examples and Comparative Examples. From Figures 1 and 3, it can be seen that a high elongation is performed at both temperatures of 25 ° C and 150 ° C according to the steel sheet and the method of production of the steel sheet according to the present invention.
    Industrial Applicability According to the present invention, the present invention can provide a steel sheet having greater elongation and V-bending ability compared to that according to the relative technique and, moreover, having excellent stability in press forming, and to a production method thereof.
    权利要求:
    Claims (8)
    [1]
    1. Sheet steel, characterized in that it consists of: as a chemical component, by mass%, 0,05% to 0,35% C; 0.05% to 2.0% Si; 0.8% to 3.0% Mn; 0.01% to 2.0% Al; equal to or less than 0.1% P; equal to or less than 0.05% S; equal to or less than 0.01% N; and optionally at least one of: 0.01% to 0.5% Mo; 0.005% to 0.1% Nb; 0.005% to 0.2% Ti; 0.005% to 0.5% V; 0.05% to 5.0% Cr; 0.05% to 5.0% W; 0.0005% to 0.05% Ca; 0.0005% to 0.05% Mg; 0.0005% to 0.05% Zr; 0.0005% to 0.05% REM; 0.02% to 2.0% Cu; 0.02% to 1.0% Ni; and 0.0003% to 0.007% B; and the balance including iron and unavoidable impurities, where: the steel plate comprises, by area, 3% or more of a retained austenite phase and 50% or more of a total ferrite phase, a bainite phase, and a tempered martensite phase, and 50% or more of the retained austenite phase crystal grains satisfy Expression 1, where Cgc represents a carbon concentration at a center of gravity, and Cgb represents a carbon concentration at the grain boundary: Cgb / Cgc> 1.2 (Expression 1), and where 40% or more of the crystal grains are small diameter crystal grains having an average grain size greater than or equal to 1 Lim and less than 2 Pm, 20 % or more of crystal grains are large diameter crystal grains having an average grain size greater than or equal to 2 Pm, 50% or more of small diameter crystal grains satisfy Expression 2, and 50% or more of large diameter crystal grains satisfy Expression 3, where: CgcS represents a small particle carbon concentration at a center of gravity, and CgbS represents a small particle carbon concentration at the grain boundary, and CgcL represents a large particle carbon concentration at a center of gravity, and CgbL represents a concentration of Large particle carbon at grain boundary: CgbS / CgcS> 1.3 (Expression 2), 1.3> CgbL / CgcL> 1.1 (Expression 3).
    [2]
    Steel plate according to claim 1, characterized in that the average grain size of the crystal grains is equal to or less than 10 µm, and the average carbon concentration in the retained austenite phase is equal to or greater than 0.7% and equal to or less than 1.5%.
    [3]
    Steel plate according to claim 1 or 2, characterized in that the steel plate has a galvanized film supplied to at least one surface.
    [4]
    Steel plate according to claim 1 or 2, characterized in that the steel plate has a galvanized annealed film provided to at least one surface.
    [5]
    A method of producing a sheet steel, characterized in that it comprises: a hot rolling process of producing a hot rolled steel sheet by performing hot rolling on a plate having the chemical components as defined. claim 1 at a finishing temperature of greater than or equal to 850 ° C and equal to or lower than 970 ° C; an air cooling process of performing air cooling on the hot-rolled steel plate for a time equal to or greater than 1 second and equal to or less than 10 seconds; a process of cooling the air-cooled hot-rolled steel sheet to a temperature range equal to or less than 650 ° C at a cooling rate equal to or greater than 10 ° C / s or less than 200 ° C / if subsequently coil the steel sheet in a temperature range equal to or less than 650 ° C; a cold rolling process of stripping the hot rolled coil at a rolling reduction ratio equal to or greater than 40% and then cold rolling the steel sheet thereby producing a cold rolled steel sheet cold; an annealing process for annealing the cold-rolled steel sheet at a maximum temperature of 700 ° C or greater and 900 ° C or less; a retention process for cooling the cold-rolled annealed steel sheet in a temperature range equal to or greater than 350 ° C and equal to or less than 480 ° C at an average cooling rate equal to or greater than 0 ° C. , 1 ° C / s equal to or less than 200 ° C / s, and retain the steel plate in this temperature range for a time equal to or greater than 1 second and equal to or less than 1000 seconds; a final cooling process of primarily cooling cold-rolled steel sheet over a temperature range of 350 ° C to 220 ° C at an average cooling rate of 5 ° C or greater or less than 25 ° C ° C / s, and secondarily cool the steel sheet over a temperature range of 120 ° C to near room temperature at an average cooling rate of 100 ° C or greater or less than 5 ° C / s, and wherein the rolling is performed with an amount of stress equal to or less than 20% in each of the two final passes in the hot rolling process.
    [6]
    Method according to claim 5, characterized in that the plate which is reheated to 1100 ° C or higher after being cooled to 1100 ° C or less is used in the hot rolling process.
    [7]
    Method according to claim 5, characterized in that it also comprises an immersion process of dipping the steel plate in a hot dip galvanizing bath after the retention process.
    [8]
    Method according to claim 7, characterized in that it also comprises an alloy forming process of carrying out an alloy forming process in a range equal to or greater than 500 ° C and equal to or less than 580 ° C after immersion process.
    类似技术:
    公开号 | 公开日 | 专利标题
    BR112012018697B1|2018-11-21|steel sheet and steel sheet production method
    RU2559070C2|2015-08-10|High-strength cold-rolled steel plate with excellent uniform relative elongation and ability for hole expansion and method of its production
    US10450642B2|2019-10-22|High-strength galvanized steel sheet and method for producing the same
    ES2663747T3|2018-04-16|Hot rolled steel sheet and its manufacturing method
    RU2566121C1|2015-10-20|High strength dip galvanized steel plate with excellent characteristic of impact strength, and method of its manufacturing, and high strength alloyed dip galvanized steel plate and method of its manufacturing
    JP5163835B2|2013-03-13|Hot-rolled steel sheet, cold-rolled steel sheet, galvanized steel sheet, and production methods thereof
    WO2016136810A1|2016-09-01|Cold-rolled steel sheet and method for manufacturing same
    US10934600B2|2021-03-02|High-strength steel sheet and production method therefor
    RU2573455C2|2016-01-20|High strength hot galvanised steel plate and method of its production
    KR101753510B1|2017-07-04|High strength steel sheet having high young's modulus and method for manufacturing the same
    BR112013026024B1|2019-01-29|hot rolled high strength steel sheet with excellent local deformability, and its manufacturing method
    EP3219821A1|2017-09-20|High-strength hot-dip galvanized steel sheet and production method thereof
    BR112014007483B1|2019-12-31|hot-dip galvanized steel sheet and manufacturing process
    JPWO2012121219A1|2014-07-17|Hot-rolled steel sheet and manufacturing method thereof
    BR112013024984B1|2018-12-11|Hot rolled steel sheet and method of production thereof
    KR101607798B1|2016-03-30|Cold-rolled steel sheet and manufacturing method for same
    US10472697B2|2019-11-12|High-strength steel sheet and production method therefor
    BR112019008336A2|2019-08-06|carburizing steel sheet, and method of fabricating carburizing steel sheet
    JP5712771B2|2015-05-07|Steel sheet with excellent Young's modulus in the direction perpendicular to rolling and method for producing the same
    BR102012025758A2|2014-05-13|HIGH RESISTANCE HOT GALVANIZED STEEL SHEET WITH LOW PERFORMANCE HOT, HIGH RESISTANCE HOT GALVANIZED STEEL SHEET, METHOD FOR PRODUCING HIGH RESISTANCE HOT GALVANIZED STEEL SHEET YIELD, AND METHOD FOR PRODUCTION OF HOT GALVANIZED STEEL SHEET AND RECOZED OF HIGH RESISTANCE WITH LOW INCOME.
    US11035019B2|2021-06-15|High-strength steel sheet and production method therefor
    JP5533765B2|2014-06-25|High-strength cold-rolled steel sheet with excellent local deformability and its manufacturing method
    BR102012017451A2|2015-08-25|Cold rolled steel sheet having excellent bending capacity and production method
    RU2511000C2|2014-04-10|Cold-rolled steel plate with excellent formability and its manufacturing method
    WO2019130713A1|2019-07-04|High strength steel sheet and method for producing same
    同族专利:
    公开号 | 公开日
    KR20120107003A|2012-09-27|
    EP2530180A1|2012-12-05|
    CA2788095C|2014-12-23|
    WO2011093490A1|2011-08-04|
    CN102770571A|2012-11-07|
    CN102770571B|2014-07-09|
    JPWO2011093490A1|2013-06-06|
    MX2012008690A|2012-08-23|
    BR112012018697A2|2016-05-03|
    JP4902026B2|2012-03-21|
    US9410231B2|2016-08-09|
    KR101477877B1|2014-12-30|
    EP2530180B1|2018-11-14|
    CA2788095A1|2011-08-04|
    EP2530180A4|2017-06-28|
    PL2530180T3|2019-05-31|
    US20120305144A1|2012-12-06|
    ES2705232T3|2019-03-22|
    引用文献:
    公开号 | 申请日 | 公开日 | 申请人 | 专利标题
    JPH0735536B2|1988-01-14|1995-04-19|株式会社神戸製鋼所|Manufacturing method of high ductility and high strength composite structure steel sheet|
    JPH0762178B2|1990-07-30|1995-07-05|新日本製鐵株式会社|Method for producing high strength hot rolled steel sheet with excellent stretch flangeability and ductility|
    US5470529A|1994-03-08|1995-11-28|Sumitomo Metal Industries, Ltd.|High tensile strength steel sheet having improved formability|
    US6319338B1|1996-11-28|2001-11-20|Nippon Steel Corporation|High-strength steel plate having high dynamic deformation resistance and method of manufacturing the same|
    US7090731B2|2001-01-31|2006-08-15|Kabushiki Kaisha Kobe Seiko Sho |High strength steel sheet having excellent formability and method for production thereof|
    JP4188608B2|2001-02-28|2008-11-26|株式会社神戸製鋼所|High-strength steel sheet with excellent workability and method for producing the same|
    JP4188609B2|2001-02-28|2008-11-26|株式会社神戸製鋼所|High-strength steel sheet with excellent workability and method for producing the same|
    US7267890B2|2001-06-06|2007-09-11|Nippon Steel Corporation|High-strength hot-dip galvanized steel sheet and hot-dip galvannealed steel sheet having fatigue resistance corrosion resistance ductility and plating adhesion after servere deformation and a method of producing the same|
    JP3775334B2|2002-04-18|2006-05-17|Ｊｆｅスチール株式会社|High-strength steel sheet with excellent workability, manufacturing method and processing method thereof|
    CN100510141C|2004-12-28|2009-07-08|株式会社神户制钢所|Ultrahigh-strength steel sheet superior in hydrogen-embrittlement resistance|
    JP4716359B2|2005-03-30|2011-07-06|株式会社神戸製鋼所|High strength cold-rolled steel sheet excellent in uniform elongation and method for producing the same|
    EP1978113B1|2005-12-06|2018-08-01|Kabushiki Kaisha Kobe Seiko Sho|High-strength galvannealed sheet steels excellent in powdering resistance and process for production of the same|
    JP4692259B2|2005-12-07|2011-06-01|Ｊｆｅスチール株式会社|High-strength steel sheet with excellent formability and shape freezeability|
    JP4964488B2|2006-04-20|2012-06-27|新日本製鐵株式会社|High strength high Young's modulus steel plate having good press formability, hot dip galvanized steel plate, alloyed hot dip galvanized steel plate and steel pipe, and production method thereof|
    JP4676923B2|2006-06-05|2011-04-27|新日本製鐵株式会社|High strength and high ductility hot dip galvanized steel sheet excellent in corrosion resistance and welding strength and method for producing the same|
    JP5245228B2|2006-08-31|2013-07-24|新日鐵住金株式会社|High-strength hot-dip galvanized steel sheet with excellent elongation and corrosion resistance and method for producing the same|
    JP5320681B2|2007-03-19|2013-10-23|Ｊｆｅスチール株式会社|High strength cold rolled steel sheet and method for producing high strength cold rolled steel sheet|
    JP5092481B2|2007-03-22|2012-12-05|住友金属工業株式会社|High-strength cold-rolled steel sheet and manufacturing method thereof|
    JP5369663B2|2008-01-31|2013-12-18|Ｊｆｅスチール株式会社|High-strength hot-dip galvanized steel sheet excellent in workability and manufacturing method thereof|US9689060B2|2011-08-17|2017-06-27|Kobe Steel, Ltd.|High-strength hot-rolled steel sheet|
    JP5636347B2|2011-08-17|2014-12-03|株式会社神戸製鋼所|High strength steel sheet with excellent formability at room temperature and warm, and its warm forming method|
    US8876987B2|2011-10-04|2014-11-04|Jfe Steel Corporation|High-strength steel sheet and method for manufacturing same|
    CN102605244B|2012-03-30|2014-02-19|武汉钢铁公司|Painted steel for corrosion-resistant structure and production method of painted steel|
    CN102700186A|2012-06-02|2012-10-03|安徽博特金属复合材料制造有限公司|Ultra-deep drawing copper steel copper cold rolling lamination composite metal material and manufacture method thereof|
    KR101449128B1|2012-10-04|2014-10-08|주식회사 포스코|High carbon steel sheet having excellent uniformity and workability and method for manufacturing thereof|
    KR101439667B1|2012-12-20|2014-09-12|주식회사 포스코|A steel containing phosphorous with excellent impact toughness and high strength|
    KR101461729B1|2012-12-21|2014-11-14|주식회사 포스코|Boron-added high carbon steel having superior strength and ductility and method for manufacturing the same|
    KR101490569B1|2012-12-27|2015-02-05|주식회사 포스코|A high strength steel containing phosphorous|
    KR101461765B1|2012-12-27|2014-11-13|주식회사 포스코|Hot rolled steel sheet having superior strength and ductility and manufacturing method thereof|
    JP2014185359A|2013-03-22|2014-10-02|Jfe Steel Corp|High strength steel sheet|
    WO2015011511A1|2013-07-24|2015-01-29|Arcelormittal Investigación Y Desarrollo Sl|Steel sheet having very high mechanical properties of strength and ductility, manufacturing method and use of such sheets|
    CN103614664A|2013-10-22|2014-03-05|芜湖市鸿坤汽车零部件有限公司|A martensite alloy steel material used for an air valve of an internal combustion engine and a preparation method of the alloy steel material|
    KR101529180B1|2013-10-30|2015-06-16|현대제철 주식회사|Steel and method of manufacturing steel product using the same|
    CN103589952A|2013-11-27|2014-02-19|内蒙古包钢钢联股份有限公司|Rare earth alloying TRIP steel|
    CN103882323B|2014-03-20|2016-06-29|马钢控股有限公司|MnCr alloying hot forming steel and production method thereof|
    KR101597418B1|2014-03-28|2016-02-24|현대제철 주식회사|High strength hot-rolled steel sheet and method of manufacturing the same|
    EP3178953A4|2014-08-07|2017-07-05|JFE Steel Corporation|High-strength steel sheet and production method for same, and production method for high-strength galvanized steel sheet|
    US10662496B2|2014-08-07|2020-05-26|Jfe Steel Corporation|High-strength steel sheet and production method for same, and production method for high-strength galvanized steel sheet|
    CN106574342B|2014-08-07|2018-10-12|杰富意钢铁株式会社|The manufacturing method of high-strength steel sheet and its manufacturing method and high strength galvanized steel plate|
    JP5983895B2|2014-08-07|2016-09-06|Ｊｆｅスチール株式会社|High strength steel plate and method for producing the same, and method for producing high strength galvanized steel plate|
    CN104213040B|2014-08-27|2016-02-17|南京创贝高速传动机械有限公司|A kind of special steel of high strength bearing and complete processing thereof|
    CN104264039B|2014-10-13|2016-08-24|内蒙古科技大学|A kind of TRIP steel plate containing rare earth La and preparation method|
    JP6282577B2|2014-11-26|2018-02-21|株式会社神戸製鋼所|High strength high ductility steel sheet|
    KR101657822B1|2014-12-24|2016-09-20|주식회사 포스코|Hot dip galvanized and galvannealed steel sheet having excellent elongation property, and method for the same|
    ES2743814T3|2015-02-20|2020-02-20|Nippon Steel Corp|Hot Rolled Steel Sheet|
    WO2016132549A1|2015-02-20|2016-08-25|新日鐵住金株式会社|Hot-rolled steel sheet|
    WO2016135898A1|2015-02-25|2016-09-01|新日鐵住金株式会社|Hot-rolled steel sheet or plate|
    BR112017017443A2|2015-02-25|2018-04-03|Nippon Steel & Sumitomo Metal Corporation|hot rolled steel sheet|
    CN106319368B|2015-06-16|2018-04-24|鞍钢股份有限公司|A kind of economical thin carrier bar and its manufacture method|
    MX2018000328A|2015-07-13|2018-03-14|Nippon Steel & Sumitomo Metal Corp|Steel sheet, hot-dip galvanized steel sheet, alloyed hot-dip galvanized steel sheet, and production methods therefor.|
    JP6460239B2|2015-07-13|2019-01-30|新日鐵住金株式会社|Steel sheet, hot-dip galvanized steel sheet, alloyed hot-dip galvanized steel sheet, and methods for producing them|
    JP6749818B2|2016-02-29|2020-09-02|株式会社神戸製鋼所|High-strength steel sheet and method for manufacturing the same|
    EP3421633B1|2016-03-31|2020-05-13|JFE Steel Corporation|Thin steel sheet, plated steel sheet, method for producing hot-rolled steel sheet, method for producing cold-rolled full-hard steel sheet, method for producing thin steel sheet, and method for producing plated steel sheet|
    CN109072375B|2016-03-31|2020-11-03|杰富意钢铁株式会社|Thin steel sheet and plated steel sheet, and method for producing hot-rolled steel sheet, method for producing cold-rolled all-hard steel sheet, method for producing thin steel sheet, and method for producing plated steel sheet|
    TWI629369B|2016-08-05|2018-07-11|日商新日鐵住金股份有限公司|Steel plate and plated steel plate|
    TWI629367B|2016-08-05|2018-07-11|日商新日鐵住金股份有限公司|Steel plate and plated steel|
    US11021776B2|2016-11-04|2021-06-01|Nucor Corporation|Method of manufacture of multiphase, hot-rolled ultra-high strength steel|
    US10968502B2|2016-11-04|2021-04-06|Nucor Corporation|Method of manufacture of multiphase, cold-rolled ultra-high strength steel|
    JP6414246B2|2017-02-15|2018-10-31|Ｊｆｅスチール株式会社|High strength steel plate and manufacturing method thereof|
    CN108950376A|2017-05-23|2018-12-07|陈章华|A kind of low chromium wear-resisting alloy steel and preparation method thereof|
    CN108950427A|2017-05-23|2018-12-07|陈章华|Low boron low chrome steel of low-carbon and preparation method thereof|
    CN108929983A|2017-05-23|2018-12-04|陈章华|Low boron high chrome alloy steel of low-carbon and preparation method thereof|
    CN108950428A|2017-05-23|2018-12-07|陈章华|A kind of middle chromium wear-resisting alloy steel and preparation method thereof|
    CN108950426A|2017-05-23|2018-12-07|陈章华|Chromium alloyed steel and preparation method thereof in the low boron of low-carbon|
    JP6860420B2|2017-05-24|2021-04-14|株式会社神戸製鋼所|High-strength steel sheet and its manufacturing method|
    CN108467988A|2018-02-08|2018-08-31|江西新能源科技职业学院|A kind of combined machine arm|
    CN109182894A|2018-08-21|2019-01-11|宁波市拓欧金属制品有限公司|A kind of precision is wear-resistant top glue stamping parts and its production technology|
    US20220025497A1|2018-10-04|2022-01-27|Nippon Steel Corporation|Galvannealed steel sheet|
    KR102153200B1|2018-12-19|2020-09-08|주식회사 포스코|High strength cold rolled steel sheet and manufacturing method for the same|
    KR102164086B1|2018-12-19|2020-10-13|주식회사 포스코|High strength cold rolled steel sheet and galvannealed steel sheet having excellent burring property, and method for manufacturing thereof|
    KR102348529B1|2019-12-18|2022-01-07|주식회사 포스코|High strength steel sheet having excellent workability and method for manufacturing the same|
    KR102321292B1|2019-12-18|2021-11-03|주식회사 포스코|High strength steel sheet having excellent workability and method for manufacturing the same|
    CN111424211B|2020-04-30|2021-08-20|鞍钢股份有限公司|Weather-resistant steel for wide 700 MPa-grade hot-rolled container and manufacturing method thereof|
    CN112226691B|2020-09-30|2022-02-15|鞍钢股份有限公司|Hot rolled steel plate for 1800 MPa-grade hot stamping wheel spoke and manufacturing method thereof|
    CN112251669B|2020-09-30|2022-02-18|鞍钢股份有限公司|Hot rolled steel plate for 2000 MPa-level hot stamping wheel spoke and manufacturing method thereof|
    CN112226690B|2020-09-30|2022-02-15|鞍钢股份有限公司|Pickled steel plate for 1800 MPa-level hot stamping wheel rim and manufacturing method thereof|
    CN112267065B|2020-09-30|2022-02-15|鞍钢股份有限公司|Pickled steel plate for 2000 MPa-level hot stamping wheel rim and manufacturing method thereof|
    CN112267067B|2020-09-30|2022-02-18|鞍钢股份有限公司|Hot rolled steel plate for 2000 MPa-level hot stamping wheel rim and manufacturing method thereof|
    CN112267066B|2020-09-30|2022-02-15|鞍钢股份有限公司|Hot rolled steel plate for 1800 MPa-grade hot stamping wheel rim and manufacturing method thereof|
    CN112760562A|2020-12-22|2021-05-07|鞍钢集团北京研究院有限公司|Delayed fracture-resistant 2000 MPa-grade steel plate and preparation method thereof|
    CN113512688A|2021-07-15|2021-10-19|重庆增隆新材料科技有限公司|Spherical powder material for aviation ultrahigh-strength steel and preparation method thereof|
    CN113462986A|2021-07-16|2021-10-01|鞍钢股份有限公司|2000MPa environment-friendly heat-resistant steel for agricultural machinery and manufacturing method thereof|
    CN113667894A|2021-08-13|2021-11-19|北京首钢冷轧薄板有限公司|800 MPa-grade dual-phase steel with excellent hole expansion performance and preparation method thereof|
    法律状态:
    2017-08-01| B25D| Requested change of name of applicant approved|Owner name: NIPPON STEEL AND SUMITOMO METAL CORPORATION (JP) |
    2018-01-23| B07A| Application suspended after technical examination (opinion) [chapter 7.1 patent gazette]|
    2018-06-05| B06A| Patent application procedure suspended [chapter 6.1 patent gazette]|
    2018-10-09| B09A| Decision: intention to grant [chapter 9.1 patent gazette]|
    2018-11-21| B16A| Patent or certificate of addition of invention granted [chapter 16.1 patent gazette]|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 31/01/2011, OBSERVADAS AS CONDICOES LEGAIS. |
    2019-11-26| B25D| Requested change of name of applicant approved|Owner name: NIPPON STEEL CORPORATION (JP) |
    2021-11-23| B21F| Lapse acc. art. 78, item iv - on non-payment of the annual fees in time|Free format text: REFERENTE A 11A ANUIDADE. |
    优先权:
    申请号 | 申请日 | 专利标题
    JP2010-019193|2010-01-29|
    JP2010019193|2010-01-29|
    JP2010-032667|2010-02-17|
    JP2010032667|2010-02-17|
    PCT/JP2011/051896|WO2011093490A1|2010-01-29|2011-01-31|Steel sheet and process for producing steel sheet|
    [返回顶部]