(19)
(11) EP 4 474 510 A1

(12) EUROPEAN PATENT APPLICATION
published in accordance with Art. 153(4) EPC

(43) Date of publication:
11.12.2024 Bulletin 2024/50

(21) Application number: 23774240.8

(22) Date of filing: 30.01.2023
(51) International Patent Classification (IPC): 
C22C 38/00(2006.01)
C22C 38/06(2006.01)
C21D 9/46(2006.01)
C22C 38/60(2006.01)
(52) Cooperative Patent Classification (CPC):
C22C 38/00; C21D 9/46; C22C 38/06; C22C 38/60
(86) International application number:
PCT/JP2023/002915
(87) International publication number:
WO 2023/181641 (28.09.2023 Gazette 2023/39)
(84) Designated Contracting States:
AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC ME MK MT NL NO PL PT RO RS SE SI SK SM TR
Designated Extension States:
BA
Designated Validation States:
KH MA MD TN

(30) Priority: 25.03.2022 JP 2022049757

(71) Applicant: JFE Steel Corporation
Tokyo 100-0011 (JP)

(72) Inventors:
  • TOBATA, Junya
    Tokyo 100-0011 (JP)
  • TOJI, Yuki
    Tokyo 100-0011 (JP)
  • MINAMI, Hidekazu
    Tokyo 100-0011 (JP)

(74) Representative: Hoffmann Eitle 
Patent- und Rechtsanwälte PartmbB Arabellastraße 30
81925 München
81925 München (DE)

   


(54) HIGH-STRENGTH STEEL SHEET AND METHOD FOR PRODUCING SAME


(57) Objects are to provide a high strength steel sheet having 980 MPa or higher TS and being excellent in press formability, flatness in the width direction, and working embrittlement resistance; and to provide a method for manufacturing the same.
The high strength steel sheet has a specific chemical composition and is such that in a region at 1/4 sheet thickness, the area fraction of tempered martensite is 38% or more and less than 90%, the volume fraction of retained austenite is less than 3%, the area fraction of the total of ferrite and bainitic ferrite is 100 or more and 60% or less, the average grain size of prior austenite is 20 um or less, and the average of the proportions of packets having the largest area in prior austenite grains is 70% by area or less of the prior austenite grain.




Description

Technical Field



[0001] The present invention relates to a high strength steel sheet excellent in tensile strength, press formability, flatness in the width direction, and working embrittlement resistance, and to a method for manufacturing the same. The high strength steel sheet of the present invention may be suitably used as structural members, such as automobile parts.

Background Art



[0002] Steel sheets for automobiles are being increased in strength in order to reduce CO2 emissions by weight reduction of vehicles and to enhance crashworthiness by weight reduction of automobile bodies at the same time, with introduction of new laws and regulations one after another. To increase the strength of automobile bodies, high strength steel sheets having a tensile strength (TS) of 1180 MPa or higher grade are increasingly applied to principal structural parts of automobiles.

[0003] High strength steel sheets used in automobiles require excellent press formability. For example, high strength steel sheets with high El and excellent hole expansion ratio λ are suitably applied to automobile frame parts, such as bumpers. From the point of view of crash safety, excellent working embrittlement resistance is required.

[0004] Furthermore, high strength steel sheets used in automobiles require high flatness. Patent Literature 1 describes that warpage of a steel sheet causes operational troubles in forming lines and adversely affects the dimensional accuracy of products. The present inventors carried out extensive studies and have found that the dimensional accuracy of products is affected not only by the warpage of steel sheets but also by the flatness in the width direction that is evaluated as steepness. For example, the steepness in the width direction is suitably 0.02 or less in order to achieve excellent dimensional accuracy.

[0005] To meet the above demands, for example, Patent Literature 2 provides a hot-dip galvanized steel sheet with excellent press formability and low-temperature toughness that has a tensile strength of 980 MPa or more, and a method for manufacturing the same. While the steel sheet of Patent Literature 2 is improved in embrittlement at low temperatures, the technique does not take into consideration the working embrittlement of the steel sheet or the flatness in the width direction.

Citation List


Patent Literature



[0006] 

PTL 1: Japanese Patent No. 4947176

PTL 2: Japanese Patent No. 6777272


Non Patent Literature



[0007] NPL 1: Journal of Smart Processing, 2013, Vol. 2, No. 3, pp. 110-118

Summary of Invention


Technical Problem



[0008] The present invention has been developed in view of the circumstances discussed above. Objects of the present invention are therefore to provide a high strength steel sheet having 980 MPa or higher TS and being excellent in press formability, flatness in the width direction, and working embrittlement resistance; and to provide a method for manufacturing the same.

Solution to Problem



[0009] The present inventors carried out extensive studies directed to solving the problems described above and have consequently found the following facts.
  1. (1) 980 MPa or higher TS and excellent press formability can be realized by limiting the amount of tempered martensite to 38% or more and less than 90%, the amount of the total of ferrite and bainitic ferrite to 10% or more and 60% or less, and the amount of retained austenite to less than 3%.
  2. (2) The flatness in the width direction can be enhanced by limiting the proportion of a packet having the largest area in tempered martensite to 70% or less of a prior austenite grain.
  3. (3) Excellent working embrittlement resistance can be achieved by limiting the proportion of a packet having the largest area in tempered martensite to 70% or less of a prior austenite grain and by limiting the average prior austenite grain size in tempered martensite to 20 um or less.


[0010] The present invention has been made based on the above findings. Specifically, a summary of configurations of the present invention is as follows.
  1. [1] A high strength steel sheet having a chemical composition including, in mass%, C: 0.030% or more and 0.500% or less, Si: 0.01% or more and 2.50% or less, Mn: 0.10% or more and 5.00% or less, P: 0.100% or less, S: 0.0200% or less, Al: 1.000% or less, N: 0.0100% or less, and O: 0.0100% or less, a balance being Fe and incidental impurities, the high strength steel sheet being such that in a region at 1/4 sheet thickness, an area fraction of tempered martensite is 38% or more and less than 90%, a volume fraction of retained austenite is less than 3%, an area fraction of the total of ferrite and bainitic ferrite is 10% or more and 60% or less, an average grain size of prior austenite is 20 um or less, and an average of the proportions of packets having the largest area in prior austenite grains is 70% by area or less of the prior austenite grain.
  2. [2] The high strength steel sheet according to [1], wherein the chemical composition further includes at least one element selected from, in mass%, Ti: 0.200% or less, Nb: 0.200% or less, V: 0.200% or less, Ta: 0.10% or less, W: 0.10% or less, B: 0.0100% or less, Cr: 1.00% or less, Mo: 1.00% or less, Co: 0.010% or less, Ni: 1.00% or less, Cu: 1.00% or less, Sn: 0.200% or less, Sb: 0.200% or less, Ca: 0.0100% or less, Mg: 0.0100% or less, REM: 0.0100% or less, Zr: 0.100% or less, Te: 0.100% or less, Hf: 0.10% or less, and Bi: 0.200% or less.
  3. [3] The high strength steel sheet according to [1] or [2], which has a coated layer on a surface of the steel sheet.
  4. [4] A method for manufacturing the high strength steel sheet according to [1] or [2], the method including providing a cold rolled steel sheet produced by subjecting a steel having the chemical composition described above to hot rolling, pickling, and cold rolling; heating the steel sheet at an annealing temperature T1 of 700°C or above and 950°C or below for a holding time t1 at the annealing temperature T1 of 10 seconds or more and 1000 seconds or less; cooling the steel sheet in such a manner that the average cooling rate from 750°C to 600°C is less than 20°C/s, the average cooling rate from (Ms + 50°C) to a quench start temperature T2 is less than 5°C/s wherein the quench start temperature T2 is (Ms - 80°C) or above and is below Ms where Ms is martensite start temperature (°C) defined by formula (1), and the average cooling rate from the quench start temperature T2 to 80°C is 300°C/s or more; and heating the steel sheet at a tempering temperature T3 of 100°C or above and 400°C or below for a holding time t3 at the tempering temperature T3 of 10 seconds or more and 10000 seconds or less,

    Ms = 519 - 474 × [% C] - 30.4 × [% Mn] - 12.1 × [% Cr] - 7.5 × [% Mo] - 17.7 × [% Ni] - T1/80
    wherein [% C], [% Mn], [% Cr], [% Mo], and [% Ni] indicate the contents (mass%) of C, Mn, Cr, Mo, and Ni, respectively, and are zero when the element is absent.
  5. [5] The method for manufacturing the high strength steel sheet according to [4], further including performing a coating treatment.

Advantageous Effects of Invention



[0011] According to the present invention, a high strength steel sheet can be obtained that has 980 MPa or higher TS and excels in press formability, flatness in the width direction and working embrittlement resistance. Furthermore, for example, the high strength steel sheet of the present invention may be applied to automobile structural members to reduce the weight of automobile bodies and thereby to enhance fuel efficiency. Thus, the present invention is highly valuable in industry.

Brief Description of Drawings



[0012] 

[Fig. 1] Fig. 1 is a set of views illustrating a structure of a packet having the largest area in a prior austenite grain according to the present invention, and how the calculation is made.

[Fig. 2] Fig. 2 is a set of views illustrating the concept of the steepness θ of a steel sheet according to the present invention, and how the steepness is calculated. Description of Embodiments



[0013] Embodiments of the present invention will be described below.

[0014] First, appropriate ranges of the chemical composition of the high strength steel sheet and the reasons why the chemical composition is thus limited will be described. In the following description, "%" indicating the contents of constituent elements of steel means "mass%" unless otherwise specified.

[C: 0.030% or more and 0.500% or less]



[0015] Carbon is one of the important basic components of steel. Particularly in the present invention, carbon is an important element that affects the fraction of martensite and the working embrittlement resistance. When the C content is less than 0.030%, the fraction of martensite is so small that realizing 980 MPa or higher TS is difficult. When, on the other hand, the C content is more than 0.500%, martensite becomes brittle to cause deterioration in working embrittlement resistance. Thus, the C content is limited to 0.030% or more and 0.500% or less. The C content is preferably 0.050% or more. The C content is preferably 0.400% or less. The C content is more preferably 0.100% or more. The C content is more preferably 0.350% or less.

[Si: 0.01% or more and 2.50% or less]



[0016] Silicon is one of the important basic components of steel. Silicon suppresses the occurrence of carbides during continuous annealing and promotes the formation of retained austenite. Thus, particularly in the present invention, silicon is an important element that affects TS and the amount of retained austenite. When the Si content is less than 0.01%, realizing 980 MPa or higher TS is difficult. When, on the other hand, the Si content is more than 2.50%, the amount of retained austenite is increased excessively to make it difficult to achieve 85% or more YR. Thus, the Si content is limited to 0.01% or more and 2.50% or less. The Si content is preferably 0.05% or more. The Si content is preferably 2.00% or less. The Si content is more preferably 0.10% or more. The Si content is more preferably 1.20% or less.

[Mn: 0.10% or more and 5.00% or less]



[0017] Manganese is one of the important basic components of steel. Particularly in the present invention, manganese is an important element that affects the fraction of martensite and the working embrittlement resistance. When the Mn content is less than 0.10%, the fraction of martensite is so small that realizing 980 MPa or higher TS is difficult. When, on the other hand, the Mn content is more than 5.00%, martensite becomes brittle to cause deterioration in working embrittlement resistance. Thus, the Mn content is limited to 0.10% or more and 5.00% or less. The Mn content is preferably 0.50% or more. The Mn content is preferably 4.50% or less. The Mn content is more preferably 0.80% or more. The Mn content is more preferably 4.00% or less.

[P: 0.100% or less]



[0018] Phosphorus is segregated at prior austenite grain boundaries and makes the grain boundaries brittle, thereby lowering the ultimate deformability of steel sheets and causing deterioration in working embrittlement resistance. Thus, the P content needs to be 0.100% or less. The lower limit of the P content is not particularly specified. In view of the fact that phosphorus is a solid solution strengthening element and can increase the strength of steel sheets, the lower limit is preferably 0.001% or more. For the reasons above, the P content is limited to 0.100% or less. The P content is preferably 0.001% or more. The P content is preferably 0.070% or less.

[S: 0.0200% or less]



[0019] Sulfur forms sulfides and lowers the ultimate deformability of steel sheets to cause deterioration in working embrittlement resistance. Thus, the S content needs to be 0.0200% or less. The lower limit of the S content is not particularly specified but is preferably 0.0001% or more due to production technique limitations. For the reasons above, the S content is limited to 0.0200% or less. The S content is preferably 0.0001% or more. The S content is preferably 0.0050% or less.

[Al: 1.000% or less]



[0020] Aluminum raises the A3 transformation temperature to allow more ferrite to be contained in the microstructure. The fraction of martensite is correspondingly lowered to make it difficult to realize 980 MPa or higher TS. Thus, the Al content needs to be 1.000% or less. The lower limit of the Al content is not particularly specified. In view of the fact that aluminum suppresses the occurrence of carbides during continuous annealing and promotes the formation of retained austenite, the Al content is preferably 0.001% or more. For the reasons above, the Al content is limited to 1.000% or less. The Al content is preferably 0.001% or more. The Al content is preferably 0.500% or less.

[N: 0.0100% or less]



[0021] Nitrogen forms nitrides and lowers the ultimate deformability of steel sheets to cause deterioration in working embrittlement resistance. Thus, the N content needs to be 0.0100% or less. The lower limit of the N content is not particularly specified but the N content is preferably 0.0001% or more due to production technique limitations. For the reasons above, the N content is limited to 0.0100% or less. The N content is preferably 0.0001% or more. The N content is preferably 0.0050% or less.

[O: 0.0100% or less]



[0022] Oxygen forms oxides and lowers the ultimate deformability of steel sheets to cause deterioration in working embrittlement resistance. Thus, the O content needs to be 0.0100% or less. The lower limit of the O content is not particularly specified but the O content is preferably 0.0001% or more due to production technique limitations. For the reasons above, the O content is limited to 0.0100% or less. The O content is preferably 0.0001% or more. The O content is preferably 0.0050% or less.

[0023] The chemical composition of the high strength steel sheet according to an embodiment of the present invention includes the components described above, and the balance is Fe and incidental impurities. Here, the incidental impurities include Zn, Pb, As, Ge, Sr, and Cs. A total of 0.100% or less of these impurities is acceptable.

[0024] In addition to the components in the proportions described above, the high strength steel sheet of the present invention may further include at least one element selected from, in mass%, Ti: 0.200% or less, Nb: 0.200% or less, V: 0.200% or less, Ta: 0.10% or less, W: 0.10% or less, B: 0.0100% or less, Cr: 1.00% or less, Mo: 1.00% or less, Ni: 1.00% or less, Co: 0.010% or less, Cu: 1.00% or less, Sn: 0.200% or less, Sb: 0.200% or less, Ca: 0.0100% or less, Mg: 0.0100% or less, REM: 0.0100% or less, Zr: 0.100% or less, Te: 0.100% or less, Hf: 0.10% or less, and Bi: 0.200% or less. These elements may be contained singly or in combination.

[0025] When the contents of Ti, Nb, and V are each 0.200% or less, coarse precipitates and inclusions will not occur in large amounts and thus will not cause lowering of the ultimate deformability of steel sheets; hence there will be no deterioration in working embrittlement resistance. Thus, the contents of Ti, Nb, and V are each preferably 0.200% or less. The lower limits of the contents of Ti, Nb, and V are not particularly specified. These elements form fine carbides, nitrides, or carbonitrides during hot rolling or continuous annealing to increase the strength of steel sheets. In view of this fact, the contents of Ti, Nb, and V are each more preferably 0.001% or more. When titanium, niobium, and vanadium are added, the contents thereof are each limited to 0.200% or less for the reasons above. The contents are each more preferably 0.001% or more. The contents are each more preferably 0.100% or less.

[0026] When the contents of Ta and W are each 0.10% or less, coarse precipitates and inclusions will not occur in large amounts and thus will not cause lowering of the ultimate deformability of steel sheets; hence there will be no deterioration in working embrittlement resistance. Thus, the contents of Ta and W are each preferably 0.10% or less. The lower limits of the contents of Ta and W are not particularly specified. These elements form fine carbides, nitrides, or carbonitrides during hot rolling or continuous annealing to increase the strength of steel sheets in some cases. In view of this fact, the contents of Ta and W are each more preferably 0.01% or more. When tantalum and tungsten are added, the contents thereof are each limited to 0.10% or less for the reasons above. The contents are each more preferably 0.01% or more. The contents are each more preferably 0.08% or less.

[0027] When the B content is 0.0100% or less, inner cracks that lower the ultimate deformability of steel sheets will not form during casting or hot rolling and thus there will be no deterioration in working embrittlement resistance. Thus, the B content is preferably 0.0100% or less. The lower limit of the B content is not particularly specified. The B content is more preferably 0.0003% or more in view of the fact that this element is segregated at austenite grain boundaries during annealing and enhances hardenability. When boron is added, the content thereof is limited to 0.0100% or less for the reasons above. The content is more preferably 0.0003% or more. The content is more preferably 0.0080% or less.

[0028] When the contents of Cr, Mo, and Ni are each 1.00% or less, coarse precipitates and inclusions will not occur in increased amounts and thus will not cause lowering of the ultimate deformability of steel sheets; hence there will be no deterioration in working embrittlement resistance. Thus, the contents of Cr, Mo, and Ni are each preferably 1.00% or less. The lower limits of the contents of Cr, Mo, and Ni are not particularly specified. In view of the fact that these elements enhance hardenability, the contents of Cr, Mo, and Ni are each more preferably 0.01% or more. When chromium, molybdenum, and nickel are added, the contents thereof are each limited to 1.00% or less for the reasons above. The contents are each more preferably 0.01% or more. The contents are each more preferably 0.80% or less.

[0029]  When the Co content is 0.010% or less, coarse precipitates and inclusions will not occur in increased amounts and thus will not cause lowering of the ultimate deformability of steel sheets; hence there will be no deterioration in working embrittlement resistance. Thus, the Co content is preferably 0.010% or less. The lower limit of the Co content is not particularly specified. In view of the fact that this element enhances hardenability, the Co content is more preferably 0.001% or more. When cobalt is added, the content thereof is limited to 0.010% or less for the reasons above. The content is more preferably 0.001% or more. The content is more preferably 0.008% or less.

[0030] When the Cu content is 1.00% or less, coarse precipitates and inclusions will not occur in increased amounts and thus will not cause lowering of the ultimate deformability of steel sheets; hence there will be no deterioration in working embrittlement resistance. Thus, the Cu content is preferably 1.00% or less. The lower limit of the Cu content is not particularly specified. In view of the fact that this element enhances hardenability, the Cu content is preferably 0.01% or more. When copper is added, the content thereof is limited to 1.00% or less for the reasons above. The content is more preferably 0.01% or more. The content is more preferably 0.80% or less.

[0031] When the Sn content is 0.200% or less, inner cracks that lower the ultimate deformability of steel sheets will not form during casting or hot rolling and thus there will be no deterioration in working embrittlement resistance. Thus, the Sn content is preferably 0.200% or less. The lower limit of the Sn content is not particularly specified. The Sn content is more preferably 0.001% or more in view of the fact that tin enhances hardenability (in general, is an element that enhances corrosion resistance). When tin is added, the content thereof is limited to 0.200% or less for the reasons above. The content is more preferably 0.001% or more. The content is more preferably 0.100% or less.

[0032] When the Sb content is 0.200% or less, coarse precipitates and inclusions will not occur in increased amounts and thus will not cause lowering of the ultimate deformability of steel sheets; hence there will be no deterioration in working embrittlement resistance. Thus, the Sb content is preferably 0.200% or less. The lower limit of the Sb content is not particularly specified. In view of the fact that this element enables control of the thickness of surface layer softening and the strength, the Sb content is more preferably 0.001% or more. When antimony is added, the content thereof is limited to 0.200% or less for the reasons above. The content is more preferably 0.001% or more. The content is more preferably 0.100% or less.

[0033] When the contents of Ca, Mg, and REM are each 0.0100% or less, coarse precipitates and inclusions will not occur in increased amounts and thus will not cause lowering of the ultimate deformability of steel sheets; hence there will be no deterioration in working embrittlement resistance. Thus, the contents of Ca, Mg, and REM are each preferably 0.0100% or less. The lower limits of the contents of Ca, Mg, and REM are not particularly specified. In view of the fact that these elements change the shapes of nitrides and sulfides into spheroidal and enhance the ultimate deformability of steel sheets, the contents of Ca, Mg, and REM are each more preferably 0.0005% or more. When calcium, magnesium, and rare earth metal(s) are added, the contents thereof are each limited to 0.0100% or less for the reasons above. The contents are each more preferably 0.0005% or more. The contents are each more preferably 0.0050% or less.

[0034] When the contents of Zr and Te are each 0.100% or less, coarse precipitates and inclusions will not occur in increased amounts and thus will not cause lowering of the ultimate deformability of steel sheets; hence there will be no deterioration in working embrittlement resistance. Thus, the contents of Zr and Te are each preferably 0.100% or less. The lower limits of the contents of Zr and Te are not particularly specified. In view of the fact that these elements change the shapes of nitrides and sulfides into spheroidal and enhance the ultimate deformability of steel sheets, the contents of Zr and Te are each more preferably 0.001% or more. When zirconium and tellurium are added, the contents thereof are each limited to 0.100% or less for the reasons above. The contents are each more preferably 0.001% or more. The contents are each more preferably 0.080% or less.

[0035] When the Hf content is 0.10% or less, coarse precipitates and inclusions will not occur in increased amounts and thus will not cause lowering of the ultimate deformability of steel sheets; hence there will be no deterioration in working embrittlement resistance. Thus, the Hf content is preferably 0.10% or less. The lower limit of the Hf content is not particularly specified. In view of the fact that this element changes the shapes of nitrides and sulfides into spheroidal and enhances the ultimate deformability of steel sheets, the Hf content is more preferably 0.01% or more. When hafnium is added, the content thereof is limited to 0.10% or less for the reasons above. The content is more preferably 0.01% or more. The content is more preferably 0.08% or less.

[0036] When the Bi content is 0.200% or less, coarse precipitates and inclusions will not occur in increased amounts and thus will not cause lowering of the ultimate deformability of steel sheets; hence there will be no deterioration in working embrittlement resistance. Thus, the Bi content is preferably 0.200% or less. The lower limit of the Bi content is not particularly specified. In view of the fact that this element reduces the occurrence of segregation, the Bi content is more preferably 0.001% or more. When bismuth is added, the content thereof is limited to 0.200% or less for the reasons above. The content is more preferably 0.001% or more. The content is more preferably 0.100% or less.

[0037] When the content of any of Ti, Nb, V, Ta, W, B, Cr, Mo, Ni, Co, Cu, Sn, Sb, Ca, Mg, REM, Zr, Te, Hf, and Bi is below the preferred lower limit, the element does not impair the advantageous effects of the present invention and is regarded as an incidental impurity.

[0038]  Next, the steel microstructure of the high strength steel sheet of the present invention will be described.

[Area fraction of tempered martensite: 38% or more and less than 90%]



[0039] When the amount of tempered martensite is less than 38%, realizing 980 MPa or higher TS is difficult. When, on the other hand, the amount of tempered martensite is 90% or more, the amount of ferrite is lowered to cause a decrease in El and consequently press formability is lowered. Thus, the amount of tempered martensite is limited to 38% or more and less than 90%. The amount is preferably 40% or more. The amount is preferably 60% or less.

[0040] Here, tempered martensite is measured as follows. A longitudinal cross section of the steel sheet is polished and is etched with 3 vol% Nital. A portion at 1/4 sheet thickness (a location corresponding to 1/4 of the sheet thickness in the depth direction from the steel sheet surface) is observed using SEM in 10 fields of view at a magnification of ×2000. In the microstructure images, tempered martensite is structures that have fine irregularities inside the structures and contain inner carbides. The values thus obtained are averaged to determine the tempered martensite.

[Amount of retained austenite: less than 3%]



[0041] This configuration is a very important requirement that constitutes the present invention. When the volume fraction of retained austenite is 3% or more, press formability is lowered. The reason for low press formability is that retained austenite with a high fraction gives rise to a lowering in λ by undergoing strain-induced transformation. Thus, the retained austenite is limited to less than 3%. The amount of retained austenite is preferably 1% or less. The lower limit of retained austenite is not particularly limited and may be 0%.

[0042] Here, retained austenite is measured as follows. The steel sheet is polished to expose a face 0.1 mm below 1/4 sheet thickness and is thereafter further chemically polished to expose a face 0.1 mm below the face exposed above. The face is analyzed with an X-ray diffractometer using CoKα radiation to determine the integral intensity ratios of the diffraction peaks of {200}, {220}, and {311} planes of fcc iron and {200}, {211}, and {220} planes of bcc iron. Nine integral intensity ratios thus obtained are averaged to determine retained austenite.

[Area fraction of the total of ferrite and bainitic ferrite: 10% or more and 60% or less]



[0043] This configuration is a very important requirement that constitutes the present invention. When the total of ferrite and bainitic ferrite is less than 10%, El is lowered and consequently press formability is deteriorated. When, on the other hand, the total of ferrite and bainitic ferrite is more than 60%, realizing 980 MPa or higher TS is difficult. Thus, the total of ferrite and bainitic ferrite is limited to 10% or more and 60% or less. The total amount is preferably 35% or more. The total amount is preferably 55% or less.

[0044] Here, the total of ferrite and bainitic ferrite is measured as follows. A longitudinal cross section of the steel sheet is polished and is etched with 3 vol% Nital. A portion at 1/4 sheet thickness (a location corresponding to 1/4 of the sheet thickness in the depth direction from the steel sheet surface) is observed using SEM in 10 fields of view at a magnification of ×2000. In the microstructure images, ferrite is recessed structures having a flat interior and containing no inner carbides. In the microstructure images, bainitic ferrite is recessed structures having a flat interior and containing inner carbides. The values thus obtained are combined and are averaged to determine the total of ferrite and bainitic ferrite.

[0045] Possible microstructures other than those described above include pearlite, fresh martensite, and acicular ferrite. These microstructures do not affect characteristics as long as their fractions are 5% or less, and thus may be present within that range.

[Average grain size of prior austenite: 20 um or less]



[0046] This configuration is a very important requirement that constitutes the present invention. Reducing the average grain size of prior austenite can suppress crack propagation and thereby enhances the working embrittlement resistance of steel sheets. In order to obtain these effects, the average grain size of prior austenite needs to be 20 um or less. The lower limit of the average grain size of prior austenite is not particularly specified. When, however, the average grain size of prior austenite is less than 2 um, more retained austenite may form. Thus, the average grain size is preferably 2 um or more. For the reasons above, the average grain size of prior austenite is limited to 20 um or less. The average grain size is preferably 2 um or more. The average grain size is preferably 15 um or less. The average grain size is more preferably 3 um or more. The average grain size is more preferably 10 um or less.

[0047] Here, the average grain size of prior austenite is measured as follows. A longitudinal cross section of the steel sheet is polished and is etched with, for example, a mixed solution of picric acid and ferric chloride to expose prior austenite grain boundaries. Portions at 1/4 sheet thickness (locations corresponding to 1/4 of the sheet thickness in the depth direction from the steel sheet surface) are photographed with an optical microscope each in 3 to 10 fields of view at a magnification of ×400. Twenty straight lines including 10 vertical lines and 10 horizontal lines are drawn at regular intervals on the image data obtained, and the grain size is determined by a linear intercept method.

[Average of the proportions of packets having the largest area in prior austenite grains: 70% by area or less]



[0048] This configuration is a very important requirement that constitutes the present invention. The proportion of a packet having the largest area in a prior austenite grain affects the flatness in the width direction and the working embrittlement resistance. As illustrated in Fig. 1, a prior austenite grain contains up to four kinds of packets distinguished by crystal habit plane formed by transformation. The packet having the largest area in a prior austenite grain is the packet that occupies the largest area among such packets.

[0049] The proportion of one packet in a prior austenite grain is determined by dividing the area of the packet of interest by the area of the whole prior austenite grain. As a result of extensive studies, the present inventors have found that strain among the packets is reduced and the flatness in the width direction is improved by lowering the proportion of a packet having the largest area in a prior austenite grain. The present inventors have also found that lowering the proportion of a packet having the largest area in a prior austenite grain leads to a fine microstructure and suppresses crack propagation, thereby enhancing the working embrittlement resistance of the steel sheet. Thus, the average of the proportions of packets having the largest area in prior austenite grains is limited to 70% or less. The average proportion is preferably 60% or less. The lower limit of the average proportion of packets having the largest area in prior austenite grains is not particularly limited. The grains contain up to four kinds of packets. When four packets are evenly distributed, the proportion of a packet having the largest area in the prior austenite grain is 25%. Thus, the lower limit of the average proportion of packets having the largest area in prior austenite grains may be 25% or more but is not necessarily limited thereto.

[0050] Here, the average proportion of packets having the largest area in prior austenite grains is measured as follows. First, a test specimen for microstructure observation is sampled from the cold rolled steel sheet. Next, the sampled test specimen is polished by vibration polishing with colloidal silica to expose a cross section in the rolling direction (a longitudinal cross section) for use as observation surface. The observation surface is specular. Next, electron backscatter diffraction (EBSD) measurement is performed with respect to a portion at 1/4 sheet thickness (a location corresponding to 1/4 of the sheet thickness in the depth direction from the steel sheet surface) to obtain local crystal orientation data. Here, the SEM magnification is ×1000, the step size is 0.2 um, the measured region is 80 um square, and the WD is 15 mm. The local orientation data obtained is analyzed with OIM Analysis 7 (OIM), and a map (a CP map) that shows close-packed plane groups (CP groups) with different colors is created using the method described in Non Patent Literature 1. In the present invention, a packet is defined as a region or regions belonging to the same CP group. From the CP map obtained, the area of the packet having the largest area is determined and is divided by the area of the whole prior austenite grain to give the proportion of the packet having the largest area in the prior austenite grain. This analysis is performed with respect to 10 or more adjacent prior austenite grains, and the results are averaged to give the average proportion of packets having the largest area in prior austenite grains.

[0051] Next, a manufacturing method of the present invention will be described.

[0052] In the present invention, a steel material (a steel slab) may be obtained by any known steelmaking method without limitation, such as a converter or an electric arc furnace. To prevent macro-segregation, the steel slab (the slab) is preferably produced by a continuous casting method.

[0053] In the present invention, the slab heating temperature, the slab soaking holding time, and the coiling temperature in hot rolling are not particularly limited. For example, the steel slab may be hot rolled in such a manner that the slab is heated and is then rolled, that the slab is subjected to hot direct rolling after continuous casting without being heated, or that the slab is subjected to a short heat treatment after continuous casting and is then rolled. The slab heating temperature, the slab soaking holding time, the finish rolling temperature, and the coiling temperature in hot rolling are not particularly limited. The lower limit of the slab heating temperature is preferably 1100°C or above. The upper limit of the slab heating temperature is preferably 1300°C or below. The lower limit of the slab soaking holding time is preferably 30 minutes or more. The upper limit of the slab soaking holding time is preferably 250 minutes or less. The lower limit of the finish rolling temperature is preferably Ar3 transformation temperature or above. Furthermore, the lower limit of the coiling temperature is preferably 350°C or above. The upper limit of the coiling temperature is preferably 650°C or below.

[0054] The hot rolled steel sheet thus produced is pickled. Pickling can remove oxides on the steel sheet surface and is thus important to ensure good chemical convertibility and a high quality of coating in the final high strength steel sheet. Pickling may be performed at a time or several. The hot rolled sheet that has been pickled may be cold rolled directly or may be subjected to heat treatment before cold rolling.

[0055] The rolling reduction in cold rolling and the sheet thickness after rolling are not particularly limited. The lower limit of the rolling reduction is preferably 30% or more. The upper limit of the rolling reduction is preferably 80% or less. The advantageous effects of the present invention may be obtained without any limitations on the number of rolling passes and the rolling reduction in each pass.

[0056] The cold rolled steel sheet obtained as described above is annealed. Annealing conditions are as follows.

[Annealing temperature T1: 700°C or above and 950°C or below]



[0057] When the annealing temperature T1 is below 700°C, the area fraction of the total of ferrite and bainitic ferrite is more than 60% to make it difficult to realize 980 MPa or higher TS. When, on the other hand, the annealing temperature T1 is above 950°C, prior austenite grains are excessively increased in size and the prior austenite grain size exceeds 20 um to give rise to a decrease in working embrittlement resistance. Thus, the annealing temperature T1 is limited to 700°C or above and 950°C or below. The annealing temperature T1 is preferably 800°C or above. The annealing temperature T1 is preferably 900°C or below.

[Holding time t1 at the annealing temperature T1: 10 seconds or more and 1000 seconds or less]



[0058] When the holding time t1 at the annealing temperature T1 is less than 10 seconds, austenitization is insufficient and the area fraction of the total of ferrite and bainitic ferrite is more than 60%. As a result, it is difficult to achieve 980 MPa or higher TS. When, on the other hand, the holding time at the annealing temperature T1 is more than 1000 seconds, the prior austenite grain size is excessively increased, and the working embrittlement resistance is lowered. For the reasons above, the holding time t1 at the annealing temperature T1 is limited to 10 seconds or more and 1000 seconds or less. The holding time t1 is preferably 50 seconds or more. The holding time t1 is preferably 500 seconds or less.

[Average cooling rate from 750°C to 600°C: less than 20°C/s]



[0059] When the average cooling rate from 750°C to 600°C is 20°C/s or more, the area fraction of the total of ferrite and bainitic ferrite is less than 10% to cause a decrease in El, thereby deteriorating press formability. For the reasons above, the average cooling rate from 750°C to 600°C is limited to less than 20°C/s. The average cooling rate is preferably 15°C/s or less.

[Average cooling rate from (Ms + 50°C) to a quench start temperature T2: less than 5°C/s]



[0060] This configuration is a very important requirement that constitutes the present invention. When the average cooling rate from (Ms + 50°C) to a quench start temperature T2 is 5°C/s or more, the area fraction of the total of ferrite and bainitic ferrite is less than 10% to cause a decrease in El, thereby deteriorating press formability. For the reasons above, the average cooling rate from (Ms + 50°C) to a quench start temperature T2 is limited to less than 5°C/s. The average cooling rate is preferably 4°C/s or less.

[Quench start temperature T2: (Ms - 80°C) or above and below Ms]



[0061] This configuration is a very important requirement that constitutes the present invention. The quench start temperature T2 is controlled to (Ms - 80°C) or above and below Ms to ensure that the martensite transformation rate before the start of quenching is 1% or more and 80% or less. In this manner, quenching can give microstructures in which the average proportion of packets having the largest area in prior austenite grains is 70% or less and the volume fraction of retained austenite is less than 3%. When the quench start temperature T2 is below (Ms - 80°C), the martensite transformation rate before the start of quenching exceeds 80% and consequently the volume fraction of retained austenite is 3% or more to cause a decrease in press formability. When, on the other hand, the quench start temperature T2 is above Ms, the martensite transformation rate before the start of quenching is less than 1% and the average proportion of packets having the largest area in prior austenite grains exceeds 70% to cause deterioration in flatness in the width direction and working embrittlement resistance. Thus, the quench start temperature T2 is limited to (Ms - 80°C) or above and below Ms. The quench start temperature T2 is preferably (Ms - 50°C) or above. The quench start temperature T2 is preferably (Ms - 5°C) or below. The martensite start temperature Ms (°C) is defined by the following formula (1):

Ms = 519 - 474 × [% C] - 30.4 × [% Mn] - 12.1 × [% Cr] - 7.5 × [% Mo] - 17.7 × [% Ni] - T1/80
wherein [% C], [% Mn], [% Cr], [% Mo], and [% Ni] indicate the contents (mass%) of C, Mn, Cr, Mo, and Ni, respectively, and are zero when the element is absent.

[Average cooling rate from the quench start temperature T2 to 80°C: 300°C/s or more]



[0062] When the average cooling rate from the quench start temperature T2 to 80°C is less than 300°C/s, the volume fraction of retained austenite is 3% or more to cause a decrease in press formability. Thus, the average cooling rate from the quench start temperature T2 to 80°C is limited to 300°C/s or more. The average cooling rate is preferably 800°C/s or more. The upper limit is not necessarily specified but is preferably 2000°C/s or less.

[Tempering temperature T3: 100°C or above and 400°C or below]



[0063] In the present invention, tempered martensite is a microstructure that is formed when martensite at 80°C or below is heat-treated at a tempering temperature of 100°C or above for a holding time of 10 seconds or more. Thus, martensite is not sufficiently tempered when the tempering temperature T3 is below 100°C. The resultant microstructures will be based on as-quenched martensite, which deteriorates the working embrittlement resistance. When, on the other hand, the tempering temperature T3 is above 400°C, martensite is excessively tempered to make it difficult to achieve 980 MPa or higher TS. For the reasons above, the tempering temperature T3 is limited to 100°C or above and 400°C or below. The tempering temperature T3 is preferably 150°C or above. The tempering temperature T3 is preferably 350°C or below.

[Holding time t3 at the tempering temperature T3: 10 seconds or more and 10000 seconds or less]



[0064] In the present invention, tempered martensite is a microstructure that is formed when martensite at 80°C or below is heat-treated at a tempering temperature of 100°C or above for a holding time of 10 seconds or more. Thus, martensite is not sufficiently tempered when the holding time t3 at the tempering temperature T3 is less than 10 seconds. The resultant microstructures will be based on as-quenched martensite, which deteriorates the working embrittlement resistance. When, on the other hand, the tempering temperature T3 is more than 10000 seconds, martensite is excessively tempered to make it difficult to achieve 980 MPa or higher TS. For the reasons above, the holding time t3 at the tempering temperature T3 is limited to 10 seconds or more and 10000 seconds or less. The holding time t3 is preferably 50 seconds or more. The holding time t3 is preferably 5000 seconds or less.

[0065] Post-temper cooling is not particularly limited and the steel sheet may be cooled to a desired temperature in an appropriate manner. Incidentally, the desired temperature is preferably about room temperature.

[0066] Furthermore, the high strength steel sheet described above may be worked under conditions where the amount of equivalent plastic strain is 0.10% or more and 5.00% or less. The working may be followed by reheating at 100°C or above and 400°C or below.

[0067] When the high strength steel sheet is a product that is traded, the steel sheet is usually traded after being cooled to room temperature.

[0068] The high strength steel sheet may be subjected to coating treatment during annealing or after annealing.

[0069] For example, the coating treatment during annealing may be hot-dip galvanizing treatment performed when the steel sheet is being cooled or has been cooled from 750°C to 600°C at an average cooling rate of less than 20°C/s. The hot-dip galvanizing treatment may be followed by alloying. For example, the coating treatment after annealing may be Zn-Ni electrical alloy coating treatment or pure Zn electroplated coating treatment performed after tempering. A coated layer may be formed by electroplated coating, or hot-dip zinc-aluminum-magnesium alloy coating may be applied. While the coating treatment has been described above focusing on zinc coating, the types of coating metals, such as Zn coating and Al coating, are not particularly limited. Other conditions in the manufacturing method are not particularly limited. From the point of view of productivity, the series of treatments including annealing, hot-dip galvanizing, and alloying treatment of the coated zinc layer is preferably performed on hot-dip galvanizing line CGL (continuous galvanizing line). To control the coating weight of the coated layer, the hot-dip galvanizing treatment may be followed by wiping. Conditions for operations, such as coating, other than those conditions described above may be determined in accordance with the usual hot-dip galvanizing technique.

[0070] After the coating treatment after annealing, the steel sheet may be worked again under conditions where the amount of equivalent plastic strain is 0.10% or more and 5.00 or less. The working may be followed by reheating at 100°C or above and 400°C or below.

EXAMPLES



[0071] Steels having a chemical composition described in Table 1 and 2, with the balance being Fe and incidental impurities, were smelted in a converter and were continuously cast into slabs. Next, the slabs obtained were heated, hot rolled, pickled, cold rolled, and subjected to annealing treatment and tempering treatment described in Tables 3 to 5. High strength cold rolled steel sheets having a sheet thickness of 0.6 to 2.2 mm were thus obtained. Incidentally, some of the steel sheets were subjected to coating treatment during or after annealing.
[Table 1]
Steels Chemical composition (mass%)  
C Si Mn P S N O Al Ti B Nb Cu Others
A 0.215 0.280 2.24 0.006 0.0011 0.005 0.006 0.047           INV. EX.
B 0.217 0.298 1.98 0.005 0.0009 0.006 0.005 0.053           INV. EX.
C 0.192 0.251 2.04 0.009 0.0008 0.002 0.003 0.015           INV. EX.
D 0.111 1.332 2.04 0.011 0.0007 0.004 0.005 0.024           INV. EX.
E 0.113 1.464 2.22 0.010 0.0014 0.006 0.002 0.018           INV. EX.
F 0.048 0.262 2.25 0.008 0.0011 0.004 0.002 0.030           INV. EX.
G 0.021 0.168 2.30 0.007 0.0013 0.003 0.005 0.036           COMP. EX.
H 0.468 0.166 2.09 0.009 0.0012 0.006 0.002 0.059           INV. EX.
I 0.522 0.248 2.00 0.010 0.0015 0.001 0.007 0.015           COMP. EX.
J 0.212 0.073 2.13 0.015 0.0010 0.005 0.006 0.052           INV. EX.
K 0.191 0.002 2.23 0.013 0.0006 0.002 0.006 0.020           COMP. EX.
L 0.210 2.339 2.22 0.006 0.0010 0.006 0.007 0.054           INV. EX.
M 0.205 2.532 1.98 0.012 0.0007 0.002 0.006 0.025           COMP. EX.
N 0.203 0.273 0.27 0.006 0.0007 0.001 0.004 0.055           INV. EX.
O 0.187 0.307 0.08 0.012 0.0009 0.007 0.005 0.033           COMP. EX.
P 0.191 0.271 4.98 0.012 0.0011 0.005 0.002 0.052           INV. EX.
Q 0.197 0.162 5.12 0.007 0.0007 0.005 0.004 0.040           COMP. EX.
R 0.216 0.314 2.12 0.099 0.0005 0.002 0.003 0.012           INV. EX.
S 0.219 0.333 2.06 0.121 0.0010 0.004 0.003 0.049           COMP. EX.
T 0.219 0.173 2.25 0.006 0.0182 0.006 0.006 0.024           INV. EX.
U 0.205 0.192 2.06 0.010 0.0222 0.004 0.002 0.024           COMP. EX.
V 0.205 0.165 2.18 0.011 0.0010 0.002 0.003 0.976           INV. EX.
W 0.195 0.165 2.10 0.015 0.0009 0.005 0.002 1.135           COMP. EX.
X 0.214 0.204 2.06 0.011 0.0009 0.0089 0.007 0.059           INV. EX.
Y 0.192 0.186 1.93 0.012 0.0007 0.0112 0.002 0.032           COMP. EX.
Z 0.182 0.229 2.22 0.011 0.0007 0.004 0.0090 0.037           INV. EX.
AA 0.206 0.271 2.19 0.009 0.0015 0.006 0.0110 0.040           COMP. EX.
AB 0.186 0.331 1.91 0.007 0.0010 0.005 0.001 0.038 0.002         INV. EX.
AC 0.190 0.327 2.29 0.013 0.0008 0.006 0.002 0.027 0.187         INV. EX.
AD 0.206 0.341 2.26 0.011 0.0012 0.006 0.003 0.038 0.223         COMP. EX.
AE 0.182 0.258 2.06 0.008 0.0009 0.005 0.005 0.038   0.0002       INV. EX.
AF 0.189 0.309 2.12 0.006 0.0005 0.007 0.003 0.048   0.0088       INV. EX.
AG 0.206 0.239 2.16 0.008 0.0009 0.003 0.005 0.031   0.0121       COMP. EX.
AH 0.187 0.164 2.27 0.006 0.0013 0.002 0.004 0.016     0.002     INV. EX.
AI 0.216 0.308 2.20 0.008 0.0011 0.002 0.003 0.031     0.189     INV. EX.
AJ 0.190 0.189 2.05 0.012 0.0006 0.003 0.007 0.051     0.203     COMP. EX.
AK 0.183 0.345 2.03 0.009 0.0013 0.002 0.005 0.023       0.03   INV. EX.
Underlines indicate being outside the range of the present invention.
[Table 2]
Steels Chemical composition (mass%)  
C Si Mn P S N O Al Ti B Nb Cu Others
AL 0.205 0.293 1.98 0.013 0.0012 0.005 0.002 0.057       0.90   INV. EX.
AM 0.190 0.317 2.29 0.007 0.0010 0.003 0.007 0.052       1.11   COMP. EX.
AN 0.214 0.261 2.25 0.007 0.0010 0.005 0.004 0.050         V:0.070 INV. EX.
AO 0.205 0.309 2.02 0.007 0.0006 0.002 0.006 0.028         Ta:0.05 INV. EX.
AP 0.213 0.215 2.26 0.014 0.0006 0.006 0.002 0.048         W:0.03 INV. EX.
AQ 0.187 0.263 2.10 0.015 0.0007 0.005 0.003 0.036         Cr:0.87 INV. EX.
AR 0.184 0.228 2.06 0.009 0.0011 0.002 0.004 0.029         Mo:0.13 INV. EX.
AS 0.193 0.288 2.29 0.012 0.0005 0.006 0.004 0.028         Co:0.008 INV. EX.
AT 0.219 0.242 2.21 0.007 0.0012 0.002 0.003 0.034         Ni:0.33 INV. EX.
AU 0.185 0.245 1.92 0.012 0.0011 0.007 0.004 0.056         Sn:0.012 INV. EX.
AV 0.185 0.301 2.08 0.009 0.0006 0.005 0.004 0.026         Sb:0.005 INV. EX.
AW 0.196 0.274 1.90 0.010 0.0012 0.004 0.002 0.056         Ca:0.0015 INV. EX.
AX 0.218 0.339 1.95 0.009 0.0009 0.004 0.004 0.022         Mg:0.0086 INV. EX.
AY 0.186 0.343 2.010 0.005 0.0008 0.002 0.002 0.051         Zr:0.083 INV. EX.
AZ 0.217 0.240 1.990 0.008 0.0013 0.007 0.003 0.024         Te:0.092 INV. EX.
BA 0.102 1.364 2.270 0.010 0.0014 0.006 0.005 0.016         Hf:0.05 INV. EX.
BB 0.128 1.390 1.960 0.012 0.0005 0.005 0.004 0.037         REM:0.0092 INV. EX.
BC 0.137 1.402 2.020 0.012 0.0007 0.003 0.005 0.030         Bi:0.164 INV. EX.
BD 0.132 1.328 1.940 0.007 0.0006 0.004 0.003 0.012         Zn:0.03 INV. EX.
BE 0.113 1.482 2.090 0.008 0.0007 0.005 0.007 0.041         Pb:0.016 INV. EX.
BF 0.111 1.374 2.000 0.007 0.0008 0.005 0.002 0.011         As:0.040 INV. EX.
BG 0.116 1.362 2.080 0.011 0.0011 0.006 0.006 0.012         Ge:0.090 INV. EX.
BH 0.133 1.387 2.220 0.009 0.0009 0.001 0.003 0.052         Sr:0.065 INV. EX.
BI 0.108 1.310 2.150 0.007 0.0012 0.001 0.004 0.037         Cs:0.082 INV. EX.
BJ 0.198 0.870 2.700 0.010 0.0003 0.004 0.001 0.045 0.007 0.0017 0.014 0.18 Ni:0.05 INV. EX.
BK 0.218 0.326 2.060 0.009 0.0008 0.007 0.007 0.012           INV. EX.
BL 0.108 1.352 1.920 0.013 0.0011 0.003 0.004 0.056           INV. EX.
BM 0.105 1.331 2.030 0.007 0.0006 0.004 0.002 0.049           INV. EX.
BN 0.207 1.374 1.910 0.007 0.0013 0.003 0.001 0.057           INV. EX.
BO 0.189 1.414 2.020 0.009 0.0015 0.003 0.003 0.050           INV. EX.
Underlines indicate being outside the range of the present invention.
[Table 3]
Nos. Steels Annealing temp. T1 (°C) Holding time t1 (s) Average cooling rate in temperature range of 750-600°C (°C/s) Average cooling rate in temperature range of (Ms+50°C)-quench start temp. T2 (°C/s) Ms (°C) (Ms-80) (°C) Quench start temp. T2 (°C) Cooling rate from T2 to 80°C (°C/s) Tempering temp. 13 (°C) Holding time t3 (s) Type"  
1 A 796 322 13 2 330 250 321 905 203 854 CR INV. EX.
2 B 783 348 7 3 337 257 323 966 189 994 CR INV. EX.
3 B 717 427 12 2 337 257 320 875 172 961 CR INV. EX.
4 B 692 255 10 2 337 257 327 957 215 989 CR COMP. EX.
5 B 927 274 7 3 336 256 322 862 151 606 CR INV. EX.
6 B 965 399 12 3 335 255 316 882 186 555 CR COMP. EX.
7 B 758 63 9 3 337 257 320 914 188 784 CR INV. EX.
8 B 777 8 6 3 336 256 322 863 199 706 CR COMP. EX.
9 B 785 896 11 2 336 256 324 888 193 931 CR INV. EX.
10 B 783 1015 11 4 336 256 322 1000 206 590 CR COMP. EX.
11 B 753 311 17 4 336 256 324 960 198 929 CR INV. EX.
12 B 924 404 25 2 335 255 321 872 212 563 CR COMP. EX.
13 B 798 223 12 4 336 256 322 831 162 596 CR INV. EX.
14 B 792 243 9 2 336 256 327 836 198 954 CR INV. EX.
15 B 759 207 7 3 335 255 328 878 215 780 CR INV. EX.
16 B 785 335 11 3 335 255 318 832 203 862 CR INV. EX.
17 B 779 381 9 4 337 257 327 842 151 693 CR INV. EX.
18 B 804 203 12 6 337 257 331 865 177 714 CR INV. EX.
19 B 790 241 7 3 336 256 261 928 156 687 CR INV. EX.
20 B 803 260 7 4 336 256 20 847 158 671 CR COMP. EX.
21 B 761 335 7 3 336 256 409 894 165 571 CR COMP. EX.
22 B 797 376 14 4 336 256 631 978 168 603 CR COMP. EX.
23 B 771 369 13 3 336 256 316 312 212 510 CR INV. EX.
24 B 755 222 10 2 336 256 326 284 201 832 CR COMP. EX.
25 B 764 414 10 3 336 256 323 34 211 741 CR COMP. EX.
26 B 788 404 9 3 337 257 331 915 167 879 CR INV. EX.
27 B 768 222 11 3 336 256 329 995 111 996 CR INV. EX.
28 B 768 437 15 3 337 257 325 846 110 639 CR INV. EX.
29 B 784 321 8 2 337 257 322 910 389 763 CR INV. EX.
30 B 772 266 13 4 336 256 321 883 398 707 CR INV. EX.
31 B 755 465 8 3 337 257 328 821 161 23 CR INV. EX.
32 B 790 311 15 3 336 256 326 897 173 12 CR INV. EX.
33 B 786 304 8 4 336 256 317 854 210 9860 CR INV. EX.
34 B 779 485 7 3 336 256 324 811 196 9878 CR INV. EX.
35 B 751 282 7 4 336 256 330 951 196 726 CR INV. EX.
36 B 808 294 14 3 336 256 328 956 178 828 CR INV. EX.
37 C 799 211 14 3 336 256 20 899 152 622 CR COMP. EX.
38 D 760 208 10 3 294 214 544 875 219 917 CR COMP. EX.
39 D 719 490 6 3 295 215 281 818 195 563 CR INV. EX.
Underlines indicate being outside the range of the present invention.
(*)CR: cold rolled steel sheet (no coating), GI: hot-dip galvanized steel sheet (no alloying of zinc coating), GA: galvannealed steel sheet, EG: electrogalvanized steel sheet
[Table 4]
Nos. Steels Annealing temp. T1 (°C) Holding time t1 (s) Average cooling rate in temperature range of 750-600°C (°C/s) Average cooling rate in temperature range of (Ms+50°C)-quench start temp. T2 (°C/s) Ms (°C) (Ms-80) (°C) Quench start temp. T2 (°C) Cooling rate from T2 to 80°C (°C/s) Tempering temp. 13 (°C) Holding time t3 (s) Type*  
40 D 935 452 14 3 294 214 276 870 159 565 CR INV. EX.
41 D 798 77 10 3 294 214 287 938 193 689 CR INV. EX.
42 D 756 903 15 3 294 214 281 827 171 585 CR INV. EX.
43 D 805 421 19 3 295 215 278 837 216 737 CR INV. EX.
44 D 794 453 11 4 294 214 277 876 159 969 CR INV. EX.
45 D 786 473 6 3 294 214 279 962 151 846 CR INV. EX.
46 D 770 485 14 4 295 215 285 878 215 607 CR INV. EX.
47 D 805 453 9 2 294 214 216 877 191 949 CR INV. EX.
48 D 793 380 12 3 294 214 287 972 187 527 CR INV. EX.
49 D 751 328 11 4 295 215 282 324 177 723 CR INV. EX.
50 D 796 292 6 4 294 214 282 822 215 652 CR INV. EX.
51 D 766 311 10 2 295 215 288 857 114 508 CR INV. EX.
52 D 808 328 12 3 295 215 281 966 391 882 CR INV. EX.
53 D 790 421 13 2 295 215 286 890 216 12 CR INV. EX.
54 D 764 295 11 3 295 215 278 980 198 9910 CR INV. EX.
55 D 795 344 13 3 294 214 283 802 177 855 CR INV. EX.
56 D 804 332 13 3 295 215 284 846 160 813 CR INV. EX.
57 D 778 361 11 3 295 215 276 836 208 558 CR INV. EX.
58 D 766 334 8 4 295 215 21 869 169 742 CR COMP. EX.
59 D 794 330 7 2 294 214 347 962 188 501 GA COMP. EX.
60 D 786 472 13 4 295 215 289 971 168 859 GA INV. EX.
61 D 756 347 7 4 295 215 277 857 174 747 GA INV. EX.
62 D 778 220 10 2 295 215 280 845 178 636 EG INV. EX.
63 D 799 304 7 3 295 215 287 888 199 977 GA INV. EX.
64 D 801 233 15 2 294 214 288 860 177 518 CR INV. EX.
65 E 776 328 9 3 298 218 280 905 167 662 CR INV. EX.
66 F 768 335 10 2 411 331 404 986 167 603 GA INV. EX.
67 G 766 285 9 3 420 340 413 991 204 546 GA COMP. EX.
68 H 775 383 12 3 213 133 199 818 189 812 GI INV. EX.
69 I 806 292 10 3 183 103 172 915 190 559 GA COMP. EX.
70 J 768 465 11 3 334 254 320 970 164 534 GA INV. EX.
71 K 794 423 8 3 329 249 317 952 212 852 GA COMP. EX.
72 L 787 397 10 4 342 262 331 994 174 783 GA INV. EX.
73 M 773 409 8 4 336 256 325 943 163 646 GI COMP. EX.
74 N 785 205 10 3 393 313 383 974 176 537 GA INV. EX.
75 O 783 203 14 2 408 328 390 896 209 789 GA COMP. EX.
76 P 779 359 13 3 272 192 261 813 164 618 GA INV. EX.
77 Q 759 297 6 3 260 180 253 957 183 728 GA COMP. EX.
78 R 766 394 8 3 329 249 322 879 158 860 GA INV. EX.
Underlines indicate being outside the range of the present invention.
(*)CR: cold rolled steel sheet (no coating), GI: hot-dip galvanized steel sheet (no alloying of zinc coating), GA: galvannealed steel sheet, EG: electrogalvanized steel sheet
[Table 5]
Nos. Steels Annealing temp. T1 (°C) Holding time t1 (s) Average cooling rate in temperature range of 750-600°C (°C/s) Average cooling rate in temperature range of (Ms+50°C)-quench start temp. T2 (°C/s) Ms (°C) (Ms-80) (°C) Quench start temp. T2 (°C) Cooling rate from T2 to 80°C (°C/s) Tempering temp. T3 (°C) Holding time t3 (s) Type*  
79 S 784 454 13 3 341 261 327 930 189 933 GI COMP. EX.
80 T 801 331 12 2 341 261 325 901 215 887 GA INV. EX.
81 U 768 416 6 3 347 267 334 919 185 770 GA COMP. EX.
82 V 771 480 11 3 336 256 327 824 187 944 GA INV. EX.
83 W 758 214 12 3 352 272 345 984 164 764 GA COMP. EX.
84 X 801 499 13 3 352 272 335 934 171 697 CR INV. EX.
85 Y 790 401 6 3 341 261 326 971 194 829 CR COMP. EX.
86 Z 791 235 5 3 339 259 333 890 203 868 GA INV. EX.
87 AA 775 413 10 3 329 249 312 865 174 528 GA COMP. EX.
88 AB 787 208 6 3 350 270 333 992 193 882 GA INV. EX.
89 AC 798 455 14 3 345 265 340 942 170 856 GA INV. EX.
90 AD 777 477 7 4 336 256 330 977 150 508 GA COMP. EX.
91 AE 802 364 11 3 348 266 335 906 156 648 GA INV. EX.
92 AF 799 203 12 2 336 258 331 1000 211 653 GA INV. EX.
93 AG 752 276 5 2 326 246 313 979 168 583 CR COMP. EX.
94 AH 804 473 14 3 331 251 320 980 185 523 CR INV. EX.
95 AI 786 370 13 2 345 265 336 846 182 795 CR INV. EX.
96 AJ 803 309 10 3 340 260 329 977 220 587 CR COMP. EX.
97 AK 807 472 14 2 340 260 323 900 152 738 CR INV. EX.
98 AL 798 340 13 3 340 260 329 834 152 641 CR INV. EX.
99 AM 755 292 10 3 325 245 313 843 156 644 CR COMP. EX.
100 AN 705 370 5 3 351 271 340 924 194 645 CR INV. EX.
101 AO 927 268 9 4 339 259 320 856 181 676 CR INV. EX.
102 AP 773 51 11 2 346 266 338 878 214 580 CR INV. EX.
103 AQ 767 864 7 2 318 236 298 1000 211 849 CR INV. EX.
104 AR 788 208 18 3 326 246 313 942 168 501 CR INV. EX.
105 AS 804 235 11 4 340 260 333 948 170 967 CR INV. EX.
106 AT 801 287 14 3 321 241 314 888 164 610 CR INV. EX.
107 AU 752 236 15 4 349 269 332 963 171 868 CR INV. EX.
108 AV 771 260 7 2 333 253 332 807 187 716 CR INV. EX.
109 AW 785 472 13 3 332 252 261 921 206 904 CR INV. EX.
110 AX 807 354 14 3 345 265 335 325 151 504 CR INV. EX.
111 AY 758 450 13 3 333 253 326 833 182 679 CR INV. EX.
112 AZ 803 289 11 3 338 258 321 901 106 597 CR INV. EX.
113 BA 790 344 15 2 283 203 274 953 394 563 CR INV. EX.
114 BB 782 379 13 3 295 215 277 977 155 23 CR INV. EX.
115 BC 797 237 9 4 283 203 273 918 200 9851 CR INV. EX.
116 BD 799 406 11 4 284 204 265 940 196 667 CR INV. EX.
117 BE 799 205 8 4 306 226 292 914 168 663 CR INV. EX.
116 BF 769 466 8 2 290 210 277 844 213 732 CR INV. EX.
119 BG 768 326 12 2 287 207 273 812 153 757 CR INV. EX.
120 BH 769 333 7 3 292 212 287 811 150 829 CR INV. EX.
121 BI 794 352 13 2 293 213 281 949 207 878 CR INV. EX.
122 BJ 880 310 19 3 331 251 420 1000 180 800 CR COMP. EX.
123 BK 758 416 8 3 349 269 330 994 166 744 CR INV. EX.
124 BL 800 400 14 4 293 213 287 843 181 895 CR INV. EX.
125 BM 800 493 6 2 284 204 267 882 207 965 CR INV. EX.
126 BN 797 330 6 3 392 312 381 931 209 677 CR INV. EX.
127 BO 810 366 8 2 403 323 392 842 181 528 CR INV. EX.
Underlines indicate being outside the range of the present invention.
(*)CR: cold rolled steel sheet (no coating), GI: hot-dip galvanized steel sheet (no alloying of zinc coating), GA: galvannealed steel sheet, EG: electrogalvanized steel sheet


[0072] The high strength cold rolled steel sheets obtained as described above were used as test steels. Tensile characteristics, flatness in the width direction, and working embrittlement resistance were evaluated in accordance with the following test methods.

(Microstructure observation)



[0073] The amount of tempered martensite, the amount of retained austenite, the total amount of ferrite and bainitic ferrite, and the average grain size of prior austenite were determined by the methods described hereinabove.

(Proportion of packets having the largest area in prior austenite grains)



[0074] The average proportion of packets having the largest area in prior austenite grains was determined by the method described hereinabove.

(Tensile test)



[0075] A JIS No. 5 test specimen (gauge length: 50 mm, parallel section width: 25 mm) was sampled so that the longitudinal direction of the test specimen would be perpendicular to the rolling direction. A tensile test was performed in accordance with JIS Z 2241 under conditions where the crosshead speed was 1.67 × 10-1 mm/sec. TS and El were thus measured. In the present invention, 980 MPa or higher TS was determined to be acceptable.

(Press formability)



[0076] A hole expansion test was performed in accordance with JIS Z 2256 (2010). The steel sheets obtained were each cut to 100 mm × 100 mm. A 10 mm diameter hole was punched with a clearance of 12% ± 1%. While holding the steel sheet on a die having an inner diameter of 75 mm with a blank holder force of 9 tons (88.26 kN), a conical punch with an apex angle of 60° was pushed into the hole to measure the critical hole diameter at the occurrence of cracking. The limiting hole expansion ratio λ (%) was determined from the formula below, and the flangeability was evaluated based on the value of limiting hole expansion ratio.

Limiting hole expansion ratio: λ (%) = {(Df - D0)/D0} × 100
wherein Df is the hole diameter (mm) at the occurrence of cracking and D0 is the initial hole diameter (mm).

[0077] Based on the tensile strength (TS), the total elongation (El), and the hole expansion ratio (λ) obtained as described above, TS × El × λ0.5/1000 was calculated. The steel sheet was evaluated as "excellent in press formability" when the calculated value was 80 or more.

(Flatness in the width direction)



[0078] The cold rolled steel sheets obtained as described above were analyzed to measure the flatness in the width direction. The measurement is illustrated in Fig. 2. Specifically, a sheet with a length of 500 mm in the rolling direction (coil width × 500 mm L × sheet thickness) was cut out from the coil and was placed on a surface plate in such a manner that the warp at the ends would face upward. The height on the steel sheet was measured with a contact displacement meter by continuously moving the stylus over the width. Based on the results, the steepness θ as an index of the flatness of the steel sheet shape was measured as illustrated in Fig. 2. The flatness was rated as "×" when the steepness was more than 0.02, as "o" when the steepness was more than 0.01 and 0.02 or less, and as "⊚" when the steepness was 0.01 or less. The steel sheet was evaluated as "excellent in the flatness in the width direction" when the steepness was 0.02 or less.

(Working embrittlement resistance)



[0079] The working embrittlement resistance was evaluated by Charpy test. A Charpy test specimen was a 2 mm deep V-notched test piece that was a stack of steel sheets fastened together with bolts to eliminate any gaps between the steel sheets. The number of steel sheets that were stacked was controlled so that the thickness of the stack as the test piece would be closer to 10 mm. When, for example, the sheet thickness was 1.2 mm, eight sheets were stacked to give a 9.6 mm thick test piece. The sheets for stacking into the Charpy test specimen were sampled so that the width direction would be the longitudinal direction. As an index of the working embrittlement resistance, the ratio vE0%/vE10% of the absorbed impact energy at room temperature of the as-produced (unworked) steel sheet to that of the steel sheet after 10% rolling was measured. The working embrittlement resistance was rated as "×" when vE0%/vE10% was less than 0.6, as "o" when vE0%/vE10% was 0.6 or more and less than 0.7, and as "⊚" when vE0%/vE10% was 0.7 or more. The Charpy test specimen was evaluated as "excellent in working embrittlement resistance" when vE0%/vE10% was 0.6 or more. Conditions other than those described above conformed to JIS Z 2242: 2018.

[0080] The results are described in Tables 6 to 8. As shown in the tables, INVENTIVE EXAMPLES achieved 980 MPa or higher TS, excellent press formability, excellent flatness in the width direction, and excellent working embrittlement resistance. In contrast, COMPARATIVE EXAMPLES were unsatisfactory in one or more of TS, press formability, flatness in the width direction, and working embrittlement resistance.
[Table 6]
Nos. Steels Tempered martensite (area%) Retained austenite (vol%) Ferrite (area%) Bainitic ferrite (area%) Total of ferrite and bainitic ferrite (area%) Proportion of largest packets in prior austenite grains (area%) Prior γ grain size (µm) TS (MPa) EI (%) λ (%) TS×EI×λ0.5 /1000 Flatness in width direction Working embrittlement resistance  
1 A 55 1 36 10 46 50 15 1602 10 59 123 INV. EX.
2 B 59 1 33 10 43 53 12 1791 8 59 110 INV. EX.
3 B 41 0 49 7 56 47 10 1006 15 42 98 INV. EX.
4 B 34 0 60 6 66 50 12 827 18 56 111 COMP. EX.
5 B 57 1 46 4 50 60 20 1758 8 42 91 INV. EX.
6 B 52 0 38 6 44 56 24 1480 10 58 113 × COMP. EX.
7 B 43 0 50 7 57 50 12 1012 15 50 107 INV. EX.
8 B 35 0 58 8 66 58 14 896 17 60 118 COMP. EX.
9 B 51 1 39 6 45 55 18 1425 11 57 118 INV. EX.
10 B 54 0 41 8 49 55 21 1540 10 44 102 × COMP. EX.
11 B 85 0 11 3 14 50 8 1947 7 40 86 INV. EX.
12 B 94 1 1 6 7 52 10 2031 5 50 72 COMP. EX.
13 B 51 1 38 9 47 55 10 1471 10 57 111 INV. EX.
14 B 57 1 42 7 49 49 10 1687 9 59 117 INV. EX.
15 B 59 0 42 8 50 49 14 1752 8 51 100 INV. EX.
16 B 54 1 36 9 45 55 13 1545 10 47 106 INV. EX.
17 B 84 1 13 7 20 50 14 1973 6 51 85 INV. EX.
18 B 92 0 2 2 4 55 9 2294 4 57 69 INV. EX.
19 B 49 2 40 7 47 57 14 1390 11 33 88 INV. EX.
20 B 52 6 32 10 42 47 10 1522 10 25 76 COMP. EX.
21 B 53 1 39 8 47 95 10 1557 9 57 106 × × COMP. EX.
22 B 57 0 33 9 42 78 11 1732 9 49 109 × × COMP. EX.
23 B 56 2 42 6 48 56 12 1621 9 34 85 INV. EX.
24 B 52 6_ 40 6 46 59 12 1458 10 24 71 COMP. EX.
25 B 45 7 37 5 42 46 8 1128 14 21 72 COMP. EX.
26 B 52 0 37 7 44 50 12 1509 10 56 113 INV. EX.
27 B 55 1 43 5 48 50 11 1728 9 45 104 INV. EX.
28 B 54 1 34 7 41 48 11 1684 9 54 111 INV. EX.
29 B 53 0 32 9 41 53 14 1221 12 43 96 INV. EX.
30 B 59 0 35 7 42 52 14 1477 10 42 96 INV. EX.
31 B 52 0 37 9 46 49 9 1518 10 46 103 INV. EX.
32 B 52 1 41 7 48 47 10 1500 10 49 105 INV. EX.
33 B 50 1 37 7 44 46 13 1354 11 43 98 INV. EX.
34 B 52 1 37 8 45 58 14 1465 10 54 108 INV. EX.
35 B 57 0 36 9 45 56 10 1690 9 54 112 INV. EX.
36 B 51 1 39 4 43 53 13 1447 11 56 119 INV. EX.
37 C 52 5 37 9 46 50 13 1480 10 23 71 COMP. EX.
38 D 54 1 36 6 42 93 9 1384 11 48 105 × × COMP. EX.
39 D 41 0 54 5 59 58 14 1035 15 56 116 INV. EX.
40 D 54 0 44 4 48 48 18 1474 10 42 96 INV. EX.
41 D 42 0 54 4 58 56 10 983 15 42 96 INV. EX.
42 D 58 0 37 4 41 57 16 1636 9 58 112 INV. EX.
43 D 84 0 11 2 13 50 14 2138 6 51 92 INV. EX.
44 D 56 0 38 10 48 56 12 1564 9 50 100 INV. EX.
45 D 54 0 41 3 44 56 13 1486 10 52 107 INV. EX.
46 D 88 1 14 3 17 59 12 2120 6 49 89 INV. EX.
47 D 49 2 42 4 46 59 14 1201 12 34 84 INV. EX.
Underlines indicate being outside the range of the present invention.
[Table 7]
Nos. Steels Tempered martensite (area% ) Retained austenite (vol%) Ferrite (area%) Bainitic ferrite (area%) Total of ferrite and bainitic ferrite (area%) Proportion of largest packets in prior austenite grains (area%) Prior γ grain size (µm) TS (MPa) EI (%) λ (%) TSxEIxλ0.5 /1000 Flatness in width direction Working embrittlement resistance  
48 D 52 1 42 4 46 56 14 1342 11 48 102 INV. EX.
49 D 57 2 40 8 48 49 14 1582 9 33 82 INV. EX.
50 D 55 0 37 8 45 47 11 1435 10 48 99 INV. EX.
51 D 55 1 43 3 46 46 9 1586 10 55 118 INV. EX.
52 D 50 0 37 5 42 52 13 1046 14 48 101 INV. EX.
53 D 53 0 35 8 43 52 8 1343 11 53 108 INV. EX.
54 D 55 1 39 4 43 55 15 1060 13 52 99 INV. EX.
55 D 58 1 37 9 46 47 9 1627 9 42 95 INV. EX.
56 D 52 0 38 4 42 49 14 1382 11 55 113 INV. EX.
57 D 52 1 39 5 44 59 9 1310 11 52 104 INV. EX.
58 D 45 5 36 7 43 57 8 1054 14 26 75_ COMP. EX.
59 D 49 0 39 6 45 88_ 9 1205 12 50 102 x x COMP. EX.
60 D 52 0 33 10 43 55 14 1370 11 52 109 INV. EX.
61 D 57 1 32 9 41 54 13 1586 10 60 123 INV. EX.
62 D 51 1 36 7 43 50 15 1310 12 42 102 INV. EX.
63 D 51 1 39 6 45 50 13 1279 12 45 103 INV. EX.
64 D 52 0 43 3 46 56 15 1357 11 54 110 INV. EX.
65 E 59 1 33 7 40 59 10 1712 9 56 115 INV. EX.
66 F 42 0 50 5 55 59 10 1036 14 51 104 INV. EX.
67 G 33 1 59 5 64 51 11 819 18 57 111 COMP. EX.
68 H 53 1 40 8 48 54 11 2022 7 56 106 INV. EX.
69 I 51 0 46 3 49 55 12 2035 7 50 101 x COMP. EX.
70 J 56 0 35 7 42 48 10 1078 11 52 86 INV. EX.
71 K 55 1 37 4 41 54 12 820 10 52 59 COMP. EX.
72 L 57 2 38 10 48 57 9 1869 8 33 86 INV. EX.
73 M 44 6 39 9 48 52 10 1286 12 26 79 COMP. EX.
74 N 42 1 50 10 60 55 12 1096 13 57 108 INV. EX.
75 O 35 0 61 4 65 51 10 687 22 49 106 COMP. EX.
76 P 59 0 38 4 42 59 15 1984 8 54 117 INV. EX.
77 Q 55 1 39 6 45 56 9 1789 9 54 118 × COMP. EX.
78 R 52 1 36 6 42 52 9 1529 10 41 98 INV. EX.
79 S 53 0 38 6 44 48 14 1533 10 48 106 × COMP. EX.
80 T 58 0 38 7 45 47 11 1719 9 47 106 INV. EX.
81 U 57 0 32 9 41 57 12 1679 9 45 101 × COMP. EX.
82 V 40 1 48 7 55 54 9 1066 14 48 103 INV. EX.
83 W 30 0 64 6 70 45 15 792 19 51 107 COMP. EX.
84 X 54 0 40 8 48 51 13 1586 9 53 104 INV. EX.
85 Y 51 0 38 6 44 45 14 1361 11 43 98 × COMP. EX.
86 Z 56 1 43 5 48 53 9 1576 10 48 109 INV. EX.
87 AA 57 1 37 10 47 46 9 1713 9 49 108 × COMP. EX.
88 AB 53 0 41 4 45 51 14 1449 10 41 93 INV. EX.
89 AC 50 0 44 3 47 55 14 1496 10 53 109 INV. EX.
90 AD 58 1 39 9 48 57 14 1533 10 54 113 × COMP. EX.
91 AE 59 1 38 5 43 55 8 1772 9 45 107 INV. EX.
92 AF 54 1 43 3 46 55 13 1816 8 54 107 INV. EX.
93 AG 54 0 38 9 47 54 10 1850 8 59 114 × COMP. EX.
Underlines indicate being outside the range of the present invention.
[Table 8]
Nos. Steels Tempered martensite (area%) Retained austenite (vol%) Ferrite (area%) Bainitic ferrite (area%) Total of ferrite and bainitic ferrite (area%) Proportion of largest packets in prior austenite grains (area%) Prior γ grain size (µm) TS (MPa) EI (%) A (%) TS×EI×λ0.5 /1000 Flatness in width direction Working embrittlement resistance  
94 AH 57 1 37 5 42 51 13 1656 9 51 106 INV. EX.
95 AI 53 0 33 10 43 47 14 1696 9 49 107 INV. EX.
96 AJ 54 1 39 4 43 47 9 1742 9 56 117 × COMP. EX.
97 AK 58 1 44 4 48 48 11 1739 8 55 103 INV. EX.
98 AL 53 0 42 8 50 55 14 1771 8 57 107 INV. EX.
99 AM 54 0 40 8 48 57 10 1810 8 60 112 × COMP. EX.
100 AN 40 1 48 7 55 50 9 1038 14 47 100 INV. EX.
101 AO 52 1 41 4 45 55 16 1466 10 58 112 INV. EX.
102 AP 43 1 47 9 56 59 8 1039 15 48 108 INV. EX.
103 AQ 57 1 34 7 41 54 18 1613 9 43 95 INV. EX.
104 AR 84 1 11 6 17 49 10 2081 6 50 88 INV. EX.
105 AS 52 1 41 9 50 52 15 1476 10 56 110 INV. EX.
106 AT 58 1 37 4 41 56 15 1798 9 47 111 INV. EX.
107 AU 84 1 14 5 19 48 11 2071 6 56 93 INV. EX.
108 AV 50 2 37 8 45 49 10 1331 11 45 98 INV. EX.
109 AW 55 0 40 6 46 51 8 1536 10 31 86 INV. EX.
110 AX 50 2 40 9 49 47 9 1444 10 34 84 INV. EX.
111 AY 55 1 36 9 45 53 13 1564 9 53 102 INV. EX.
112 AZ 54 0 42 4 46 47 13 1682 9 57 114 INV. EX.
113 BA 50 1 40 7 47 51 9 1041 15 49 109 INV. EX.
114 BB 56 1 39 7 46 47 8 1603 9 56 108 INV. EX.
115 BC 52 1 32 9 41 59 15 1378 11 54 111 INV. EX.
116 BD 58 1 33 8 41 53 14 1633 9 42 95 INV. EX.
117 BE 52 0 37 9 46 52 9 1389 11 52 110 INV. EX.
118 BF 51 1 38 6 44 47 12 1257 12 53 110 INV. EX.
119 BG 57 1 39 6 45 50 14 1632 9 48 102 INV. EX.
120 BH 59 1 40 4 44 54 11 1774 9 40 101 INV. EX.
121 BI 54 0 36 4 40 60 8 1403 11 57 117 INV. EX.
122 BJ 89 0 9 1 10 88 9 1520 9 45 92 × × COMP. EX.
123 BK 57 1 37 5 42 45 13 1743 9 49 110 INV. EX.
124 BL 52 1 42 4 46 54 8 1339 11 47 101 INV. EX.
125 BM 51 1 43 4 47 57 8 1255 12 56 113 INV. EX.
126 BN 50 1 36 6 42 58 14 1406 11 52 112 INV. EX.
127 BO 59 0 34 9 43 46 10 1828 8 51 104 INV. EX.
Underlines indicate being outside the range of the present invention.



Claims

1. A high strength steel sheet having a chemical composition comprising, in mass%,

C: 0.030% or more and 0.500% or less,

Si: 0.01% or more and 2.50% or less,

Mn: 0.10% or more and 5.00% or less,

P: 0.100% or less,

S: 0.0200% or less,

Al: 1.000% or less,

N: 0.0100% or less, and

O: 0.0100% or less,

a balance being Fe and incidental impurities,

the high strength steel sheet being such that in a region at 1/4 sheet thickness,

an area fraction of tempered martensite is 38% or more and less than 90%,

a volume fraction of retained austenite is less than 3%,

an area fraction of the total of ferrite and bainitic ferrite is 10% or more and 60% or less,

an average grain size of prior austenite is 20 um or less, and

an average of proportions of packets having the largest area in prior austenite grains is 70% by area or less of the prior austenite grain.


 
2. The high strength steel sheet according to claim 1, wherein the chemical composition further comprises at least one element selected from, in mass%,

Ti: 0.200% or less, Nb: 0.200% or less,

V: 0.200% or less, Ta: 0.10% or less,

W: 0.10% or less, B: 0.0100% or less,

Cr: 1.00% or less, Mo: 1.00% or less,

Co: 0.010% or less, Ni: 1.00% or less,

Cu: 1.00% or less, Sn: 0.200% or less,

Sb: 0.200% or less, Ca: 0.0100% or less,

Mg: 0.0100% or less, REM: 0.0100% or less,

Zr: 0.100% or less, Te: 0.100% or less,

Hf: 0.10% or less, and Bi: 0.200% or less.


 
3. The high strength steel sheet according to claim 1 or 2, which has a coated layer on a surface of the steel sheet.
 
4. A method for manufacturing the high strength steel sheet according to claim 1 or 2, the method comprising:

providing a cold rolled steel sheet produced by subjecting a steel having the chemical composition to hot rolling, pickling, and cold rolling;

heating the steel sheet at an annealing temperature T1 of 700°C or above and 950°C or below for a holding time tl at the annealing temperature T1 of 10 seconds or more and 1000 seconds or less;

cooling the steel sheet in such a manner that:

the average cooling rate from 750°C to 600°C is less than 20°C/s,

an average cooling rate from (Ms + 50°C) to a quench start temperature T2 is less than 5°C/s wherein the quench start temperature T2 is (Ms - 80°C) or above and is below Ms where Ms is martensite start temperature (°C) defined by formula (1), and

an average cooling rate from the quench start temperature T2 to 80°C is 300°C/s or more; and

heating the steel sheet at a tempering temperature T3 of 100°C or above and 400°C or below for a holding time t3 at the tempering temperature T3 of 10 seconds or more and 10000 seconds or less,

Ms = 519 - 474 × [% C] - 30.4 × [% Mn] - 12.1 × [% Cr] - 7.5 × [% Mo] - 17.7 × [% Ni] - Tl/80

wherein [% C], [% Mn], [% Cr], [% Mo], and [% Ni] indicate contents (mass%) of C, Mn, Cr, Mo, and Ni, respectively, and are zero when the element is absent.


 
5. The method for manufacturing the high strength steel sheet according to claim 4, further comprising performing a coating treatment.
 




Drawing










Search report










Cited references

REFERENCES CITED IN THE DESCRIPTION



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Patent documents cited in the description




Non-patent literature cited in the description