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WO2017203994A1 - Tôle d'acier revêtue et son procédé de fabrication - Google Patents

Tôle d'acier revêtue et son procédé de fabrication Download PDF

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Publication number
WO2017203994A1
WO2017203994A1 PCT/JP2017/017912 JP2017017912W WO2017203994A1 WO 2017203994 A1 WO2017203994 A1 WO 2017203994A1 JP 2017017912 W JP2017017912 W JP 2017017912W WO 2017203994 A1 WO2017203994 A1 WO 2017203994A1
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WIPO (PCT)
Prior art keywords
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steel sheet
average
volume fraction
grain size
Prior art date
Application number
PCT/JP2017/017912
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English (en)
Japanese (ja)
Inventor
克利 ▲高▼島
央海 澤西
公一 谷口
崇 小林
哲哉 田川
池田　倫正
Original Assignee
Ｊｆｅスチール株式会社
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Ｊｆｅスチール株式会社 filed Critical Ｊｆｅスチール株式会社
Priority to KR1020187033519A priority Critical patent/KR102145293B1/ko
Priority to JP2017544984A priority patent/JP6424967B2/ja
Priority to CN201780029820.5A priority patent/CN109154045B/zh
Priority to MX2018014261A priority patent/MX2018014261A/es
Publication of WO2017203994A1 publication Critical patent/WO2017203994A1/fr

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese

Definitions

  • the present invention relates to a plated steel sheet and a method for manufacturing the same, and particularly to a plated steel sheet suitable as a member of a structural component such as an automobile.
  • Patent Document 1 discloses a technique for improving delayed fracture resistance (hydrogen embrittlement resistance) by controlling an iron-based carbide containing Si or Si and Al in a steel sheet structure.
  • Patent Document 2 discloses a technique for improving surface cracks during resistance welding by controlling the amounts of Si, Al, and Mn added.
  • Patent Document 1 not only does the iron-based carbide become a hydrogen trap site, but it does not have an effect of improving resistance welding cracking resistance, and the iron-based carbide exists at the grain boundary. This may promote cracking during resistance welding. Moreover, with the technique described in Patent Document 2, it is difficult to achieve a high strength of 980 MPa or more, and it is difficult to obtain excellent delayed fracture resistance. In this way, it is difficult to improve both delayed fracture resistance and resistance weld cracking resistance in a plated steel sheet of 980 MPa or more, and these characteristics can be achieved even if steel sheets other than plated steel sheets are included. The actual situation is that no steel plate has been developed.
  • high strength steel sheets used for automobile structural members and reinforcing members are concerned about delayed fracture (hydrogen embrittlement) due to invading hydrogen due to the environment of use.
  • high strength steel plates are often combined with press-formed parts by resistance welding (spot welding).
  • spot welding resistance welding
  • the present invention has been made in view of such circumstances, and solves the problems in the prior art, and provides a plated steel sheet excellent in delayed fracture resistance and resistance weld crack resistance, and a method for producing the same. With the goal.
  • the inventors of the present invention have made extensive studies in order to improve both delayed fracture resistance and resistance weld cracking resistance.
  • the volume fraction of the steel sheet structure of ferrite, retained austenite, martensite, bainite, and non-recrystallized ferrite is controlled at a specific ratio, and the average crystal grain size of each steel sheet structure is refined, It has been found that excellent delayed fracture resistance and resistance weld cracking characteristics can be obtained by producing fine carbides of Ti or Nb.
  • the present invention is based on the above findings.
  • Delayed fracture occurs when hydrogen enters the steel sheet and cracks are generated and propagated.
  • a hot-dip galvanized steel sheet that can also be used as a thin steel sheet for automobiles
  • the coating may be scratched for some reason and the surface of the ground iron may be exposed.
  • generation of hydrogen is accelerated on the iron surface because zinc becomes an anode and iron becomes a cathode. Therefore, in the plated steel sheet, it is necessary to consider the delayed fracture characteristics of the steel sheet, not the components and composition of the plating layer.
  • the resistance welding crack in the present invention indicates this inner crack.
  • this inner crack occurs, there is a concern that the fatigue strength of the welded portion is particularly reduced. Therefore, it is necessary to avoid this internal crack when used for an automobile or the like.
  • Observation of the inner crack revealed that cracks due to intergranular fracture occurred in the place where the martensite single phase was formed after welding of the heat affected zone (HAZ).
  • Fine Ti or Nb carbides not only serve as hydrogen trap sites, but also suppress nucleation of ferrite and austenite during recrystallization during annealing, and promote nucleation of ferrite and austenite.
  • the component composition further includes: % By mass V: 0.10% or less, Cu: 0.50% or less, Ni: 0.50% or less, Mo: 0.50% or less, Cr: 0.80% or less 2.
  • Hot-rolled steel sheet is subjected to hot rolling at a temperature of 850 ° C or higher and 950 ° C or lower,
  • the hot-rolled steel sheet is cooled to 680 ° C. or less at a first average cooling rate of 75 ° C./s or more, and is cooled to a range of 400 ° C. or more and 580 ° C. or less at a second average cooling rate of 5 ° C./s or more.
  • Winding, cold rolling to make a cold rolled steel sheet The cold-rolled steel sheet is heated to a temperature range of 760 ° C. to 900 ° C. at an average heating rate of 3 to 30 ° C./s, and is soaked for 15 seconds or more in the temperature range of 760 ° C.
  • Annealing to cool to a temperature range of 600 ° C or lower at an average cooling rate of 3-30 ° C / s, A method for producing a plated steel sheet, wherein the cold-rolled steel sheet after annealing is plated.
  • the component composition further includes: % By mass V: 0.10% or less, Cu: 0.50% or less, Ni: 0.50% or less, Mo: 0.50% or less, Cr: 0.80% or less Ca and / or REM: The manufacturing method of the plated steel plate of said 3 containing the 1 type (s) or 2 or more types chosen from 0.0050% or less.
  • the present invention has an extremely high tensile strength and has excellent delayed fracture resistance that does not cause delayed fracture due to hydrogen entering from the environment even after being molded into a member. Excellent resistance to weld cracking.
  • % representing the content of each component element means “% by mass” unless otherwise specified.
  • C 0.05% or more and 0.22% or less C is an element effective for increasing the strength of a steel sheet, and the formation of the second phase (structure other than ferrite as the first phase) of bainite, martensite and retained austenite in the present invention. Contribute. If it is less than 0.05%, it is difficult to ensure the strength because necessary bainite, martensite, and retained austenite volume fraction are difficult to ensure. Preferably it is 0.06% or more. More preferably, it is 0.065% or more. On the other hand, if added excessively, the hardness after resistance welding becomes high, the toughness at the time of resistance welding decreases, and the resistance weld cracking characteristics deteriorate, so the content is made 0.22% or less. Preferably it is 0.20% or less, More preferably, it is 0.18% or less.
  • Si 0.05% or more and 1.80% or less Si is an element effective for increasing strength by strengthening ferrite in solid solution.
  • addition of 0.05% or more is necessary.
  • it is 0.10% or more. More preferably, it is 0.20% or more.
  • the content is made 1.80% or less.
  • it is 1.60% or less. More preferably, it is 1.50% or less.
  • Mn 1.45% or more and 3.35% or less
  • Mn is an element that contributes to high strength by strengthening solid solution and generating the second phase. Moreover, it is an element that stabilizes austenite, and is an element necessary for controlling the fraction of the second phase. In order to acquire the effect, it is necessary to contain 1.45% or more. Preferably it is 1.60% or more. More preferably, it is 1.80% or more. On the other hand, if it is contained excessively, the volume fraction of the second phase becomes excessive, and if hydrogen penetrates into the steel sheet, the slip constraint at the grain boundary increases and cracks at the grain boundary tend to progress. Therefore, the delayed fracture resistance is deteriorated. Therefore, the content is made 3.35% or less. Preferably it is 3.20% or less. More preferably, it is 3.0% or less.
  • P 0.05% or less P contributes to strengthening by solid solution strengthening, but if added excessively, segregation at the grain boundary becomes remarkable and the grain boundary becomes brittle, so resistance weld cracking characteristics Decreases. Therefore, the content is 0.05% or less. Preferably it is 0.04% or less. More preferably, it is 0.03% or less. Although there is no particular lower limit, it is preferable to contain 0.0005% or more because extremely low P increases the steelmaking cost. More preferably, it is 0.0008% or more.
  • the upper limit of the content is made 0.005%.
  • it is 0.0045% or less. More preferably, it is 0.004% or less.
  • the extremely low S content is preferably 0.0002% or more because steelmaking costs increase in the same manner as P. More preferably, it is 0.0004% or more.
  • Al 0.01% or more and 0.10% or less
  • Al is an element necessary for deoxidation, and in order to obtain this effect, it is necessary to contain 0.01% or more. Preferably it is 0.015% or more. On the other hand, if the content exceeds 0.10%, the effect is saturated, so the content is made 0.10% or less. Preferably it is 0.06% or less. More preferably, it is 0.05% or less.
  • N 0.010% or less Since N forms coarse nitrides and deteriorates delayed fracture resistance, the content must be suppressed. In particular, when N exceeds 0.010%, this tendency becomes remarkable, so the N content is set to 0.010% or less. Preferably it is 0.008% or less. More preferably, it is 0.006% or less.
  • B 0.0002% or more and 0.0045% or less B is an element that improves the hardenability, contributes to high strength by generating the second phase, ensures hardenability, and does not lower the martensitic transformation start point. Moreover, since the grain boundary strength is improved by segregating at the grain boundaries, it is effective for delayed fracture resistance. In order to exert this effect, 0.0002% or more is contained. Preferably it is 0.0003% or more. However, excessive addition degrades the resistance weld cracking characteristics in order to degrade toughness, so the content is made 0.0045% or less. Preferably it is 0.0035% or less. More preferably, it is 0.0030% or less.
  • Ti is an element that can contribute to strength increase by forming fine carbonitride.
  • the fine carbonitride of Ti serves as a hydrogen trap site and is effective in reducing resistance weld cracking because it is effective in refining crystal grains.
  • the lower limit of the Ti content is set to 0.005%.
  • a preferred lower limit is 0.008%.
  • a more preferred lower limit is 0.010%.
  • the content is made 0.090% or less. Preferably it is 0.080% or less.
  • Nb as well as Ti, forms fine carbonitrides, which contributes to strength increase and also serves as a hydrogen trap site and is effective for crystal grain refinement.
  • the lower limit of the Nb content is set to 0.005%.
  • a preferred lower limit is 0.008%.
  • a more preferred lower limit is 0.010%.
  • the content is 0.090% or less.
  • it is 0.080% or less. More preferably, it is 0.070% or less.
  • the basic components of the present invention have been described above.
  • the balance other than the above components is Fe and unavoidable impurities, but in the present invention, one or more of the following components may be added in addition to the above basic components.
  • V 0.10% or less
  • V can contribute to an increase in strength by forming fine carbonitrides.
  • the V content is preferably 0.10% or less. More preferably, it is 0.08% or less.
  • Cu 0.50% or less
  • Cu is an element that contributes to strengthening by solid solution strengthening and contributes to strengthening by forming a second phase, and can be added as necessary. In order to exhibit such an effect, it is preferable to make it contain 0.05% or more. More preferably, it is 0.08% or more. On the other hand, even if the content exceeds 0.50%, the effect is saturated and surface defects due to Cu are likely to occur. Therefore, the content is preferably 0.50% or less. More preferably, it is 0.35% or less.
  • Ni 0.50% or less
  • Ni is an element that contributes to strengthening by solid solution strengthening and also contributes to strengthening by generating a second phase. It can be added as necessary. it can. In order to exhibit such an effect, it is preferable to make it contain 0.05% or more. More preferably, it is 0.08% or more. Moreover, since it has the effect of suppressing the surface defect resulting from Cu when it adds simultaneously with Cu, it is effective at the time of Cu addition. On the other hand, since the effect is saturated even if the content exceeds 0.50%, the content is preferably 0.50% or less. More preferably, it is 0.35% or less.
  • Mo 0.50% or less
  • Mo is an element that contributes to increasing the strength by generating the second phase, and further contributes to increasing the strength by generating some carbides, and can be added as necessary. In order to exhibit such an effect, it is preferable to make it contain 0.05% or more. More preferably, it is 0.08% or more. On the other hand, since the effect is saturated even if the content exceeds 0.50%, the content is preferably 0.50% or less. More preferably, it is 0.35% or less.
  • Cr 0.80% or less Cr is an element that contributes to increasing the strength by generating the second phase, and can be added as necessary. In order to exhibit such an effect, it is preferable to make it contain 0.10% or more. More preferably, it is 0.13% or more. On the other hand, if the content exceeds 0.80%, the hot dip galvanizing property is deteriorated so that plating is not performed. Therefore, the content is made 0.80% or less. More preferably, it is 0.70% or less.
  • Ca and / or REM 0.0050% or less in total (combined)
  • Ca and REM rare earth elements
  • the content exceeds 0.0050%, the effect is saturated, so the content is made 0.0050% or less. More preferably, it is 0.0035% or less.
  • the remainder other than the above shall be Fe and inevitable impurities.
  • Inevitable impurities include, for example, Sb, Zn, Co, Sn, Zr, etc.
  • the allowable ranges of these contents are Sb: 0.01% or less, Zn: 0.01% or less, Co: 0.10% or less, Sn: 0.10% or less, Zr: 0.10% or less.
  • Ta and Mg are contained within the range of the normal steel composition, the effect is not lost.
  • ferrite has a volume fraction of 35% to 70%
  • residual austenite has a volume fraction of 12% or less (including 0%)
  • martensite has a volume fraction of 15% to 60%
  • the balance is bainite.
  • the average crystal grain size of ferrite With a volume fraction of 30% or less (including 0%) and unrecrystallized ferrite with a volume fraction of 5% or less (including 0%), the average crystal grain size of ferrite being 5 ⁇ m or less, and retained austenite
  • the average crystal grain size is 2 ⁇ m or less
  • the average crystal grain size of martensite is 2 ⁇ m or less
  • the average crystal grain size of bainite is 3 ⁇ m or less.
  • the volume fraction described here is the volume fraction with respect to the entire steel sheet, and so on.
  • the volume fraction of ferrite is 70% or less. Preferably it is 65% or less, More preferably, it is 60% or less. In addition, when the volume fraction is less than 35%, the second phase having a high dislocation density increases, so that the delayed fracture resistance is deteriorated. Therefore, the volume fraction of ferrite is 35% or more. In order to improve elongation, it is preferably made 40% or more.
  • the crystal grain size of ferrite is 5 ⁇ m or less.
  • the thickness is preferably 4 ⁇ m or less. In order to improve the elongation, the thickness is preferably 0.5 ⁇ m or more.
  • Residual austenite is less than 12% in volume fraction. Residual austenite contributes to strength by transformation-induced martensite transformation. Further, since it becomes a hydrogen trap site, it is also effective for delayed fracture resistance. However, when martensitic transformation is performed, a high dislocation density is maintained, so that cracks are generated due to hydrogen penetration, and the delayed fracture resistance is inferior. Therefore, the volume fraction of retained austenite is 12% or less. Preferably it is more than 0% and 10% or less. More preferably, it is 1% or more. More preferably, it is 7% or less. The volume fraction of retained austenite may be 0%.
  • the average grain size of retained austenite is 2 ⁇ m or less.
  • the average grain size of retained austenite is affected by the C distribution in retained austenite, which tends to generate martensite during press molding, resulting in reduced delayed fracture resistance.
  • the upper limit is 2 ⁇ m.
  • the lower limit is not particularly specified, but if it is 0.3 ⁇ m or more, the contribution to elongation becomes large, so 0.3 ⁇ m or more is preferable.
  • Martensite volume fraction 15% or more and 60% or less In order to secure the desired strength, the martensite volume fraction should be 15% or more. Preferably it is 20% or more. More preferably, it is 23% or more. On the other hand, when the volume fraction of martensite is more than 60%, not only is crack formation easy at the time of hydrogen intrusion, but the crack growth rate increases, so the upper limit is made 60%. Preferably it is 57% or less. More preferably, it is 55% or less.
  • the average grain size of martensite is 2 ⁇ m or less If the average grain size of martensite is more than 2 ⁇ m, the crystal grains are further coarsened during resistance welding, resulting in deterioration of toughness and internal cracks. Therefore, the average crystal grain size of martensite is 2 ⁇ m or less. Preferably, it is 1.8 ⁇ m or less.
  • the martensite here refers to martensite generated after annealing, but it has undergone martensite transformation during cooling of the annealing, self-tempered (autotempered) martensite, tempered martensite after martensitic transformation. , And fresh martensite which has been martensitic transformed from austenite without tempering.
  • bainite contributes to high strength, it includes high dislocation density, so if the volume fraction exceeds 30%, delayed fracture resistance deteriorates. Therefore, the upper limit is 30%. Preferably it is more than 0% and 25% or less. More preferably, it is 5% or more. More preferably, it is 20% or less.
  • the volume fraction of bainite may be 0%.
  • the average crystal grain size of bainite is 3 ⁇ m or less. If the average grain size of bainite is more than 3 ⁇ m, the grain size is further coarsened during resistance welding, resulting in toughness deterioration and internal cracking. And Preferably it is 2.5 ⁇ m or less.
  • Non-recrystallized ferrite as a balance is 5% or less in volume fraction. Moreover, unrecrystallized ferrite also contributes to increase in strength, but the upper limit is 5% because it contains a high dislocation density like bainite. Preferably it is more than 0% and 3% or less. More preferably, it is 1% or less. The volume fraction of non-recrystallized ferrite may be 0%.
  • pearlite in addition to ferrite, bainite, martensite, retained austenite and non-recrystallized ferrite, pearlite may be generated, but the volume of the above ferrite, bainite, martensite, retained austenite and unrecrystallized ferrite.
  • the effect of the present invention can be obtained if the fraction, the average crystal grain size of ferrite, bainite, martensite and retained austenite, and the distribution state of Ti or Nb-based precipitates (carbides) satisfy the ranges specified as the present invention. be able to.
  • the volume fraction of pearlite is preferably 5% or less, more preferably 3% or less.
  • an average of 30 or more Ti or Nb precipitates having an average particle size of 0.10 ⁇ m or less per 100 ⁇ m 2
  • an average of 30 or more Ti or Nb precipitates having an average particle size of 0.10 ⁇ m or less per 100 ⁇ m 2 It is necessary to contain. This is because Ti or Nb-based precipitates serve as hydrogen trap sites to improve delayed fracture resistance and are effective for refinement of crystal grains, and to improve resistance weld cracking resistance.
  • the particle size exceeds 0.10 ⁇ m, or the average number of the precipitates is less than 30 per 100 ⁇ m 2 , the delayed fracture resistance and resistance weld cracking characteristics deteriorate.
  • the number is preferably 50 or more per 100 ⁇ m 2 . More preferably, the number is 60 or more per 100 ⁇ m 2 .
  • Specific examples of Ti or Nb-based precipitates include carbides.
  • a steel slab having the above component composition (chemical component) is hot-rolled at a finish rolling end temperature of 850 ° C. or higher and 950 ° C. or lower, and the first average cooling rate of 75 ° C./s or higher as the primary cooling is 680 ° C.
  • the cold-rolled steel sheet After cooling to below °C, after winding in the range of 400 °C to 580 °C at the second average cooling rate of 5 °C / s or more as secondary cooling, after pickling the hot-rolled steel sheet, Subsequently, cold rolling is performed, and then in the annealing step, the cold-rolled steel sheet is heated to a temperature range of 760 ° C to 900 ° C at an average heating rate of 3 to 30 ° C / s, and the first soaking temperature is 760 ° C or higher. Hold for 15 seconds or more in a temperature range of 900 ° C or lower, cool to 600 ° C or lower at an average cooling rate of 3 to 30 ° C / s, anneal, and then hot dip galvanize and cool to room temperature.
  • the steel slab is cast and then hot rolled at 1150 ° C or higher and 1300 ° C or lower without reheating, or reheated to 1150 ° C or higher and 1300 ° C or lower, and then hot rolled. It is preferable to start.
  • the steel slab to be used is preferably produced by a continuous casting method in order to prevent macro segregation of components, but can also be produced by an ingot casting method or a thin slab casting method.
  • after manufacturing the steel slab after cooling to room temperature and then reheating it, without cooling, it is charged in a heating furnace as it is without being cooled, or after heat retention Energy-saving processes such as direct rolling and direct rolling, in which rolling is performed immediately or after casting, can be applied without problems.
  • Hot rolling process ⁇ Finish rolling finish temperature: 850 ° C or more and 950 ° C or less Hot rolling improves the delayed fracture resistance after annealing and resistance weld cracking resistance by homogenizing the structure in the steel sheet and reducing material anisotropy. It is necessary to finish in the austenite single phase region. Therefore, the finish rolling end temperature is set to 850 ° C. or higher. On the other hand, when the finish rolling finish temperature exceeds 950 ° C., the hot rolled structure becomes coarse, and the crystal grains after annealing also become coarse. Therefore, the finish rolling end temperature is set to 850 ° C. or higher and 950 ° C. or lower.
  • the steel sheet structure after annealing is controlled by controlling the precipitation form of Ti or Nb precipitates during hot rolling, so cooling after finish rolling is an important process. is there. After the hot rolling is completed, austenite undergoes ferrite transformation in the cooling process, but the ferrite becomes coarse at high temperatures.
  • the primary cooling is performed at a first average cooling rate of 75 ° C./s or higher to 680 ° C. or lower.
  • the temperature cooled by the primary cooling exceeds 680 ° C., pearlite in the steel sheet structure of the hot-rolled steel sheet is excessively generated and the steel sheet structure becomes inhomogeneous, so that the resistance weld cracking resistance is deteriorated.
  • a desired average crystal grain size cannot be obtained for martensite.
  • it is set to 650 ° C. or lower.
  • the temperature is preferably set to 400 ° C. or higher.
  • the subsequent secondary cooling is performed at a second average cooling rate of 5 ° C./s or more to a range of 400 ° C. or more and 580 ° C. or less. Cooling to less than 5 ° C / s or more than 580 ° C results in excessive formation of ferrite or pearlite in the steel sheet structure of the hot-rolled steel sheet, resulting in a decrease in resistance weld cracking characteristics after annealing. Further, with respect to martensite, a desired average crystal grain size cannot be obtained, and an average of 30 or more Ti or Nb-based precipitates having an average crystal grain size of 0.10 ⁇ m or less per 100 ⁇ m 2 cannot be obtained. Preferably, it is 10 ° C./s or more. Further, since Ti and Nb are excessively dissolved, it is preferably set to 65 ° C./s or less.
  • the upper limit of the winding temperature is preferably 580 ° C. More preferably, it is 550 ° C or lower.
  • the winding temperature is preferably 400 ° C. or higher. More preferably, it is set to 420 ° C. or higher.
  • the pickling step is not particularly limited, and may be performed according to a conventional method.
  • Cold rolling process A cold rolling process is performed in which the sheet is rolled into a cold-rolled sheet having a predetermined thickness.
  • a cold rolling process is not specifically limited, What is necessary is just to implement by a conventional method.
  • a preferable range of the rolling reduction in the cold rolling is 30% or more and 95% or less.
  • ⁇ Average heating rate 3-30 °C / s
  • the average heating rate is 3 to 30 ° C./s, it becomes possible to refine the crystal grains after annealing. When heated rapidly, recrystallization hardly proceeds. Also, the desired average crystal grain size cannot be obtained for bainite, the desired volume fraction for unrecrystallized ferrite, and Ti or Nb-based precipitates with an average crystal grain size of 0.10 ⁇ m or less are 30 per 100 ⁇ m 2 on average. I can't get more. Therefore, the upper limit of the average heating rate is 30 ° C./s. Since non-recrystallized ferrite increases, the temperature is preferably 25 ° C./s or less.
  • the heating rate is too low, the ferrite and martensite grains become coarse and a predetermined average particle diameter cannot be obtained. Further, an average of 30 or more Ti or Nb-based precipitates having an average crystal grain size of 0.10 ⁇ m or less cannot be obtained per 100 ⁇ m 2 . Therefore, an average heating rate of 3 ° C./s or more is necessary. Preferably it is 5 degrees C / s or more.
  • -Soaking temperature (holding temperature): 760 ° C or more and 900 ° C or less Soaking temperature is soaked in the temperature range of two phases of ferrite and austenite or single phase of austenite. If it is less than 760 ° C., the ferrite fraction increases and it becomes difficult to ensure the strength. Also, the desired average crystal grain size cannot be obtained for ferrite and martensite. Therefore, the lower limit of the soaking temperature is 760 ° C. Preferably, the temperature is 780 ° C or higher. If the soaking temperature is too high, the crystal grain growth of ferrite, martensite and austenite becomes remarkable, and the resistance of the resistance weld cracking property decreases due to the coarsening of the crystal grains.
  • the upper limit of soaking temperature is set to 900 ° C. Preferably it is 880 degrees C or less.
  • the soaking time needs to be maintained for 15 seconds or more in order to carry out austenite transformation for the progress and part or all of recrystallization. Since the volume ratio of non-recrystallized ferrite increases, it is preferably set to 20 seconds or more.
  • the upper limit is not particularly limited, but is preferably within 600 seconds.
  • the average cooling rate exceeds 30 ° C./s, not only is martensite generated excessively, but it is also difficult to realize this in terms of equipment. Further, when the cooling stop temperature exceeds 600 ° C., pearlite is excessively generated, so that a predetermined volume fraction in the microstructure of the steel sheet cannot be obtained, and it is difficult to ensure strength. Further, 30 or more Ti or Nb-based precipitates having an average crystal grain size of 0.10 ⁇ m or less cannot be obtained on average per 100 ⁇ m 2 , and the delayed fracture resistance and resistance weld cracking characteristics deteriorate.
  • the above average cooling rate is an average of cooling rates in the range of 600 ° C. or less until dipping in the plating bath, and it is only necessary to maintain an average cooling rate of 3 to 30 ° C./s in this temperature range. .
  • a plating process After the annealing, a plating process is performed and the temperature is cooled to room temperature.
  • the plating process include a hot dip galvanizing process and an electrogalvanizing process.
  • the temperature of the steel sheet immersed in the plating bath is preferably (hot dip galvanizing bath temperature ⁇ 40) ° C. to (hot dip galvanizing bath temperature + 50) ° C. If the temperature of the steel sheet immersed in the plating bath is below (hot dip galvanizing bath temperature ⁇ 40) ° C., when the steel plate is immersed in the plating bath, a part of the molten zinc solidifies and deteriorates the plating appearance. There is.
  • the lower limit is (hot dip galvanizing bath temperature ⁇ 40) ° C. Moreover, since the temperature of a plating bath will rise when the steel plate temperature immersed in a plating bath exceeds (hot-dip galvanization bath temperature +50) degreeC, a problem arises in mass productivity. About other conditions, the conditions currently performed by the normal plating process can be used.
  • the plating can be alloyed in a temperature range of 450 ° C. or higher and 600 ° C. or lower.
  • the Fe concentration during plating becomes 7 to 15% by mass, and the adhesion of plating and the corrosion resistance after coating are improved.
  • the temperature is lower than 450 ° C, alloying does not proceed sufficiently, leading to a decrease in sacrificial anticorrosive action and a decrease in slidability.
  • the alloying proceeds excessively and the powdering resistance decreases. .
  • Other production method conditions are not particularly limited, but from the viewpoint of productivity, the series of treatments such as annealing, plating treatment, and alloying treatment of plating are performed by continuous melting when performing hot dip galvanizing treatment. It is preferable to carry out in a galvanizing line (CGL). In addition, it is preferable to use a galvanizing bath containing 0.10 to 0.20% by mass of Al for hot dip galvanizing. After plating, wiping can be performed to adjust the amount of plating.
  • CGL galvanizing line
  • wiping can be performed to adjust the amount of plating.
  • the cold-rolled steel sheet thus obtained was subjected to an annealing treatment in accordance with the production conditions shown in Table 2 in a continuous hot dip galvanizing line, and after the hot dip galvanizing treatment, an alloying treatment was further performed at a temperature shown in Table 2.
  • An alloyed hot-dip galvanized steel sheet (GA) was obtained.
  • the plating treatment is as follows: zinc plating bath temperature: 460 ° C., zinc plating bath Al concentration: 0.14 mass% (when alloying treatment is performed), 0.18 mass% (when alloying treatment is not performed), plating adhesion per side The amount was 45 g / m 2 (double-sided plating).
  • Some of the steel sheets were made of non-alloyed hot dip galvanized steel sheets (GI) without being alloyed by galvanization.
  • a JIS No. 5 tensile test piece was taken from the manufactured steel sheet so that the direction perpendicular to the rolling direction was the longitudinal direction (tensile direction), and the tensile strength (TS) was measured by a tensile test (JIS Z2241 (1998)).
  • TS tensile strength
  • JIS Z2241 1998
  • the obtained cold-rolled steel sheet was cut into 30 mm x 100 mm with the rolling direction as the longitudinal direction, and the end face was ground and the specimen was bent 180 ° with a curvature radius of 10 mm at the punch tip. gave.
  • resistance welding spot welding
  • spot welding was performed using a test piece cut into 50 ⁇ 150 mm with the direction perpendicular to the rolling direction of the obtained cold-rolled steel sheet as the longitudinal direction.
  • Welding is performed by spot spot welding with the plate assembly tilted 4 ° using a servo motor pressurization type single phase direct current (50Hz) resistance welder attached to the welding gun. Carried out.
  • the welding conditions were a pressure of 3.5 kN and a hold time of 0.36 seconds.
  • the welding current and welding time were adjusted so that the nugget diameter was 5.9 mm.
  • After welding cut the test piece in half and observe the cross-section with an optical microscope. Good resistance to resistance cracking of cracks with no cracks of 0.2 mm or more ( ⁇ ), cracks of 0.2 mm or more The resistance resistance cracking resistance was inferior (x).
  • the volume fraction of ferrite, martensite, and non-recrystallized ferrite in the steel sheet is 2000 times using SEM (scanning electron microscope) after corroding the plate thickness section parallel to the rolling direction of the steel sheet and then corroding with 3vol% nital.
  • the area ratio was measured by a point count method (according to ASTM E562-83 (1988)), and the area ratio was defined as the volume fraction.
  • the average grain size of ferrite and martensite is calculated by taking the images of each ferrite and martensite crystal grains that have been identified in advance from steel sheet structure images using Media-Cybernetics Image-Pro. The circle equivalent diameter was calculated and the values were averaged.
  • the volume fraction of retained austenite was determined by diffracting X-ray intensities on a 1/4 plane of the plate thickness after polishing the steel plate to 1/4 plane in the thickness direction.
  • the X-ray diffraction method device: RINT2200 made by Rigaku
  • the ⁇ 200 ⁇ plane, ⁇ 211 ⁇ plane, ⁇ 220 ⁇ plane of iron ferrite and austenite Measure the integrated intensity of X-ray diffraction lines on the ⁇ 200 ⁇ , ⁇ 220 ⁇ , and ⁇ 311 ⁇ planes of the X-ray diffraction handbook (2000)
  • the volume fraction of retained austenite was obtained from the calculation formula described in p.26, 62-64.
  • the average grain size of retained austenite was observed at a magnification of 5000 using EBSD (electron beam backscattering diffraction method), the equivalent circle diameter was calculated using Image-Pro, and the values were averaged. Asked. Further, the steel sheet structure was observed by SEM, TEM (transmission electron microscope), and FE-SEM (field emission scanning electron microscope), and bainite was observed to obtain the volume fraction in the same manner as described above. The average crystal grain size of bainite was also calculated by calculating the equivalent circle diameter from the steel sheet structure photograph using the above-mentioned Image-Pro and averaging these values.
  • EBSD electron beam backscattering diffraction method
  • the particle size of Ti or Nb-based precipitates is observed by using SEM and TEM at magnifications of 5000, 10000, and 20000, and using Image-Pro, the particle equivalent diameter is calculated by calculating the equivalent circle diameter. It was. The number of Ti or Nb-based precipitates was observed using SEM and TEM at magnifications of 5000, 10000, and 20000, and the average number of 10 locations was determined.
  • Table 3 shows the measured tensile properties, delayed fracture resistance, resistance weld cracking characteristics, and steel sheet structure measurement results. From the results shown in Table 3, in all of the inventive examples, ferrite having an average crystal grain size of less than 5 ⁇ m is 35 to 70% in volume fraction, and residual austenite having an average crystal grain size of 2 ⁇ m or less is 12% or less in volume fraction. Martensite with an average particle size of 2 ⁇ m or less is 15 to 60% by volume, bainite with an average particle size of 3 ⁇ m or less is 30% or less, and unrecrystallized ferrite is 5% or less by volume.

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Abstract

La présente invention vise à fournir une tôle d'acier revêtue possédant une résistance à la traction extrêmement élevée et une excellente résistance à la rupture différée et une suppression de la fissuration lors de soudage par résistance. À cet effet, l'invention concerne une tôle d'acier revêtue: qui a une structure comportant 35 % à 70 % de ferrite en fraction volumique, pas plus de 12 % d'austénite retenue en fraction volumique, 15 % à 60 % de martensite en fraction volumique, et pour le reste, pas plus de 30 % de bainite en fraction volumique et pas plus de 5 % de ferrite non recristallisée en fraction volumique; la taille moyenne des grains cristallins de la ferrite étant égale ou inférieure à 5 µm, la taille moyenne des grains cristallins de l'austénite retenue étant égale ou inférieure à 2 µm, la taille moyenne des grains cristallins de la martensite étant égale ou inférieure à 2 µm, et la taille moyenne des grains cristallins de la bainite étant égale ou inférieure à 3 µ m; et la structure contenant, en moyenne, au moins 30 grains pour 100 µm 2 de dépôts de Ti ou Nb ayant une taille de grain moyenne égale ou inférieure à 0,10 µm.
PCT/JP2017/017912 2016-05-25 2017-05-11 Tôle d'acier revêtue et son procédé de fabrication WO2017203994A1 (fr)

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JP2022520485A (ja) * 2019-02-18 2022-03-30 タタ、スティール、アイモイデン、ベスローテン、フェンノートシャップ 機械的特性が改善された高強度鋼
US11326226B2 (en) 2020-09-01 2022-05-10 Hyundai Steel Company Material for hot stamping and method for manufacturing the same
US20220275471A1 (en) * 2019-08-06 2022-09-01 Jfe Steel Corporation High-strength thin steel sheet and method for manufacturing same
CN115244201A (zh) * 2020-05-08 2022-10-25 日本制铁株式会社 热轧钢板及其制造方法
JP2023538652A (ja) * 2020-09-01 2023-09-08 ヒュンダイ スチール カンパニー ホットスタンピング用素材及びその製造方法
JP2023540210A (ja) * 2020-09-01 2023-09-22 ヒュンダイ スチール カンパニー ホットスタンピング用素材及びその製造方法
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WO2021020439A1 (fr) * 2019-07-31 2021-02-04 Ｊｆｅスチール株式会社 Tôle d'acier à haute résistance, élément à haute résistance, et procédés respectifs pour fabrication de ces produits
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WO2020145108A1 (fr) * 2019-01-09 2020-07-16 Ｊｆｅスチール株式会社 Tôle d'acier laminée à froid à résistance élevée et procédé pour sa production
US12241137B2 (en) 2019-01-09 2025-03-04 Jfe Steel Corporation High-strength cold-rolled steel sheet and production method for same
JP2022520485A (ja) * 2019-02-18 2022-03-30 タタ、スティール、アイモイデン、ベスローテン、フェンノートシャップ 機械的特性が改善された高強度鋼
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US20220275471A1 (en) * 2019-08-06 2022-09-01 Jfe Steel Corporation High-strength thin steel sheet and method for manufacturing same
CN115244201A (zh) * 2020-05-08 2022-10-25 日本制铁株式会社 热轧钢板及其制造方法
CN115244201B (zh) * 2020-05-08 2023-05-12 日本制铁株式会社 热轧钢板及其制造方法
US11326226B2 (en) 2020-09-01 2022-05-10 Hyundai Steel Company Material for hot stamping and method for manufacturing the same
US11898218B2 (en) 2020-09-01 2024-02-13 Hyundai Steel Company Material for hot stamping and method for manufacturing the same
JP2023540210A (ja) * 2020-09-01 2023-09-22 ヒュンダイ スチール カンパニー ホットスタンピング用素材及びその製造方法
JP2023538652A (ja) * 2020-09-01 2023-09-08 ヒュンダイ スチール カンパニー ホットスタンピング用素材及びその製造方法
JP7684385B2 (ja) 2020-09-01 2025-05-27 ヒュンダイ スチール カンパニー ホットスタンピング用素材及びその製造方法
US12312652B2 (en) 2020-09-01 2025-05-27 Hyundai Steel Company Material for hot stamping and method of manufacturing the same
JP7684386B2 (ja) 2020-09-01 2025-05-27 ヒュンダイ スチール カンパニー ホットスタンピング用素材及びその製造方法

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