WO2023048495A1 - Tôle d'acier laminée à froid à très haute résistance ayant une excellente extensibilité de trou et son procédé de fabrication - Google Patents

Tôle d'acier laminée à froid à très haute résistance ayant une excellente extensibilité de trou et son procédé de fabrication Download PDF

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WO2023048495A1
WO2023048495A1 PCT/KR2022/014244 KR2022014244W WO2023048495A1 WO 2023048495 A1 WO2023048495 A1 WO 2023048495A1 KR 2022014244 W KR2022014244 W KR 2022014244W WO 2023048495 A1 WO2023048495 A1 WO 2023048495A1
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steel sheet
rolled steel
excluding
cold
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PCT/KR2022/014244
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Korean (ko)
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구민서
김은영
김상현
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주식회사 포스코
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Priority to CN202280063997.8A priority Critical patent/CN117980524A/zh
Publication of WO2023048495A1 publication Critical patent/WO2023048495A1/fr

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    • 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
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • 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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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 an ultra-high strength cold-rolled steel sheet with excellent hole expandability and a method for manufacturing the same, and more specifically, to an ultra-high strength cold-rolled steel sheet with excellent hole expandability and a method for manufacturing the same, which can be mainly used for automobile collisions and structural members. .
  • the roll forming method which has higher productivity than general press forming and hot press forming, is a method of manufacturing complex shapes through multi-stage roll forming, and is usually applied to forming parts of ultra-high strength materials with low elongation, and its application is also It is an expanding trend.
  • Steel sheets applied to this roll forming method are mainly manufactured in continuous annealing facilities equipped with water cooling facilities.
  • workability is deteriorated and material variation by position occurs when roll forming is applied due to poor shape quality due to temperature deviations in the width and length directions during water cooling. Therefore, there is a need to devise an alternative to the rapid cooling method through water cooling.
  • One aspect of the present invention is to provide an ultra-high-strength cold-rolled steel sheet with excellent hole expandability and a method for manufacturing the same.
  • One embodiment of the present invention by weight%, C: 0.2 to 0.4%, Si: 0.5% or less (excluding 0%), Mn: 1.0 to 2.0%, P: 0.03% or less (excluding 0%), S : 0.015% or less (excluding 0%), Al: 0.1% or less (excluding 0%), Cr: 0.5% or less (excluding 0%), Mo: less than 0.2% (excluding 0%), Ti: 0.1 % or less (excluding 0%), Nb: 0.1% or less (excluding 0%), B: 0.005% or less (excluding 0%), N: 0.01% or less (excluding 0%), balance Fe and other unavoidable contains impurities, and the microstructure is composed of a tempered martensite single-phase structure or a martensite + tempered martensite mixed structure, and the microstructure has F HAGB of 60 area% or more per unit area 45 ⁇ m ⁇ 45 ⁇ m, L Provided is an ultra-high-strength cold-rolled steel sheet having excellent hole expandability having a HAGB of 8 mm or
  • F HAGB represents the fraction of crystal grains having a high angle grain boundary
  • L HAGB represents the total length of a grain boundary having a high angle grain boundary
  • the high angle grain boundary refers to a grain boundary having a discrepancy angle between adjacent crystal grains of 15° or more. meaning.
  • C 0.2 to 0.4%, Si: 0.5% or less (excluding 0%), Mn: 1.0 to 2.0%, P: 0.03% or less (excluding 0%), S : 0.015% or less (excluding 0%), Al: 0.1% or less (excluding 0%), Cr: 0.5% or less (excluding 0%), Mo: less than 0.2% (excluding 0%), Ti: 0.1 % or less (excluding 0%), Nb: 0.1% or less (excluding 0%), B: 0.005% or less (excluding 0%), N: 0.01% or less (excluding 0%), balance Fe and other unavoidable heating the steel slab containing impurities to a temperature of 1100 to 1300 ° C; Obtaining a hot-rolled steel sheet by finish hot-rolling the heated steel slab at a temperature of Ar3 or higher; winding the hot-rolled steel sheet at a temperature of 720° C.
  • an ultra-high-strength cold-rolled steel sheet having excellent hole expandability and tensile strength of 1470 MPa or more and a manufacturing method thereof.
  • Example 1 is a photograph of Inventive Example 5 and Comparative Example 5 according to an embodiment of the present invention observed with an optical microscope.
  • Example 2 is a photograph of analyzing high-angle grain boundaries and low-angle grain boundaries after measuring microstructures of Inventive Example 5 and Comparative Example 5 according to an embodiment of the present invention by electron backscattering diffraction attached to a scanning electron microscope.
  • C is an element added to secure the strength of martensite, and is preferably added in an amount of 0.2% or more for the above effect. However, if the content of C exceeds 0.4%, weldability may be deteriorated. Therefore, the content of C is preferably in the range of 0.2 to 0.4%.
  • the lower limit of the C content is more preferably 0.21%, and even more preferably 0.22%.
  • the upper limit of the C content is more preferably 0.3%, even more preferably 0.29%, and most preferably 0.28%.
  • Si 0.5% or less (excluding 0%)
  • the Si as a ferrite stabilizing element, has the disadvantage of weakening the strength by promoting the generation of ferrite during slow cooling after annealing in a continuous annealing furnace in which a slow cooling section exists.
  • the Si content is preferably in the range of 0.5% or less.
  • the Si content is more preferably 0.4% or less, and even more preferably 0.3% or less.
  • Mn is an element that inhibits ferrite formation and facilitates austenite formation.
  • Mn content is preferably in the range of 1.0 to 2.0%.
  • the lower limit of the Mn content is more preferably 1.3%, and even more preferably 1.5%.
  • P is an impurity element, and if its content exceeds 0.03%, it is preferable to limit the upper limit to 0.03% because weldability deteriorates, the risk of brittleness of steel increases, and the possibility of causing dent defects increases.
  • the P content is more preferably 0.025% or less, and even more preferably 0.02% or less.
  • S is an impurity element similar to P, and is an element that impairs the ductility and weldability of the steel sheet. If the content of S exceeds 0.015%, it is highly likely to impair the ductility and weldability of the steel sheet, so it is preferable to limit the upper limit to 0.015%.
  • the S content is more preferably 0.01% or less, and even more preferably 0.005% or less.
  • Al is an alloying element that expands the ferrite transformation period.
  • the upper limit is limited to 0.1%.
  • the Al content is more preferably 0.07% or less, and even more preferably 0.05% or less.
  • Cr is an alloying element that facilitates securing a low-temperature transformation structure by suppressing ferrite transformation, and has an advantage of suppressing ferrite formation when a continuous annealing process in which slow cooling is present is used as in the present invention.
  • the Cr content exceeds 0.5%, delayed fracture resistance may be deteriorated, and carbides such as CrC may be formed to impair hole expandability and bending workability, and costs may increase due to an excessive amount of alloy input. there is. Therefore, the Cr content is preferably in the range of 0.5% or less.
  • the Cr content is more preferably 0.4% or less, and even more preferably 0.3% or less.
  • Mo has an effect of improving the hardenability of steel, an effect of generating fine carbides containing Mo serving as a hydrogen trap site, and an effect of improving delayed fracture resistance by refining martensite.
  • the Mo content is preferably less than 0.2%.
  • the lower limit of the Mo content is more preferably 0.03%, more preferably 0.05%, and most preferably 0.1%.
  • Ti is a nitride-forming element that deposits N in steel as TiN and performs scavenging.
  • the Ti content exceeds 0.1%, the strength of martensite may be reduced by additional carbide precipitation in addition to the removal of dissolved N, and hole expandability and bending workability are improved by the formation of carbon nitrides such as TiC and TiN. can hinder Therefore, the Ti content is preferably in the range of 0.1% or less.
  • the Ti content is more preferably 0.07% or less, and even more preferably 0.05% or less. Meanwhile, for the scavenging effect and suppression of AlN formation, the Ti may be added in a chemical equivalent of 48/14*[N] or more.
  • Nb 0.1% or less (excluding 0%)
  • Nb is an element that is segregated at austenite grain boundaries and suppresses coarsening of austenite grains during annealing heat treatment.
  • the Nb content is preferably in the range of 0.1% or less.
  • the Nb content is more preferably 0.08% or less, and even more preferably 0.06% or less.
  • the B is an element that suppresses the formation of ferrite, and thus, in the present invention, there is an advantage of suppressing the formation of ferrite during cooling after annealing.
  • the content of B is preferably in the range of 0.005% or less.
  • the B content is more preferably 0.004% or less, and most preferably 0.003% or less.
  • N is an impurity element, and if its content exceeds 0.01%, it greatly increases the risk of cracking during playing due to AlN formation, so it is preferable to limit the upper limit to 0.01%.
  • the N content is more preferably 0.008% or less, and most preferably 0.006% or less.
  • the rest may include Fe and unavoidable impurities. Inevitable impurities can be unintentionally mixed in the normal steel manufacturing process, and cannot be completely excluded, and those skilled in the ordinary steel manufacturing field can easily understand the meaning. Further, the present invention does not entirely exclude the addition of other compositions than the aforementioned steel composition.
  • the cold-rolled steel sheet of the present invention may further include at least one of Cu: 0.5% or less and Ni: 0.5% or less.
  • the content of Cu is preferably in the range of 0.5% or less.
  • the Cu content is more preferably 0.4% or less, and even more preferably 0.3% or less.
  • Ni like Cu, also improves corrosion resistance and plays a role in reducing surface defects that tend to occur according to the addition of Cu.
  • the content of Ni is preferably in the range of 0.5% or less.
  • the Ni content is more preferably 0.4% or less, and even more preferably 0.3% or less.
  • cold-rolled steel sheet of the present invention may further include Sb: 0.05% or less.
  • Sb is an element that contributes to high strength and improvement of delayed fracture resistance by suppressing oxidation or nitrification of the surface layer.
  • the content of Sb is preferably in the range of 0.05% or less.
  • the Sb content is more preferably 0.04% or less, and even more preferably 0.03% or less.
  • the microstructure of the cold-rolled steel sheet of the present invention is preferably composed of a tempered martensite single-phase structure or a martensite + tempered martensite mixed structure.
  • the microstructure of the present invention is more preferably a tempered martensite single-phase structure, but may be composed of a martensite + tempered martensite mixed structure because tempering does not completely occur in the manufacturing process.
  • the fraction of the martensite + tempered martensite mixed structure is not particularly limited, but, for example, the mixed structure may have a tempered martensite fraction of 80 area% or more, more preferably 90 area% % or more.
  • the microstructure of the present invention preferably has an F HAGB of 60 area% or more and an L HAGB of 8 mm or more per unit area of 45 ⁇ m ⁇ 45 ⁇ m.
  • the F HAGB represents the fraction of crystal grains having a high angle grain boundary
  • L HAGB represents the total length of the grain boundary having a high angle grain boundary
  • the high angle grain boundary means that the discrepancy angle between adjacent crystal grains is 15° or more. means grain boundaries with When the F HAGB is less than 60 area% or the L HAGB is less than 8 mm, there is a disadvantage in that hole expandability is inferior.
  • the cold-rolled steel sheet of the present invention may have a prior-austenite average particle diameter of 6 ⁇ m or less.
  • the average particle diameter of prior austenite exceeds 6 ⁇ m, there may be disadvantages in that hole expandability and bending workability are inferior.
  • the cold-rolled steel sheet of the present invention provided as described above has a tensile strength (TS) of 1470 MPa or more, and a value of tensile strength (TS) (MPa) ⁇ hole expansion (HER) (%) of 73500 MPa % or more, High strength and excellent hole expandability can be secured at the same time.
  • TS tensile strength
  • HER hole expansion
  • a steel slab having the above-described alloy composition is heated to a temperature of 1100 to 1300 ° C. If the heating temperature is less than 1100 ° C, a problem occurs that the hot rolling load increases rapidly, and if it exceeds 1300 ° C, the amount of surface scale increases, which may lead to loss of material. Therefore, the heating temperature of the steel slab is preferably in the range of 1100 to 1300 °C.
  • the heated steel slab is finished hot-rolled at a temperature of Ar3 or higher to obtain a hot-rolled steel sheet.
  • the Ar3 temperature is a temperature at which ferrite begins to appear when austenite is cooled.
  • the finish rolling temperature is less than Ar3, two-phase or ferrite reverse rolling of ferrite + austenite is performed to create a mixed texture, and malfunction of the hot rolling equipment may be concerned due to fluctuations in the hot rolling load.
  • the finish hot rolling temperature is more preferably 800°C or higher, even more preferably 850°C or higher, and most preferably 900°C or higher.
  • the hot-rolled steel sheet is wound at a temperature of 720° C. or lower.
  • the coiling temperature exceeds 720° C., an excessive oxide film is formed on the surface of the steel sheet, which may cause defects.
  • the lower the coiling temperature the higher the strength of the hot-rolled steel sheet, and there is a disadvantage that the rolling load of the cold rolling, which is a subsequent process, increases.
  • the coiling temperature is more preferably 700°C or less, more preferably 680°C or less, and most preferably 650°C or less.
  • the coiled hot-rolled steel sheet is cold-rolled to obtain a cold-rolled steel sheet.
  • the cold rolling process is not particularly limited, and all processes commonly used in the art may be used. Meanwhile, a pickling process may be additionally performed before the cold rolling process.
  • the cold-rolled steel sheet is subjected to an annealing heat treatment in a temperature range of 780 to 900 ° C.
  • the annealing heat treatment temperature is less than 780° C.
  • strength may be reduced due to the formation of a large amount of ferrite.
  • material deviation may occur due to the temperature gradient of the top and end parts of the steel material of the present invention.
  • the annealing heat treatment temperature exceeds 900 ° C., durability of the continuous annealing furnace is deteriorated, which may cause difficulties in product production. Therefore, the annealing heat treatment temperature preferably has a range of 780 ⁇ 900 °C.
  • the lower limit of the annealing heat treatment temperature is more preferably 800°C, more preferably 820°C, and most preferably 840°C.
  • the upper limit of the annealing heat treatment temperature is more preferably 880°C, and even more preferably 860°C.
  • a continuous annealing furnace has a slow cooling section after annealing heat treatment. That is, after the above-described annealing heat treatment process, slow cooling is performed for a certain period.
  • a continuous annealing furnace that usually includes a slow cooling section, there is a slow cooling section of 100 to 200 m after annealing, and as a soft phase such as ferrite is formed by slow cooling after annealing at high temperature, There are disadvantages that make manufacturing difficult.
  • the time maintained in the slow cooling section is 60 seconds, and the annealing temperature is 830 ° C and the end of the slow cooling section is maintained.
  • the temperature is 650 ° C
  • the cooling rate in the slow cooling section is very low at 3 ° C / s. For this reason, the possibility of producing a soft phase such as ferrite is very high.
  • an additional cooling device must be introduced in order to increase the cooling rate at the time of slow cooling after the annealing to be higher than 5° C./sec, problems such as manufacturing cost or equipment replacement may occur.
  • the present invention rapidly cools the slowly cooled cold-rolled steel sheet to 150° C. or less at a cooling rate of 40° C./s or more.
  • the microstructure may be transformed into martensite through the quenching process. If the quenching rate is less than 40 °C / s or the quenching end temperature exceeds 150 °C, martensitic transformation is not sufficiently achieved, and it may be difficult to secure the microstructure to be obtained by the present invention.
  • the quenching rate is more preferably 50 °C/s or more, more preferably 60 °C/s or more, and most preferably 70 °C/s or more.
  • the quenching end temperature is more preferably 140°C or less, and even more preferably 130°C or less.
  • the quenched cold-rolled steel sheet is subjected to reheating and overaging heat treatment at 180 to 240 ° C.
  • reheating and overaging heat treatment martensite obtained through the above-described rapid cooling process may be transformed into tempered martensite.
  • the lower limit of the reheating and overaging heat treatment temperatures is more preferably 190°C, and even more preferably 200°C.
  • the upper limit of the reheating and overaging heat treatment temperatures is more preferably 230°C, and even more preferably 220°C.
  • the overaging heat treatment may be performed for 400 seconds or more.
  • the overaging heat treatment time is less than 400 seconds, tempering is not sufficiently performed, resulting in low yield strength.
  • the overaging heat treatment time is not particularly limited, but it is difficult to exceed 1000 seconds due to the nature of the continuous annealing equipment.
  • the lower limit of the overaging heat treatment time is more preferably 500 seconds, and more preferably 600 seconds.
  • Fm (Fk x 10 6 )/((0.67n + z) x V 2 ).
  • Fm is the average particle diameter of old austenite
  • Fk is the total area of the microstructure picture
  • Z is the number of crystal grains entering the inside of the circle
  • n is the number of crystal grains spanning the circle
  • V is the magnification when measuring the microstructure .
  • F HAGB and L HAGB measured the microstructure within a measurement area of 45 ⁇ m ⁇ 45 ⁇ m and a measurement interval of 0.75 ⁇ m using electron backscatter diffraction (EBSD), and then determined the criticality using TSL-OIM software. It was analyzed based on the value of 15 ⁇ .
  • EBSD electron backscatter diffraction
  • Tensile strength (TS) and yield strength (YS) were measured by taking a tensile test piece of JIS No. 5 size in the direction perpendicular to the rolling direction and conducting a tensile test at a strain rate of 0.01/s.
  • Hole expansion ratio was measured according to the ISO 16630 standard. The size of the specimen was 120 mm ⁇ 120 mm, and the initial hole diameter was 10 mm based on the clearance 12% standard. The punching holding load was 20 ton and the test speed was 12 mm/min.
  • R/t bending characteristics
  • the R/t value was obtained by dividing the minimum bending radius (R) at which this does not occur by the thickness (t) of the test piece.
  • FIG. 1 is a photograph of Inventive Example 5 and Comparative Example 5 observed under an optical microscope. As can be seen from FIG. 1, in the case of Inventive Example 5, the average particle diameter of prior austenite is fine, whereas in the case of Comparative Example 5, it can be seen that the average particle diameter of prior austenite is relatively large.
  • FIG. 2 is a photograph of analyzing high-angle grain boundaries and low-angle grain boundaries after measuring microstructures of Inventive Example 5 and Comparative Example 5 by electron backscattering diffraction attached to a scanning electron microscope.
  • FIG. 2 in the case of Inventive Example 5, F HAGB and L HAGB have high values, whereas in Comparative Example 5, it can be seen that they are at a low level.

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Abstract

La présente invention concerne une tôle d'acier laminée à froid à très haute résistance ayant une excellente extensibilité de trou et son procédé de fabrication et, plus particulièrement, une tôle d'acier laminée à froid à très haute résistance ayant une excellente extensibilité de trou qui peut être principalement utilisée pour des éléments structuraux et pour assurer une sécurité en cas de collision d'automobile, et son procédé de fabrication.
PCT/KR2022/014244 2021-09-23 2022-09-23 Tôle d'acier laminée à froid à très haute résistance ayant une excellente extensibilité de trou et son procédé de fabrication WO2023048495A1 (fr)

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CN202280063997.8A CN117980524A (zh) 2021-09-23 2022-09-23 扩孔性优异的超高强度冷轧钢板及其制造方法

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KR1020210125545A KR102568217B1 (ko) 2021-09-23 2021-09-23 구멍확장성이 우수한 초고강도 냉연강판 및 그 제조방법
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EP3950975A4 (fr) * 2019-03-29 2022-12-14 Nippon Steel Corporation Tôle d'acier

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KR20200121872A (ko) * 2018-03-29 2020-10-26 닛폰세이테츠 가부시키가이샤 핫 스탬프 성형체
KR20200062428A (ko) * 2018-11-26 2020-06-04 현대제철 주식회사 냉연 도금 강판 및 그 제조방법
CN113166828A (zh) * 2018-12-18 2021-07-23 安赛乐米塔尔公司 经冷轧和热处理的钢板及其制造方法
CN111748745A (zh) * 2019-03-29 2020-10-09 宝山钢铁股份有限公司 780MPa级具有较高成形性的冷轧热镀锌双相钢及其制造方法
WO2021070951A1 (fr) * 2019-10-10 2021-04-15 日本製鉄株式会社 Feuille d'acier laminée à froid et son procédé de fabrication

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