WO2006118425A1 - Feuille d’acier laminee a froid ayant une formabilite superieure et un rapport de rendement eleve et son procede de production - Google Patents

Feuille d’acier laminee a froid ayant une formabilite superieure et un rapport de rendement eleve et son procede de production Download PDF

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WO2006118425A1
WO2006118425A1 PCT/KR2006/001670 KR2006001670W WO2006118425A1 WO 2006118425 A1 WO2006118425 A1 WO 2006118425A1 KR 2006001670 W KR2006001670 W KR 2006001670W WO 2006118425 A1 WO2006118425 A1 WO 2006118425A1
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Prior art keywords
steel sheet
rolled steel
less
cold rolled
precipitates
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PCT/KR2006/001670
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English (en)
Inventor
Jeong-Bong Yoon
Noi-Ha Cho
Jin-Hee Chung
Man-Young Park
Kwang-Geun Chin
Sang-Ho Han
Sung-Il Kim
Ho-Seok Kim
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Posco
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Priority claimed from KR1020050129237A external-priority patent/KR100723163B1/ko
Application filed by Posco filed Critical Posco
Priority to US11/913,175 priority Critical patent/US20090126837A1/en
Priority to MX2007013676A priority patent/MX2007013676A/es
Priority to EP06732897.1A priority patent/EP1888800B1/fr
Priority to JP2008509936A priority patent/JP4954981B2/ja
Publication of WO2006118425A1 publication Critical patent/WO2006118425A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • C21D11/00—Process control or regulation for heat treatments
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper

Definitions

  • the present invention relates to niobium (Nb) and titanium (Ti) -added interstitial free (IF) cold rolled steel sheets that are used as materials for automobiles, household electronic appliances, etc. More specifically, the present invention relates to highly formable IF cold rolled steel sheets whose yield strength is enhanced due to the distribution of fine precipitates, and a process for producing the IF cold rolled steel sheets.
  • cold rolled steel sheets for use in automobiles and household electronic appliances are required to have excellent room-temperature aging resistance and bake hardenability, together with high strength and superior formability.
  • Aging is a strain aging phenomenon that arises from hardening caused by dissolved elements, such as C and N, fixed to dislocations. Since aging causes defect, called “stretcher strain", it is important to secure excellent room-temperature aging resistance.
  • Bake hardenability means increase in strength due to the presence of dissolved carbon after press formation, followed by painting and drying, by leaving a slight small amount of carbon in a solid solution state. Steel sheets with excellent bake hardenability can overcome the difficulties of press formability resulting from high strength.
  • Room-temperature aging resistance and bake hardenability can be imparted to aluminum (Al) -killed steels by batch annealing of the Al-killed steels.
  • Al-killed steels have a bake hardening (BH) value (a difference in yield strength before and after painting) of 10-20 MPa, which demonstrates that an increase in yield strength is low.
  • BH bake hardening
  • interstitial free (IF) steels with excellent room-temperature aging resistance and bake hardenability have been developed by adding carbide and nitride-forming elements, such as Ti and Nb, followed by continuous annealing.
  • Japanese Unexamined Patent Publication No. Sho 57-041349 describes an enhancement in the strength of a Ti-based IF steel by adding 0.4-0.8% of manganese (Mn) and 0.04-0.12% of phosphorus (P).
  • Mn manganese
  • P phosphorus
  • Japanese Unexamined Patent Publication No. Hei 5-078784 describes an enhancement in strength by the addition of Mn as a solid solution strengthening element in an amount exceeding 0.9% and not exceeding 3.0%.
  • Korean Patent Laid-open No. 2003-0052248 describes an improvement in secondary working embrittlement resistance as well as strength and workability by the addition of 0.5-2.0% of Mn instead of P, together with aluminum (Al) and boron (B) .
  • Japanese Unexamined Patent Publication No. Hei 10-158783 describes an enhancement in strength by reducing the content of P and using Mn and Si as solid solution strengthening elements.
  • Mn is used in an amount of up to 0.5%
  • Al as a deoxidizing agent is used in an amount of 0.1%
  • nitrogen (N) as an impurity is limited to 0.01% or less. If the Mn content is increased, the plating characteristics are worsened.
  • Japanese Unexamined Patent Publication No. Hei 6-057336 discloses an enhancement in the strength of an IF steel by adding 0.5-2.5% of copper (Cu) to form ⁇ -Cu precipitates. High strength of the IF steel is achieved due to the presence of the ⁇ -Cu precipitates, but the workability of the IF steel is worsened.
  • Japanese Unexamined Patent Publication Nos. Hei 6-240365 and Hei 7-216340 describe the addition of a combination of Cu and P to improve the corrosion resistance of baking hardening type IF steels. According to these publications, Cu is added in an amount of 0.05-1.0% to ensure improved corrosion resistance. However, in actuality, Cu is added in an excessively large amount of 0.2% or more. Japanese Unexamined Patent Publication Nos.
  • Hei 10- 280048 and Hei 10-287954 suggest the dissolution of carbosulfide (Ti-C-S based) in a carbide at the time of reheating and annealing to obtain a solid solution in crystal grain boundaries, thereby achieving a bake hardening (BH) value (a difference in yield strength before and after baking) of 30 MPa or more.
  • BH bake hardening
  • a cold rolled steel sheet which has a composition comprising 0.01% or less of C, 0.01-0.2% of Cu, 0.01-0.3% of Mn, 0.005- 0.08% of S, 0.1% or less of Al, 0.004-0.02% of N, 0.2% or less of P, 0.0001-0.002% of B, 0.002-0.04% of Nb, 0.005-0.15% of Ti, by weight, and the balance of Fe and other unavoidable impurities wherein the composition satisfies the following relationships: 1 ⁇ (Mn/55 + Cu/63.5) / (S * /32) ⁇ 30, 1 ⁇
  • the steel sheet comprises (Mn, Cu) S and AlN precipitates having an average size of 0.2 ⁇ m or less.
  • the cold rolled steel sheets of the present invention have characteristics of soft cold rolled steel sheets of the order of 280 MPa and high-strength cold rolled steel sheets of the order of 340 MPa or more.
  • soft cold rolled steel sheets of the order of 280 MPa are produced.
  • the soft cold rolled steel sheets further contain at least one solid solution strengthening element selected from Si and Cr, or the P content is in the range of 0.015-0.2%, a high strength of 340 MPa or more is attained.
  • the P content in the high-strength steels containing P alone is preferably in the range of 0.03% to 0.2%.
  • the Si content in the high-strength steels is preferably in the range of 0.1 to 0.8%.
  • the Cr content in the high-strength steels is preferably in the range of 0.2 to 1.2.
  • the P content may be freely designed in an amount of 0.2% or less.
  • the cold rolled steel sheets of the present invention may further contain 0.01-0.2 wt% of Mo.
  • a process for producing the cold rolled steel sheets comprising reheating a slab satisfying one of the compositions to a temperature of 1,100 0 C or higher, hot rolling the reheated slab at a finish rolling temperature of the Ar 3 transformation point or higher to provide a hot rolled steel sheet, cooling the hot rolled steel sheet at a rate of 300 °C/min., winding the cooled steel sheet at 700 0 C or lower, cold rolling the wound steel sheet, and continuously annealing the cold rolled steel sheet.
  • Fine precipitates having a size of 0.2 ⁇ m or less are distributed in the cold rolled steel sheets of the present invention.
  • examples of such precipitates include MnS precipitates, CuS precipitates, and composite precipitates of
  • the yield strength of the IF steels is enhanced and the in-plane anisotropy index of the IF steels is lowered, thus leading to an improvement in workability.
  • the present invention has been achieved based on this finding.
  • the precipitates used in the present invention have drawn little attention in conventional
  • the precipitates have not been actively used from the viewpoint of yield strength and in- plane anisotropy index.
  • the dissolved carbon is present in a larger amount in the crystal grain boundaries than within the crystal grains, thus achieving excellent room-temperature non- aging properties. Since the dissolved carbon present within the crystal grains can more freely migrate, it binds to movable dislocations, thus affecting the room-temperature aging properties. In contrast, the dissolved carbon segregated in stable positions, such as in the crystal grain boundaries and in the vicinity of the precipitates, is activated at a high temperature, for example, a temperature for painting/baking treatment, thus affecting the bake hardenability.
  • the fine precipitates distributed in the steel sheets of the present invention have a positive influence on the increase of yield strength arising from precipitation enhancement, improvement in strength-ductility balance, in- plane anisotropy index, and plasticity anisotropy.
  • the fine (Mn, Cu) S precipitates and AlN precipitates must be uniformly distributed.
  • contents of components affecting the precipitation, composition between the components, production conditions, and particularly cooling rate after hot rolling have a great influence on the distribution of the fine precipitates.
  • the content of carbon (C) is preferably limited to 0.01% or less.
  • Carbon (C) affects the room-temperature aging resistance and bake hardenability of the cold rolled steel sheets. When the carbon content exceeds 0.01%, the addition of the expensive agents Nb and Ti is required to remove the remaining carbon, which is economically disadvantageous and is undesirable in terms of formability. When it is intended to achieve room-temperature aging resistance only, it is preferred to maintain the carbon content at a low level, which enables the reduction of the amount of the expensive agents Nb and Ti added. When it is intended to ensure desired bake hardenability, the carbon is preferably added in an amount of 0.001% or more, and more preferably 0.005% to 0.01%. When the carbon content is less than 0.005%, room-temperature aging resistance can be ensured without increasing the amounts of Nb and Ti.
  • the content of copper (Cu) is preferably in the range of 0.01-0.2%.
  • Copper serves to form fine CuS precipitates, which make the crystal grains fine. Copper lowers the in-plane anisotropy index of the cold rolled steel sheets and enhances the yield strength of the cold rolled steel sheets by precipitation promotion.
  • the Cu content In order to form fine precipitates, the Cu content must be 0.01% or more. When the Cu content is more than 0.2%, coarse precipitates are obtained.
  • the Cu content is more preferably in the range of 0.03 to 0.2%.
  • the content of manganese (Mn) is preferably in the range of 0.01-0.3%.
  • Manganese serves to precipitate sulfur in a solid solution state in the steels as MnS precipitates, thereby preventing occurrence of hot shortness caused by the dissolved sulfur, or is known as a solid solution strengthening element. From such a technical standpoint, manganese is generally added in a large amount. The present inventors have found that when the manganese content is reduced and the sulfur content is optimized, very fine MnS precipitates are obtained. Based on this finding, the manganese content is limited to 0.3% or less. In order to ensure this characteristic, the manganese content must be 0.01% or more. When the manganese content is less than 0.01%, i.e. the sulfur content remaining in a solid solution state is high, hot shortness may occur.
  • Mn content is within the range of 0.01 to 0.12%.
  • the content of sulfur (S) is preferably limited to 0.08% or less.
  • S Sulfur
  • Cu and/or MnS precipitates reacts with Cu and/or Mn to form CuS and MnS precipitates, respectively.
  • the sulfur content is greater than 0.08%, the proportion of dissolved sulfur is increased. This increase of dissolved sulfur greatly deteriorates the ductility and formability of the steel sheets and increases the risk of hot shortness.
  • a sulfur content of 0.005% or more is preferred.
  • the content of aluminum (Al) is preferably limited to 0.1% or less.
  • Aluminum reacts with nitrogen (N) to form fine AlN precipitates, thereby completely preventing aging by dissolved nitrogen.
  • N nitrogen
  • the nitrogen content is 0.004% or more, AlN precipitates are sufficiently formed.
  • the distribution of the fine AlN precipitates in the steel sheets allows the formation of minute crystal grains and enhances the yield strength of the steel sheets by precipitation enhancement.
  • a more preferable Al content is in the range of 0.01 to 0.1%.
  • the content of nitrogen (N) is preferably limited to 0.02% or less.
  • nitrogen is added in an amount of up to 0.02%. Otherwise, the nitrogen content is controlled to 0.004% or less. When the nitrogen content is less than 0.004%, the number of the AlN precipitates is small, and therefore, the minuteness effects of crystal grains and the precipitation enhancement effects are negligible. In contrast, when the nitrogen content is greater than 0.02%, it is difficult to guarantee aging properties by use of dissolved nitrogen.
  • the content of phosphorus (P) is preferably limited to 0.2% or less.
  • Phosphorus is an element that has excellent solid solution strengthening effects while allowing a slight reduction in r-value. Phosphorus guarantees high strength of the steel sheets of the present invention in which the precipitates are controlled. It is desirable that the phosphorus content in steels requiring a strength of the order of 280 MPa be defined to 0.015% or less. It is desirable that the phosphorus content in high-strength steels of the order of 340 MPa be limited to a range exceeding 0.015% and not exceeding 0.2%. A phosphorus content exceeding 0.2% can lead to a reduction in ductility of the steel sheets. Accordingly, the phosphorus content is preferably limited to a maximum of 0.2%. When Si and Cr are added in the present invention, the phosphorus content can be appropriately controlled to be 0.2% or less to achieve the desired strength.
  • the content of boron (B) is preferably in the range of 0.0001 to 0.002%. Boron is added to prevent occurrence of secondary working embrittlement . To this end, a preferable boron content is 0.0001% or more. When the boron content exceeds 0.002%, the deep drawability of the steel sheets may be markedly deteriorated.
  • the content of niobium (Nb) is preferably in the range of 0 . 002 to 0 . 04% .
  • Nb is added for the purpose of ensuring the non-aging properties and improving the formability of the steel sheets.
  • Nb which is a potent carbide-forming element
  • NbC precipitates permit the steel sheets to be well textured during annealing, thus greatly improving the deep drawability of the steel sheets.
  • the NbC precipitates are obtained in very small amounts. Accordingly, the steel sheets are not well textured and thus there is little improvement in the deep drawability of the steel sheets.
  • the Nb content exceeds 0.04%
  • the NbC precipitates are obtained in very large amounts. Accordingly, the deep drawability and elongation of the steel sheets are lowered, and thus the formability of the steel sheets may be markedly deteriorated.
  • the content of titanium (Ti) is preferably in the range of 0.005 to 0.15%.
  • Titanium is added for the purpose of ensuring the non- aging properties and improving the formability of the steel sheets.
  • Ti which is a potent carbide-forming element, is added to steels to form TiC precipitates in the steels.
  • the TiC precipitates allow the precipitation of dissolved carbon to ensure non-aging properties .
  • the content of Ti added is less than 0.005%, the TiC precipitates are obtained in very small amounts. Accordingly, the steel sheets are not well textured and thus there is little improvement in the deep drawability of the steel sheets.
  • the titanium is added in an amount exceeding 0.15%, very large TiC precipitates are formed. Accordingly, minuteness effects of crystal grains are reduced, resulting in high in-plane anisotropy index, reduction of yield strength and marked worsening of plating characteristics.
  • S * which is determined by Relationship 2, represents the content of sulfur that does not react with Ti and thereafter reacts with Cu.
  • the value of (Cu/63.5) /(S * /32) be equal to or greater than 1. If the value of (Cu/63.5) /(S * /32) is greater than 30, coarse CuS precipitates are distributed, which is undesirable.
  • the value of (Cu/63.5) / (S * /32) is preferably in the range of 1 to 20, more preferably 1 to 9, and most preferably 1 to 6. 1 ⁇ (Mn/55 + Cu/63.5 ) / (S * /32 ) ⁇ 30 ( 3 )
  • Relationship 3 is associated with the formation of
  • (Mn, Cu) S precipitates are obtained.
  • a more preferable value of (Cu/63.5) / (S * /32) is preferably in the range of 1 to 20, more preferably 1 to 9, and most preferably
  • Cu is more preferably 0.05-0.4%.
  • the reason for this limitation to the sum of Mn and Cu is to obtain fine (Mn, Cu) S precipitates. 1 ⁇ (Al/27)/(N * /14) ⁇ 10 (4)
  • N * N - 0.8 x (Ti - 0.8 x (48/32) x S)) x (14/48) (5)
  • Relationship 4 is associated with the formation of fine
  • N * which is determined by Relationship 5
  • the value of (Al/27) / (N * /14) be in the range of 1-10.
  • the value of (Al/27) / (N * /14) be in the range of 1-10.
  • (Al/27) /(N * /14) must be 1 or greater. If the value of (Al/27) /(N * /14) is greater than 10, coarse AlN precipitates are obtained and thus poor workability and low yield strength are caused. It is preferred that the value of (Al/27) / (N * /14) be in the range of 1 to 6.
  • the steel sheet comprises at least one kind selected from MnS, CuS, MnS and AlN precipitates having an average size of 0.2 ⁇ m or less. That is, one or more kinds selected from the group consisting of 0.01-0.2% of Cu, 0.01-0.3% of Mn and 0.004-0.2% of N lead to various combinations of (Mn, Cu) S and AlN precipitates having a size not greater than 0.2 ⁇ m.
  • carbon is precipitated into NbC and TiC forms .
  • the room- temperature aging resistance and bake hardenability of the steel sheets are affected depending on the conditions of dissolved carbon under which NbC and TiC precipitates are not obtained. Taking into account these requirements, it is most preferred that the Nb, Ti and C contents satisfy the following relationships .
  • Ti * Ti - 0.8 x ((48/14) x N + (48/32) x S) (7)
  • Relationship 6 is associated with the formation of NbC and TiC precipitates to remove the carbon in a solid solution state, thereby achieving room-temperature non-aging properties.
  • Ti * which is determined by Relationship 7, represents the content of titanium that reacts with N and S and thereafter reacts with C.
  • Relationship 8 is associated with the achievement of bake hardenability.
  • Cs which is expressed in ppm by Relationship 8, represents the content of dissolved carbon that is not precipitated into NbC and TiC forms.
  • the Cs value In order to achieve a high bake hardening value, the Cs value must be 5 ppm or more. If the Cs value exceeds 30 ppm, the content of dissolved carbon is increased, making it difficult to attain room-temperature non-aging properties . It is advantageous that the fine precipitates are uniformly distributed in the compositions of the present invention. It is preferable that the precipitates have an average size of 0.2 ⁇ m or less.
  • the precipitates when the precipitates have an average size greater than 0.2 ⁇ m, the steel sheets have poor strength and low in-plane anisotropy index. Further, large amounts of precipitates having a size of 0.2 ⁇ m or less are distributed in the compositions of the present invention. While the number of the distributed precipitates is not particularly limited, it is more advantageous with higher number of the precipitates.
  • the number of the distributed precipitates is preferably 1 x 10 5 /mm 2 or more, more preferably 1 x 10 6 /mm 2 or more, and most preferably 1 x 10 7 /mm 2 or more.
  • the plasticity-anisotropy index is increased and the in-plane anisotropy index is lowered with increasing number of the precipitates, and as a result, the workability is greatly improved. It is commonly known that there is a limitation in increasing the workability because the in-plane anisotropy index is increased with increasing plasticity-anisotropy index. It is worth noting that as the number of the precipitates distributed in the steel sheets of the present invention increases, the plasticity-anisotropy index of the steel sheets is increased and the in-plane anisotropy index of the steel sheets is lowered.
  • the steel sheets of the present invention in which the fine precipitates are formed satisfy a yield ratio (yield strength/tensile strength) of 0.58 or higher.
  • the steel sheets of the present invention When the steel sheets of the present invention are applied to high-strength steel sheets, they may further contain at least one solid solution strengthening element selected from P, Si and Cr.
  • P solid solution strengthening element
  • Si solid solution strengthening element
  • the content of silicon (Si) is preferably in the range of 0.1 to 0.8%.
  • Si is an element that has solid solution strengthening effects and shows a slight reduction in elongation. Si guarantees high strength of the steel sheets of the present invention in which the precipitates are controlled. Only when the Si content is 0.1% or more, high strength can be ensured. However, when the Si content is more than 0.8%, the ductility of the steel sheets is deteriorated.
  • the content of chromium (Cr) is preferably in the range of 0.2 to 1.2%.
  • Cr is an element that has solid solution strengthening effects, lowers the secondary working embrittlement temperature, and lowers the aging index due to the formation of Cr carbides.
  • Cr guarantees high strength of the steel sheets of the present invention in which the precipitates are controlled and serves to lower the in-plane anisotropy index of the steel sheets. Only when the Cr content is 0.2% or more, high strength can be ensured. However, when the Cr content exceeds 1.2%, the ductility of the steel sheets is deteriorated.
  • the cold rolled steel sheets of the present invention may further contain molybdenum (Mo) .
  • the content of molybdenum (Mo) in the cold rolled steel sheets of the present invention is preferably in the range of 0.01 to 0.2%. Mo is added as an element that increases the plasticity- anisotropy index of the steel sheets. Only when the molybdenum content is not lower than 0.01%, the plasticity- anisotropy index of the steel sheets is increased. However, when the molybdenum content exceeds 0.2%, the plasticity- anisotropy index is not further increased and there is a danger of hot shortness.
  • the process of the present invention is characterized in that a steel satisfying one of the steel compositions defined above is processed through hot rolling and cold rolling to form precipitates having an average size of 0.2 ⁇ m or less in a cold rolled sheet.
  • the average size of the precipitates in the cold rolled plate is affected by the design of the steel composition and the processing conditions, such as reheating temperature and winding temperature. Particularly, cooling rate after hot rolling has a direct influence on the average size of the precipitates.
  • Hot rolling conditions such as reheating temperature and winding temperature.
  • a steel satisfying one of the compositions defined above is reheated, and is then subjected to hot rolling.
  • the reheating temperature is preferably 1,100 0 C or higher.
  • the hot rolling is performed at a finish rolling temperature not lower than the Ar 3 transformation point.
  • the finish rolling temperature is lower than the Ar 3 transformation point, rolled grains are created, which deteriorates the workability and causes poor strength.
  • the cooling is preferably performed at a rate of 300 °C/min or higher before winding and after hot rolling.
  • the composition of the components is controlled to obtain fine precipitates, the precipitates may have an average size greater than 0.2 um at a cooling rate of less than 300 °C/min. That is, as the cooling rate is increased, many nuclei are created and thus the size of the precipitates becomes finer and finer. Since the size of the precipitates is decreased with increasing cooling rate, it is not necessary to define the upper limit of the cooling rate.
  • the cooling rate is preferably in the range of 300-1000 °C/min.
  • winding is performed at a temperature not higher than 700 0 C.
  • the winding temperature is higher than 700 0 C, the precipitates are grown too coarsely, thus making it difficult to ensure high strength.
  • the steel is cold rolled at a reduction rate of 50-90%. Since a cold reduction rate lower than 50 % leads to creation of a small amount of nuclei upon annealing recrystallization, the crystal grains are grown excessively upon annealing, thereby coarsening of the crystal grains recrystallized through annealing, which results in reduction of the strength and formability. A cold reduction rate higher than 90 % leads to enhanced formability, while creating an excessively large amount of nuclei, so that the crystal grains recrystallized through annealing become too fine, thus deteriorating the ductility of the steel. Continuous annealing
  • Continuous annealing temperature plays an important role in determining the mechanical properties of the final product.
  • the continuous annealing is preferably performed at a temperature of 700 to 900 0 C.
  • the continuous annealing is performed at a temperature lower than 700 0 C, the recrystallization is not completed and thus a desired ductility cannot be ensured.
  • the continuous annealing is performed at a temperature higher than 900 0 C, the recrystallized grains become coarse and thus the strength of the steel is deteriorated.
  • the continuous annealing is maintained until the steel is completely recrystallized.
  • the recrystallization of the steel can be completed for about 10 seconds or more.
  • the continuous annealing is preferably performed for 10 seconds to 30 minutes .
  • the aging index of the steel sheets is defined as a yield point elongation measured by annealing each of the samples, followed by 1.0% skin pass rolling and thermally processing at 100 0 C for 2 hours.
  • the bake hardening (BH) value of the standard samples was measured by the following procedure. After a 2% strain was applied to each of the samples, the strained sample was annealed at 17O 0 C for 20 minutes . The yield strength of the annealed sample was measured. The BH value was calculated by subtracting the yield strength measured before annealing from the yield strength value measured after annealing.
  • Example 1 steel slabs were prepared in accordance with the compositions shown in the following tables.
  • the steel slabs were reheated and finish hot-rolled to provide hot rolled steel sheets.
  • the hot rolled steel sheets were cooled at a rate of 400 °C/min., wound at 650 0 C, cold-rolled at a reduction rate of 75%, followed by continuous annealing to produce cold rolled steel sheets.
  • the finish hot rolling was performed at 910 0 C, which is above the Ar3 transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830 0 C for 40 seconds to produce the final cold rolled steel sheets.
  • YS Yield strength
  • TS Tensile Strength
  • El Elongation
  • r m Plasticity-anisotropy index
  • ⁇ r In-plane anisotropy index
  • AI Aging
  • steel slabs were prepared in accordance with the compositions shown in the following tables.
  • the steel slabs were reheated and finish hot-rolled to provide hot rolled steel sheets.
  • the hot rolled steel sheets were cooled at a rate of 400 °C/min., wound at 650 0 C, cold-rolled at a reduction rate of 75%, followed by continuous annealing to produce cold rolled steel sheets.
  • the finish hot rolling was performed at 910 0 C, which is above the Ar 3 transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830 0 C for 40 seconds to produce the final cold rolled steel sheets.
  • YS Yield strength
  • TS Tensile Strength
  • El Elongation
  • r m Plasticity-anisotropy index
  • ⁇ r In-plane anisotropy index
  • SWE Secondary Working Embrittlement
  • AI Aging Index
  • IS Inventive Steel
  • CS Comparative steel
  • steel slabs were prepared in accordance with the compositions shown in the following tables.
  • the steel slabs were reheated and finish hot-rolled to provide hot rolled steel sheets.
  • the hot rolled steel sheets were cooled at a rate of 400 °C/min., wound at 650 0 C, cold-rolled at a reduction rate of 75%, followed by continuous annealing to produce cold rolled steel sheets.
  • the finish hot rolling was performed at 91O 0 C, which is above the Ar 3 transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830 0 C for 40 seconds to produce the final cold rolled steel sheets.
  • YS Yield strength
  • TS Tensile Strength
  • El Elongation
  • r m Plasticity-anisotropy index
  • ⁇ r In-plane anisotropy index
  • SWE Secondary Working Embrittlement
  • AI Aging Index
  • IS Inventive Steel
  • CS Comparative steel
  • steel slabs were prepared in accordance with the compositions shown in the following tables.
  • the steel slabs were reheated and finish hot-rolled to provide hot rolled steel sheets.
  • the hot rolled steel sheets were cooled at a rate of 400 °C/min., wound at 650 0 C, cold-rolled at a reduction rate of 75%, followed by continuous annealing to produce cold rolled steel sheets.
  • the finish hot rolling was performed at 910 0 C, which is above the Ar 3 transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830 0 C for 40 seconds to produce the final cold rolled steel sheets .
  • Example 5 steel slabs were prepared in accordance with the compositions shown in the following tables.
  • the steel slabs were reheated and finish hot-rolled to provide hot rolled steel sheets.
  • the hot rolled steel sheets were cooled at a rate of 400 °C/min., wound at 65O 0 C, cold-rolled at a reduction rate of 75%, followed by continuous annealing to produce cold rolled steel sheets.
  • the finish hot rolling was performed at 910 0 C, which is above the Ar 3 transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830 0 C for 40 seconds to produce the final cold rolled steel sheets.
  • YS Yield strength
  • TS Tensile Strength
  • El Elongation
  • r m Plasticity-anisotropy index
  • ⁇ r In-plane anisotropy index
  • AI Aging Index
  • SWE Secondary Working Embrittlement
  • IS Inventive Steel
  • CS Comparative steel
  • steel slabs were prepared in accordance with the compositions shown in the following tables.
  • the steel slabs were reheated and finish hot-rolled to provide hot rolled steel sheets.
  • the hot rolled steel sheets were cooled at a rate of 400 °C/min., wound at 650 0 C, cold-rolled at a reduction rate of 75%, followed by continuous annealing to produce cold rolled steel sheets.
  • the finish hot rolling was performed at 910 0 C, which is above the Ar 3 transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 83O 0 C for 40 seconds to produce the final cold rolled steel sheets.
  • YS Yield strength
  • TS Tensile Strength
  • El Elongation
  • r m Plasticity-anisotropy index
  • ⁇ r In-plane anisotropy index
  • SWE Secondary Working Embrittlement
  • AI Aging Index
  • IS Inventive Steel
  • CS Comparative steel
  • steel slabs were prepared in accordance with the compositions shown in the following tables .
  • the steel slabs were reheated and finish hot-rolled to provide hot rolled steel sheets.
  • the hot rolled steel sheets were cooled at a rate of 400 °C/min., wound at 65O 0 C, cold-rolled at a reduction rate of 75%, followed by continuous annealing to produce cold rolled steel sheets.
  • the finish hot rolling was performed at 910 0 C, which is above the Ar 3 transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830 0 C for 40 seconds to produce the final cold rolled steel sheets.
  • YS Yield strength
  • TS Tensile Strength
  • El Elongation
  • r ra Plasticity-anisotropy index
  • ⁇ r In-plane anisotropy index
  • AI Aging Index
  • SWE Secondary Working Embrittlement
  • IS Inventive Steel
  • CS Comparative steel
  • Example 8 steel slabs were prepared in accordance with the compositions shown in the following tables.
  • the steel slabs were reheated and finish hot-rolled to provide hot rolled steel sheets.
  • the hot rolled steel sheets were cooled at a rate of 400 °C/min., wound at 65O 0 C, cold-rolled at a reduction rate of 75%, followed by continuous annealing to produce cold rolled steel sheets.
  • the finish hot rolling was performed at 910 0 C, which is above the Ar 3 transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830 0 C for 40 seconds to produce the final cold rolled steel sheets.
  • YS Yield strength
  • TS Tensile Strength
  • El Elongation
  • r m Plasticity-anisotropy index
  • ⁇ r In-plane anisotropy index
  • AI Aging Index
  • SWE Secondary Working Embrittlement
  • IS Inventive Steel
  • CS Comparative steel
  • steel slabs were prepared in accordance with the compositions shown in the following tables.
  • the steel slabs were reheated and finish hot-rolled to provide hot rolled steel sheets.
  • the hot rolled steel sheets were cooled at a rate of 400 °C/min., wound at 650 0 C, cold-rolled at a reduction rate of 75%, followed by continuous annealing to produce cold rolled steel sheets.
  • the finish hot rolling was performed at 91O 0 C, which is above the Ar 3 transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830 0 C for 40 seconds to produce the final cold rolled steel sheets.
  • YS Yield strength
  • TS Tensile Strength
  • El Elongation
  • r m Plasticity-anisotropy index
  • ⁇ r In-plane anisotropy index
  • AI Aging Index
  • SWE Secondary Working Embrittlement
  • IS Inventive Steel
  • CS Comparative steel
  • steel slabs were prepared in accordance with the compositions shown in the following tables.
  • the steel slabs were reheated and finish hot-rolled to provide hot rolled steel sheets.
  • the hot rolled steel sheets were cooled at a rate of 400 °C/min., wound at 650 0 C, cold-rolled at a reduction rate of 75%, followed by continuous annealing to produce cold rolled steel sheets.
  • the finish hot rolling was performed at 910 0 C, which is above the Ar 3 transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 83O 0 C for 40 seconds to produce the final cold rolled steel sheets.
  • YS Yield strength
  • TS Tensile Strength
  • El Elongation
  • r m Plasticity-anisotropy index
  • ⁇ r In-plane anisotropy index
  • AI Aging Index
  • SWE Secondary Working Embrittlement
  • IS Inventive Steel
  • CS Comparative steel
  • steel slabs were prepared in accordance with the compositions shown in the following tables.
  • the steel slabs were reheated and finish hot-rolled to provide hot rolled steel sheets.
  • the hot rolled steel sheets were cooled at a rate of 400 °C/min., wound at 650 0 C, cold-rolled at a reduction rate of 75%, followed by continuous annealing to produce cold rolled steel sheets.
  • the finish hot rolling was performed at 910 0 C, which is above the Ar 3 transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830 0 C for 40 seconds to produce the final cold rolled steel sheets.
  • YS Yield strength
  • TS Tensile Strength
  • El Elongation
  • r m Plasticity-anisotropy index
  • ⁇ r In-plane anisotropy index
  • AI Aging Index
  • SWE Secondary Working Embrittlement
  • IS Inventive Steel
  • CS Comparative steel
  • steel slabs were prepared in accordance with the compositions shown in the following tables.
  • the steel slabs were reheated and finish hot-rolled to provide hot rolled steel sheets.
  • the hot rolled steel sheets were cooled at a rate of 400 °C/min., wound at 650 0 C, cold-rolled at a reduction rate of 75%, followed by continuous annealing to produce cold rolled steel sheets.
  • the finish hot rolling was performed at 91O 0 C, which is above the Ar 3 transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 83O 0 C for 40 seconds to produce the final cold rolled steel sheets.
  • YS Yield strength
  • TS Tensile Strength
  • El Elongation
  • r m Plasticity-anisotropy index
  • ⁇ r In-plane anisotropy index
  • AI Aging Index
  • SWE Secondary Working Embrittlement
  • IS Inventive Steel
  • CS Comparative steel
  • steel slabs were prepared in accordance with the compositions shown in the following tables.
  • the steel slabs were reheated and finish hot-rolled to provide hot rolled steel sheets.
  • the hot rolled steel sheets were cooled at a rate of 400 °C/min., wound at 650 0 C, cold-rolled at a reduction rate of 75%, followed by continuous annealing to produce cold rolled steel sheets.
  • the finish hot rolling was performed at 910 0 C, which is above the Ar 3 transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830 0 C for 40 seconds to produce the final cold rolled steel sheets.
  • YS Yield strength
  • TS Tensile Strength
  • El Elongation
  • r m Plasticity-anisotropy index
  • ⁇ r In-plane anisotropy index
  • AI Aging Index
  • SWE Secondary Working Embrittlement
  • IS Inventive Steel
  • CS Comparative steel
  • steel slabs were prepared in accordance with the compositions shown in the following tables.
  • the steel slabs were reheated and finish hot-rolled to provide hot rolled steel sheets.
  • the hot rolled steel sheets were cooled at a rate of 400 °C/min., wound at 650 0 C, cold-rolled at a reduction rate of 75%, followed by continuous annealing to produce cold rolled steel sheets.
  • the finish hot rolling was performed at 910 0 C, which is above the Ar 3 transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830 0 C for 40 seconds to produce the final cold rolled steel sheets.
  • YS Yield strength
  • TS Tensile Strength
  • El Elongation
  • r m Plasticity-anisotropy index
  • ⁇ r In-plane anisotropy index
  • AI Aging Index
  • SWE Secondary Working Embrittlement
  • IS Inventive Steel
  • CS Comparative steel
  • the distribution of fine precipitates in Nb-Ti composite IF steels allows the formation of minute crystal grains, and as a result, the in-plane anisotropy index is lowered and the yield strength is enhanced by precipitation enhancement.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

La présente invention concerne un acier FI composite Nb-Ti dans lequel de fins précipités, comme des précipités CuS, ayant une taille de 0,2 µm ou moins, sont distribués. La distribution des fins précipités dans l’acier FI de composite Nb-Ti améliore la limite d’élasticité et diminue l’indice d’anisotropie plane. Les précipités de taille nanométrique permettent la formation de grains de cristaux de taille infime. Il en résulte la présence de carbone dissous en plus grande quantité dans les joints des grains de cristaux qu’à l’intérieur des grains de cristaux, ce qui est avantageux en termes de propriétés non vieillissantes à température ambiante et de durcissabilité à la cuisson
PCT/KR2006/001670 2005-05-03 2006-05-03 Feuille d’acier laminee a froid ayant une formabilite superieure et un rapport de rendement eleve et son procede de production WO2006118425A1 (fr)

Priority Applications (4)

Application Number Priority Date Filing Date Title
US11/913,175 US20090126837A1 (en) 2005-05-03 2006-05-03 Cold rolled steel sheet having superior formability and high yield ratio, process for producing the same
MX2007013676A MX2007013676A (es) 2005-05-03 2006-05-03 Lamina de acero laminada en frio que tiene formabilidad superior y alta relacion de deformacion, proceso para producirla.
EP06732897.1A EP1888800B1 (fr) 2005-05-03 2006-05-03 Feuille d acier laminee a froid ayant une formabilite superieure et un rapport de rendement eleve et son procede de production
JP2008509936A JP4954981B2 (ja) 2005-05-03 2006-05-03 成形性に優れた高降伏比冷延鋼板とその製造方法。

Applications Claiming Priority (10)

Application Number Priority Date Filing Date Title
KR10-2005-0037183 2005-05-03
KR20050037183 2005-05-03
KR1020050129237A KR100723163B1 (ko) 2005-05-03 2005-12-26 면내이방성이 우수한 냉연강판과 그 제조방법
KR10-2005-0129235 2005-12-26
KR1020050129235A KR100723165B1 (ko) 2005-05-03 2005-12-26 소성이방성이 우수한 냉연강판과 그 제조방법
KR10-2005-0129239 2005-12-26
KR10-2005-0129237 2005-12-26
KR1020050129239A KR100723181B1 (ko) 2005-05-03 2005-12-26 성형성이 우수한 냉연강판과 그 제조방법
KR10-2005-0129236 2005-12-26
KR1020050129236A KR100723164B1 (ko) 2005-05-03 2005-12-26 가공성이 우수한 냉연강판과 그 제조방법

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US8398786B2 (en) 2005-10-06 2013-03-19 Posco Precipitation hardening cold rolled steel sheet having excellent yield ratios, and the method for manufacturing the same
CN114231845A (zh) * 2021-12-03 2022-03-25 本钢板材股份有限公司 一种屈服强度220Mpa级冷轧深冲高强钢及其生产方法

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EP0120976A1 (fr) * 1982-10-08 1984-10-10 Kawasaki Steel Corporation Procede de fabrication d'acier lamine a froid pour l'emboutissage profond
WO1993021351A1 (fr) * 1991-02-08 1993-10-28 Mcgill University Aciers depourvus d'elements interstitiels
JPH10280048A (ja) 1997-04-09 1998-10-20 Kawasaki Steel Corp 耐歪時効性に優れた塗装焼付硬化型冷延鋼板の製造方法
JPH10287954A (ja) 1997-04-15 1998-10-27 Kawasaki Steel Corp 耐歪時効特性に優れた塗装焼付硬化型冷延鋼板およびその製造方法
US6290788B1 (en) * 1996-07-08 2001-09-18 Mannesmann Ag Process for manufacture of precision interstitial-free steel tubes
JP2003041342A (ja) * 2002-05-29 2003-02-13 Nkk Corp 打ち抜き性に優れる冷延鋼板

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TW415967B (en) * 1996-02-29 2000-12-21 Kawasaki Steel Co Steel, steel sheet having excellent workability and method of the same by electric furnace-vacuum degassing process
EP1136575A4 (fr) * 1999-08-10 2008-04-23 Jfe Steel Corp Procede de production de feuillards d'acier lamines a froid
KR100473497B1 (ko) * 2000-06-20 2005-03-09 제이에프이 스틸 가부시키가이샤 박강판 및 그 제조방법
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JP4448856B2 (ja) * 2003-11-10 2010-04-14 ポスコ 加工性の優れた耐時効冷延鋼板及びその製造方法
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Publication number Priority date Publication date Assignee Title
EP0120976A1 (fr) * 1982-10-08 1984-10-10 Kawasaki Steel Corporation Procede de fabrication d'acier lamine a froid pour l'emboutissage profond
WO1993021351A1 (fr) * 1991-02-08 1993-10-28 Mcgill University Aciers depourvus d'elements interstitiels
US6290788B1 (en) * 1996-07-08 2001-09-18 Mannesmann Ag Process for manufacture of precision interstitial-free steel tubes
JPH10280048A (ja) 1997-04-09 1998-10-20 Kawasaki Steel Corp 耐歪時効性に優れた塗装焼付硬化型冷延鋼板の製造方法
JPH10287954A (ja) 1997-04-15 1998-10-27 Kawasaki Steel Corp 耐歪時効特性に優れた塗装焼付硬化型冷延鋼板およびその製造方法
JP2003041342A (ja) * 2002-05-29 2003-02-13 Nkk Corp 打ち抜き性に優れる冷延鋼板

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US8398786B2 (en) 2005-10-06 2013-03-19 Posco Precipitation hardening cold rolled steel sheet having excellent yield ratios, and the method for manufacturing the same
US8864922B2 (en) 2005-10-06 2014-10-21 Posco Method for manufacturing a precipitation-hardening cold-rolled steel sheet having excellent yield ratios
CN114231845A (zh) * 2021-12-03 2022-03-25 本钢板材股份有限公司 一种屈服强度220Mpa级冷轧深冲高强钢及其生产方法

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