EP1885899B1 - Kaltgewalztes stahlblech mit hohem streckgrenzenverhältnis und weniger anisotropie und herstellungsverfahren dafür - Google Patents

Kaltgewalztes stahlblech mit hohem streckgrenzenverhältnis und weniger anisotropie und herstellungsverfahren dafür Download PDF

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EP1885899B1
EP1885899B1 EP06732896.3A EP06732896A EP1885899B1 EP 1885899 B1 EP1885899 B1 EP 1885899B1 EP 06732896 A EP06732896 A EP 06732896A EP 1885899 B1 EP1885899 B1 EP 1885899B1
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steel sheet
less
rolled steel
cold rolled
composition
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French (fr)
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EP1885899A1 (de
EP1885899A4 (de
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Jeong-Bong c/o Posco Yoon
Jin-Hee c/o Posco Chung
Kwang-Geun c/o Posco Chin
Sang-Ho c/o Posco Han
Sung-Il c/o Posco Kim
Ho-Seok c/o Posco Kim
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Posco Holdings Inc
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Posco Co Ltd
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Priority claimed from KR1020050130130A external-priority patent/KR100723216B1/ko
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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
    • 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
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • 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
    • C21D8/0421—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 characterised by the working steps
    • C21D8/0426—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
    • C21D8/04—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
    • C21D8/0421—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 characterised by the working steps
    • C21D8/0436—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
    • C21D8/04—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
    • C21D8/0447—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 characterised by the heat treatment
    • C21D8/0463—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 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
    • 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
    • C21D8/0447—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 characterised by the heat treatment
    • C21D8/0473—Final recrystallisation annealing
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations

Definitions

  • the present invention relates to niobium (Nb) based interstitial free (IF) cold rolled steel sheets that are used as materials for automobiles, household electronic appliances, etc. More particularly, the present invention relates to IF cold rolled steel sheets with high yield ratio whose in-plane anisotropy is lowered due to the distribution of fine precipitates, and a method for producing such steel sheets.
  • Nb niobium
  • IF interstitial free
  • 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.
  • extended time of the batch annealing causes low productivity of the Al-killed steels and severe variation in steel materials at different sites.
  • 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 Patent Application 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 Patent Application 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 Application Publication 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 Patent Application 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 Patent Application 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 Patent Application Publication Nos. Hei 9-227951 and Hei 10-265900 suggest technologies associated with improvement in workability or surface defects due to carbides by the use of Cu as a nucleus for precipitation of the carbides.
  • 0.005-0.1% of Cu is added to precipitate CuS during temper rolling of an IF steel, and the CuS precipitates are used as nuclei to form Cu-Ti-C-S precipitates during hot rolling.
  • the former publication states that the number of nuclei forming a ⁇ 111 ⁇ plane parallel to the surface of a plate increases in the vicinity of the Cu-Ti-C-S precipitates during recrystallization, which contributes to an improvement in workability.
  • Japanese Patent Application 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.
  • Cu is added in an amount of 0.05-1.0% to ensure improved corrosion resistance.
  • Cu is added in an excessively large amount of 0.2% or more.
  • Japanese Patent Application 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
  • EP-A-1136575 discloses a method of producing cold rolled steel sheet.
  • An object of certain embodiments of the invention is to provide Nb based IF cold rolled steel sheets and a method for producing such steel sheets that are capable of achieving a high yield ratio and a low in-plane anisotropy index.
  • Another object of certain embodiments of the invention is to provide a method for producing such steel sheets.
  • the C and Nb contents preferably satisfy a relationship, by weight: 0.8 ⁇ (Nb/93) / (C/12) ⁇ 5.0.
  • 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.
  • 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 MnS and CuS. These precipitates are referred to simply as "(Mn,Cu)S".
  • the present inventors have found that when fine precipitates are distributed in Nb based IF steels, 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 IF steels. Particularly, the precipitates have not been actively used from the viewpoint of yield strength and in-plane anisotropy index.
  • the fine precipitates thus obtained allow the formation of minute crystal grains. Minuteness in the size of crystal grains relatively increases the proportion of crystal grain boundaries. Accordingly, 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. According to the cold rolled steel sheets of the present invention, 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 limited to 0.01% or less.
  • Carbon (C) affects the room-temperature aging resistance and bake hardenability of the cold rolled steel sheets.
  • 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.
  • the carbon is preferably added in an amount of 0.001% or more, and more preferably 0.005% to 0.01%.
  • 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) may be 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 may more preferably be in the range of 0.03 to 0.2%.
  • the content of manganese (Mn) may be 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. When the manganese content is greater than 0.3%, coarse MnS precipitates are formed, thus making it difficult to achieve desired strength. A preferable Mn content is within the range of 0.01 to 0.12%.
  • the content of sulfur (S) is 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.
  • 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 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
  • 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 limited to 0.02% or 0.004% 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 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 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 in the range of 0.0001 to 0.002%.
  • boron is added to prevent occurrence of secondary working embrittlement.
  • 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.
  • niobium (Nb) is 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, is added to steels to form NbC precipitates in the steels.
  • the NbC precipitates permit the steel sheets to be well textured during annealing, thus greatly improving the deep drawability of the steel sheets.
  • the content of Nb added is not greater than 0.002%, 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.
  • Relationship 1 is associated with the formation of (Mn,Cu)S precipitates. To obtain fine CuS precipitates, it is preferred that the value of relationship 1 be equal to or greater than 1. If the value of relationship 1 is greater than 30, coarse CuS precipitates are distributed, which is undesirable. To stably obtain CuS precipitates having a size of 0.2 ⁇ m or less, the value of relationship 1 is preferably in the range of 1 to 9, and most preferably 1 to 6. The reason for this limitation is to obtain fine (Mn,Cu)S precipitates. 1 ⁇ Mn / 55 + Cu / 63.5 / S / 32 ⁇ 30
  • Relationship 2 is associated with the formation of (Mn,Cu)S precipitates, and is obtained by adding a Mn content to Relationship 1.
  • the value of relationship 2 must be 1 or greater.
  • the value of Relationship 2 is greater than 30, coarse (Mn,Cu)S precipitates are obtained.
  • the value of relationship 2 is preferably in the range of 1 to 9, and most preferably 1 to 6. 1 ⁇ Al / 27 / N / 14 ⁇ 10
  • Relationship 3 is associated with the formation of AlN precipitates. When the value of Relationship 3 is less than 1, aging may take place due to dissolved N. When the value of Relationship 3 is greater than 10, coarse AlN precipitates are obtained, and thus sufficient strength is not obtained. Preferably, the value of relationship 3 is in the range of 1 to 5.
  • the present invention provides a cold rolled steel sheet with high yield ratio and low in-plane anisotropy index, the cold rolled sheet having a composition comprising: 0.01% or less C, 0.08% or less S, 0.1% or less Al, 0.004% or less N, 0.2% P, 0.0001 to 0.002% of B, 0.002 to 0.04% of Nb, at least one kind selected from 0.01 to 0.2% of Cu, 0.01 to 0.3% of Mn and 0.004 to 0.2% of N, by weight, and the balance Fe and other unavoidable impurities, wherein the composition satisfies following relationships: 1 ⁇ (Mn/55+Cu/63.5)/(S/32) ⁇ 30, 1 ⁇ (Al/27)/(N/14) ⁇ 10, where the N content is 0.004% or more.
  • the steel sheet comprises at least one kind selected from NnS precipitates, CuS precipitates, composite precipitates of MnS and CuS, 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.
  • NbC and TiC forms carbon is precipitated into NbC and TiC forms. Accordingly, 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. 0.8 ⁇ Nb / 93 / C / 12 ⁇ 5.0
  • Relationship 4 is associated with the formation of NbC precipitates to remove the carbon in a solid solution state, thereby achieving room-temperature non-aging properties.
  • the value of relationship 4 is less than 0.8, it is difficult to ensure room-temperature non-aging properties.
  • the value of relationship 4 is greater than 5, the amounts of Nb and Ti remaining in a solid solution state in the steels are large, which deteriorates the ductility of the steels.
  • it is intended to achieve room-temperature non-aging properties without securing bake hardenability it is preferred to limit the carbon content to 0.005% or less.
  • Relationship 5 is associated with the achievement of bake hardenability.
  • Cs which represents the content of dissolved carbon, and is expressed in ppm.
  • 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.
  • 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. According to a study conducted by the present inventors, 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.
  • 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 of the order of 340MPa, they may further contain at least one solid solution strengthening element selected from P, Si and Cr.
  • P solid solution strengthening element selected from P, Si and Cr.
  • 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.
  • a steel satisfying one of the compositions defined above is reheated, and is then subjected to hot rolling.
  • the reheating temperature is 1,100°C or higher.
  • coarse precipitates formed during continuous casting are not completely dissolved and remain. The coarse precipitates still remain even after hot rolling.
  • the hot rolling is performed at a finish rolling temperature not lower than the Ar 3 transformation point.
  • 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 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 ⁇ m 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°C.
  • the winding temperature is higher than 700°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 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°C.
  • the continuous annealing is performed at a temperature lower than 700°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°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 mechanical properties of steel sheets produced in the following examples were evaluated according to the ASTM E-8 standard test methods. Specifically, each of the steel sheets was machined to obtain standard samples. The yield strength, tensile strength, elongation, plasticity-anisotropy index (r m value) and in-plane anisotropy index ( ⁇ r value), and the aging index were measured using a tensile strength tester (available from INSTRON Company, Model 6025).
  • 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°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°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°C for 40 seconds to produce the final cold rolled steel sheets.
  • 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°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°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°C for 40 seconds to produce the final cold rolled steel sheets.
  • 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°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°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°C for 40 seconds to produce the final cold rolled steel sheets.
  • 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°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°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°C for 40 seconds to produce the final cold rolled steel sheets.
  • 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°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°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°C for 40 seconds to produce the final cold rolled steel sheets.
  • 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°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°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°C for 40 seconds to produce the final cold rolled steel sheets.
  • 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°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°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°C for 40 seconds to produce the final cold rolled steel sheets.
  • 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°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°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°C for 40 seconds to produce the final cold rolled steel sheets.
  • 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°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°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°C for 40 seconds to produce the final cold rolled steel sheets.
  • 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°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°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°C for 40 seconds to produce the final cold rolled steel sheets.
  • the distribution of fine precipitates in Nb based 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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Claims (40)

  1. Kaltgewalztes Stahlblech mit hoher Streckgrenze und niedrigem Anisotropie-Index in der Ebene, worin das Stahlblech eine Zusammensetzung aufweist, die umfasst:
    0,01% oder weniger C, 0,01bis 0,2 % Cu, 0,005 bis 0,08 % S, 0,1 % oder weniger Al, 0,004 % oder weniger N, 0,2 % oder weniger P, 0,0001 bis 0,002 % B, 0,002 bis 0,04 % Nb, wahlweise 0,1 bis 0,8 % Si, 0,2 bis 1,2 % Cr und 0,01bis 0,2 % Mo, und als Rest Fe und andere unvermeidbare Verunreinigungen,
    worin die Zusammensetzung die folgende Beziehung erfüllt: 1 ≤ (Cu/63,5)/(S/32) ≤ 30, und worin das Stahlblech CuS-Ausfällungen mit einer durchschnittlichen Größe von 0,2 µm oder weniger umfaßt.
  2. Kaltgewalztes Stahlblech mit hohem Streckgrenzenverhältnis und niedrigem Anisotropie-Index in der Ebene, worin das Stahlblech eine Zusammensetzung aufweist, die umfaßt:
    0,01% oder weniger C, 0,01 bis 0,2 % Cu, 0,005 bis 0,06 % S, 0,1 % oder weniger Al, 0,004 % oder weniger N, 0,2 % oder weniger P, 0,0001 bis 0,002 % B, 0,002 bis 0,04 % Nb und als Rest Fe und andere unvermeidbare Verunreinigungen,
    worin die Zusammensetzung die folgende Beziehung erfüllt: 1 ≤ (Mn/55+Cu/63,5)/(S/32) ≤ 30, und worin das Stahlblech (Mn,Cu)S-Ausfällungen mit einer durchschnittlichen Größe von 0,2 µm oder weniger umfaßt.
  3. Kaltgewalztes Stahlblech mit hohem Streckgrenzenverhältnis und niedrigem Anisotropie-Index in der Ebene, worin das Stahlblech eine Zusammensetzung aufweist, die umfaßt:
    0,1 % oder weniger C, 0,01 bis 0,2 % Cu, 0,005 bis 0,08 % S, 0,1 % oder weniger Al, 0,004 % oder weniger N, 0,2 % oder weniger P, 0,0001 bis 0,002 % B, 0,002 bis 0,04 % Nb und andere unvermeidbare Verunreinigungen,
    worin die Zusammensetzung die folgenden Beziehungen erfüllt: 1 ≤ (Cu/63,5)/(S/32) ≤ 30 und 1 ≤ (A1/27) / (N/14) ≤ 10; und
    worin das Stahlblech Mn,Cu)S-Ausfällungen mit einer durchschnittlichen Größe von 0,2 µm oder weniger umfaßt.
  4. Kaltgewalztes Stahlblech mit hohem Streckgrenzenverhältnis und niedrigem Anisotropie-Index in der Ebene, worin das Stahlblech eine Zusammensetzung aufweist, die umfaßt:
    0,01% oder weniger C, 0,01 bis 0,2 % Cu, 0,005 bis 0,08 % S, 0,1 % oder weniger Al, 0,004 % oder weniger N, 0,2 % oder weniger P, 0,0001 bis 0,002 % B, 0,002 bis 0,04 % Nb und als Rest Fe und andere unvermeidbare Verunreinigungen,
    worin die Zusammensetzung die folgenden Beziehungen erfüllt: 1 ≤ (Mn/55+Cu/63,5)/(S/32) ≤ 30 und 1 ≤ (Al/27)/(N/14) ≤ 10, und
    worin das Stahlblech (Mn,Cu)S-Ausfällungen und AIN-Ausfällungen mit einer durchschnittlichen Größe von 0,2 µm oder weniger umfaßt.
  5. Kaltgewalztes Stahlblech mit hohem Streckgrenzenverhältnis und niedrigem Anisotropie-Index in der Ebene, worin das Stahlblech eine Zusammensetzung aufweist, die umfasst;
    0,01% oder weniger C, 0,08 % oder weniger S, 0,1 % oder weniger Al, 0,02 % oder weniger N, 0,2 % oder weniger P, 0,0001 bis 0,002 % B, 0,002 bis 0,04 % Nb, mindestens eines von 0,01 bis 0.2 % Cu und 0,01bis 0,3 % Mn, wahlweise 0,1 bis 0,8 % Si, 0,2 bis 1,2 % Cr und 0,01 bis 0,2 % Mo, und als Rest Fe und andere unvermeidbare Verunreinigungen,
    worin (1) wenn die Zusammensetzung weniger als 0,004 % N umfasst, die Zusammensetzung die folgende Beziehung erfüllt: 1 ≤ (Mn/55+Cu/63,5)/(S/32) ≤ 30, und worin das Stahlblech umfaßt (Mn,Cu)S-Ausfällungen mit einer durchschnittlichen Größe von 0,2 µm oder weniger, oder worin (2) wenn die Zusammensetzung 0,004 bis 0,02% N umfaßt, die Zusammensetzung die folgenden Beziehung erfüllt: 1 ≤ (Mn/55+Cu/63,5)/(S/32) ≤ 30 und 1 ≤ (Al/27)/(N/14) ≤ 10, und worin das Stahlblech mindestens eines umfaßt von (Mn,Cu)S-Ausfällungen und AIN-Ausfällungen mit einer durchschnittlichen Größe von 0,2 µm oder weniger.
  6. Kaltgewalztes Stahlblech nach Anspruch 1 oder 5, worin die Zusammensetzung die folgende Beziehung erfüllt: 0,8 ≤ (Nb/93)/(C/12) ≤ 5,0.
  7. Kaltgewalztes Stahlblech nach Anspruch 6, worin die Zusammensetzung 0,005% oder weniger C umfasst.
  8. Kaltgewalztes Stahlblech nach Anspruch 1 oder 5 r, worin gelöster Kohlenstoff (Cs) von 5 bis 30 beträgt, worin Cs = (C- Nb x 12/93) x 10.000.
  9. Kaltgewalztes Stahlblech nach Anspruch. 8, worin die Zusammensetzung 0,001 bis 0,01% C umfasst.
  10. Kaltgewalztes Stahlblech nach Anspruch 1 oder 5, worin die Zusammensetzung 0,015 % oder weniger P enthält.
  11. Kaltgewalztes Stahlblech nach Anspruch 1 oder 5, worin die Zusammensetzung 0,03 bis 0,2 % P enthält.
  12. Kaltgewalztes Stahlblech nach Anspruch 1 oder 5, worin die Zusammensetzung weiter mindestens eines von 0,1 bis 0,8 % Si und 0,2 bis 1,2 % Cr umfasst.
  13. Kaltgewalztes Stahlblech nach Anspruch 12, worin die Zusammensetzung weiter 0,01 bis 0,2 % Mo umfasst.
  14. Kaltgewalztes Stahlblech nach Anspruch 1 oder 5,
    worin die Zusammensetzung weiter 0,01 bis 0,2 % Mo enthält.
  15. Kaltgewalztes Stahlblech nach Anspruch 1, worin die Zusammensetzung 0,08 bis 0,4% Mn und Cu umfasst.
  16. Kaltgewalztes Stahlblech nach Anspruch 2, 4 oder 5, worin die Zusammensetzung 0,01 bis 0,12 % Mn umfasst.
  17. Kaltgewalztes Stahlblech nach Anspruch 2, 4 oder 5, worin der Wert von (Mn/55+Cu/63,5)/(S/32) von 1 bis 9 beträgt.
  18. Kaltgewalztes Stahlblech nach Anspruch 3, 4 oder S, worin der Wert von (Al/27)/(N/14) von 1 bis 5 beträgt.
  19. Kaltgewalztes Stahlblech nach einem der Ansprüche 1 bis 5, worin der kaltgewalzte Stahl einem Streckgrenzenverhältnis (Streckgrenze/Zugfestigkeit) von 0,58 oder höher genügt.
  20. Kaltgewalztes Stahlblech nach einem der Ansprüche 1 bis 5, worin die Anzahl der Ausfällungen 1x106/mm2 oder mehr beträgt.
  21. Verfahren zur Herstellung eines kaltgewalzten Stahlblechs mit hohem Streckgrenzenverhältnis und niedrigem Anisotropie-Index in der Ebene, wobei das Verfahren die folgenden Schritte umfasst;
    Wiedererwärmen einer Schlacke auf eine Temperatur von 1100 °C oder höher,
    worin die Schlacke eine Zusammensetzung aufweist, die umfaßt:
    0,01% oder weniger C, 0,01 bis 0,2 % Cu, 0,005 bis 0,08 % S, 0,1 % oder weniger Al, 0,004 % oder weniger N, 0,2 % oder weniger P, 0,0001 bis 0,002 % B, 0,002 bis 0,04 % Nb, wahlweise 0.1 bis 0,8 % Si, 0,2 bis 1,2 % Cr und 0,01 bis 0,2 % Mo und als Rest Fe und andere unvermeidbare Verunreinigungen, und worin die Zusammensetzung die folgende Beziehung erfüllt: 1 ≤ (Cu/63,5)/(S/32) ≤ 30;
    Warmwalzen der wiedererwärmten Schlacke bei einer Fertigwalztemperatur des Ar3-Umwandlungspunktes oder höher, um ein warmgewalztes Stahlblech bereitzustellen;
    Abkühlen des warmgewalzten Stahlblechs bei einer Rate von 300°C/min oder höher;
    Wickeln des gekühlten Stahlblechs bei 700°C oder niedriger;
    Kaltwalzen des gewickelten Stahlblechs; und
    kontinuierliches Annealen des kaltgewalzten Stahlblechs, worin das Stahlblech CuS-Ausfällungen mit einer durchschnittlichen Größe von 0,2 µm oder weniger umfaßt.
  22. Verfahren zur Herstellung eines kaltgewalzten Stahlblechs mit hohem Streckgrenzenverhältnis und niedrigem Anisotropie-Index in der Ebene, wobei das Verfahren die folgenden Schritte umfaßt:
    Wiedererwärmen einer Schlacke auf eine Temperatur von 1100°C oder höher,
    worin die Schlacke eine Zusammensetzung aufweist, die umfasst: 0,01% oder weniger C, 0,01 bis 0,2 % Cu, 0,005 bis 0,08 % S, 0,1 % oder weniger Al, 0,004 % oder weniger N, 0,2 % oder weniger P, 0,0001 bis 0,002 % B, 0,002 bis 0,04 % Nb und als Rest Fe und andere unvermeidbare Verunreinigungen, worin die Zusammensetzung die folgende Beziehung erfüllt: 1 ≤ (Mn/55+Cu/63,5)/(S/32) ≤ 30;
    Warmwalzen der wiedererwärmten Schlacke bei einer Fertigwalztemperatur des Ar3-Umwandlungspunktes oder höher, um ein warmgewalztes Stahlblech bereitzustellen;
    Abkühlen des warmgewalzten Stahlblechs bei einer Rate von 300 °C/min oder höher;
    Aufwickeln des gekühlten Stahlblechs bei 700°C oder niedriger;
    Kaltwalzen des gewickelten Stahlblechs; und
    kontinuierliches Annealen des kaltgewalzten Stahlblechs, worin das Stahlblech (Mn, Cu)S-Ausfällungen mit einer durchschnittlichen Größe von 0,2 µm oder weniger umfaßt.
  23. Verfahren zur Herstellung eines kaltgewalzten Stahlblechs mit hohem Streckgrenzenverhältnis und niedrigem Anisotropie-Index in der Ebene, wobei das Verfahren die folgenden Schritte umfaßt
    Wiedererwärmen einer Schlacke auf eine Temperatur von 1100°C oder höher,
    worin die Schlacke eine Zusammensetzung aufweist, die umfaßt:
    0,0 % oder weniger C, 0,01bis 0,2 % Cu, 0,005 bis 0,08 % S, 0,1 % oder weniger Al, 0,004 % oder weniger N, 0,2 % oder weniger P, 0,0001 bis 0,002 % B, 0,002 bis 0,04 % Nb, bezogen auf das Gewicht, und als Rest Fe und andere unvermeidbare Verunreinigungen, und worin die Zusammensetzung die folgenden Beziehungen erfüllt: 1 ≤ (Cu/63,5)/(S/32) ≤ 30 und 1 ≤ (Al/27)/(N/14) ≤ 10;
    Warmwalzen der wiedererwärmten Schlacke bei einer Fertigwalztemperatur des Ar3-Umwandlungspunktes oder höher, um ein warmgewalztes Stahlblech bereitzustellen;
    Abkühlen des warmgewalzten Stahlblechs bei einer Rate von 300°C/min oder höher;
    Wickeln des gekühlten Stahlblechs bei 700°C oder niedriger;
    Kaltwalzen des gewickelten Stahlblechs; und
    kontinuierliches Annealen des kaltgewalzten Stahlblechs, worin das Stahlblech (Mn, Cu)S-Ausfällungen mit einer durchschnittlichen Größe von 0,2 µm oder weniger umfaßt.
  24. Verfahren zur Herstellung eines kaltgewalzten Stahlblechs mit hohem Streckgrezenverhältnis und niedrigem Anisotropie-Index in der Ebene, wobei das Verfahren die folgenden Schritte umfaßt:
    Wiedererwärmen einer Schlacke auf eine Temperatur von 1100°C oder höher,
    worin die Schlacke eine Zusammensetzung aufweist, die umfaßt:
    0,01% oder weniger C, 0,01 bis 0,2 % Cu, 0,005 bis 0,08 % S, 0,1 % oder weniger Al, 0,004 % oder weniger N, 0,2 % oder weniger P, 0,0001 bis 0,002 % B, 0,002 bis 0,04 % Nb, Rest Fe und andere unvermeidbare Verunreinigungen, worin die Zusammensetzung die folgenden Beziehungen erfüllt: 1 ≤ (Mn/55+Cu/63,5)/(S/32) ≤ 30 und 1 ≤ (Al/27)/(N/14) ≤ 10;
    Warmwalzen der wiedererwärmten Schlacke bei einer Fertigwalztemperatur des Ar3-Umwandlungspunktes oder höher, um ein warmgewalztes Stahlblech bereitzustellen; Abkühlen des warmgewalzten Stahlblechs: mit einer Rate von 300°C/min oder höher; Wickeln des gekühlten Stahlblechs bei 700°C oder niedriger
    Kaltwalzen des gewickelten Stahlblechs; und
    kontinuierliches Glühen des kaltgewalzten Stahlblechs, worin das Stahlblech (Mn,Cu)S-Ausfällungen und A1N-Ausfällungen mit einer durchschnittlichen Größe von 0,2 µm oder weniger umfaßt.
  25. Verfahren zur Herstellung eines kaltgewalzten Stahlblechs mit hoher Streckgrenze und niedrigem Anisotropie-Index in der Ebene, worin das Verfahren die folgenden Schritte umfasst:
    Wiedererwärmen einer Schlacke auf eine Temperatur von 1100 °C oder höher,
    worin die Schlacke eine Zusammensetzung aufweist, die umfasst:
    0,01 % oder weniger C, 0,08 % oder weniger S, 0,1 % oder weniger Al, 0,02 % oder weniger N, 0,2 % oder weniger P, 0,0001 bis 0,002 % B, 0,002 bis 0,04 % Nb, mindestens eines von 0,01 bis 0.2 % Cu und 0,01 bis 0,3 % Mn, wahlweise 0,1 bis 0,8 % Si, 0,2 bis 1,2 % Cr und 0,01 bis 0,2 % Mo, und als Rest Fe und andere unvermeidbare Verunreinigungen,
    worin (1) wenn die Zusammensetzung weniger als 0,004% von N umfasst, die Zusammensetzung die folgende Beziehung erfüllt: 1 ≤ (Mn/SS+Cu/63,5)/(S/32) ≤ 30, oder worin (2) wenn die Zusammensetzung 0,004 bis 0,02% N enthält, die Zusammensetzung die folgenden Beziehung erfüllt: 1 ≤ (Mn/55+Cu/63,5J/(S/32) ≤ 30 und 1 ≤ (Al/27)/(N/14) ≤ 10;
    Warmwalzen der wiedererwärmten Schlacke bei einer Fertigwalztemperatur des Ar3-Umwandlungspunkts oder höher, um ein warmgewalztes Stahlblech bereitzustellen;
    Abkühlen des warmgewalzten Stahlblechs bei einer Rate von von 300°C/min oder höher;
    Wickeln des gekühlten Stahlblechs bei 700°C oder niedriger;
    Kaltwalzen des gewickelten Stahlblechs; und
    kontinuierliches Glühen des kaltgewalzten Stahlblechs, worin (1) wenn die Zusammensetzung weniger als 0,004 % N umfaßt, das Stahlblech (Mn,Cu)S-Ausfällungen mit einer durchschnittlichen Größe von 0,2 µm oder weniger umfaßt, oder worin (2) wenn die Zusammensetzung 0,004 bis 0,021 % N umfaßt, das Stahlblech mindestens eine der Ausfällungen (Mn,Cu)S und AlN-Ausfällungen mit einer durchschnittlichen Größe von 0,2 µm oder weniger umfaßt.
  26. Verfahren nach Anspruch 21 oder 25, worin die Zusammensetzung die folgende Beziehung erfüllt: 0.8 ≤ (Nb/93)/(C/12) ≤ 5,0.
  27. Verfahren nach Anspruch 26, worin die Zusammensetzung 0,005 % oder weniger C enthält.
  28. Verfahren nach Anspruch 21 oder 25, worin der gelöste Kohlenstoff (Cs) von 5 bis 30 beträgt, worin Cs = (C - Nb x 12/93) x 10.000.
  29. Verfahren nach Anspruch 28, worin die Zusammensetzung 0,001 bis 0,01 % C umfasst.
  30. Verfahren nach Anspruch 21 oder 25, worin die Zusammensetzung 0,015% oder weniger P enthält.
  31. Verfahren nach Anspruch 21 oder 25, worin die Zusammensetzung 0,03 bis 0,2 % P enthält.
  32. Verfahren nach Anspruch 21 oder 25, worin die Zusammensetzung weiter mindestens eines von 0,1 bis 0,8 % Si und 0,2 bis 1,2 % Cr umfasst.
  33. Verfahren nach Anspruch 32, worin die Zusammensetzung weiter 0,01 bis 0,2 % Mo enthält.
  34. Verfahren nach Anspruch 21 oder 25, worin die Zusammensetzung weiter 0,01 bis 0,2 % Mo enthält.
  35. Verfahren nach Anspruch 22, 24 oder 25, worin die Zusammensetzung 0,08 bis 0,4 % Mn und Cu enthält.
  36. Verfahren nach Anspruch 22, 24 oder 25, worin die Zusammensetzung 0,01 bis 0,12 % Mn enthält.
  37. Verfahren nach Anspruch 22, 24 oder 25, worin der Wert von (Mn/55+Cu/63,5)/(S/32) von 1 bis 9 beträgt.
  38. Verfahren nach Anspruch 23, 24 oder 25, worin der Wert von (Al/27)/(N/14) von 1 bis 5 beträgt.
  39. Verfahren nach einem der Ansprüche 21 bis 25, worin der kaltgewalzte Stahl ein Streckgrenzenverhältnis (Streckgrenze/Zugfestigkeit) von 0,58 oder höher erfüllt.
  40. Verfahren nach einem der Ansprüche 21 bis 25, worin die Anzahl der Ausfällungen 1x106/mm2 oder mehr beträgt.
EP06732896.3A 2005-05-03 2006-05-03 Kaltgewalztes stahlblech mit hohem streckgrenzenverhältnis und weniger anisotropie und herstellungsverfahren dafür Active EP1885899B1 (de)

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Application Number Priority Date Filing Date Title
KR20050037183 2005-05-03
KR1020050130130A KR100723216B1 (ko) 2005-05-03 2005-12-26 소성이방성이 우수한 냉연강판과 그 제조방법
KR1020050130131A KR100742818B1 (ko) 2005-05-03 2005-12-26 가공성이 우수한 냉연강판과 그 제조방법
KR1020050129243A KR100723158B1 (ko) 2005-05-03 2005-12-26 성형성이 우수한 냉연강판과 그 제조방법
KR1020050130132A KR100742819B1 (ko) 2005-05-03 2005-12-26 면내이방성이 우수한 냉연강판과 그 제조방법
PCT/KR2006/001669 WO2006118424A1 (en) 2005-05-03 2006-05-03 Cold rolled steel sheet having high yield ratio and less anisotropy, process for producing the same

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EP1885899A4 EP1885899A4 (de) 2010-12-29
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KR20070038730A (ko) 2005-10-06 2007-04-11 주식회사 포스코 항복비가 우수한 석출강화형 냉연강판 및 그 제조방법
CN115058572B (zh) * 2022-06-13 2023-07-04 北京科技大学 一种添加中间层的不锈钢/碳钢层状复合板及其制备方法

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JPS5967322A (ja) * 1982-10-08 1984-04-17 Kawasaki Steel Corp 深絞り用冷延鋼板の製造方法
JPH0747797B2 (ja) * 1989-03-10 1995-05-24 川崎製鉄株式会社 耐つまとび性、耐泡・黒点欠陥性及びプレス成形性に優れたほうろう用鋼板並びにその製造方法
US5200005A (en) * 1991-02-08 1993-04-06 Mcgill University Interstitial free steels and method thereof
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
DE19628714C1 (de) * 1996-07-08 1997-12-04 Mannesmann Ag Verfahren zur Herstellung von Präzisionsstahlrohren
WO2001012864A1 (fr) 1999-08-10 2001-02-22 Nkk Corporation Procede de production de feuillards d'acier lamines a froid
US20030015263A1 (en) * 2000-05-26 2003-01-23 Chikara Kami Cold rolled steel sheet and galvanized steel sheet having strain aging hardening property and method for producing the same
EP2312009A1 (de) * 2000-06-20 2011-04-20 JFE Steel Corporation Stahlblech und Verfahren zu dessen Herstellung
JP2003041342A (ja) * 2002-05-29 2003-02-13 Nkk Corp 打ち抜き性に優れる冷延鋼板
EP1689901B1 (de) * 2003-11-10 2018-03-21 Posco Warmgewalztes stahlblech mit hervorragender alterungsbeständigkeit und höherer formbarkeit und herstellungsverfahren dafür
WO2005061748A1 (en) * 2003-12-23 2005-07-07 Posco Bake-hardenable cold rolled steel sheet having excellent formability, and method of manufacturing the same

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EP1885899A4 (de) 2010-12-29
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