Classifications

• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
• • C—CHEMISTRY; METALLURGY
  • 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
  • C22C38/04—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
• • 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

Definitions

• the present invention relates to titanium (Ti) based 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 Ti based IF cold rolled steel sheets whose yield strength is enhanced due to the distribution of fine precipitates, and a process for producing the Ti-based 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.
• 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 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 E-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 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 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.
• 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 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
• 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° 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° 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 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 Ti-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 preferably 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 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 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. When the manganese content is greater than 0.3%, coarse MnS precipitates are formed, thus making it difficult to achieve desired strength. A more preferable 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.
• 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
• 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.
• 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 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.
• Relationship 3 is associated with the formation of (Mn,Cu)S precipitates, and is obtained by adding a Mn content to Relationship 1.
• the value of (Mn/55+Cu/63.5)/(S*/32) must be 1 or greater.
• 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 1 to 6.
• the sum of Mn and 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.
• N N ⁇ 0.8 ⁇ (Ti ⁇ 0.8 ⁇ (48/32) ⁇ S)) ⁇ (14/48) (5)
• Relationship 4 is associated with the formation of fine (Mn,Cu)S precipitates.
• 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) 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.
• 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.
• Ti* Ti ⁇ 0.8 ⁇ ((48/14) ⁇ N+(48/32) ⁇ S) (7)
• Relationship 6 is associated with the formation of 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.
• Ti* is defined as 0.
• 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 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.
• 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 ⁇ 10 5 /mm 2 or more, more preferably 1 ⁇ 10 6 /mm 2 or more, and most preferably 1 ⁇ 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, they may further contain at least one solid solution strengthening element selected from P, Si and Cr.
• P solid solution strengthening element
• Si silicon
• 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 preferably 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 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 ⁇ 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 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° 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 170° 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.
• 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.
• 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 Ti-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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