COLD ROLLED STEEL SHEET HAVING SUPERIOR FORMABILITY AND HIGH YIELD RATIO, PROCESS FOR PRODUCING THE SAME

Description

[Technical Field]

[0001] The present invention relates to niobium (Nb) and titanium (Ti)-added interstitial free (IF) cold rolled steel sheets that are used as materials for automobiles, household electronic appliances, etc. More specifically, the present invention relates to highly formable IF cold rolled steel sheets whose yield strength is enhanced due to the distribution of fine precipitates, and a process for producing the IF cold rolled steel sheets.

[Background Art]

[0002] In general, 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.

[0003] 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.

[0004] 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.

[0005] Room-temperature aging resistance and bake hardenability can be imparted to aluminum (Al)-killed steels by batch annealing of the Al-killed steels. However, extended time of the batch annealing causes low productivity of the Al-killed steels and severe variation in steel materials at different sites. In addition, 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.

[0006] Under such circumstances, 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.

[0007] For example, 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). In very low carbon IF steels, however, P causes the problem of secondary working embrittlement due to segregation in grain boundaries.

[0008] 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%.

[0009] 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).

[0010] 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. According to this publication, Mn is used in an amount of up to 0.5%, Al as a deoxidizing agent is used in an amount of 0.1%, and nitrogen (N) as an impurity is limited to 0.01% or less. If the Mn content is increased, the plating characteristics are worsened.

[0011] 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 ε-Cu precipitates. High strength of the IF steel is achieved due to the presence of the ε-Cu precipitates, but the workability of the IF steel is worsened.

[0012] 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. According to the former publication, 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. In addition, 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. According to the latter publication, 0.01-0.05% of Cu is added to an IF steel to obtain CuS precipitates and then the CuS precipitates are used as nuclei for precipitation of carbides to reduce the amount of dissolved carbon (C), leading to an improvement in surface defects. According to the prior art, since coarse CuS precipitates are used during production of cold rolled steel sheets, carbides remain in the final products. Further, since emulsion-forming elements, such as Ti and Zr, are added in an amount greater than the amount of sulfur (S) in an atomic weight ratio, a main portion of the sulfur (S) reacts with Ti or Zr rather than Cu.

[0013] On the other hand, Japanese Unexamined Patent Publication Nos. Hei 6-240365 and Hei 7-216340 describe the addition of a combination of Cu and P to improve the corrosion resistance of baking hardening type IF steels. According to these publications, Cu is added in an amount of 0.05-1.0% to ensure improved corrosion resistance. However, in actuality, Cu is added in an excessively large amount of 0.2% or more.

[0014] 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.

[0015] According to the aforementioned publications, strength is enhanced by strengthening solid solution or using ε-Cu precipitates. Cu is used to form ε-Cu precipitates and improve corrosion resistance. In addition, Cu is used as a nucleus for precipitation of carbides. No mention is made in these publications about an increase in high yield ratio (i.e. yield strength/tensile strength) and a reduction in in-plane anisotropy index. If the tensile strength-to-yield strength ratio (i.e. yield ratio) of an IF steel sheet is high, the thickness of the IF steel sheet can be reduced, which is effective in weight reduction. In addition, if the in-plane anisotropy index of an IF steel sheet is low, fewer wrinkles and ears occur during processing and after processing, respectively.

[0016] EP-A-1136575 discloses a method for manufacturing cold-rolled steel sheet which comprises the steps of: rough-rolling a slab using a rough-rolling unit; finish-rolling the sheet bar using a continuous hot finishing-rolling mill; cooling the hot-rolled steel strip on a runout table; coiling thus cooled hot-rolled steel strip; and applying picking, cold-rolling the hot-rolled steel strip, and final annealing to the cold-rolled steel strip.

[Disclosure]

[Technical Problem]

[0017] It is one object of certain embodiments of the present invention to provide Nb and Ti-added IF cold rolled steel sheets that are capable of achieving a high yield ratio and a low in-plane anisotropy index.

[0018] It is another object of certain embodiments of the present invention to provide a process for producing the IF cold rolled steel sheets.

[Technical Solution]

[0019] According to the present invention, there is provided a colled rolled sheet steel of claim 1, 2, 3 or 4.

[0020] When the cold rolled steel sheets of the present invention satisfy the following relationships between the C, Ti, Nb, N and S contents: 0.8 ≤ (Ti*/48 + Nb/93)/(C/12) ≤ 5.0 and Ti* = Ti - 0.8 x ((48/14) x N + (48/32) x S), they show room-temperature non-aging properties. In addition, when solute carbon (Cs) [Cs = (C - Nb x 12/93 - Ti* x 12/48) x 10000 wherein Ti* = Ti - 0.8 x ((48/14) x N + (48/32) x S), provided that when Ti* is less than 0, Ti* is defined as 0], which is determined by the C and Ti contents, is from 5 to 30, the cold rolled steel sheets of the present invention show bake hardenability.

[0021] Depending on the design of the compositions, 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.

[0022] When the content of P in the compositions of the present invention is 0.015% or less, soft cold rolled steel sheets of the order of 280 MPa are produced. When 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. In the case where the cold rolled steel sheets of the present invention contain at least one element selected from Si and Cr, the P content may be freely designed in an amount of 0.2% or less.

[0023] For better workability, the cold rolled steel sheets of the present invention may further contain 0.01-0.2 wt% of Mo.

[0024] According to the present invention, there is provided a process for producing the cold rolled steel sheet of claim 17, 18, 19 or 20.

[Best Mode]

[0025] The present invention will be described in detail below.

[0026] Fine precipitates having a size of 0.2 µm 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".

[0027] The present inventors have found that when fine precipitates are distributed in Nb and Ti-added IF steels (also referred to simply as "Nb-Ti composite 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.

[0028] Regulation of the components in the Nb-Ti composite IF steels is required to obtain (Mn,Cu)S precipitates and/or AlN precipitates. If the IF steels contain Ti, Zr and other elements, S and N preferentially react with Ti and Zr. Since the cold rolled steel sheets of the present invention are Nb-Ti composite IF steels, Ti reacts with C, N and S. Accordingly, it is necessary to regulate the components so that S and N are precipitated into (Mn,Cu)S and AlN forms, respectively.

[0029] 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.

[0030] 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. To this end, 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.

[0031] The constituent components of the cold rolled steel sheets according to the present invention will be explained.

[0032] The content of carbon (C) is preferably limited to 0.01% or less.

[0033] Carbon (C) affects the room-temperature aging resistance and bake hardenability of the cold rolled steel sheets. When the carbon content exceeds 0.01%, the addition of the expensive agents Nb and Ti is required to remove the remaining carbon, which is economically disadvantageous and is undesirable in terms of formability. When it is intended to achieve room-temperature aging resistance only, it is preferred to maintain the carbon content at a low level, which enables the reduction of the amount of the expensive agents Nb and Ti added. When it is intended to ensure desired bake hardenability, the carbon is preferably added in an amount of 0.001% or more, and more preferably 0.005% to 0.01%. When the carbon content is less than 0.005%, room-temperature aging resistance can be ensured without increasing the amounts of Nb and Ti.

[0034] The content of copper (Cu) is preferably in the range of 0.01-0.2%.

[0035] 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. 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%.

[0036] The content of manganese (Mn) is preferably in the range of 0.01-0.3%.

[0037] 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%.

[0038] The content of sulfur (S) is preferably limited to 0.08% or less.

[0039] Sulfur (S) reacts with Cu and/or Mn to form CuS and MnS precipitates, respectively. When the sulfur content is greater than 0.08%, the proportion of dissolved sulfur is increased. This increase of dissolved sulfur greatly deteriorates the ductility and formability of the steel sheets and increases the risk of hot shortness. In order to obtain as many CuS and/or MnS precipitates as possible, a sulfur content of 0.005% or more is preferred.

[0040] The content of aluminum (Al) is preferably limited to 0.1% or less.

[0041] Aluminum reacts with nitrogen (N) to form fine AlN precipitates, thereby completely preventing aging by dissolved nitrogen. When the nitrogen content is 0.004% or more, AlN precipitates are sufficiently formed. The distribution of the fine AlN precipitates in the steel sheets allows the formation of minute crystal grains and enhances the yield strength of the steel sheets by precipitation enhancement. A more preferable Al content is in the range of 0.01 to 0.1%.

[0042] The content of nitrogen (N) is preferably limited to 0.02% or less.

[0043] When it is intended to use AlN precipitates, 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.

[0044] The content of phosphorus (P) is preferably limited to 0.2% or less.

[0045] 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.

[0046] The content of boron (B) is preferably in the range of 0.0001 to 0.002%.

[0047] Boron is added to prevent occurrence of secondary working embrittlement. To this end, a preferable boron content is 0.0001% or more. When the boron content exceeds 0.002%, the deep drawability of the steel sheets may be markedly deteriorated.

[0048] The content of niobium (Nb) is preferably in the range of 0.002 to 0.04%.

[0049] 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. In addition, the NbC precipitates permit the steel sheets to be well textured during annealing, thus greatly improving the deep drawability of the steel sheets. When 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. In contrast, when 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.

[0050] The content of titanium (Ti) is preferably in the range of 0.005 to 0.15%.

[0051] 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. When 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. In contrast, when 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.

[0052] To obtain (Mn,Cu)S and AlN precipitates, the Mn, Cu, S, Nb, Ti, Al, N and C contents are adjusted within the ranges defined by the following relationships. The respective components indicated in the following relationships are expressed as percentages by weight.

[0053] In Relationship 1, S*, which is determined by Relationship 2, represents the content of sulfur that does not react with Ti and thereafter reacts with Cu. To obtain fine CuS precipitates, it is preferred that 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. To stably obtain CuS precipitates having a size of 0.2 µm or less, 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.

[0054] Relationship 3 is associated with the formation of (Mn,Cu)S precipitates, and is obtained by adding a Mn content to Relationship 1. To obtain effective (Mn,Cu)S precipitates, the value of (Mn/55 + Cu/63.5)/(S*/32) must be 1 or greater. When the value of Relationship 3 is greater than 30, coarse (Mn,Cu)S precipitates are obtained. To stably obtain (Mn,Cu)S precipitates having a size of 0.2 µm or less, 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. When Mn and Cu are added together, 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.

[0055] Relationship 4 is associated with the formation of fine (Mn,Cu)S precipitates. In Relationship 4, N*, which is determined by Relationship 5, represents the content of nitrogen that does not react with Ti and thereafter reacts with Al. To obtain fine AlN precipitates, it is preferred that the value of (Al/27)/(N*/14) be in the range of 1-10. To obtain effective AlN precipitates, 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.

[0056] The components of the cold rolled steel sheets according to the present invention may be combined in various ways according to the kind of precipitates to be obtained. For example, the present invention provides a cold rolled steel sheet which has a composition comprising 0.01% or less of C, 0.08% or less of S, 0.1% or less of Al, 0.004% or less of N, 0.2% or less of P, 0.0001-0.002% of B, 0.002-0.04% of Nb, 0.005-0.15% of Ti, at least one kind selected from 0.01-0.2% of Cu, 0.01-0.3% of Mn and 0.004-0.2% of N, by weight, and the balance of Fe and other unavoidable impurities, wherein the composition satisfies the following relationships: 1 ≤ (Mn/55 + Cu/63.5)/(S*/32) ≤ 30, 1 ≤ (Al/27)/(N*/14) ≤ 10 (with the proviso that the N content is 0.004% or more), S* = S - 0.8 x (Ti - 0.8 x (48/14) x N) x (32/48) and N* = N - 0.8 x (Ti - 0.8 x (48/32) x S)) x (14/48), and the steel sheet comprises at least one kind selected from MnS, CuS, MnS and AlN precipitates having an average size of 0.2 µm 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 µm.

[0057] In the steel sheets of the present invention, 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.

[0058] Relationship 6 is associated with the formation of NbC and TiC precipitates to remove the carbon in a solid solution state, thereby achieving room-temperature non-aging properties. In Relationship 6, Ti*, which is determined by Relationship 7, represents the content of titanium that reacts with N and S and thereafter reacts with C.

[0059] When the value of (Ti*/48 + Nb/93)/(C/12) is less than 0.8, it is difficult to ensure room-temperature non-aging properties. In contrast, when the value of (Ti*/48 + Nb/93)/(C/12) 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. When 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. Although the carbon content is more than 0.005%, room-temperature non-aging properties can be achieved when Relationship 6 is satisfied but the amounts of Nb and TiC precipitates are increased, thus deteriorating the workability of the steel sheets.

(provided that when Ti* is less than 0, Ti* is defined as 0.)

[0060] Relationship 8 is associated with the achievement of bake hardenability. Cs, which is expressed in ppm by Relationship 8, represents the content of dissolved carbon that is not precipitated into NbC and TiC forms. 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.

[0061] It is advantageous that the fine precipitates are uniformly distributed in the compositions of the present invention. It is preferable that the precipitates have an average size of 0.2 µm or less. According to a study conducted by the present inventors, when the precipitates have an average size greater than 0.2 µm, the steel sheets have poor strength and low in-plane anisotropy index. Further, large amounts of precipitates having a size of 0.2 µm 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 10⁵/mm² or more, more preferably 1 x 10⁶/mm² or more, and most preferably 1 x 10⁷/mm² or more. The plasticity-anisotropy index is increased and the in-plane anisotropy index is lowered with increasing number of the precipitates, and as a result, the workability is greatly improved. It is commonly known that there is a limitation in increasing the workability because the in-plane anisotropy index is increased with increasing plasticity-anisotropy index. It is worth noting that as the number of the precipitates distributed in the steel sheets of the present invention increases, the plasticity-anisotropy index of the steel sheets is increased and the in-plane anisotropy index of the steel sheets is lowered. The steel sheets of the present invention in which the fine precipitates are formed satisfy a yield ratio (yield strength/tensile strength) of 0.58 or higher.

[0062] @ 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. The addition effects of P have been previously described, and thus their explanation is omitted.

[0063] The content of silicon (Si) is preferably in the range of 0.1 to 0.8%.

[0064] 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.

[0065] The content of chromium (Cr) is preferably in the range of 0.2 to 1.2%.

[0066] 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.

[0067] The cold rolled steel sheets of the present invention may further contain molybdenum (Mo).

[0068] 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%.

[0069] 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.

Production of cold rolled steel sheets

[0070] Hereinafter, a process for producing the cold rolled steel sheets of the present invention will be explained with reference to the preferred embodiments that follow. Various modifications of the embodiments of the present invention can be made, and such modifications are within the scope of the present invention.

[0071] 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 µm or less in a cold rolled sheet. The average size of the precipitates in the cold rolled plate is affected by the design of the steel composition and the processing conditions, such as reheating temperature and winding temperature. Particularly, cooling rate after hot rolling has a direct influence on the average size of the precipitates.

Hot rolling conditions

[0072] In the present invention, 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. When the steel is reheated to a temperature lower than 1,100°C, coarse precipitates formed during continuous casting are not completely dissolved and remain. The coarse precipitates still remain even after hot rolling.

[0073] It is preferred that the hot rolling is performed at a finish rolling temperature not lower than the Ar₃ transformation point. When the finish rolling temperature is lower than the Ar₃ transformation point, rolled grains are created, which deteriorates the workability and causes poor strength.

[0074] The cooling is preferably performed at a rate of 300 °C/min or higher before winding and after hot rolling. Although the composition of the components is controlled to obtain fine precipitates, the precipitates may have an average size greater than 0.2 µm 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. When the cooling rate is higher than 1,000 °C/min., however, a significant improvement in the size reduction effects of the precipitates is not further shown. Therefore, the cooling rate is preferably in the range of 300-1000 °C/min.

Winding conditions

[0075] After the hot rolling, winding is performed at a temperature not higher than 700°C. When the winding temperature is higher than 700°C, the precipitates are grown too coarsely, thus making it difficult to ensure high strength.

Cold rolling conditions

[0076] 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

[0077] Continuous annealing temperature plays an important role in determining the mechanical properties of the final product. According to the present invention, the continuous annealing is preferably performed at a temperature of 700 to 900°C. When 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. In contrast, when 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.

[Mode for Invention]

[0078] The present invention will now be described in more detail with reference to the following examples.

[0079] 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 (Δr value), and the aging index were measured using a tensile strength tester (available from INSTRON Company, Model 6025). The plasticity-anisotropy index r_m and in-plane anisotropy index (Δr value) were calculated by the following equations: r_m = (r₀ + 2r₄₅ + r₉₀)/4 and Δr = (r₀ - 2r₄₅ + r₉₀)/2, respectively.

[0080] 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.

Example 1

[0081] First, 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. At this time, the finish hot rolling was performed at 910°C, which is above the Ar₃ transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830°C for 40 seconds to produce the final cold rolled steel sheets.

TABLE 1

Sample No.	Chemical Components (wt%)
	C	Cu	S	Al	N	P	B	Nb	Ti	Others
A11	0.0006	0.14	0.008	0.032	0.0012	0.048	0.0003	0.014	0.008
A12	0.0017	0.12	0.012	0.043	0.0026	0.082	0.0006	0.02	0.022	Si:0.17
A13	0.0031	0.09	0.012	0.028	0.0016	0.106	0.0012	0.028	0.02	Si:0.28
A14	0.0012	0.118	0.02	0.042	0.0015	0.078	0.0011	0.033	0.033	Si:0.15
										Mo:0.09
A15	0.0018	0.1	0.018	0.036	0.0019	0.085	0.0009	0.04	0.018	Si:0.15
										Cr:0.15
A16	0.0022	0.11	0.01	0.038	0.0015	0.059	0	0	0
A17	0.0012	0	0.011	0.034	0.0027	0.12	0.0008	0.03	0.16

TABLE 2

Sample No.	S*	(Cu/63.5)/(S*/32)	(Ti*/48+Nb/93)/ (C/12)	Average size of CuS precipitates (µm)	Number of CuS precipitates (mm-2)
A11	0.0055	12.854	0.97	0.04	1.5 x 107
A12	0.0041	14.858	1.59	0.05	2.5 x 107
A13	0.0037	12.345	1.26	0.05	3.8 x 107
A14	0.0046	12.943	4.57	0.05	4.1 x 107
A15	0.0112	4.5077	1.64	0.04	5.2 x 107
A16	0.0122	4.5458	-1.8	0.08	4.5 x 106
A17	-0.07	0	32.3	0.08	6.7 x 104
S*=S-0.8x(Ti-0.8x(48/14)xN)x(32/48)
Ti*=Ti-0.8x((48/14)xN+(48/32)xS)

TABLE 3

Sample No.	Mechanical Properties							Remarks
	YS (MPa)	TS (MPa)	El (%)	rm	Δr	AI (%)	SWE (DBTT-°C)
A11	208	345	46	2.32	0.14	0	-70	IS
A12	263	402	39	1.88	0.18	0	-60	IS
A13	332	448	36	1.73	0.12	0	-50	IS
A14	329	452	36	1.84	0.18	0	-50	IS
A15	334	450	37	1.74	0.13	0	-60	IS
A16	232	348	43	1.12	0.29	0.62	-70	CS
A17	270	445	28	1.82	0.48	0	-50	CS

* Note: YS = Yield strength, TS = Tensile Strength, El = Elongation, rm = Plasticity-anisotropy index, Δr = In-plane anisotropy index, AI = Aging Index, SWE = Secondary Working Embrittlement, IS = Inventive Steel, CS = Comparative steel

Example 2

[0082] First, 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. At this time, the finish hot rolling was performed at 910°C, which is above the Ar₃ transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830°C for 40 seconds to produce the final cold rolled steel sheets.

TABLE 4

Sample No.	Chemical Components (wt%)
	C	mn	Cu	S	Al	N	P	B	Nb	Ti	Others
A21	0.0007	0.06	0.08	0.007	0.038	0.0011	0.05	0.0008	0.01	0.009
A22	0.0014	0.15	0.15	0.013	0.027	0.0018	0.082	0.0009	0.02	0.019	Si:0.22
A23	0.0029	0.18	0.12	0.02	0.041	0.0025	0.12	0.0011	0.029	0.028	Si:0.33
A24	0.0015	0.08	0.11	0.018	0.028	0.0026	0.085	0.0009	0.039	0.015	Si:0.22
											Mo:0.11
A25	0.0012	0.13	0.15	0.022	0.032	0.0011	0.073	0.0009	0.005	0.032	Si:0.3
											Cr:0.24
A26	0.0036	0.45	0.14	0.009	0.033	0.0024	0.048	0.005	0	0	Si:0.05
A27	0.0015	0.13	0	0.008	0.038	0.0021	0.118	0	0.04	0.02	Si:0.35

TABLE 5

Sample No.	Cu+Mn	S*	(Mn/55+Cu/63.5)/ (S*/32)	(Ti*/48+Nb/93)/ (C/12)	Average size of (Mn,Cu)S precipitates (pm)	Number of (Mn,Cu)S precipitates (mm-2)
A21	0.14	0.0038	19.748	0.98	0.04	3.3 x 107
A22	0.3	0.0055	29.613	1.57	0.04	4.2 x 107
A23	0.3	0.0087	18.937	1.04	0.03	5.0 x 107
A24	0.19	0.0138	7.3879	1.07	0.04	4.5 x 107
A25	0.28	0.0065	23.115	1.08	0.04	4.9 x 107
A26	0.59	0.0125	26.566	-1.2	0.25	5.5 x 106
A27	0.13	0.0004	186.6	4.21	0.16	4.3 x 104
S*=S-0.8x(Ti-0.8x(48/14)xN)x(32/48)
Ti*=Ti-0.8x((48/14)xN+(48/32)xS)

TABLE 6

Sample No.	Mechanical Properties							Remarks
	YS (MPa)	TS (MPa)	El (%)	rm	Δr	SWE (DBTT-°C)	AI (%)
A21	218	348	45	2.1	0.19	-40	0	IS
A22	262	410	36	1.94	0.17	-40	0	IS
A23	328	455	33	1.89	0.17	-40	0	IS
A24	247	401	35	1.89	0.19	-50	0	IS
A25	229	392	38	1.79	0.17	-40	0	IS
A26	233	359	37	1.11	0.62	-60	1.56	CS
A27	283	425	33	1.81	0.57	-40	0	CS

* Note: YS = Yield strength, TS = Tensile Strength, El = Elongation, rm = Plasticity-anisotropy index, Δr = In-plane anisotropy index, SWE = Secondary Working Embrittlement, AI = Aging Index, IS = Inventive Steel, CS = Comparative steel

Example 3

[0083] First, 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. At this time, the finish hot rolling was performed at 910°C, which is above the Ar₃ transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830°C for 40 seconds to produce the final cold rolled steel sheets.

TABLE 7

Sample No.	Chemical Components (wt%)
	C	Cu	S	Al	N	P	B	Nb	Ti	Others
A31	0.0005	0.08	0.007	0.029	0.0139	0.044	0.0008	0.025	0.038
A32	0.0012	0.13	0.016	0.026	0.011	0.08	0.0008	0.05	0.028	Si:0.11
A33	0.0025	0.14	0.011	0.04	0.0148	0.116	0.0009	0.032	0.051	Si:0.26
A34	0.0013	0.17	0.012	0.031	0.0088	0.047	0.0011	0.043	0.029	Si:0.09
										Mo:0.12
A35	0.0005	0.15	0.015	0.03	0.0089	0.043	0.0009	0.009	0.04	Si:0.11
										Cr:0.22
A36	0.0038	0.09	0.013	0.032	0.0012	0.042	0.0005	0	0
A37	0.0014	0	0.009	0.055	0.012	0.12	0.0005	0	0.14	Si:0.13

TABLE 8

Sample No.	S*	(Cu/63.5)/ (S*/32)	(Ti*/48+Nb/93) /(C/12)	N*	(Al/27)/ (N*14)	Average size of precipitates (µm)	Number of precipitates (mm-2)
A31	0.0071	5.7046	2.19	0.007	2.15	0.04	3.3 x 107
A32	0.0172	3.8181	0.92	0.0089	1.51	0.04	4.2 x 107
A33	0.0055	12.944	1.37	0.006	3.47	0.03	5.0 x 107
A34	0.0094	9.1075	2.43	0.0054	2.98	0.04	4.5 x 107
A35	0.0067	11.306	1.12	0.0038	4.13	0.04	4.9 x 107
A36	0.0148	3.0737	0	0.0048	3.43	0.25	5.5 x 106
A37	0	0	17.2	0	-1.6	0.16	4.3 x 104
S*=S-0.8x(Ti-0.8x(48/14)xN)x(32/48)
Ti*=Ti-0.8x((48/14)xN+(48/32)xS)
N*=N-0.8x(Ti-0.8x(48/32)xS))x(14/48)

TABLE 9

Sample No.	Mechanical Properties							Remarks
	YS (MPa)	Ts (MPa)	El (%)	rm	Δr	SWE (DBTT-°C)	AI (%)
A31	218	348	45	2.1	0.19	-40	0	IS
A32	262	410	36	1.94	0.17	-40	0	IS
A33	328	455	33	1.89	0.17	-40	0	IS
A34	247	401	35	1.89	0.19	-50	0	IS
A35	229	392	38	1.79	0.17	-40	0	IS
A36	233	359	37	1.11	0.62	-60	1.56	CS
A37	283	425	33	1.81	0.57	-40	0	CS

* Note: YS = Yield strength, TS = Tensile Strength, El = Elongation, rm = Plasticity-anisotropy index, Δr = In-plane anisotropy index, SWE = Secondary Working Embrittlement, AI = Aging Index, IS = Inventive Steel, CS = Comparative steel

Example 4

[0084] First, 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. At this time, the finish hot rolling was performed at 910°C, which is above the Ar₃ transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830°C for 40 seconds to produce the final cold rolled steel sheets.

TABLE 10

Sample No.	Chemical Components (wt%)
	C	Mn	Cu	S	Al	N	P	B	Nb	Ti	Others
A41	0.0008	0.07	0.15	0.009	0.025	0.0089	0.045	0.0009	0.018	0.03	Si:0.03
A42	0.0015	0.15	0.12	0.014	0.034	0.011	0.082	0.001	0.039	0.039	Si:0.12
A43	0.0028	0.12	0.16	0.011	0.029	0.0109	0.118	0.0007	0.03	0.038	Si:0.09
A44	0.0012	0.15	0.1	0.02	0.03	0.013	0.035	0.0011	0.012	0.063	Si:0.12
											Mo:0.09
A45	0.0019	0.13	0.14	0.017	0.053	0.0132	0.034	0.0008	0.045	0.05	Si:0.09
											Cr:0.22
A46	0.0034	0.45	0.1	0.0083	0.038	0.0015	0.048	0.0005	0	0
A47	0.0038	0.07	0	0.012	0.035	0.0024	0.13	0.0005	0	0.17	Si:0.08

TABLE 11

Sample No.	Cu+Mn	S*	(Mn/55+C u/63.5)/ (S*/32)	(Ti*/48+Nb/ 93)/(C/12)	N*	(Al/27) /(N*14)	Average size of precipitates (µm)	Number of precipitates (mm-2)
A41	0.22	0.006	19.324	1.27	0.0044	2.93	0.04	9.4 x 107
A42	0.27	0.0093	15.901	2.03	0.0058	3.03	0.03	9.0 x 107
A43	0.28	0.0067	22.527	0.93	0.0051	2.94	0.04	8.2 x 107
A44	0.25	0.0054	25.413	1.99	0.0039	3.99	0.04	7.9 x 107
A45	0.27	0.0096	15.16	2.19	0.0063	4.37	0.03	9.6 x 107
A46	0.55	0.0105	29.751	-1	0.0038	5.15	0.25	1.5 x 104
A47	0.07	0	0	9.8	0	0	0.04	3.5 x 105
S*=S-0.8x(Ti-0.8x(48/14)xN)x(32/48)
Ti*=Ti-0.8x((48/14)xN+(48/32)xS)
N*=N-0.8x(Ti-0.8x(48/32)xS))x(14/48)

TABLE 12

Sample No.	Mechanical Properties							Remarks
	YS (MPa)	TS (MPa)	El (%)	rm	Δr	AI (%)	SWE (DBTT-°C)
A41	222	357	43	2.22	0.09	0	-70	IS
A42	260	409	35	1.93	0.06	0	-60	IS
A43	332	453	34	1.73	0.06	0	-60	IS
A44	229	367	40	2.18	0.08	0	-60	IS
A45	231	359	45	1.89	0.07	0	-50	IS
A46	202	355	38	1.59	0.39	0	-60	CS
A47	338	458	24	1.31	0.58	0.55	-70	CS

* Note: YS = Yield strength, TS = Tensile Strength, El = Elongation, rm = Plasticity-anisotropy index, Δr = In-plane anisotropy index, AI = Aging Index, SWE = Secondary Working Embrittlement, IS = Inventive Steel, CS = Comparative steel

Example 5

[0085] First, 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. At this time, the finish hot rolling was performed at 910°C, which is above the Ar₃ transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830°C for 40 seconds to produce the final cold rolled steel sheets.

TABLE 13

Sample No.	Chemical Components (wt%)
	C	Mn	P	S	Al	Ti	Nb	B	N	Others
A51	0.0009	0.08	0.008	0.006	0.042	0.008	0.017	0.0005	0.0018
A52	0.0016	0.12	0.059	0.012	0.033	0.016	0.025	0.0008	0.0012	Si:0.11
A53	0.0026	0.12	0.094	0.021	0.043	0.026	0.039	0.0011	0.0033	Si:0.31
A54	0.0012	0.11	0.129	0.013	0.033	0.016	0.038	0.0009	0.0012	Si:0.26
										Mo:0.14
A55	0.0015	0.13	0.053	0.021	0.039	0.032	0.011	0.0009	0.0011	Si:0.33
										Cr:0.24
A56	0.0028	0.48	0.052	0.009	0.033	0.022	0.021	0.0005	0.0024	Si:0.05
A57	0.0015	0.13	0.118	0.008	0.038	0	0	0	0.0021	Si:0.35

TABLE 14

Sample No.	S*	(Mn/55) / (S*/32)	(Ti*/48+Nb/93) / (C/12)	Average size of precipitates (µm)	Number of precipitates (mm-2)
A51	0.0044	10.66	1.29	0.06	3.8 x 106
A52	0.0052	13.37	1.75	0.06	4.6 x 106
A53	0.012	5.8373	1.14	0.05	5.2 x 106
A54	0.0062	10.286	3.48	0.06	4.1 x 106
A55	0.0055	13.647	1.58	0.06	3.9 x 106
A56	0.0008	359.18	1.38	0.28	1.2 x 104
A57	0.0111	6.8313	-2.6	0.18	6.3 x 105
S*=S-0.8x(Ti-0.8x(48/14)xN)x(32/48)
Ti*=Ti-0.8x((48/14)xN+(48/32)xS)

TABLE 15

Sample No.	Mechanical Properties							Remarks
	YS (MPa)	TS (MPa)	El (%)	rm	(Δr)	AI (%)	SWE (DBTT-°C)
A51	188	302	49	2.09	0.25	0	-60	IS
A52	221	352	42	1.93	0.22	0	-50	IS
A53	256	409	38	1.73	0.19	0	-40	IS
A54	270	444	34	1.69	0.21	0	-40	IS
A55	231	362	43	1.87	0.21	0	-50	IS
A56	202	356	41	1.85	0.29	0	-40	CS
A57	254	401	37	1.28	0.54	2.33	-40	CS

* Note: YS = Yield strength, TS = Tensile Strength, El = Elongation, rm = Plasticity-anisotropy index, Δr = In-plane anisotropy index, AI = Aging Index, SWE = Secondary Working Embrittlement, IS = Inventive Steel, CS = Comparative steel

Example 6

[0086] First, 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. At this time, the finish hot rolling was performed at 910°C, which is above the Ar₃ transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830°C for 40 seconds to produce the final cold rolled steel sheets.

TABLE 16

Sample No.	Chemical Components (wt%)
	C	P	S	Al	Ti	Nb	B	N	Others
A61	0.0007	0.01	0.009	0.042	0.039	0.03	0.0008	0.011
A62	0.0015	0.037	0.017	0.053	0.029	0.042	0.0009	0.0074	Si:0.11
A63	0.0028	0.073	0.012	0.049	0.048	0.039	0.0009	0.0123	Si:0.22
A64	0.0014	0.119	0.011	0.038	0.029	0.044	0.0011	0.0085	Si:0.12
									Mo:0.12
A65	0.0007	0.035	0.016	0.037	0.04	0.022	0.0009	0.0089	Si:0.11
									Cr:0.27
A66	0.0025	0.074	0.011	0.039	0.025	0.022	0.0005	0.0018	Si:0.05
A67	0.0015	0.053	0.012	0.038	0	0	0	0.0026	Si:0.35

TABLE 17

Sample No.	(Ti*/48+Nb/93) /(C/12)	N*	(Al/27)/(N* /14)	Average size of precipitates (µm)	Number of precipitates
A61	4.83	0.0044	4.93	0.05	6.8 x 105
A62	1.66	0.0054	5.1	0.05	5.3 x 105
A63	1.78	0.0045	5.7	0.05	7.2 x 105
A64	2.71	0.0048	4.09	0.05	5.5 x 105
A65	2.77	0.004	4.74	0.05	6.3 x 105
A66	1.82	-0.001	-21	0.05	2.8 x 104
A67	0	0.006	3.31	0.05	3.3 x 104
Ti*=Ti-0.8x((48/14)xN+(48/32)xS)
N*=N-0.8x(Ti-0.8x(48/32)xS))x(14/48)

TABLE 18

Sample	Mechanical Properties							Remarks
No.	YS (MPa)	TS (MPa)	El (%)	rm	Δr	SWE (DBTT-°C)	AI (%)
A61	218	352	43	2.03	0.25	-60	0	IS
A62	228	369	42	1.82	0.24	-50	0	IS
A63	269	417	36	1.73	0.27	-50	0	IS
A64	289	452	33	1.71	0.29	-50	0	IS
A65	222	358	40	1.83	0.21	-60	0	IS
A66	202	356	40	1.92	0.34	-40	0	CS
A67	254	401	37	1.28	0.54	-40	2.33	CS

* Note: YS = Yield strength, TS = Tensile Strength, El = Elongation, rm = Plasticity-anisotropy index, Δr = In-plane anisotropy index, SWE = Secondary Working Embrittlement, AI = Aging Index, IS = Inventive Steel, CS = Comparative steel

Example 7

[0087] First, 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. At this time, the finish hot rolling was performed at 910°C, which is above the Ar₃ transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830°C for 40 seconds to produce the final cold rolled steel sheets.

TABLE 19

Sample No.	Chemical Components (wt%)
	C	mn	P	S	Al	Ti	Nb	B	N	Others
A71	0.0007	0.09	0.009	0.012	0.039	0.028	0.025	0.0006	0.0084
A72	0.0017	0.14	0.038	0.015	0.039	0.041	0.047	0.0005	0.0109	Si:0.14
A73	0.0025	0.16	0.078	0.012	0.047	0.039	0.029	0.0007	0.011
A74	0.0014	0.09	0.12	0.021	0.043	0.063	0.013	0.0011	0.0128	Si:0.12
										Mo:0.11
A75	0.0015	0.13	0.042	0.016	0.059	0.052	0.048	0.0009	0.013	Si:0.1
										Cr:0.29
A76	0.0028	0.48	0.052	0.009	0.033	0.022	0.021	0.0005	0.0024	Si:0.05
A77	0.0015	0.13	0.118	0.008	0.038	0	0	0	0.0021	Si:0.35

TABLE 20

Sample No.	S*	(Mn/55) /(S*/32)	(Ti*/48+N b/93)/(C/ 12)	N*	(Al/27) /(N*/14)	Average size of precipitates (µm)	Number of precipitates (mm-2)
A71	0.0094	5.5976	1.24	0.0052	3.87	0.05	2.9 x 107
A72	0.0091	8.9723	2.55	0.0055	3.65	0.05	3.5 x 107
A73	0.0073	12.767	0.94	0.0053	4.63	0.05	3.3 x 107
A74	0.0061	8.5498	1.68	0.004	5.6	0.04	4.5 x 107
A75	0.0073	10.384	3.65	0.0053	5.72	0.04	4.2 x 107
A76	0.0008	359.18	1.38	-2E-04	-80	0.28	1.2 x 104
A77	0.0111	6.8313	0	0.0043	4.54	0.18	6.3 x 105
S*=S-0.8x(Ti-0.8x(48/14)xN)x(32/48)
Ti*=Ti-0.8x((48/14)xN+(48/32)xS)
N*=N-0.8x(Ti-0.8x(48/32)xS))x(14/48)

TABLE 21

Sample No.	Mechanical Properties							Remarks
	YS (MPa)	TS (MPa)	El (%)	rm	Δr	SWE (DBTT-°C)	AI (%)
A71	215	347	46	2.1	0.25	-60	0	IS
A72	254	404	38	1.91	0.27	-40	0	IS
A73	265	411	36	1.61	0.22	-50	0	IS
A74	292	450	32	1.65	0.24	-50	0	IS
A75	246	395	37	1.67	0.22	-50	0	IS
A76	202	356	41	1.85	0.29	-40	0	CS
A77	254	401	37	1.28	0.54	-40	2.33	CS

* Note: YS = Yield strength, TS = Tensile Strength, El = Elongation, rm = Plasticity-anisotropy index, Δr = In-plane anisotropy index, AI = Aging Index, SWE = Secondary Working Embrittlement, IS = Inventive Steel, CS = Comparative steel

Example 8

[0088] First, 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. At this time, the finish hot rolling was performed at 910°C, which is above the Ar₃ transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830°C for 40 seconds to produce the final cold rolled steel sheets.

TABLE 22

Sample No.	Chemical components (wt%)
	C	P	S	Al	Cu	Ti	Nb	B	N	Others
B81	0.0017	0.009	0.009	0.039	0.11	0.005	0.005	0.0005	0.0012
B82	0.0016	0.032	0.007	0.042	0.09	0.004	0.004	0.0007	0.0021
B83	0.0018	0.048	0.01	0.034	0.09	0.005	0.004	0.0004	0.0005	Si:0.05
B84	0.0026	0.083	0.011	0.038	0.09	0.012	0.005	0.0008	0.0021	Si:0.15
B85	0.0028	0.11	0.012	0.042	0.14	0.02	0.006	0.001	0.0022	Si:0.26
B86	0.0025	0.086	0.008	0.042	0.1	0.01	0.005	0.0007	0.0016	Si:0.19
										Mo:0.071
B87	0.0025	0.084	0.01	0.033	0.15	0.009	0.004	0.0006	0.0016	Si:0.21
										Cr:0.21
B88	0.0017	0.065	0.012	0.035	0.11	0.033	0.02	0.0009	0.0012
B89	0.0039	0.123	0.011	0.035	0	0	0	0.0008	0.0025

TABLE 23

Sample No.	(Cu/63.5)/(S*/32)	Cs	Average size of precipitates (µm)	Number of precipitates (mm-2)
B81	6.85	17	0.06	3.3 x 106
B82	5.71	16	0.06	3.5 x 106
B83	5.62	18	0.06	3.1 x 106
B84	5.91	26	0.05	4.5 x 106
B85	15.5	21.3	0.05	4.8 x 106
B86	10.1	25	0.05	5.2 x 106
B87	10	25	0.05	4.1 x 106
B88	-14	-36	0.08	2.5 x 106
B89	0	39	0.08	6.2 x 104
S*=S-0.8x(Ti-0.8x(48/14)xN)x(32/48)
Cs=(C-Nbx12/93-Ti*x12/48)x10000,
Ti*=Ti-0.8x((48/14)xN+(48/32)xS)

TABLE 24

Sample No.	Mechanical Properties								Remarks
	YS (MPa)	TS (MPa)	El (%)	rm	Δr	AI (%)	BH value (MPa)	SWE (DBTT-°C)
B81	189	308	49	2.04	0.31	0	42	-40	IS
B82	193	320	45	2.01	0.34	0	44	-50	IS
B83	209	352	43	1.93	0.28	0	37	-40	IS
B84	276	406	39	1.78	0.25	0	58	-50	IS
B85	335	450	35	1.62	0.19	0	55	-60	IS
B86	329	452	36	1.55	0.21	0	49	-50	IS
B87	333	449	34	1.66	0.24	0	45	-50	IS
B88	210	346	42	1.98	0.22	0	0	-50	CS
B89	285	463	29	1.22	0.28	3.9	89	-70	CS

* Note: YS = Yield strength, TS = Tensile Strength, El = Elongation, rm = Plasticity-anisotropy index, Δr = In-plane anisotropy index, AI = Aging Index, SWE = Secondary Working Embrittlement, IS = Inventive Steel, CS = Comparative steel

Example 9

[0089] First, 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. At this time, the finish hot rolling was performed at 910°C, which is above the Ar₃ transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830°C for 40 seconds to produce the final cold rolled steel sheets.

TABLE 25

Sample No.	Chemical Components (wt%)
	C	Mn	P	S	Al	Cu	Ti	Nb	B	N	Others
B91	0.0018	0.11	0.009	0.008	0.038	0.06	0.007	0.004	0.0005	0.0019
B92	0.0016	0.1	0.023	0.01	0.042	0.11	0.009	0.005	0.0008	0.0022
B93	0.0015	0.09	0.042	0.011	0.028	0.08	0.006	0.005	0.0006	0.0005	Si:0.1
B94	0.0021	0.11	0.08	0.009	0.041	0.11	0.011	0.012	0.0008	0.0012	Si:0.22
B95	0.0028	0.12	0.1	0.008	0.031	0.16	0.011	0.009	0.0005	0.002	Si:0.31
B96	0.0019	0.09	0.081	0.011	0.042	0.11	0.005	0.008	0.0011	0.0029	Si:0.25
											Mo:0.15
B97	0.0023	0.1	0.078	0.008	0.035	0.13	0.007	0.005	0.0008	0.002	Si:0.3
											Cr:0.27
B98	0.0025	0.55	0.05	0.009	0.037	0	0.022	0.018	0.0009	0.0028
B99	0.0041	0.11	0.116	0.017	0.038	0.08	0	0	0.009	0.0021	Si:0.33

TABLE 26

Sample No.	Cu+Mn	(Mn/55+Cu/63.5)/(S*/32)	Cs	Average size of precipitates (µm)	Number of precipitates (mm-2)
B91	0.17	13.4	18	0.05	3.5 x 106
B92	0.21	13.5	16	0.05	3.7 x 106
B93	0.17	10.9	15	0.05	3.3 x 106
B94	0.22	24.4	13.2	0.05	5.2 x 106
B95	0.28	29.7	26.6	0.05	5.5 x 106
B96	0.2	8.57	19	0.05	4.3 x 106
B97	0.23	17.2	23	0.04	5.9 x 106
B98	0.55	235	4.52	0.29	2.5 x 104
B99	0.19	5.2	41	0.06	2.7 x 105
S*=S-0.8x(Ti-0.8x(48/14)xN)x(32/48)
Cs=(C-Nbx12/93-Ti*x12/48)x10000,
Ti*=Ti-0.8x((48/14)xN+(48/32)xS)

TABLE 27

Sample No.	Mechanical Properties								Remarks
	YS (MPa)	TS (MPa)	El (%)	rm	Δr	AI	BH value (MPa)	SWE (DBTT-°C)
B91	197	308	47	1.95	0.31	0	42	-40	IS
B92	210	332	47	1.92	0.29	0	35	-50	IS
B93	222	350	45	1.92	0.27	0	35	-50	IS
B94	292	405	39	1.71	0.22	0	44	-60	IS
B95	341	456	35	1.65	0.2	0	61	-50	IS
B96	338	452	34	1.62	0.23	0	42	-60	IS
B97	333	457	35	1.61	0.22	0	46	-50	IS
B98	193	347	41	1.99	0.35	0	0	-50	CS
B99	327	446	32	1.17	0.2	5.3	93	-60	CS

* Note: YS = Yield strength, TS = Tensile Strength, El = Elongation, rm = Plasticity-anisotropy index, Δr = In-plane anisotropy index, AI = Aging Index, SWE = Secondary Working Embrittlement, IS = Inventive Steel, CS = Comparative steel

Example 10

[0090] First, 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. At this time, the finish hot rolling was performed at 910°C, which is above the Ar₃ transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830°C for 40 seconds to produce the final cold rolled steel sheets.

TABLE 28

Sample No.	Chemical Components (wt%)
	C	P	S	Al	Cu	Ti	Nb	B	N	Others
B01	0.0015	0.008	0.008	0.052	0.09	0.009	0.004	0.0006	0.0073
B02	0.0017	0.022	0.01	0.038	0.11	0.01	0.004	0.0009	0.011
B03	0.0018	0.045	0.008	0.032	0.12	0.005	0.003	0.0005	0.0075	Si:0.07
B04	0.0023	0.081	0.011	0.052	0.13	0.011	0.004	0.001	0.0103	Si:0.14
B05	0.0026	0.118	0.011	0.028	0.16	0.021	0.005	0.0009	0.012	Si:0.2
B06	0.0021	0.046	0.021	0.052	0.09	0.038	0.004	0.0009	0.0118	Mo:0.082
B07	0.0015	0.045	0.008	0.067	0.12	0.011	0.003	0.0007	0.0071	Cr:0.23
B08	0.0022	0.044	0.01	0.028	0	0.021	0.022	0.0009	0.0015
B09	0.0042	0.12	0.009	0.052	0.13	0	0	0.0008	0.0073	Si:0.15

TABLE 29

Sample No.	(Cu/63.5)/(S*/32)	(Al/27)/(N*/14)	Cs	Average size of precipitates (µm)	Number of precipitates (mm-2)
B01	3.27	3.624	15	0.06	2.7 x 106
B02	2.67	1.718	17	0.06	3.9 x 106
B03	3.71	1.935	18	0.06	3.6 x 106
B04	3.24	2.493	23	0.05	6.4 x 106
B05	4.65	1.426	26	0.05	8.3 x 106
B06	2.52	3.059	21	0.05	8.5 x 106
B07	4.83	5.129	15	0.04	7.9 x 106
B08	0	-24.2	-8.5	0.2	3.7 x 104
B09	3.33	2.746	42	0.05	5.1 x 106
S*=S-0.8x(Ti-0.8x(48/14)xN)x(32/48)
Cs=(C-Nbx12/93-Ti*x12/48)x10000,
Ti*=Ti-0.8x((48/14)xN+(48/32)xS)
N*=N-0.8x(Ti-0.8x(48/32)xS))x(14/48)

TABLE 30

Sample No.	Mechanical Properties								Remarks
	YS (MPa)	TS (MPa)	El (%)	rm	Δr	AI	BH value (MPa)	SWE (DBTT-°C)
B01	201	315	48	2.05	0.29	0	38	-40	IS
B02	213	347	46	1.96	0.27	0	42	-50	IS
B03	212	353	42	1.93	0.27	0	38	-40	IS
B04	294	418	35	1.79	0.24	0	53	-50	IS
B05	323	451	34	1.69	0.21	0	48	-40	IS
B06	254	394	38	1.79	0.28	0	55	-50	IS
B07	231	387	37	1.71	0.27	0	35	-40	IS
B08	205	348	40	2.03	0.46	0	0	-50	CS
B09	299	452	31	1.21	0.17	4.4	84	-40	CS

* Note: YS = Yield strength, TS = Tensile Strength, El = Elongation, rm = Plasticity-anisotropy index, Δr = In-plane anisotropy index, AI = Aging Index, SWE = Secondary Working Embrittlement, IS = Inventive Steel, CS = Comparative steel

Example 11

[0091] First, 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. At this time, the finish hot rolling was performed at 910°C, which is above the Ar₃ transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830°C for 40 seconds to produce the final cold rolled steel sheets.

TABLE 31

Sample No.	Chemical Components (wt%)
	C	Mn	P	S	Al	Cu	Ti	Nb	B	N	Others
B11	0.0014	0.11	0.008	0.008	0.042	0.08	0.009	0.004	0.0007	0.0072
B12	0.0019	0.08	0.0028	0.008	0.036	0.11	0.011	0.004	0.0005	0.011
B13	0.0015	0.09	0.043	0.007	0.034	0.09	0.01	0.003	0.0009	0.011	Si:0.09
B14	0.0024	0.11	0.082	0.009	0.042	0.13	0.01	0.004	0.0011	0.012	Si:0.12
B15	0.0027	0.08	0.11	0.008	0.067	0.12	0.025	0.006	0.0009	0.0087	Si:0.1
B16	0.0025	0.15	0.037	0.012	0.073	0.14	0.02	0.005	0.0009	0.0072	Si:0.11
											Mo:0.087
B17	0.0022	0.1	0.037	0.012	0.041	0.13	0.009	0.004	0.0007	0.014	Si:0.13
											Cr:0.31
B18	0.0013	0.55	0.044	0.007	0.03	0	0.03	0.012	0.0005	0.0027
B19	0.0045	0.08	0.121	0.013	0.04	0.15	0	0	0.0008	0.0018

TABLE 32

Sample No.	Cu+Mn	(Mn/55+Cu/63. 5)/(S*/32)	(Al/27)/(N*/ 14)	Cs	Average size of precipitates (µm)	Number of precipitates (mm-2)
B11	0.19	7.6	2.967	14	0.06	2.3 x 107
B12	0.19	5.6	1.749	19	0.06	2.9 x 107
B13	0.18	5.5	1.659	15	0.06	2.5 x 107
B14	0.24	6.1	1.787	24	0.05	4.2 x 107
B15	0.2	14.5	6.803	27	0.05	2.9 x 107
B16	0.29	13.3	6.423	25	0.05	3.1 x 107
B17	0.23	4.47	1.393	22	0.04	3.4 x 107
B18	0.55	-63	-6.65	-28	0.27	1.2 x 104
B19	0.23	7.81	3.813	45	0.06	9.5 x 105
S*=S-0.8x(Ti-0.8x(48/14)xN)x(32/48)
Cs=(C-Nbx12/93-Ti*x12/48)x10000,
Ti*=Ti-0.8x((48/14)xN+(48/32)xS)
N*=N-0.8x(Ti-0.8x(48/32)xS))x(14/48)

TABLE 33

Sample No.	Mechanical Properties								Remarks
	YS (MPa)	TS (MPa)	El (%)	rm	Δr	AI	BH value (MPa)	SWE (DBTT-°C)
B11	192	320	48	2.06	0.31	0	37	-40	IS
B12	211	349	46	1.98	0.29	0	48	-60	IS
B13	221	359	42	1.93	0.27	0	33	-60	IS
B14	252	403	37	1.78	0.27	0	45	-50	IS
B15	321	457	34	1.62	0.31	0	58	-60	IS
B16	234	355	41	1.88	0.27	0	51	-60	IS
B17	222	351	42	1.87	0.3	0	51	-50	IS
B18	189	359	42	1.95	0.38	0	0	-50	CS
B19	336	461	27	1.27	0.21	3.5	96	-60	CS

* Note: YS = Yield strength, TS = Tensile Strength, El = Elongation, rm = Plasticity-anisotropy index, Δr = In-plane anisotropy index, AI = Aging Index, SWE = Secondary Working Embrittlement, IS = Inventive Steel, CS = Comparative steel

Example 12

[0092] First, 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. At this time, the finish hot rolling was performed at 910°C, which is above the Ar₃ transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830°C for 40 seconds to produce the final cold rolled steel sheets.

TABLE 34

Sample No.	Chemical Components (wt%)
	C	Mn	P	S	Al	Ti	Nb	B	N	Others
B21	0.0018	0.09	0.011	0.009	0.036	0.011	0.004	0.0005	0.0019
B22	0.0015	0.07	0.054	0.012	0.042	0.012	0.003	0.0007	0.0016
B23	0.0023	0.1	0.064	0.009	0.023	0.01	0.004	0.0008	0.0021	Si:0.15
B24	0.0025	0.07	0.11	0.009	0.037	0.008	0.005	0.0005	0.003
B25	0.0028	0.12	0.09	0.01	0.024	0.015	0.006	0.0011	0.0015	Mo:0.1
B26	0.0024	0.12	0.095	0.008	0.031	0.014	0.004	0.001	0.0016	Cr:0.19
B27	0.0019	0.47	0.042	0.011	0.03	0.028	0.016	0.0007	0.002
B28	0.0042	0.32	0.12	0.01	0.024	0	0	0.0014	0.0013

TABLE 35

Sample No.	(Mn/55)/(S*/32)	Cs	Average size of precipitates (µm)	Number of precipitates (mm-2)
B21	8.86	18	0.06	1.9 x 105
B22	5.13	15	0.06	1.8 x 105
B23	8.63	23	0.05	2.7 x 105
B24	4.46	25	0.05	3.3 x 106
B25	16.6	23	0.05	2.9 x 106
B26	24.3	18.8	0.04	4.1 x 106
B27	-271	-13	0.28	1.1 x 104
B28	15.6	42	0.22	7.4 x 103
S*=S-0.8x(Ti-0.8x(48/14)xN)x(32/48)
Cs=(C-Nbx12/93-Ti*x12/48)x10000,
Ti*=Ti-0.8x((48/14)xN+(48/32)xS)

TABLE 36

Sample No.	Mechanical Properties								Remarks
	YS (MPa)	TS (MPa)	El (%)	rm	Δr	AI (%)	BH value (MPa)	SWE (DBTT-°C)
B21	188	305	49	2.18	0.34	0	48	-40	IS
B22	221	350	43	2.09	0.3	0	33	-50	IS
B23	245	397	37	1.88	0.29	0	43	-50	IS
B24	316	444	33	1.62	0.26	0	54	-50	IS
B25	275	452	33	1.55	0.24	0	55	-40	IS
B26	319	446	31	1.5	0.21	0	49	-50	IS
B27	219	362	38	2.09	0.37	0	0	-50	CS
B28	251	466	26	1.2	0.19	4.2	87	-60	CS

* Note: YS = Yield strength, TS = Tensile Strength, El = Elongation, rm = Plasticity-anisotropy index, Δr = In-plane anisotropy index, AI = Aging Index, SWE = Secondary Working Embrittlement, IS = Inventive Steel, CS = Comparative steel

Example 13

[0093] First, 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. At this time, the finish hot rolling was performed at 910°C, which is above the Ar₃ transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830°C for 40 seconds to produce the final cold rolled steel sheets.

TABLE 37

Sample No.	Chemical Components (wt%)
	C	P	S	Al	Ti	Nb	B	N	Others
B31	0.0019	0.009	0.01	0.047	0.008	0.004	0.0005	0.0094
B32	0.0017	0.047	0.01	0.059	0.009	0.003	0.0008	0.0072	Si:0.03
B33	0.0024	0.086	0.008	0.067	0.016	0.003	0.001	0.0068	Si:0.11
B34	0.0026	0.118	0.012	0.047	0.027	0.005	0.0009	0.0125	Si:0.25
B35	0.0024	0.037	0.01	0.051	0.036	0.003	0.0007	0.011	Si:0.26
									Mo:0.074
B36	0.0026	0.115	0.009	0.039	0.01	0.005	0.0011	0.01	Si:0.22
									Cr:0.23
B37	0.0022	0.057	0.011	0.035	0.02	0.024	0.0007	0.0011
B38	0.0045	0.125	0.015	0.042	0	0	0.0008	0.012

TABLE 38

Sample No.	(Al/27)/(N*/14)	Cs	Average size of precipitates (pm)	Number of precipitates (mm-2)
B31	2.358	19	0.06	5.1 x 106
B32	3.872	17	0.06	4.3 x 106
B33	6.547	24	0.05	4.4 x 106
B34	2.549	26	0.05	6.3 x 106
B35	4.897	24	0.05	5.2 x 106
B36	1.985	26	0.04	7.4 x 106
B37	19.87	8.3	0.29	1.1 x 104
B38	1.344	45	0.06	2.8 x 106
Cs=(C-Nbx12/93-Ti*x12/48)x10000,
Ti*=Ti-0.8x((48/14)xN+(48/32)xS)
N*=N-0.8x(Ti-0.8x(48/32)xS))x(14/48)

TABLE 39

Sample No.	Mechanical Properties								Remarks
	YS (MPa)	TS (MPa)	El (%)	rm	Δr	AI (%)	BH value (MPa)	SWE (DBTT-°C)
B31	221	325	47	2.02	0.31	0	43	-40	IS
B32	232	352	44	1.87	0.27	0	35	-50	IS
B33	263	409	37	1.76	0.26	0	58	-50	IS
B34	325	450	31	1.7	0.28	0	58	-50	IS
B35	232	358	42	1.81	0.29	0	49	-50	IS
B36	334	463	31	1.55	0.28	0	58	-50	IS
B37	205	369	38	2.11	0.33	0	0	-40	CS
B38	343	461	29	1.19	0.22	4.3	109	-40	CS

* Note: YS = Yield strength, TS = Tensile Strength, El = Elongation, rm = Plasticity-anisotropy index, Δr = In-plane anisotropy index, AI = Aging Index, SWE = Secondary Working Embrittlement, IS = Inventive Steel, CS = Comparative steel

Example 14

[0094] First, 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. At this time, the finish hot rolling was performed at 910°C, which is above the Ar₃ transformation point, and the continuous annealing was performed by heating the hot rolled steel sheets at a rate of 10 °C/second to 830°C for 40 seconds to produce the final cold rolled steel sheets.

TABLE 40

Sample No.	Chemical Components (wt%)
	C	Mn	P	S	Al	Ti	Nb	B	N	Others
B41	0.0012	0.11	0.009	0.008	0.052	0.009	0.004	0.0005	0.0072
B42	0.0017	0.09	0.024	0.011	0.039	0.011	0.003	0.0009	0.013
B43	0.0014	0.07	0.046	0.006	0.067	0.019	0.003	0.0007	0.0069	Si:0.04
B44	0.0022	0.12	0.073	0.01	0.039	0.013	0.005	0.0005	0.0103	Si:0.1
B45	0.0022	0.08	0.113	0.01	0.05	0.029	0.004	0.001	0.012	Si:0.11
B46	0.0027	0.09	0.038	0.012	0.048	0.035	0.005	0.0008	0.0093	Si:0.21
										Mo:0.083
B47	0.0025	0.13	0.04	0.011	0.048	0.018	0.003	0.0011	0.011	Cr:0.26
B48	0.0028	0.68	0.043	0.013	0.038	0.03	0.02	0.0005	0.0021
B49	0.0044	0.08	0.12	0.009	0.025	0	0	0.0011	0.0067	Si:0.05

TABLE 41

Sample No.	(Mn/55)/(S*/32)	(Al/27)/(N*/14)	Cs	Average size of precipitates (pm)	Number of precipitates (mm-2)
B41	4.66	3.673	12	0.05	5.2 x 106
B42	2.17	1.496	17	0.05	7.5 x 106
B43	6.83	8.378	14	0.05	6.7 x 106
B44	3.85	2.009	22	0.05	6.9 x 106
B45	3.85	3.227	22	0.04	9.6 x 106
B46	7.55	5.539	27	0.05	5.9 x 106
B47	4.32	2.519	25	0.05	7.8 x 106
B48	5495	-15.6	-6.1	0.21	1.2 x 104
B49	2.48	1.406	44	0.06	8.7 x 105
S*=S-0.8x(Ti-0.8x(48/14)xN)x(32/48)
Cs=(C-Nbx12/93-Ti*x12/48)x10000,
Ti*=Ti-0.8x((48/14)xN+(48/32)xS)
N*=N-0.8x(Ti-0.8x(48/32)xS))x(14/48)

TABLE 42

Sample No.	Mechanical Properties								Remarks
	YS (MPa)	TS (MPa)	El (%)	rm	Δr	AI (%)	BH value (MPa)	SWE (DBTT-°C)
B41	196	308	48	2.03	0.3	0	37	-40	IS
B42	211	349	47	1.92	0.29	0	47	-50	IS
B43	220	362	43	1.87	0.31	0	38	-50	IS
B44	263	390	37	1.7	0.28	0	44	-40	IS
B45	320	457	32	1.62	0.21	0	51	-60	IS
B46	231	364	43	1.73	0.31	0	57	-50	IS
B47	218	360	44	1.61	0.28	0	53	-50	IS
B48	209	359	39	1.92	0.37	0	0	-40	CS
B49	356	471	28	1.25	0.18	5.6	93	-60	CS

* Note: YS = Yield strength, TS = Tensile Strength, El = Elongation, rm = Plasticity-anisotropy index, Δr = In-plane anisotropy index, AI = Aging Index, SWE = Secondary Working Embrittlement, IS = Inventive Steel, CS = Comparative steel

[0095] The preferred embodiments illustrated in the present invention do not serve to limit the present invention, but are set forth for illustrative purposes. Any embodiment having substantially the same constitution and the same operational effects thereof as the technical spirit of the present invention as defined in the appended claims is encompassed within the technical scope of the present invention.

[Industrial Applicability]

[0096] As apparent from the above description, according to the cold rolled steel sheets of the present invention, the distribution of fine precipitates in Nb-Ti composite IF steels allows the formation of minute crystal grains, and as a result, the in-plane anisotropy index is lowered and the yield strength is enhanced by precipitation enhancement.

Claims

1. A cold rolled steel sheet with superior formability and high yield ratio, the cold rolled steel sheet having a composition comprising 0.01% or less of C, 0.01-0.2% of Cu, 0.005-0.08% of S, 0.1% or less of Al, 0.004% or less of N, 0.2% or less of P, 0.0001-0.002% of B, 0.002-0.04% of Nb, 0.005-0.15% of Ti, optionally at least one of 0.1-0.8% of Si and 0.2-1.2% of Cr, optionally 0.01-0.2% of Mo, by weight, and the balance of Fe and other unavoidable impurities,
wherein the composition satisfies the following relationships: 1 ≤ (Cu/63.5)/(S*/32) ≤ 30 and S* = S - 0.8 x (Ti - 0.8 x (48/14) x N) x (32/48), and
wherein the steel sheet comprises CuS precipitates having an average size of 0.2 µm or less.

2. A cold rolled steel sheet with superior formability and high yield ratio, the cold rolled steel sheet having a composition comprising 0.01% or less of C, 0.01-0.2% of Cu, 0.01-0.3% of Mn, 0.005-0.08% of S, 0.1% or less of Al, 0.004% or less of N, 0.2% or less of P, 0.0001-0.002% of B, 0.002-0.04% of Nb, 0.005-0.15% of Ti, by weight, and the balance of Fe and other unavoidable impurities,
wherein the composition satisfies the following relationships: 1 ≤ (Mn/55 + Cu/63.5)/(S*/32) ≤ 30 and S* = S - 0.8 x (Ti - 0.8 x (48/14) x N) x (32/48), and the steel sheet comprises (Mn,Cu)S precipitates having an average size of 0.2 µm or less.

3. A cold rolled steel sheet with superior formability and high yield ratio, the cold rolled steel sheet having a composition comprising 0.01% or less of C, 0.01-0.2% of Cu, 0.005-0.08% of S, 0.1% or less of Al, 0.004-0.02% of N, 0.2% or less of P, 0.0001-0.002% of B, 0.002-0.04% of Nb, 0.005-0.15% of Ti, by weight, and the balance of Fe and other unavoidable impurities, wherein the composition satisfies the following relationships: 1 ≤ (Cu/63.5)/(S*/32) ≤ 30, 1 ≤ (Al/27)/(N*/14) ≤ 10, S* = S - 0.8 x (Ti - 0.8 x (48/14) x N) x (32/48) and N* = N - 0.8 x (Ti - 0.8 x (48/32) x S) x (14/48), and the steel sheet comprises CuS precipitates and AlN precipitates having an average size of 0.2 µm or less.

4. A cold rolled steel sheet with superior formability and high yield ratio, the cold rolled steel sheet having a composition comprising 0.01% or less of C, 0.01-0.2% of Cu, 0.01-0.3% of Mn, 0.005-0.08% of S, 0.1% or less of Al, 0.004-0.02% of N, 0.2% or less of P, 0.0001-0.002% of B, 0.002-0.04% of Nb, 0.005-0.15% of Ti, by weight, and the balance of Fe and other unavoidable impurities,
wherein the composition satisfies the following relationships: 1 ≤ (Mn/55 + Cu/63.5)/(S*/32) ≤ 30, 1 ≤ (Al/27)/(N*/14) ≤ 10, S* = S - 0.8 x (Ti - 0.8 x (48/14) x N) x (32/48) and N* = N - 0.8 x (Ti - 0.8 x (48/32) x S) x (14/48), and the steel sheet comprises (Mn,Cu)S precipitates and AlN precipitates having an average size of 0.2 µm or less.

5. The cold rolled steel sheet according to claim 1, wherein the C, Ti, Nb, N and S contents satisfy the following relationships: 0.8 ≤ (Ti*/48 + Nb/93)/(C/12) ≤ 5.0 and Ti* = Ti - 0.8 x ((48/14) x N + (48/32) x S).

6. The cold rolled steel sheet according to claim 5, wherein the C content is 0.005% or less.

7. The cold rolled steel sheet according to claim 1, wherein solute carbon (Cs) [Cs = (C - Nb x 12/93 - Ti* x 12/48) x 10000 in which Ti* = Ti - 0.8 x ((48/14) x N + (48/32) x S), provided that when Ti* is less than 0, Ti* is defined as 0], which is determined by the C and Ti contents, is from 5 to 30.

8. The cold rolled steel sheet according to claim 7, wherein the C content is 0.001-0.01%.

9. The cold rolled steel sheet according to any of claims 1 to 4, wherein the cold rolled steel sheet satisfies a yield ratio (yield strength/tensile strength) of 0.58 or higher.

10. The cold rolled steel sheet according to any of claims 1 to 4, wherein the number of the precipitates is 1 x 10⁶/mm² or more.

11. The cold rolled steel sheet according to claim 1, wherein the P content is 0.015% or less.

12. The cold rolled steel sheet according to claim 1, wherein the P content is from 0.03% to 0.2%.

13. The cold rolled steel sheet according to claim 2 or 4, wherein the sum of Mn and Cu is from 0.05% to 0.4%.

14. The cold rolled steel sheet according to claim 2 or 4, wherein the Mn content is 0.01-0.12%.

15. The cold rolled steel sheet according to claim 2 or 4, wherein the value of (Mn/55 + Cu/63.5)/(S*/32) is in the range of 1 to 9.

16. The cold rolled steel sheet according to claim 3 or 4, wherein the value of (Al/27)/(N*/14) is in the range of 1 to 6.

17. A method for producing a cold rolled steel sheet with superior formability and high yield ratio, the method comprising the steps of:

reheating a slab to a temperature of 1,100°C or higher, the slab having a composition comprising 0.01% or less of C, 0.01-0.2% of Cu, 0.005-0.08% of S, 0.1% or less of Al, 0.004% or less of N, 0.2% or less of P, 0.0001-0.002% of B, 0.002-0.04% of Nb, 0.005-0.15% of Ti, optionally at least one of 0.1-0.8% of Si and 0.2-1.2% of Cr, optionally 0.01-0.2% of Mo, by weight, and the balance of Fe and other unavoidable impurities, and the composition satisfying the following relationships: 1 ≤ (Cu/63.5)/(S*/32) ≤ 30 and S* = S - 0.8 x (Ti - 0.8 x (48/14) x N) x (32/48) ;

hot rolling the reheated slab at a finish rolling temperature of the Ar₃ transformation point or higher to provide a hot rolled steel sheet;

cooling the hot rolled steel sheet at a rate of 300 °C/min or higher;

winding the cooled steel sheet at 700°C or lower;

cold rolling the wound steel sheet; and

continuously annealing the cold rolled steel sheet, the cold rolled steel sheet comprising CuS precipitates having an average size of 0.2 µm or less.

18. A method for producing a cold rolled steel sheet with superior formability and high yield ratio, the method comprising the steps of:

reheating a slab to a temperature of 1,100°C or higher, the slab having a composition comprising 0.01% or less of C, 0.01-0.2% of Cu, 0.01-0.3% of Mn, 0.005-0.08% of S, 0.1% or less of Al, 0.004% or less of N, 0.2% or less of P, 0.0001-0.002% of B, 0.002-0.04% of Nb, 0.005-0.15% of Ti, by weight, and the balance of Fe and other unavoidable impurities, and the composition satisfying the following relationships: 1 ≤ (Mn/55 + Cu/63.5)/(S*/32) ≤ 30 and S* = S - 0.8 x (Ti - 0.8 x (48/14) x N) x (32/48);

hot rolling the reheated slab at a finish rolling temperature of the Ar₃ transformation point or higher to provide a hot rolled steel sheet;

cooling the hot rolled steel sheet at a rate of 300 °C/min or higher;

winding the cooled steel sheet at 700°C or lower;

cold rolling the wound steel sheet; and

continuously annealing the cold rolled steel sheet, the cold rolled steel sheet comprising (Mn,Cu)S precipitates having an average size of 0.2 µm or less.

19. A method for producing a cold rolled steel sheet with superior formability and high yield ratio, the method comprising the steps of:

reheating a slab to a temperature of 1,100°C or higher, the slab having a composition comprising 0.01% or less of C, 0.01-0.2% of Cu, 0.005-0.08% of S, 0.1% or less of Al, 0.004-0.02% of N, 0.2% or less of P, 0.0001-0.002% of B, 0.002-0.04% of Nb, 0.005-0.15% of Ti, by weight, and the balance of Fe and other unavoidable impurities, and the composition satisfying the following relationships: 1 ≤ (Cu/63.5)/(S*/32) ≤ 30, 1 ≤ (Al/27)/(N*/14) ≤ 10, S* = S - 0.8 x (Ti - 0.8 x (48/14) x N) x (32/48) and N* = N - 0.8 x (Ti - 0.8 x (48/32) x S) x (14/48);

hot rolling the reheated slab at a finish rolling temperature of the Ar₃ transformation point or higher to provide a hot rolled steel sheet;

cooling the hot rolled steel sheet at a rate of 300 °C/min or higher;

winding the cooled steel sheet at 700°C or lower;

cold rolling the wound steel sheet; and

continuously annealing the cold rolled steel sheet, the cold rolled steel sheet comprising CuS precipitates and AlN precipitates having an average size of 0.2 µm or less.

20. A method for producing a cold rolled steel sheet with superior formability and high yield ratio, the method comprising the steps of:

reheating a slab to a temperature of 1,100°C or higher, the slab having a composition comprising 0.01% or less of C, 0.01-0.2% of Cu, 0.01-0.3% of Mn, 0.005-0.08% of S, 0.1% or less of Al, 0.004-0.02% of N, 0.2% or less of P, 0.0001-0.002% of B, 0.002-0.04% of Nb, 0.005-0.15% of Ti, by weight, and the balance of Fe and other unavoidable impurities, and the composition satisfying the following relationships: 1 ≤ (Mn/55 + Cu/63.5)/(S*/32) ≤ 30, 1 ≤ (Al/27)/(N*/14) ≤ 10, S* = S - 0.8 x (Ti - 0.8 x (48/14) x N) x (32/48) and N* = N - 0.8 x (Ti - 0.8 x (48/32) x S) x (14/48) ;

hot rolling the reheated slab at a finish rolling temperature of the Ar₃ transformation point or higher to provide a hot rolled steel sheet;

cooling the hot rolled steel sheet at a rate of 300 °C/min or higher;

winding the cooled steel sheet at 700°C or lower;

cold rolling the wound steel sheet; and

continuously annealing the cold rolled steel sheet, the cold rolled steel sheet comprising (Mn,Cu)S precipitates and AlN precipitates having an average size of 0.2 µm or less.

21. The method according to claim 17, wherein the C, Ti, Nb, N and S contents satisfy the following relationships: 0.8 ≤ (Ti*/48 + Nb/93)/(C/12) ≤ 5.0 and Ti* = Ti - 0.8 x ((48/14) x N + (48/32) x S).

22. The method according to claim 21, wherein the C content is 0.005% or less.

23. The method according to claim 17, wherein solute carbon (Cs) [Cs = (C - Nb x 12/93 - Ti* x 12/48) x 10000 in which Ti* = Ti - 0.8 x ((48/14) x N + (48/32) x S), provided that when Ti* is less than 0, Ti* is defined as 0], which is determined by the C and Ti contents, is from 5 to 30.

24. The method according to claim 23, wherein the C content is 0.001-0.01%.

25. The method according to any of claims 17 to 20, wherein the cold rolled steel sheet satisfies a yield ratio (yield strength/tensile strength) of 0.58 or higher.

26. The method according to any of claims 17 to 20, wherein the number of the precipitates is 1 x 10⁶/mm² or more.

27. The method according to claim 17, wherein the P content is 0.015% or less.

28. The method according to claim 17, wherein the P content is from 0.03% to 0.2%.

29. The method according to claim 18 or 20, wherein the sum of Mn and Cu is from 0.08% to 0.4%.

30. The method according to claim 18 or 20, wherein the Mn content is 0.01-0.12%.

31. The method according to claim 18 or 20, wherein the value of (Mn/55 + Cu/63.5)/(S*/32) is in the range of 1 to 9.

32. The method according to claim 19 or 20, wherein the value of (Al/27)/(N*/14) is in the range of 1 to 6.

Ansprüche

1. Kaltgewalztes Blech mit verbesserter Formbarkeit und hohem Streckgrenzenverhältnis, worin das kaltgewalzte Blech eine Zusammensetzung aufweist, umfassend 0,01% oder weniger von C, 0,01-0,2% von Cu, 0,005-0,08% von S, 0,1% oder weniger von Al, 0,004% oder weniger von N, 0,2% oder weniger von P, 0,0001-0,002% von B, 0,002-0,04% von Nb, 0,005-0,15% von Ti, wahlweise mindestens eines von 0,1-0,8% von Si und 0,2-1,2% von Cr, wahlweise 0,01-0,2% von Mo, bezogen auf das Gewicht,
worin der Rest Fe und andere nicht-vermeidbare Verunreinigungen sind, worin die Zusammensetzung den folgenden Verhältnissen genügt: 1 ≤ (Cu/63,5)/(S*/32) ≤ 30 und S* = S - 0,8 x (Ti - 0,8 x (48/14) x N) x (32/48), und worin das Blech CuS-Ausfällungen mit einer durchschnittlichen Größe von 0,2 µm oder weniger umfasst.

2. Kaltgewalztes Blech mit verbesserter Formbarkeit und hohem Streckgrenzenverhältnis, worin das kaltgewalzte Blech eine Zusammensetzung aufweist, umfassend 0,01% oder weniger von C, 0,01-0,2% von Cu, 0,01-0,3% von Mn, 0,005-0,08% von S, 0,1% oder weniger von Al, 0,004% oder weniger von N, 0,2% oder weniger von P, 0,0001-0,002 % von B, 0,002-0,04 % von Nb, 0,005-0,15% von Ti, bezogen auf das Gewicht, worin der Rest Fe und andere nicht-vermeidbare Verunreinigungen sind,
worin die Zusammensetzung den folgenden Verhältnissen genügt: 1 ≤ (Mn/55 + Cu/63,5)/(S*/32) ≤ 30 und S* = S - 0,8 x (Ti - 0,8 x (48/14) x N) x (32/48), und worin das Blech (Mn,Cu)S-Ausfällungen mit einer durchschnittlichen Größe von 0,2 µm oder weniger umfasst.

3. Kaltgewalztes Blech mit verbesserter Formbarkeit und hohem Streckgrenzenverhältnis, worin das kaltgewalzte Blech eine Zusammensetzung aufweist, umfassend 0,01% oder weniger von C, 0,01-0,2% von Cu, 0,005-0,08% von S, 0,1% oder weniger von Al, 0,004-0,02% von N, 0,2% oder weniger von P, 0,0001-0,002% von B, 0,002-0,04% von Nb, 0,005-0,15% von Ti, bezogen auf das Gewicht, worin der Rest Fe und andere nicht-vermeidbare Verunreinigungen sind, worin die Zusammensetzung den folgenden Verhältnissen genügt: 1 ≤ (Cu/63,5)/(S*/32) ≤30, 1 ≤ (Al/27)/(N*/14) ≤ 10, S* = S - 0,8 x (Ti - 0,8 x (48/14) x N) x (32/48) und N* = N - 0,8 x (Ti - 0,8 x (48/32) x S) x (14/48), und das Blech CuS-Ausfällungen und AlN-Ausfällungen mit einer durchschnittlichen Größe von 0,2 µm oder weniger umfasst.

4. Kaltgewalztes Blech mit verbesserter Formbarkeit und hohem Streckgrenzenverhältnis, worin das kaltgewalzte Blech eine Zusammensetzung aufweist, umfassend 0,01% oder weniger von C, 0,01-0,2 % von Cu, 0,01-0,3 % von Mn, 0,005-0,08 % von S, 0,1% oder weniger von Al, 0,004-0,02% von N, 0,2% oder weniger von P, 0,0001-0,002 % von B, 0,002-0,04 % von Nb, 0,005 -0,15% von Ti, bezogen auf das Gewicht, worin der Rest Fe und andere nicht-vermeidbare Verunreinigungen sind,
worin die Zusammensetzung den folgenden Verhältnissen genügt: 1 ≤ (Mn/55 + Cu/63,5)/(S*/32) ≤ 30, 1 ≤ (Al/27)/(N*/14) ≤ 10, S* = S - 0,8 x (Ti - 0,8 x (48/14) x N) x (32/48) und N* = N - 0,8 x (Ti - 0,8 x (48/32) x S) x (14/48), und worin das Blech (Mn,Cu)S-Ausfällungen und AlN-Ausfällungen mit einer durchschnittlichen Größe von 0,2 µm oder weniger umfasst.

5. Kaltgewalztes Blech nach Anspruch 1, worin der Gehalt an C, Ti, Nb, N und S den folgenden Verhältnissen genügt: 0,8 ≤ (Ti*/48 + Nb/93)/(C/12) ≤ 5,0 und Ti* = Ti - 0,8 x ((48/14) x N + (48/32) x S).

6. Kaltgewalztes Blech nach Anspruch 5, worin der Gehalt an C 0,005% ist oder weniger.

7. Kaltgewalztes Blech nach Anspruch 1, worin gelöster Kohlenstoff (Cs) [Cs = (C - Nb x 12/93 - Ti* x 12/48) x 10000 worin Ti* = Ti - 0,8 x ((48/14) x N + (48/32) x S) von 5 bis 30 ist, mit der Maßgabe, dass wenn Ti* weniger ist als 0, Ti* als 0 definiert wird, bestimmt anhand des Gehalts von C und Ti.

8. Kaltgewalztes Blech nach Anspruch 7, worin der Gehalt an C 0,001-0,01% ist.

9. Kaltgewalztes Blech nach einem der Ansprüche 1 bis 4, worin das kaltgewalzte Blech einem Streckgrenzenverhältnis (Formänderungsfestigkeit/Bruchkraft) von 0,58 oder höher genügt.

10. Kaltgewalztes Blech nach einem der Ansprüche 1 bis 4, worin die Anzahl an Ausfällungen 1 x 10⁶/mm² oder mehr beträgt.

11. Kaltgewalztes Blech nach Anspruch 1, worin der Gehalt an P 0,015% oder weniger ist.

12. Kaltgewalztes Blech nach Anspruch 1, worin der Gehalt an P von 0,03% bis 0,2% ist.

13. Kaltgewalztes Blech nach Anspruch 2 oder 4, worin die Summe an Mn und Cu von 0,05% bis 0,4% ist.

14. Kaltgewalztes Blech nach Anspruch 2 oder 4, worin der Gehalt an Mn 0,01-0,12% ist.

15. Kaltgewalztes Blech nach Anspruch 2 oder 4, worin der Wert von (Mn/55 + Cu/63,5)/(S*/32) im Bereich von 1 bis 9 ist.

16. Kaltgewalztes Blech nach Anspruch 3 oder 4, worin der Wert von (Al/27)/(N*/14) im Bereich von 1 bis 6 ist.

17. Verfahren zur Herstellung von kaltgewalztem Blech mit verbesserter Formbarkeit und hohem Streckgrenzenverhältnis, wobei das Verfahren die Schritte umfasst:

erneutes Erhitzen einer Platte auf eine Temperatur von 1.100°C oder höher, worin die Platte eine Zusammensetzung aufweist, umfassend 0,01% oder weniger von C, 0,01-0,2% von Cu, 0,005-0,08% von S, 0,1% oder weniger von Al, 0,004% oder weniger von N, 0,2% oder weniger von P, 0,0001-0,002 % von B, 0,002-0,04% von Nb, 0,005-0.15% von Ti, wahlweise mindestens eines von 0,1-0,8% von Si und 0,2-1,2% von Cr, wahlweise 0,01-0,2% von Mo, bezogen auf das Gewicht, worin der Rest Fe und andere nicht-vermeidbare Verunreinigungen sind, worin die Zusammensetzung den folgenden Verhältnissen genügt: 1 ≤ (Cu/63,5)/(S*/32) ≤ 30 und S* = S - 0,8 x (Ti - 0,8 x (48/14) x N) x (32/48);

Heißwalzen der wiedererhitzten Platte bei einer endgültigen Walztemperatur des Ar₃ Transformationspunkt oder höher um heißgewalztes Blech zu liefern;

Kühlen des heißgewalzten Blechs bei einer Rate von 300 °C/min oder höher;

Winden des gekühlten Blechs bei 700 ° C oder darunter;

Kaltwalzen des gewundenen Blechs; und

kontinuierliches Annealen des kaltgewalzten Blechs, worin das kaltgewalzte Blech CuS-Ausfällungen mit einer durchschnittlichen Größe von 0,2 µm oder weniger enthält.

18. Verfahren zur Herstellung von kaltgewalztem Blech mit verbesserter Formbarkeit und hohem Streckgrenzenverhältnis, wobei das Verfahren die Schritte umfasst:

erneutes Erhitzen einer Platte auf eine Temperatur von 1.100° C oder höher, worin die Platte eine Zusammensetzung aufweist, umfassend 0,01% oder weniger von C, 0,01-0,2% von Cu, 0,01-0,3% von Mn, 0,005-0,08 % von S, 0,1% oder weniger von Al, 0,004% oder weniger von N, 0,2% oder weniger von P, 0,0001-0,002% von B, 0,002- 0,04% von Nb, 0,005-0,15% von Ti, bezogen auf das Gewicht, worin der Rest Fe und andere nicht-vermeidbare Verunreinigungen sind, worin die Zusammensetzung den folgenden Verhältnissen genügt: 1 ≤ (Mn/55 + Cu/63,5)/(S*/32) ≤ 30 und S* = S - 0,8 X (Ti - 0,8 X (48/14) X N) X (32/48);

Heißwalzen der wiedererhitzten Platte auf eine Endwalz-Temperatur des Ar₃ Transformationspunkts oder höher, um ein heißgewalztes Blech zu liefern;

Kühlen des heißgewalzten Blechs bei einer Rate von 300 °C/min oder höher;

Winden des gekühlten Blechs bei 700° C oder darunter;

Kaltwalzen des gewundenen Blechs; und

kontinuierliches Annealen des kaltgewalzten Blechs, worin das kaltgewalzte Blech (Mn,Cu)S-Ausfällungen mit einer durchschnittlichen Größe von 0,2 µm oder weniger umfasst.

19. Verfahren zur Herstellung eines kaltgewalzten Blechs mit verbesserter Verformbarkeit und hohem Streckgrenzenverhältnis, wobei das Verfahren die Schritte umfasst:

Wiedererhitzen einer Platte auf eine Temperatur von 1.100° C oder höher, worin die Platte eine Zusammensetzung aufweist, umfassend 0,01% oder weniger von C, 0,01-0,2% von Cu, 0,005-0,08% von S, 0,1% oder weniger von Al, 0,004-0,02% von N, 0,2% oder weniger von P, 0,0001-0,002 % von B, 0,002-0,04 % von Nb, 0,005-0,15 % von Ti, bezogen auf das Gewicht, worin der Rest Fe und andere nicht-vermeidbare Verunreinigungen sind, worin die Zusammensetzung den folgenden Verhältnissen genügt: 1 ≤ (Cu/63,5)/(S*/32) ≤ 30, 1 ≤ (Al/27)/(N*/14) ≤ 10, S* = S - 0,8 x (Ti - 0,8 x (48/14) x N) x (32/48) und N* = N - 0,8 X (Ti - 0,8 X (48/32) X S) X (14/48);

Heißwalzen der wiedererhitzten Platte bei einer End-Walz-Temperatur des Ar₃ Transformations-Punkts oder höher, um ein heißgewalztes Blech zu liefern;

Kühlen des heißgewalzten Blechs bei einer Rate von 300 °C/min oder höher;

Winden des gekühlten Blechs bei 700 °C oder tiefer;

Kaltwalzen des gewundenen Blechs; und

kontinuierliches Annealen des kaltgewalzten Blechs, worin das das kaltgewalzte Blech CuS-Ausfällungen und AlN-Ausfällungen mit einer durchschnittlichen Größe von 0,2 µm oder weniger umfasst.

20. Verfahren zur Herstellung von kaltgewalztem Blech mit verbesserter Formbarkeit und hohem Streckgrenzenverhältnis, wobei das Verfahren die Schritte umfasst:

erneutes Erhitzen einer Platte auf eine Temperatur von 1.100 °C oder höher, worin die Platte eine Zusammensetzung aufweist, umfassend 0,01% oder weniger von C, 0,01-0,2% von Cu, 0,01-0,3% von Mn, 0,005-0,08% von S, 0,1% oder weniger von Al, 0,004-0,02% von N, 0,2% oder weniger von P, 0,0001-0,002% von B, 0,002-0,04% of Nb, 0,005-0,15% von Ti, bezogen auf das Gewicht, worin der Rest Fe und andere nicht-vermeidbare Verunreinigungen sind, worin die Zusammensetzung den folgenden Verhältnissen genügt: 1 ≤ (Mn/55 + Cu/63,5)/(S*/32) ≤ 30, 1 ≤ (Al/27)/(N*/14) ≤ 10, S* = S - 0,8 X (Ti - 0,8 x (48/14) x N) x (32/48) und N* = N - 0,8 x (Ti - 0,8 x (48/32) x S) x (14/48);

Heißwalzen der wiedererhitzten Platte bei einer End-Walz-Temperatur des Ar₃ Transformationspunkts oder höher, um ein heißgewalztes Blech zu liefern;

Kühlen der heißgewalzten Blechs bei einer Rate bei 300 °C/min oder darüber;

Winden des gekühlten Blechs bei 700 °C oder darunter;

Kaltwalzen des gewundenen Blechs; und

kontinuierliches Annealing des kaltgewalzten Blechs, worin das kaltgewalzte Blech (Mn,Cu)S-Ausfällungen und AlN-Ausfällungen mit einer durchschnittlichen Größe von 0,2 µm oder weniger umfasst.

21. Verfahren nach Anspruch 17, wobei der Gehalt an C, Ti, Nb, N und S den folgenden Verhältnissen genügt: 0,8 ≤ (Ti*/48 + Nb/93) / (C/12) ≤ 5,0 und Ti* = Ti - 0,8 x ((48/14) x N + (48/32) x S).

22. Verfahren nach Anspruch 21, wobei der Gehalt an C 0,005% oder weniger ist.

23. Verfahren nach Anspruch 17, wobei gelöster Kohlenstoff (Cs) [Cs = (C - Nb x 12/93 - Ti* x 12/48) x 10000 worin Ti* = Ti - 0,8 x ((48/14) x N + (48/32) x S) von 5 bis 30 ist, mit der Maßgabe, dass wenn Ti* weniger als 0 ist, Ti* als 0 definiert wird, bestimmt durch den Gehalt an C und Ti.

24. Verfahren nach Anspruch 23, wobei der Gehalt an C 0,001-0,01% ist.

25. Verfahren nach einem der Ansprüche 17 bis 20,
wobei das kaltgewalzte Blech einem Streckgrenzenverhältnis (Formänderungsfestigkeit/ Bruchkraft) von 0,58 oder höher genügt.

26. Verfahren nach einem der Ansprüche 17 bis 20, wobei die Anzahl an Ausfällungen 1 x 10⁶/mm² oder mehr ist.

27. Verfahren nach Anspruch 17, wobei der Gehalt an P 0,015% oder weniger ist.

28. Verfahren nach Anspruch 17, wobei der Gehalt an P von 0,03% bis 0,2% ist.

29. Verfahren nach Anspruch 18 oder 20, wobei die Summe von Mn und Cu von 0,08% bis 0,4% ist.

30. Verfahren nach Anspruch 18 oder 20, wobei der Gehalt an Mn 0,01-0,12% ist.

31. Verfahren nach Anspruch 18 oder 20, wobei der Wert von (Mn/55 + Cu/63,5)/(S*/32) im Bereich von 1 bis 9 ist.

32. Verfahren nach Anspruch 19 oder 20, wobei der Wert von (Al/27)/(N*/14) im Bereich von 1 bis 6 ist.

Revendications

1. Feuille d'acier laminée à froid ayant une formabilité supérieure et un rapport d'élasticité élevé, la feuille d'acier laminée à froid ayant une composition comprenant 0,01 % de C ou moins, 0,01 à 0,2 % de Cu, 0,005 à 0,08 % de S, 0,1 % de Al ou moins, 0,004 % de N ou moins, 0,2 % de P ou moins, 0,0001 à 0,002 % de B, 0,002 à 0,04 % de Nb, 0,005 à 0,15 % de Ti, facultativement au moins un parmi 0,1 à 0,8 % de Si et 0,2 à 1,2 % de Cr, facultativement 0,01 à 0,2 % de Mo, en poids, et le reste étant Fe et autres impuretés inévitables,
la composition satisfaisant les relations suivantes : 1 ≤ (Cu/63,5)/(S*/32) ≤ 30 et S* = S-0,8 x (Ti-0,8 x (48/14) x N) x (32/48), et
la feuille d'acier comprenant des précipités de CuS ayant une taille moyenne de 0,2 µm ou moins.

2. Feuille d'acier laminée à froid ayant une formabilité supérieure et un rapport d'élasticité élevé, la feuille d'acier laminée à froid ayant une composition comprenant 0,01 % de C ou moins, 0,01 à 0,2 % de Cu, 0,01 à 0,3 % de Mn, 0,005 à 0,08 % de S, 0,1 % de Al ou moins, 0,004 % de N ou moins, 0,2 % de P ou moins, 0,0001 à 0,002 % de B, 0,002 à 0,04 % de Nb, 0,005 à 0,15 % de Ti, en poids, et le reste étant Fe et autres impuretés inévitables,
la composition satisfaisant les relations suivantes : 1 ≤ (Mn/55 + Cu/63,5)/(S*/32) ≤ 30 et S* = S-0,8 x (Ti-0,8 x (48/14) x N) x (32/48), et la feuille d'acier comprenant des précipités de (Mn,Cu)S ayant une taille moyenne de 0,2 µm ou moins.

3. Feuille d'acier laminée à froid ayant une formabilité supérieure et un rapport d'élasticité élevé, la feuille d'acier laminée à froid ayant une composition comprenant 0,01 % de C ou moins, 0,01 à 0,2 % de Cu, 0,005 à 0,08 % de S, 0,1 % de Al ou moins, 0,004 à 0,02 % de N, 0,2 % de P ou moins, 0,0001 à 0,002 % de B, 0,002 à 0,04 % de Nb, 0,005 à 0,15 % de Ti, en poids, et le reste étant Fe et autres impuretés inévitables,
la composition satisfaisant les relations suivantes : 1 ≤ (Cu/63,5)/(S*/32) ≤ 30, 1 ≤ (Al/27)/(N*/14) ≤ 10, S* = S-0,8 x (Ti-0,8 x (48/14) x N) x (32/48) et N* = N-0,8 x (Ti-0,8 x (48/32) x S) x (14/48), et la feuille d'acier comprenant des précipités de CuS et des précipités de AlN ayant une taille moyenne de 0,2 µm ou moins.

4. Feuille d'acier laminée à froid ayant une formabilité supérieure et un rapport d'élasticité élevé, la feuille d'acier laminée à froid ayant une composition comprenant 0,01 % de C ou moins, 0,01 à 0,2 % de Cu, 0,01 à 0,3 % de Mn, 0,005 à 0,08 % de S, 0,1 % de Al ou moins, 0,004 à 0,02 % de N, 0,2 % de P ou moins, 0,0001 à 0,002 % de B, 0,002 à 0,04 % de Nb, 0,005 à 0,15 % de Ti, en poids, et le reste étant Fe et autres impuretés inévitables,
la composition satisfaisant les relations suivantes : 1 ≤ (Mn/55 + Cu/63,5)/(S*/32) ≤ 30, 1 ≤ (Al/27)/(N*/14) ≤ 10, S* = S-0,8 x (Ti-0,8 x (48/14) x N) x (32/48) et N* = N-0,8 x (Ti-0,8 x (48/32) x S) x (14/48), et la feuille d'acier comprenant des précipités de (Mn,Cu)S et des précipités de AlN ayant une taille moyenne de 0,2 µm ou moins.

5. Feuille d'acier laminée à froid selon la revendication 1, dans laquelle les teneurs en C, Ti, Nb et S satisfont les relations suivantes : 0,8 ≤ (Ti*/48 + Nb/93)/(C/12) ≤ 5,0 et Ti* = Ti-0,8 x ((48/14) x N + (48/32) x S).

6. Feuille d'acier laminée à froid selon la revendication 5, dans laquelle la teneur en C est de 0,005 % ou moins.

7. Feuille d'acier laminée à froid selon la revendication 1, dans laquelle du soluté de carbone (Cs) [Cs = (C - Nb x 12/93 - Ti* x 12/48) x 1000 où Ti* = Ti-0,8 x (((48/14) x N + (48/32) x S), à condition que, lorsque Ti* est inférieur à 0, Ti* soit défini comme étant 0], qui est déterminé par les teneurs en C et Ti, est compris entre 5 et 30.

8. Feuille d'acier laminée à froid selon la revendication 7, dans laquelle la teneur en C est comprise entre 0,001 et 0,01 %.

9. Feuille d'acier laminée à froid selon l'une quelconque des revendications 1 à 4, dans laquelle la feuille d'acier laminée à froid satisfait un rapport d'élasticité (limite d'élasticité/résistance à la traction) de 0,58 ou plus.

10. Feuille d'acier laminée à froid selon l'une quelconque des revendications 1 à 4, dans laquelle le nombre des précipités est 1 x 10⁶/mm² ou plus.

11. Feuille d'acier laminée à froid selon la revendication 1, dans laquelle la teneur en P est de 0,015 % ou moins.

12. Feuille d'acier laminée à froid selon la revendication 1, dans laquelle la teneur en P est comprise entre 0,03 % et 0,2 %.

13. Feuille d'acier laminée à froid selon la revendication 2 ou 4, dans laquelle la somme de Mn et Cu est comprise entre 0,05 % et 0,4 %.

14. Feuille d'acier laminée à froid selon la revendication 2 ou 4, dans laquelle la teneur en Mn est comprise entre 0,01 et 0,12 %.

15. Feuille d'acier laminée à froid selon la revendication 2 ou 4, dans laquelle la valeur de (Mn/55 + Cu/63,5)/(S*/32) est comprise dans la plage allant de 1 à 9.

16. Feuille d'acier laminée à froid selon la revendication 3 ou 4, dans laquelle la valeur de (Al/27)/(N*/14) est comprise dans la plage allant de 1 à 6.

17. Procédé de production d'une feuille d'acier laminée à froid ayant une formabilité supérieure et un rapport d'élasticité élevé, le procédé comprenant les étapes :

réchauffer une plaque à une température de 1100 °C ou plus, la plaque ayant une composition comprenant 0,01 % de C ou moins, 0,01 à 0,2 % de Cu, 0,005 à 0,08 % de S, 0,1 % de Al ou moins, 0,004 % de N ou moins, 0,2 % de P ou moins, 0,0001 à 0,002 % de B, 0,002 à 0,04 % de Nb, 0,005 à 0,15 % de Ti, facultativement au moins un parmi 0,1 à 0,8 % de Si et 0,2 à 1,2 % de Cr, facultativement 0,01 à 0,2 % de Mo, en poids, et le reste étant Fe et autres impuretés inévitables, et la composition satisfaisant les relations suivantes : 1 ≤ (Cu/63,5)/(S*/32) ≤ 30 et S* = S-0,8 x (Ti-0,8 x (48/14) x N) x (32/48) ;

laminer à chaud la plaque réchauffée à une température de laminage de finition du point de transformation Ar₃ ou plus, pour fournir une feuille d'acier laminée à chaud ;

refroidir la feuille d'acier laminée à chaud à une vitesse de 300°C/min ou plus ;

enrouler la feuille d'acier refroidie à 700°C ou moins ;

laminer à froid la feuille d'acier enroulée ; et

recuire de manière continue la feuille d'acier laminée à froid, la feuille d'acier laminée à froid comprenant des précipités de CuS ayant une taille moyenne de 0,2 µm ou moins.

18. Procédé de production d'une feuille d'acier laminée à froid ayant une formabilité supérieure et un rapport d'élasticité élevé, le procédé comprenant les étapes :

réchauffer une plaque à une température de 1100°C ou plus, la plaque ayant une composition comprenant 0,01 % de C ou moins, 0,01 à 0,2 % de Cu, 0,01 à 0,3 % de Mn, 0,005 à 0,08 % de S, 0,1 % de Al ou moins, 0,004 % de N ou moins, 0,2 % de P ou moins, 0,0001 à 0,002 % de B, 0,002 à 0,04 % de Nb, 0,005 à 0,15 % de Ti, en poids, et le reste étant Fe et autres impuretés inévitables, et la composition satisfaisant les relations suivantes : 1 ≤ (Mn/55 + Cu/63,5)/(S*/32) ≤ 30 et S* = S-0,8 x (Ti-0,8 x (48/14) x N) x (32/48) ;

laminer à chaud la plaque réchauffée à une température de laminage de finition du point de transformation Ar3 ou plus, pour fournir une feuille d'acier laminée à chaud ;

refroidir la feuille d'acier laminée à chaud à une vitesse de 300°C/min ou plus ;

enrouler la feuille d'acier refroidie à 700°C ou moins ;

laminer à froid la feuille d'acier enroulée ; et

recuire de manière continue la feuille d'acier laminée à froid, la feuille d'acier laminée à froid comprenant des précipités de (Mn,Cu)S ayant une taille moyenne de 0,2 µm ou moins.

19. Procédé de production d'une feuille d'acier laminée à froid ayant une formabilité supérieure et un rapport d'élasticité élevé, le procédé comprenant les étapes :

réchauffer une plaque à une température de 1100°C ou plus, la plaque ayant une composition comprenant 0,01 % de C ou moins, 0,01 à 0,2 % de Cu, 0,005 à 0,08 % de S, 0,1 % de Al ou moins, 0,004 à 0,02 % de N, 0,2 % de P ou moins, 0,0001 à 0,002 % de B, 0,002 à 0,04 % de Nb, 0,005 à 0,15 % de Ti, en poids, et le reste étant Fe et autres impuretés inévitables, et la composition satisfaisant les relations suivantes : 1 ≤ (Cu/63,5)/(S*/32) ≤ 30, 1 ≤ (Al/27)/(N*/14) ≤ 10, S* = S-0,8 x (Ti-0,8 x (48/14) x N) x (32/48) et N* = N-0,8 x (Ti-0,8 x (48/32) x S) x (14/48) ;

laminer à chaud la plaque réchauffée à une température de laminage de finition du point de transformation Ar3 ou plus, pour fournir une feuille d'acier laminée à chaud ;

refroidir la feuille d'acier laminée à chaud à une vitesse de 300°C/min ou plus ;

enrouler la feuille d'acier refroidie à 700°C ou moins ;

laminer à froid la feuille d'acier enroulée ; et

recuire de manière continue la feuille d'acier laminée à froid, la feuille d'acier laminée à froid comprenant des précipités de CuS et des précipités de AlN ayant une taille moyenne de 0,2 µm ou moins.

20. Procédé de production d'une feuille d'acier laminée à froid ayant une formabilité supérieure et un rapport d'élasticité élevé, le procédé comprenant les étapes :

réchauffer une plaque à une température de 1100°C ou plus, la plaque ayant une composition comprenant 0,01 % de C ou moins, 0,01 à 0,2 % de Cu, 0,01 à 0,3 % de Mn, 0,005 à 0,08 % de S, 0,1 % de Al ou moins, 0,004 à 0,02 % de N, 0,2 % de P ou moins, 0,0001 à 0,002 % de B, 0,002 à 0,04 % de Nb, 0,005 à 0,15 % de Ti, en poids, et le reste étant Fe et autres impuretés inévitables, et la composition satisfaisant les relations suivantes : 1 ≤ (Mn/55 + Cu/63,5)/(S*/32) ≤ 30, 1 ≤ (Al/27)/(N*/14) ≤ 10, S* = S-0,8 x (Ti-0,8 x (48/14) x N) x (32/48) et N* = N-0,8 x (Ti-0,8 x (48/32) x S) x (14/48) ;

laminer à chaud la plaque réchauffée à une température de laminage de finition du point de transformation Ar3 ou plus, pour fournir une feuille d'acier laminée à chaud ;

refroidir la feuille d'acier laminée à chaud à une vitesse de 300°C/min ou plus ;

enrouler la feuille d'acier refroidie à 700°C ou moins ;

laminer à froid la feuille d'acier enroulée ; et

recuire de manière continue la feuille d'acier laminée à froid, la feuille d'acier laminée à froid comprenant des précipités de (Mn,Cu)S et des précipités de AlN ayant une taille moyenne de 0,2 µm ou moins.

21. Procédé selon la revendication 17, dans lequel les teneurs en C, Ti, Nb, N et S satisfont les relations suivantes : 0,8 ≤ (Ti*/48 + Nb/93)/(C/12) ≤ 5,0 et Ti* = Ti-0,8 x ((48/14) x N + (48/32) x S).

22. Procédé selon la revendication 21, dans lequel la teneur en C est de 0,005 % ou moins.

23. Procédé selon la revendication 17, dans lequel du soluté de carbone (Cs) [Cs = (C - Nb x 12/93 - Ti* x 12/48) x 1000 où Ti* = Ti-0,8 x (((48/14) x N + (48/32) x S), à condition que, lorsque Ti* est inférieur à 0, Ti* soit défini comme étant 0], qui est déterminé par les teneurs en C et Ti, est compris entre 5 et 30.

24. Procédé selon la revendication 23, dans lequel la teneur en C est comprise entre 0,001 et 0,01 %.

25. Procédé selon l'une quelconque des revendications 17 à 20, dans lequel la feuille d'acier laminée à froid satisfait un rapport d'élasticité (limite d'élasticité/résistance à la traction) de 0,58 ou plus.

26. Procédé selon l'une quelconque des revendications 17 à 20, dans lequel le nombre des précipités est 1 x 10⁶/mm² ou plus.

27. Procédé selon la revendication 17, dans lequel la teneur en P est de 0,015 % ou moins.

28. Procédé selon la revendication 17, dans lequel la teneur en P est comprise entre 0,03 % et 0,2 %.

29. Procédé selon la revendication 18 ou 20, dans lequel la somme de Mn et Cu est comprise entre 0,08 % et 0,4 %.

30. Procédé selon la revendication 18 ou 20, dans lequel la teneur en Mn est comprise entre 0,01 et 0,12 %.

31. Procédé selon la revendication 18 ou 20, dans lequel la valeur de (Mn/55 + Cu/63,5)/(S*/32) est comprise dans la plage allant de 1 à 9.

32. Procédé selon la revendication 19 ou 20, dans lequel la valeur de (Al/27)/(N*/14) est comprise dans la plage allant de 1 à 6.