TWI276692B - High strength cold rolled steel sheet and method for manufacturing the same - Google Patents

High strength cold rolled steel sheet and method for manufacturing the same Download PDF

Info

Publication number
TWI276692B
TWI276692B TW094105020A TW94105020A TWI276692B TW I276692 B TWI276692 B TW I276692B TW 094105020 A TW094105020 A TW 094105020A TW 94105020 A TW94105020 A TW 94105020A TW I276692 B TWI276692 B TW I276692B
Authority
TW
Taiwan
Prior art keywords
steel sheet
rolled steel
mass
strength cold
less
Prior art date
Application number
TW094105020A
Other languages
Chinese (zh)
Other versions
TW200532032A (en
Inventor
Yoshihiko Ono
Fusato Kitano
Yasunobu Nagataki
Yasushi Tanaka
Hisanori Ando
Original Assignee
Jfe Steel Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Jfe Steel Corp filed Critical Jfe Steel Corp
Publication of TW200532032A publication Critical patent/TW200532032A/en
Application granted granted Critical
Publication of TWI276692B publication Critical patent/TWI276692B/en

Links

Classifications

    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/14Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/06Ferrous alloys, e.g. steel alloys containing aluminium
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426Hot rolling
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/008Ferrous alloys, e.g. steel alloys containing tin
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/02Ferrous alloys, e.g. steel alloys containing silicon
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/04Ferrous alloys, e.g. steel alloys containing manganese
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/60Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0436Cold rolling
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0473Final recrystallisation annealing
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0478Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing involving a particular surface treatment

Landscapes

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

Abstract

The present invention relates to a high strength cold rolled steel sheet consisting of 0.015% or less of C, 1.5% or less of Si, 0.4 to 3% of Mn, 0.15% or less of P, 0.02% or less of S, 0.1 to 1% of sol.Al, 0.01% or less of N, 0.2% or less of Ti, by mass %, and the balance of Fe and inevitable impurities. In this steel sheet, 1 <= ([Ti]/48)/([C]/12+[N]/14) is satisfied, in which [M] represents the content of the element M. Since having the superior deep drawability and the TS of 340 to 590 MPa, the high strength cold rolled steel sheet of the present invention is preferably used for automobiles parts difficult to be press formed, such as a side outer panel and a door inner panel.

Description

1276692 九、發明說明: 【發明所屬之技術領域】 本發明為關於汽車、家電製品等所使用的高強度冷軋鋼 ; 板,特別為關於具有 3 4 0至 5 9 0 MPa之拉伸強度(TS, tensile strength)之深拉伸成形性(deep drawability) 優良的高強度冷軋鋼板、及其製造方法。 【先前技術】 習知,於外側外板和門内板之成形困難的汽車零件中, φ 係使用TS為270MPa左右,r值為1.8至2.0之具有優異 深拉伸成形性的 I F ( I n t e r s t i t i a 1 F r e e,無縫)軟質冷軋 鋼板(S P C 2 7 0 E,F )。近年,由於對於汽車車體之輕量化的需 求更加提高,故於此等難成形零件亦發展出應用具有340 至590MPa之TS的IF高強度冷軋鋼板。但是,此等零件若 欲使用現在所量產之TS為340至390MPa、且r值為1.7 左右之南強度冷軋鋼板;TS為440MPa左右、且r值為1.5 左右之南強度冷軋鋼板,及TS為590MPa左右、且r值為 ^ 1 . 0左右之高強度冷軋鋼板予以成形,則於拉伸部位易發 生裂痕,故任一種高強度冷軋鋼板於實際情況僅可應用於 -較淺的拉伸零件。此外,要求TS為3 4 0至5 9 0 MPa、且具 ^ 有更高r值的高強度冷軋鋼板。具體而言,期望TS為340 至400MPa、且有1.8以上之r值,以為4〇〇至590MPa、 且有1 · 6以上、較佳為1 · 7以上之r值。 迄今,作為提高r值之方法,已知使用令c和n極力減 低’且大量添加T i和N b的IF鋼,於熱軋後於6 8 0。(:以上 312XP/發明說明書(補件 V94_〇5/941 〇5〇2〇 1276692 之高溫下捲取,令固溶C和N極力減低並且使析出物粗大 化,且於退火時促進具有有利於r值之集合組織的再結晶 粒之生成和成長的方法。作為同樣的方法,於日本專利特 &lt; 開平6 - 1 0 8 1 5 5號公報和日本專利3 2 9 1 6 3 9號公報中,揭示 .有使用令C和N極力減低、並添加T i的I F鋼,令T i (C,S) 生成,且於退火時令有利於r值的集合組織發達的方法。 但是,日本專利特開平 6 _ 1 0 8 1 5 5號公報所揭示之方法 中,係以具有2 6 0至3 Ο Ο Μ P a之T S的軟質冷軋鋼板作為對 φ 象,若應用於現存之大量添加P和Μη之具有340MPa以上 T S的I F高強度冷軋鋼板,則在熱軋後的捲取時,因在粒 界生成大量Fe-Ti-P、Fe-Nb-P等之P化物,且因Μη本身 大量,故r值顯著降低。又,日本專利3 2 9 1 6 3 9號公報所 揭示之方法中,雖提案添加大量P之具有340MPa以上之 TS的深拉伸用高強度冷軋鋼板,但於加壓成形時,有時因 P 的鑄造偏析所造成之板厚方向的不均勻組織而發生破 裂。1276692 IX. Description of the Invention: [Technical Field of the Invention] The present invention relates to a high-strength cold-rolled steel used for automobiles, home electric appliances, and the like; a plate, particularly for a tensile strength of 300 to 590 MPa (TS) , tensile strength) High-strength cold-rolled steel sheet excellent in deep drawability and a method for producing the same. [Prior Art] Conventionally, in an automobile part in which the outer outer panel and the inner panel of the door are difficult to form, φ is an IF having an excellent deep drawability of about 270 MPa and an r value of 1.8 to 2.0 (I nterstitia 1) F ree, seamless) soft cold rolled steel sheet (SPC 2 7 0 E, F ). In recent years, as the demand for weight reduction of automobile bodies has been further increased, IF high-strength cold-rolled steel sheets having a TS of 340 to 590 MPa have been developed for such difficult-to-shape parts. However, if these parts are to be used, the south strength cold-rolled steel sheet with a TS of 340 to 390 MPa and an r value of about 1.7 is used; the south strength cold-rolled steel sheet having a TS of about 440 MPa and an r value of about 1.5 is used. And when the high-strength cold-rolled steel sheet with a TS of about 590 MPa and an r value of about 1.9 is formed, cracks are likely to occur at the stretched portion, so any high-strength cold-rolled steel sheet can be applied only in actual conditions. Shallow stretch parts. Further, a high-strength cold-rolled steel sheet having a TS of 340 to 590 MPa and having a higher r value is required. Specifically, it is desirable that the TS is 340 to 400 MPa and has an r value of 1.8 or more, and is an r value of 4 〇〇 to 590 MPa and more than 1.6 or more, preferably 1. 7 or more. Heretofore, as a method of increasing the r value, it is known to use an IF steel in which c and n are extremely reduced and a large amount of T i and N b are added, after hot rolling at 680. (: The above 312XP / invention manual (supplement V94_〇5/941 〇5〇2〇1276692) coiled at a high temperature, so that the solid solution C and N are reduced in intensity and coarsened the precipitate, and promotes favorable during annealing. A method for producing and growing recrystallized grains of a set of r values. As a method of the same, it is disclosed in Japanese Patent Laid-Open No. Hei. No. Hei. No. 6-1 0 8 15 5 and Japanese Patent No. 3 2 9 1 6 3 9 In the publication, it is disclosed that there is a method in which T IF (C, S) is generated by using an IF steel in which C and N are minimized and T 1 is added, and a set structure favorable for r value is developed at the time of annealing. In the method disclosed in Japanese Laid-Open Patent Publication No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. When a large amount of IF high-strength cold-rolled steel sheet having 340 MPa or more TS is added to P and Μη, a large amount of Fe-Ti-P, Fe-Nb-P, and the like are formed at the grain boundary during coiling after hot rolling. Further, since the η itself is large in number, the value of r is remarkably lowered. Further, in the method disclosed in Japanese Patent No. 3 2 921 369, the proposal is added. The amount P of 340MPa TS having the above deep drawn high-strength cold rolled steel sheet, but in the press molding, casting times the plate thickness due to uneven tissue caused by the segregation of P in the direction of the rupture occurs.

另一方面,亦提案有對製造方法下功夫以令r值提高的 方法。例如,於日本專利特開平7 - 1 8 8 7 7 6號公報中揭示於 熱軋時一邊以α區域潤滑一邊進行完工軋製的方法。於曰 本專利特開平 9 - 2 7 9 2 4 9號公報中揭示於退火時以5 5 0至 7 5 0 °C之溫度區域施加1至5 0 %之軋製的方法。於日本專利 特開平 2 0 0 1 - 1 3 1 6 4 3號公報中揭示控制 N b、B添加鋼之 S i、Μ η、P量,並於酸洗、冷軋、退火後施加0 . 3至5 %的 軋製,並再度施以酸洗且通過熔融鍍鋅流線的方法。 ⑧ 312ΧΡ/發明說明書(補件)/94-05/94105020 1276692 板以5 0至9 Ο %之軋縮率予以冷軋作成冷軋鋼板的步驟;以 及令冷軋鋼板以7 5 0至8 7 0 °C予以連續退火、或以6 0 0至 7 5 0 °C予以閉箱退火的步驟;之製造方法而製造。 480 S CTS 580 + 0. 1 7/{([Ti] + 0· 08x[ sol· A1 ])x[P] }…(5) 此處,[Μ]為表示元素Μ之含量(質量%)。 【實施方式】 本發明者等人調查各種合金元素對於 IF高強度冷軋鋼 板之r值所造成之影響,得到以下之發現。On the other hand, there is also a proposal to work on the manufacturing method to increase the r value. For example, a method of performing finish rolling while lubricating in the α region during hot rolling is disclosed in Japanese Laid-Open Patent Publication No. Hei 7-108-76. A method of applying 1 to 50% of a rolling at a temperature of 550 to 750 ° C during annealing is disclosed in Japanese Laid-Open Patent Publication No. Hei 9- 2 7 9 2 4-9. The amount of S i, η η, and P of the steel to be added to N b and B is controlled and disclosed in Japanese Patent Laid-Open Publication No. Hei. No. 2 0 0 1 - 1 3 1 6 4 3, and is applied after pickling, cold rolling, and annealing. 3 to 5% of the rolling, and again subjected to pickling and passing through a hot-dip galvanizing line. 8 312 ΧΡ / invention manual (supplement) /94-05/94105020 1276692 The board is cold-rolled to a cold-rolled steel sheet at a rolling reduction ratio of 50 to 9 Ο %; and the cold-rolled steel sheet is 750 to 8 7 Manufactured by continuous annealing at 0 °C or by closed-loop annealing at 600 to 750 °C; 480 S CTS 580 + 0. 1 7/{([Ti] + 0· 08x[ sol· A1 ])x[P] } (5) Here, [Μ] is the content of the element Μ (% by mass) . [Embodiment] The inventors of the present invention investigated the influence of various alloying elements on the r value of the IF high-strength cold-rolled steel sheet, and obtained the following findings.

i ) 與先前之高強度冷軋鋼板相比較,若更大量添加 s ο 1 . A 1量,則 r值顯著提高。此效果在添加 0 . 4 % 以上之Μη時特別顯著。 ii) Si、Ρ之添加為有效於提高r值。 iii) 經由令P、sol · Al、Ti及視需要之Nb量與熱軋後 之捲取溫度適切化,則可取得更高之r值。 本發明係根據上述發現而進行,以下說明其詳細内容。 1) sol·A1量與r值 為了調查s ο 1 . A 1量與r值之關係,進行以下之試驗。 將 C ·· 0· 0 0 2 % 、 S i : 0· 2 5 % 、 P : 0 . 0 8 % &gt; S ·· 0 · 0 0 7 % 、 N b : 0 . 0 1 5 %、T i : 0 · 0 3 %、N : 0 · 0 0 2 %、B : 0 · 0 0 1 % 為一定,且 s ο 1 . A 1量以0 · 0 1至1 · 2 %、Μ η量以0 · 6至1 . 8 %變化之扁鋼 胚於1 2 5 0 °C中加熱,其後施以熱軋作成板厚3 m m的熱軌鋼 板,並施以5 8 0 °C下捲取1小時的模擬熱處理。將此熱軋 鋼板予以冷軋,作成板厚0 . 7 5 m m的冷軋鋼板,且於8 2 0 °C 下施以6 0秒鐘的連續退火,並施以伸長率0 . 7 %的調質軋 312XP/發明說明書(補件)/94-05/94105020 1276692 製。其後,以下列方法測定r值和TS。 將 J I S 5號試驗片由軋製方向、相對於軋製方向4 5 °方 向、相對於軋製方向 9 0 °方向採取,並且測定對於各個方 向的r值、T S,求出以下式所示之鋼板面内的平均值。 平均值=([T〇]+2[T45] + [T9〇])/4 此處,[T。]為軋製方向、[T 4 5 ]為相對於軋製方向4 5 °方 向、[T9〇]為相對於軋製方向90°方向之r值或TS。i) If the amount of s ο 1 . A 1 is added in a larger amount than in the previous high-strength cold-rolled steel sheet, the r value is remarkably improved. This effect is particularly noticeable when adding Μη of 0.4% or more. Ii) The addition of Si and yttrium is effective to increase the r value. Iii) A higher r value can be obtained by making P, sol · Al, Ti and, if necessary, the amount of Nb suitable for the coiling temperature after hot rolling. The present invention has been made based on the above findings, and the details thereof will be described below. 1) sol·A1 amount and r value In order to investigate the relationship between s ο 1 . A 1 amount and r value, the following test was performed. C ···0· 0 0 2 % , S i : 0· 2 5 % , P : 0 . 0 8 % &gt; S ·· 0 · 0 0 7 % , N b : 0 . 0 1 5 %, T i : 0 · 0 3 %, N : 0 · 0 0 2 %, B : 0 · 0 0 1 % is constant, and s ο 1 . A 1 amount is 0 · 0 1 to 1 · 2 %, Μ η The flat steel of 0. 6 to 1.8% change is heated at 1 250 °C, and then hot rolled into a hot-steel plate with a thickness of 3 mm and applied at 580 °C. Take 1 hour of simulated heat treatment. The hot-rolled steel sheet is cold-rolled to form a cold-rolled steel sheet having a thickness of 0.75 mm, and subjected to continuous annealing at 80 ° C for 60 seconds, and an elongation of 0.7% is applied. Tempering and rolling 312XP / invention manual (supplement) / 94-05/94105020 1276692 system. Thereafter, the r value and TS were measured in the following manner. The JIS No. 5 test piece was taken from the rolling direction, the direction of 45° with respect to the rolling direction, and the direction of the rolling direction of 90°, and the r value and TS for each direction were measured, and the following formula was obtained. The average value inside the steel plate. Average = ([T〇]+2[T45] + [T9〇])/4 Here, [T. ] is the rolling direction, [T 4 5 ] is a direction of 45° with respect to the rolling direction, and [T9〇] is an r value or TS of 90° with respect to the rolling direction.

圖1中示出s ο 1 . A1量與r值、T S的關係。圖中,黑圈 為Μ η量為1 . 8 %時之結果,白圈為s ο 1 . A 1與Μ η之總量為 1 . 8 %時之結果。 Μ η量為1 . 8 %時,r值在s ο 1 . A 1為0 . 1 %以上則為1 . 6以 上、在0 . 2至0 . 7 %則為1 . 7以上,若超過0 . 7 %則降低。T S 在sol.Al為0.1%以上則超過460MPa,且與sol.Al量一起 成比例地增加。 此時,sol.Al量每 1%之TS增加量為 35MPa。其與Μη 之固溶強化能力大約相同,故 s ο 1 . A 1與 Μ η之總量若為 1 . 8 %,則可得到白圈般之強度保持一定時之T S與r值的關 係。由此可知,添加 s ο 1 . A 1並削減Μ η,可於同一強度下 取得更高的r值。 又,若s ο 1 . A 1超過1 %,則於爲鋼胚之連續鑄造時,微 細的A 1 N於沃斯田鐵粒界析出,令粒界脆化,於扁鋼胚之 彎曲矯正時和其後之粗軋製時,易在扁鋼胚表面易發生破 裂。然後,由於此種扁鋼胚表面的破裂,易因鋼垢發生表 面缺陷,且最終製品之表面品質顯著降低。 ⑧ 312XP/發明說明書(補件)/94-05/94105020 1276692 由以上之結果,即使TS超過400MPa,若 sol.Al量為 0 . 1至1 %、較佳為0 . 2至0 . 7 %,則可取得1 . 6以上、較佳 為1.7以上之高r值。 : s ο 1 . A 1量為0 . 1至1 %時可取得高r值的理由認為如下。 ,即,A 1為令A r 3變態點上升的元素,故於熱軋時,由沃斯 田鐵變態成肥粒鐵後,於高溫之α區域中促進碳化物的析 出,且固溶C減少並且碳化物粗大化,故於退火時形成有 利於r值的再結晶集合組織,且r值提高。又,此外,推 φ 測A 1所造成之冷軋組織的變化等,亦有助於r值的提高。 2) Si 、 P量與r值 為了調查Si、P量與r值之關係,使用C: 0.002%、Μη: 1%、 S i : 0 . 0 0 7 % 、 s ο 1 . A 1 : 0 . 2 5 % 、 N b : 0 . 0 2% 、 T i : 0 . 0 1 % 、 N : 0 . 0 0 2 %、B : 0 . 0 0 10/〇 為一定,且 Si 量以 0 . 0 0 5 至 1.5%' P 量以0 . 0 0 3至0 . 1 5 %變化的扁鋼胚,進行與1 )之情況同樣 的試驗。Fig. 1 shows the relationship between s ο 1 . A1 amount and r value, T S . In the figure, the black circle is the result of the Μ η amount being 1.8%, and the white circle is s ο 1 . The total amount of A 1 and Μ η is 1.8%. When the amount of Μ η is 1.8%, the value of r is s ο 1 . A 1 is 0. 1% or more is 1.6 or more, and 0.2 to 0.7% is 1. 7 or more. 0. 7 % is lowered. T S exceeds 460 MPa in a case where sol. Al is 0.1% or more, and increases in proportion to the amount of sol. At this time, the TS increase per 1% of the amount of sol. Al was 35 MPa. It has about the same solid solution strengthening ability as Μη, so if the total amount of s ο 1 . A 1 and Μ η is 1.8%, the relationship between the T S and the r value when the intensity of the white circle is kept constant can be obtained. From this, it can be seen that by adding s ο 1 . A 1 and reducing Μ η, a higher r value can be obtained at the same intensity. Further, if s ο 1 . A 1 exceeds 1%, fine A 1 N is precipitated at the Worthfield iron grain boundary during continuous casting of the steel blank, and the grain boundary is embrittled, and the bending of the flat steel embryo is corrected. At the time of rough rolling and subsequent rolling, it is easy to crack on the surface of the flat steel. Then, due to the cracking of the surface of the flat steel, it is easy to cause surface defects due to the steel scale, and the surface quality of the final product is remarkably lowered. 8 312XP / invention manual (supplement) /94-05/94105020 1276692 From the above results, even if TS exceeds 400 MPa, if the amount of sol.Al is 0.1 to 1%, preferably 0.2 to 0.7% Further, a high r value of 1.6 or more, preferably 1.7 or more is obtained. : s ο 1 . The reason why the high value of r can be obtained when the amount of A 1 is from 0.1 to 1% is as follows. That is, A 1 is an element that raises the metamorphic point of Ar 3 , so when hot rolling, the ferrite is transformed into ferrite iron, and then the precipitation of carbides is promoted in the α region of high temperature, and solid solution C Since the carbide is coarsened and coarsened, a recrystallized aggregate structure favorable for the r value is formed at the time of annealing, and the r value is increased. In addition, it is also helpful to improve the r value by pushing φ to measure the change in the cold-rolled structure caused by A 1 . 2) The amount of Si, P and r are the relationship between the amount of Si and P and the value of r. C: 0.002%, Μη: 1%, S i : 0. 0 0 7 %, s ο 1 . A 1 : 0 2 5 % , N b : 0 . 0 2% , T i : 0 . 0 1 % , N : 0 . 0 0 2 %, B : 0 . 0 0 10/〇 is constant, and the amount of Si is 0. The 0 0 5 to 1.5% 'P quantity of flat steel embryos varying from 0. 0 0 3 to 0.15 % was subjected to the same test as in the case of 1).

圖2中,示出[Si] + 10x[P]與r值之關係。另外,圖中之 數字表示S i量。 sol.Al量為0 · 2 5 %的本發明鋼,若滿足下述式(2 ),則得 知可取得1 . 7以上之高r值。 0.3^ [Si] + 10x[P]^ 1.4 …(2) 此處,[M]為表示元素Μ的含量(質量%)。 但是,若S i、1 0 X Ρ的份量均超過1 . 5 %,則r值的惡化 大,故令S i、P量分別為1 . 5 %以下、0 . 1 5 %以下。 另外,對本發明之高強度冷軋鋼板施以合金化熔融鍍鋅 312XP/發明說明書(補件)/94-05/94105020 10 ⑧ 1276692 之情形,此些元素易引起鍵層的密黏不良,故令 S i量為 0 . 5 %以下、P量為0 . 0 8 %以下為佳。又,S i、P為令肥粒鐵 固溶強化的有效元素,故S i量為0 . 0 0 3 %以上、P量為0 . 0 1 % 以上為佳。 3 ) 其他之成分In Fig. 2, the relationship between [Si] + 10x [P] and the value of r is shown. In addition, the numbers in the figures indicate the amount of Si. When the steel of the present invention having a sol. Al content of 0 · 2 5 % satisfies the following formula (2), it is known that a high r value of 1.7 or more can be obtained. 0.3^ [Si] + 10x [P]^ 1.4 (2) Here, [M] represents the content (% by mass) of the element cerium. However, if the amount of S i and 1 0 X 均 exceeds 1.5%, the deterioration of the r value is large, so that the amounts of S i and P are respectively 1.5% or less and 0.15% or less. In addition, in the case of applying the alloyed hot-dip galvanized steel plate 312XP/invention specification (supplement)/94-05/94105020 10 8 1276692 to the high-strength cold-rolled steel sheet of the present invention, such elements are liable to cause poor adhesion of the bonding layer, so Let the amount of S i be 0.5% or less, and the amount of P be 0. 0 8 % or less. Further, since S i and P are effective elements for solid solution strengthening of the ferrite iron, the amount of Si is 0. 0 0 3 % or more, and the amount of P is 0. 0 1 % or more. 3) Other ingredients

C : C為與T i和N b結合形成碳化物。其量若超過0 . 0 1 5 %, 則此碳化物的量變多且r值顯著降低,故C量為0 . 0 1 5 %以 下、較佳為0 . 0 0 8 %以下、更佳為未滿0 . 0 0 4 %。但,C亦具 有以T i C、N b C型式經由析出強化而令強度增加之效果,故 於例如 T S為 4 4 Ο Μ P a左右的鋼中含有 0 . 0 0 4 %以上較有效 果。即,若C量為0.004至0.008 %,且Ti、Nb以與C之 原子比添加1 . 0以上,則可抑制r值的降低並且圖謀強度 上升。另外,於C量未滿0 . 0 0 0 5 %之情況,於退火時肥粒 鐵粒粗大化,且於加壓成形時易發生表面質地粗糙,故令 C量為0 . 0 0 0 5 %以上為佳。 Μη : Μη為經由固溶強化令強度增加的元素,於I F之高強 度冷軋鋼板中為不可或缺的元素。於取得 340MPa以上之 T S方面,必須令Μ η量為0 . 4 %以上。另一方面,其份量若 超過3 %則r值顯著降低,故令Μ η量為3 %以下、較佳為2 °/〇 以下、更佳為1 . 5 %以下。 Μη量增多則令r值降低的原因雖未必明朗,但認為係因 Μ η與固溶C進行相互作用而令r值降低。更且,推測Μ η 令 A r 3變態點降低,故熱軋時令析出的碳化物微細化,且 延遲碳化物的析出並增加固溶 C,故退火時無法形成有利 11 312XP/發明說明書(補件)/94-05/94105020 1276692 於r值的再結晶集合組織,令r值降低。 S : S為以硫化物型式存在於鋼中。其量若超過0 . 0 2 %則導 致延性的惡化,故S量為0 . 0 2 %以下、較佳為0 . 0 1 %以下。 : 另外,由除垢除銹性之觀點而言,期望S量為0 . 0 0 4 %以上。 k N : N量若超過0 . 0 1 %,則於扁鋼胚之連續鑄造時在肥粒鐵 粒界析出微細的 A 1 N、N b N、N b ( C,N ),令粒界脆化,且於 扁鋼胚鑄造時和其後之粗軋製時於扁鋼胚表面易發生破 裂。因此,令N量為0.01%以下。另外,N量愈少愈佳,但 φ 於目前的製鋼技術中極限在0 . 0 0 1 °/◦左右。 T i : T i具有令熱軋後之結晶粒微細化,且與C和N形成 析出物令固溶C、N減少而提高r值之效果。為充分發揮此 類T i效果,必須滿足下述式(1 ),添加T i。 1 ^ ([Ti]/48)/([C]/12+[N]/14) …(1) 此處,[M]為表示元素Μ之含量(質量%)。C : C is a combination of T i and N b to form a carbide. If the amount is more than 0.015%, the amount of the carbide is increased and the value of r is remarkably lowered. Therefore, the amount of C is 0. 0 1 5 % or less, preferably 0. 0 0 8 % or less, more preferably Less than 0. 0 0 4 %. However, C also has an effect of increasing the strength by precipitation strengthening in the T i C and N b C type. Therefore, for example, the steel having a TS of 4 4 Ο Μ P a contains 0.04% or more. . In other words, when the amount of C is from 0.004 to 0.008%, and Ti and Nb are added at a ratio of 1.0 or more to the atomic ratio of C, the decrease in the r value can be suppressed and the drawing strength can be increased. In addition, in the case where the amount of C is less than 0.05 0 5 %, the iron particles of the ferrite are coarsened during annealing, and the surface texture is liable to be rough during press forming, so that the amount of C is 0. 0 0 0 5 More than % is better. Μη : Μη is an element which increases strength by solid solution strengthening and is an indispensable element in high-strength cold-rolled steel sheets of I F . In order to obtain a T S of 340 MPa or more, the amount of Μ η must be 0.4% or more. On the other hand, if the amount exceeds 3%, the r value is remarkably lowered, so that the amount of Μ η is 3% or less, preferably 2 ° / 〇 or less, more preferably 1.5 % or less. Although the reason why the amount of Μη increases, the value of r is lowered is not necessarily clear, but it is considered that the value of r is lowered by the interaction of Μη with solid solution C. Furthermore, it is presumed that Μ η causes the Ar 3 metamorphic point to decrease, so that the precipitated carbide is finer during hot rolling, and the precipitation of the carbide is delayed and the solid solution C is increased, so that it is impossible to form an advantage during annealing. 11 312XP/Invention Manual ( Replenishment) /94-05/94105020 1276692 The recrystallization set structure at r values reduces the value of r. S : S is present in the steel in the form of a sulfide. If the amount exceeds 0.2%, the ductility is deteriorated. Therefore, the amount of S is 0.2% or less, preferably 0. 0% or less. Further, from the viewpoint of descaling and rust removing properties, the amount of S is desirably 0.04% or more. If the amount of k N : N exceeds 0.01%, fine A 1 N, N b N, N b ( C, N ) are precipitated at the ferrite grain boundary during continuous casting of the flat steel embryo. It is embrittled, and it is easy to crack on the surface of the flat steel when the flat steel is cast and coarsely rolled. Therefore, the amount of N is made 0.01% or less. In addition, the smaller the amount of N, the better, but the limit of φ in the current steelmaking technology is around 0.01 °C. T i : T i has an effect of making the crystal grains after hot rolling fine, and forming precipitates with C and N to reduce the solid solution C and N and increase the r value. In order to fully exert such a T i effect, it is necessary to satisfy the following formula (1) and add T i . 1 ^ ([Ti]/48)/([C]/12+[N]/14) (1) Here, [M] is a content (% by mass) indicating the element Μ.

但是,即使T i量為超過0. 2 %,r值的上升仍小,故令 T i量為0 . 2 %以下。另外,對本發明之高強度冷軋鋼板施以 合金化熔融鍍鋅之情況,由防止鍍層不句的觀點而言,令 T i量為0 . 0 4 %以下為佳。又,為確實取得T i添加所造成的 高r值,Ti量為0.005%以上為佳。 殘餘部分為Fe及不可避免的雜質。 除上述成分,再添加NbO. 002%以上,於取得更高r值方 面為佳。另外,此時,必須以滿足下述式(3 )之方式調整 Nb、Ti、C、N 之份量。 ([Nb]/93+[Ti]/48)/([C]/12+[N]/14) …(3) 312XP/發明說明書(補件)/94-05/94105020 12 ⑧However, even if the amount of T i is more than 0.2%, the rise of the r value is still small, so that the amount of T i is 0.2% or less. Further, in the case where the high-strength cold-rolled steel sheet of the present invention is subjected to alloying hot-dip galvanizing, the amount of T i is preferably 0.4% or less from the viewpoint of preventing plating. Further, in order to obtain a high r value due to the addition of T i , the amount of Ti is preferably 0.005% or more. The remainder is Fe and unavoidable impurities. In addition to the above ingredients, NbO. 002% or more is added, and it is preferable to obtain a higher r value. Further, at this time, it is necessary to adjust the amounts of Nb, Ti, C, and N in such a manner as to satisfy the following formula (3). ([Nb]/93+[Ti]/48)/([C]/12+[N]/14) (3) 312XP/Invention Manual (supplement)/94-05/94105020 12 8

1276692 °·00^ [Sb] + [Sn]/2^〇 2 …⑷ 此處^ [M]為表示元素M之含量(質量%)。 經由 S h、S π &gt; on&lt;添加,可防止扁鋼胚加熱時、捲取 才目退火爐(B A F )、連續退火流線(c A L)、連續熔融鍍 (C G L)等所造成之退火時的表層氮化和氧化,並且改 不句和錢層密黏性的惡化。又,防止鋅浴中之鋅氧 附著’並且提高鍍層外觀。更且,Sb、Sn減輕表面 才P希〗疲勞特性的惡化和拉伸成形後之韌性的惡化。 但是’ S b、S η之份量若超過〇. 2 %,則令鍍鋅密 韌性惡化。 4 ) 製造方法 本發明之高強度冷軋鋼板為經由具有:令具有上 之扁鋼胚於1080至1350 °C中加熱的步驟、令加熱 鋼胚以(Ar3變態點-20)至(Ar3變態點+150)。(:之完 溫度予以熱軋而作成熱軋鋼板的步驟、在熱軋鋼板 加N b之情況滿足下述式(5 );於添加n b之情況則滿 式(6)之捲取溫度CT予以捲取的步驟、令捲取後之 板以5 0至9 0 %之軋縮率予以冷軋而作成冷軋鋼板的 以及令冷軋鋼板以 7 5 0至 8 7 0 °C予以連讀退火;或 至7 5 0 °C予以閉箱退火的步驟之製造方法則可製造 480 SCTTS 5 80 + 0.1 7/{([Ti] + 0.08x[sol.Al])x[P]} ··· 480^CT^ 580+0.17/((0. 6x[Nb] + [Ti]+0. 08x[sol. A1 ])x[P]} 此處,[M]為表示元素M之含量(質量%)。1276692 °·00^ [Sb] + [Sn]/2^〇 2 (4) where ^ [M] is the content (% by mass) of the element M. By S h, S π &gt; on &lt; addition, it can prevent annealing caused by flat steel embryo heating, coiling annealing furnace (BAF), continuous annealing flow line (c AL), continuous hot-melt plating (CGL), etc. When the surface layer is nitrided and oxidized, and the change of the viscosity of the money layer is not changed. Further, zinc oxide adhesion in the zinc bath is prevented&apos; and the appearance of the plating layer is improved. Further, Sb and Sn alleviate the deterioration of the fatigue properties of the surface and the deterioration of the toughness after the stretch forming. However, if the amount of 'S b, S η exceeds 〇. 2%, the galvanizing tightness is deteriorated. 4) Manufacturing method The high-strength cold-rolled steel sheet of the present invention has a step of heating the steel preform at (Ar3 metamorphosis point -20) to (Ar3 metamorphosis) by having a step of heating the upper flat steel embryo at 1080 to 1350 °C. Point +150). (The step of hot rolling to form a hot-rolled steel sheet at the end of the temperature, the case of adding Nb to the hot-rolled steel sheet satisfies the following formula (5); and the case where the nb is added, the coiling temperature of the full-type (6) is applied to the CT The winding step, the rolled sheet is cold-rolled at a rolling reduction ratio of 50 to 90% to form a cold-rolled steel sheet, and the cold-rolled steel sheet is continuously annealed at 75 to 80 °C. Or 750 SCTTS 5 80 + 0.1 7/{([Ti] + 0.08x[sol.Al])x[P]} ··· 480^CT^ 580+0.17/((0. 6x[Nb] + [Ti]+0. 08x[sol. A1 ])x[P]} where [M] is the content of the element M (% by mass) ).

扁鋼胚為了令鐵塊中生成的Fe-Ti-P、Fe-Nb-P 3 UXP/發明說明書(補件)/94-05/941 〇5〇2〇 時、閉 鋅流線 善鑛層 化物的 氧化且 黏性和 述組成 後之扁 工軋製 為無添 足下述 熱札鋼 步驟、 以 6 0 0 〇 (5) …(6) 之P化 14 1276692 物充分固溶,必須令熱軋前之加熱溫度 S R T為 1 Ο 8 0 °C以 上。但是,若超過1 3 5 0 °C則表面品質惡化,故S R T必須為 1 3 5 0 °C 以下。 為取得優良之外觀,不僅對於初次鍋垢,對於熱軋時所 生成的二次鍋垢亦充分除去為佳。另外,於熱軋中,亦可 經由棒式加熱器進行加熱。 熱軋之完工軋製溫度F D T為了令熱軋後之組織微細化, 必須為(A r 3變態點-2 0 )至(A r 3變態點+ 1 5 0 )t:。In order to make the Fe-Ti-P, Fe-Nb-P 3 UXP/invention specification (supplement)/94-05/941 〇5〇2〇, the closed zinc flow line good ore layer formed in the iron block The oxidation and viscosity of the compound and the flat-rolling after the composition are fully dissolved in the following hot-strip steel step, and the P 14 1476692 of 6 0 〇(5) ...(6) must be fully dissolved. The heating temperature SRT before rolling is 1 Ο 80 °C or higher. However, if it exceeds 1 3 50 °C, the surface quality deteriorates, so S R T must be 1 3 50 °C or less. In order to obtain an excellent appearance, it is preferable not only for the first pot scale but also for the second pot scale generated during hot rolling. Further, in hot rolling, heating may also be carried out via a rod heater. The finishing rolling temperature F D T of the hot rolling must be (A r 3 metamorphic point - 2 0 ) to (A r 3 metamorphic point + 1 50 ) t: in order to refine the microstructure after hot rolling.

熱軋後之捲取溫度,對於複合添加A 1、P、T i及視需要 之N b之本發明的冷軋鋼板的r值造成極大影響。其係因添 加P的IF鋼,對於如上述之r值而言為不佳,並且易生成 Fe-Ti-P和Fe-Nb-Ρ等P化合物。一般,若捲取溫度為高 溫且析出物粗大化、且固溶C減少,則r值顯著提高。但 是,若捲取溫度超過適切溫度且呈高溫,則生成如上述的 P化物,且r值顯著降低。 於是,對於添加各種A 1、P、T i及視需要之N b的鋼, 調查最適合的捲取溫度,結果得知捲取溫度 CT於無添加 Nb 之情況若超過 580+0.17/{([Ti]+0.08x[sol.Al])x [P]}、 於添加 Nb 之情況若超過 580 + 0·17/{(0·6χ [N b ] + [ T i ] + 0 · 0 8 X [ s ο 1 · A 1 ] ) X [ Ρ ] },則生成 Ρ 化物且 r 值顯 著降低。又,捲取溫度C T若低於4 8 0 °C ,則即使未生成P 化物,亦令捲取時之碳化物的析出不夠充分,r值惡化。 因此,捲取溫度CT必須滿足上述之式(5 )或(6 )。The coiling temperature after hot rolling greatly affects the r value of the cold rolled steel sheet of the present invention in which A 1 , P, T i and optionally N b are added in combination. This is because the IF steel to which P is added is not preferable for the r value as described above, and P compounds such as Fe-Ti-P and Fe-Nb-Ρ are easily formed. In general, when the coiling temperature is high and the precipitates are coarsened and the solid solution C is decreased, the r value is remarkably improved. However, if the coiling temperature exceeds the appropriate temperature and is high, a P compound as described above is formed, and the r value is remarkably lowered. Therefore, for the steels in which various kinds of A 1 , P, T i and, if necessary, N b are added, the most suitable coiling temperature is investigated, and as a result, it is found that the coiling temperature CT exceeds 580 + 0.17 / { in the case where no Nb is added. [Ti]+0.08x[sol.Al])x [P]}, if the case of adding Nb exceeds 580 + 0·17/{(0·6χ [N b ] + [ T i ] + 0 · 0 8 X [ s ο 1 · A 1 ] ) X [ Ρ ] }, a telluride is formed and the r value is significantly lowered. Further, when the coiling temperature C T is lower than 480 ° C, even if the P compound is not formed, the precipitation of carbides during winding is insufficient, and the r value is deteriorated. Therefore, the coiling temperature CT must satisfy the above formula (5) or (6).

另外,於上述式(5 )與(6 )之(上限值-4 0 )至(上限值)°C 312XP/發明說明書(補件)/94-05/94105020 15 ⑧ 1276692 之溫度範圍中捲取為佳。 冷軋中,由提高 r值之觀點而言,必須令軋縮率為 5 0 至9 0 %,較佳為6 5至8 0 %。In addition, in the temperature range of the above formulas (5) and (6) (upper limit value - 4 0) to (upper limit value) °C 312XP / invention specification (supplement) /94-05/94105020 15 8 1276692 Rolling is better. In the cold rolling, from the viewpoint of increasing the r value, the rolling reduction ratio must be 50 to 90%, preferably 65 to 80%.

退火溫度A T於以C a 1和C G L予以連續退火之情況,必 須為7 5 0至8 7 0 °C。於低於7 5 0 °C之溫度下,再結晶不夠充 分,無法取得高r值。又,延伸等特性顯著惡化。於超過 8 7 0 °C之溫度下,Μ η量多之鋼板變成在超過 A r 3變態點進 行退火,強度極端增加且延伸,η值顯著惡化。為了安定 取得更高r值、高延伸,在820 °C以上之溫度下退火為佳。 又,以BAF退火之情況,因為退火時間長,故退火溫度AT 必須為6 0 0至7 5 0 °C 。 對於退火後之冷軋鋼板,視需要亦可經由電鍍或熔融鍍 層施以含鋅的鍍層。含鋅的鍍層可列舉鍍鋅、鍍合金化鋅、 鍍鋅鎳合金等。又,鍍層後亦可賦予有機皮膜處理。 (實施例) 將表1所示之鋼No.A至X之鋼溶製後,連續鑄造230mm 厚之扁鋼胚。此扁鋼胚以表2所示之加熱溫度SRT予以再 加熱後,以表2所示之完工軋製溫度F D T熱軋至板厚3. 2 m m 為止,並以表2所示之捲取溫度CT予以捲取。將此熱軋板 冷軋至板厚0.8mm為止後,以表2所示之退火溫度AT經由 CAL、CGL、BAF進行退火,並進行伸長率0.8%的調質軋製, 製作鋼板No. 1至34。另外,CGL中,退火後之鋼板於460 。(:之熔融鍍鋅浴中浸潰,其後以線上合金化處理爐 (in-line alloying treatment furnace)於 500 °C 下進行 16 312XP/發明說明書(補件)/94-05/94105020 1276692 合金化處理。鍍層表觀量為每單側45g/m2。 其後,以上述方法測定r值及TS。又,以目視檢查表面 缺陷並且調查表面品質。 結果示於表2。 表1、表2中均在最上段之式中的[Nb],在Nb無添加之 情況係視為0。The annealing temperature A T is continuously annealed with C a 1 and C G L and must be 750 to 870 °C. At temperatures below 750 °C, recrystallization is not sufficient enough to achieve high r values. Moreover, characteristics such as elongation are significantly deteriorated. At temperatures above 870 °C, the steel sheet with a large amount of Μ η becomes annealed at a point beyond the A r 3 metamorphic point, the strength is extremely increased and extended, and the η value is significantly deteriorated. In order to achieve higher r value and high elongation for stability, annealing at a temperature of 820 °C or higher is preferred. Also, in the case of BAF annealing, since the annealing time is long, the annealing temperature AT must be 600 to 750 °C. For the cold rolled steel sheet after annealing, a zinc-containing plating layer may be applied via electroplating or molten plating as needed. Examples of the zinc-containing plating layer include galvanization, zinc alloy plating, and galvanized nickel alloy. Further, the organic film may be treated after plating. (Example) After the steels of steel No. A to X shown in Table 1 were dissolved, a 230 mm thick flat steel blank was continuously cast. The flat steel blank is reheated by the heating temperature SRT shown in Table 2, and hot rolled to a thickness of 3.2 mm by the completion rolling temperature FDT shown in Table 2, and the coiling temperature shown in Table 2 is used. CT will be taken. After the hot-rolled sheet was cold-rolled to a thickness of 0.8 mm, the annealing temperature AT shown in Table 2 was annealed by CAL, CGL, and BAF, and temper rolling was performed at an elongation of 0.8% to prepare a steel sheet No. 1 To 34. In addition, in CGL, the annealed steel plate is at 460. (: impregnation in a hot-dip galvanizing bath, followed by in-line alloying treatment furnace at 500 °C 16 312XP / invention specification (supplement) / 94-05/94105020 1276692 alloy The coating amount was 45 g/m2 per one side. Thereafter, the r value and TS were measured by the above method. Further, the surface defects were visually inspected and the surface quality was investigated. The results are shown in Table 2. Table 1 and Table 2 [Nb] in the uppermost formula is considered to be 0 when Nb is not added.

本發明例之鋼板No. 1至24,可取得TS為3 4 0至40 OMPa、 r值1.8以上,TS為400至590MPa、且r值1.6以上,表 面品質亦良好。又,若與相同強度之比較例相比較,可知 本發明例之r值顯著較高。尤其Μ η量若超過1 %,則其效 果可顯著察見。 另一方面,比較例之鋼板Ν 〇. 2 5至3 4,無法取得T S為 340 至 400MPa、 r 值 1.8 以上,TS 為 400 至 590MPa、且 r 值1 . 6以上。相當於高Μ η量之習知高強度冷軋鋼板的鋼板 No. 27、28、29,r 值為低。又,鋼板 No. 30、31、32、33、 34 中,(Nb+Ti)/(C+N)比、C、 Si、 Μη、 P、 sol.Al、 Nb 均 在本發明範圍外,r值為低。其中,C量、(Nb + Ti)/(C + N) 比未被適切化,且固溶C、Μ η為共存之相當於習知低碳高 強度冷軋鋼板的鋼板Ν 〇. 3 0,即使提高s ο 1 . A 1亦無法取得 高 r值。又,Nb或Nb及sol.Al為本發明範圍外之鋼板 Ν 〇. 3 1、3 4,表面品質差。 另外,相當於習知之軟質冷軋鋼板SPC 2 7 0 F的鋼板 No. 25若與其中添力口有大量sol.Al量之鋼板Νο·26相比 較,則可知即使Μ η、Ρ量為低且添加s ο 1 . A 1,提高r值的 312XP/發明說明書(補件)/94-05/94105020 17 ⑧ 1276692 效果仍小。In the steel sheets No. 1 to 24 of the examples of the present invention, the TS was obtained from 340 to 40 OMPa, the r value was 1.8 or more, the TS was 400 to 590 MPa, and the r value was 1.6 or more, and the surface quality was also good. Further, when compared with the comparative example of the same strength, it is understood that the r value of the example of the present invention is remarkably high. In particular, if the amount of Μ η exceeds 1%, the effect can be clearly seen. On the other hand, in the steel sheet of the comparative example 2 2 2 25 to 34, the T S was 340 to 400 MPa, the r value was 1.8 or more, the TS was 400 to 590 MPa, and the r value was 1.6 or more. The steel plate No. 27, 28, and 29 of the conventional high-strength cold-rolled steel sheet corresponding to the high η η amount has a low r value. Further, in the steel sheets No. 30, 31, 32, 33, and 34, the ratio of (Nb + Ti) / (C + N), C, Si, Μη, P, sol. Al, and Nb are all outside the scope of the present invention, r The value is low. Among them, the amount of C, (Nb + Ti) / (C + N) ratio is not suitable, and the solid solution C and η η are coexisting steel sheets equivalent to conventional low carbon high strength cold rolled steel sheets. 3 0 Even if s ο 1 . A 1 is raised, a high r value cannot be obtained. Further, Nb or Nb and sol. Al are steel sheets Ν 3 3 1 and 3 4 outside the scope of the present invention, and the surface quality is poor. In addition, the steel sheet No. 25 which is equivalent to the conventional soft cold-rolled steel sheet SPC 2 7 0 F is compared with the steel sheet Νο·26 in which the amount of sol. And add s ο 1 . A 1, increase the r value of 312XP / invention manual (supplement) /94-05/94105020 17 8 1276692 The effect is still small.

312XP/發明說明書(補件)/94-05/94105020 18 1276692 $ lQI/〔N〕laI/s)/(8寸/〔u〕+ls/〔qN〕)(ss ¥^愈 oco οο·ζ312XP/Invention Manual (supplement)/94-05/94105020 18 1276692 $ lQI/[N]laI/s)/(8 inch/[u]+ls/[qN])(ss ¥^^oco οο·ζ

9CO °°z oco9CO °°z oco

I l 1½^ ¥5^生 ¥^愈 ΐ^φ ΐπΒφ ΐπΒφI l 11⁄2^ ¥5^生 ¥^越 ΐ^φ ΐπΒφ ΐπΒφ

5S 蛋s5S egg s

5S ss ¥SJ± ss5S ss ¥SJ± ss

5S is5S is

5S 95S 9

LoLo

LocdLocd

L.I rzL.I rz

l/Zl/Z

9CO9CO

Inco 9.1 ulx2+nsInco 9.1 ulx2+ns

Is u.o 2 寸oo 0 gs ocoIs u.o 2 inch oo 0 gs oco

IS 900 cooo Z9 ζοο 900 卜s 60 0 60IS 900 cooo Z9 ζοο 900 卜 60 0 60

IsIs

Is 96.0Is 96.0

Is 061Is 061

OS 1001 19 ·0 ZO&quot;TNVi ^·0··ΟΪΓΖ·0··ώ lo&lt;?:qs S000 Ό §OS 1001 19 ·0 ZO&quot;TNVi ^·0··ΟΪΓΖ·0··ώ lo&lt;?:qs S000 Ό §

8000 ·0 9S 200,0 § Z100 ·08000 · 0 9S 200,0 § Z100 ·0

Locoo 9000 ·0Locoo 9000 ·0

Locoo 10 ·0 scoo soo ·0 0£ _ 6000‘ggloo soirozol 9000 ·0 i 00000,ο 100 ·0Locoo 10 ·0 scoo soo ·0 0£ _ 6000‘ggloo soirozol 9000 ·0 i 00000,ο 100 ·0

qN 9200 io 600 ·0 9S0qN 9200 io 600 ·0 9S0

OIO 600 Ό 600.0 0910 090 090 Ό 一CN1I00 ·0 990 ·0 zooo ·0 〇〇0·0 goo ·0〇〇0 9000 ,0 § )100 ·0 9CO0 卜 so .οΙόεο οι 9000.020OIO 600 Ό 600.0 0910 090 090 Ό One CN1I00 ·0 990 ·0 zooo ·0 〇〇0·0 goo ·0〇〇0 9000 ,0 § )100 ·0 9CO0 卜 so .οΙόεο οι 9000.020

9000 Ό ISO 9000 ,0 § §0,09000 Ό ISO 9000 , 0 § § 0,0

SCOOOSCOOO

LooooLoooo

OIOO 卜一00 9Ϊ00 9100 OOI00 ioOIOO 卜 00 9Ϊ00 9100 OOI00 io

ISO zzoo 010· so IZOO ·0ISO zzoo 010· so IZOO ·0

Lolo 1 ZIOO ·0 OOI00 ·0 2:00,0 itzoo ♦0 91000 10 ·0 9S0 ·0 61,0 i ZZOO ♦0Lolo 1 ZIOO ·0 OOI00 ·0 2:00,0 itzoo ♦0 91000 10 ·0 9S0 ·0 61,0 i ZZOO ♦0

LOIO i ·0LOIO i ·0

_O_O

I 寸ZOO ·0I inch ZOO ·0

Iv.os s 豪·0 oos 9CO.0Iv.os s 豪·0 oos 9CO.0

Loro Ξ ss 0卜·0 9CO.0Loro Ξ ss 0 Bu·0 9CO.0

6S6S

LosLos

Los s.o cooLos s.o coo

LOS ΚΓ0LOS ΚΓ0

SO coo 6Z.0SO coo 6Z.0

Gz.o lz.0 0ΖΌGz.o lz.0 0ΖΌ

0°°I too 900 900 900 900 900 900 900 基 d §·0 0 — oso § oso 020 00卜0 s ·0 so 1^0 900 900 oog 900 cooo 900 so 900 ocoo 20°°I too 900 900 900 900 900 900 900 base d §·0 0 — oso § oso 020 00 bu 0 s ·0 so 1^0 900 900 oog 900 cooo 900 so 900 ocoo 2

I 190 Ό 9900 0090.0 0 990 ·0 0000 0000 G§ 00卜0 09卜0 i .0 1.0 oso 9Ό 6·0 6.1 ΖΊI 190 Ό 9900 0090.0 0 990 · 0 0000 0000 G§ 00 Bu 0 09 Bu 0 i .0 1.0 oso 9Ό 6·0 6.1 ΖΊ

i.CNI 9*0 ocvi coCNi 3i.CNI 9*0 ocvi coCNi 3

LO.I oLOroLO.I oLOro

!S 10. 10!S 10. 10

OCNI ozOCNI oz

OZ oz 09 10OZ oz 09 10

ICNI 3ICNI 3

Logo 00100Logo 00100

ZZOO i )200ZZOO i )200

OHO onoo οειοο 0ΖΙ00 Ξ Ό 0卜00 iro^oo ΟΟΓ0 soOHO onoo οειοο 0ΖΙ00 Ξ Ό 0卜00 iro^oo ΟΟΓ0 so

Is 9CO00 10Is 9CO00 10

OCNIOO ooros 06100 010 ·0 〇〇·0 10 看00 —0OCNIOO ooros 06100 010 ·0 〇〇·0 10 See 00 —0

rCNIrCNI

OCNI ocozoo ro οδ.οζ.ε CN1OCNI ocozoo ro οδ.οζ.ε CN1

00 Ό I 8ΙΌ §0·0 卜 I°00 Ό I 8ΙΌ §0·0 Bu I°

r-HooIOO 9100 s 0·0 9Z00 L.o 00 9S0 •ONl I&lt;r-HooIOO 9100 s 0·0 9Z00 L.o 00 9S0 •ONl I&lt;

VV

OQ 0 a 0OQ 0 a 0

H 0 dH 0 d

H sH s

I il ΛI il Λ

IkIk

X 0ss56/s46/ip}s)_^^SRa®/dxzIe ⑧ 1276692 表2 鋼板 No. 鋼No. 熱軋彳条件 退火條件 退火流線 機械特性 表面品質趙 580+0.17/((0. 6[Nb]+ [Ti]+0. 08x[sol. Al]) χ[Ρ]Γ 備註 SRT (°C) FDT CC) CT CC) AT CC) r值 TS (MPa) 1 A 1250 890 640 840 CGL 1.89 347 〇 666 發明例 2 1250 890 540 720 BAF 1.86 342 〇 666 發明例 3 1280 990 640 840 CGL 1.85 345 〇 666 發明例 4 1220 850 640 840 CGL 1.90 349 〇 666 發明例 5 1220 780 640 840 CGL 1.77 340 〇 666 發明例 6 B 1220 870 620 770 CGL 1.83 408 〇 622 發明例 7 1220 870 620 840 CGL 1.87 395 〇 622 發明例 8 1220 870 620 870 CGL 1.88 390 〇 622 發明例 9 1300 975 620 870 CGL 1.85 385 〇 622 發明例 10 1220 840 620 870 CGL 1.90 392 〇 622 發明例 — 1220 760 620 870 CGL 1.85 387 〇 622 發明例 C 1220 850 580 820 CGL 1.81 446 〇 618 發明例 13 1220 850 615 820 CGL 1.85 444 〇 618 發明例 14 D 1220 850 620 820 CGL 1. 66 440 〇 630 發明例 15 E 1250 940 600 830 CGL 1.73 442 〇 603 發明例 16 F 1220 860 680 800 CGL 1.75 403 〇 - 發明例 17 G 1290 840 580 860 CAL 1.60 530 〇 599 發明例 18 H 1220 890 670 850 CGL 1.90 340 〇 698 發明例 19 I 1220 840 600 820 CGL 1.90 440 〇 611 發明例 20 J 1220 830 580 790 CAL 1.85 445 〇 602 發明例 21 K 1220 830 600 830 CGL 1.96 440 〇 609 發明例 22 L 1220 850 600 840 CGL 1.89 442 〇 613 發明例 23 M 1220 850 600 840 CGL 1.85 449 〇 608 發明例 24 N 1220 850 600 830 CGL 1.82 445 〇 611 發明例 m 0 1200 910 680 830 CGL 1.82 289 〇 - 比較例 26 P 1200 930 680 830 CGL 1.83 294 〇 793 比較例 27 Q 1230 880 640 830 CGL 1.69 340 〇 697 比較例 28 R 1220 880 640 820 CGL 1.62 392 〇 642 比較例 .29 S 1220 840 640 800 CGL 1.46 440 〇 632 比較例 30 T 1220 890 680 770 CGL 1.12 405 〇 682 比較例 31 U 1270 950 640 820 CAL 1.40 480 X 一 比較例 ^32 V 1270 840 640 800 CAL 1.43 450 〇 641 比較例 33 w 1270 950 600 820 CAL 1.49 475 〇 599 比較例 '34 X 1290 1000 600 820 CAL 1.52 444 X 595 比較例 XI:超過800°C者視為-。 ※2:〇表面無缺陷或在容許範圍内;X因锅垢性表面缺陷造成表面惡化。 312XP/發明說明書(補件)/94·05/94105020 1276692 【圖式簡單說明】 圖1為示出sol. A1量與r值、TS之關係之圖。 圖2為示出[Si] + 10x[P]與r值之關係之圖。X 0ss56/s46/ip}s)_^^SRa®/dxzIe 8 1276692 Table 2 Steel Plate No. Steel No. Hot Rolling Condition Annealing Condition Annealing Streamline Mechanical Properties Surface Quality Zhao 580+0.17/((0. 6[ Nb]+ [Ti]+0. 08x[sol. Al]) χ[Ρ]Γ Remarks SRT (°C) FDT CC) CT CC) AT CC) r value TS (MPa) 1 A 1250 890 640 840 CGL 1.89 347 〇 666 Inventive Example 2 1250 890 540 720 BAF 1.86 342 〇 666 Inventive Example 3 1280 990 640 840 CGL 1.85 345 〇 666 Inventive Example 4 1220 850 640 840 CGL 1.90 349 〇 666 Inventive Example 5 1220 780 640 840 CGL 1.77 340 〇 666 Inventive Example 6 B 1220 870 620 770 CGL 1.83 408 〇 622 Inventive Example 7 1220 870 620 840 CGL 1.87 395 〇 622 Inventive Example 8 1220 870 620 870 CGL 1.88 390 〇 622 Inventive Example 9 1300 975 620 870 CGL 1.85 385 〇 622 Inventive Example 10 1220 840 620 870 CGL 1.90 392 〇 622 Inventive Example - 1220 760 620 870 CGL 1.85 387 〇 622 Inventive Example C 1220 850 580 820 CGL 1.81 446 〇 618 Inventive Example 13 1220 850 615 820 CGL 1.85 444 〇 618 Inventive Example 14 D 1220 850 620 820 CGL 1. 66 440 〇630 Inventive Example 15 E 1250 940 600 830 CGL 1. 73 442 〇 603 Inventive Example 16 F 1220 860 680 800 CGL 1.75 403 〇 - Invention Example 17 G 1290 840 580 860 CAL 1.60 530 〇 599 Inventive Example 18 H 1220 890 670 850 CGL 1.90 340 〇 698 Inventive Example 19 I 1220 840 600 820 CGL 1.90 440 〇 611 Inventive Example 20 J 1220 830 580 790 CAL 1.85 445 〇 602 Inventive Example 21 K 1220 830 600 830 CGL 1.96 440 〇 609 Inventive Example 22 L 1220 850 600 840 CGL 1.89 442 〇613 Inventive Example 23 M 1220 850 600 840 CGL 1.85 449 〇608 Inventive Example 24 N 1220 850 600 830 CGL 1.82 445 〇 611 Inventive Example m 0 1200 910 680 830 CGL 1.82 289 〇 - Comparative Example 26 P 1200 930 680 830 CGL 1.83 294 〇 793 Comparative Example 27 Q 1230 880 640 830 CGL 1.69 340 〇697 Comparative Example 28 R 1220 880 640 820 CGL 1.62 392 〇642 Comparative Example. 29 S 1220 840 640 800 CGL 1.46 440 〇 632 Comparative Example 30 T 1220 890 680 770 CGL 1.12 405 〇 682 Comparative Example 31 U 1270 950 640 820 CAL 1.40 480 X A comparative example ^32 V 1270 840 640 800 CAL 1.43 450 〇641 Comparative Example 33 w 1270 950 600 820 CAL 1.49 475 〇599 Comparative Example '34 X 1 290 1000 600 820 CAL 1.52 444 X 595 Comparative Example XI: Those exceeding 800 °C are considered to be -. *2: The surface of the crucible is free from defects or within the allowable range; X is deteriorated due to surface defects of the scale. 312XP/Invention Manual (Supplement)/94·05/94105020 1276692 [Simplified Schematic Description] Fig. 1 is a view showing the relationship between the amount of sol. A1 and the r value and TS. Fig. 2 is a graph showing the relationship between [Si] + 10x [P] and r value.

312XP/發明說明書(補件)/94-05/94105020 21312XP/Invention Manual (supplement)/94-05/94105020 21

Claims (1)

—— _~ 2ϋΒ6 - 4 SEP 作年彳月7曰修(更)正本&amp; 欠 十、申請專利範圍: -^ 1 . 一種高強度冷軋鋼板,其特徵為包含質量%計之 C : 0 . 0 1 5 % 以下、S i : 1 · 5 % 以下、Μ η ·· (K 4 至 3 %、P U 5 % 以下、 S : 0 · 0 2 %以下、酸可溶A 1 (以下表示為s ο 1 · A 1 ) : 0 . 1至1 %、 N : 0 . 0 1 %以下、T i : 0 . 2 %以下,殘餘部分為F e及不可避免的 雜質,且滿足下述之式(1 ); 1 ^ ([Ti ]/48)/( [C]/12 + [N]/14) …(1) 其中,[M]表示元素Μ之含量(質量%)。 2. 如申請專利範圍第1項之高強度冷軋鋼板,其中質量°/〇 計之 s ο 1 · A 1 ·· 0 · 2 至 0 . 7 %。 3. 如申請專利範圍第1項之高強度冷軋鋼板,其為滿足 下述之式(2); 0.3^ [Si] + 10x[P]^ 1.4 …(2 ) 其中,[M]表示元素Μ之含量(質量%)。 4. 如申請專利範圍第2項之高強度冷軋鋼板,其為滿足 下述之式(2 ); 0.3^ [Si] + 10x[P]^ 1.4 …(2 ) 其中,[M]表示元素Μ之含量(質量%)。 5 .如申請專利範圍第1項之高強度冷軋鋼板,其中進一 步含有質量%計之N b : 0 · 0 0 2至0 . 0 2 %,且滿足下述之式(3 ); ([Nb]/93+[Ti]/48)/([C]/12+[N]/14)…(3) 其中,[M]表示元素Μ之含量(質量%)。 6 .如申請專利範圍第4項之高強度冷軋鋼板,其中進一 步含有質量%計之N b : 0 . 0 0 2至0 . 0 2 %,且滿足下述之式(3 ); 22 326\總檔\94\94105020\94105020(替換)-1 1276692 ([Nb]/93+[Ti]/48)/([C]/12+[N]/14)…(3) 其中,[M]表示元素M之含量(質量%)。 7 .如申請專利範圍第1項之高強度冷軋鋼板,其中進一 步含有質量%計之Β : 0 . 0 0 0 1至0 . 0 0 3 °/〇。 8 .如申請專利範圍第6項之高強度冷軋鋼板,其中進一 步含有質量%計之Β : 0 . 0 0 0 1至0 . 0 0 3 %。—— _~ 2ϋΒ6 - 4 SEP Year of the year 7 曰 repair (more) original &amp; owe ten, the scope of application for patent: -^ 1. A high-strength cold-rolled steel sheet characterized by a mass% of C: 0 0 1 5 % or less, S i : 1 · 5 % or less, Μ η ·· (K 4 to 3%, PU 5 % or less, S: 0 · 0 2 % or less, acid soluble A 1 (hereinafter referred to as s ο 1 · A 1 ) : 0 . 1 to 1 %, N : 0 . 0 1 % or less, T i : 0 . 2 % or less, the residual portion is F e and unavoidable impurities, and the following formula is satisfied (1); 1 ^ ([Ti ]/48)/( [C]/12 + [N]/14) (1) where [M] represents the content of the element ( (% by mass). The high-strength cold-rolled steel sheet of the first item of the patent range, wherein the mass ° / 之 s ο 1 · A 1 ·· 0 · 2 to 0.7%. 3. High-strength cold rolling as in claim 1 Steel sheet which satisfies the following formula (2); 0.3^ [Si] + 10x [P]^ 1.4 (2) wherein [M] represents the content of the element ( (% by mass). The high-strength cold-rolled steel sheet of item 2, which satisfies the following formula (2); 0.3^ [Si] + 10x [P]^ 1.4 (2) [M] represents the content of the element ( (% by mass). 5. The high-strength cold-rolled steel sheet of claim 1 which further contains N% of mass %: 0 · 0 0 2 to 0. 0 2 %, and satisfy the following formula (3); ([Nb]/93+[Ti]/48)/([C]/12+[N]/14) (3) where [M] represents an element Content of bismuth (% by mass) 6. High-strength cold-rolled steel sheet according to item 4 of the patent application, further containing N% of mass %: 0. 0 0 2 to 0. 0 2 %, and satisfying the following Equation (3); 22 326\Total file\94\94105020\94105020 (replacement)-1 1276692 ([Nb]/93+[Ti]/48)/([C]/12+[N]/14) (3) where [M] represents the content (% by mass) of the element M. 7. The high-strength cold-rolled steel sheet according to item 1 of the patent application, further containing % by mass: 0. 0 0 0 1 To 0. 0 0 3 ° / 〇 8. The high-strength cold-rolled steel sheet according to claim 6 of the patent application, further containing 5% by mass: 0. 0 0 0 1 to 0. 0 0 3 %. 9 .如申請專利範圍第1項之高強度冷軋鋼板,其中進一 步含有自質量%計之Cm 0 · 0 3至0 · 5 %、N i : 0 · 0 3至0 . 5 %、 Cr:0.03 至 0.5%、Μ〇:0·05 至 0.3% 及 V : 0 . 0 0 5 JL 0.5% 之中 選出之至少一種元素。 1 0 .如申請專利範圍第 8項之高強度冷軋鋼板,其中進 一步含有自質量%計之C ικ 0 . 0 3至0 · 5 %、N i : 0 · 0 3至0 . 5 %、 Cr : 0. 03 ^ (L5%、M〇:0.05 至 0.3 % 及[0.005 至 0.5% 之中 選出之至少一種元素。9. The high-strength cold-rolled steel sheet according to item 1 of the patent application, further comprising Cm 0 · 0 3 to 0 · 5 % by mass %, N i : 0 · 0 3 to 0.5%, Cr: At least one element selected from 0.03 to 0.5%, Μ〇: 0.05 to 0.3%, and V: 0. 0 0 5 JL 0.5%. 1 0. The high-strength cold-rolled steel sheet according to item 8 of the patent application, further comprising C κκ 0 . 0 3 to 0 · 5 % by mass %, N i : 0 · 0 3 to 0.5%, Cr : 0. 03 ^ (L5%, M〇: 0.05 to 0.3% and at least one of [0.005 to 0.5% selected). 1 1 .如申請專利範圍第1項之高強度冷軋鋼板,其中進 一步含有自質量%計之31):0.002至0.2%及811:0.002至 0.2 %之中選出之至少一種元素,且滿足下述之式(4); 0. 0 0 2 ^ [Sb] + [Sn]/2^ 0. 2 …(4) 其中,[M]表示元素Μ之含量(質量%)。 1 2 .如申請專利範圍第1 0項之高強度冷軋鋼板,其中進 一步含有自質量%計之 S b : 0 · 0 0 2至 0 · 2 %及 S η : 0 . 0 0 2至 0.2 %之中選出之至少一種元素,且滿足下述之式(4); 0.0 0 2 ^ [Sb] + [Sn]/2^ 0. 2 …(4) 其中,[M]表示元素Μ之含量(質量%)。 23 326\總檔\94\94105020\94105020(替換)-1 1276692 1 3 . —種高強度冷軋鋼板之製造方法,其特徵為具有: 令具有申請專利範圍第1至1 2項中任一項組成之扁鋼 胚,於1 0 8 0至1 3 5 0 °C中加熱的步驟; 令上述加熱後之扁鋼胚,以(A r3變態點-2 0 )至(A r3變態 點+ 1 5 0 ) °C之完工軋製溫度予以熱軋而作成熱軋鋼板的步 驟; 令上述熱軋鋼板以滿足下述式(5)或(6)之捲取溫度 CT 予以捲取的步驟;1 1 . The high-strength cold-rolled steel sheet according to item 1 of the patent application, further comprising at least one element selected from the group consisting of 31% by mass: 0.002 to 0.2% and 811: 0.002 to 0.2%, and satisfying The formula (4); 0. 0 0 2 ^ [Sb] + [Sn]/2^ 0. 2 (4) where [M] represents the content of the element Μ (% by mass). 1 2 . The high-strength cold-rolled steel sheet of claim 10, further comprising S b from 0% to 0. 2% and S η: 0. 0 0 2 to 0.2. At least one element selected from %, and satisfying the following formula (4); 0.0 0 2 ^ [Sb] + [Sn]/2^ 0. 2 (4) where [M] represents the content of the element Μ (quality%). 23 326\总档\94\94105020\94105020 (replacement)-1 1276692 1 3 . A method for manufacturing a high-strength cold-rolled steel sheet, characterized by having: one of claims 1 to 12 a flat steel embryo consisting of heating in a temperature of 1 800 to 1 350 ° C; to make the above-mentioned heated flat steel embryo, (A r3 metamorphosis point - 2 0 ) to (A r3 metamorphic point + a step of forming a hot-rolled steel sheet by hot rolling at a finishing rolling temperature of 10.5; and a step of winding the hot-rolled steel sheet to satisfy a coiling temperature CT of the following formula (5) or (6); 令上述捲取後之熱軋鋼板以5 0至9 0 %之軋縮率予以冷軋 而作成冷軋鋼板的步驟;以及 令上述冷軋鋼板於 750至 870 °C下連續退火、或於 600 至7 5 0 °C下閉箱退火的步驟; 480 SCTS 580 + 0· 17/{([Ti] + 0. 08x[sol. Α1])χ[Ρ]} ”·(5) 480 ^CT^ 580 + 0. 17/{(0. 6x[Nb] + [Ti ] + 0. 08x[sol. A1 ] )χ[Ρ]} --(6) 其中,[M]表示元素M之含量(質量%)。a step of cold-rolling the hot-rolled steel sheet after the coiling at a rolling reduction ratio of 50 to 90% to form a cold-rolled steel sheet; and continuously annealing the cold-rolled steel sheet at 750 to 870 ° C or at 600 The step of closed-box annealing to 750 °C; 480 SCTS 580 + 0· 17/{([Ti] + 0. 08x[sol. Α1])χ[Ρ]} ”·(5) 480 ^CT^ 580 + 0. 17/{(0. 6x[Nb] + [Ti ] + 0. 08x[sol. A1 ] )χ[Ρ]} --(6) where [M] represents the content of the element M (quality) %). 24 326\總檔\94\94105020\94105020(替換)-124 326\main file\94\94105020\94105020 (replace)-1
TW094105020A 2004-02-25 2005-02-21 High strength cold rolled steel sheet and method for manufacturing the same TWI276692B (en)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
JP2004049034 2004-02-25

Publications (2)

Publication Number Publication Date
TW200532032A TW200532032A (en) 2005-10-01
TWI276692B true TWI276692B (en) 2007-03-21

Family

ID=34747463

Family Applications (1)

Application Number Title Priority Date Filing Date
TW094105020A TWI276692B (en) 2004-02-25 2005-02-21 High strength cold rolled steel sheet and method for manufacturing the same

Country Status (6)

Country Link
US (1) US20060037677A1 (en)
EP (1) EP1568791A1 (en)
KR (2) KR20060042036A (en)
CN (1) CN100439544C (en)
CA (1) CA2496212C (en)
TW (1) TWI276692B (en)

Families Citing this family (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CA2575241C (en) 2004-07-27 2011-07-12 Nippon Steel Corporation Steel sheet having high young's modulus, hot-dip galvanized steel sheet using the same, alloyed hot-dip galvanized steel sheet, steel pipe having high young's modulus, and methodsfor manufacturing these
JP5042232B2 (en) * 2005-12-09 2012-10-03 ポスコ High-strength cold-rolled steel sheet excellent in formability and plating characteristics, galvanized steel sheet using the same, and method for producing the same
JP5228447B2 (en) 2006-11-07 2013-07-03 新日鐵住金株式会社 High Young's modulus steel plate and method for producing the same
DE102009053260B4 (en) * 2009-11-05 2011-09-01 Salzgitter Flachstahl Gmbh Process for coating steel strips and coated steel strip
JP5786318B2 (en) * 2010-01-22 2015-09-30 Jfeスチール株式会社 High-strength hot-dip galvanized steel sheet with excellent fatigue characteristics and hole expansibility and method for producing the same
JP5786316B2 (en) * 2010-01-22 2015-09-30 Jfeスチール株式会社 High-strength hot-dip galvanized steel sheet excellent in workability and impact resistance and method for producing the same
JP6111522B2 (en) * 2012-03-02 2017-04-12 Jfeスチール株式会社 High-strength hot-dip galvanized steel sheet and manufacturing method thereof
KR101647224B1 (en) * 2014-12-23 2016-08-10 주식회사 포스코 High strength galvanized steel sheet having excellent surface qualities, plating adhesion and formability and method for manufacturing the same
EP3342893A4 (en) * 2015-08-24 2019-01-16 Nippon Steel & Sumitomo Metal Corporation Alloying molten zinc-plated steel sheet and manufacturing method therefor
CA2995917C (en) * 2015-08-24 2020-04-14 Nippon Steel & Sumitomo Metal Corporation Rail vehicle axle
CN106119495B (en) * 2016-08-19 2019-02-01 武汉钢铁有限公司 A kind of manufacturing method of cold rolling medium high carbon structural steel
CN111926252B (en) * 2020-07-31 2022-01-18 马鞍山钢铁股份有限公司 Hot-rolled pickled steel plate for deep drawing and production method thereof
CN115558858A (en) * 2022-10-08 2023-01-03 北京首钢股份有限公司 Steel strip, preparation method thereof and automobile outer plate

Family Cites Families (19)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS63317627A (en) * 1987-06-18 1988-12-26 Kawasaki Steel Corp Semiprocessing non-oriented silicon steel sheet combining low iron loss with high magnetic permeability and its production
US5360493A (en) * 1992-06-08 1994-11-01 Kawasaki Steel Corporation High-strength cold-rolled steel sheet excelling in deep drawability and method of producing the same
JP2671726B2 (en) * 1992-09-30 1997-10-29 日本鋼管株式会社 Manufacturing method of cold rolled steel sheet for ultra deep drawing
CN1039034C (en) * 1993-01-14 1998-07-08 日本钢管株式会社 Cold rolled steel sheet of excellent delayed fracture resistance and superhigh strength and method of manufacturing the same
US5470529A (en) * 1994-03-08 1995-11-28 Sumitomo Metal Industries, Ltd. High tensile strength steel sheet having improved formability
US5853903A (en) * 1996-05-07 1998-12-29 Nkk Corporation Steel sheet for excellent panel appearance and dent resistance after panel-forming
TW515847B (en) * 1997-04-09 2003-01-01 Kawasaki Steel Co Coating/baking curable type cold rolled steel sheet with excellent strain aging resistance and method for producing the same
JP2000199031A (en) * 1998-10-29 2000-07-18 Sumitomo Metal Ind Ltd Cold rolled steel sheet excellent in workability and its production
EP1669472B1 (en) * 1998-12-07 2008-02-27 JFE Steel Corporation High strength cold rolled steel sheet and method for manufacturing the same
JP3740875B2 (en) * 1998-12-28 2006-02-01 Jfeスチール株式会社 Cold-rolled thin steel sheet for deep drawing with excellent impact resistance
KR100433248B1 (en) * 1999-12-28 2004-05-27 주식회사 포스코 a cold-rolled steel with good formability and anti-dent property and the method of manufacturing the same
JP3968964B2 (en) * 2000-06-30 2007-08-29 Jfeスチール株式会社 Steel plate for heat shrink band
WO2002022904A1 (en) * 2000-09-12 2002-03-21 Nkk Corporation Super high tensile cold-rolled steel plate and method for production thereof
KR20020073564A (en) * 2000-11-28 2002-09-27 가와사끼 세이데쓰 가부시키가이샤 Composite structure type high tensile strength steel plate, plated plate of composite structure type high tensile strength steel and method for their production
US6786981B2 (en) * 2000-12-22 2004-09-07 Jfe Steel Corporation Ferritic stainless steel sheet for fuel tank and fuel pipe
KR100530073B1 (en) * 2001-12-20 2005-11-22 주식회사 포스코 High strength steel sheet having superior workability and method for manufacturing there of
KR100530077B1 (en) * 2001-12-21 2005-11-22 주식회사 포스코 Deep Drawing High Strength Steel Sheet With Secondary Working Brittleness Resistance and Formability and A Method for Manufacturing Thereof
JP2003193189A (en) * 2001-12-25 2003-07-09 Jfe Steel Kk High tensile strength galvanized steel sheet with composite structure having excellent deep drawability and production method therefor
JP4414883B2 (en) * 2002-06-28 2010-02-10 ポスコ High-strength cold-rolled steel sheet for ultra-deep drawing excellent in formability and weldability and its manufacturing method

Also Published As

Publication number Publication date
KR20070089670A (en) 2007-08-31
KR20060042036A (en) 2006-05-12
TW200532032A (en) 2005-10-01
US20060037677A1 (en) 2006-02-23
CN1661127A (en) 2005-08-31
CA2496212C (en) 2010-01-12
EP1568791A1 (en) 2005-08-31
CN100439544C (en) 2008-12-03
CA2496212A1 (en) 2005-08-25

Similar Documents

Publication Publication Date Title
TWI276692B (en) High strength cold rolled steel sheet and method for manufacturing the same
JP5042232B2 (en) High-strength cold-rolled steel sheet excellent in formability and plating characteristics, galvanized steel sheet using the same, and method for producing the same
TWI468534B (en) High-strength cold rolled steel sheet and manufacturing method thereof
KR101217921B1 (en) High-strength hot-dip galvanized steel sheet and manufacturing method therefor
JP7055171B2 (en) TWIP steel sheet with austenitic matrix
EP2753725B1 (en) Low density high strength steel and method for producing said steel
US11965222B2 (en) Method for producing hot-rolled steel sheet and method for producing cold-rolled full hard steel sheet
JP5569657B2 (en) Steel sheet with excellent aging resistance and method for producing the same
JP6225604B2 (en) 440 MPa class high-strength galvannealed steel sheet excellent in deep drawability and method for producing the same
WO2017168991A1 (en) Thin steel sheet, plated steel sheet, hot-rolled steel sheet manufacturing method, cold-rolled full hard steel sheet manufacturing method, thin steel sheet manufacturing method, and plated steel sheet manufacturing method
JP2006307327A (en) High ductility and high strength alloyed hot-dip galvanized steel sheet having excellent surface property and brittle resistance to secondary processing and method for producing same
JP6606905B2 (en) Alloyed hot-dip galvanized steel sheet for outer panel of automobile and manufacturing method thereof
JP2023547102A (en) Ultra-high strength steel plate with excellent ductility and its manufacturing method
WO2014178358A1 (en) Galvanized steel sheet and production method therefor
JP5397141B2 (en) Alloyed hot-dip galvanized steel sheet and method for producing the same
JP2013076139A (en) High-strength hot-dip galvanized steel sheet superior in plating adhesion and formability, and method for manufacturing the same
JP6007571B2 (en) High-strength cold-rolled steel sheet and high-strength galvanized steel sheet
JP4613618B2 (en) High-strength cold-rolled steel sheet excellent in deep drawability and its manufacturing method
JP4415579B2 (en) Method for producing hot-dip galvanized steel sheet
JP5151227B2 (en) High strength steel plate and manufacturing method thereof
JP2017031453A (en) Alloy galvanized steel sheet and manufacturing method therefor
WO2020110795A1 (en) High-strength steel sheet and method for manufacturing same
JP5953694B2 (en) High-strength hot-dip galvanized steel sheet with excellent plating adhesion and formability and its manufacturing method
US20240011116A1 (en) Bake-hardened hot-dip galvanized steel sheet with excellent powdering resistance, and manufacturing method therefor
JP2006274288A (en) High strength hot dip galvanized steel sheet having excellent surface appearance

Legal Events

Date Code Title Description
MM4A Annulment or lapse of patent due to non-payment of fees