EP1960563A1 - High strength thin steel sheet having excellent plating and elongation property and the method for manufacturing the same - Google Patents
High strength thin steel sheet having excellent plating and elongation property and the method for manufacturing the sameInfo
- Publication number
- EP1960563A1 EP1960563A1 EP06823915A EP06823915A EP1960563A1 EP 1960563 A1 EP1960563 A1 EP 1960563A1 EP 06823915 A EP06823915 A EP 06823915A EP 06823915 A EP06823915 A EP 06823915A EP 1960563 A1 EP1960563 A1 EP 1960563A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- less
- steel sheet
- steel
- strength
- relational expression
- Prior art date
- Legal status (The legal status 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 status listed.)
- Granted
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
Definitions
- the present invention relates to a thin steel sheet which is largely used for
- the present invention relates to a thin steel sheet for deep-drawing which is capable of securing tensile strength of more than 440 MPa and has excellent plating and elongation properties, and a method for manufacturing the same.
- strength-improving elements solid solution strengthening elements such as manganese (Mn), phosphorus (P), silicon (Si) and the like
- workability-improving elements carbonitride-forming elements such as titanium (Ti), niobium (Nb), and the like
- Ti titanium
- Nb niobium
- the thin steel sheets for deep-drawing is typically manufactured using ultra-low carbon interstitial free (ULC-IF) steel in which amounts of interstitial solid solution elements such as carbon (C) and nitrogen (N) are reduced to a level of less than 50 ppm and the carbonitride-forming elements such as Ti, Nb, and the like are added alone or in any combination thereof during a steel-making process, so as to secure good formability.
- ULC-IF ultra-low carbon interstitial free
- the present invention has been made in view of the above problems, and it is an object of the present invention to provide a high-strength, thin steel sheet for deep-drawing having excellent plating and elongation properties in conjunction with high tensile strength of more than 440 MPa, by appropriate control of contents of alloying elements; and a method for manufacturing the same.
- a high-strength, thin steel sheet having excellent plating and elongation properties comprising (i) less than 0.01 wt% of carbon (C), less than 0.3 wt% of silicon (Si), 0.03-0.2 wt% of manganese (Mn), less than 0.15 wt% of phosphorus (P), 0.003-0.015 wt% of sulfur (S), 0.1-0.4 wt% of soluble aluminum (SoLAl), less than 0.01 wt% of nitrogen (N), 0.003-0.01 wt% of titanium (Ti), 0.003-0.04 wt% of niobium (Nb), 0.0002-0.002 wt% of boron (B), less than 0.05 wt% of molybdenum (Mo), 0.005-0.2 wt% of copper (Cu), 0.05-0.5 wt% of chromium (C), less than 0.01 wt% of carbon (C), less than 0.3 wt% of silicon (S
- a method for manufacturing a high-strength, thin steel sheet having excellent plating and elongation properties comprising re-heating a steel slab composed of less than 0.01 wt% of carbon (C), less than 0.3 wt% of silicon (Si), 0.03-0.2 wt% of manganese (Mn), less than 0.15 wt% of phosphorus (P), 0.003-0.015 wt% of sulfur (S), 0.1-0.4 wt% of soluble aluminum (Sol.Al), less than 0.01 wt% of nitrogen (N), 0.003-0.01 wt% of titanium (Ti), 0.003-0.04 wt% of niobium (Nb), 0.0002-0.002 wt% of boron (B), less than 0.05 wt% of molybdenum (Mo), 0.005-0.2 wt% of copper (Cu), 0.05-0.5 w
- a thin steel sheet can secure high tensile
- a surface defect-free, high-strength thin steel sheet having excellent plating properties can be provided by inhibiting migration of oxides into the steel sheet surface.
- the present invention can achieve stable deep drawability even at a
- the Sol.Al affects the formation behavior of carbonitrides such as titanium and niobium precipitates, which consequently leads to coarsening of the precipitate size, causing the development of a ⁇ 111 ⁇ texture.
- the present invention can provide a steel sheet having excellent
- Carbon (C) is an interstitial solid solution element, and inhibits the formation of a
- the carbon content is preferably limited to the range of less than 0.01 wt%.
- Si is a solid solution strengthening element. Addition of Si is advantageous for improvement of the steel strength, but leads to migration of silicon oxides on the steel surface upon annealing, thereby resulting in degradation of a plating surface properties. Therefore, it is preferred to add a smaller amount of Si. However, in order to secure the steel strength which is desired by the present invention, the silicon content is preferably limited to the range of less than 0.3 wt%.
- Manganese (Mn) is an element known to prevent hot shortness due to solid-solution sulfur (S) by precipitation of solid-solution sulfur in the steel as MnS.
- the present invention provides significant improvement of the strength and planar anisotropy by controlling the Mn content to a range of 0.03 to 0.2 wt%, such that very fine MnS can be precipitated via the elaborate control of Mn and S contents.
- the content of manganese is lower than 0.03 wt%, it is difficult to achieve the above-mentioned effects.
- the content of manganese exceeds 0.2 wt%, this may result in the high possibility of poor aging resistance, due to formation of coarse MnS precipitates. Therefore, the content of Mn is preferably limited to the range of 0.03 to 0.2 wt%.
- Phosphorus (P) is a typical solid solution strengthening element which is added to enhance the strength, in conjunction with Mn.
- Ti-Nb based component system corresponding to the subject steel of the present invention, exhibits an increase of the strength, as well as development of a ⁇ 111 ⁇ texture which is favorable for an r-value, due to grain refining and grain boundary segregation.
- the content of phosphorus (P) exceeding 0.15 wt% leads to a significant increase of embrittlement, in conjunction with a sharp decrease of an elongation ratio. Therefore, the content of P is preferably limited to the range of 0.15 wt%.
- a content of sulfur (S) is lower than 0.003 wt%, this leads to formation of small amounts of MnS, CuS, (Mn 5 Cu)S precipitates and excessive coarsening of the precipitates, which in turn are likely to deteriorate the strength and aging resistance.
- a content of sulfur (S) is higher than 0.015 wt%, this leads to an increased content of solid-solution sulfur, which consequently results in significant deterioration of the ductility and formability and may cause the risk of hot shortness. Therefore, the content of S is preferably limited to the range of 0.003 to 0.015 wt%.
- Soluble aluminum (SoLAl) 0.1-0.4 wt%
- Soluble aluminum serves to ensure stable securing of the deep drawability even at a relatively low annealing temperature, while maintaining an amount of dissolved oxygen in the steel at a sufficiently low level. That is, the SoLAl in the present invention serves to coarsen (Ti 5 Nb)C precipitates and to interfere with re- crystallization inhibitory action of phosphorus (P), thereby facilitating re- crystallization and the development of a ⁇ 111 ⁇ texture. Further, the SoLAl in the present invention affects the formation behavior of carbonitrides, e.g. Ti and Nb precipitates, which thereby leads to coarsening of the precipitates.
- N Nitrogen significantly decreases the workability of the steel, when it is present in a solid solution state. If a content of N exceeds 0.01 wt%, it is necessary to increase addition amounts of Ti and Nb for fixation thereof as the precipitates. Therefore, the content of N is preferably limited to the range of less than 0.01 wt%.
- a content of titanium (Ti) is lower than 0.003 wt%, it may be difficult to achieve effective precipitation of the residual nitrogen which is not precipitated in the form of AlN, and therefore the processed surface may be inferior due to the occurrence of the aging during steel processing.
- a content of titanium (Ti) exceeds 0.01 wt%, titanium oxides are migrated on the steel surface during a plating process, thereby resulting in poor plating surface properties. Therefore, the content of Ti is preferably limited to the range of 0.003 to 0.01 wt%.
- Nb niobium
- Mn, Si, etc. solid solution elements
- the content of Nb is preferably limited to the range of 0.003 to 0.04 wt%.
- Boron (B) is a grain boundary-strengthening element, and is a useful component which is capable of improving fatigue properties of spot welds and preventing phosphorus -induced grain boundary embrittlement. If a content of B is lower than 0.0002 wt%, it is difficult to achieve the above-mentioned effects. On the other hand, if a content of B is higher than 0.002 wt%, this leads to a sharp decrease of the workability and degradation of surface properties of the plated steel sheet. Therefore, the content of B is preferably limited to the range of 0.0002-0.002 wt%.
- Molybdenum (Mo) is an element of improving secondary work embrittlement
- Copper (Cu) serves to increase the strength of the steel sheet.
- Cu is lower than 0.005 wt%, it is difficult to achieve the steel strength which is desired by the present invention.
- a content of Cu is higher than 0.2 wt%, this leads to no significant advantage in terms of improvement of the strength due to coarsening of copper precipitates, and increased production costs. Therefore, the content of Cu is preferably limited to the range of 0.005-0.2 wt%.
- Chromium (Cr) serves as an element of improving elongation properties by precipitation of solid-solution carbon present in the steel, through the formation of chromium carbide (CrC) upon annealing of the steel.
- CrC chromium carbide
- a content of Cr is lower than 0.05 wt%, insufficient precipitation of CrC leads to deterioration of the workability.
- the content of Cr is preferably limited to the range of 0.05 to 0.5 wt%.
- Antimony (Sb) is a very important element in the present invention, and is an
- Sb improves plating properties by blocking the migration of Si and Mn oxides on the steel sheet surface upon annealing.
- Sb is primarily segregated at grain boundaries, blocks migration paths of Mn and Si oxides to thereby reduce surface defects, consequently obtaining excellent plating properties. If a content of Sb is lower than 0.02 wt%, there is substantially no blocking effect on migration paths of Mn and Si oxides. On the other hand, if a content of Sb is higher than 0.1 wt%, excessive amounts of Sb in the solid-solution state lead to deterioration of elongation properties of the steel.
- the content of Sb is preferably limited to the range of 0.02 to 0.1 wt%.
- the steel sheet of the present invention comprises MnS, CuS and (Mn 5 Cu)S precipitates, wherein more than 75% of the precipitates is MnS, CuS and (Mn 5 Cu)S precipitates having a size of less than 20 nm.
- the size of the precipitates exceeding 20 nm does not make a great contribution to securing of the strength. Further, when an amount of the precipitates having a size of less than 20 nm is lower than 75%, it is also difficult to achieve the steel strength which is desired by the present invention.
- the amount of the precipitates having a size of less than 20 nm is preferably limited to the range of more than 75%.
- N added to the steel is commonly precipitated in the form of TiN and AlN, thereby improving the workability of the steel. Therefore, if contents of Ti and Al are not sufficient, aging may take place due to solid-solution N, and the drawability may also be lowered.
- solid-solution Ti in the steel exceeds a given content, the steel may be highly susceptible to deterioration of the stretchability, upon processing and lowering of the plating properties. That is, where the value of the above relational expression is smaller than 5.2, this may lead to high susceptibility to the occurrence of the aging and causes deterioration of the drawability. On the other hand, where the value of the above relational expression is larger than 21.1, this may result in deterioration of the stretchability and plating properties. Therefore, the value of the relational expression is preferably limited to the range of 5.2 to 21.1.
- the above relational expression is an empirical formula for stable securing of the deep drawability and the stretchability. Where the value of the relational expression is lower than 1.2, this may lead to deterioration of the drawability due to incomplete scavenging of carbon in the steel. On the other hand, where the value of the relational expression exceeds 12.1, this may lead to increased production costs and significant deterioration of the stretchability due to increased contents of solid-solution Nb and Cr in the steel. Therefore, the value of the relational expression is preferably limited to the range of 1.2 to 12.1.
- the steel sheet of the present invention contains more than 75% MnS, CuS and (Mn 5 Cu)S precipitates having a size of less than 20 nm and can therefore achieve the steel strength which is desired by the present invention.
- the value of the relational expression is smaller than 6.7, there are substantially no precipitation effects, making it difficult to secure the steel strength which is desired by the present invention.
- the relational expression is preferably limited to the range of 6.7 to 14.6.
- the hot finish rolling temperature is preferably limited to the range of 88O 0 C or higher.
- the hot-rolled steel sheet is subjected to the winding at a temperature of less than 700 0 C and cold-rolling at a cold-rolling reduction ratio of less than 65%. Where the winding temperature exceeds 700 0 C, there are substantially no effects on improvements of the strength due to excessive coarsening of the precipitates.
- the winding temperature is preferably limited to the range of less than 700 0 C.
- the cold-rolling at the above-specified reduction ratio can increase an r- value which is a workability evaluation index, whereas the cold-rolling at the reduction ratio exceeding 65% leads to frequent occurrence of work troubles due to high load on the roll upon field work. Therefore, the cold-rolling reduction ratio is preferably limited to the range of less than 65%.
- the cold-rolled steel sheet is subjected to continuous annealing in a temperature range of 78O 0 C to 83O 0 C.
- the annealing temperature is lower than 78O 0 C, this may probably result in deterioration of the elongation properties.
- the annealing temperature exceeds 83O 0 C, this may lead to very high risk of problems associated with threading performance of steel strips due to high- temperature annealing during the operation, and deterioration of the plating properties due to increased feasibility in surface migration of silicon and manganese oxides. Therefore, the annealing temperature is preferably limited to the range of 78O 0 C to 83O 0 C.
- the continuously annealed steel of the present invention may be subjected to alloying treatment by a conventional method.
- the annealed steel sheets thus obtained were processed into standard test specimens according to ASTM E-8 standard. Yield strength, tensile strength, elongation, plastic anisotropy factor (r value) and planar anisotropy factor ( ⁇ r value) of the test specimens were measured using a tensile testing machine (INSTRON Model 6025).
- Inventive materials (1 to 9) manufactured according to the method of the present invention using Inventive steels (1 to 5) satisfying a steel composition range of the present invention, achieved high tensile strength of more than 440 MPa by the formation of more than 75% fine precipitates having a size of less than 20 nm, an elongation ratio of more than 34%, and a plastic anisotropy factor (r value) of more than 1.88, thus representing 2 to 3% improvements of elongation properties as compared to Comparative steels.
- Inventive steel materials of the present invention secured secondary work embrittlement resistance (DBBT) of less than -4O 0 C, and a peeling width of 4 to 5 mm, thus representing excellent plating performance as compared to Comparative steels.
- DBBT secondary work embrittlement resistance
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
Claims
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
KR1020050118741A KR100711362B1 (en) | 2005-12-07 | 2005-12-07 | High strength thin steel sheet having excellent plating and elongation property and the method for manufacturing the same |
PCT/KR2006/005208 WO2007066955A1 (en) | 2005-12-07 | 2006-12-05 | High strength thin steel sheet having excellent plating and elongation property and the method for manufacturing the same |
Publications (3)
Publication Number | Publication Date |
---|---|
EP1960563A1 true EP1960563A1 (en) | 2008-08-27 |
EP1960563A4 EP1960563A4 (en) | 2010-09-22 |
EP1960563B1 EP1960563B1 (en) | 2013-02-20 |
Family
ID=38123054
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP06823915A Expired - Fee Related EP1960563B1 (en) | 2005-12-07 | 2006-12-05 | High strength thin steel sheet having excellent plating and elongation property and the method for manufacturing the same |
Country Status (5)
Country | Link |
---|---|
EP (1) | EP1960563B1 (en) |
JP (1) | JP5097712B2 (en) |
KR (1) | KR100711362B1 (en) |
CN (1) | CN101326301B (en) |
WO (1) | WO2007066955A1 (en) |
Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH04285125A (en) * | 1991-03-13 | 1992-10-09 | Kawasaki Steel Corp | Production of cold rolled high tensile strength steel sheet for deep drawing |
JPH06158175A (en) * | 1992-11-17 | 1994-06-07 | Kobe Steel Ltd | Production of cold rolled steel sheet for ultradeep drawing |
US5853659A (en) * | 1996-02-29 | 1998-12-29 | Kawasaki Steel Corporation | Steel, steel sheet having excellent workability and method of producing the same by electric furnace-vacuum degassing process |
WO2006118423A1 (en) * | 2005-05-03 | 2006-11-09 | Posco | Cold rolled steel sheet having superior formability , process for producing the same |
Family Cites Families (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH04224653A (en) * | 1990-12-26 | 1992-08-13 | Sumitomo Metal Ind Ltd | High tensile strength steel excellent in hydrogen induced cracking resistance |
JP2653616B2 (en) * | 1992-12-04 | 1997-09-17 | 新日本製鐵株式会社 | Manufacturing method of high strength steel for large heat input welding with excellent low temperature toughness |
JP3420370B2 (en) * | 1995-03-16 | 2003-06-23 | Jfeスチール株式会社 | Thin steel sheet excellent in press formability and method for producing the same |
CA2310335C (en) * | 1998-09-29 | 2009-05-19 | Kawasaki Steel Corporation | High strength thin steel sheet, high strength galvannealed steel sheet and manufacturing method thereof |
JP3534023B2 (en) * | 1999-11-05 | 2004-06-07 | Jfeスチール株式会社 | High-strength steel sheet with excellent secondary work brittleness resistance and method for producing the same |
DE60110586T2 (en) * | 2000-05-31 | 2005-12-01 | Jfe Steel Corp. | COLD-ROLLED STEEL PLATE WITH EXCELLENT RECALTERING CHARACTERISTICS AND MANUFACTURING METHOD FOR SUCH STEEL PLATE |
CN100336930C (en) * | 2001-10-04 | 2007-09-12 | 新日本制铁株式会社 | Steel sheet for container and method of producing the same |
JP3924159B2 (en) * | 2001-11-28 | 2007-06-06 | 新日本製鐵株式会社 | High-strength thin steel sheet with excellent delayed fracture resistance after forming, its manufacturing method, and automotive strength parts made from high-strength thin steel sheet |
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 |
JP4507851B2 (en) * | 2003-12-05 | 2010-07-21 | Jfeスチール株式会社 | High-strength cold-rolled steel sheet and manufacturing method thereof |
KR101105132B1 (en) * | 2003-12-23 | 2012-01-16 | 주식회사 포스코 | Baking hardening cold rolled steel sheet having high strength, process for producing the same |
JP4506438B2 (en) * | 2004-03-31 | 2010-07-21 | Jfeスチール株式会社 | High-rigidity and high-strength steel sheet and manufacturing method thereof |
-
2005
- 2005-12-07 KR KR1020050118741A patent/KR100711362B1/en active IP Right Grant
-
2006
- 2006-12-05 EP EP06823915A patent/EP1960563B1/en not_active Expired - Fee Related
- 2006-12-05 WO PCT/KR2006/005208 patent/WO2007066955A1/en active Application Filing
- 2006-12-05 CN CN2006800463577A patent/CN101326301B/en active Active
- 2006-12-05 JP JP2008544248A patent/JP5097712B2/en active Active
Patent Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH04285125A (en) * | 1991-03-13 | 1992-10-09 | Kawasaki Steel Corp | Production of cold rolled high tensile strength steel sheet for deep drawing |
JPH06158175A (en) * | 1992-11-17 | 1994-06-07 | Kobe Steel Ltd | Production of cold rolled steel sheet for ultradeep drawing |
US5853659A (en) * | 1996-02-29 | 1998-12-29 | Kawasaki Steel Corporation | Steel, steel sheet having excellent workability and method of producing the same by electric furnace-vacuum degassing process |
WO2006118423A1 (en) * | 2005-05-03 | 2006-11-09 | Posco | Cold rolled steel sheet having superior formability , process for producing the same |
Non-Patent Citations (1)
Title |
---|
See also references of WO2007066955A1 * |
Also Published As
Publication number | Publication date |
---|---|
CN101326301A (en) | 2008-12-17 |
CN101326301B (en) | 2011-06-08 |
EP1960563B1 (en) | 2013-02-20 |
WO2007066955A1 (en) | 2007-06-14 |
EP1960563A4 (en) | 2010-09-22 |
KR100711362B1 (en) | 2007-04-27 |
JP5097712B2 (en) | 2012-12-12 |
JP2009518540A (en) | 2009-05-07 |
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