WO2005095664A1 - 高剛性高強度薄鋼板およびその製造方法 - Google Patents
高剛性高強度薄鋼板およびその製造方法 Download PDFInfo
- Publication number
- WO2005095664A1 WO2005095664A1 PCT/JP2005/006327 JP2005006327W WO2005095664A1 WO 2005095664 A1 WO2005095664 A1 WO 2005095664A1 JP 2005006327 W JP2005006327 W JP 2005006327W WO 2005095664 A1 WO2005095664 A1 WO 2005095664A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- less
- steel sheet
- phase
- strength
- modulus
- Prior art date
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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
-
- 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
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Definitions
- the present invention relates to a high-rigidity, high-strength thin steel sheet suitable mainly for an automobile body and a method for producing the same.
- the high-rigidity, high-strength thin steel sheet of the present invention is a column-shaped structural member having a rigidity sensitivity index close to 1 such as an automobile center villa, rocker, side frame, cross member, etc. It is suitable for a wide range of applications. Background art
- the stiffness of a part having the same part shape or welding condition is represented by the product of the Young's modulus of the member and the second moment of area of the part. It can be expressed as approximately proportional to ⁇ .
- ⁇ is the thickness sensitivity index
- the shape of the part Take a value of 1 to 3 depending on the condition. For example, ⁇ takes a value close to 3 when the shape is a single plate such as an automobile panel component, and ⁇ takes a value close to 1 when the shape is a column such as a structural component.
- the Young's modulus is largely controlled by the texture and increases in the direction of the closest density of atoms. Therefore, in the steel process of rolling by rolls and heat treatment, it is effective to develop (112K110) in order to develop an orientation favorable to the Young's modulus of the steel, which is a body-centered cubic lattice. Young's modulus in the direction perpendicular to the direction can be increased.
- the aggregate structure of ferrite at the hot-rolled sheet stage was changed to ⁇ 311 ⁇ 011> and ⁇ 332 ⁇ 113>, and the initial orientation was used for cold rolling and recrystallization annealing.
- a technique for increasing the Young's modulus in a direction perpendicular to the rolling direction by setting ⁇ 211 ⁇ 011> as the main orientation by performing the rolling process is disclosed.
- Patent Document 2 Nb, Mo, and B are added to low-carbon steel having a C content of 0.02 to 0.15%, and Ti and V added according to the strength, and Ar to 950 is added. By reducing the draft at 50 ° C to 50% or more, ⁇ 211 ⁇ ⁇
- Patent Document 3 Ar transformation is performed by adding Si and A1 to a low carbon steel having a C content of 0.05% or less.
- Patent Document 1 JP-A-5-255804
- Patent Document 2 JP-A-8-311541
- Patent Document 3 JP-A-953118
- Patent Document 1 controls the texture by using ultra-low carbon steel with a C content of 0.01% or less and increases the Young's modulus of the steel sheet.
- Patent Document 3 has a problem in that rolling in the ferrite region results in coarsening of crystal grains, resulting in a significant decrease in workability.
- the high Young's modulus of a steel sheet in the prior art is intended for a steel sheet having a large thickness, a hot-rolled steel sheet, or a soft steel sheet. It was difficult to achieve a high Young's modulus of a high-strength steel sheet as thin as 2.0 mm or less.
- a strengthening mechanism for increasing the tensile strength of the steel sheet to 590 MPa or more there are mainly a precipitation strengthening mechanism and a transformation structure strengthening mechanism.
- a precipitation strengthening mechanism is used as the strengthening mechanism, it is possible to increase the strength while suppressing the decrease in the Young's modulus of the steel sheet as much as possible, but this involves the following difficulties. That is, for example, if a precipitation strengthening mechanism that makes fine precipitation of carbonitrides such as Ti and Nb is used, in hot-rolled steel sheets, high strength can be achieved by making fine precipitation during winding after hot rolling. On the other hand, in cold-rolled steel sheets, coarsening of precipitates in the recrystallization annealing process after cold rolling was inevitable, and it was difficult to increase the strength by precipitation strengthening.
- the Young's modulus of the steel sheet decreases due to the strain contained in the low-temperature transformation phase such as the bainite phase or the martensite phase. There was a problem.
- An object of the present invention is to solve the above-mentioned problems and to have high tensile strength of 59 knits or more, more preferably 700 MPa or more, and a Young's modulus of 230 Gpa or more, more preferably 240 GPa or more.
- the gist configuration of the present invention is as follows.
- the structure has a ferrite phase as the main phase, a martensite phase with an area ratio of 1% or more, and a tensile strength of 590 MPa or more and a Young's modulus of 230%.
- Ti * Ti- (47.9 / 14) XN- (47.9 / 32.1) X S ⁇ 0.01
- the total rolling reduction at 950 ° C or less should be 30% or more, finish rolling at 800 to 900 ° C, winding at 650 ° C or less, pickling
- cold rolling was performed at a reduction rate of 50% or more, and then the temperature was raised from 500 ° C to l ⁇ 30 ° C / s, and the temperature was increased to 780 ⁇ 900 ° C, and A method for producing a high-rigidity, high-strength thin steel sheet, comprising performing annealing at a cooling rate up to 500 ° C at a rate of 5 ° C / s or more.
- Ti * Ti- (47.9 / 14) XN- (47.9 / 32.1) X S ⁇ 0.01
- the present invention it is possible to provide a thin steel sheet having high tensile strength of 590 MPa or more and high rigidity with a Young's modulus of 30 GPa or more.
- the low-carbon steel material to which Mn and Ti are added is subjected to hot rolling at 950 ° C or lower to promote the transformation of unrecrystallized austenite to fly,
- a low-temperature transformation phase that suppresses the decrease in Young's modulus is generated in the cooling process, and it is advantageous for improving the Young's modulus.
- By leaving a large amount of the ferrite phase it is possible to manufacture a thin steel sheet that satisfies both high strength and high Young's modulus, and this has an industrially effective effect.
- the crystal orientation of ⁇ 113 ⁇ ⁇ 110> is advantageous for improving the Young's modulus ⁇ 112 ⁇ .
- the ⁇ 112 ⁇ In addition to promoting the recrystallization of ferrite with, the non-recrystallized ferrite of ⁇ 112 ⁇ 110 ⁇ Austenite transformation can be promoted.
- the austenite phase is transformed into the fly phase at the time of cooling after soaking, the ferrite grains having the orientation of ⁇ 112 ⁇ ⁇ 110> grow to increase the Young's modulus and increase the Mn addition.
- a low-temperature transformation phase is formed, and high strength can be achieved.
- the austenite phase transformed from ferrite having the orientation of ⁇ 112 ⁇ ⁇ 110> is formed by retransformation during cooling, the low-temperature transformation phase has a low crystal transformation orientation. Can also develop ⁇ 112 ⁇ ⁇ 110>.
- the Young's modulus is increased by developing the ⁇ 112 ⁇ -110> of the ferrite phase, and the orientation of the low-temperature transformation phase, which has a large effect on the decrease of the Young's modulus, is particularly increased.
- the strength can be increased by the formation of the low-temperature transformation phase, and the decrease in the Young's modulus due to the formation of the low-temperature transformation phase can be greatly suppressed.
- FIG. 1 is a graph showing the influence of the total draft at 950 ° C. or less on the Young's modulus.
- FIG. 2 is a graph showing the influence of the final temperature of hot finish rolling on the Young's modulus.
- FIG. 3 is a diagram showing the influence of the winding temperature on the Young's modulus.
- FIG. 4 is a graph showing the effect of the rolling reduction in cold rolling on the Young's modulus.
- FIG. 5 is a graph showing the influence of the average heating rate from 500 ° C. to the soaking temperature during annealing on the Young's modulus.
- the high-rigidity, high-strength thin steel sheet of the present invention has a tensile strength of at least 59 Pa, more preferably
- the steel plate targeted by the present invention include not only cold-rolled steel sheets but also steel sheets which have been subjected to surface treatment such as alloying-based hot-dip galvanized materials and electric zinc-coated materials.
- the unit of the content of each element in the component composition of the steel sheet is a force of “% by mass” or less, and is simply indicated by “%” unless otherwise specified.
- C is an element that stabilizes austenite, and greatly contributes to high strength by enhancing hardenability and greatly promoting the formation of a low-temperature transformation phase in a cooling process during annealing after cold rolling. be able to. Further, C promotes austenite transformation of ferrite grains having an orientation of ⁇ 112 ⁇ ⁇ 110> after cold rolling from unrecrystallized ferrite during the temperature raising step in the annealing step, thereby increasing the Young's modulus. It can also contribute to daggers.
- the C content needs to be 0.02% or more, more preferably 0.05% or more, and still more preferably 0.06% or more.
- the C content is more than 0.15%, the fraction of the hard low-temperature transformation phase becomes large, and the steel becomes extremely high in strength and the addition property deteriorates.
- the content of a large amount of C suppresses recrystallization in an orientation advantageous for high Young's modulus in an annealing step after cold rolling. Further, a large amount of C causes deterioration of weldability.
- the C content needs to be 0.15% or less, and more preferably 0.10% or less.
- ⁇ Si 1.5% or less
- Si raises the Ar transformation point during hot rolling, it must be rolled at 800 to 900 ° C.
- the Si content is preferably 0.5% or less.
- Si is an element that stabilizes the fly, and promotes ferrite transformation in the cooling process after soaking in the two-phase region in the annealing process after cold rolling, and enriches C in austenite. By doing so, austenite can be stabilized and the formation of a low-temperature transformation phase can be promoted. Therefore, the strength of the steel can be increased as required, and in order to obtain such an effect, the Si content is desirably 0.2% or more.
- ⁇ is one of the important elements of the present invention.
- ⁇ has an effect of suppressing recrystallization of worked austenite during hot rolling.
- ⁇ 113 ⁇ ⁇ 110> can be developed, and the Young's modulus can be improved in the subsequent cold rolling and annealing steps.
- ⁇ which is an austenite stabilizing element, lowers the Ac transformation point during the heating process in the annealing step after cold rolling, and changes the austenite transformation from unrecrystallized ferrite.
- the orientation of the low-temperature transformation phase generated in the cooling process after soaking can be promoted to develop an orientation that is advantageous for improving the Young's modulus, and the decrease in the Young's modulus accompanying the formation of the low-temperature transformation phase can be suppressed. it can.
- Mn greatly contributes to high strength by enhancing hardenability and greatly promoting the formation of a low-temperature transformation phase. Can also The And, by acting as a solid solution strengthening strengthening element, it can also contribute to increasing the strength of steel. To obtain such an effect, the Mn content needs to be 1.0% or more, and more preferably 1.5% or more.
- the content of a large amount of Mn exceeding 3.5% excessively lowers the Ac transformation point in the temperature rising process in the annealing step after cold rolling, so that the ferrite phase in the two-phase region is re-formed.
- ferrite in the ⁇ 112 ⁇ ⁇ 110> direction which is advantageous for high Young's modulus obtained by recrystallization of the processed ferrite, cannot be developed, resulting in a decrease in Young's modulus.
- the presence of a large amount of Mn also deteriorates the weldability of the steel sheet.
- a large amount of Mn increases the deformation resistance of the steel and increases the rolling load, which causes operational difficulties. Therefore, the Mn content should be 3.5% or less.
- the content must be 0.05% or less.
- ⁇ is an element effective for increasing the strength as a solid solution strengthening element, and also has an effect of promoting the concentration of C in austenite as an element for stabilizing ferrite.
- the steel to which Si is added has an effect of suppressing the generation of red scale.
- the P content is preferably set to 0.01% or more.
- S remarkably reduces the ductility in hot, causing hot cracking and significantly deteriorating the surface properties. Furthermore, S not only contributes little to the strength, but also reduces ductility and hole-expandability by forming coarse MnS as an impurity element. These problems become significant when the S content exceeds 0.01%, so it is desirable to reduce them as much as possible. Therefore, the S content is set to 0.01% or less. Further, from the viewpoint of particularly improving the hole expanding property, the content is preferably 0.005% or less.
- A1 is an element that is useful for improving the cleanliness of steel by adding it for deoxidation of steel.
- Al is a ferrite-stabilizing element and significantly increases the Ar transformation point of steel.
- the A1 content needs to be 1.5% or less, and from this viewpoint, it is more preferable to limit the A1 content to 0.1% or less, which is more preferable when the A1 content is low.
- the ferrite-forming element A1 stabilizes austenite by promoting ferrite formation and enriching C in austenite in the cooling process after soaking in the two-phase region in the annealing step after cold rolling. As a result, the formation of a low-temperature transformation phase can be promoted. Therefore, the strength of the steel can be increased as necessary, and in order to obtain such an effect, it is desirable that the A1 content be 0.2% or more.
- ⁇ is a harmful element that causes slab cracks during hot rolling and generates surface flaws. ⁇ When the content exceeds 0.01%, slab cracks and surface flaws become noticeable. Further, ⁇ indicates that when a carbonitride forming element such as Ti or Nb is added, a coarse nitride is formed at a high temperature, and the effect of adding the carbonitride forming element is suppressed. Therefore, the N content must be 0.01% or less.
- Ti is the most important element in the present invention.
- Ti promotes ferrite transformation from unrecrystallized austenite by suppressing recrystallization of processed austenite in the finish rolling process in hot rolling, and develops ⁇ 113 ⁇ ⁇ 110>.
- the Young's modulus can be improved in the subsequent cold rolling and annealing steps.
- austenite transformation from unrecrystallized fly is promoted, and the cooling process after soaking is reduced.
- the orientation of the low-temperature transformation phase generated by the formation an orientation advantageous for improving the Young's modulus can be developed, and a decrease in the Young's modulus accompanying the generation of the low-temperature transformation phase can be suppressed.
- fine carbonitrides of Ti can also contribute to an increase in strength. In order to have such an effect, the Ti content needs to be 0.02% or more, and more preferably 0.03% or more.
- Ti * Ti- (47.9 / 14) X N- (47.9 / 32.1) X S ⁇ 0.01
- the amount of Ti * Ti (47.9 / 14) XN— (47.9 / 32.1) XS, which is the amount of Ti not fixed by the nitride and the sulphide, must be 0.01% or more, and more preferably 0.02%. Above.
- C which is not fixed as carbide
- the introduction of distortion during cold rolling becomes non-uniform, and it is advantageous for increasing the Young's modulus in annealing after cold rolling. Since recrystallization in various orientations is also suppressed, the amount of C not fixed as carbide calculated by (C (12 / 47.9) X Ti *) must be 0.05% or less.
- the C content is not fixed as carbide and the C content is as small as less than 0.01%, the C content in austenite decreases due to annealing in the two-phase region after cold rolling, and the martensitic phase after cooling. The suppression of the formation of steel makes it difficult to increase the strength of steel. Therefore, the amount of C— (12 / 47.9) ⁇ *, which is the amount of C not fixed as carbides, is set to 0.01 to 0.05%.
- the balance is substantially iron and unavoidable impurities means that those containing other trace elements are within the scope of the present invention as long as the action and effect of the present invention are not impaired. Means to be included. In order to further improve the strength, In addition to the component specifications, if necessary, one or two of Nb: 0.005 to 0.04% and V: 0.01 to 0.20%, or one or more selected from Cr, Ni, Mo, Cu and B May be added to the ingredients.
- Nb is an element that contributes to an increase in strength by forming fine carbonitrides. Further, in the finish rolling step in hot rolling, by suppressing recrystallization of processed austenite, it is an element that promotes ferrite transformation from unrecrystallized austenite and contributes to high Young's modulus. In order to have such an effect, the Nb content is preferably set to 0.005% or more. On the other hand, even if Nb is contained in excess of 0.04%, the rolling load in hot rolling and cold rolling is significantly increased, and this involves production difficulties.Therefore, the Nb content is 0.04% or less. More preferably, it is 0.01% or less.
- V 0.01 to 0.20%
- V is an element that contributes to an increase in strength by forming fine carbonitrides.
- the content of V is preferably set to 0.01% or more.
- V is contained in excess of 0.20%, the effect of increasing the strength over 0.20% is small and the alloy cost is increased.
- the content of V is preferably set to 0.01 to 0.20%.
- Nb and V form carbides, thereby reducing the amount of C not fixed as carbides. Therefore, in order to reduce the amount of C not fixed as carbides to 0.01 to 0.05%, Nb and Z or V In the case of adding soybean curd, it is necessary to make the value of C- (12 / 47.9) — ⁇ * — (12 / 92.9) X Nb— (12 / 50.9) XV to be 0.01 to 0.05%.
- Cr is an element that enhances hardenability by suppressing the formation of cementite.
- the generation of a low-temperature transformation phase is greatly promoted, which can greatly contribute to an increase in strength.
- the hot rolling process by suppressing the recrystallization of the worked austenite, the ferrite transformation from unrecrystallized austenite is promoted, and ⁇ 113 ⁇ ⁇ 110> is developed, followed by cold rolling and annealing.
- the Young's modulus can be improved in the process. In order to obtain such an effect, it is preferable to contain Cr in an amount of 0.1% or more.
- the thin steel sheet of the present invention is used as a hot-dip galvanized steel sheet, it is preferable to contain Cr at 0.5% or less because Cr oxide generated on the surface induces non-plating. .
- Ni is an element that enhances hardenability by stabilizing austenite, and greatly contributes to high strength by greatly promoting the formation of a low-temperature transformation phase in the cooling process after soaking in the annealing process. be able to. Further, Ni, which is an austenite stabilizing element, is used in an annealing process after cold rolling in a temperature increasing process in an annealing process.
- Ni suppresses the generation of surface defects. can do.
- Mo is an element that enhances hardenability by reducing the mobility of the interface.In the cooling process in the annealing process after cold rolling, the formation of a low-temperature transformation phase is greatly promoted to increase the strength. Can be greatly contributed to. Furthermore, recrystallization of the processed austenite can be suppressed, and by promoting ferrite transformation from unrecrystallized austenite, ⁇ 113 ⁇ ⁇ 110> can be developed, and the Young's modulus can be reduced in the subsequent cold rolling and annealing processes. Can be improved. In order to obtain such an effect, it is preferable to contain 0.1% or more of Mo. On the other hand, even if Mo is contained in a large amount exceeding 1.0%, the above effect is not only saturated, but also the alloy cost increases. Therefore, it is preferable to contain Mo at 1.0% or less.
- ⁇ is an element that enhances the hardenability by suppressing the transformation from the austenite phase to the ferrite phase, and greatly promotes the formation of the low-temperature transformation phase in the cooling process in the annealing process after cold rolling. , Can greatly contribute to high strength. Furthermore, it can suppress the recrystallization of worked austenite and promote the transformation of ferrite from unrecrystallized austenite to develop ⁇ 113 ⁇ ⁇ 110>. Rate can be improved. In order to obtain this effect, it is preferable to contain 0.0005% or more. On the other hand, if the content of ⁇ ⁇ ⁇ exceeds 0.0030%, the deformation resistance during hot rolling increases and the rolling load increases, which causes operational difficulties.Therefore, ⁇ is preferably contained at 0.0030% or less. .
- Cu is an element that enhances hardenability, and in the cooling process in the annealing process after cold rolling, it can greatly contribute to high strength by greatly promoting the formation of a low-temperature transformation phase. In order to obtain this effect, it is preferable to contain Cu in an amount of 0.1% or more. On the other hand, an excessive Cu content exceeding 2.0% reduces hot ductility, induces surface defects due to cracking during hot rolling, and saturates the quenching effect of Cu. Is preferably contained at 2.0% or less.
- the thin steel sheet of the present invention it is necessary to have a structure having a ferrite phase as a main phase and a martensite phase at an area ratio of 1% or more.
- the term “ferrite phase as the main phase” means that the area ratio of the ferrite phase is 50% or more.
- the ferrite phase has a small distortion, is advantageous for high Young's modulus, is excellent in ductility, and has good workability. Therefore, it is necessary that the structure be mainly composed of the ferrite phase.
- the composite phase is formed by forming the low-temperature transformation phase, which is a hard phase, in the V, the so-called second phase, which is a part other than the ferrite phase, which is the main phase. I need to do it.
- having a particularly hard martensite phase in the structure among the low-temperature transformation phases reduces the fraction of the second phase to obtain the target tensile strength level and increases the fraction of the ferrite phase. Therefore, it is advantageous because a high Young's modulus can be achieved and the processability can be further improved. Therefore, the area ratio of the martensite phase needs to be 1% or more with respect to the whole structure. Further, in order to obtain a strength of 700 MPa or more, the area ratio of the martensite phase is preferably set to 16% or more.
- the structure of the steel sheet of the present invention is preferably a structure composed of the ferrite phase and the martensite phase, but U has a bainite phase or a retained austenite phase, or has a ferrite phase such as a pearlite phase or a cementite phase.
- the area ratio of the phase other than the phase and the martensite phase is 10% or less, more preferably 5% or less. That is, the total area ratio of the ferrite phase and the martensite phase is preferably 90% or more, more preferably 95% or more.
- composition of the steel material used in the production method of the present invention is the same as the composition of the steel plate described above, the description of the reason for limiting the steel material composition is omitted.
- the thin steel sheet of the present invention is obtained by subjecting a steel material having the same composition as the above-described steel sheet to hot rolling to form a hot rolled sheet, and pickling and cooling the hot rolled sheet after pickling.
- the winding temperature after finish rolling exceeds 650 ° C, the carbonitrides of Ti become coarse, and the effect of suppressing the recrystallization of ferrite during the heating process in the annealing process after cold rolling is reduced. It becomes difficult to transform unrecrystallized ferrite into austenite. As a result, the orientation of the low-temperature transformation phase that transforms in the cooling process after soaking cannot be controlled, and the Young's modulus is greatly reduced by the low-temperature transformation phase having this distortion. Therefore, the winding temperature after finish rolling must be 650 ° C or less. If the winding temperature is too low, a large amount of a hard low-temperature transformation phase is formed, and the load in the subsequent cold rolling increases, resulting in operational difficulties. Is preferred.
- pickling is performed to remove scale formed on the surface of the steel sheet.
- the pickling may be performed according to a conventional method.
- cold rolling is performed.
- the structure after the subsequent annealing step also increases the ⁇ 112 ⁇ ⁇ 110> orientation in ferrite, and furthermore, the low-temperature transformation phase
- the Young's modulus can be increased. To obtain such an effect, the rolling reduction during cold rolling must be 50% or more.
- the heating rate in the annealing step is an important process condition in the present invention.
- the annealing process during the process of raising the temperature to the soaking temperature in the two-phase region, that is, the soaking temperature of 780 to 900 ° C, it promotes the recrystallization of ferrite having the ⁇ 112 ⁇ A part of the ferrite grains with the ⁇ 110 ⁇ orientation can reach the two-phase region in an unrecrystallized state, causing the austenitic transformation from the unrecrystallized ferrite with the ⁇ 112 ⁇ 110> orientation. Can be promoted.
- the Young's modulus can be increased by promoting the grain growth of ferrite having the orientation of ⁇ 112 ⁇ ⁇ 110>. Furthermore, when the low-temperature transformation phase is generated and the strength is increased, the austenite phase transformed from the ferrite including the ⁇ 112 ⁇ ⁇ 110> orientation is re-transformed upon cooling. ⁇ 112 ⁇ ⁇ 110> can be developed. As described above, the Young's modulus is increased by developing the ⁇ 112 ⁇ ⁇ 110> of the ferrite phase, and ⁇ 112 ⁇ ⁇ 110> is increased in the orientation of the low-temperature transformation phase, which has a great effect on the decrease of the Young's modulus.
- the temperature from 500 ° C which has a significant effect on the recrystallization behavior, has a soaking temperature of 780 to 780 ° C.
- the average heating rate up to 900 ° C should be 1-30 ° C / s.
- the soaking temperature is set to 780 to 900 ° C because if it is lower than 780 ° C, unrecrystallized yarn remains, and if it is higher than 900 ° C, it is austenitic. This is because it is difficult to generate ferrite having a ⁇ 112 ⁇ ⁇ 110> orientation which is advantageous for improving the Young's modulus.
- the soaking time does not need to be particularly limited, but is not limited to the formation of austenite. While it is preferable that the time is set to be not less than seconds, if the length is too long, the production efficiency deteriorates.
- Cooling rate up to 500 ° C after soaking 5 ° C / s or more
- the average cooling rate up to 500 ° C after soaking must be 5 ° C / s or more.
- steel having a chemical composition corresponding to the intended strength level is melted.
- the smelting method can be appropriately applied, such as a normal converter method or an electric furnace method.
- the molten steel is formed into a slab and then hot-rolled as it is or after being cooled and heated.
- hot rolling after finishing under the above-mentioned finishing conditions, winding is performed at the above-described winding temperature, and then normal pickling and cold rolling are performed.
- the annealing the temperature is raised under the above-described conditions, and the cooling after soaking can increase the cooling rate within a range in which a desired low-temperature transformation phase is obtained. Then, in the case of a cold-rolled steel sheet, it may be overaged!
- it If it is to be manufactured as a hot-dip galvanized steel sheet, it can be plated by passing it through hot-dip zinc, and furthermore, it can be alloyed When manufactured as galvannealed steel sheet, it can be reheated to a temperature of 500 ° C or higher for alloying treatment.
- steel A having the components shown in Table 1 was melted in a laboratory vacuum melting furnace, and once cooled to room temperature to produce a steel ingot (steel material).
- hot rolling, pickling, cold rolling and annealing were sequentially performed in a laboratory.
- the basic manufacturing conditions are as follows.
- the ingot is heated at 1250 ° C for 1 hour and then hot-rolled to reduce the total rolling reduction below 950 ° C, that is, to reduce the total rolling reduction below 950 ° C by 40%.
- the final rolling temperature (corresponding to the finish temperature of finish rolling) was 860 ° C, and a hot-rolled sheet having a thickness of 4.0 mm was obtained.
- the temperature reached 600 ° C it was placed in a furnace at 600 ° C, held for 1 hour, and then cooled in the furnace to simulate winding conditions (equivalent to a winding temperature of 600 ° C).
- the hot-rolled sheet obtained in this manner was pickled, cold-rolled at a rolling reduction of 60%, the sheet thickness was set to 1.6 mm, and the temperature was raised to 500 ° C at an average of 10 ° C / s. Thereafter, the temperature was further increased from 500 ° C to a soaking temperature of 820 ° C at an average of 5 ° C / s. Next, after soaking at 820 ° C for 180 seconds, cooling at an average cooling rate of 10 ° C / s up to 500 ° C, holding at 500 ° C for 80 seconds, Air cooled to warm.
- the annealed sample had a length of 10 mm X
- the mechanical property values under the basic conditions in the present experiment according to the production method of the present invention were as follows: Young's modulus E: 242 GPa, TS: 780 MPa, El: 23%, and ferrite phase fraction: 67%, The martensite phase fraction was 28%, and the steel sheet had an excellent strength-ductility balance and a high Young's modulus.
- the remainder other than the ferrite phase and the martensite phase was It was one of the knight phase, retained austenite phase, pearlite phase and cementite phase.
- the tensile strength was 730 to 820 MPa
- the ferrite phase fraction was 55 to 80%
- the martensite phase fraction was 17 to 38%
- the balance was bainite phase, retained austenite phase, It was either a pearlite phase or a cementite phase.
- FIG. 1 shows the effect of the total rolling reduction at 950 ° C. or lower on the Young's modulus.
- the Young's modulus showed an excellent value of 230 GPa or more.
- FIG. 2 shows the effect of the final temperature of hot finish rolling on the Young's modulus.
- the Young's modulus showed an excellent value of 230 GPa or higher.
- FIG. 3 shows the effect of the winding temperature on the Young's modulus.
- the winding temperature was 650 ° C. or lower as claimed in the present invention
- the Young's modulus showed an excellent value of 230 GPa or higher.
- FIG. 4 shows the effect of the rolling reduction in cold rolling on the Young's modulus.
- the rolling reduction was 50% or more as claimed in the present invention
- the Young's modulus showed an excellent value of 230 GPa or more.
- Fig. 5 shows the effect of the average heating rate from 500 ° C during annealing to 820 ° C, which is the soaking temperature, on the Young's modulus.
- the heating rate was in the range of 1 to 30 ° C / s, which is the claimed range of the present invention, the Young's modulus showed an excellent value of 230 GPa or more.
- steels B to Z and AA to AI having the components shown in Table 2 were melted in a laboratory vacuum melting furnace, and once cooled to room temperature to produce a steel ingot (steel material). Thereafter, hot rolling, pickling, cold rolling and annealing were sequentially performed in the laboratory under the conditions shown in Table 3.
- the ingot was heated at 1250 ° C for 1 hour, and then hot-rolled, and rolled at various rolling temperatures to obtain a hot-rolled sheet having a thickness of 4.0 mm. Then, after reaching the target winding temperature, it was placed in a furnace at the winding temperature, held for 1 hour, and cooled in the furnace to simulate the winding conditions.
- the hot-rolled sheet was pickled, cold-rolled at various rolling reductions, the sheet thickness was set to 0.8 to 1.6 mm, and the temperature was raised to 500 ° C at an average of 10 ° C / s.
- cooling was performed at various average cooling rates shown in Table 3 until 500 ° C, and the temperature was kept at 500 ° C for 80 seconds, and then the temperature was lowered to room temperature. Air cooled.
- Table 4 summarizes the characteristics obtained from the test survey.
- the structure other than the martensite phase and the ferrite phase was a shift from the bainite phase, the retained austenite phase, the pearlite phase, and the cementite phase.
- Nb 0.02
- V 0.05
- Cr 0.1
- Ni 0.02
- Steel type AD has a high C content of 0.16% and a high SC of 0.14%, and the ferrite phase fraction is as small as 25%, and the Young's modulus is smaller than the claimed range of the present invention.
- the Mn content is as low as 0.9%, and the TS and the Young's modulus are smaller than the claims of the present invention.
- Steel type AI has a Ti content as low as 0.01% and Ti * as low as 0.00%. The Young's modulus is smaller than the claimed range of the present invention.
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
Description
Claims
Priority Applications (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CA002546009A CA2546009A1 (en) | 2004-03-31 | 2005-03-31 | High-rigidity high-strength thin steel sheet and method for producing same |
EP05728004.2A EP1731627B1 (en) | 2004-03-31 | 2005-03-31 | High-rigidity high-strength thin steel sheet and method for producing same |
AU2005227564A AU2005227564B2 (en) | 2004-03-31 | 2005-03-31 | High-rigidity high-strength thin steel sheet and method for producing same |
US10/578,524 US20070144633A1 (en) | 2004-03-31 | 2005-03-31 | High-stiffness high-strength thin steel sheet and method for producing the same |
Applications Claiming Priority (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2004107040 | 2004-03-31 | ||
JP2004-107040 | 2004-03-31 | ||
JP2004-346620 | 2004-11-30 | ||
JP2004346620 | 2004-11-30 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2005095664A1 true WO2005095664A1 (ja) | 2005-10-13 |
Family
ID=35063806
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2005/006327 WO2005095664A1 (ja) | 2004-03-31 | 2005-03-31 | 高剛性高強度薄鋼板およびその製造方法 |
Country Status (7)
Country | Link |
---|---|
US (1) | US20070144633A1 (ja) |
EP (1) | EP1731627B1 (ja) |
KR (1) | KR100881047B1 (ja) |
AU (1) | AU2005227564B2 (ja) |
CA (1) | CA2546009A1 (ja) |
TW (1) | TW200604352A (ja) |
WO (1) | WO2005095664A1 (ja) |
Cited By (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP2088218A1 (en) * | 2006-11-07 | 2009-08-12 | Nippon Steel Corporation | High young's modulus steel plate and process for production thereof |
KR101458039B1 (ko) * | 2006-10-30 | 2014-11-03 | 티센크루프 스틸 유럽 악티엔게젤샤프트 | 복상 조직을 형성하는 강으로부터 평판형 강 제품을 제조하는 방법 |
KR101458577B1 (ko) * | 2006-10-30 | 2014-11-07 | 티센크루프 스틸 유럽 악티엔게젤샤프트 | 마르텐사이트 조직을 형성하는 강으로부터 평판형 강 제품을 제조하는 방법 |
KR101461584B1 (ko) | 2006-10-30 | 2014-11-13 | 티센크루프 스틸 유럽 악티엔게젤샤프트 | 알루미늄으로 합금화된 다상 강으로부터 평판형 강 제품을 제조하는 방법 |
KR101461583B1 (ko) * | 2006-10-30 | 2014-11-13 | 티센크루프 스틸 유럽 악티엔게젤샤프트 | 보론으로 미량 합금화된 다상 강으로부터 평판형 강 제품을 제조하는 방법 |
KR101461585B1 (ko) | 2006-10-30 | 2015-02-23 | 티센크루프 스틸 유럽 악티엔게젤샤프트 | 실리콘으로 합금화된 다상 강으로부터 평판형 강 제품을 제조하는 방법 |
US11155902B2 (en) * | 2006-09-27 | 2021-10-26 | Nucor Corporation | High strength, hot dip coated, dual phase, steel sheet and method of manufacturing same |
US11225697B2 (en) | 2014-12-19 | 2022-01-18 | Nucor Corporation | Hot rolled light-gauge martensitic steel sheet and method for making the same |
Families Citing this family (27)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US7442268B2 (en) * | 2004-11-24 | 2008-10-28 | Nucor Corporation | Method of manufacturing cold rolled dual-phase steel sheet |
US7959747B2 (en) * | 2004-11-24 | 2011-06-14 | Nucor Corporation | Method of making cold rolled dual phase steel sheet |
US8337643B2 (en) | 2004-11-24 | 2012-12-25 | Nucor Corporation | Hot rolled dual phase steel sheet |
KR101177161B1 (ko) * | 2006-06-16 | 2012-08-24 | 신닛뽄세이테쯔 카부시키카이샤 | 고강도 전자기 강판 및 그 제조 방법 |
US7608155B2 (en) * | 2006-09-27 | 2009-10-27 | Nucor Corporation | High strength, hot dip coated, dual phase, steel sheet and method of manufacturing same |
CN100435987C (zh) * | 2006-11-10 | 2008-11-26 | 广州珠江钢铁有限责任公司 | 一种基于薄板坯连铸连轧流程采用Ti微合金化工艺生产700MPa级高强耐候钢的方法 |
JP5194878B2 (ja) * | 2007-04-13 | 2013-05-08 | Jfeスチール株式会社 | 加工性および溶接性に優れる高強度溶融亜鉛めっき鋼板およびその製造方法 |
JP4445522B2 (ja) * | 2007-06-20 | 2010-04-07 | 豊田鉄工株式会社 | 車両用センターピラーの補強部材 |
JP5272548B2 (ja) * | 2007-07-11 | 2013-08-28 | Jfeスチール株式会社 | 降伏強度が低く、材質変動の小さい高強度冷延鋼板の製造方法 |
EP2028282B1 (de) * | 2007-08-15 | 2012-06-13 | ThyssenKrupp Steel Europe AG | Dualphasenstahl, Flachprodukt aus einem solchen Dualphasenstahl und Verfahren zur Herstellung eines Flachprodukts |
EP2031081B1 (de) * | 2007-08-15 | 2011-07-13 | ThyssenKrupp Steel Europe AG | Dualphasenstahl, Flachprodukt aus einem solchen Dualphasenstahl und Verfahren zur Herstellung eines Flachprodukts |
EP2209926B1 (en) * | 2007-10-10 | 2019-08-07 | Nucor Corporation | Complex metallographic structured steel and method of manufacturing same |
JP4894863B2 (ja) | 2008-02-08 | 2012-03-14 | Jfeスチール株式会社 | 加工性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法 |
JP5201625B2 (ja) | 2008-05-13 | 2013-06-05 | 株式会社日本製鋼所 | 耐高圧水素環境脆化特性に優れた高強度低合金鋼およびその製造方法 |
JP5609223B2 (ja) * | 2010-04-09 | 2014-10-22 | Jfeスチール株式会社 | 温間加工性に優れた高強度鋼板およびその製造方法 |
KR101382981B1 (ko) * | 2011-11-07 | 2014-04-09 | 주식회사 포스코 | 온간프레스 성형용 강판, 온간프레스 성형 부재 및 이들의 제조방법 |
KR101649456B1 (ko) * | 2012-07-31 | 2016-08-19 | 신닛테츠스미킨 카부시키카이샤 | 냉연 강판, 전기 아연계 도금 냉연 강판, 용융 아연 도금 냉연 강판, 합금화 용융 아연 도금 냉연 강판 및 그들의 제조 방법 |
WO2015015738A1 (ja) * | 2013-08-02 | 2015-02-05 | Jfeスチール株式会社 | 高強度高ヤング率鋼板およびその製造方法 |
US10563279B2 (en) * | 2013-08-02 | 2020-02-18 | Jfe Steel Corporation | High strength steel sheet having high Young's modulus and method for manufacturing the same |
MX2017012310A (es) * | 2015-03-27 | 2018-01-18 | Jfe Steel Corp | Lamina de acero de alta resistencia y metodo de produccion para la misma. |
BR112018011831B1 (pt) | 2015-12-15 | 2022-11-29 | Tata Steel Ijmuiden Bv | Tira de aço galvanizada por imersão a quente de alta resistência e método de produção |
JP6515292B2 (ja) * | 2016-01-29 | 2019-05-22 | Jfeスチール株式会社 | 高強度鋼板の製造方法 |
KR101726130B1 (ko) | 2016-03-08 | 2017-04-27 | 주식회사 포스코 | 성형성이 우수한 복합조직강판 및 그 제조방법 |
US11008632B2 (en) | 2016-03-31 | 2021-05-18 | Jfe Steel Corporation | Steel sheet, coated steel sheet, method for producing hot-rolled steel sheet, method for producing cold-rolled full hard steel sheet, method for producing heat-treated sheet, method for producing steel sheet, and method for producing coated steel sheet |
KR102165051B1 (ko) * | 2016-03-31 | 2020-10-13 | 제이에프이 스틸 가부시키가이샤 | 박강판 및 도금 강판, 그리고, 박강판의 제조 방법 및 도금 강판의 제조 방법 |
WO2019174730A1 (de) | 2018-03-15 | 2019-09-19 | Thyssenkrupp Steel Europe Ag | Unterfahrschutz für ein batteriegehäuse |
TWI808779B (zh) * | 2022-06-07 | 2023-07-11 | 中國鋼鐵股份有限公司 | 汽車用鋼材及其製造方法 |
Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH055156A (ja) * | 1990-08-17 | 1993-01-14 | Kawasaki Steel Corp | 成形加工用高強度鋼板とその製造方法 |
JPH11343535A (ja) * | 1998-05-29 | 1999-12-14 | Kawasaki Steel Corp | 塗装焼付硬化型高張力鋼板およびその製造方法 |
JP2000017387A (ja) * | 1998-07-02 | 2000-01-18 | Kawasaki Steel Corp | 形状維持性に優れる缶用鋼板およびその製造方法 |
JP2005120472A (ja) * | 2003-09-26 | 2005-05-12 | Jfe Steel Kk | 高強度鋼板およびその製造方法 |
Family Cites Families (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH05263191A (ja) * | 1992-01-24 | 1993-10-12 | Sumitomo Metal Ind Ltd | 板幅方向のヤング率の高い熱延鋼板およびその製造方法 |
JP3511272B2 (ja) * | 1995-05-18 | 2004-03-29 | 住友金属工業株式会社 | 高ヤング率鋼板の製造方法 |
JP3972467B2 (ja) * | 1998-06-04 | 2007-09-05 | Jfeスチール株式会社 | 加工用高張力鋼板 |
CA2372388C (en) * | 2000-04-07 | 2009-05-26 | Kawasaki Steel Corporation | Hot-rolled steel sheet, cold-rolled steel sheet and hot-dip galvanized steel sheet excellent in strain age hardening property, and manufacturing method thereof |
JP3762700B2 (ja) * | 2001-12-26 | 2006-04-05 | 新日本製鐵株式会社 | 成形性と化成処理性に優れた高強度鋼板およびその製造方法 |
JP3870840B2 (ja) * | 2002-05-23 | 2007-01-24 | Jfeスチール株式会社 | 深絞り性と伸びフランジ性に優れた複合組織型高張力冷延鋼板およびその製造方法 |
JP4506439B2 (ja) * | 2004-03-31 | 2010-07-21 | Jfeスチール株式会社 | 高剛性高強度薄鋼板およびその製造方法 |
-
2005
- 2005-03-31 CA CA002546009A patent/CA2546009A1/en not_active Abandoned
- 2005-03-31 KR KR1020067014872A patent/KR100881047B1/ko active IP Right Grant
- 2005-03-31 EP EP05728004.2A patent/EP1731627B1/en not_active Expired - Fee Related
- 2005-03-31 TW TW094110219A patent/TW200604352A/zh not_active IP Right Cessation
- 2005-03-31 US US10/578,524 patent/US20070144633A1/en not_active Abandoned
- 2005-03-31 AU AU2005227564A patent/AU2005227564B2/en not_active Ceased
- 2005-03-31 WO PCT/JP2005/006327 patent/WO2005095664A1/ja not_active Application Discontinuation
Patent Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH055156A (ja) * | 1990-08-17 | 1993-01-14 | Kawasaki Steel Corp | 成形加工用高強度鋼板とその製造方法 |
JPH11343535A (ja) * | 1998-05-29 | 1999-12-14 | Kawasaki Steel Corp | 塗装焼付硬化型高張力鋼板およびその製造方法 |
JP2000017387A (ja) * | 1998-07-02 | 2000-01-18 | Kawasaki Steel Corp | 形状維持性に優れる缶用鋼板およびその製造方法 |
JP2005120472A (ja) * | 2003-09-26 | 2005-05-12 | Jfe Steel Kk | 高強度鋼板およびその製造方法 |
Cited By (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US11155902B2 (en) * | 2006-09-27 | 2021-10-26 | Nucor Corporation | High strength, hot dip coated, dual phase, steel sheet and method of manufacturing same |
KR101458039B1 (ko) * | 2006-10-30 | 2014-11-03 | 티센크루프 스틸 유럽 악티엔게젤샤프트 | 복상 조직을 형성하는 강으로부터 평판형 강 제품을 제조하는 방법 |
KR101458577B1 (ko) * | 2006-10-30 | 2014-11-07 | 티센크루프 스틸 유럽 악티엔게젤샤프트 | 마르텐사이트 조직을 형성하는 강으로부터 평판형 강 제품을 제조하는 방법 |
KR101461584B1 (ko) | 2006-10-30 | 2014-11-13 | 티센크루프 스틸 유럽 악티엔게젤샤프트 | 알루미늄으로 합금화된 다상 강으로부터 평판형 강 제품을 제조하는 방법 |
KR101461583B1 (ko) * | 2006-10-30 | 2014-11-13 | 티센크루프 스틸 유럽 악티엔게젤샤프트 | 보론으로 미량 합금화된 다상 강으로부터 평판형 강 제품을 제조하는 방법 |
KR101461585B1 (ko) | 2006-10-30 | 2015-02-23 | 티센크루프 스틸 유럽 악티엔게젤샤프트 | 실리콘으로 합금화된 다상 강으로부터 평판형 강 제품을 제조하는 방법 |
EP2088218A1 (en) * | 2006-11-07 | 2009-08-12 | Nippon Steel Corporation | High young's modulus steel plate and process for production thereof |
EP2088218A4 (en) * | 2006-11-07 | 2013-04-03 | Nippon Steel & Sumitomo Metal Corp | STEEL PLATE WITH HIGH YOUNGSCHEM ELASTICITY MODULE AND MANUFACTURING METHOD THEREFOR |
US11225697B2 (en) | 2014-12-19 | 2022-01-18 | Nucor Corporation | Hot rolled light-gauge martensitic steel sheet and method for making the same |
Also Published As
Publication number | Publication date |
---|---|
AU2005227564B2 (en) | 2008-02-21 |
EP1731627A4 (en) | 2007-10-31 |
AU2005227564A1 (en) | 2005-10-13 |
TWI312810B (ja) | 2009-08-01 |
CA2546009A1 (en) | 2005-10-13 |
KR20060134029A (ko) | 2006-12-27 |
EP1731627A1 (en) | 2006-12-13 |
US20070144633A1 (en) | 2007-06-28 |
TW200604352A (en) | 2006-02-01 |
EP1731627B1 (en) | 2013-08-21 |
KR100881047B1 (ko) | 2009-02-05 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
WO2005095664A1 (ja) | 高剛性高強度薄鋼板およびその製造方法 | |
JP4843982B2 (ja) | 高剛性高強度薄鋼板およびその製造方法 | |
JP5157215B2 (ja) | 加工性に優れた高剛性高強度鋼板およびその製造方法 | |
JP5233142B2 (ja) | 穴拡げ性に優れた高剛性高強度鋼板およびその製造方法 | |
JP4843981B2 (ja) | 高剛性高強度薄鋼板およびその製造方法 | |
EP1731626B1 (en) | High-rigidity high-strength thin steel sheet and method for producing same | |
JP5370620B1 (ja) | 薄鋼板およびその製造方法 | |
JP2019524986A (ja) | 強度及び成形性に優れたクラッド鋼板及びその製造方法 | |
JP4506434B2 (ja) | 剛性に優れた高強度鋼板およびその製造方法 | |
JP4815974B2 (ja) | 剛性に優れた高強度冷延鋼板の製造方法 | |
JP5845837B2 (ja) | 剛性に優れた高強度薄鋼板およびその製造方法 | |
JP4506439B2 (ja) | 高剛性高強度薄鋼板およびその製造方法 | |
JP3840901B2 (ja) | 成形後の熱処理による強度上昇能に優れた冷延鋼板およびめっき鋼板ならびに冷延鋼板の製造方法 | |
JP4506438B2 (ja) | 高剛性高強度薄鋼板およびその製造方法 | |
JP2002226941A (ja) | 深絞り性に優れた複合組織型高張力冷延鋼板およびその製造方法 | |
JP3870840B2 (ja) | 深絞り性と伸びフランジ性に優れた複合組織型高張力冷延鋼板およびその製造方法 | |
JP4736617B2 (ja) | 剛性の高い高強度冷延鋼板およびその製造方法 | |
JP3945373B2 (ja) | 微細粒組織を有する疲労特性に優れた冷延鋼板の製造方法 | |
JP2013087331A (ja) | 剛性に優れた薄鋼板 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
AK | Designated states |
Kind code of ref document: A1 Designated state(s): AE AG AL AM AT AU AZ BA BB BG BR BW BY BZ CA CH CN CO CR CU CZ DE DK DM DZ EC EE EG ES FI GB GD GE GH GM HR HU ID IL IN IS KE KG KP KR KZ LC LK LR LS LT LU LV MA MD MG MK MN MW MX MZ NA NI NO NZ OM PG PH PL PT RO RU SC SD SE SG SK SL SM SY TJ TM TN TR TT TZ UA UG US UZ VC VN YU ZA ZM ZW |
|
AL | Designated countries for regional patents |
Kind code of ref document: A1 Designated state(s): GM KE LS MW MZ NA SD SL SZ TZ UG ZM ZW AM AZ BY KG KZ MD RU TJ TM AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IS IT LT LU MC NL PL PT RO SE SI SK TR BF BJ CF CG CI CM GA GN GQ GW ML MR NE SN TD TG |
|
121 | Ep: the epo has been informed by wipo that ep was designated in this application | ||
WWE | Wipo information: entry into national phase |
Ref document number: 2005227564 Country of ref document: AU |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2007144633 Country of ref document: US Ref document number: 10578524 Country of ref document: US |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2546009 Country of ref document: CA |
|
ENP | Entry into the national phase |
Ref document number: 2005227564 Country of ref document: AU Date of ref document: 20050331 Kind code of ref document: A |
|
WWP | Wipo information: published in national office |
Ref document number: 2005227564 Country of ref document: AU |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2005728004 Country of ref document: EP |
|
WWE | Wipo information: entry into national phase |
Ref document number: 1020067014872 Country of ref document: KR |
|
WWE | Wipo information: entry into national phase |
Ref document number: 200580003779.1 Country of ref document: CN |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
WWW | Wipo information: withdrawn in national office |
Country of ref document: DE |
|
WWP | Wipo information: published in national office |
Ref document number: 2005728004 Country of ref document: EP |
|
WWP | Wipo information: published in national office |
Ref document number: 1020067014872 Country of ref document: KR |
|
WWP | Wipo information: published in national office |
Ref document number: 10578524 Country of ref document: US |