WO2009099238A1 - 高強度熱延鋼板およびその製造方法 - Google Patents
高強度熱延鋼板およびその製造方法 Download PDFInfo
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- WO2009099238A1 WO2009099238A1 PCT/JP2009/052245 JP2009052245W WO2009099238A1 WO 2009099238 A1 WO2009099238 A1 WO 2009099238A1 JP 2009052245 W JP2009052245 W JP 2009052245W WO 2009099238 A1 WO2009099238 A1 WO 2009099238A1
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- 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
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- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
- C21D1/20—Isothermal quenching, e.g. bainitic hardening
-
- 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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- 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
- C22C38/02—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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- 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
- C21D2211/002—Bainite
-
- 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
- C21D2211/004—Dispersions; Precipitations
-
- 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
Definitions
- the present invention is a high-strength hot-rolled steel sheet that has a tensile strength (TS) of 540 to 780 MPa that is useful for use in automobile steel sheets and the like, and has excellent strength uniformity with small strength variation between and within the coils. And a manufacturing method thereof.
- TS tensile strength
- Patent Document 1 discloses that when hot rolling a low-Mn steel containing Nb (Mn: 0.5% or less), the sheet bar after rough rolling is temporarily coiled.
- a method for achieving uniform uniformity in the coil of a high-strength hot-rolled steel sheet is disclosed by joining it to the preceding sheet bar while rolling it back into a steel sheet and then continuously rolling it. Yes.
- Patent Document 2 proposes a high-strength hot-rolled steel sheet that is excellent in strength uniformity with small strength variation, in which very fine precipitates are uniformly dispersed by compound addition of Ti and Mo. .
- Patent Document 1 Japanese Patent Laid-Open No. 4 2 8 9 1 2 5
- Patent Document 2 Japanese Patent Application Laid-Open No. 2 00 2-3 2 2 5 4 1 Disclosure of Invention
- Patent Document 1 In the method described in Patent Document 1, there is a problem that the coil is divided again at the time of cutting. In addition, Nb addition increases costs and is economically disadvantageous. Further, although the steel sheet described in Patent Document 2 is Ti-based, expensive Mo needs to be added, resulting in an increase in cost. Furthermore, none of the patent documents considers the two-dimensional intensity uniformity in the coil plane including both the width direction and the longitudinal direction of the coil. Such fluctuations in the strength of the coil surface inevitably occur because the cooling history of the coil after scraping differs from position to position, regardless of how uniformly the scraping temperature is controlled.
- the present invention advantageously solves the above-mentioned problems, uses an inexpensive Ti-based general-purpose steel plate, has a tensile strength (TS) of 540 to 780 MPa, and has high strength uniformity with small strength variation. It aims at providing a hot-rolled copper plate and its manufacturing method.
- TS tensile strength
- the strength of the hot-rolled copper sheet was controlled by controlling the chemical composition of the steel sheet, the metal structure, and the precipitation state of Ti that contributes to precipitation strengthening.
- the present inventors have succeeded in obtaining a high-strength hot-rolled steel sheet having excellent strength uniformity with little variation, leading to the present invention.
- the gist of the high strength hot-rolled steel sheet and its manufacturing method according to the present invention which is excellent in strength uniformity with small variations in in-plane strength, is as follows.
- Component composition in mass% C 0.05 to 0.123 ⁇ 4, Si: 0.5% or less, Mn: 0.8 to 1.83 ⁇ 4, P: 0.030% or less, S: 0.00. 01% or less, A1: 0.005 to 0.1, N: 0.01% or less, Ti: 0.030 to 0.0803 ⁇ 4, the balance is Fe and inevitable impurities, the metal structure is
- the amount of Ti that exists in precipitates with nitite ferrite present in a fraction of 70% or more and less than 20 nm in size is A high-strength hot-rolled copper sheet characterized by being 50% or more of the value of Ti * calculated by equation (1).
- Ti * [Ti] -48 ⁇ 14 X [N]... (1)
- [Ti] and [N] indicate the component composition (mass%) of Ti and N of the steel sheet, respectively.
- component composition is mass% C: 0.05 to 0.12%, Si: 0.5% or less, Mn: 0.8 to 1.8%, P: 0.030% or less, S: 0 A steel slab containing 01% or less, A1: 0.005 to 0.1%, N: 0.01% or less, Ti: 0.030 to 0.080%, the balance being Fe and inevitable impurities After heating to a heating temperature of 1150 to 1300 ° C, hot finish rolling is performed at a finishing temperature of 800 to 950 ° C.
- a method for producing a high-strength hot-rolled steel sheet characterized by starting cooling at a speed, stopping cooling at a temperature of 620 ° C or lower, and subsequently scooping it at a temperature of 550 ° C or higher.
- a high strength hot rolled steel sheet with a tensile strength (TS) of 540 to 780 MPa can be used to reduce the strength variation in the coil. Stabilization of freezing, component strength, and durability performance will be achieved, and reliability during production and use of automobile parts will be improved. Furthermore, in the present invention, the above effect can be obtained without adding expensive raw materials such as Nb, so that the cost can be reduced.
- Fig. 1 is a graph showing the results of investigating the correlation between the fraction of vanitic ferrite and the tensile strength TS (MPa).
- Figure 2 shows the results of investigating the correlation between the percentage of Ti contained in precipitates with a size of less than 20 nm relative to Ti * and the tensile strength TS (MPa).
- An example of the target steel sheet is a coiled coil with a weight of 5t or more and a steel sheet width of 500mm or more.
- both the innermost and outermost windings in the longitudinal direction at the front end and the rear end in the hot-rolled state and both in the width direction are used.
- the 10mm edge is not subject to evaluation.
- the strength variation is evaluated based on the tensile strength distribution measured two-dimensionally in at least 10 divisions in the longitudinal direction and at least 5 divisions in the width direction. Further, the present invention is intended for the range where the tensile strength (TS) of the steel sheet is not less than 540 MPa and not more than 780 MPa.
- C is an important element in the present invention together with Ti described later. C forms carbides with Ti and is effective in increasing the strength of copper sheets by precipitation strengthening.
- the C content is preferably 0.05% or more, more preferably 0.06% or more.
- the C content exceeding 0.012% does not adversely affect the good stretchability of the hole, and the upper limit of the C content is set to 0.12%, preferably not more than 0.10%.
- Si has the effect of improving ductility as well as the effect of solid solution strengthening. In order to obtain the above effects, it is effective to contain Si by 0.01% or more. On the other hand, if Si is contained in excess of 0.5%, surface defects called red scale are likely to occur during hot rolling, which may deteriorate the surface appearance of the steel sheet.
- the amount is preferably 0.5% or less, more preferably 0.3% or less.
- ⁇ is effective for increasing the strength, and has the effect of lowering the transformation point and making the ferrite grain size finer.
- Mn needs to be contained in an amount of 0.8% or more, preferably 1.0% or more. To do. On the other hand, if it contains excessive Mn exceeding 1.8%, a low-temperature transformation phase is generated after hot rolling, resulting in reduced ductility and unstable TiC precipitation. The upper limit is 1.8%.
- P is an element that has a solid solution strengthening effect and also has the effect of reducing Si-induced scale defects.
- the upper limit of the P content is set to 0.030%.
- s 0.01% or less s is an impurity that causes hot cracking and also exists as an inclusion in the steel and degrades various properties of the steel sheet, so it must be reduced as much as possible. Specifically, the s content is
- Al has the effect of fixing solute N present as an impurity and improving the normal temperature aging resistance.
- the A1 content needs to be 0.005% or more.
- the content of A1 exceeding 0.1% leads to high alloy costs and is liable to induce surface defects, so the upper limit of the A1 content is set to 0.1%.
- N is an element that degrades aging resistance at room temperature, and it is an element that is preferably reduced as much as possible.
- the N content increases, the room temperature aging resistance deteriorates, and a large amount of A1 or Ti is required to fix solute N, so it is preferable to reduce it as much as possible, and the upper limit of the N content is 0.01. %.
- Ti is an important element for strengthening copper by precipitation strengthening. In the case of the present invention, it contributes to precipitation strengthening by forming carbide with C.
- the size of the precipitate is preferably less than 20 nm.
- the precipitate containing fine Ti less than 20 nm is formed by adding both Ti and C within the above range.
- these precipitates containing Ti and C are collectively referred to as Ti-based carbides.
- Ti carbides include TiC and Ti 4 C 2 S 2 ′.
- N may be included in the carbide as a composition, or may be precipitated in combination with MnS or the like.
- Ti-based carbides having a precipitate size of less than 20 nm are mainly precipitated in the vanity ferrite small. This is because the solid solubility limit of C in basic ferrite is small, so supersaturated C is This is presumably because it tends to precipitate as carbides in the ferrite. For this reason, such precipitates make the vanite ferrite even harder (higher strength), and a tensile strength (TS) of 540 MPa or more and 780 MPa or less can be obtained.
- TS tensile strength
- Ti is a preferable element for fixing solute N because Ti easily binds to solute N. In that sense, it should be 0.030% or more.
- excessive addition of Ti is not preferable because it only produces TiC, which is a coarse undissolved carbide of Ti that does not contribute to strength in the heating stage, and is uneconomical. From this point of view, the upper limit of Ti is set to 0.080%.
- the balance other than the above-described components is substantially composed of iron and inevitable impurities.
- the amount of Ti in the precipitates with a fraction containing 70% or more of the vitality squealite and the size of less than 20 nm is 50% of Ti * expressed by formula (1). more than .
- the strength of the high-strength hot-rolled copper sheet according to the present invention is obtained by superimposing the amounts of strengthening by the three strengthening mechanisms of solid solution strengthening, structure strengthening or precipitation strengthening on the base strength of the steel itself. It is determined. Of these, the base strength is the original strength of iron, and the solid solution strengthening is almost uniquely determined once the chemical composition is determined, so these two strengthening mechanisms have little to do with the strength variation in the coil. Precipitation strengthening is most closely related to strength variation, followed by structure strengthening.
- the amount of precipitation strengthening is determined by the size and dispersion of the precipitates (specifically, the precipitate interval). Since the dispersion of precipitates can be expressed by the amount and size of precipitates, the amount of strengthening by precipitation strengthening is determined once the size and amount of precipitates are determined.
- the structure strengthening is determined by the type of steel structure. The type of copper structure is determined by the temperature range that transforms from austenite. Once the chemical composition and steel structure are determined, the amount of reinforcement is determined.
- Fig. 1 shows the results of investigating the correlation between the percentage (%) and the tensile strength TS (MPa).
- the tensile strength TS tends to increase with the increase of the vinylite fraction, but the fluctuation of TS becomes smaller and stabilizes at a veinite fraction of 70% or more.
- the fraction of the vinylite ferrite can be obtained as follows.
- the corrosion appearance structure with 5% nital is magnified 1000 times with a scanning electron microscope (SEM).
- SEM scanning electron microscope
- the other forms of ferrite are distinguished from different transformation phases such as perlite and bainette. These are color-coded on the image analysis software, and the area ratio is used as the vinyl / ferrite ratio.
- the steel structure was controlled to a fractional range where the ferrite ferrite was 703 ⁇ 4 or more, and the amount of Ti contained in precipitates with a size of less than 20 nm was less than that of Ti * expressed by the following formula (1). If it is controlled to be in the range of 50% or more, the cooling history of the coil after scraping will be affected. Even if strength variations are unavoidable due to differences in the installations, it has been conceived that the resulting strength variations can be made extremely small and practically acceptable.
- [Ti] and [N] indicate the Ti and N component composition (mass%) of the steel sheet, respectively. Therefore, the requirement of the present invention, that is, the amount of Ti contained in precipitates having a structure containing a vinylite ferrite in a fraction of 70% or more and having a size of less than 20 nm is represented by the above formula (1). If it is achieved at any position of the steel sheet, the strengthening amount of the steel sheet at each position is almost the same even if the coil cooling history varies from position to position. As a result, the steel sheet can be excellent in strength uniformity with small strength variations.
- the amount of Ti contained in precipitates of size less than 20 nm can be measured by the following method.
- the sample piece is taken out of the electrolytic solution and immersed in a solution having dispersibility.
- the precipitate contained in this solution is filtered using a filter having a pore diameter of 20 nm.
- the precipitates that have passed through the filter with a pore size of 20 nm together with the filtrate are less than 20 nm in size.
- the filtrate after filtration is analyzed by selecting appropriately from inductively coupled plasma (ICP) emission spectrometry, ICP mass spectrometry, atomic absorption spectrometry, etc., and precipitates with a size of less than 20 nm Find the amount of Ti at.
- ICP inductively coupled plasma
- the composition of the steel slab used in the production method of the present invention is the same as the composition of the copper plate described above, and the reason for the limitation is also the same.
- the high-strength hot-rolled copper sheet of the present invention can be produced by using a copper slab having a composition in the above-described range as a raw material, and subjecting the raw material to a rough rolling to obtain a hot-rolled steel sheet.
- the slab heating temperature is preferably 1150 ° C or higher for hot-rolled steel sheets so that Ti-based carbides such as TiC do not dissolve in the heating stage. This is because it is preferable to avoid the Ti-based carbide from becoming insoluble since it adversely affects the tensile strength of the hot-rolled steel sheet.
- the upper limit of the slab heating temperature is preferably 1300.
- the steel slab heated under the above conditions is subjected to hot rolling for rough rolling and finish rolling.
- This The steel slab is made into a sheet bar by rough rolling.
- the conditions for rough rolling need not be specified, and may be determined according to ordinary methods. From the viewpoint of reducing the slab heating temperature and preventing troubles during hot rolling, it is preferable to use a so-called sheet bar heater that heats the sheet bar.
- the sheet bar is finish-rolled to obtain a hot-rolled steel sheet.
- the finishing temperature should be 800 or more and 950 ° C or less.
- Lubrication rolling may be performed between some or all passes of finish rolling.
- Lubrication rolling is effective from the viewpoint of uniform steel plate shape and uniform strength.
- the friction coefficient during lubrication rolling is preferably in the range of 0.10 to 0.25.
- Cooling at a cooling rate of 20 to 80 ° C / s or less within 20 seconds within 2 seconds after hot finish rolling If more than 2 seconds elapse before starting cooling after finish rolling, the runout table will become coarse. TiC and the like are likely to precipitate unevenly, which tends to cause strength variation. The same phenomenon is likely to occur when the cooling rate is below 20 ° C / s. When the cooling rate exceeds 80 / s, a hard low-temperature transformation phase is likely to be generated, which causes variation in strength. For this reason, it is preferable to cool at a cooling rate of 20 ° C./s to 80 / s within 2 seconds after hot finish rolling.
- Molten steel with the composition shown in Table 1 was melted in a converter and slab was formed by continuous forging. These steel slabs were heated to 1250 ° C and roughly rolled into sheet bars, and then hot rolled copper sheets were formed by a hot rolling process in which finish rolling under the conditions shown in Table 2 was performed.
- these hot-rolled copper sheets were pickled and subjected to temper rolling with an elongation of 0.5%, and then the edge 10 in the width direction was removed by trimming, and various properties were evaluated.
- a copper plate was taken from the position where the innermost and outermost punches were pressed at the front and rear ends of the coil, and from the dividing point where the inside was divided into 20 equal parts in the longitudinal direction.
- Tensile specimens and precipitate analysis samples were collected from these width ends and the dividing points divided into 8 in the width direction.
- Tensile test specimens were taken in the direction parallel to the rolling direction (L direction) and processed into JIS No. 5 tensile specimens. Tensile tests were performed at a crosshead speed of 10 / min in accordance with JIS Z 2241 regulations to determine the tensile strength (TS). Table 2 shows the results of investigations on the tensile properties of the obtained hot-rolled copper sheets.
- the microstructure is identified by magnifying the corrosion manifestation structure by nital with a scanning electron microscope (SEM) 5000 times for the portion of the L cross section (cross section parallel to the rolling direction) excluding the surface layer of 10%.
- SEM scanning electron microscope
- Ti was quantified in precipitates having a size of less than 20 nm by the following quantification method.
- the hot-rolled copper sheet obtained as described above is cut to an appropriate size, and about 0.2 g of current is applied in 10% AA electrolyte (10 vol% acetylacetone-lmass% tetramethylammonium chloride-methanol).
- N density 20mA was constant current electrolysis in m 2.
- the SHMP aqueous solution aqueous sodium hexametaphosphate solution (500 mg / l) (hereinafter referred to as the SHMP aqueous solution).
- the precipitate was peeled off from the sample piece and extracted into an aqueous SHMP solution.
- the SHMP aqueous solution containing the precipitate was filtered using a filter with a pore size of 20 nm, and the filtered filtrate was analyzed using an ICP emission spectrophotometer, and the absolute amount of Ti in the filtrate was measured. .
- the absolute amount of Ti was divided by the electrolytic weight to obtain the amount (mass%) of Ti contained in the precipitate having a size of less than 20 nm.
- the electrolytic weight was determined by measuring the weight of the sample after the deposit was peeled off and subtracting it from the sample weight before electrolysis.
- the amount of Ti (mass 3 ⁇ 4) contained in the precipitate of size less than 20 nm obtained above was calculated by substituting the Ti and N contents shown in Table 1 into the formula (1). To obtain the ratio (%) of the amount of Ti contained in precipitates of size less than 20 nm.
- the vitality toughlite fraction, the ratio of the amount of Ti contained in precipitates with a size of less than 20 nm to the Ti * shown in formula (1), and the tensile strength TS are:
- the value at the center of the length and the center of the width of the coil is used as a representative value.
- the steel structure conformity rate is the proportion of the 189 measured points that satisfy both requirements, including the fraction of the basic ferrite and the proportion of Ti in Ti-based precipitates with a size of less than 20 nm. It is.
- TS conformance rate is the ratio of 189 measured points that showed a value of 540 MPa or more.
- a TS is obtained by multiplying the standard deviation ⁇ by four times, using the TS of 189 points measured.
- TS has a high strength of 540 MPa or more, and strength variation (A TS) in the coil surface is as small as 50 MPa or less. A good steel sheet is obtained.
- a hot-rolled copper sheet having a tensile strength (TS) of 540 MPa or more and a small variation in strength can be stably produced at a low cost, and an industrially significant effect can be achieved.
- TS tensile strength
- the high-strength hot-rolled steel sheet of the present invention is applied to automobile parts, the amount of springback after forming in high tension and the variation in collision characteristics can be reduced, making it possible to improve the accuracy of the vehicle body design. There is an effect that it can sufficiently contribute to collision safety and weight reduction.
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Abstract
Description
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Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
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EP09707458.7A EP2243851B1 (en) | 2008-02-08 | 2009-02-04 | High-strength hot-rolled steel sheet and process for production thereof |
CN2009801045878A CN101939458B (zh) | 2008-02-08 | 2009-02-04 | 高强度热轧钢板及其制造方法 |
US12/866,513 US8696832B2 (en) | 2008-02-08 | 2009-02-04 | High-strength hot-rolled steel sheet and method for manufacturing same |
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JP2008-028453 | 2008-02-08 | ||
JP2008028453A JP5194857B2 (ja) | 2008-02-08 | 2008-02-08 | 高強度熱延鋼板およびその製造方法 |
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WO2009099238A1 true WO2009099238A1 (ja) | 2009-08-13 |
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US (1) | US8696832B2 (ja) |
EP (1) | EP2243851B1 (ja) |
JP (1) | JP5194857B2 (ja) |
KR (1) | KR101218020B1 (ja) |
CN (1) | CN101939458B (ja) |
WO (1) | WO2009099238A1 (ja) |
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JP5482204B2 (ja) * | 2010-01-05 | 2014-05-07 | Jfeスチール株式会社 | 高強度熱延鋼板およびその製造方法 |
JP5482205B2 (ja) * | 2010-01-05 | 2014-05-07 | Jfeスチール株式会社 | 高強度熱延鋼板およびその製造方法 |
JP5776398B2 (ja) * | 2011-02-24 | 2015-09-09 | Jfeスチール株式会社 | 低温靭性に優れた低降伏比高強度熱延鋼板およびその製造方法 |
JP5505572B2 (ja) * | 2012-01-06 | 2014-05-28 | Jfeスチール株式会社 | 高強度熱延鋼板およびその製造方法 |
CN104846276A (zh) * | 2015-05-11 | 2015-08-19 | 唐山钢铁集团有限责任公司 | 一种汽车结构钢及其生产方法 |
KR20190126100A (ko) * | 2017-03-31 | 2019-11-08 | 닛폰세이테츠 가부시키가이샤 | 열간 압연 강판 및 강제 단조 부품 및 그들의 제조 방법 |
CN110475889A (zh) * | 2017-03-31 | 2019-11-19 | 日本制铁株式会社 | 热轧钢板和钢制锻造部件及其制造方法 |
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JP2004027249A (ja) * | 2002-06-21 | 2004-01-29 | Sumitomo Metal Ind Ltd | 高張力熱延鋼板およびその製造方法 |
JP2007239097A (ja) * | 2006-02-10 | 2007-09-20 | Jfe Steel Kk | 高強度冷延鋼板用熱延鋼板の製造方法 |
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JPH09111355A (ja) * | 1995-10-20 | 1997-04-28 | Sumitomo Metal Ind Ltd | 耐食性と加工性に優れた高強度熱延鋼板の製造方法 |
JP3790135B2 (ja) * | 2000-07-24 | 2006-06-28 | 株式会社神戸製鋼所 | 伸びフランジ性に優れた高強度熱延鋼板およびその製造方法 |
CN1214127C (zh) * | 2000-12-07 | 2005-08-10 | 新日本制铁株式会社 | 扩孔性和延展性优良的高强度热轧钢板及其制造方法 |
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JP4692015B2 (ja) * | 2004-03-30 | 2011-06-01 | Jfeスチール株式会社 | 伸びフランジ性と疲労特性に優れた高延性熱延鋼板およびその製造方法 |
CN100519805C (zh) * | 2004-03-31 | 2009-07-29 | 杰富意钢铁株式会社 | 高刚度高强度薄钢板及其制造方法 |
JP5070732B2 (ja) * | 2005-05-30 | 2012-11-14 | Jfeスチール株式会社 | 伸び特性、伸びフランジ特性および引張疲労特性に優れた高強度熱延鋼板およびその製造方法 |
JP5040197B2 (ja) * | 2006-07-10 | 2012-10-03 | Jfeスチール株式会社 | 加工性に優れ、かつ熱処理後の強度靭性に優れた熱延薄鋼板およびその製造方法 |
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JPH0711382A (ja) * | 1993-06-28 | 1995-01-13 | Kobe Steel Ltd | 伸びフランジ性に優れた高強度熱延鋼板とその製造方法 |
JP2002322541A (ja) | 2000-10-31 | 2002-11-08 | Nkk Corp | 材質均一性に優れた高成形性高張力熱延鋼板ならびにその製造方法および加工方法 |
JP2002161340A (ja) * | 2000-11-24 | 2002-06-04 | Nippon Steel Corp | バーリング加工性と疲労特性に優れた熱延鋼板およびその製造方法 |
JP2004027249A (ja) * | 2002-06-21 | 2004-01-29 | Sumitomo Metal Ind Ltd | 高張力熱延鋼板およびその製造方法 |
JP2007239097A (ja) * | 2006-02-10 | 2007-09-20 | Jfe Steel Kk | 高強度冷延鋼板用熱延鋼板の製造方法 |
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EP2243851B1 (en) | 2017-08-02 |
US20100314010A1 (en) | 2010-12-16 |
CN101939458A (zh) | 2011-01-05 |
US8696832B2 (en) | 2014-04-15 |
KR101218020B1 (ko) | 2013-01-02 |
KR20100097748A (ko) | 2010-09-03 |
EP2243851A1 (en) | 2010-10-27 |
CN101939458B (zh) | 2013-02-06 |
EP2243851A4 (en) | 2012-04-25 |
JP5194857B2 (ja) | 2013-05-08 |
JP2009185360A (ja) | 2009-08-20 |
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