WO2009035120A1 - 製缶用高強度薄鋼板及びその製造方法 - Google Patents
製缶用高強度薄鋼板及びその製造方法 Download PDFInfo
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- WO2009035120A1 WO2009035120A1 PCT/JP2008/066616 JP2008066616W WO2009035120A1 WO 2009035120 A1 WO2009035120 A1 WO 2009035120A1 JP 2008066616 W JP2008066616 W JP 2008066616W WO 2009035120 A1 WO2009035120 A1 WO 2009035120A1
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- martensite
- steel sheet
- strength
- ferrite
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
-
- 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
-
- 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
- C21D8/0236—Cold rolling
-
- 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
- C21D8/0273—Final recrystallisation annealing
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
Definitions
- the present invention relates to a high-strength steel sheet for can making used as a material for food cans and beverage cans and a method for producing the same.
- the high strength thin steel sheet means a thin steel sheet having a tensile strength of 590 M Pa or more.
- a cold-pressed steel sheet having a product thickness t of 0.1 to 0.5 mm is used as a steel sheet for can manufacturing. Since the steel plate for cans can be made thinner as the strength becomes higher, the strength as much as possible is required.
- the high-strength steel sheet for cans produced by these conventional techniques has a defect that the workability is extremely low, and it is easy to form defects in the can-making process.
- the final process is cold rolling
- this tendency is remarkable because the product consists of a cold rolled structure with low ductility.
- a method of strain relief annealing after cold rolling has also been proposed, but the steel sheet is never recrystallized, so the ductility remains the same. Therefore, these high-strength steel sheets for cans are mainly used for bending, and can be used when not much ductility is required, but cannot be used when large ductility is required.
- steel sheets for can manufacturing are required to have both strength and ductility.
- both strength and ductility are required for automotive steel sheets.
- a ferrite having excellent ductility is used. It has been proposed to achieve both ductility and strength by forming a two-phase (DP) structure consisting of a solid phase and a hard precipitated phase.
- DP two-phase
- the steel plate for food cans and beverage cans is made of high-strength steel for cans because ASTM strictly limits alloying components from the viewpoint of harmlessness to the human body. It cannot be applied to thin steel sheets.
- the crystal grains are refined by containing 1.5 ′ to 3.5% of M n. The upper limit is 0.6%, which is outside the standard.
- an object of the present invention is to solve the above-mentioned conventional problems and to provide a high-strength thin steel sheet for can making that has excellent workability and achieves both strength and ductility while clearing the regulations of AS TM. It is what.
- the upper limit values of the alloy components of steel sheets for cans according to A S TM are as follows.
- the first invention of the present invention which has been made to solve the above problems, is a high-strength steel sheet for can manufacturing having a product sheet thickness t of 0.1 to 0.5 mm, in mass%,
- a l 0.0 1 to 0.2%
- the balance is Fe and an inevitable impurity steel composition
- the steel structure is a composite structure of Ferrite ⁇ ⁇ and Martensi ⁇ mainly composed of ferrite,
- the proration rate is 5% or more and less than 30%
- the 30 T hardness is 60 or more.
- the second aspect of the present invention is that the product thickness t is 0.1 to In high-strength steel sheet for can manufacturing that is 0.5 mm,
- a l 0.0 1 to 0.2%
- the balance is Fe and the steel composition consisting of inevitable impurities, and the steel structure is a composite structure of Ferrite ⁇ ⁇ and Martensi ⁇ mainly composed of ferrite,
- the martensite fraction is 5% or more and less than 30%
- Martensite particle size d (unit: am), product sheet thickness t (mm), and martensite hardness (H v> satisfy the following formula ⁇ >, and 30 0 hardness is 60 or more It is characterized by.
- the third invention of the present invention is the mass composition in the steel composition of the first or second invention
- V 0.02% or less
- N b 0.02% or less
- One type or two or more types can be contained, and the hardenability can be improved.
- the fourth invention of the present invention is an invention of a method for producing a high-strength thin steel sheet for can making according to any one of the first to third, wherein hot finish rolling is performed at a finishing temperature Ar 3 or higher. After that, after winding at a temperature of 75 ° C. or less, cold rolling at a cold rolling rate of 80% or more, and holding at a temperature of A or more and 8700 at the following temperature for 3 minutes or less in the annealing process The temperature range from 75 0 to 4 0 0 is cooled to 3 0 0 or less as a cooling rate of 10 0 t: Z seconds or more.
- the finish temperature of hot finish rolling is Ar 3 or more and 9 20 t: or less, and from 8 5 0 in the subsequent cooling step
- the average cooling rate up to 60,000 is 20 nos or more, and the coiling temperature is 5500, which is below.
- the martensite particle size d is controlled in accordance with the product sheet thickness t, a product that achieves both strength and ductility while clearing the regulations of ASTM. A high-strength steel sheet for cans can be obtained.
- the martensite particle size d is controlled in consideration of the product sheet thickness t and the martensite hardness HV, and both strength and ductility can be achieved at a higher level.
- the hardenability is improved by adding an alloy element that promotes the precipitation of martensite, and the strength is increased by adding an alloy element that compensates for insufficient strength. Can be increased.
- the alloy components of the third invention include elements that are obstructive in the recycling process (removal It is not included.
- the product with the controlled martensite particle size d can be produced as described in the first to third inventions without repeating the cold rolling twice.
- High strength steel sheets for cans can be produced efficiently.
- Fig. 1 is a diagram that shows whether the elongation is good or not by the plate thickness and martensite grain size.
- Fig. 2 is an illustration of whether the elongation is good or not based on the ultra-fine Vickers hardness of martensite and the martensite grain size.
- the high-strength thin steel sheet for cans of the present invention is, by mass%, C: 0.04 to 0.13%, Si: more than 0.01% to 0.03%, Mn: 0. 1 to 0.6%, P: 0.02% or less, S: 0.03% or less, A1: 0.01 to 0.2%, N: 0.00 1 to 0.02 %, With the balance being Fe and an inevitable impurity, so the reason for limiting the numerical values of each component will be explained first.
- C is 0.04% or more in order to secure the necessary strength for the steel plate for cans.
- ASTM cannot be cleared when it exceeds 0.13%, C is limited to the range of 0.04 to 0.13%. More preferably, although depending on the strength level of the target steel sheet, as the C content increases, the strength of the martensite obtained tends to increase. Therefore, in order to achieve a good balance between elongation and strength, the C content Is preferably 0.04% or more and less than 0.07%. S i: 0. 0 More than 1% to 0.0 3%
- S i is an element that increases the deformation resistance in hot rolling and cold rolling, and in order to ensure strength, it is necessary to contain an amount exceeding 0.01%, and more preferably 0. 0 1 5% or more.
- the upper limit was set to 0.03% as defined by A S TM.
- M n is a useful element that prevents hot cracking due to S, suppresses the increase in strength of hot-rolled sheets, increases the strength of cold-rolled steel sheets, and further refines crystal grains. It is necessary to contain 0.1%. By containing Mn in an amount of 0.1% or more, a martensitic transformation is likely to occur in a relatively short time even with heat retention at the coiling temperature or heat history from the coiling temperature to annealing.
- the upper limit was set to 0.6 0% as defined by A S TM. More preferably, the force depending on the target strength level, M n is a solid solution strengthening element, and tends to improve the strength by increasing the addition amount. It is preferably 1% or more and less than 0.5%.
- P is an element that lowers the ductility of the steel sheet, and P has a strong tendency to segregate in the steel, resulting in embrittlement due to the prayer. Therefore, P is preferably reduced as much as possible.
- the upper limit is set to 0.02%. This upper limit is consistent with the value specified by A S TM.
- the upper limit is set to 0.0 3% It was. This upper limit is consistent with the value specified by A S TM.
- a 1 A 1: 0.0 1 to 0.2%
- a 1 is a useful element that acts as a deoxidizer, improves the cleanliness of the steel, and refines the structure. In order to obtain such an effect, it is desirable to contain 0.01% or more. The upper limit was set at 0.2% as defined by AS TM.
- N is an element that has the effect of increasing the strength (yield strength and tensile strength) of the steel sheet by solid solution strengthening and strain age hardening. To obtain this effect, 0.0 0 1% It is necessary to contain more than 0
- M o 0.05% or less
- B: 0.02% or less 0.05% or less
- All of these are components for improving the hardenability of the steel sheet and are effective in increasing the strength, but the upper limit is limited by A S T M as described above.
- the addition of these components is not essential, but it is desirable to add them appropriately when the intended strength is high. Excessive addition suppresses ferrite and leads to a decrease in ductility, so the above range is also appropriate in that sense.
- the above basic steel composition may further contain one or two kinds of Nb: 0.02% or less and Ti: 0.02% or less in mass%. it can. These are all precipitation strengthening elements and are effective in increasing the strength. The upper limits of these components are also limited by AS TM as described above. The components for improving the hardenability and the precipitation strengthening component may be used alone or in combination.
- the high-strength thin steel sheet for can manufacturing according to the present invention has the above-described steel composition, and has a product sheet thickness t force SO .1 to 0.5 mm.
- the high-strength steel sheet for cans of the present invention has a composite structure of ferritic and martensite steel mainly composed of ferrite. It is. Ferrite is an essential phase for improving the workability of steel sheets, and this is the main phase. On the other hand, martensite is an indispensable phase in the present invention in order to increase the strength of the steel sheet, and by using a two-phase structure of these ferrite and martensite, both ductility and strength are achieved.
- the martensite fraction (martensite area ratio in the structure) is preferably 5% or more and less than 30%. If the martensite is less than 5%, the strength is insufficient, and if it exceeds 30%, the ferritic fraction is relatively lowered and the workability is lowered.
- the martensite particle size d (fm) is controlled in relation to the product thickness t (mm), and in the first invention, the following formula ⁇ A> is satisfied. .
- the following formula ⁇ B> is obtained by dividing the entire formula obtained by replacing 4Zd in the formula ⁇ A> with 2400 ZHV by the martensite particle size d (m). To do.
- Figure 2 shows the results when the martensite particle size is 5% or more, and the elongation is 5% or less, and the less than 5% is rejected as X, and the result is approximated by natural logarithm. The above formula ⁇ B>.
- HV is the martensite micro Vickers hardness
- the measurement method is, for example, the hardness measured by HMV-1 AD manufactured by Shimadzu Corporation with the measurement load applied to the tissue to 10 g or less.
- HMV-1 AD manufactured by Shimadzu Corporation with the measurement load applied to the tissue to 10 g or less.
- the 30 T hardness is evaluated based on 30 T of JISZ 2 2 4 5, so if the 30 T hardness is less than 60, the strength will be insufficient when used on the body of the can. This is achieved by cooling at a cooling rate of 100 seconds or more at 100, which will be described later, or by cooling to 300,000 or below.
- the upper limit is not particularly defined, the upper limit of 30 T hardness that can be achieved by the present rapid cooling is about 90, which is regarded as the upper limit. More preferably, it is 65 to 85 from the balance of elongation and strength.
- the high-strength steel sheet for can manufacturing according to the present invention is basically manufactured through processes of hot rolling, winding, cold rolling, annealing, and rapid cooling. This reduces the crystal grain size of the hot-rolled sheet and reduces the crystal grain size by cold rolling at a high cold rolling rate of 80% or more, causing austenite transformation in the annealing process. Fine martensite is generated by appropriately controlling the quenching rate.
- hot rolling is performed at a hot finishing rolling temperature of Ar 3 or higher.
- a hot finishing rolling temperature of Ar 3 or higher In order to reduce the grain size of the cold-rolled steel sheet, it is effective to reduce the crystal grain size of the hot-rolled sheet. For this purpose, it is preferable to reduce the hot-rolling temperature as low as possible. It is preferable to do.
- the hot rolling temperature is below Ar 3 , rolling is performed in the two-phase region of Ferrite to austenite ⁇ , and coarse grains are generated on the surface layer of the hot rolled sheet, and the martensite grain size d in the subsequent process. Therefore, the hot finish rolling temperature is preferably Ar 3 or more and 9 20 or less.
- the hot-rolled steel sheet is cooled and wound, but it is preferable that the average cooling rate from 85 O t to 60 00 in the cooling process is 20 ° C. Z seconds or more. This is because the cooling rate from 850 to 600 is important for reducing the crystal grain size of the hot-rolled steel sheet. If the average cooling rate in this temperature range is slower than 20 seconds, the particle size becomes large, and subsequent refinement cannot be achieved.
- the coiling temperature is 7 5 0 or less, preferably 5 5 0 or less. If the coiling temperature is higher than this, a layered structure of ferrite and parlor cocoon is formed in the hot rolling stage, and the uniformity is impaired. is there.
- the wound steel sheet is then processed by cold rolling to a desired sheet thickness within the range of 0.1 to 0.5 mm.
- the cold rolling rate in this cold rolling is set to 80%. It is important to have a large value of% or more. If this cold rolling rate is less than 80%, the ferritic grain size during annealing will increase. As a result, the martensite cannot be reduced to a predetermined size. Since it is difficult to set the cold rolling rate to 95% or more due to the performance of the cold rolling mill, the cold rolling rate is in the range of 80 to 95%, preferably 83 to 93%. .
- the subsequent annealing and rapid cooling are important processes for obtaining a composite structure of Ferai and martensite.
- cold-rolled steel sheets are A r!
- the temperature is maintained at 870 at the following temperature for 3 minutes or less.
- Holding temperature is A r! If it is below, austenite transformation does not occur in the annealing process, so martensite cannot be produced even if it is rapidly cooled.
- the holding temperature is 870 or more, recrystallization during annealing proceeds too much, and the ferri iron becomes coarse and the martensite cannot be reduced to a predetermined size or less.
- the holding time was set to 3 minutes or less in order to suppress the progress of recrystallization.
- the temperature range from 75 ° C. to 400 ° C. is cooled to 30 ° C. or below as a cooling rate of 100 ° X nosec or more.
- the cooling rate is slower than this, martensite will not be formed.
- the temperature range for cooling at a cooling rate of 100 ° C or more from 7 50 to 4 0 0 is for the most efficient precipitation of martensite. If the temperature is lower than 7500 ° C, the growth of ferrules will progress and it will be difficult to miniaturize martensites. In addition, if rapid cooling is not performed up to 400 0 X, martensite will not be generated and the strength will be insufficient. When cooled to below 30 O: in this way, the crystal structure becomes stable, and the high strength thin steel sheet for cans of the present invention in which fine martensite grains are dispersed in the ferrite can be obtained.
- the cooling rate is arbitrary in the following temperature range at 400.
- the high-strength steel sheets for cans made in this way are the first and second steel sheets. It has the martensite particle size d described clearly, and can achieve both strength and ductility. Moreover, the alloy components satisfy AS TM and can be used with confidence as a material for food cans and beverage cans. Examples of the present invention are shown below.
- the martensi moth was identified by means of the propeller etching, and the field of view of at least 0.211 m X 0.2 / m was observed with an optical microscope of 100 000 times. Image analysis is performed across the field of view to determine the martensite fraction (the area ratio of the martensite occupying the tissue). For the martensite particle size, the equivalent circle diameter is calculated and averaged by the same measurement.
- the hardness is evaluated based on 30 T of J I S Z 2 2 4 5. If the 30 T hardness is less than 60, the strength will be insufficient when used on the body of the can as described above.
- a material test was conducted based on JI S No. 5 of JISZ 2 2 4 1, and as described above, those with an elongation of 5% or more were accepted and those with less than 5% were rejected.
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Abstract
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Priority Applications (2)
Application Number | Priority Date | Filing Date | Title |
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KR1020107001822A KR101159824B1 (ko) | 2007-09-10 | 2008-09-09 | 제관용 고강도 박강판 및 그 제조 방법 |
CN2008801062794A CN101802236B (zh) | 2007-09-10 | 2008-09-09 | 制罐用高强度薄钢板及其制造方法 |
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JP2007-233629 | 2007-09-10 | ||
JP2007233629 | 2007-09-10 |
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WO2009035120A1 true WO2009035120A1 (ja) | 2009-03-19 |
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JP (1) | JP4235247B1 (ja) |
KR (1) | KR101159824B1 (ja) |
CN (1) | CN101802236B (ja) |
WO (1) | WO2009035120A1 (ja) |
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EP2860124A4 (en) * | 2012-06-06 | 2015-08-19 | Jfe Steel Corp | Three-part tin and method for the production thereof |
US20200332383A1 (en) * | 2017-10-31 | 2020-10-22 | Jfe Steel Corporation | High-strength steel sheet and method for producing same |
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JP5794004B2 (ja) * | 2011-07-12 | 2015-10-14 | Jfeスチール株式会社 | フランジ加工性に優れる高強度缶用鋼板およびその製造方法 |
DE102011056847B4 (de) * | 2011-12-22 | 2014-04-10 | Thyssenkrupp Rasselstein Gmbh | Stahlblech zur Verwendung als Verpackungsstahl sowie Verfahren zur Herstellung eines Verpackungsstahls |
DE102011056846B4 (de) * | 2011-12-22 | 2014-05-28 | Thyssenkrupp Rasselstein Gmbh | Verfahren zur Herstellung eines Aufreißdeckels sowie Verwendung eines mit einer Schutzschicht versehenen Stahlblechs zur Herstellung eines Aufreißdeckels |
JP5974999B2 (ja) * | 2013-08-30 | 2016-08-23 | Jfeスチール株式会社 | 高強度缶用鋼板 |
TWI560280B (en) * | 2014-10-17 | 2016-12-01 | Nippon Steel & Sumitomo Metal Corp | Steel sheet for drawn-can and producing method thereof |
KR101918426B1 (ko) | 2014-11-12 | 2018-11-13 | 제이에프이 스틸 가부시키가이샤 | 캔용 강판 및 캔용 강판의 제조 방법 |
ES2866892T3 (es) | 2016-02-29 | 2021-10-20 | Jfe Steel Corp | Chapa de acero para lata y método para fabricar la misma |
CN106282809A (zh) * | 2016-08-31 | 2017-01-04 | 广西盛隆冶金有限公司 | 储罐用含镍铬钢的制造方法 |
JP7131596B2 (ja) * | 2019-12-04 | 2022-09-06 | Jfeスチール株式会社 | 高強度缶用鋼板およびその製造方法 |
KR20220127912A (ko) | 2020-02-21 | 2022-09-20 | 제이에프이 스틸 가부시키가이샤 | 강판 및 강판의 제조 방법 |
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2008
- 2008-08-28 JP JP2008219140A patent/JP4235247B1/ja active Active
- 2008-09-09 WO PCT/JP2008/066616 patent/WO2009035120A1/ja active Application Filing
- 2008-09-09 CN CN2008801062794A patent/CN101802236B/zh active Active
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EP2860124A4 (en) * | 2012-06-06 | 2015-08-19 | Jfe Steel Corp | Three-part tin and method for the production thereof |
US20200332383A1 (en) * | 2017-10-31 | 2020-10-22 | Jfe Steel Corporation | High-strength steel sheet and method for producing same |
US11913087B2 (en) * | 2017-10-31 | 2024-02-27 | Jfe Steel Corporation | High-strength steel sheet and method for producing same |
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JP2009084687A (ja) | 2009-04-23 |
KR101159824B1 (ko) | 2012-06-26 |
KR20100029132A (ko) | 2010-03-15 |
CN101802236A (zh) | 2010-08-11 |
CN101802236B (zh) | 2012-05-30 |
JP4235247B1 (ja) | 2009-03-11 |
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