WO2003076675A1 - Tole d'acier soumise a un traitement thermique et procede de production correspondant - Google Patents
Tole d'acier soumise a un traitement thermique et procede de production correspondant Download PDFInfo
- Publication number
- WO2003076675A1 WO2003076675A1 PCT/JP2003/002300 JP0302300W WO03076675A1 WO 2003076675 A1 WO2003076675 A1 WO 2003076675A1 JP 0302300 W JP0302300 W JP 0302300W WO 03076675 A1 WO03076675 A1 WO 03076675A1
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- WO
- WIPO (PCT)
- Prior art keywords
- steel sheet
- heat treatment
- less
- steel
- mass
- Prior art date
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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
- 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
- C22C38/14—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
- 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
Definitions
- the present invention relates to a heat-treating steel sheet which can be stably increased in strength by being subjected to heat treatment after being formed by press forming or the like, and has excellent delayed fracture resistance, and a steel sheet for heat treatment. It relates to the manufacturing method.
- Background Art As steel sheets for automobiles, from the viewpoint of weight reduction for improving fuel efficiency and high strength for protecting occupants from accidents, etc., they are used in body structural members, reinforcing members, and various other mechanical structural parts. High strength steel plate is applied. However, with the increase in strength, it has become difficult to manufacture parts with complicated shapes due to reduced formability, and the frequency of brittle fractures due to hydrogen intrusion from the operating environment, so-called delayed fractures, has increased. Or other problems arise.
- a cold-rolled steel sheet or a hot-rolled steel sheet excellent in formability is formed by press forming or the like, and then heated by a high-frequency heating method or an atmospheric heating method.
- a method of increasing the strength by quenching water cooling, oil cooling, press quench, etc. is adopted.
- Several steel sheets suitable for such methods have also been developed.
- Japanese Patent Publication No. 3-2942 proposes a steel sheet for precision punching having excellent composite formability and short-time rapid heating and quenching properties.
- the steel sheet is a Cr-B added steel containing C: 0.10 to 0.19 and Mn: 0.7 to 1.5.
- Japanese Patent No. 2713382 proposes a method for manufacturing a high-strength member having excellent delayed fracture resistance.
- C 0.2 to 0.5
- ⁇ 0.5 to 1.6
- Cr 0.5 to 1.5%
- the steel is characterized by being treated with a lubricating film forming agent, then molded, quenched and tempered.
- Japanese Patent Publication No. 7-103420 proposes a method of manufacturing a member using B-added steel.
- B-added steel containing C: 0.15 to 0.40 and Mn: 0.60 to 1.50 is cold-pressed, and then heated to a quenching temperature of 850 ° C or more and less than 950 ° C, It is characterized by water quenching at a temperature of 0.35 cm-i or more and less than 1.50 cm_i.
- JP-A-5-98356 and JP-A-5-98357 propose a method for producing a Ti-B-based high-carbon thin steel sheet which is excellent in formability and toughness and has no tempering treatment.
- C 0.15 to 0.40, ⁇ & 1: 0.6 to 1.50 are used.1
- Use of 8-added steel, suppress precipitation of cementite, and secure hardenability by adding B Furthermore, it is characterized in that abnormal growth of austenite grains is suppressed by the precipitation of A1N and (TIN).
- Japanese Patent Application Laid-Open No. 6-116679 proposes a thin steel sheet suitable for manufacturing a safety part at the time of a vehicle collision by a press quench method and a method for manufacturing the component.
- This thin steel sheet is obtained by heating 11-1 «5-8 added carotenoid steel containing C: 0.20 to 0.40 and: 0.20 to 0.40 after hot rolling for ⁇ to ⁇ hours after heating and then ( It is manufactured by cooling at a cooling rate of 20 ° C / h or less to a temperature below Aci-30) ° C. After forming this thin steel sheet into a prescribed shape, it is heated to a temperature of 850 ° C or higher, and is constrained by a mold to a temperature range of 500 to 450 ° C.
- Japanese Patent Application Laid-Open No. 8-269615 states that, without impairing stretch flangeability, the surface is hardened without cracking by subjecting it to rapid heating quenching such as induction hardening after molding, and wear resistance.
- a hot-rolled steel sheet capable of imparting properties has been proposed.
- This steel plate is C: 0.18 ⁇ 0.30, Si: 0.01 ⁇ 1.0%, Mn: 0.2 ⁇ : L.5, Cr: 0.1 ⁇ 0.5, B: 0.0006 ⁇ 0.0040, and P: 0.03 by weight S: 0.02% or less, sol Al: 0.08 or less, N: 0.01 or less, the balance consisting of iron and unavoidable impurities, and having a mixed structure of ferrite and bainite.
- Japanese Patent Application Laid-Open No. L-96031 discloses that ductility is excellent before quenching, and that Methods have been proposed for efficiently producing high-carbon hot-rolled steel sheets and high-carbon cold-rolled steel sheets that can obtain the hardness and toughness of steel.
- C 0.25 to 0.65
- Mn 0.20 to 0.40
- Japanese Patent Application Laid-Open No. H10-147816 proposes a method for producing a high-carbon thin steel sheet which has excellent formability and has sufficient strength by heat treatment after forming.
- Cr-Ti-B-added steel containing 0.25 to 0.45 and Mn: 0.2 to 0.5 is hot-rolled, wound at a temperature of 550 to 600 ° C, pickled, and then placed in a hydrogen atmosphere.
- Japanese Patent Application Laid-Open No. Hei 10-251757 proposes a method for producing a high-carbon thin steel sheet having excellent formability and having sufficient strength by heat treatment after forming.
- This method involves hot rolling a Cr-Ti-B-added steel containing 0.25 to 0.45% C and also 0.2 to 0.5 Mn at a finishing temperature of (Ar3 + 20) to (Ar3 + 50) ° C.
- Japanese Patent Application Laid-Open No. H10-60522 proposes a steel sheet exhibiting excellent formability and capable of melting and rapidly solidifying by high-density energy irradiation such as laser irradiation to achieve sufficiently high strength.
- This steel sheet contains C: 0.04-0.3, Mn: 3 and below, high density energy irradiation is performed for a time that satisfies the specified formula, and bead spacing by high density energy irradiation exceeds lmm It is characterized by.
- Japanese Patent Application Laid-Open No. 2000-144319 discloses a thin steel sheet having sufficient formability that can be applied to forming of a body structural part and the like, and capable of easily achieving high strength by hardening after forming, and a method of manufacturing the same. Proposed.
- This thin steel sheet has C: 0.05 ⁇ 0.20, Mn: 0.8 ⁇ It is made of Ti-B added steel containing 2.0, and contains Ti in the range of 3.4 XN (or less).
- the thin steel sheet is prepared by hot rolling a steel slab having the above composition to form a hot-rolled coil at a winding temperature of 600 or more, or a hot-rolled coil at a winding temperature of 480 ° C or more. Manufactured by cold rolling and annealing.
- the above prior art has the following problems.
- Japanese Patent Publication No. 3-2942 is inferior in delayed fracture resistance after quenching because of its high C content, and after quenching because its Mn content is as low as 0.7-; L.5 *. Is not stable.
- Japanese Patent No. 2713382 The technology disclosed in Japanese Patent No. 2713382 is inferior in delayed fracture resistance after quenching due to its high C content, and its strength after quenching is not stable due to its low Mn content of 0.51.6. Furthermore, since tempering treatment is essential, the manufacturing cost of parts (heat treatment cost) is high. JP-B-7-103420, JP-A-5-98356, JP-A-6-116679, JP-A-8-269615, JP-A-10-96031, JP-A-10-147816, JP In any of the techniques disclosed in Japanese Patent Application Laid-Open No. Hei 10-251757, the C content is high, so the delayed fracture resistance after quenching is poor, and the strength after quenching is not stable due to the low Mn content.
- An object of the present invention is to provide a steel sheet for heat treatment, which can stably increase the strength by heat treatment after forming by press forming or the like and obtain excellent delayed fracture resistance, and a method for producing the same.
- the purpose is substantially as follows: mass: C: 0.05 to 0.09, Si: 1 or less, Mn: 1.6 to 2.4%, P: 0.02 or less, S: 0.02 or less, sol.
- A1 0.01 to 0.1
- N 0.005% or less
- B 0.0003 to 0.003
- Ti in a range that satisfies the following equation (1), the balance being Fe, and the average particle size of iron carbide precipitated in steel is as follows: Achieved by heat-treating steel plate of 2 m or less.
- the steel sheet for heat treatment according to the present invention is, for example, a steel slab having the above-mentioned components is hot-rolled into a steel sheet, and the hot-rolled steel sheet is cooled at an average cooling rate of 30 ° C / s or less. It can be manufactured by winding the steel sheet at a winding temperature of 500 ° C or more.
- MODES FOR CARRYING OUT THE INVENTION The present inventors studied a steel sheet that can be subjected to heat treatment after press forming to stably increase the strength and obtain excellent delayed fracture resistance. , And control of iron carbide was found to be effective. The details are described below.
- c is an important element for increasing the strength of the steel sheet by heat treatment, and it is necessary to add 0.05 or more in order to sufficiently increase the strength. On the other hand, if C exceeds 0.09, the delayed fracture resistance after heat treatment deteriorates. Therefore, C is set to 0.05 to 0.09.
- Si can be added at 3 ⁇ 4t. If it exceeds 1, not only does the chemical conversion property deteriorate, but also the production cost increases. Therefore, Si is set to 1 or less.
- Mn is an essential element for stably increasing the strength of the steel sheet regardless of the heat treatment conditions such as the holding temperature, the holding time, and the cooling rate in the heat treatment. If Mn is less than 1.6, the hardenability cannot be sufficiently stabilized, while if it exceeds 2.4, the press formability of the steel sheet deteriorates. Therefore, Mn is set to 1.6 to 2.4.
- P is an impurity contained in steel, and if it exceeds 0.02, the formability and Deteriorates weldability. Therefore, P is set to 0.02 or less. It is desirable to remove and reduce as much as possible in the steelmaking process, but if it is reduced more than necessary, the cost of refining increases.
- S is an impurity contained in the steel, and when it exceeds 0.02, the formability and weldability of the steel sheet are deteriorated. Therefore, S is set to 0.02 or less. It is desirable to remove and reduce as much as possible in the steelmaking process, but if it is reduced more than necessary, the cost of refining increases.
- sol.Al Al is added as a deoxidizing agent and to precipitate N as A1N. This effect is not sufficient if sol. A1 is less than 0.01, while if sol. A1 exceeds 0.1, the effect of addition becomes saturated, leading to an increase in cost. Therefore, 301.1 is set to 0.01 to 0.1.
- N is an impurity contained in steel. If it exceeds 0.005, the formability of the steel sheet is deteriorated. Therefore, N is set to 0.005 or less. It is desirable to remove and reduce as much as possible in the steelmaking process, but if it is reduced more than necessary, the cost will increase.
- Ti has the effect of precipitating N as TiN, preventing B from precipitating as BN, and exhibiting the effect of B addition.
- Ti forms a sulphide nitride prior to nitride formation during cooling after slab heating, it is necessary to use Ti at least the atomic equivalent of N and S, ie, (48 8) It is necessary to add N + (48/32) S or more.
- Ti is set to (48/14) N + (48/32) S to 2 [(48/14) N + (48/32) S]%.
- B is an element that is present as solid solution B in steel and is necessary for stably increasing the strength of the steel sheet regardless of the processing conditions such as the holding temperature, holding time or cooling rate in heat treatment. is there. If B is less than 0.0003, the effect of stably increasing the strength is not sufficient, while if it exceeds 0.003, the effect of adding B is not only saturated, but also decreases the productivity in the steel sheet manufacturing process. Therefore, B is set to 0.0003 to 0.003.
- the balance is substantially iron, and can contain other trace elements including unavoidable impurities as long as the functions and effects of the present invention are not lost.
- the average particle size of the iron carbide precipitated in the steel affects the solution of the iron carbide during heat treatment.
- iron carbide can be dissolved in austenite in a very short time, and high strength can be obtained after quenching.
- the steel sheet for heat treatment of the present invention includes a step of hot-rolling a steel slab having the above components to produce a steel sheet, and a step of cooling the steel sheet after hot rolling with an average cooling itJ of 30 ° C / s or less. And a step of winding the cooled steel sheet at a winding temperature of 500 ° C. or more.
- the reason why the steel sheet after hot rolling is cooled at an average cooling rate of 30 ° C / s or less is that if the average cooling rate exceeds 30 / s, a low-temperature transformation phase is generated and the formability of the steel sheet decreases. This is due to deterioration.
- the reason why the winding temperature is set to 500 ° C. or higher is that if the temperature is lower than 500 ° C., a low-temperature transformation phase is generated, and the formability of the steel sheet is deteriorated.
- the steel sheet for heat treatment of the present invention includes a step of hot-rolling a steel slab having the above-described components, cold rolling, and then performing recrystallization annealing to produce a steel sheet. It can also be manufactured by a method of manufacturing a steel sheet for heat treatment in which the steel sheet is cooled to 400 ° C at an average cooling rate of 30/3 or less.
- the temperature of slab heating prior to hot rolling is preferably 1200 to: L250: from the viewpoint of improving formability.
- the finishing temperature at the time of hot rolling is desirably Ar 3 to 890 ° C. from the viewpoint of making ferrite uniform and fine.
- the slab heating temperature is set to 1200 to 1250 ° C from the viewpoint of improving the formability in order to improve the formability, and to obtain a uniform and fine ferrite. Therefore, it is desirable that the finishing temperature be Ar 3 to 890. Also, for even cooling rate after hot rolling, the average cooling rate from hot rolling final pass exit side to the take-up exceeds 30/3, the lower productivity in cold rolling to produce the low temperature transformation phase is low Therefore, it is better to keep the temperature below 30 ° C / s.
- the rolling reduction is desirably 60 or more in order to obtain fine iron carbide having an average particle size of 2 m or less, which is essential for the present invention.
- annealing it is desirable to set the heating temperature to 670 720 ° C for box annealing and 690 730 ° C or 800 850 ° C for continuous annealing from the viewpoint of improving formability.
- cold-rolled steel sheet 114 was produced by performing recrystallization annealing simulating continuous annealing at 720 ° C for 2 minutes. After recrystallization annealing, the cold-rolled steel sheet was cooled to 400 ° C at an average cooling rate of 10 ° C / s, and temper rolling was performed at an elongation of 1.5. The cold-rolled steel sheets 13 and 14 were further heat-treated at 600 ° C to adjust the carbide grain size.
- JIS No. 5 bow I tension test specimens were sampled in the direction perpendicular to the rolling direction (width direction) of the cold-rolled steel sheet, and the mechanical properties were investigated.
- Heat treatment condition 1 Water quenching after holding at 1000 ° C for 5 minutes
- Heat treatment condition 2 Hold at 1000 ° C for 5 minutes, air-cool to 800 ° C, and then water quench
- Heat treatment condition 3 Water quenching after holding 900 X 5 seconds
- heat treatment condition 1 is an ideal solution treatment and quenching condition
- heat treatment condition 2 is a condition in which quenching after solution treatment is delayed
- heat treatment condition 3 is a simulation of low temperature and short time solution treatment such as induction hardening. This is the condition. It is desirable that the steel sheet for heat treatment should stably achieve high strength after quenching under any of these 13 heat treatment conditions.
- a 30 X 100 mm strip test piece was cut out from the cold-rolled steel sheet treated under heat treatment condition 1, and bent 180 ° with a radius of lOmmR. Ports were passed through both ends of the U-shaped test piece, and a spring was inserted. The bag was tightened and fixed, immersed in 0.1N hydrochloric acid, and the time until cracking was measured to examine delayed fracture.
- the criteria for excellent delayed fracture resistance is that there should be no cracking for 30 days or more (delayed fracture time exceeds 30 days).
- Table 2 shows mechanical properties, strength after quenching, and delayed fracture time.
- the steel sheets 2, 7, 11 to 13 of the present invention all have high ductility (E1) and excellent formability, have a strength after quenching of 1200 MPa or more regardless of heat treatment conditions, and have a delayed fracture time of 30 days or more. Shows good delayed fracture resistance.
- the steel sheet 1 of the comparative example has insufficient strength after quenching because the C content is lower than the range of the present invention.
- Steel sheet 3 has a delayed fracture time as short as 3 days because the C content is higher than the range of the present invention, and is inferior in delayed fracture resistance.Furthermore, since the average carbide particle size exceeds 2 m, sufficient quenching under heat treatment conditions 3 at low temperature and short time Later strength cannot be obtained.
- Steel sheet 4 has insufficient strength after quenching under heat treatment condition 2 because the amount of Mn is lower than the range of the present invention. Since the steel sheet 5 has a higher Mn content than the range of the present invention, it has low ductility and poor formability.
- Steel sheet 6 has insufficient strength after quenching under heat treatment condition 2 because the Ti content is lower than the range of the present invention.
- the steel sheet 8 has low ductility and poor formability because the Ti content is higher than the range of the present invention.
- the steel sheet 9 has insufficient strength after quenching under the heat treatment condition 2 because the B content is lower than the range of the present invention.
- Steel sheet 10 has low ductility and poor formability because the B content is higher than the range of the present invention. Since the steel sheet 14 has an average carbide particle size of more than 2 im, sufficient strength after quenching cannot be obtained under a low-temperature, short-time heat treatment condition 3.
- the steel sheets A, D, E, and F of the present invention all have high ductility and excellent formability, have a strength after quenching of 1200 MPa or more regardless of heat treatment conditions, and have a delayed fracture time of 30 days or more. It shows excellent delayed fracture resistance.
- the steel sheet B of the comparative example has a high cooling rate after hot rolling
- the steel sheet C has a low winding temperature after hot rolling
- the steel sheet B has a high cooling rate after continuous annealing. Low ductility and poor moldability.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Description
Claims
Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP03743986A EP1484423B1 (en) | 2002-03-08 | 2003-02-28 | Steel plate subjected to heat treatment and process for producing the same |
US10/505,575 US20050121119A1 (en) | 2002-03-08 | 2003-02-28 | Steel plate subjected to heat treatment and process for producing the same |
DE60306500T DE60306500T2 (de) | 2002-03-08 | 2003-02-28 | Wärmebehandelte stahlplatte und herstellungsverfahren dafür |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2002063488A JP3918589B2 (ja) | 2002-03-08 | 2002-03-08 | 熱処理用鋼板およびその製造方法 |
JP2002-63488 | 2002-03-08 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2003076675A1 true WO2003076675A1 (fr) | 2003-09-18 |
Family
ID=27800192
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2003/002300 WO2003076675A1 (fr) | 2002-03-08 | 2003-02-28 | Tole d'acier soumise a un traitement thermique et procede de production correspondant |
Country Status (5)
Country | Link |
---|---|
US (1) | US20050121119A1 (ja) |
EP (1) | EP1484423B1 (ja) |
JP (1) | JP3918589B2 (ja) |
DE (1) | DE60306500T2 (ja) |
WO (1) | WO2003076675A1 (ja) |
Families Citing this family (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB2406891B (en) * | 2003-10-07 | 2006-09-27 | Renold Plc | A transmission chain |
JP2005188638A (ja) * | 2003-12-25 | 2005-07-14 | Sanden Corp | 動力伝達装置 |
JP4959245B2 (ja) * | 2006-07-08 | 2012-06-20 | 株式会社デルタツーリング | 高強度金属部材の製造方法 |
NZ594927A (en) * | 2009-03-10 | 2013-01-25 | Nisshin Steel Co Ltd | Zinc-based alloy-plated steel material excellent in resistance to molten-metal embrittlement cracking |
KR101149728B1 (ko) * | 2009-07-21 | 2012-07-09 | 부산대학교 산학협력단 | 차량용 멤버 제작방법 |
PL2703511T3 (pl) * | 2011-04-27 | 2018-10-31 | Nippon Steel & Sumitomo Metal Corporation | Blacha stalowa cienka na elementy wytłaczane na gorąco i sposób jej wytwarzania |
CN111801436B (zh) | 2019-02-05 | 2021-10-29 | 日本制铁株式会社 | 钢构件、钢板及它们的制造方法 |
EP3922738A4 (en) | 2019-02-05 | 2022-03-23 | Nippon Steel Corporation | STEEL ELEMENT, COATED STEEL SHEET AND METHOD FOR ITS MANUFACTURE |
Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0873985A (ja) * | 1994-09-08 | 1996-03-19 | Nippon Steel Corp | 加工性および溶接性の良い高強度熱延鋼板 |
JP2000178684A (ja) * | 1998-12-11 | 2000-06-27 | Nippon Steel Corp | 熱処理硬化能に優れた薄鋼板及び高強度プレス成形体の製造方法 |
Family Cites Families (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US5294271A (en) * | 1991-06-14 | 1994-03-15 | Nisshin Steel Co., Ltd. | Heat treatment for manufacturing spring steel excellent in high-temperature relaxation resistance |
US5853903A (en) * | 1996-05-07 | 1998-12-29 | Nkk Corporation | Steel sheet for excellent panel appearance and dent resistance after panel-forming |
JP3166652B2 (ja) * | 1997-03-14 | 2001-05-14 | 住友金属工業株式会社 | 成形性にすぐれた高炭素薄鋼板の製造方法 |
JP4214330B2 (ja) * | 1998-11-17 | 2009-01-28 | 住友金属工業株式会社 | 成形性および焼入れ性にすぐれた鋼板とその製造方法 |
-
2002
- 2002-03-08 JP JP2002063488A patent/JP3918589B2/ja not_active Expired - Fee Related
-
2003
- 2003-02-28 WO PCT/JP2003/002300 patent/WO2003076675A1/ja active IP Right Grant
- 2003-02-28 EP EP03743986A patent/EP1484423B1/en not_active Expired - Lifetime
- 2003-02-28 US US10/505,575 patent/US20050121119A1/en not_active Abandoned
- 2003-02-28 DE DE60306500T patent/DE60306500T2/de not_active Expired - Fee Related
Patent Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0873985A (ja) * | 1994-09-08 | 1996-03-19 | Nippon Steel Corp | 加工性および溶接性の良い高強度熱延鋼板 |
JP2000178684A (ja) * | 1998-12-11 | 2000-06-27 | Nippon Steel Corp | 熱処理硬化能に優れた薄鋼板及び高強度プレス成形体の製造方法 |
Non-Patent Citations (1)
Title |
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See also references of EP1484423A4 * |
Also Published As
Publication number | Publication date |
---|---|
DE60306500D1 (de) | 2006-08-10 |
DE60306500T2 (de) | 2006-11-09 |
JP3918589B2 (ja) | 2007-05-23 |
US20050121119A1 (en) | 2005-06-09 |
EP1484423B1 (en) | 2006-06-28 |
EP1484423A1 (en) | 2004-12-08 |
EP1484423A4 (en) | 2005-04-06 |
JP2003268489A (ja) | 2003-09-25 |
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