CA2224813A1 - Multi-phase steel, production of rolled products and use of the steel - Google Patents
Multi-phase steel, production of rolled products and use of the steel Download PDFInfo
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- CA2224813A1 CA2224813A1 CA002224813A CA2224813A CA2224813A1 CA 2224813 A1 CA2224813 A1 CA 2224813A1 CA 002224813 A CA002224813 A CA 002224813A CA 2224813 A CA2224813 A CA 2224813A CA 2224813 A1 CA2224813 A1 CA 2224813A1
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Classifications
-
- 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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- 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
- C21D2211/001—Austenite
-
- 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
- C21D2211/005—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
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
- Laminated Bodies (AREA)
Abstract
The invention concerns a multiphase steel, a process for producing rolled products from this steel with an up to 70 vol % polygonal-ferritic structure, and its use. The steel should have high strength, good cold-working properties and improved surface quality after the final hot-working stage.
Description
WE/wa 96043 15 February 1996 Multi-pha5~ steel, production Or rolled products and ~se o~ the 8tel3l The invention concerns a ~ulti-phase steel, a process for producing rolled products from this steel with up to ~0~
by volume of polygonal-ferritic structure, as ~ell as the use of the said s~eel. The steel should be of high strength and have a good ability to be cold-reduced a~
well as have an improved surface quality after hot-forming in the last production stage.
Dual-phase steels are known which have a structure, e.g.
of up to 80~ by volume of polygonal, relatively soft, ferrite with the remainder being carbon-rich martensite.
The second phase, of lesser quantity, which is rich in carbon, is embedded in the proeutectic ferritic phase, in the shape of an island. Such a steel has good mechanical properties and a good ability to be cold-reduced.
Known steels with predominantly polygonal ferrite in the struct~re as well as martensite embedded therein, comprise (in% by mass) 0.03 to 0.12~ C, up to 0.8~ Si and 0.8 to 1.7% Mn (De 29 24 340 C2) or 0.02 to 0.2~ C, 0.05 to 2.0~ Si, 0.5 to 2~ Mn, 0.3 to 1.5~ Cr as well as up to 1~ Cu, Ni a~d Mo (~P 0 072 867 sl). Both steels are killed by aluminium and have soluble residual con~ents of less than 0.1~ Al. Silicon in these steels promotes ferrite tran~formation. In combination with manganese and if applicable chromium, perlite formation is suppressed In this way adequate enrichment of carbon in the second phase is ensured and the formation of polygonal ferrite in predomln~nt relation to the second phase is attained.
However, these known alloys have the disadvantage that during hot rolling an inhomogenous surface structure forms which becomes evident from patterns of red scaLe.
After pickling, surface unevenne~s remains. For many applications, such material i~ not saleable. So far improvement of the surface quality o~ these hot-rolled steels has not been successful. Therefore these steels are not useable for certain purposes such as cold-reduced wheel disks for motor vehicles or other products made by cold-reduction such as cold-reduced construction profile~
and similar. In addition, steels of this type with a predominant quantity of relatively soft polygonal ferrite in the structure only attain tensile strengths up to 700 N/mm2. Thus weight reduction which maintains a linear relationship to strength, is severely limited.
It is thus the object of the invention to develop a steel which at least maintains the outstanding spectrum of the mechanical properties of known steels, has greater streng~h ~han the known dual-phase steels, can be cold-reduced as well as these, but after production by hot-forming provides a better surface structure than these steels.
To meet this objective, a multi-phase steel is proposed, comprising (in% by mass) 0.12 to 0.3~ carbon 1.2 to 3.5~ manganese 1.1 to 2.2~ aluminium less than 0.2% silicon the remainder being iron, including unavoidable impurities such as phosphorus and sulphur ~ith a perlite-free structure of le~s than 70~ by volume of soft polygonal ferrite and the remainder being bainitic ferrite and more than 4~ by volu~e, preferably up to 20~ by volume, of carbon-enriched residual austenite as well as if applicable, smaller percentages of carbon-enriched martensite which contains aluminium in a quantity in% by mass of Al ~ 7.6 Cequ. - 0.36 with a carbon equivalent (Ce~.) of 0.2 ~ Ce~" -% C ~ 1/20% Mn + 1/20~6 Cr ~ l/1596 Mo ~ 0.325.
Such a steel surpasses the product Rm . A5 of known silicon-alloyed dual-phase steels and after completion of hot-forming, its surface quality is improved, as is for example required for wheel disks for motor ~ehicles, which disks are produced by cold-reducing the hot-rolled steel. In addition, the following elements up to the percentages indicated ~in% by mass) can be added to the steel by alloying:
up to 0.05~ titanium up to 0.8~ chromium up to 0.5% molybdenum up to 0.8~ copper Up to O.5~s nickel.
Such a steel, all~yed with aluminium instead of with silicon, attains a ductile yield Rm ~ As > 18~000 N/mm2 %, i.e. a ductile yield of A5 > 18,000/ Rm in ~ at a value o~
tensile strength Rm up to 900 N/mm2.
The steel according to the invention is characterised by an aluminium content of 1.1 - 2.2% which is significan~ly higher than that of known steels. Instead, according to the invention, the-silicon content is limited to le~s than 0.2~.
By contrast, known steels of this type usually require silicon contents in excess of 0.5%. The steel alloyed with aluminium, according to the invention, compri~es the multi-phase mlcrostructure with residual austenite, as described, and has excellent mechanical strength characteristics. Above all, the surface quality of the hot-formed product after the last hot-forming stage is significantly improved when compared to hitherto-known silicon-alloy steels. There is a more pronounced delay in perlite formation, when compared with known steels:
perlite formation can be safely avoided by observing the claimed process parameters.
At 0.12 to 0.3~, the carbon content is in the usual range for steels of this type.
In order to a~oid perlite ~ormation, manganese is added in percentages of 1.2 to 3.5~. ~anganese has a solid solution hardening effect and increases the level of strength. In view of perlite avoidance and the effect on ferrite formation, carbon content and manganese content are exchangeable within the limits of the carbon equivalent. ~he carbon equivalent i5 determin~d ;~35 follows:
O . 2 ~ Ce~ =% C + 1/20~- Mn ~ 1~20~ Cr + 1/15~ Mo ' O . 325 .
According to the invention, the intersection of ~he caxbon-equivalent value and the matching aluminium value is to be within the shaded area shown in Fig. 1 in order to ensure a ferrite content below 70~ by volume and a residual austenite content exceeding 4% by volume.
Addition of titanium up to 0.05% ensures nitrogen setting and avoids the formation of elongated manganese sulphides.
Up to 0.8~ by mass of chromium can be added to improve martensite tempering properties and to avoid perlite formation.
Molybdenum, up to 0.5~ by mass increases the range of successful cooling rates.
Copper and nickel, up to 0.5~ by mass each, can contribute to lowering the transformation temperature and to avoiding perlite.
In order to influence coalescence o~ sulphides, treatment of the molten bath with calcium-silicon is advantageous.
The hot-rolling end-temperature ~T should be in the range of Ar3 - 50~C < ET < Ar3 + 100~C.
The Ar3 temperature which should be in the range of 750 to 950~C is calculated as follows 750~C ' Ar3 = 900 ~ 100~ Al - 60~ Mn - 300~ c ~ 950~C
Cooling down from hot-roll end-temperature to reeling temperature which i~ bet~een 200 and 500~C takes place in an accelerated way at a cooling-down speed of 15 to 70 E~/s .
Whe~ cooling down from the hot-roll end-temperature, in the process according to the invention, it is possible in the range of A~3 to Ar3 - 200~C, to further improve the formation of polygonal ferrite by observing a cooling pause of 2 to 30 s, during which the cooling rate is ~elow 15 K/s.
Fig. 2 shows a diagrammatic representation of hot-strip production coupled with the cooling progression of the steel according to the invention, at and after hot-rolling.
It shows that any undesired entering of the perlite region can safely be avoided if the conditions stated for the hot-roll end-temperature, the cooling-down speed and the reeling temperature, are observed.
A steel A according to the invention, with a ccmposi~ion according to Table 1 was hot rolled to a final strip thickness of 3.7 mm at a hot-roll end-temperature of 855~C.
Cooling from this temperature was at 30 K/s to the reel tempera~ure (RT) of 415~C. The characteristics of this steel A according to the in~ention were determined according to DIN EN 10002 on flat-drawn specimens.
Table 2 shows the values for the apparent yield point, tensile strength, elongation and the ratio of yield point to tensile strength for the layers along and across the ~ire~t.ion of ro.l.llng.
By way o~ comparison, Table 2 also shows the respective strength properties of a steel B, known from EP O 586 704 Al, with a composition as shown in Table 1.
Due to its spectrum of characteristics, the steel according to the invention is particularly suitable for the production of cold-reduced structural elements for motor ~ehicles, such as floor stiffener elements, transverse links, or for wheel disks.
Table 1 C~ Mn~ Si~ Cu-~O Ni9~ Cr~ P~ S% N%
A 0, 21G 1,3~ 1, B3 0, 06 0, 5 1 0,27 0,52 0,010 cO, 001 0,OOZ4 0,21 1,50 0,057 1,'16 <0,01 0,01 0,02 ~0,005 0,004 0,006 r '~ * ~ccording to EP O 586 704 A1 -~ CA 02224813 1997-12-16 . ~ O ~D
,~
r r m r ~ L~
O C) O C) L') L') ~ O
E L') C::~ O D
E E ~c~ o a L') ~o~ ~ ~ ,~ c~
~ ~ r r ~ ~ -Q O
- E L')~D ~ r E E ~ N
r r r ~ L~
o ~ _ o r o -- ~ILr) r z ~D L') C~
U~
~ O
O O
0:
~) ~I L'l ,_, o ~
L" O
E~ C~ L~ ~D
~:~ C CD C~
a~ ~ m U~
by volume of polygonal-ferritic structure, as ~ell as the use of the said s~eel. The steel should be of high strength and have a good ability to be cold-reduced a~
well as have an improved surface quality after hot-forming in the last production stage.
Dual-phase steels are known which have a structure, e.g.
of up to 80~ by volume of polygonal, relatively soft, ferrite with the remainder being carbon-rich martensite.
The second phase, of lesser quantity, which is rich in carbon, is embedded in the proeutectic ferritic phase, in the shape of an island. Such a steel has good mechanical properties and a good ability to be cold-reduced.
Known steels with predominantly polygonal ferrite in the struct~re as well as martensite embedded therein, comprise (in% by mass) 0.03 to 0.12~ C, up to 0.8~ Si and 0.8 to 1.7% Mn (De 29 24 340 C2) or 0.02 to 0.2~ C, 0.05 to 2.0~ Si, 0.5 to 2~ Mn, 0.3 to 1.5~ Cr as well as up to 1~ Cu, Ni a~d Mo (~P 0 072 867 sl). Both steels are killed by aluminium and have soluble residual con~ents of less than 0.1~ Al. Silicon in these steels promotes ferrite tran~formation. In combination with manganese and if applicable chromium, perlite formation is suppressed In this way adequate enrichment of carbon in the second phase is ensured and the formation of polygonal ferrite in predomln~nt relation to the second phase is attained.
However, these known alloys have the disadvantage that during hot rolling an inhomogenous surface structure forms which becomes evident from patterns of red scaLe.
After pickling, surface unevenne~s remains. For many applications, such material i~ not saleable. So far improvement of the surface quality o~ these hot-rolled steels has not been successful. Therefore these steels are not useable for certain purposes such as cold-reduced wheel disks for motor vehicles or other products made by cold-reduction such as cold-reduced construction profile~
and similar. In addition, steels of this type with a predominant quantity of relatively soft polygonal ferrite in the structure only attain tensile strengths up to 700 N/mm2. Thus weight reduction which maintains a linear relationship to strength, is severely limited.
It is thus the object of the invention to develop a steel which at least maintains the outstanding spectrum of the mechanical properties of known steels, has greater streng~h ~han the known dual-phase steels, can be cold-reduced as well as these, but after production by hot-forming provides a better surface structure than these steels.
To meet this objective, a multi-phase steel is proposed, comprising (in% by mass) 0.12 to 0.3~ carbon 1.2 to 3.5~ manganese 1.1 to 2.2~ aluminium less than 0.2% silicon the remainder being iron, including unavoidable impurities such as phosphorus and sulphur ~ith a perlite-free structure of le~s than 70~ by volume of soft polygonal ferrite and the remainder being bainitic ferrite and more than 4~ by volu~e, preferably up to 20~ by volume, of carbon-enriched residual austenite as well as if applicable, smaller percentages of carbon-enriched martensite which contains aluminium in a quantity in% by mass of Al ~ 7.6 Cequ. - 0.36 with a carbon equivalent (Ce~.) of 0.2 ~ Ce~" -% C ~ 1/20% Mn + 1/20~6 Cr ~ l/1596 Mo ~ 0.325.
Such a steel surpasses the product Rm . A5 of known silicon-alloyed dual-phase steels and after completion of hot-forming, its surface quality is improved, as is for example required for wheel disks for motor ~ehicles, which disks are produced by cold-reducing the hot-rolled steel. In addition, the following elements up to the percentages indicated ~in% by mass) can be added to the steel by alloying:
up to 0.05~ titanium up to 0.8~ chromium up to 0.5% molybdenum up to 0.8~ copper Up to O.5~s nickel.
Such a steel, all~yed with aluminium instead of with silicon, attains a ductile yield Rm ~ As > 18~000 N/mm2 %, i.e. a ductile yield of A5 > 18,000/ Rm in ~ at a value o~
tensile strength Rm up to 900 N/mm2.
The steel according to the invention is characterised by an aluminium content of 1.1 - 2.2% which is significan~ly higher than that of known steels. Instead, according to the invention, the-silicon content is limited to le~s than 0.2~.
By contrast, known steels of this type usually require silicon contents in excess of 0.5%. The steel alloyed with aluminium, according to the invention, compri~es the multi-phase mlcrostructure with residual austenite, as described, and has excellent mechanical strength characteristics. Above all, the surface quality of the hot-formed product after the last hot-forming stage is significantly improved when compared to hitherto-known silicon-alloy steels. There is a more pronounced delay in perlite formation, when compared with known steels:
perlite formation can be safely avoided by observing the claimed process parameters.
At 0.12 to 0.3~, the carbon content is in the usual range for steels of this type.
In order to a~oid perlite ~ormation, manganese is added in percentages of 1.2 to 3.5~. ~anganese has a solid solution hardening effect and increases the level of strength. In view of perlite avoidance and the effect on ferrite formation, carbon content and manganese content are exchangeable within the limits of the carbon equivalent. ~he carbon equivalent i5 determin~d ;~35 follows:
O . 2 ~ Ce~ =% C + 1/20~- Mn ~ 1~20~ Cr + 1/15~ Mo ' O . 325 .
According to the invention, the intersection of ~he caxbon-equivalent value and the matching aluminium value is to be within the shaded area shown in Fig. 1 in order to ensure a ferrite content below 70~ by volume and a residual austenite content exceeding 4% by volume.
Addition of titanium up to 0.05% ensures nitrogen setting and avoids the formation of elongated manganese sulphides.
Up to 0.8~ by mass of chromium can be added to improve martensite tempering properties and to avoid perlite formation.
Molybdenum, up to 0.5~ by mass increases the range of successful cooling rates.
Copper and nickel, up to 0.5~ by mass each, can contribute to lowering the transformation temperature and to avoiding perlite.
In order to influence coalescence o~ sulphides, treatment of the molten bath with calcium-silicon is advantageous.
The hot-rolling end-temperature ~T should be in the range of Ar3 - 50~C < ET < Ar3 + 100~C.
The Ar3 temperature which should be in the range of 750 to 950~C is calculated as follows 750~C ' Ar3 = 900 ~ 100~ Al - 60~ Mn - 300~ c ~ 950~C
Cooling down from hot-roll end-temperature to reeling temperature which i~ bet~een 200 and 500~C takes place in an accelerated way at a cooling-down speed of 15 to 70 E~/s .
Whe~ cooling down from the hot-roll end-temperature, in the process according to the invention, it is possible in the range of A~3 to Ar3 - 200~C, to further improve the formation of polygonal ferrite by observing a cooling pause of 2 to 30 s, during which the cooling rate is ~elow 15 K/s.
Fig. 2 shows a diagrammatic representation of hot-strip production coupled with the cooling progression of the steel according to the invention, at and after hot-rolling.
It shows that any undesired entering of the perlite region can safely be avoided if the conditions stated for the hot-roll end-temperature, the cooling-down speed and the reeling temperature, are observed.
A steel A according to the invention, with a ccmposi~ion according to Table 1 was hot rolled to a final strip thickness of 3.7 mm at a hot-roll end-temperature of 855~C.
Cooling from this temperature was at 30 K/s to the reel tempera~ure (RT) of 415~C. The characteristics of this steel A according to the in~ention were determined according to DIN EN 10002 on flat-drawn specimens.
Table 2 shows the values for the apparent yield point, tensile strength, elongation and the ratio of yield point to tensile strength for the layers along and across the ~ire~t.ion of ro.l.llng.
By way o~ comparison, Table 2 also shows the respective strength properties of a steel B, known from EP O 586 704 Al, with a composition as shown in Table 1.
Due to its spectrum of characteristics, the steel according to the invention is particularly suitable for the production of cold-reduced structural elements for motor ~ehicles, such as floor stiffener elements, transverse links, or for wheel disks.
Table 1 C~ Mn~ Si~ Cu-~O Ni9~ Cr~ P~ S% N%
A 0, 21G 1,3~ 1, B3 0, 06 0, 5 1 0,27 0,52 0,010 cO, 001 0,OOZ4 0,21 1,50 0,057 1,'16 <0,01 0,01 0,02 ~0,005 0,004 0,006 r '~ * ~ccording to EP O 586 704 A1 -~ CA 02224813 1997-12-16 . ~ O ~D
,~
r r m r ~ L~
O C) O C) L') L') ~ O
E L') C::~ O D
E E ~c~ o a L') ~o~ ~ ~ ,~ c~
~ ~ r r ~ ~ -Q O
- E L')~D ~ r E E ~ N
r r r ~ L~
o ~ _ o r o -- ~ILr) r z ~D L') C~
U~
~ O
O O
0:
~) ~I L'l ,_, o ~
L" O
E~ C~ L~ ~D
~:~ C CD C~
a~ ~ m U~
Claims (6)
1. A multi-phase steel, comprising (in % by mass) 0.12 to 0.3% carbon 1.2 to 3.5% manganese 1.1 to 2.2% aluminium less than 0.2% silicon the remainder being iron, including unavoidable impurities, including phosphorus and sulphur, with a perlite-free structure comprising up to 70% by volume of soft polygonal ferrite and the remainder being bainitic ferrite and more than 4% by volume of carbon-enriched residual austenite as well as if applicable, smaller percentages of carbon-enriched martensite which contains aluminium in a quantity in% by mass of Al < 7.6 ~ Cequ.- 0.36 with a carbon equivalent (Caqu.) of 0.2 ~ Cequ. =% C+1/20% Mn+ 1/20% Cr + 1/15% Mo ~ 0.325.
2. A multi-phase steel according to claim 1, characterised by a residual austenite content of up to 20% by volume.
3. A process for producing rolled product from a multi-phase steel composed according to claim 1 or 2, of high strength, good tenacity, good surface quality in hot-rolled condition and good ability to be cold-rolled, with a perlite-free structure comprising up to 70% by volume polygonal ferrite with the remainder being bainitic ferrite and more than 4% by volume of carbon-enriched residual austenite as well as if applicable, in addition, smaller percentages of carbon-enriched martensite; the said steel being continuous-cast and hot-rolled at a hot roll initial temperature exceeding 1000°C
and a hot-roll end-temperature (ET) in the range of Ar3 - 50°C < ET < Ar3 + 100°C, and subsequently cooled down from the hot-roll end temperature (ET) at a rate of 15 to 70 K/s to a reeling temperature in the range from 200 to 500°C and reeled up.
and a hot-roll end-temperature (ET) in the range of Ar3 - 50°C < ET < Ar3 + 100°C, and subsequently cooled down from the hot-roll end temperature (ET) at a rate of 15 to 70 K/s to a reeling temperature in the range from 200 to 500°C and reeled up.
4. A process according to claim 3, characterised in that one or several of the following are added to the steel by alloying (in % by mass):
up to 0.05% titanium up to 0.8% chromium up to 0.5% molybdenum up to 0.5% copper up to 0.8% nickel.
up to 0.05% titanium up to 0.8% chromium up to 0.5% molybdenum up to 0.5% copper up to 0.8% nickel.
5. A process according to claim 3, characterised in that in the temperature range between Ar3 to Ar3 - 200°C, a cooling pause of 2 to 30 s is observed, during which the cooling rate is below 15 K/s.
6. The use of a steel with a composition according to claim 1, 2 or 4 as a material for the production of cold-reduced structural elements for motor vehicles, such as floor stiffener elements, transverse links, or for wheel disks.
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE19521836.1 | 1995-06-16 | ||
| DE19521836 | 1995-06-16 | ||
| DE19605697A DE19605697C2 (en) | 1995-06-16 | 1996-02-16 | Multi-phase steel, production of rolled products and use of the steel |
| DE19605697.7 | 1996-02-16 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA2224813A1 true CA2224813A1 (en) | 1997-01-03 |
Family
ID=26016012
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002224813A Abandoned CA2224813A1 (en) | 1995-06-16 | 1996-06-01 | Multi-phase steel, production of rolled products and use of the steel |
Country Status (10)
| Country | Link |
|---|---|
| EP (1) | EP0748874A1 (en) |
| CN (1) | CN1190998A (en) |
| AR (1) | AR002502A1 (en) |
| BR (1) | BR9608969A (en) |
| CA (1) | CA2224813A1 (en) |
| CZ (1) | CZ402697A3 (en) |
| HU (1) | HUP9801755A3 (en) |
| PL (1) | PL324556A1 (en) |
| TR (1) | TR199701721T1 (en) |
| WO (1) | WO1997000331A1 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20080251160A1 (en) * | 2005-03-30 | 2008-10-16 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd) | High-Strength Cold-Rolled Steel Sheet Excellent in Uniform Elongation and Method for Manufacturing Same |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2748033B1 (en) * | 1996-04-26 | 1998-05-22 | Lorraine Laminage | PROCESS FOR PRODUCING A STRIP OF VERY HIGH STRENGTH HOT-ROLLED STEEL FOR USE IN FORMING AND IN PARTICULAR FOR STAMPING |
| JP4214006B2 (en) | 2003-06-19 | 2009-01-28 | 新日本製鐵株式会社 | High strength steel sheet with excellent formability and method for producing the same |
| CN103695762B (en) * | 2013-12-13 | 2016-06-08 | 安徽工业大学 | A kind of tensile strength 560��590MPa hot rolled wheel rim steel and manufacture method thereof |
| CA3000554A1 (en) * | 2015-09-22 | 2017-03-30 | Tata Steel Ijmuiden B.V. | A hot-rolled high-strength roll-formable steel sheet with excellent stretch-flange formability and a method of producing said steel |
| DE102016202005A1 (en) * | 2016-02-10 | 2017-08-10 | Thyssenkrupp Ag | Commercial vehicle wheel and use |
| DE102016211411A1 (en) * | 2016-06-24 | 2017-12-28 | Thyssenkrupp Ag | Vehicle wheel and use |
Family Cites Families (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| IT1000219B (en) * | 1973-12-06 | 1976-03-30 | Centro Speriment Metallurg | STEEL FOR MARINE USE WITH HIGH MECHANICAL RESISTANCE |
| JPS5827329B2 (en) * | 1978-04-05 | 1983-06-08 | 新日本製鐵株式会社 | Manufacturing method of low yield ratio high tensile strength hot rolled steel sheet with excellent ductility |
| BE899253A (en) * | 1984-03-27 | 1984-07-16 | Gielen Paul M E L | High strength low alloy steel - contg. only carbon aluminium and manganese additives |
| JP2952624B2 (en) * | 1991-05-30 | 1999-09-27 | 新日本製鐵株式会社 | High yield ratio type hot rolled high strength steel sheet excellent in formability and spot weldability and its manufacturing method and high yield ratio type hot rolled high strength steel sheet excellent in formability and its manufacturing method |
| JP3412157B2 (en) * | 1991-08-27 | 2003-06-03 | 住友金属工業株式会社 | High-ductility hot-rolled high-strength steel sheet and its manufacturing method |
| JPH06264183A (en) * | 1993-03-11 | 1994-09-20 | Sumitomo Metal Ind Ltd | Hot rolled high tensile strength steel plate with high workability and its production |
| US5470529A (en) * | 1994-03-08 | 1995-11-28 | Sumitomo Metal Industries, Ltd. | High tensile strength steel sheet having improved formability |
-
1996
- 1996-05-17 EP EP96107885A patent/EP0748874A1/en not_active Withdrawn
- 1996-06-01 CN CN96195602A patent/CN1190998A/en active Pending
- 1996-06-01 CA CA002224813A patent/CA2224813A1/en not_active Abandoned
- 1996-06-01 CZ CZ974026A patent/CZ402697A3/en unknown
- 1996-06-01 TR TR97/01721T patent/TR199701721T1/en unknown
- 1996-06-01 BR BR9608969A patent/BR9608969A/en not_active Application Discontinuation
- 1996-06-01 WO PCT/EP1996/002382 patent/WO1997000331A1/en not_active Application Discontinuation
- 1996-06-01 PL PL96324556A patent/PL324556A1/en unknown
- 1996-06-01 HU HU9801755A patent/HUP9801755A3/en unknown
- 1996-06-14 AR ARP960103182A patent/AR002502A1/en unknown
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20080251160A1 (en) * | 2005-03-30 | 2008-10-16 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd) | High-Strength Cold-Rolled Steel Sheet Excellent in Uniform Elongation and Method for Manufacturing Same |
| US9074272B2 (en) * | 2005-03-30 | 2015-07-07 | Kobe Steel, Ltd. | High-strength cold-rolled steel sheet excellent in uniform elongation and method for manufacturing same |
Also Published As
| Publication number | Publication date |
|---|---|
| HUP9801755A3 (en) | 1999-09-28 |
| EP0748874A1 (en) | 1996-12-18 |
| BR9608969A (en) | 1999-06-29 |
| HUP9801755A2 (en) | 1998-11-30 |
| PL324556A1 (en) | 1998-06-08 |
| MX9710229A (en) | 1998-03-29 |
| TR199701721T1 (en) | 1998-04-21 |
| AR002502A1 (en) | 1998-03-25 |
| CN1190998A (en) | 1998-08-19 |
| CZ402697A3 (en) | 1998-06-17 |
| WO1997000331A1 (en) | 1997-01-03 |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| FZDE | Discontinued |