AU2007299343B2 - Method for producing a steel strip - Google Patents
Method for producing a steel strip Download PDFInfo
- Publication number
- AU2007299343B2 AU2007299343B2 AU2007299343A AU2007299343A AU2007299343B2 AU 2007299343 B2 AU2007299343 B2 AU 2007299343B2 AU 2007299343 A AU2007299343 A AU 2007299343A AU 2007299343 A AU2007299343 A AU 2007299343A AU 2007299343 B2 AU2007299343 B2 AU 2007299343B2
- Authority
- AU
- Australia
- Prior art keywords
- steel
- metallic inclusions
- strip
- sulfur content
- melt
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Ceased
Links
- 238000004519 manufacturing process Methods 0.000 title abstract description 4
- 229910000831 Steel Inorganic materials 0.000 title description 31
- 239000010959 steel Substances 0.000 title description 31
- 239000000161 steel melt Substances 0.000 claims abstract description 33
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims abstract description 26
- 229910000655 Killed steel Inorganic materials 0.000 claims abstract description 11
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 8
- 229910052717 sulfur Inorganic materials 0.000 claims description 26
- 239000011593 sulfur Substances 0.000 claims description 26
- 238000000034 method Methods 0.000 claims description 14
- 239000002184 metal Substances 0.000 claims description 2
- 229910052751 metal Inorganic materials 0.000 claims description 2
- 238000005516 engineering process Methods 0.000 claims 1
- 150000002739 metals Chemical class 0.000 claims 1
- 230000007547 defect Effects 0.000 abstract description 10
- 239000005864 Sulphur Substances 0.000 abstract 1
- 238000005266 casting Methods 0.000 description 29
- 230000008018 melting Effects 0.000 description 28
- 238000002844 melting Methods 0.000 description 28
- 239000007788 liquid Substances 0.000 description 19
- 239000000203 mixture Substances 0.000 description 18
- 229910004298 SiO 2 Inorganic materials 0.000 description 14
- 238000007711 solidification Methods 0.000 description 7
- 230000008023 solidification Effects 0.000 description 7
- 238000005336 cracking Methods 0.000 description 6
- 230000000694 effects Effects 0.000 description 5
- 230000005496 eutectics Effects 0.000 description 5
- 239000000155 melt Substances 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 238000009434 installation Methods 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 229910000851 Alloy steel Inorganic materials 0.000 description 2
- 229910001208 Crucible steel Inorganic materials 0.000 description 2
- 238000007654 immersion Methods 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- BYFGZMCJNACEKR-UHFFFAOYSA-N Al2O Inorganic materials [Al]O[Al] BYFGZMCJNACEKR-UHFFFAOYSA-N 0.000 description 1
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000010924 continuous production Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000006477 desulfuration reaction Methods 0.000 description 1
- 230000023556 desulfurization Effects 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 239000011261 inert gas Substances 0.000 description 1
- 238000013021 overheating Methods 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000004088 simulation Methods 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
- 150000003463 sulfur Chemical class 0.000 description 1
- 150000003464 sulfur compounds Chemical class 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Continuous Casting (AREA)
- Treatment Of Steel In Its Molten State (AREA)
- Coating With Molten Metal (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The invention relates to a method for producing a strip-cast, low-carbon, partly Mn/Si killed steel strip that is largely free of cracks and surface defects from a steel melt with a sulphur content of between 20 and 300 ppm and an Mn/Si ratio ≥ 3.5, using a strip forming force of between 2 and 50 kN/m.
Description
2006P20176WO - 1 Process for producing a steel strip The invention relates to a process for the continuous production of a steel strip using at least two casting rolls and, if appropriate, laterally arranged side plates, wherein a casting reservoir, from which liquid steel melt can be introduced to the casting rolls, can be formed between the casting rolls and the side plates during operation. Background of the invention During the production of a steel strip from a low-carbon, partly Mn/Si killed steel melt, the steel strip produced, when the two-roll casting process known from the prior art is used, has many cracks and surface defects which significantly reduce the quality of the steel strip produced. It is known from W003024644 and US2005145304 to prevent or at least reduce the number of cracks and surface defects by selecting the composition of a steel melt in such a way that liquid non-metallic inclusions are produced in the steel melt, and these remain liquid during the solidification of the steel shell and permit a homogeneous heat flow and therefore a homogeneous cooling effect to be achieved by forming a liquid film on the surface of the casting rolls. During melting operation on an industrial scale, the MnO/SiO 2 ratios actually present in a partly Mn/Si killed steel melt are often substantially lower than those calculated theoretically due to operational reasons. The melting temperature of the non metallic inclusions in partly Mn/Si killed steel melts is very sensitive to changes in the steel composition and to associated changes in the MnO/SiO 2 ratio in the composition of said inclusions. When observing the metallurgical rules specified in the prior art for producing the liquid, non-metallic inclusions, it is therefore not possible to assume, during melting operation on an industrial scale, that each treated 2 ladle has a composition which ensures that liquid, non-metallic inclusions are present during the casting process. Cracks and surface defects can therefore reappear. 5 OBJECT OF THE INVENTION It is the object of the present invention to substantially overcome or ameliorate one or more of the disadvantages of the prior art. SUMMARY OF THE INVENTION 10 The present invention provides a process for producing a strip-cast, low-carbon, partly Mn/Si killed steel strip, wherein a steel melt is introduced from a melt reservoir between at least two casting rolls, that are cooled and move together with a steel strip, and at least partly solidifies on the casting rolls to form the steel strip, wherein the steel melt has a sulfur content of between 20 and 300 ppm and an Mn/Si ratio =3.5 and, during is normal operation, the roll separating force is between 2 and 50 kN/m. DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS The present invention provides a process for producing a steel strip, which is largely free of cracks and surface defects and has a homogeneous surface, from a low 20 carbon, partly Mn/Si killed steel melt. In this process, the tolerance of the melting temperature of non-metallic inclusions to deviations from a desired value of the steel composition should be sufficient to ensure that liquid, non-metallic inclusions are present in each treated ladle during the casting process during melting operation on an industrial scale. 25 To this end, the present invention provides a process in which a steel melt with a particular Mn/Si content ratio and with a particular sulfur content is processed, during normal operation, using a particular roll separating force (RSF). The invention provides a process for producing a strip-cast, low-carbon, partly Mn/Si killed steel strip, wherein a steel melt is introduced from a melt reservoir between 30 at least two casting rolls, that are cooled and move together with a steel strip, and at least partly solidifies on the casting rolls to form the steel strip. The steel melt has a sulfur content of between 20 and 300 ppm and an Mn/Si ratio =3.5 and, during normal operation, the roll separating force is between 2 and 50 kN/m. A steel strip produced in this way is unexpectedly largely free of cracks and 35 surface defects and has a homogeneous surface.
2006P20176WO - 3 A low-carbon steel strip is to be understood as meaning a steel strip with a carbon content of less than 0.1% by weight. The composition of the steel melt according to the invention ensures that the non-metallic inclusions have a low melting temperature. The low melting temperature has the effect that the non-metallic inclusions are present in a liquid state during the solidification of the steel shell on the casting rolls during the casting process. The tolerance of the melting temperature of non-metallic inclusions to deviations from a desired value of the steel composition is increased by the broadening of the composition range in which liquid, non metallic inclusions are present in the multiphase system. This broadened composition range ensures that the steel melt has a composition which guarantees liquid, non-metallic inclusions during the casting process even when the desired value for a particular steel composition is not exactly met during melting operation on an industrial scale. During the preparation of steel, oxidic or sulfidic non metallic inclusions are produced in a steel melt. The main components of the non-metallic inclusions in partly Mn/Si killed steel melts are MnO and SiO 2 . The setting of the sulfur content to values of between 20 and 300 ppm and of the Mn/Si ratio to values = 3.5, in accordance with the invention, has the effect that the non-metallic inclusions are principally composed of a multiphase system having the main components MnO-SiO 2 -MnS. If the MnS content of this multiphase system is less than 37% by weight MnS, the melting temperature of the multiphase system is less than the melting temperature of a multiphase system composed of the main components MnO and SiO 2 . The 3-phase system MnO-SiO 2 -MnS has a ternary eutectic at approximately 1130 0
C.
2006P20176WO - 4 The modeling of the 3-phase system MnO-SiO 2 -MnS in figure 1 shows that the liquidus range meets the binary boundary system MnO-SiO 2 at the eutectic temperature of 1251 0 C of the latter at the eutectic point, and expands during the transition to a 3 phase system with an increasing MnS content. At lower temperatures, the liquidus range moved away from the boundary system and can still be found only above certain minimum MnS contents. Typical operating points, which simultaneously have a low melting temperature of the non-metallic inclusions and a tolerance of the melting temperature to fluctuations in the MnS content which is sufficient during melting operation on an industrial scale, are approximately 15% by weight MnS in the case of the composition of the steel melt according to the invention. The simulation of the solidification conditions in a thin-strip casting installation using immersion tests at inert gas, contact time and overheating levels corresponding to strip casting and with sulfur contents of the steel melt of between 150 and 500 ppm resulted in mean MnS contents of the liquid, non-metallic inclusions of between 7 and 40% by weight. Increased sulfur contents of partly Mn/Si killed steel melts lead to increased MnS contents of the non-metallic inclusions. Figure 2 shows the influence of the sulfur content of a low carbon, partly Mn/Si killed steel melt (0.05% by weight C; 0.7% by weight Mn; 0.2% by weight Si) with an Mn/Si ratio = 3.5 on the tendency to cracking, expressed by the frequency of cracking or by the width of the melting interval of the steel melt, in relation to the composition of non-metallic inclusions and in relation to the melting temperatures (liquidus temperatures) of the non-metallic inclusions. The measured data in figure 2 were obtained from the above-mentioned immersion tests.
2006P20176WO - 5 Below a sulfur content of the melt which leads to an MnS content of the non-metallic inclusions which corresponds to the ternary eutectic at approximately 11300C, the melting temperature of the non-metallic inclusions decreases with an increasing sulfur content. Above a sulfur content of the melt which leads to an MnS content of the non-metallic inclusions which corresponds to the ternary eutectic at approximately 11300C, the melting temperatures of the non-metallic inclusions and also the frequency of cracking increase rapidly. The width of the melting interval increases up to a sulfur content of approximately 300 ppm, and then remains approximately constant. Figure 2 shows the relative behavior between increasing tendency to hot cracking and decreasing melting temperature of the non-metallic inclusions. The sulfur content which is recommended according to the invention and at which sufficiently low melting temperatures of the non-metallic inclusions and simultaneously a tolerable tendency to hot cracking are achieved can therefore be derived from figure 2. The presence of sulfur in a steel alloy expands the solid/liquid 2-phase area, i.e. the melting interval, of the steel alloy while simultaneously reducing the solidus temperature thereof, and this expands the temperature range in which hot cracks are produced between the liquid impenetration temperature (LIT) and the zero ductility temperature (ZDT). The width of the 2-phase area increases approximately linearly up to approximately 45C at a sulfur content of up to 300 ppm in the steel melt. Above this sulfur content, the width of the 2-phase area remains approximately constant because MnS precipitates during the solidification with an increasing sulfur content. These MnS precipitates are deposited in solid form on the surfaces of the casting rolls and thereby prevent a homogeneous heat flow or a homogeneous cooling effect, and this encourages the formation of surface defects and cracks. An 2006P20176WO - 6 increasing sulfur content of the steel melt leads to increasing quantities of MnS precipitates and therefore to an increase in the number of surface defects and cracks. According to the invention, the maximum sulfur content is therefore limited to 300 ppm. At a sulfur content of the steel melt of less than 20 ppm, the lowering of the melting temperature of the liquid, non-metallic inclusions compared to multiphase systems composed of the main components MnO and SiO 2 is not large enough to ensure that liquid, non-metallic inclusions are present during the solidification of the steel shell on the casting rolls during the casting process. In addition, at a sulfur content of less than 20 ppm, the width of the composition range in which liquid, non-metallic inclusions are present in the multiphase system is not large enough to ensure that there is a sufficient tolerance to deviations from a desired value of the steel composition during melting operation on an industrial scale. The sulfur content is preferably at least 50 ppm, particularly preferably at least 70 ppm. The upper limit of the sulfur content is preferably 250 ppm, particularly preferably 200 ppm. The sulfur content of the steel melt can be adjusted to the desired level by desulfurization or by the controlled addition of sulfur or of sulfur compounds. At an Mn/Si ratio of less than 3.5 in the steel melt, no multiphase system which is composed of the main components MnO SiO 2 -MnS and has a sufficient reduction of the melting temperature of the liquid, non-metallic inclusions to values below the' melting temperature of the steel mixture compared to a multiphase system composed of the main components MnO and SiC 2 is formed. According to the invention, the Mn/Si ratio therefore needs to be greater than or equal to 3.5.
2006P20176WO - 7 The roll separating force is the force with which the casting rolls are pressed against one another during the casting process, based on the width of the steel strip. The roll separating force influences the presence of cracks and surface defects in a strip-cast steel strip. The greater the roll separating force, the more temperature inhomogeneities that occur at the kissing point of the steel shells. Temperature inhomogeneities of this type result in non uniform cooling of the steel strip, and this can result in surface cracks. In addition, large roll separating forces mean that stresses are built up in the strip-cast steel strip, and these stresses can also result in cracks and impaired mechanical properties. The use of a small roll separating force avoids these problems and additionally affords the advantage that the casting apparatus is subjected to less mechanical stress. However, the selection of a small roll separating force may adversely affect the stability of the casting process since, in the case of a small roll separating force, there is the risk that the metal shells solidified on the casting rolls are insufficiently pressed together owing to inhomogeneities during the solidification and the steel strip cracks under its own weight, that the steel shells remain adhered to parts or over the whole width of the casting roll, and that cracks occur in the steel shell. In processes according to the prior art, the magnitude of the roll separating force, during normal operation, is between 5 and 250 kN/m. According to the invention, the roll separating force is less than 50 kN/m. Since the composition of the steel melt according to the invention minimizes the occurrence of inhomogeneities during the solidification of the steel shells owing to the fact that it ensures the occurrence of liquid, non-metallic 2006P20176WO - 8 inclusions, such a small roll separating force can be used without risking the stability of the casting process. The frequency of cracking increases with an increasing roll separating force. When roll separating forces of more than 50 kN/m are used, it is not possible to ensure the production of a homogeneous surface of the steel strip which is largely free of cracks and surface defects. According to the invention, the lower limit for the roll separating force is 2 kN/m. Sufficient stability of the casting process is not ensured below this value. The roll separating force is preferably at least 5 kN/m. The upper limit thereof is preferably 30 kN/m. The stated values for the roll separating force refer to the steady-state normal operation of a casting installation, but not to the conditions when the installation is starting up or when extraordinary load effects temporarily occur. According to a further preferred embodiment of the process according to the invention, the non-metallic inclusions in the steel melt have a mass fraction of A1 2 0 3 of less than 45% by weight. The resultant multiphase system with the main components MnO-SiO 2 -MnS-Al2O 3 has a melting temperature which is less than the melting temperature of a multiphase system composed of the main components MnO and SiO 2 . In addition, the composition range in which liquid, non-metallic inclusions are present is broader in the multiphase system with the main components MnO-SiO 2 -MnS-Al 2 0 3 than in the multiphase system composed of the main components MnO and SiO 2 . The A1 2 0 3 content is set by selecting the starting materials for producing the steel melt and, if appropriate, by the targeted addition of Al or Al compounds.
Claims (3)
- 2. The process as claimed in claim 1, wherein the steel melt has a sulfur content of between 50 and 250 ppm.
- 3. The process as claimed in claim I or 2, wherein the roll separating force is between 5 and 30 kN/m. is 4. The process as claimed in any one of the preceding claims, wherein the steel melt contains non-metallic inclusions with a mass fraction of A1 2 0 3 of less than 45% by weight.
- 5. The process as claimed in claim 1, wherein the steel melt has a sulfur content of between 70 and 200 ppm. 20 6. A process for producing a strip-cast, low-carbon, partly Mn/Si killed steel strip substantially as hereinbefore described with reference to the accompanying drawings. Dated 4 May, 2011 25 Siemens VAI Metals Technologies GmbH & Co. Patent Attorneys for the Applicant/Nominated Person SPRUSON & FERGUSON
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| ATA1593/2006 | 2006-09-22 | ||
| AT0159306A AT504225B1 (en) | 2006-09-22 | 2006-09-22 | METHOD FOR PRODUCING A STEEL STRIP |
| PCT/EP2007/007228 WO2008034502A1 (en) | 2006-09-22 | 2007-08-16 | Method for producing a steel strip |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| AU2007299343A1 AU2007299343A1 (en) | 2008-03-27 |
| AU2007299343B2 true AU2007299343B2 (en) | 2011-09-08 |
Family
ID=38541914
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| AU2007299343A Ceased AU2007299343B2 (en) | 2006-09-22 | 2007-08-16 | Method for producing a steel strip |
Country Status (16)
| Country | Link |
|---|---|
| US (1) | US20100018665A1 (en) |
| EP (1) | EP2066466B2 (en) |
| JP (1) | JP5129253B2 (en) |
| KR (1) | KR101442724B1 (en) |
| CN (1) | CN101516544B (en) |
| AT (2) | AT504225B1 (en) |
| AU (1) | AU2007299343B2 (en) |
| BR (1) | BRPI0717489B1 (en) |
| DK (1) | DK2066466T3 (en) |
| ES (1) | ES2366139T5 (en) |
| MX (1) | MX2009002629A (en) |
| PL (1) | PL2066466T3 (en) |
| RU (1) | RU2418650C2 (en) |
| SI (1) | SI2066466T1 (en) |
| UA (1) | UA93097C2 (en) |
| WO (1) | WO2008034502A1 (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US7975754B2 (en) * | 2007-08-13 | 2011-07-12 | Nucor Corporation | Thin cast steel strip with reduced microcracking |
| CN113198995A (en) * | 2021-04-25 | 2021-08-03 | 芜湖新兴铸管有限责任公司 | Peritectic steel continuous casting billet depression improvement control method |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20020174746A1 (en) * | 2001-04-02 | 2002-11-28 | Clay Gross | Ladle refining of steel |
| WO2003024644A1 (en) * | 2001-09-14 | 2003-03-27 | Nucor Corporation | Casting steel strip |
| WO2004035247A1 (en) * | 2002-10-15 | 2004-04-29 | Voest-Alpine Industrieanlagenbau Gmbh & Co | Method for continuously producing a thin steel strip |
Family Cites Families (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP3016632B2 (en) † | 1991-07-09 | 2000-03-06 | 日新製鋼株式会社 | Operation control method of twin roll continuous caster. |
| JP3308102B2 (en) * | 1994-05-26 | 2002-07-29 | キャストリップ・リミテッド・ライアビリティ・カンパニー | Metal strip continuous casting method |
| AUPN281195A0 (en) * | 1995-05-05 | 1995-06-01 | Bhp Steel (Jla) Pty Limited | Casting steel strip |
| JPH09168844A (en) * | 1995-12-19 | 1997-06-30 | Mitsubishi Heavy Ind Ltd | Twin roll continuous casting method |
| JP3117638B2 (en) * | 1996-03-28 | 2000-12-18 | 新日本製鐵株式会社 | Continuous slab casting method |
| IT1291931B1 (en) * | 1997-06-19 | 1999-01-21 | Voest Alpine Ind Anlagen | PROCEDURE FOR THE PRODUCTION OF RAW STEEL CASTING TAPES WITH LOW CARBON CONTENT AND THIS OBTAINABLE TAPES |
| FR2791286B1 (en) * | 1999-03-26 | 2001-05-04 | Lorraine Laminage | PROCESS FOR PRODUCING CARBON STEEL STRIPS BY CONTINUOUS CASTING BETWEEN TWO CYLINDERS |
| JP4518645B2 (en) * | 2000-01-21 | 2010-08-04 | 日新製鋼株式会社 | High strength and high toughness martensitic stainless steel sheet |
| AUPR047900A0 (en) * | 2000-09-29 | 2000-10-26 | Bhp Steel (Jla) Pty Limited | A method of producing steel |
| DE10125669B4 (en) * | 2001-05-25 | 2006-04-27 | Hammelmann Maschinenfabrik Gmbh | Pump, in particular plunger pump |
| FR2834722B1 (en) * | 2002-01-14 | 2004-12-24 | Usinor | MANUFACTURING PROCESS OF A COPPER-RICH CARBON STEEL STEEL PRODUCT, AND THUS OBTAINED STEEL PRODUCT |
| KR100489018B1 (en) * | 2002-08-30 | 2005-05-11 | 주식회사 포스코 | Method of Manufacturing High Manganese Steel Strip With Twin Roll Strip Casting Apparatus |
| AU2004205421B2 (en) | 2003-01-24 | 2009-11-26 | Nucor Corporation | Casting steel strip |
| NZ546189A (en) * | 2003-10-10 | 2009-09-25 | Ishikawajima Harima Heavy Ind | Casting steel strip |
| WO2007079545A1 (en) * | 2006-01-16 | 2007-07-19 | Nucor Corporation | Thin cast steel strip with reduced microcracking |
| US7464746B2 (en) † | 2006-08-09 | 2008-12-16 | Nucor Corporation | Method of casting thin cast strip |
-
2006
- 2006-09-22 AT AT0159306A patent/AT504225B1/en not_active IP Right Cessation
-
2007
- 2007-08-16 BR BRPI0717489A patent/BRPI0717489B1/en not_active IP Right Cessation
- 2007-08-16 WO PCT/EP2007/007228 patent/WO2008034502A1/en active Application Filing
- 2007-08-16 UA UAA200902521A patent/UA93097C2/en unknown
- 2007-08-16 PL PL07801685T patent/PL2066466T3/en unknown
- 2007-08-16 ES ES07801685.4T patent/ES2366139T5/en active Active
- 2007-08-16 SI SI200730701T patent/SI2066466T1/en unknown
- 2007-08-16 DK DK07801685.4T patent/DK2066466T3/en active
- 2007-08-16 US US12/442,189 patent/US20100018665A1/en not_active Abandoned
- 2007-08-16 AU AU2007299343A patent/AU2007299343B2/en not_active Ceased
- 2007-08-16 JP JP2009528610A patent/JP5129253B2/en not_active Expired - Fee Related
- 2007-08-16 RU RU2009115180/02A patent/RU2418650C2/en not_active IP Right Cessation
- 2007-08-16 KR KR1020097008241A patent/KR101442724B1/en not_active Expired - Fee Related
- 2007-08-16 CN CN2007800353340A patent/CN101516544B/en active Active
- 2007-08-16 AT AT07801685T patent/ATE514502T1/en active
- 2007-08-16 MX MX2009002629A patent/MX2009002629A/en active IP Right Grant
- 2007-08-16 EP EP07801685.4A patent/EP2066466B2/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20020174746A1 (en) * | 2001-04-02 | 2002-11-28 | Clay Gross | Ladle refining of steel |
| WO2003024644A1 (en) * | 2001-09-14 | 2003-03-27 | Nucor Corporation | Casting steel strip |
| WO2004035247A1 (en) * | 2002-10-15 | 2004-04-29 | Voest-Alpine Industrieanlagenbau Gmbh & Co | Method for continuously producing a thin steel strip |
| US20050211412A1 (en) * | 2002-10-15 | 2005-09-29 | Gerald Hohenbichler | Installation for continuously producing a thin steel strip |
Also Published As
| Publication number | Publication date |
|---|---|
| DK2066466T3 (en) | 2011-10-24 |
| EP2066466A1 (en) | 2009-06-10 |
| ATE514502T1 (en) | 2011-07-15 |
| RU2009115180A (en) | 2010-10-27 |
| CN101516544A (en) | 2009-08-26 |
| RU2418650C2 (en) | 2011-05-20 |
| WO2008034502A1 (en) | 2008-03-27 |
| KR20090064462A (en) | 2009-06-18 |
| AT504225B1 (en) | 2008-10-15 |
| CN101516544B (en) | 2011-06-08 |
| PL2066466T3 (en) | 2011-11-30 |
| JP5129253B2 (en) | 2013-01-30 |
| SI2066466T1 (en) | 2011-10-28 |
| BRPI0717489A2 (en) | 2013-10-15 |
| BRPI0717489B1 (en) | 2016-02-10 |
| AU2007299343A1 (en) | 2008-03-27 |
| MX2009002629A (en) | 2009-03-24 |
| EP2066466B2 (en) | 2014-08-27 |
| KR101442724B1 (en) | 2014-09-23 |
| JP2010504214A (en) | 2010-02-12 |
| EP2066466B1 (en) | 2011-06-29 |
| AT504225A1 (en) | 2008-04-15 |
| ES2366139T3 (en) | 2011-10-17 |
| US20100018665A1 (en) | 2010-01-28 |
| UA93097C2 (en) | 2011-01-10 |
| ES2366139T5 (en) | 2014-10-06 |
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