EP2623626B1 - Non-oriented electric steel plate without corrugated fault and production method thereof - Google Patents
Non-oriented electric steel plate without corrugated fault and production method thereof Download PDFInfo
- Publication number
- EP2623626B1 EP2623626B1 EP11827949.6A EP11827949A EP2623626B1 EP 2623626 B1 EP2623626 B1 EP 2623626B1 EP 11827949 A EP11827949 A EP 11827949A EP 2623626 B1 EP2623626 B1 EP 2623626B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- slab
- temperature
- controlled
- rolling
- steel sheet
- 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.)
- Active
Links
Images
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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D25/00—Special casting characterised by the nature of the product
-
- 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
- B22D11/16—Controlling or regulating processes or operations
- B22D11/18—Controlling or regulating processes or operations for pouring
- B22D11/181—Controlling or regulating processes or operations for pouring responsive to molten metal level or slag level
- B22D11/182—Controlling or regulating processes or operations for pouring responsive to molten metal level or slag level by measuring temperature
-
- 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
- B22D11/16—Controlling or regulating processes or operations
- B22D11/22—Controlling or regulating processes or operations for cooling cast stock or mould
- B22D11/225—Controlling or regulating processes or operations for cooling cast stock or mould for secondary cooling
-
- 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
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
-
- 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
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular fabrication or treatment of ingot or slab
-
- 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
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1222—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
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1233—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
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1272—Final recrystallisation annealing
-
- 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
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1277—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular surface treatment
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
-
- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/16—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys in the form of sheets
-
- 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
- C21D2201/00—Treatment for obtaining particular effects
- C21D2201/05—Grain orientation
Definitions
- the present invention relates to a non-oriented electrical steel sheet and a manufacturing method thereof, especially to a middle steel grade non-oriented electrical steel sheet without corrugated defect, which has an excellent magnetism, and a manufacturing method thereof.
- corrugated defect For a non-oriented electrical steel sheet having a high extent of silicon, in the surface of a finished strip, accidented waves, similar to corrugations, appear in a direction of rolling, which is generally called "corrugated defect". This defect will reduce a stacking coefficient of the finished strip notably, making the magnetism of the finished strip worse and the electrical resistance between insulating film layers decreased, thus reducing the service performance and life of terminal production. Therefore, almost all of users have a definite demand that a finished strip having corrugated defects is not allowed.
- the mechanism of the generation of the corrugated defects may be explained as follows: the equiaxed crystal ratio in the slab is low, whereas the columnar crystal is gross and growing.
- the growing direction of the columnar crystal ⁇ 001> which is the normal direction of (001), is the direction in which the heat flux gradient is the largest. In such a hot rolling process, the gross columnar crystal can not thoroughly break due to dynamic recovery and slow re-crystallization.
- the slab columnar crystals are easy to grow in the direction of heat flux, and form gross columnar crystals having a certain orienting relation, resulting in inhomogeneous deformations in a rolling process, the center in sheet thickness is fiber texture primarily after hot rolling process, and austenite and ferrite have no phase transition in subsequent process, and will not re-crystallize in the following cold rolling and annealing process, which does not make the homogeneity of the texture eliminated, and leaving behind to the finished product, finally forming accidented corrugated defects.
- the conventional methods for treating corrugated defects are mainly as follows: by utilizing electromagnetic stirring, the equiaxed crystal ratio in the slab may be improved, for example, in Japanese Patent Application Laid-open No. 49-39526 ; by adding the contents of carbon and manganese into steel, the phase transiting temperature in hot rolling process may be reduced, for example, in Japanese Patent Application Laid-open No. 48-49617 , Chinese Patent Application CN10127519 , CN1548569 and CN101139681 etc.; by utilizing low temperature pouring, the equiaxed crystal ratio in the slab may be improved, for example, in Japanese Patent Application Laid-open No. 53-14609 and No.
- the strip may re-crystallize sufficiently, for example, in Japanese Patent Application Laid-open No. 49-27420 , No. 49-38813 , No. 53-2332 , No. 61-69923 , Chinese Patent Application CN1548569 ; and by utilizing a normalized process, the strip may re-crystallize sufficiently, for example, in Japanese Patent Application Laid-open No. 61-127817 , etc.
- CN1611616 relates to a method of manufacturing cold-rolled non-oriented electrical steel, including steps of continuously casting blanks, hot-rolling, cold rolling and then annealing thin slabs, to achieve high proportions of recrystallisation.
- the equiaxed crystal ratio in the slab may be improved.
- This method utilizes electromagnetic stirring, the columnar crystals may break under electromagnetic force, and therefore, the effect thereof is the most effective.
- This method will remarkably reduce the columnar crystal ratio in the slab and improve the equiaxed crystal ratio in the temperature in a planishing process, and controlling the degrees of reduction of the first and the last pass in the hot rolling process, the gross columnar crystals in the slab may break, so as to prohibit the development of the gross deformation crystal grains as well as to make the strip re-crystallized sufficiently.
- the main disadvantage of this method is that increasing the furnace tap temperature of the slab will make the impurities such as MnS, AlN etc., solutionized intensively, thus make the magnetism of the finished strip worse. Meanwhile, in order to ensure the re-crystallization effect of the strip, the contents of impurity elements such as S, N etc., in steel are strictly demanded. Also, improving the degrees of reduction of the first and the last pass in the hot rolling process is restricted by self-capability of a rolling mill.
- the strip may re-crystallize sufficiently.
- the steel grade that has a high content of silicon needs to carry out the normalized process, one of the objects is to increase the re-crystallizing ratio in the hot rolling sheet, so as to avoid the generation of the corrugated defects.
- the main disadvantage of this method is that the manufacturing cost is very high, which is not applied in low or middle steel grade silicon steel of which the additional value is relatively low.
- the object of the present invention is to provide a non-oriented electrical steel sheet without the corrugated defect and a manufacturing method thereof.
- the manufacture of a middle steel grade non-oriented electrical steel sheet without corrugated defect can be accomplished, which has advantages of easy operation, low cost, energy conservation and environmental protection, and excellent magnetism, by strictly controlling the cooling speed of the slab in continuous casting and pouring process, the temperature difference in the length direction of the slab in the heating furnace, and by controlling the temperature drop before planishing the slab.
- the casting speed of the slab in continuous casting and pouring process is normal, so that the relatively high superheat of the liquid steel can be maintained, and the relatively low furnace tap temperature of the slab, and normal end-rolling temperature and coiling temperature etc., can be maintained in the hot rolling and steel reheating process, so that the strip in the hot rolling process does not need to carry out a normalized process.
- the technical solution of the present invention is that a middle steel grade non-oriented electrical steel sheet without the corrugated defect, wherein the weight percentage of the chemical composition thereof is that C is no more than 0.005%, Si is 1.2-2.2%, Mn is 0.2-0.4%, P is no more than 0.2%, S is no more than 0.005%, Al is 0.2-0.6%, N is no more than 0.005%, O is no more than 0.005%, balance Fe and inevitable impurities; where the equiaxed crystal ratio in the steel sheet is at least 43%, and where the thickness of the sheet is 2.0mm - 2.8mm.
- C is no more than 0.005%.
- C is an element for strongly inhibiting the growth of crystal grains, which is easy to result in the increase of iron loss of a strip, producing the serious magnetic aging. Meanwhile, C may further widen ⁇ phase, and increase the transition amount between ⁇ phase and ⁇ phase when in the normalized process, so as to reduce Acl point notably, and to fine crystallizing structure. Therefore, C is necessary to be controlled to no more than 0.005%.
- Si is 1.2%-2.2%. Si is an effective element for increasing the electrical resistivity of the steel. If the content of Si is lower than 1.2%, the electromagnetic performance of the steel is not good, whereas if the content of Si is higher than 2.2%, phase change will not occur in the hot rolling process, and the cold-working performance is not good.
- Al is 0.2%-0.6%. Al is an effective element for increasing the electrical resistivity of the steel. If the content of Al is lower than 0.2%, the electromagnetic performance is not stable, whereas if the content of Al is higher than 0.6%, the smelting and pouring process will become difficult, thus increasing the manufacturing cost.
- Mn is 0.2%-0.4%. Like the elements Si and Al, Mn may increase the electrical resistivity of the steel, as well as improve the surface state of the electrical steel, so it is necessary to add no less than 0.2% of Mn. While the content of Mn is higher than 0.4%, the smelting and pouring process will become difficult, thus increasing the manufacturing cost.
- P is no more than 0.2%. Adding some phosphorus into steel can improve the workability of steel sheet, but if the content of phosphorus is more than 0.2%, it instead makes the cold rolling workability of steel plate deteriorated.
- S is no more than 0.005%. If the content of S is more than 0.005%, the deposition amount of sulfide such as MnS, will increase greatly, thus strongly preventing crystal grains growing and making iron loss worse.
- N is no more than 0.005%. If the content of N is more than 0.005%, the deposition amount of nitride such as AlN, will increase greatly, thus strongly preventing crystal grains growing and making iron loss worse.
- O is no more than 0.005%. If the content of O is more than 0.005%, the impurity amount of oxidate such as Al 2 O 3 , will increase greatly, thus strongly preventing crystal grains growing and making iron loss worse.
- a method for manufacturing a non-oriented electrical steel sheet without corrugated defect of the present invention comprises the following steps:
- the middle steel grade non-oriented electrical steel sheet without corrugated defect of the present invention and the manufacturing method thereof comprise the following steps:
- the average superheat of liquid steel in the pouring process is controlled to 10-45°C.
- the water flowrate of cooling water is adjusted to 100-190 l/min, so as to improve the equiaxed crystal ratio in the slab, avoiding columnar crystals in the slab gross and growing.
- the temperature difference between the random two points in the length direction when the slab is heated is controlled to be lower than 25°C; the temperature difference between the watermark points of the slab is limited within 25°C, meanwhile the residence time of the slab in after-firing zone should be no less than 45 min, so as to ensure uniform heating, making the temperatures of both surfaces of the slab close.
- the furnace tap temperature of the slab can be reduced to no higher than 1150°C, avoiding the impurities such as MnS, AlN etc., solutionized intensively, which thus making the magnetism of the finished strip worse.
- Hot rolling sheet is rolled to have a thickness of 2.0mm-2.8mm.
- the entry temperature in the planishing process is controlled to no lower than 970°C so as to facilitate sufficient re-crystallization, and the end-rolling temperature is controlled to about 850 °C, the coiling temperature is controlled to about 600 °C.
- the hot rolling is rolled to thick strip that has a thickness of 0.5mm, and then is annealed continuously in a dry atmosphere.
- the electromagnetic performance of the steel is further improved by warming up the finished strip quickly in a preheating zone, in which the heat-up speed is no less than 1000°C/min, and by controlling the atmosphere mode in furnace.
- the content of silicon when the content of silicon is less than 2.2%, the content of silicon does not affect the growth of the columnar crystal as greatly as the cooling speed of the slab, therefore, the water flowrate of cooling water in the continuous casting process can be adjusted to reduce the heat flux gradient of the slab in the growing direction of the columnar crystal, so that the ratio of gross and growing columnar crystals can be reduced effectively.
- the temperature of the slab at the location where the slab contacts the roller table is relatively low in the slab heating process, which affects the re-crystallization of the fiber texture in the interior of the slab, not making the homogeneity of the texture eliminated and leaving behind to the finished product, therefore, it is necessary to strictly control the temperature of the watermark point of the slab.
- the main reason on improving the entry temperature in the planishing process is to facilitate the break and elimination of the columnar crystals in the rolling process and improve the re-crystallization ratio of the fiber texture in the hot rolling strip.
- the content of silicon is no more than 1.2%, the phase change from ⁇ phase to ⁇ phase in the hot rolling process is sufficient, the corrugated defects will not occur in the surface of the subsequent finished product.
- the columnar crystals in the slab may be broken due to highly electromagnetic stirring force, as possible as to transit to fine equiaxed crystals, so as to improve the equiaxed crystal ratio in the slab greatly; or the phase change from ⁇ phase to ⁇ phase happens in the interior of the slab by increasing the furnace tap temperature of the slab in the heat process greatly, meanwhile the re-crystallization of the slab is improved by utilizing high temperature status to enlarge the re-crystallizing structure in the interior of the slab.
- the electromagnetic stirring technology is hard to match the superheat of the liquid steel precisely, if the superheat of the liquid steel is controlled improperly, the controlling effect of the electromagnetic stirring is not stable, which is hard to obtain the expecting effect; and by increasing the furnace tap temperature of the slab, the heating load distribution in the heating furnace will forward, making high temperature time zone relatively long, which affects the magnetism of the finished strip.
- This method is easy to result in mass defect at the edge of the strip with respect to high-silicon steel grade.
- the water flowrate of cooling water in the continuous casting process can be adjusted to reduce the heat flux gradient of the slab in the growing direction of the columnar crystal, so that the ratio of gross and growing columnar crystals can be reduced effectively. It is more important that this method is substantially affected by the change in the superheat of the liquid steel, so the range of application is relatively wide. Meanwhile, the adjustment on the water flowrate of cooling water is very simple and controllable, so the difficulty in implementation is low, the stability is good. Further, the equipment load may be reduced by utilizing lower furnace tap temperature of the slab, avoiding the deposition of fine impurities in the steel and affecting the magnetism of final product.
- the temperature at the watermark points in the slab may be adjusted to increase re-crystallizing ratio of the fiber texture of the slab in the hot rolling process, and to improve the homogeneity of the texture of the slab in the hot rolling strip, which facilitates to the corrugated defects in the surface of the finished strip.
- the chemical composition of the tundish liquid steel in the continuous casting process is controlled as follows: C is 0.001%, Si is 1.22%, Mn is 0.25%, P is 0.02%, S is 0.003%, Al is 0.33%, N is 0.001%, O is 0.004%, balance Fe and inevitable impurities.
- the average superheat of the liquid steel is 34.6°C
- the casting speed is 1.07m/min
- the water flowrate of the cooling water is 185 l/min
- the temperature drop speed of the slab is 11.6min/°C
- the surface temperature of the slab at the outlet of a caster is 710 °C
- the equiaxed crystal ratio is 43%.
- the temperature difference between the watermark points is 22°C
- the residence time in after-firing zone of the slab is 46 minutes.
- the rolling process will be carried out after heating for 3h at 1125°C
- the temperature at the inlet in planishing process is 978°C
- the end-rolling temperature is 856°C
- the coiling temperature is 567°C.
- the hot rolling sheet is rolled to 0.5mm thickness of strip with the single cold rolling method, and then is annealed continuously in a dry atmosphere. Corrugated defects are not generated in the surface of the finished strip, the iron loss is 4.743 W/kg, and the magnetic induction is 1.727T.
- the chemical composition of the tundish liquid steel in the continuous casting process is controlled as follows: C is 0.002%, Si is 1.42%, Mn is 0.30%, P is 0.06%, S is 0.002%, Al is 0.25%, N is 0.002%, O is 0.002%, balance Fe and inevitable impurities.
- the average superheat of the liquid steel is 31.4°C
- the casting speed is 1.04m/min
- the water flowrate of the cooling water is 175 l/min
- the temperature drop speed of the slab is 9.6 min/°C
- the surface temperature of the slab at the outlet of a caster is 680°C
- the equiaxed crystal ratio is 57%.
- the temperature difference between the watermark points is 22°C
- the residence time in after-firing zone of the slab is 48 minutes.
- the rolling process will be carried out after heating for 3h at 1135°C, the temperature at the inlet in planishing process is 973°C, the end-rolling temperature is 853°C and the coiling temperature is 563 °C .
- the hot rolling sheet is rolled to 0.5mm thickness of strip with the single cold rolling method, and then is annealed continuously in a dry atmosphere. Corrugated defects are not generated in the surface of the finished strip, the iron loss is 3.130 W/kg, and the magnetic induction is 1.741T.
- the chemical composition of the tundish liquid steel in the continuous casting process is controlled as follows: C is 0.002%, Si is 1.49%, Mn is 0.49%, P is 0.02%, S is 0.003%, Al is 0.59%, N is 0.001%, O is 0.002%, balance Fe and inevitable impurities.
- the average superheat of the liquid steel is 28.7°C
- the casting speed is 0.99m/min
- the water flowrate of the cooling water is 189 l/min
- the temperature drop speed of the slab is 8.7 min/°C
- the surface temperature of the slab at the outlet of a caster is 660°C
- the equiaxed crystal ratio is 63%.
- the temperature difference between the watermark points is 24°C
- the residence time in after-firing zone of the slab is 53 minutes.
- the rolling process will be carried out after heating for 3h at 1102°C, the temperature at the inlet in planishing process is 983°C, the end-rolling temperature is 854°C and the coiling temperature is 575°C .
- the hot rolling sheet is rolled to 0.5mm thickness of strip with the single cold rolling method, and then is annealed continuously in a dry atmosphere. Corrugated defects are not generated in the surface of the finished strip, the iron loss is 3.559 W/kg, and the magnetic induction is 1.737T.
- the chemical composition of the tundish liquid steel in the continuous casting process is controlled as follows: C is 0.001%, Si is 2.12%, Mn is 0.25%, P is 0.01%, S is 0.002%, Al is 0.36%, N is 0.001%, O is 0.004%, balance Fe and inevitable impurities.
- the average superheat of the liquid steel is 31.2°C
- the casting speed is 0.95m/min
- the water flowrate of the cooling water is 173 l/min
- the temperature drop speed of the slab is 13.2 min/°C
- the surface temperature of the slab at the outlet of a caster is 680°C and the equiaxed crystal ratio is 59%.
- the temperature difference between the watermark points is 20°C
- the residence time in after-firing zone of the slab is 48 minutes.
- the rolling process will be carried out after heating for 3h at 1097°C
- the temperature at the inlet in planishing process is 972°C
- the end-rolling temperature is 844°C
- the coiling temperature is 583°C.
- the hot rolling sheet is rolled to 0.5mm thickness of strip with the single cold rolling method, and then is annealed continuously in a dry atmosphere. Corrugated defects are not generated in the surface of the finished strip, the iron loss is 2.833 W/kg, and the magnetic induction is 1.726T.
- the chemical composition of the tundish liquid steel in the continuous casting process is controlled as follows: C is 0.001%, Si is 1.47%, Mn is 0.32%, P is 0.02%, S is 0.003%, Al is 0.25%, N is 0.002%, O is 0.002%, balance Fe and inevitable impurities.
- the average superheat of the liquid steel is 28.9°C
- the casting speed is 1.03m/min
- the water flowrate of the cooling water is 257 l/min
- the temperature drop speed of the slab is 17.4 min/°C
- the temperature difference between the watermark points is 37°C
- the residence time in after-firing zone of the slab is 41 minutes.
- the rolling process will be carried out after heating for 3h at 1153°C
- the temperature at the inlet in planishing process is 947°C
- the end-rolling temperature is 847°C
- the coiling temperature is 567°C.
- the hot rolling sheet is rolled to 0.5mm thickness of strip with the single cold rolling method, and then is annealed continuously in a dry atmosphere.
- the percentage of the generation of corrugated defects in the surface of the finished strip is as high as no less than 90%
- the iron loss is 3.273 W/kg
- the magnetic induction is 1.736T.
- Fig. 1 shows the relation between the water flowrate of the cooling water and the equiaxed crystal ratio in the slab.
- Fig.l on the premise of not utilizing an electromagnetic stirring, by decreasing the water flowrate of the cooling water and strictly controlling it to no more than 190 l/min, the equiaxed crystal ratio in the slab is improved remarkably.
- the equiaxed crystal ratio in the slab may be controlled when the superheat of the liquid steel is relatively high.
- the equiaxed crystal ratio in the slab when the water flowrate of the cooling water is 173 l/m, the equiaxed crystal ratio in the slab is up to 59%, in the comparative example, when the water flowrate of the cooling water is 257 l/min, the equiaxed crystal ratio in the slab is only 28%. Also, in the third embodiment, the control of the equiaxed crystal ratio in the slab is better, up to 63%.
- Fig. 2 shows the relation between the entry temperature in the hot rolling and planishing process and the incidence of the corrugated defects in a finished product. It is indicated in accordance with the statistical results that by increasing the entry temperature in the hot rolling and planishing process and up to more than 970°C, because the re-crystallizing ratio of the fiber texture of the slab in the hot rolling process is increased remarkably, the incidence of the corrugated defects in the finished strip may be reduced greatly.
- the entry temperatures in the hot rolling and planishing process of most of strips are less than 970°C, the percentage of the generation of corrugated defects in the surface of the finished strip is as high as no less than 90%.
- most of the entry temperatures in the hot rolling and planishing process of strips are more than 970°C, corrugated defects are not generated in the surface of the finished strip, respectively.
- Fig. 3 shows the relation between the furnace tap temperature of the slab and the magnetism of the finished product. The higher the furnace tap temperature of the slab is, the worse the magnetism of the finished product is.
- Figs. 4 and 5 are metallographic structures of strips in hot rolling process corresponding to different watermark point temperatures.
- the watermark point temperatures are all less than 25°C in the first to fourth embodiments, so re-crystallizing structures of the strips in the hot rolling process are very homogeneous, the fiber textures disappear completely, whereas in the comparative example, the temperature at the watermark point is as high as 37 °C, the fiber texture of the strip in the hot rolling process is clear, which is hard to re-crystallized in the period of the subsequent cold rolling and annealing process, not being able to destroy the homogeneity of the structures and leaving behind to the finished product, finally forming accidented corrugated defects.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Electromagnetism (AREA)
- Dispersion Chemistry (AREA)
- Power Engineering (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
- Continuous Casting (AREA)
- Soft Magnetic Materials (AREA)
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CN2010102989655A CN102443734B (zh) | 2010-09-30 | 2010-09-30 | 无瓦楞状缺陷的无取向电工钢板及其制造方法 |
PCT/CN2011/072766 WO2012041053A1 (zh) | 2010-09-30 | 2011-04-14 | 无瓦楞状缺陷的无取向电工钢板及其制造方法 |
Publications (3)
Publication Number | Publication Date |
---|---|
EP2623626A1 EP2623626A1 (en) | 2013-08-07 |
EP2623626A4 EP2623626A4 (en) | 2017-11-22 |
EP2623626B1 true EP2623626B1 (en) | 2019-11-20 |
Family
ID=45891876
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP11827949.6A Active EP2623626B1 (en) | 2010-09-30 | 2011-04-14 | Non-oriented electric steel plate without corrugated fault and production method thereof |
Country Status (8)
Country | Link |
---|---|
US (1) | US20130224064A1 (ja) |
EP (1) | EP2623626B1 (ja) |
JP (1) | JP2013540900A (ja) |
KR (1) | KR20130049822A (ja) |
CN (1) | CN102443734B (ja) |
MX (1) | MX357357B (ja) |
RU (1) | RU2550440C2 (ja) |
WO (1) | WO2012041053A1 (ja) |
Families Citing this family (24)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN103305659B (zh) * | 2012-03-08 | 2016-03-30 | 宝山钢铁股份有限公司 | 磁性优良的无取向电工钢板及其钙处理方法 |
CN103509906B (zh) * | 2012-06-29 | 2016-01-20 | 宝山钢铁股份有限公司 | 磁性优良的无取向电工钢板的冶炼方法 |
JP5942712B2 (ja) * | 2012-09-06 | 2016-06-29 | 新日鐵住金株式会社 | スカム堰、薄肉鋳片の製造方法、薄肉鋳片の製造装置 |
CN102925795A (zh) * | 2012-10-23 | 2013-02-13 | 鞍钢股份有限公司 | 无取向电工钢中低牌号产品控制横纵向电磁性能的生产方法 |
CN104073714A (zh) * | 2013-03-28 | 2014-10-01 | 宝山钢铁股份有限公司 | 表面良好的高磁感低铁损无取向电工钢板及其制造方法 |
CN104164544A (zh) * | 2013-05-17 | 2014-11-26 | 宝山钢铁股份有限公司 | 一种无线状凸起缺陷的无取向电工钢板的制造方法 |
CN104726763B (zh) * | 2013-12-23 | 2017-04-12 | 鞍钢股份有限公司 | 一种电工钢的热轧方法 |
CN104073715B (zh) * | 2014-06-19 | 2016-04-20 | 马钢(集团)控股有限公司 | 一种高磁感无取向电工钢的制造方法 |
CN104342604B (zh) * | 2014-11-10 | 2016-11-30 | 五行科技股份有限公司 | 一种高强度带材制造方法 |
CN104789862A (zh) | 2015-03-20 | 2015-07-22 | 宝山钢铁股份有限公司 | 表面状态良好的高磁感低铁损无取向电工钢板及其制造方法 |
KR101901313B1 (ko) | 2016-12-19 | 2018-09-21 | 주식회사 포스코 | 무방향성 전기강판 및 그 제조방법 |
CN111719078B (zh) * | 2019-03-19 | 2021-06-15 | 江苏集萃冶金技术研究院有限公司 | 一种消除瓦楞状缺陷的无取向硅钢生产方法 |
CN109825775B (zh) * | 2019-04-04 | 2020-03-27 | 中山市中圣金属板带科技有限公司 | 一种冷轧无取向电工钢35wd1900及其生产方法 |
CN112430780B (zh) * | 2019-08-26 | 2022-03-18 | 宝山钢铁股份有限公司 | 一种含Cu高洁净度无取向电工钢板及其制造方法 |
KR20220124775A (ko) * | 2020-02-20 | 2022-09-14 | 닛폰세이테츠 가부시키가이샤 | 무방향성 전자 강판용 강판 |
CN111560554A (zh) * | 2020-05-06 | 2020-08-21 | 包头钢铁(集团)有限责任公司 | 一种稀土无取向硅钢的制备方法 |
CN111748740A (zh) * | 2020-06-30 | 2020-10-09 | 武汉钢铁有限公司 | 一种无瓦楞状缺陷且磁性优良的无取向硅钢及其生产方法 |
CN111961980B (zh) * | 2020-09-16 | 2022-06-07 | 内蒙古工业大学 | 一种csp流程无常化工艺生产薄规格中高牌号无取向硅钢的方法 |
CN115198203B (zh) * | 2021-04-09 | 2024-02-13 | 宝山钢铁股份有限公司 | 一种免常化中间退火的无取向电工钢板及其制造方法 |
CN115704073B (zh) * | 2021-08-09 | 2024-01-09 | 宝山钢铁股份有限公司 | 一种表面状态良好的无取向电工钢板及其制造方法 |
CN114369761B (zh) * | 2022-01-07 | 2022-11-25 | 山西太钢不锈钢股份有限公司 | 一种薄规格无取向硅钢及其制备方法 |
CN114393185B (zh) * | 2022-01-27 | 2023-08-15 | 马鞍山钢铁股份有限公司 | 一种提高连铸高拉速下无取向电工钢铸坯等轴晶率的方法 |
CN114854966B (zh) * | 2022-04-12 | 2024-05-10 | 湖南华菱涟钢特种新材料有限公司 | 电工钢及其制备方法和制品 |
CN116117096B (zh) * | 2023-01-04 | 2023-07-18 | 安庆新普电气设备有限公司 | 一种高等轴晶率无取向电工钢连铸坯及其制备方法 |
Family Cites Families (30)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS512289B2 (ja) | 1971-10-28 | 1976-01-24 | ||
JPS5037127B2 (ja) | 1972-07-08 | 1975-12-01 | ||
JPS5037132B2 (ja) | 1972-08-18 | 1975-12-01 | ||
JPS5238490B2 (ja) | 1972-08-23 | 1977-09-29 | ||
JPS532332A (en) * | 1976-06-29 | 1978-01-11 | Nippon Steel Corp | Production of nondirectional electrical steel sheet having excellent surface property |
JPS5314609A (en) | 1976-07-27 | 1978-02-09 | Nippon Steel Corp | Production of nondirectional electromagnetic steel sheet free from ridging |
JPS6169923A (ja) * | 1984-09-13 | 1986-04-10 | Kawasaki Steel Corp | 表面性状の良好な無方向性けい素鋼板の製造方法 |
JPS61127817A (ja) | 1984-11-26 | 1986-06-16 | Kawasaki Steel Corp | リジングの少ない無方向性けい素鋼板の製造方法 |
JPH0620593B2 (ja) * | 1989-01-20 | 1994-03-23 | 新日本製鐵株式会社 | 無方向性電磁鋼板用鋳片の製造方法 |
JPH0784617B2 (ja) * | 1989-03-24 | 1995-09-13 | 住友金属工業株式会社 | フェライト系ステンレス鋼板の製造方法 |
JP2536976B2 (ja) * | 1991-05-17 | 1996-09-25 | 新日本製鐵株式会社 | 表面性状および磁気特性の優れた無方向性電磁鋼板の製造方法 |
KR100240995B1 (ko) * | 1995-12-19 | 2000-03-02 | 이구택 | 절연피막의 밀착성이 우수한 무방향성 전기강판의 제조방법 |
JP4207231B2 (ja) * | 1997-08-08 | 2009-01-14 | Jfeスチール株式会社 | 無方向性電磁鋼板の製造方法 |
CN1258608A (zh) * | 1998-12-25 | 2000-07-05 | 傅元竹 | 单自动离合器 |
JP2000273549A (ja) * | 1999-03-25 | 2000-10-03 | Nkk Corp | 磁気特性の優れた無方向性電磁鋼板の製造方法 |
FR2818664B1 (fr) * | 2000-12-27 | 2003-12-05 | Usinor | Acier magnetique a grains non orientes, procede de fabrication de toles et toles obtenues |
KR20100072376A (ko) * | 2002-05-08 | 2010-06-30 | 에이케이 스틸 프로퍼티즈 인코포레이티드 | 무방향성 전기 강판의 연속 주조방법 |
DE10221793C1 (de) * | 2002-05-15 | 2003-12-04 | Thyssenkrupp Electrical Steel Ebg Gmbh | Nichtkornorientiertes Elektroband oder -blech und Verfahren zu seiner Herstellung |
JP4331969B2 (ja) * | 2003-05-06 | 2009-09-16 | 新日本製鐵株式会社 | 無方向性電磁鋼板の製造方法 |
CN1258610C (zh) * | 2003-05-12 | 2006-06-07 | 宝山钢铁股份有限公司 | 无瓦楞状缺陷的无取向电工钢板及其制造方法 |
CN1258608C (zh) * | 2003-10-27 | 2006-06-07 | 宝山钢铁股份有限公司 | 冷轧无取向电工钢的制造方法 |
KR100912974B1 (ko) * | 2004-11-04 | 2009-08-20 | 신닛뽄세이테쯔 카부시키카이샤 | 저철손 무방향성 전자기 강판 |
US7846271B2 (en) * | 2004-12-21 | 2010-12-07 | Posco Co., Ltd. | Non-oriented electrical steel sheets with excellent magnetic properties and method for manufacturing the same |
CN1796015A (zh) * | 2004-12-28 | 2006-07-05 | 宝山钢铁股份有限公司 | 薄板坯连铸连轧生产冷轧无取向电工钢的方法 |
CN100446919C (zh) * | 2005-06-30 | 2008-12-31 | 宝山钢铁股份有限公司 | 低铁损高磁感冷轧无取向电工钢板的生产方法 |
CN100999050A (zh) * | 2006-01-11 | 2007-07-18 | 宝山钢铁股份有限公司 | 低铁损高磁感冷轧无取向电工钢板的生产方法 |
CN100436631C (zh) * | 2006-05-18 | 2008-11-26 | 武汉科技大学 | 一种低碳高锰取向电工钢板及其制造方法 |
CN101139681B (zh) | 2007-10-26 | 2010-07-21 | 山西太钢不锈钢股份有限公司 | 中高牌号冷轧无取向硅钢及其制造方法 |
CN101306434B (zh) * | 2008-06-23 | 2012-05-30 | 首钢总公司 | 一种低碳低硅无铝半工艺无取向电工钢的制备方法 |
JP4510911B2 (ja) * | 2008-07-24 | 2010-07-28 | 新日本製鐵株式会社 | 高周波用無方向性電磁鋼鋳片の製造方法 |
-
2010
- 2010-09-30 CN CN2010102989655A patent/CN102443734B/zh active Active
-
2011
- 2011-04-14 WO PCT/CN2011/072766 patent/WO2012041053A1/zh active Application Filing
- 2011-04-14 JP JP2013530533A patent/JP2013540900A/ja active Pending
- 2011-04-14 KR KR1020137008046A patent/KR20130049822A/ko active Search and Examination
- 2011-04-14 MX MX2013003261A patent/MX357357B/es active IP Right Grant
- 2011-04-14 EP EP11827949.6A patent/EP2623626B1/en active Active
- 2011-04-14 RU RU2013114859/02A patent/RU2550440C2/ru active
- 2011-04-14 US US13/823,311 patent/US20130224064A1/en not_active Abandoned
Non-Patent Citations (1)
Title |
---|
None * |
Also Published As
Publication number | Publication date |
---|---|
JP2013540900A (ja) | 2013-11-07 |
US20130224064A1 (en) | 2013-08-29 |
WO2012041053A1 (zh) | 2012-04-05 |
EP2623626A1 (en) | 2013-08-07 |
CN102443734A (zh) | 2012-05-09 |
RU2550440C2 (ru) | 2015-05-10 |
KR20130049822A (ko) | 2013-05-14 |
MX2013003261A (es) | 2013-05-01 |
EP2623626A4 (en) | 2017-11-22 |
CN102443734B (zh) | 2013-06-19 |
RU2013114859A (ru) | 2014-11-10 |
MX357357B (es) | 2018-07-05 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP2623626B1 (en) | Non-oriented electric steel plate without corrugated fault and production method thereof | |
JP6580700B2 (ja) | 表面状態が良好な高磁束密度・低鉄損・無方向性電磁鋼板及びその製造方法 | |
TWI472626B (zh) | 方向性電磁鋼板的製造方法及方向性電磁鋼板的再結晶退火設備 | |
JP2013540900A5 (ja) | ||
JP7454646B2 (ja) | 高磁気誘導方向性ケイ素鋼およびその製造方法 | |
WO2014027452A1 (ja) | 無方向性電磁鋼板の製造方法 | |
WO2011111862A1 (ja) | 方向性電磁鋼板の製造方法 | |
CN104073714A (zh) | 表面良好的高磁感低铁损无取向电工钢板及其制造方法 | |
US20140377124A1 (en) | Non-Oriented Electrical Steel Plate and Manufacturing Process Therefor | |
CN100436042C (zh) | 一种薄板坯工艺高磁感取向电工钢板及其制造方法 | |
JP6079580B2 (ja) | 方向性電磁鋼板の製造方法 | |
CN103834908A (zh) | 一种提高取向硅钢电磁性能的生产方法 | |
US4437909A (en) | Process for producing a grain-oriented silicon steel sheet or strip having excellent magnetic properties | |
CN111719078B (zh) | 一种消除瓦楞状缺陷的无取向硅钢生产方法 | |
US5330586A (en) | Method of producing grain oriented silicon steel sheet having very excellent magnetic properties | |
JP5920387B2 (ja) | 方向性電磁鋼板の製造方法 | |
CN110640104A (zh) | 一种磁性能优良的无取向电工钢板及其制造方法 | |
JP7378585B2 (ja) | 無方向性電磁鋼板及びその製造方法 | |
JP4279993B2 (ja) | 一方向性珪素鋼板の製造方法 | |
JPH03229820A (ja) | 無方向性電磁鋼板の製造方法 | |
JP6056675B2 (ja) | 方向性電磁鋼板の製造方法 | |
CN108431244B (zh) | 取向电工钢板及其制造方法 | |
JP4258156B2 (ja) | 方向性電磁鋼板およびその製造方法 | |
KR100240984B1 (ko) | 0.5밀리 두께의 방향성 전기강판 제조방법 | |
CN104878288A (zh) | 一种控制硅钢瓦楞缺陷的方法 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
17P | Request for examination filed |
Effective date: 20130304 |
|
AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
DAX | Request for extension of the european patent (deleted) | ||
RA4 | Supplementary search report drawn up and despatched (corrected) |
Effective date: 20171023 |
|
RIC1 | Information provided on ipc code assigned before grant |
Ipc: C21D 8/02 20060101ALI20171017BHEP Ipc: B22D 11/22 20060101ALI20171017BHEP Ipc: C21D 8/12 20060101ALI20171017BHEP Ipc: C22C 38/06 20060101AFI20171017BHEP Ipc: C22C 38/02 20060101ALI20171017BHEP Ipc: H01F 1/16 20060101ALI20171017BHEP Ipc: B22D 11/18 20060101ALI20171017BHEP Ipc: C22C 38/04 20060101ALI20171017BHEP Ipc: C21D 6/00 20060101ALI20171017BHEP Ipc: C22C 38/00 20060101ALI20171017BHEP |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: EXAMINATION IS IN PROGRESS |
|
17Q | First examination report despatched |
Effective date: 20181019 |
|
GRAP | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOSNIGR1 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: GRANT OF PATENT IS INTENDED |
|
INTG | Intention to grant announced |
Effective date: 20190731 |
|
GRAS | Grant fee paid |
Free format text: ORIGINAL CODE: EPIDOSNIGR3 |
|
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: THE PATENT HAS BEEN GRANTED |
|
AK | Designated contracting states |
Kind code of ref document: B1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: FG4D |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: EP |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: FG4D |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R096 Ref document number: 602011063544 Country of ref document: DE |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: REF Ref document number: 1204270 Country of ref document: AT Kind code of ref document: T Effective date: 20191215 |
|
REG | Reference to a national code |
Ref country code: NL Ref legal event code: MP Effective date: 20191120 |
|
REG | Reference to a national code |
Ref country code: LT Ref legal event code: MG4D |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: NL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20191120 Ref country code: FI Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20191120 Ref country code: BG Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200220 Ref country code: LT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20191120 Ref country code: ES Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20191120 Ref country code: LV Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20191120 Ref country code: SE Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20191120 Ref country code: GR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200221 Ref country code: NO Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200220 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: HR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20191120 Ref country code: RS Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20191120 Ref country code: IS Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200320 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: AL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20191120 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: CZ Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20191120 Ref country code: RO Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20191120 Ref country code: PT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200412 Ref country code: EE Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20191120 Ref country code: DK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20191120 |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: UEP Ref document number: 1204270 Country of ref document: AT Kind code of ref document: T Effective date: 20191120 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R097 Ref document number: 602011063544 Country of ref document: DE |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: SK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20191120 Ref country code: SM Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20191120 |
|
PLBE | No opposition filed within time limit |
Free format text: ORIGINAL CODE: 0009261 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT |
|
26N | No opposition filed |
Effective date: 20200821 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: PL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20191120 Ref country code: SI Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20191120 Ref country code: MC Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20191120 |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: PL |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: LU Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20200414 Ref country code: LI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20200430 Ref country code: CH Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20200430 |
|
REG | Reference to a national code |
Ref country code: BE Ref legal event code: MM Effective date: 20200430 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: BE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20200430 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20200414 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: TR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20191120 Ref country code: MT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20191120 Ref country code: CY Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20191120 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: MK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20191120 |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: PLFP Year of fee payment: 13 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: GB Payment date: 20230330 Year of fee payment: 13 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: IT Payment date: 20230412 Year of fee payment: 13 Ref country code: FR Payment date: 20230411 Year of fee payment: 13 Ref country code: DE Payment date: 20230331 Year of fee payment: 13 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: AT Payment date: 20230412 Year of fee payment: 13 |