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
  • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
  • C21D8/0273—Final recrystallisation annealing
• • C—CHEMISTRY; METALLURGY
  • 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
  • C21D8/1244—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
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
• • 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
  • C22C38/004—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
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
• • 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
• • 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
  • H01F1/147—Alloys characterised by their composition
  • H01F1/14766—Fe-Si based alloys
  • H01F1/14775—Fe-Si based alloys in the form of sheets

Definitions

• the invention relates to a non-grain oriented electrical steel strip or sheet for electrical applications, an electrical component made from such an electrical steel strip or sheet, and a method for producing an electrical steel strip or sheet.
• a NO electric steel strip or sheet having a yield strength of at least 60 kg-f / mm 2 (about 589 MPa) and made of a steel containing, in addition to iron and unavoidable impurities (in% by weight) to to 0.04% C, 2.0 - less than 4.0% Si, up to 2.0% Al, up to 0.2% P and at least one element from the group "Mn, Ni", wherein the Sum of the contents of Mn and Ni is at least 0.3% and at most 10%.
• the thus composed steel is according to the US 5,084,112 poured into slabs, which are then hot rolled into a hot strip, which optionally annealed, then pickled and then cold rolled to a cold-rolled strip of a given final thickness. Finally, the cold strip obtained is subjected to a recrystallizing annealing, in which it is annealed at a temperature of at least 650 ° C, but less than 900 ° C annealing temperature.
• the object of the invention was to provide a NO electrical steel strip or sheet and a manufactured from such a sheet or strip component for electrical applications, the increased strength, in particular a higher yield strength, and at the same time has good magnetic properties, in particular a low loss of magnetization at high frequencies.
• a method for producing such a NO electrical strip or sheet should be given.
• the solution according to the invention of the above-mentioned object with respect to the component for electrical applications is that such a component is produced from an electrical steel sheet or strip according to the invention.
• a non-grain-oriented electrical steel strip or sheet for electrotechnical applications obtained in accordance with the invention is thus made from a steel consisting of (in% by weight) 1.0-4.5% Si, in particular 2.4-3.4% Si, to to 2.0% Al, in particular up to 1.5% Al, up to 1.0% Mn, up to 0.01% C, in particular up to 0.006%, particularly advantageously up to 0.005% C, up to 0, 01% N, in particular up to 0.006% N, up to 0.012% S, in particular up to 0.006% S, 0.1 - 0.5% Ti, and 0.1 - 0.3% P and the remainder of iron and unavoidable Impurities is, wherein for the ratio% Ti /% P of Ti content% Ti to P content% P applies 1 . 0 ⁇ % Ti / % P ⁇ 2 . 0th
• the invention uses FeTi phosphides (FeTiP) to increase the strength.
• FeTiP FeTi phosphides
• Form precipitates and increase the strength of NO electrical steel strip or sheet by particle hardening.
• a particularly practical embodiment of the inventive alloy of an electrical strip or sheet is obtained when the contents of the steel of Si, C, N, S, Ti and P are each optionally (in wt .-%) to 2.4 - 3, 4% Si, up to 0.005% C, up to 0.006% N, up to 0.006% S, up to 0.5% Ti or up to 0.3% P.
• up to 2.0% Al and up to 1.0% Mn can be present in the steel according to the invention.
• the invention uses to increase the strength instead of the carbonitrides usually used for FeTi phosphides. In this way, on the one hand the magnetic aging can be avoided, which can occur as a result of high C and / or N contents.
• the ratio of Ti content% Ti to P content% P satisfies the condition specified in claim 1, according to which the ratio of the titanium content to the phosphorus content of the electrical steel strip or sheet according to the invention is greater than or equal to 1.0 and at the same time less than or equal to 2.0.
• the electrical steel sheet or strip assembled in accordance with the invention has a sufficient number and sufficient distribution of FeTiP particles, in addition to sufficiently high strength also to ensure good electromagnetic properties.
• a harmful excess of phosphorus is avoided, which would lead to embrittlement in the electrical steel strip or sheet according to the invention.
• an excessive excess of titanium is avoided by the ratio predetermined according to the invention. Such an excess of Ti could lead to the formation of titanium nitrides, which would adversely affect the magnetic properties of the electrical steel strip or sheet.
• the invention is based on the recognition that a maximum of the present invention used effect of the simultaneous presence of Ti and P is achieved in a non-grain oriented electrical sheet or strip according to the invention, if its contents of Ti and P with the smallest possible deviations of the stoichiometric ratio of 1.55.
• a particularly important embodiment of the invention provides that the ratio% Ti /% P of the Ti content% Ti to the P content% P applies 1 . 43 ⁇ % Ti / % P ⁇ 1 . 67th
• the FeTiP particles made possible by the steel composition according to the invention regularly have a diameter which is much smaller than 0.1 ⁇ m. This takes into account the effect that although the strength of a material increases with the number of lattice defects, such as foreign atoms, dislocations, grain boundaries or particles of another phase, these lattice defects have a negative influence on the magnetic characteristics of a material.
• the negative influence is, as known per se, the strongest when the particle size is in the range of the Bloch wall thickness (transition region between magnetic domains with different magnetization), d. H. is about 0.1 microns.
• This negative influence occurs in an electrical steel sheet according to the invention at most in a highly minimized form.
• FeTiP particles may also be present in the material according to the invention which are significantly larger than 0.1 ⁇ m. However, these influence the properties of a product according to the invention at most to a negligible extent.
• Micro-alloying elements such as Nb, Zr or V, are no longer needed in conjunction with high levels of carbon or nitrogen. Higher contents of C and N have a negative impact on the magnetic properties of the correspondingly assembled non-grain oriented electrical steel strip or sheet because they entail undesirable magnetic aging of the materials during practical use. According to the invention, therefore, the increase in strength is achieved by particle hardening, namely by the presence of FeTiP precipitates, but not with the help of carbon and / or nitrogen whose presence would lead to aging effects.
• electrical tapes or sheets composed according to the present invention regularly have remagnetization losses P 1.0 / 400 at a polarization of 1.0 Tesla and a frequency of 400 Hz at a thickness of the electrical steel or sheet of 0.5 mm of at most 65 W / kg and at a thickness of 0.35 mm at most 45 W / kg.
• they regularly increase the yield strength of at least 60 MPa.
• the inventive method is designed so that it enables the reliable production of a non-grain-oriented electrical tape or sheet according to the invention.
• a hot strip composed in the manner explained above for the non-grain-oriented electrical sheet or strip according to the invention is provided, which is subsequently cold-rolled and subjected to a final annealing as a cold-rolled strip.
• the final annealed cold-rolled strip obtained after the final annealing then represents the electrical strip or sheet assembled and obtained according to the invention.
• the manufacture of the hot strip provided according to the invention can be carried out conventionally as far as possible.
• a molten steel having a composition corresponding to the specification according to the invention (Si: 1.0-4.5%, Al: up to 2.0%, Mn: up to 1.0%, C: up to 0.01% , N: up to 0.01%, S: up to 0.012%, Ti: 0.1-0.5%, P: 0.1-0.3%, remainder iron and unavoidable impurities, data in% by weight.
• % wherein for the ratio% Ti /% P of the Ti content% Ti to the P content% P is 1.0 ⁇ % Ti /% P ⁇ 2.0) are melted and cast to a starting material, in which it in conventional manufacturing can be a slab or thin slab.
• a starting material in which it in conventional manufacturing can be a slab or thin slab.
• the precipitation formation processes according to the invention take place only after solidification, it is in principle also possible to cast the molten steel into a cast strip, which is then hot rolled into a hot strip.
• the starting material thus produced can then be brought to a pre-material temperature of 1020-1300 ° C.
• the starting material is, if necessary, reheated or kept at the respective target temperature by utilizing the casting heat.
• the thus heated starting material can then be hot rolled to a hot strip having a thickness which is typically 1.5-4 mm, in particular 2-3 mm.
• the hot rolling starts in a conventional manner at a hot rolling start temperature of 1000 - 1150 ° C and ends with a hot rolling end temperature of 700 - 920 ° C, in particular 780 - 850 ° C.
• the resulting hot strip can then be cooled to a coiling temperature and coiled into a coil.
• the coiler temperature is ideally chosen so that precipitation of the Fe-Ti phosphides is avoided in order to avoid problems during subsequent cold rolling.
• the reel temperature for this purpose, for example, at most 700 ° C.
• the hot strip can be subjected to a hot strip annealing.
• the supplied hot strip is cold rolled to a cold strip having a thickness typically in the range of 0.15-1.1 mm, especially 0.2-0.65 mm.
• the final annealing contributes significantly to the formation of FeTiP particles used in the present invention for increasing the strength.
• By varying the annealing conditions of the final annealing it is possible to optimize the material properties optionally in favor of a higher strength or a lower loss of core loss.
• Non-grain-oriented electrical sheets or tapes according to the invention having yield strengths of between 390 and 550 MPa and remagnetization losses P of 1.0 / 400 , which are less than 27 W / kg at a strip thickness of 0.35 mm and a strip thickness of 0, 5 mm less than 47 W / kg, can be particularly reliable achieved in accordance with a first variant of the method according to the invention that the cold strip in the course of the final annealing completed in a continuous furnace two-stage Kurzzeitglühung in which the cold strip in the first annealing stage d.1) first annealed over an annealing period of 1 - 100 s at an annealing temperature of at least 900 ° C and at most 1150 ° C and then in a second annealing stage d.2) over an annealing period of 30 - 120 s at an annealing temperature of 500 - 850 ° C.
• the already existing FeTiP precipitates are dissolved in the first annealing stage d.1) and a complete recrystallization of the microstructure is achieved.
• the second annealing stage d.2) then the targeted excretion of FeTiP particles.
• the long-term annealing optionally carried out in the hood furnace may be followed by the two-stage short-time annealing, in which the cold strip is baked at temperatures of 550-660 ° C over a Annealing time of 0.5 - 20 h is annealed.
• the achievable by this additional Langzeitglühung increase in yield strength is regularly at least 50 MPa.
• Non-grain oriented electrical sheets or tapes having yield strengths of 500-800 MPa and remagnetization losses P 1.0 / 400 of less than 45 W / kg for 0.35 mm thick electrical sheets or tapes can also be produced thereby according to a second variant of the method of the invention in that the final annealing is carried out as a short-time annealing, in which the cold strip is annealed in the continuous furnace for an annealing period of 20 to 250 seconds at an annealing temperature of 750 to 900 ° C. Due to the lower annealing temperature in this case no complete recrystallization of the microstructure is achieved. However, the desired strength-increasing FeTiP precipitates form.
• a short-time annealing in the continuous furnace can also be carried out, in which the respective cold-rolled strip is annealed at 750 ° C.-900 ° C. over an annealing period of 20-250 seconds.
• This additional Kurzzeitglühung can improve the degree of recrystallization of the structure. Along with this, an improvement in the loss of magnetization is to be expected.
• the cold strip in the course of the third variant of the inventive method between the long-term annealing and the Kurzzeitglühung optionally a deformation with a degree of deformation of at least 0.5 % and at most 12%.
• a forming step which is usually carried out as an additional cold-rolling step, furthermore contributes to the improvement of the flatness of the non-grain-oriented electrical sheet or strip obtained at the end of this process variant according to the invention.
• the effects achieved with the optionally additionally carried out cold deformation can be achieved particularly reliably if the degrees of deformation of the cold deformation amount to 1 to 8%.
• the final annealing may be followed by a smoothing pass carried out in a conventional manner.
• the obtained, non-grain oriented electrical steel strip or sheet material may be finally subjected to a conventional flash annealing.
• this flash annealing can still be performed in the coil of the manufacturer of NO-electric strip or sheet according to the invention, or it can first be divided from the produced in the inventive manner electrical strip or sheet, the blanks processed at the final processor, then the Be subjected to flash annealing.
• the slabs were brought to 1250 ° C temperature and with a hot rolling start temperature of 1020 ° C and a hot rolling end temperature of 840 ° C to hot-rolled into a 2 mm thick hot strip.
• the respective hot strip has been cooled to a reel temperature T reel . Subsequently, a typical cooling in the coil has been simulated.
• the samples produced from the steel according to the invention have somewhat of 3.9-4.8 W / kg for 0.5 mm thick sheets and less than 3.7 W / kg for 0.35 mm thick sheets higher Ummagnetleitersmanne P 1.5 than that from the Reference steel produced samples. Again, the reel temperature has no significant influence.
• the magnetic reversal losses P 1.0 for the invention and the reference samples are very close to each other.
• the samples with the higher temperature T low of 700 ° C show here in the case of 0.5 mm thick sheets with less than 39 W / kg at 400 Hz and less than 180 W / kg at 1 kHz lower Ummagnetleitersppe P 1.0 than the reference material. In the case of the 0.35 mm thick sheets, the same loss of magnetization is achieved as with the reference material.
• the slabs were reheated to 1250 ° C and then hot rolled to hot strip with a hot strip thickness of 2.1 mm and 2.4 mm, respectively.
• the hot rolling start temperature was in each case 1020 ° C.
• the hot rolling end temperature was in each case 840 ° C.
• the resulting hot strips were then reeled at a reel temperature of 620 ° C.
• the hot strips thus obtained were cold rolled without prior hot strip annealing to 0.35 mm thick cold strip.
• a two-stage Kurzzeitglühung has been completed in a continuous furnace.
• annealing times t G1 are met and there also mentioned respective maximum annealing temperatures T max1 achieved while the second stage respectively in the annealing times t G2 also shown in Table 5 at the same there maximum annealing temperatures T max2 has been completed.
• the mechanical and magnetic properties determined on the thus obtained final annealed NO-electric sheet samples in transverse direction Q and longitudinal direction L are also listed in Table 5.
• a sample of the finally heat-treated samples according to the first variant has subsequently been subjected to additional long-term annealing in a hood furnace.
• the annealing times t GH and maximum annealing temperatures T maxH are shown in Table 6.
• the mechanical and magnetic properties determined on the additionally long-time annealed NO electric sheet in the transverse direction Q and in the longitudinal direction L are likewise recorded in Table 6. It can be seen that the supplementary long-term annealing achieved a significant increase in the yield strength R e and the tensile strength R m , whereas the magnetic properties did not deteriorate significantly.
• samples of the cold strips have been subjected to long-term annealing at different temperatures T maxH in the hood furnace over an annealing time t GH .
• the respective temperatures T maxH and the respective annealing time t GH are listed in Table 7.
• Table 7 also shows the mechanical and magnetic properties determined on the long-time-annealed NO-electric sheet samples obtained in the transverse direction Q and in the longitudinal direction L.
• samples of the cold strips have been subjected to single-stage short-time annealing at different temperatures T maxD in the continuous furnace over an annealing time t GD .
• the respective temperatures T maxD and the respective annealing time t GD are listed in Table 8.
• Table 8 also shows the mechanical and magnetic properties determined on the long-time-annealed NO electric-sheet samples obtained in the transverse direction Q and in the longitudinal direction L.
• the invention accordingly relates to a non-grain-oriented electrical steel sheet or sheet comprising, in addition to iron and unavoidable impurities (in% by weight) Si: 1.0-4.5%, Al: up to 2.0%, Mn: up to 1.0%, C: up to 0.01%, N: up to 0.01%, S: up to 0.012%, Ti: 0.1-0.5%, P: 0.1-0 , 3%, wherein the ratio% Ti /% P of the Ti content% Ti to the P content% P is 1.0 ⁇ % Ti /% P ⁇ 2.0.
• An inventive non-grain oriented electrical steel strip or sheet and made of such a sheet or strip components for electrical applications are characterized by increased Strengths and at the same time good magnetic properties.
• the NO sheet or strip according to the invention can be produced by cold-rolling a hot strip consisting of a steel with the above-mentioned composition into a cold strip and subjecting this cold strip to a final annealing.
• the invention provides various variants of this final annealing available. Table 1 variants Si al Mn C N S Ti P TiP 2, 99 0,004 0.58 0,006 0.0021 ⁇ 0.001 0.148 0,100 Ref 2.96 0,006 0, 64 0,006 0.0021 0.001 0.001 0,004 Residual iron and unavoidable impurities, Data in% by weight stolen According to the invention? Hot strip annealing?

Landscapes

• 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)
• Electromagnetism (AREA)
• Manufacturing & Machinery (AREA)
• Dispersion Chemistry (AREA)
• Power Engineering (AREA)
• Manufacturing Of Steel Electrode Plates (AREA)
• Soft Magnetic Materials (AREA)
• Heat Treatment Of Sheet Steel (AREA)

Priority Applications (12)

Applications Claiming Priority (1)

Publications (2)

Family

ID=47358495

Family Applications (1)

Country Status (12)

Cited By (5)

Families Citing this family (10)

Citations (5)

Family Cites Families (9)

• 2012
  • 2012-01-05 EP EP12150315.5A patent/EP2612942B1/fr active Active
  • 2012-01-05 PL PL12150315T patent/PL2612942T3/pl unknown
  • 2012-12-18 CN CN201280019922.6A patent/CN103687974B/zh active Active
  • 2012-12-18 US US14/118,720 patent/US9637805B2/en active Active
  • 2012-12-18 BR BR112013020464-8A patent/BR112013020464B1/pt not_active IP Right Cessation
  • 2012-12-18 MX MX2013009017A patent/MX2013009017A/es active IP Right Grant
  • 2012-12-18 RU RU2013144581/02A patent/RU2605730C2/ru active
  • 2012-12-18 KR KR1020137025479A patent/KR101587967B1/ko active IP Right Grant
  • 2012-12-18 WO PCT/EP2012/075966 patent/WO2013102556A1/fr active Application Filing
  • 2012-12-18 AU AU2012364385A patent/AU2012364385B2/en not_active Ceased
  • 2012-12-18 CA CA2825852A patent/CA2825852C/fr not_active Expired - Fee Related
  • 2012-12-18 JP JP2014523348A patent/JP5750196B2/ja active Active

Patent Citations (5)

Non-Patent Citations (1)

Also Published As

Similar Documents

Legal Events