EP2366035A1 - Feuillard d'acier au manganèse à teneur accrue en phosphore et son procédé de fabrication - Google Patents

Feuillard d'acier au manganèse à teneur accrue en phosphore et son procédé de fabrication

Info

Publication number
EP2366035A1
EP2366035A1 EP09760726A EP09760726A EP2366035A1 EP 2366035 A1 EP2366035 A1 EP 2366035A1 EP 09760726 A EP09760726 A EP 09760726A EP 09760726 A EP09760726 A EP 09760726A EP 2366035 A1 EP2366035 A1 EP 2366035A1
Authority
EP
European Patent Office
Prior art keywords
steel strip
manganese steel
cold
austenitic manganese
rolled austenitic
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.)
Granted
Application number
EP09760726A
Other languages
German (de)
English (en)
Other versions
EP2366035B1 (fr
Inventor
Reinhold Schneider
Ludovic Samek
Enno Arenholz
Klemens Mraczek
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Voestalpine Stahl GmbH
Original Assignee
Voestalpine Stahl GmbH
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Voestalpine Stahl GmbH filed Critical Voestalpine Stahl GmbH
Publication of EP2366035A1 publication Critical patent/EP2366035A1/fr
Application granted granted Critical
Publication of EP2366035B1 publication Critical patent/EP2366035B1/fr
Not-in-force legal-status Critical Current
Anticipated expiration legal-status Critical

Links

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
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • 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
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite

Definitions

  • the invention relates to an austenitic manganese steel strip and to a method for producing austenitic manganese steel strips. Furthermore, the invention relates to a manganese steel sheet with a deformed, in particular stretched or deep-drawn sheet steel section.
  • Manganese austenites are lightweight structural steels that are particularly strong and elastic at the same time.
  • the weight reduction afforded by the higher strength makes manganese austenite a material of great potential in the automotive industry. Because through lighter bodies fuel consumption can be reduced, with a high elasticity and stability for the production of the body parts and their crash behavior are important.
  • TRIP steel which are increasingly used in the automotive industry.
  • High-alloyed TRIP steels reach high tensile strengths of up to more than 1000 MPa and can have elongations of up to about 30%. Due to these high mechanical properties thinner plates and thus a reduction in body weight can be achieved in vehicle construction.
  • TRIP steel consists of several phases of iron-carbon alloys, mainly ferrite, bainite and carbon-rich residual austenite.
  • the TRIP effect is based on the deformation-induced transformation of residual austenite into martensite. This reshaping of the crystal structure results in a simultaneous increase in the strength and formability during product production or during product use in the event of a crash.
  • the TRIP effect can be specifically influenced by admixing the alloying elements aluminum and silicon.
  • TWIP The recently developed TWIP steels differ from TRIP steels in that they have a higher elongation at break (50% and more).
  • TWIP stands for
  • TWinning Induced Plasticity ie a plasticity induced by twinning.
  • the particular ductility of TWIP steels can be caused by different mechanisms in the crystal structure.
  • the extensibility can be promoted by lattice defects in the crystal structure, at which the crystal structure can be folded in a deformation-induced manner, wherein the folding mechanism proceeds at a mirror plane and regularly produces mirrored crystal regions (so-called twins). Different types of twins can be distinguished.
  • further effects such as the occurrence of slip bands can influence the mechanical properties. Due to their high ductility, TWIP steels are excellently suited for the production of metal sheets in the vehicle industry, especially for accident-relevant areas of the body.
  • TWIP steels have an austenitic structure and are characterized by a high manganese content (usually over 25%) and relatively high alloying additions of aluminum and silicon.
  • One object of the invention is to provide a steel with improved mechanical properties.
  • good weldability of the steel and / or good formability should be achievable.
  • the invention aims to provide a method for producing a steel with improved mechanical properties, in particular high ductility in combination specify with high tensile strength, and in particular a good weldability and a good formability.
  • the steel according to the invention is characterized, inter alia, by the fact that with a carbon content in wt .-% of about 0.4% ⁇ C ⁇ 1.2%, a manganese content of about 12.0% ⁇ Mn ⁇ 25.0 % is available.
  • the percentages of chemical constituents in this document always refer to percentages by weight.
  • Phosphorus which increases the yield strength or tensile strength, reduces the elongation at break, promotes brittleness, lowers the austenite stability, hampers cementitious precipitation and usually reduces weldability, according to the invention in a relatively high proportion of at least 0.01%. to be alloyed. It turned out that with a largely omission of the alloying element aluminum (Al ⁇ 0.05%) with this alloying concept, high mechanical properties and a surprisingly good weldability with very good formability of the produced manganese steel strip can be achieved.
  • micro-twin formation i.e., the formation of small twins of small thickness
  • the high density of micro-twins found after forming (e.g., thermoforming) and their small thickness compared to the density and thickness of the micro-twins in conventional high manganese steel results in an increase in elongation at break. This is at least partly due to the fact that with the density of the twins the number of dislocation obstacles increases significantly.
  • the average thickness of the micro-twins lay with samples of the manganese steel strip according to the invention after they had been subjected to a forming process, preferably below 30 nm, in particular below 20 nm and in particular below 10 nm.
  • Gemini with a thickness of less than 10 nm also become referred to as nano-twins.
  • nano-twins After the deformation stress, in comparison to the usual density of twins, in particular a significantly increased density of nano-twins was present. It is believed that as the phosphorus content is increased and the stacking fault energy decreased, the density of the micro-twins, and especially the nano-twins, increases. These act directly on the ductility of the material and offer an unusual very high elongation in combination with high tensile strength.
  • Solid solution hardening is caused by high levels of interstitially dissolved alloying elements such as P and C. As a result, high strengths (in particular greater than
  • Dynamic strain aging The occurrence of dynamic strain aging is due to the high content of interstitially dissolved alloying elements in the steel and can be recognized by the stress-strain curves. This effect can make an additional contribution to improving the strength and elongation at break of the material.
  • the bake-hardening effect can also be used to increase the yield strength.
  • the bake hardening values were determined according to the European standard EN 10325.
  • the high levels of interstitially dissolved alloying elements ensure an increased bake-hardening potential and can further improve the mechanical properties of the final product.
  • the manganese content of an austenitic manganese steel strip according to the invention may preferably be in the range of 14% ⁇ Mn ⁇ 18.0%, in particular 14% ⁇ Mn ⁇ 16.5%.
  • the grain size can be influenced in a targeted manner by the ratio of N to Al.
  • AlN aluminum nitride
  • a high particle size can be made possible with an austenitic manganese steel strip.
  • the proportion of Al in the alloying concept pursued here can be kept very low, since much carbon is available for the deoxidation of the liquid steel.
  • the manganese steel according to the invention can have the smallest possible proportion of aluminum, which is limited only by unavoidable impurities in the production process (that is, no aluminum addition). In the case of the steel strip according to the invention, this enables maximum grain size growth during recrystallization (that is to say during hot rolling or annealing).
  • phosphorus contents of 0.03% ⁇ P, in particular 0.05% ⁇ P, 0.06% ⁇ P, 0.07% ⁇ P, 0.08% ⁇ P and also 0.10% ⁇ P are used. It may even be provided a phosphorus content 0.20% ⁇ P.
  • a high phosphorus content can increase the tensile strength and especially the yield strength at higher particle sizes. Surprisingly, no significant reduction in elongation at break and no significant deterioration in weldability were observed with an increase in the phosphorus content.
  • the mean grain size in the metal structure the tensile strength and the yield strength as well as the elongation at break of the produced steel strip can be changed in a targeted manner. The larger the grain, the lower the tensile strength as well as the yield strength and the higher the
  • Elongation at break It is possible to set average particle sizes of more than 5 ⁇ m or more than 10 ⁇ m. In particular, it can be provided that in the hot-rolled austenitic manganese steel a large average grain size of more than 13 microns, especially about 18 microns is set, and that in the cold-rolled austenitic manganese steel a large average grain size of more than 15 microns, especially about 20 microns is set.
  • silicon Similar to aluminum, silicon also impedes the precipitation of carbides such as cementite ((Fe, Mn) 3 C), which occurs during hot rolling and annealing. As cementite precipitation lowers the elongation at break, it can be expected that the elongation at break can be increased by adding silicon.
  • carbides such as cementite ((Fe, Mn) 3 C)
  • the manganese steel according to the invention preferably has a very low silicon content (Si ⁇ 1.0%, in particular Si ⁇ 0.2%, more preferably Si ⁇ 0.05%), which may be limited only by unavoidable impurities in the production process is (ie in this case no silicon addition, the Si content may then be below Si ⁇ 0.03%).
  • silicon has an influence on deformation mechanisms. Silicon impairs the formation of twins, ie a low silicon concentration facilitates the formation of twins and possibly especially the formation of small micro-twins or nano-twins.
  • the silicon content of the manganese steel of the present invention can be set low, preferably as low as possible.
  • the silicon content can be kept very low, since much carbon is available for the deoxidation of the liquid steel, and because the strength of the steel (silicon causes an increase in strength) by other measures such as high concentrations of C and / or P is guaranteed.
  • Niobium (Nb), vanadium (V) and titanium (Ti) are elements that form precipitates (carbides, nitrides, carbonitrides) and may optionally be added to improve strength through precipitation hardening.
  • these elements have a grain-fine effect, which is why their
  • Concentration should be kept low, if a high grain size should be guaranteed.
  • Nickel can stabilize the austenite phase (so-called ⁇ -stabilizer). Nickel may optionally be added in larger amounts (e.g., over 1% to 5% or even 10%).
  • the solid solubility enhancer (chromium (Cr)) stabilizes the ⁇ -ferrites. Additions of chromium up to 10% by weight prefer the formation of ⁇ -martensite and / or ⁇ '-martensite, resulting in higher tensile strength and lower ductility.
  • the proportion of chromium should therefore be limited. Preferably, e.g. Cr ⁇ 5%, in particular Cr ⁇ 0.2%.
  • Molybdenum (Mo) and tungsten (W) also show a grain refining effect.
  • Tungsten has a high affinity for carbon and forms the hard and very stable carbides W 2 C and WC steel.
  • the proportion of tungsten should be limited.
  • Tungsten is an even better solid solubility enhancer than chromium and also forms carbides (but to a lesser extent than chromium).
  • Mo ⁇ 2%, in particular Mo ⁇ 0.02% can be set.
  • the grain size of a hot-rolled steel strip is also greatly influenced by the final rolling temperature during hot rolling.
  • the steel strip according to the invention can with a final rolling temperature between 75O 0 C to 1050 0 C, preferably be- see 800 0 C and 900 0 C, are rolled.
  • the choice of the final rolling temperature allows the average particle size to be set.
  • the tensile strength of the hot-rolled steel may preferably be above 1050 MPa.
  • Cold rolling can increase the mechanical properties of the hot rolled austenitic manganese steel strip.
  • the grain size of a cold-rolled steel strip is strongly influenced by the annealing temperature.
  • the annealing performed after the cold rolling can be carried out, for example, at an annealing temperature between 75O 0 C and 1050 0 C, and in particular the annealing temperature can be greater than 900 0 C.
  • Tensile strengths of more than 1100 MPa, in particular more than 1200 MPa can be achieved with an elongation at break of more than 75%, in particular over 80%.
  • An inventive manganese steel sheet having the said chemical compositions has a formed, in particular stretched or deep-drawn sheet steel section whose microstructure micro twins having an average thickness of less than 30 nm, in particular less than 20 nm and nano-twins having an average thickness of less than 10 nm.
  • these micro- and nano-twins form during the reforming process, whereby the high mechanical properties of the probably derived - at least in part - from this deformation mechanism.
  • the semifinished product is heated to a temperature above HOO 0 C after casting, a semifinished product made of steel.
  • the heated semi-finished product is rolled with a final rolling temperature between 750 0 C and 1050 0 C, preferably between 800 0 C and 900 0 C.
  • the rolled steel strip is cooled at a rate of 20 ° C./s or higher.
  • rapid cooling of the hot rolled steel strip is performed at a rate of 50 ° C / s or higher, more preferably 200 ° C / s or higher.
  • Rapid cooling helps to provide high solids solubility of the E, C, N and P elements in the granules. To put it bluntly, the rapid cooling leads to a "freezing" of the dissolved elements without or with only little excretion formation. In other words, precipitate formation can be largely prevented by rapid cooling. In particular, the occurrence of grain boundary carbides as well as embrittlement (grain boundary segregation) of the steel structure caused by high phosphorus contents can be prevented by a rapid cooling. The higher the cooling rate, the better and smoother carbon and phosphorus can be kept in solution. Cooling rates of over 100 ° C / s to 400 ° C / s were used. Cooling rates of more than 400 ° C / s to even more than 600 ° C / s are also possible. If necessary, before the rapid cooling an intermediate phase of several seconds, in particular 1 to 4 seconds, persist, in which the
  • the hot-rolled steel strip is cold-rolled and then annealed for recrystallization.
  • high reduction of thickness in the range of more than 45%, in particular more than 60%, particularly preferably more than 80%, is preferably carried out by using high radial forces.
  • the annealing temperature can be between 750 0 C and 1150 0 C and in particular greater than 900 0 C.
  • the grain size can be changed again, after annealing, a grain size of about 15 microns, especially about 20 microns, may be provided to achieve a high elongation at break and possibly an improvement in the solid solubility of carbon, phosphorus and optionally nitrogen.
  • a high tensile strength can be ensured in particular by a relatively high proportion of phosphorus (and carbon).
  • the rolled steel strip is cooled at a rate of 20 ° C / s or higher.
  • rapid cooling of the cold-rolled steel strip is conducted at a rate of 50 ° C / sec or higher, more preferably 200 ° C / sec or higher.
  • a rapid cooling also contributes to effecting a high and uniform solid solubility of carbon, phosphorus and nitrogen in the grains and thereby to achieve a high tensile strength even with large grains. Cooling rates of over 100 ° C / s to 400 ° C / s were used. Cooling rates of more than 400 ° C / s to even more than 600 ° C / s are also possible. If necessary, before the rapid cooling an intermediate phase of several seconds, in particular 1 to 6 seconds, persist, in which the steel strip slowly cools in air to improve the recrystallization of the phosphorus-alloyed steel strip.
  • Fig. 1 is a graph in which for cold-rolled steels, the average grain size compared to the annealing temperature is shown;
  • strain hardening n 10/20 value
  • perpendicular anisotropy r o / i 5 -, r 45/15 -, and r 90 / i 5 - Value
  • FIGS. 3A-C show schematic representations of twins and micro-twins or nano-twins in the microstructure of steels
  • FIG. 5 shows a microsection of the weld nugget of a welded steel structure according to the invention.
  • pig iron is produced in a blast furnace or by a smelting reduction process such as Corex or Finex.
  • the Tecnored process is also possible.
  • the pig iron is then converted into steel, for example, in an oxygen inflation process (eg in an LD (Linz-Donawitz) / BOF (Bottom Oxygen Furnace) process).
  • a vacuum degasification eg according to the Ruhrstahl-Heraeus method (RH)
  • RH Ruhrstahl-Heraeus method
  • Ladle Furnace ladle furnace
  • a second production route which may be particularly suitable for manganese steel, uses an electric arc furnace (EAF: Electric Are Furnace) for steelmaking and an AOD converter for decarburizing the liquid steel.
  • EAF Electric Are Furnace
  • AOD converter for decarburizing the liquid steel.
  • a ladle furnace can be used to heat and alloy the molten metal.
  • the steel thus produced can be further processed by means of various casting techniques such as block casting, casting rolls, thin strip casting or continuous casting.
  • the steel body produced during casting is called semifinished and may e.g. be realized in the form of slabs, billets or blocks.
  • the slab is further processed in hot strip mills to hot strip.
  • rolling mills for narrow strip width less than 100 mm
  • middle strip width between 100 mm and 600 mm
  • broadband width greater 600 mm
  • blocks and billets into profiles, pipes or wires is possible.
  • a rolling temperature between about 1100 0 C and 1300 0 C, optionally also higher, can be used.
  • the rolling end temperature may, for example, between 750 0 C and 1050 0 C and in particular between 800 0 C and 900 0 C.
  • Different rolling end temperatures result in different average particle sizes of the hot-rolled steel strip according to the dynamic recrystallization at the prevailing temperature. The lower the final rolling temperature, the smaller the average particle size obtained for a given chemical composition. With a reduction in the average grain size, the tensile strength and the breaking strength of the hot-rolled steel strip increase, the elongation at break decreases.
  • the mean grain size of the hot strip steel strip is further influenced by the content of aluminum and nitrogen. It is known that manganese increases the solubility of nitrogen in liquid iron. Nitrogen dissolved in liquid iron forms aluminum nitride precipitates with aluminum, which hinder the migration of grain boundaries and thus grain growth. Aluminum nitride may further cause hot working cracking. It has been found that by targeted control of the aluminum and nitrogen content in the steel low Endwalztemperaturen significantly below 950 0 C and especially below 900 0 C down to 750 0 C are possible without causing cracking occurs. However, the formation of large cementite particles, which begins with a lowering of the final rolling temperature below about 740 0 C to 800 0 C, to avoid. Particularly preferred final rolling in the hot rolling process can therefore be in the range of 800 0 C to 900 0 C.
  • the avoidance of cracking at said final rolling temperatures in the range of 800 0 C to 900 0 C has been achieved with chemical compositions in which an extremely small amount of aluminum up to 0.008% or 0.010% in combination with a low content of nitrogen to eg 0.030% or 0.036% were used.
  • the respective concentrations of the elements are interdependent. If less nitrogen is used, more aluminum minium permissible and vice versa. In this respect, higher nitrogen contents than stated above are possible with a low aluminum content.
  • rapid cooling of the hot strip is performed at as high a cooling rate as possible (e.g., above 50 ° C / s or higher).
  • the cooling can be done by applying the hot strip with water.
  • the hot strip is then in a continuously working
  • the hot strip may have a thickness of 1.5 to 2.0 mm, for example. However, it is also possible to realize hot-rolled strip products with strip thicknesses which are smaller or larger than those specified above.
  • An annealing step is usually not carried out in the hot strip products produced here. In a particular embodiment, however, such an annealing step is carried out and causes a grain coarsening as well as an increase in the elongation at break.
  • the hot strip produced in the manner described above can be further processed by cold rolling and annealing to the cold strip product.
  • Cold rolling further reduces the thickness of the hot strip and sets the mechanical and technological properties of the strip. For example, low strip thicknesses in the range of about 0.7 mm to 1.75 mm of the cold strip can be produced.
  • Cold-rolled products with such small thicknesses are of particular interest in the automotive sector for crash-absorbing components.
  • the cold rolling is preferably carried out using high rolling forces.
  • Rolling mills with 2 to 20 rollers can be used.
  • To apply the high cold rolling forces for example, designed for high rolling pressures rolling stands with 12 or 20 rolls, in particular Sendzimir type (Cluster roller) can be used.
  • a Sendzimir rolling mill with 12 rolls for example, consists of a symmetrical arrangement of 3 back rolls, 2 intermediate rolls and 1 pressure roll defining the roll gap.
  • a Sendzimir rolling mill with 20 rolls for example, consists of a symmetrical arrangement of 4 back rolls, 3 outer intermediate rolls, 2 inner intermediate rolls and 1 pressure roll defining the roll gap. It showed a surprisingly good rolling and low cracking compared to other manganese steels.
  • the percent reduction in thickness (cold rolling degree) achieved during cold rolling may be above 40%, e.g. between 40% and 60%.
  • Cold rolling was also carried out with cold rolling degrees above 60%, especially above 80%. It was cold rolled with and without train.
  • the steel strip is annealed for recrystallization.
  • the annealing may e.g. be carried out after the continuous annealing or annealing process.
  • the solidification of the microstructure occurring during cold rolling is reduced again. It comes here about nucleation and grain growth to a rebuilding of the structure.
  • the annealing can be at temperatures between 750 0 C to 1250 0 C, in particular 750 0 C are made to 1150 0 C and continue for approximately 5 seconds to 5 minutes, in particular 2 to 5 minutes at the annealing temperature.
  • the annealing time is sufficient to heat the band substantially full volume to the respective annealing temperature. It can also be carried out several rolling steps and intermediately Eisenglüh Kunststoffe at a suitable temperature, for example about 950 0 C.
  • the hot steel strip is rapidly cooled, preferably quenched by exposure to water or in the gas stream (Gasj et). It turned out provides that a particularly rapid cooling is helpful to cause a high solids solubility of the elements C, N and P in the grains.
  • the embrittlement (grain boundary segregations) critical with a high phosphorus content could be largely or completely prevented by increasing the cooling rate. Cooling speeds of more than about 50 ° C. or more than 100 ° C. per second are advantageous.
  • cooling rates of over 200 °, 300 0 C or 400 0 C can be seen the ERI second, which also attempts at cooling than 500 0 C and 600 0 C per second have been successfully carried out.
  • cold rolling After cold rolling, annealing and cooling, cold rolling can be performed to achieve a suitable flatness of the cold strip.
  • thickness reductions e.g. 0.5%, 1.5%, 5%, 25% and more than 40%, or appropriate intermediate values.
  • hot-dip galvanizing or electrolytic galvanizing may be added depending on the field of application and customer requirements.
  • the chemical composition of the steel may vary over a wide range in other alloying elements.
  • optional upper limit values are 0.5%> V, 0.5%> Nb, 0.5%> Ti, 10%> Cr, 10%> Ni, 1%> W, 1%> Mo, 3%> Cu, 0.02%> B, the rest as mentioned iron and production-related impurities.
  • Specific embodiments of the invention use the following ranges: 0.85%> C> 0.70%, 16.2%> Mn> 15.5%, 0.015%> Al> 0.0005%,
  • Table 1 shows the chemical composition of four steel strips X80Mnl6-0.01P, X80Mnl6-0.03P, X80Mnl6-0.08P and X80Mnl6-0.1OP with a phosphorus concentration between 0.011 and 0.102% by weight.
  • the hot strip (WB) can optionally be further processed into a cold strip (KB).
  • the cold-strip processing was carried out with the processing parameters given in Table 3.
  • Table 3 The mechanical properties of the cold-rolled products of the chemical compositions X80Mnl6-0.01P, X80Mnl6 - 0.03P, X80Mnl6 -0.08P and X80Mnl6-0.1OP prepared in this way are given in Table 3. All values given in Table 3 are also disclosed as lower limits on the size to which they relate.
  • the cold strip were products with the KB numbers 1 to 7 and 9 with a finish rolling - rolling temperature of 900 0 C in the hot strip process. Otherwise, the same hot strip process was used as that underlying the hot strip products in Table 2.
  • the cold-rolled products with the KB numbers 1 to 3 are therefore based on approximately the hot-rolled product with the WB number 2 (the final rolling temperatures differ only by 10 0 C) and the cold-rolled products with the KB numbers 4 to 6 is approximately based on the hot-rolled product with the WB number 5 (the final rolling temperatures differ only by 30 0 C).
  • Table 3 shows that tensile strengths Rm above 1100 MPa and even above 1200 MPa are achieved and that even with large average particle sizes (over 15 ⁇ m in the case of X80Mn16- 0.03P (KB No. 6) and X80Mnl6-0.1OP ( KB No. 10) as well as over 20 ⁇ m or possibly even 25 ⁇ m in the case of the other ben) tensile strengths Rm above 1000 MPa can be achieved.
  • the tensile strength Rm is defined as the stress occurring at maximum tensile force on the workpiece.
  • the elongation at break A 50 given in Table 3 is the percentage permanent change in length after breakage of the tensile test specimen (according to EN 10002-1), based on the initial measuring length, based on an initial measuring length of 50 mm.
  • EN 10002-1 the percentage permanent change in length after breakage of the tensile test specimen
  • Another important parameter for the mechanical properties of steel strips is the product of tensile strength and elongation at break. Especially with large average particle sizes, high product values are achieved. The reason for this is that large grains lead to higher elongation at break values and the tensile strength, which usually decreases markedly with increasing grain size, is maintained as far as possible according to the invention by the relatively high carbon and / or phosphorus content.
  • Table 4 shows the results of a study of
  • the mean grain size of the cold rolled aluminum nitride-poor steel strips with the chemical compositions X80Mnl6-0.01P, X80Mnl6-0.03P, X80Mn16-0.08P and X80Mn16-0.1OP, given in Table 3, is dependent on the annealing temperature Cold strip process shown. Those illustrated cold-rolled products was a final rolling temperature of 900 0 C in the hot strip process is based. The graph shows that the steel strips X80Mnl6-0.01P and X80Mnl6-0.03P reach annealing temperatures of about 920 0 C average grain sizes over 15 microns.
  • the phosphorus-rich steel strips of the chemical compositions X80Mnl6-0.08P and X80Mnl6-0.1OP achieved even larger average particle sizes at comparable annealing temperatures.
  • the mean particle sizes were determined by light microscopic investigations on micrographs.
  • Fig. 2 shows a graph in which the work hardening n (here the ni O / 2 o value) of the above-mentioned steel strips, which is also referred to as solidification exponent , compared to the vertical anisotropy (r o / is-, r 45/15 -, and r 90 / is-value) is shown.
  • the n-value was determined in accordance with standard ISO 10275, issue 2006-07, which is hereby incorporated by reference in the Of content of this document is included.
  • the vertical anisotropy is defined in accordance with standard ISO 10113, edition 2006-09, which is hereby incorporated by reference into the disclosure of this document. Since the mechanical properties have a greater scattering than the mean grain size shown in FIG.
  • the steel strips according to the invention have a good cold workability, which is particularly important for further processing in drawing and deep drawing processes.
  • the average thickness for example, was less than 30 nm and, for example, in the range between 5 and 25 nm, in particular 10 and 20 nm, was.
  • a value of 17 nm for the average thickness of the micro- and nano-twins was determined on the cold-rolled product X80Mnl6-0.03P.
  • the presence of these small micro-twins, in particular the nano-twins can explain the high elongation at break values, since it leads, rather than the usual twinning, to an increasing inhibition of the dislocation movement and an increase of dislocation sources.
  • FIGS 3A-C are schematic representations of microstructures observed in electron beam microscopic studies on reshaped samples of steels of the invention.
  • FIG. 3A shows a unidirectionally activated system with conventional twinning, wherein lines 1 represent the mirror lines of the twins.
  • Fig. 3B shows a unidirectional system with micro- or nano-twins 2.
  • the micro- or nano-twins 2 are lath-shaped and often arranged side by side in greater numbers.
  • the lath thickness is referred to as the thickness d of the micro- or nano-twins 2 and is typically much smaller than the thickness of common twins.
  • Fig. 3C shows a bi-directionally activated system
  • Micro- or nano-twins 2 It can be seen that micro- or nano-twins 2 extending in both directions occur.
  • FIG. 4 shows an electron micrograph of a steel structure according to the invention after deformation or tensile stress. A large number of pale-shaped micro- and nano-twins are recognizable in the bright field. ,
  • Fig. 5 shows a micrograph of a weld nugget inventions' to the invention the steel structure by a weld.
  • X80Mnl6-0.1OP samples were used. It can be seen that the basic hardness as well as the maximum hardness in the heat-affected zones and the hardness in the weld nugget agree well and have only slight deviations. These deviations are in the range of the measuring tolerance. It is further recognized that there are no cracks or martensite in the structure.
  • the n value is largely determined by the chemical composition. That is, the strength of the final product that can be achieved by deformation depends on how easily dislocations can travel in the crystal. In the fcc crystal lattice, the solid solubility of C and N is greater than in the bcc crystal lattice.
  • the increase in tensile strength caused by solid solution of C and P is exploited, whereby in recent investigations tensile strength values of 1100 MPa with an extremely high elongation at break of 95% could be measured.
  • the hardening achieved by solid solution of said elements makes it possible to increase the n value considerably. As a result, the highest reported product values of tensile strength and elongation at break are achieved. This is attributed in particular to the use of high phosphorus concentrations and the associated increase in strength-in particular with relatively large average particle sizes.
  • the hot strip or cold strip is cut in further processing into steel sheets, e.g. be used in automotive technology for the production of body parts.
  • steel according to the invention can also be used in rails, switches, in particular switch hearts, rod material, pipes, hollow profiles or high-strength wires.
  • the steel sheets are brought by forming processes such as deep drawing in the desired shape and then further processed into the final products (eg body part).
  • forming processes such as deep drawing in the desired shape and then further processed into the final products (eg body part).
  • the steel sheets of a mechanical stress usually tensile stress

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)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

L'invention concerne un feuillard d'acier au manganèse austénitique laminé à chaud, ayant une composition chimique en masse de 0,4 % = C = 1,2 %, de 12,0 % = Mn = 25,0 %, de P = 0,01 % et de Al = 0,05 %, un produit d'allongement à la rupture en MPa et de résistance à la traction en % de plus de 65 000, en particulier de plus de 70 000 MPa%. Un feuillard d'acier au manganèse austénitique laminé à froid ayant la même composition chimique atteint un produit d'allongement à la rupture en % et de résistance à la traction en MPa de plus de 75 000, en particulier de plus de 80 000 MPa%.
EP09760726.1A 2008-11-12 2009-11-12 Feuillard d'acier au manganèse à teneur accrue en phosphore et son procédé de fabrication Not-in-force EP2366035B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102008056844A DE102008056844A1 (de) 2008-11-12 2008-11-12 Manganstahlband und Verfahren zur Herstellung desselben
PCT/EP2009/008065 WO2010054813A1 (fr) 2008-11-12 2009-11-12 Feuillard d'acier au manganèse à teneur accrue en phosphore et son procédé de fabrication

Publications (2)

Publication Number Publication Date
EP2366035A1 true EP2366035A1 (fr) 2011-09-21
EP2366035B1 EP2366035B1 (fr) 2017-07-05

Family

ID=41796429

Family Applications (1)

Application Number Title Priority Date Filing Date
EP09760726.1A Not-in-force EP2366035B1 (fr) 2008-11-12 2009-11-12 Feuillard d'acier au manganèse à teneur accrue en phosphore et son procédé de fabrication

Country Status (7)

Country Link
US (1) US9677146B2 (fr)
EP (1) EP2366035B1 (fr)
KR (1) KR101387040B1 (fr)
CN (1) CN102216474B (fr)
DE (1) DE102008056844A1 (fr)
ES (1) ES2642891T3 (fr)
WO (1) WO2010054813A1 (fr)

Families Citing this family (34)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102011000089A1 (de) * 2011-01-11 2012-07-12 Thyssenkrupp Steel Europe Ag Verfahren zum Herstellen eines warmgewalzten Stahlflachprodukts
CN102296232B (zh) * 2011-09-08 2012-12-26 上海交通大学 超高强度高塑性低碳相变与孪晶诱发塑性热轧钢板及制法
CN104136647A (zh) * 2011-12-28 2014-11-05 Posco公司 在焊接热影响区具有优异机械加工性及韧性的耐磨奥氏体钢及其生产方法
DE112013001144A5 (de) * 2012-02-25 2014-10-30 Technische Universität Bergakademie Freiberg Verfahren zur Herstellung hochfester Formteile aus hochkohlenstoff- und hochmanganhaltigem austenitischem Stahlguss mit TRIP/TWIP-Eigenschaften
ITRM20120647A1 (it) * 2012-12-19 2014-06-20 Ct Sviluppo Materiali Spa ACCIAIO INOSSIDABILE AUSTENITICO AD ELEVATA PLASTICITÀ INDOTTA DA GEMINAZIONE, PROCEDIMENTO PER LA SUA PRODUZIONE, E SUO USO NELLÂeuro¿INDUSTRIA MECCANICA.
EP2940173B1 (fr) * 2012-12-26 2019-11-06 Posco Acier à base austénitique à haute résistance ayant une ténacité remarquable d'une zone affectée par la chaleur de soudage et son procédé de préparation
US20140261918A1 (en) * 2013-03-15 2014-09-18 Exxonmobil Research And Engineering Company Enhanced wear resistant steel and methods of making the same
EP2824213A1 (fr) * 2013-07-12 2015-01-14 Voestalpine Stahl GmbH Procédé d'amélioration de l'adhérence sur une tôle d'acier dotée d'un revêtement de protection
UA117494C2 (uk) * 2013-07-26 2018-08-10 Ніппон Стіл Енд Сумітомо Метал Корпорейшн Високоміцна марганцева сталь для нафтової свердловини і труба для нафтових свердловин
RU2659549C2 (ru) 2014-01-06 2018-07-02 Ниппон Стил Энд Сумитомо Метал Корпорейшн Горячеформованный элемент и способ его изготовления
US10774405B2 (en) 2014-01-06 2020-09-15 Nippon Steel Corporation Steel and method of manufacturing the same
AR101904A1 (es) * 2014-09-29 2017-01-18 Nippon Steel & Sumitomo Metal Corp Material de acero y tuberías expansibles para la industria del petróleo
MX2017004258A (es) * 2014-10-01 2017-06-06 Nippon Steel & Sumitomo Metal Corp Material de acero de alta resistencia para pozos de petróleo y productos tubulares para la industria del petróleo.
KR101665810B1 (ko) * 2014-12-24 2016-10-13 주식회사 포스코 표면경도가 우수한 오스테나이트계 강재 및 이의 제조방법
JP6693217B2 (ja) * 2015-04-02 2020-05-13 日本製鉄株式会社 極低温用高Ｍｎ鋼材
JP6703608B2 (ja) * 2015-12-22 2020-06-03 ポスコＰｏｓｃｏ 耐水素脆化性に優れたオーステナイト系鋼材
EP3438312B1 (fr) * 2016-03-30 2020-12-23 Nippon Steel Corporation Matériau d'acier de haute résistance et son procédé de fabrication
WO2017203315A1 (fr) 2016-05-24 2017-11-30 Arcelormittal Tôle mince en acier laminée à froid et recuite, son procédé de production et utilisation d'un tel acier pour produire des pièces de véhicule
CN106282804B (zh) * 2016-11-10 2017-12-26 钢铁研究总院 一种Cr‑Al‑Nb‑V合金化的高耐磨高锰铸钢
RU2659542C2 (ru) * 2016-12-09 2018-07-02 федеральное государственное бюджетное образовательное учреждение высшего образования "Уфимский государственный авиационный технический университет" Сверхпрочная высокомарганцевая сталь, полученная за счет комбинирования механизмов упрочнения
KR101940874B1 (ko) * 2016-12-22 2019-01-21 주식회사 포스코 저온인성 및 항복강도가 우수한 고 망간 강 및 제조 방법
KR101920973B1 (ko) * 2016-12-23 2018-11-21 주식회사 포스코 표면 특성이 우수한 오스테나이트계 강재 및 그 제조방법
EP3610049A1 (fr) * 2017-04-11 2020-02-19 ThyssenKrupp Steel Europe AG Produit plat en acier laminé à froid, recuit sur base, et procédé de fabrication s'y rapportant
CN107574376A (zh) * 2017-09-07 2018-01-12 北京科技大学 一种低成本高强塑型高锰twip/trip效应共生钢及其制备方法
CN107574377B (zh) * 2017-09-07 2019-05-03 北京科技大学 一种基于纳米结构的高吸能型高锰twip钢及其制备方法
KR102109270B1 (ko) * 2017-10-18 2020-05-12 주식회사 포스코 표면품질이 우수한 저온용 고 망간강재 및 제조방법
AU2018412622A1 (en) 2018-03-29 2019-10-17 Nippon Steel Corporation Austenitic wear-resistant steel plate
WO2019209933A1 (fr) * 2018-04-24 2019-10-31 Nucor Corporation Alliages d'acier exempts d'aluminium et leurs procédés de fabrication
WO2020085852A1 (fr) * 2018-10-25 2020-04-30 주식회사 포스코 Acier austénitique à haute teneur en manganèse ayant une haute limite d'élasticité et son procédé de fabrication
CN113308626B (zh) * 2020-02-27 2022-03-18 南京理工大学 一种含有梯度纳米结构的镍基合金及其制备方法
CN111659732B (zh) * 2020-06-08 2022-04-19 首钢集团有限公司 一种解决高锰热成型钢酸洗后锈蚀的方法
CN112522624B (zh) * 2020-11-30 2021-11-16 湖南华菱涟源钢铁有限公司 高锰奥氏体耐磨钢及其制造方法
CN112877606B (zh) * 2021-01-12 2022-03-08 钢铁研究总院 一种超高强全奥氏体低密度钢及制备方法
WO2023233186A1 (fr) * 2022-06-02 2023-12-07 Arcelormittal Acier laminé à chaud à haute teneur en manganèse et son procédé de production

Family Cites Families (18)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4968357A (en) 1989-01-27 1990-11-06 National Science Council Hot-rolled alloy steel plate and the method of making
US5431753A (en) 1991-12-30 1995-07-11 Pohang Iron & Steel Co. Ltd. Manufacturing process for austenitic high manganese steel having superior formability, strengths and weldability
KR970001324B1 (ko) * 1994-03-25 1997-02-05 김만제 열간가공성이 우수한 고망간강 및 그 열간압연 방법
DE19727759C2 (de) 1997-07-01 2000-05-18 Max Planck Inst Eisenforschung Verwendung eines Leichtbaustahls
FR2796083B1 (fr) 1999-07-07 2001-08-31 Usinor Procede de fabrication de bandes en alliage fer-carbone-manganese, et bandes ainsi produites
DE10259230B4 (de) 2002-12-17 2005-04-14 Thyssenkrupp Stahl Ag Verfahren zum Herstellen eines Stahlprodukts
FR2857980B1 (fr) * 2003-07-22 2006-01-13 Usinor Procede de fabrication de toles d'acier austenitique fer-carbone-manganese, a haute resistance, excellente tenacite et aptitude a la mise en forme a froid, et toles ainsi produites
FR2876708B1 (fr) * 2004-10-20 2006-12-08 Usinor Sa Procede de fabrication de toles d'acier austenitique fer-carbone-manganese laminees a froid a hautes caracteristiques mecaniques, resistantes a la corrosion et toles ainsi produites
WO2006048034A1 (fr) * 2004-11-03 2006-05-11 Thyssenkrupp Steel Ag Bande ou tole d'acier extremement resistante a proprietes twip et procede de fabrication de ladite bande a l'aide de la 'coulee directe de bandes'
FR2878257B1 (fr) * 2004-11-24 2007-01-12 Usinor Sa Procede de fabrication de toles d'acier austenitique, fer-carbone-manganese a tres hautes caracteristiques de resistance et d'allongement, et excellente homogeneite
FR2881144B1 (fr) 2005-01-21 2007-04-06 Usinor Sa Procede de fabrication de toles d'acier austenitique fer-carbone-manganese a haute resistance a la fissuration differee, et toles ainsi produites
JP5318421B2 (ja) 2005-02-02 2013-10-16 タタ、スティール、アイモイデン、ベスローテン、フェンノートシャップ 高い強度および成型性を有するオーステナイト系鋼、該鋼の製造方法およびその使用
KR100711361B1 (ko) * 2005-08-23 2007-04-27 주식회사 포스코 가공성이 우수한 고망간형 고강도 열연강판 및 그 제조방법
DE202005021771U1 (de) 2005-12-20 2010-02-18 Salzgitter Flachstahl Gmbh Umformbarer Leichtbaustahl
KR100742833B1 (ko) 2005-12-24 2007-07-25 주식회사 포스코 내식성이 우수한 고 망간 용융도금강판 및 그 제조방법
KR100742823B1 (ko) 2005-12-26 2007-07-25 주식회사 포스코 표면품질 및 도금성이 우수한 고망간 강판 및 이를 이용한도금강판 및 그 제조방법
EP1878811A1 (fr) 2006-07-11 2008-01-16 ARCELOR France Procede de fabrication d'une tole d'acier austenitique fer-carbone-manganese ayant une excellente resistance a la fissuration differee, et tole ainsi produit
DE102006039307B3 (de) 2006-08-22 2008-02-21 Thyssenkrupp Steel Ag Verfahren zum Beschichten eines 6-30 Gew.% Mn enthaltenden warm- oder kaltgewalzten Stahlbands mit einer metallischen Schutzschicht

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See references of WO2010054813A1 *

Also Published As

Publication number Publication date
KR20110083735A (ko) 2011-07-20
ES2642891T3 (es) 2017-11-20
CN102216474A (zh) 2011-10-12
EP2366035B1 (fr) 2017-07-05
WO2010054813A1 (fr) 2010-05-20
DE102008056844A1 (de) 2010-06-02
US20110308673A1 (en) 2011-12-22
KR101387040B1 (ko) 2014-04-18
US9677146B2 (en) 2017-06-13
CN102216474B (zh) 2014-08-20

Similar Documents

Publication Publication Date Title
EP2366035B1 (fr) Feuillard d'acier au manganèse à teneur accrue en phosphore et son procédé de fabrication
EP2864517B1 (fr) Acier multiphase à haute résistance et procédé pour la fabrication d'une bande faite de cet acier présentant une résistance à la traction minimale de 580 mpa
EP3535431B1 (fr) Produit d'acier à teneur en manganèse intermédiaire pour application à basse température et son procédé de fabrication
EP3027784B1 (fr) Acier multiphase à haute résistance, micro-allié et contenant du silicium, présentant une résistance minimale à la traction de 750 mpa et des propriétés améliorées et procédé de fabrication d'une bande à partir de cet acier
DE60300835T2 (de) Kaltgewalztes Stahlblech mit ultrafeinem Korngefüge und Verfahren zu dessen Herstellung
EP3504349B1 (fr) Procédé de fabrication d'une bande d'acier à résistance très élevée présentant des propriétés améliorées lors du traitement ultérieur et une telle bande d'acier
EP3221484B1 (fr) Procédé de production d'une bande en acier polyphasé, durcissant à l'air, ayant une haute résistance et ayant d'excellentes propriétés de mise en oeuvre
EP3221483B1 (fr) Acier multiphases autotrempant en profondeur à haute résistance mécanique avec excellent aptitude au faconnage et procédé de fabrication d'une bande de cet acier
EP3325678B1 (fr) Acier léger deformable de construction présentant des propriétés mécaniques améliorées et procédé de fabrication de produit semi-fini à partir de cet acier
EP3692178B1 (fr) Procede de fabrication d'une bande d'acier a partir d'un acier multiphase a tres haute resistance
WO2015117934A1 (fr) Produit en acier plat de résistance élevée ayant une texture à base de bainite et de martensite et procédé de fabrication d'un tel produit en acier plat
EP2009120B1 (fr) Utilisation d'un alliage d'acier très solide destiné à la fabrication de tuyaux en acier très résistants et ayant une bonne déformabilité
EP4298255A1 (fr) Produit plat en acier laminé à chaud à haute résistance ayant une aptitude au formage à froid locale élevée et procédé de production d?un tel produit plat en acier
EP4301886A1 (fr) Produit plat en acier laminé à froid et son procédé de production
EP3964591A1 (fr) Produit en acier plat laminé à chaud et procédé de fabrication d'un produit en acier plat laminé à chaud
DE102016115618A1 (de) Verfahren zur Herstellung eines höchstfesten Stahlbandes mit verbesserten Eigenschaften bei der Weiterverarbeitung und ein derartiges Stahlband
WO2020038883A1 (fr) Produit plat en acier laminé à chaud n'ayant pas subi un traitement par trempe et revenu, laminé à chaud ayant subi un traitement par trempe et revenu, ainsi que procédé de production associé
EP4392584A1 (fr) Produit plat en acier laminé à froid et son procédé de production
EP3847284A1 (fr) Produit plat laminé à chaud en acier et procédé de fabrication
WO2015144661A2 (fr) Composants en alliage d'acier et procédé de fabrication de composants à haute résistance
WO2024115199A1 (fr) Produit plat en acier laminé à froid et son procédé de fabrication
DE102021119047A1 (de) Verfahren zur Herstellung eines kaltgewalzten Stahlflachprodukts mit einem bainitischen Grundgefüge und kaltgewalztes Stahlflachprodukt mit einem bainitischen Grundgefüge

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: 20110610

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): 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 SE SI SK SM TR

RIN1 Information on inventor provided before grant (corrected)

Inventor name: MRACZEK, KLEMENS

Inventor name: ARENHOLZ, ENNO

Inventor name: SCHNEIDER, REINHOLD

Inventor name: SAMEK, LUDOVIC

DAX Request for extension of the european patent (deleted)
17Q First examination report despatched

Effective date: 20151124

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

INTG Intention to grant announced

Effective date: 20170127

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): 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 SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

Free format text: NOT ENGLISH

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 906658

Country of ref document: AT

Kind code of ref document: T

Effective date: 20170715

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

Free format text: LANGUAGE OF EP DOCUMENT: GERMAN

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 502009014128

Country of ref document: DE

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20170705

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2642891

Country of ref document: ES

Kind code of ref document: T3

Effective date: 20171120

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 9

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: 20170705

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: 20170705

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: 20170705

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: 20170705

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: 20171005

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

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: 20171005

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: 20170705

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: 20171105

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: 20171006

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: 20170705

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 502009014128

Country of ref document: DE

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: 20170705

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: 20170705

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: 20170705

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

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

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: 20170705

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: 20170705

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: 20170705

26N No opposition filed

Effective date: 20180406

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

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: 20170705

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20171130

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20171130

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: 20171112

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: 20170705

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20171130

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

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: 20170705

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: 20171112

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: 20171130

REG Reference to a national code

Ref country code: AT

Ref legal event code: MM01

Ref document number: 906658

Country of ref document: AT

Kind code of ref document: T

Effective date: 20171112

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20171112

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20091112

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CY

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170705

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: 20170705

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: SE

Payment date: 20191127

Year of fee payment: 11

Ref country code: DE

Payment date: 20191127

Year of fee payment: 11

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20191125

Year of fee payment: 11

Ref country code: IT

Payment date: 20191125

Year of fee payment: 11

Ref country code: ES

Payment date: 20191202

Year of fee payment: 11

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: 20170705

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: GB

Payment date: 20191127

Year of fee payment: 11

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

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: 20170705

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 502009014128

Country of ref document: DE

REG Reference to a national code

Ref country code: SE

Ref legal event code: EUG

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20201112

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20201113

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20201130

Ref country code: IT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20201112

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210601

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20201112

REG Reference to a national code

Ref country code: ES

Ref legal event code: FD2A

Effective date: 20220201

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: ES

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20201113