EP3115482B1 - Cold-rolled steel sheet, manufacturing method therefor, and car part - Google Patents

Cold-rolled steel sheet, manufacturing method therefor, and car part Download PDF

Info

Publication number
EP3115482B1
EP3115482B1 EP15759246.0A EP15759246A EP3115482B1 EP 3115482 B1 EP3115482 B1 EP 3115482B1 EP 15759246 A EP15759246 A EP 15759246A EP 3115482 B1 EP3115482 B1 EP 3115482B1
Authority
EP
European Patent Office
Prior art keywords
acid
steel sheet
cold
concentration
pickling
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
Application number
EP15759246.0A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP3115482A1 (en
EP3115482A4 (en
Inventor
Hiroyuki Masuoka
Shoichiro Taira
Yuta TERASAKI
Hirotsugu Kondo
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.)
JFE Steel Corp
Original Assignee
JFE Steel Corp
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 JFE Steel Corp filed Critical JFE Steel Corp
Publication of EP3115482A1 publication Critical patent/EP3115482A1/en
Publication of EP3115482A4 publication Critical patent/EP3115482A4/en
Application granted granted Critical
Publication of EP3115482B1 publication Critical patent/EP3115482B1/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • 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
    • C22C38/02—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
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
    • C23G1/08—Iron or steel
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
    • C23G1/08—Iron or steel
    • C23G1/081—Iron or steel solutions containing H2SO4
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
    • C23G1/08—Iron or steel
    • C23G1/085—Iron or steel solutions containing HNO3
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
    • C23G1/08—Iron or steel
    • C23G1/086—Iron or steel solutions containing HF
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0478—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing involving a particular surface treatment
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals

Definitions

  • the present invention relates to a method for producing a cold-rolled steel sheet.
  • the present invention relates to a method for producing a cold-rolled steel sheet having excellent chemical convertibility and high corrosion resistance after coating, which is evaluated by a hot salt water immersion test or a combined cyclic corrosion test.
  • Patent Literature 1 proposes a high-strength cold-rolled steel sheet in which the Si concentration on the surface of the steel sheet is decreased by heating a slab at a temperature of 1200°C or higher during hot-rolling, performing descaling at high pressure, grinding the surface of the resulting hot-rolled steel sheet using a nylon brush with abrasive grains before pickling, and immersing the steel sheet in a 9% hydrochloric acid tank twice to perform pickling.
  • Patent Literature 2 proposes a high-strength cold-rolled steel sheet whose corrosion resistance is improved by controlling the line width of a Si-containing linear oxide observed at a depth of 1 to 10 ⁇ m from the steel sheet surface to 300 nm or less.
  • Patent Literature 3 proposes a technique for improving the ability to remove oxides by controlling the concentration of iron ions (Fe(II)) in hydrochloric acid to 0.5% to 18%.
  • Patent Literature 1 In the high-strength cold-rolled steel sheet described in Patent Literature 1, however, even when the Si concentration on the steel sheet surface is decreased before cold-rolling, a Si-containing oxide is formed on the steel sheet surface due to annealing performed after the cold-rolling. Therefore, the corrosion resistance after coating is not improved.
  • the corrosion resistance is not problematic in a corrosive environment such as a salt spray test specified in JIS Z2371.
  • a corrosive environment such as a salt spray test specified in JIS Z2371.
  • sufficient corrosion resistance after coating is not achieved in a severe corrosive environment such as a hot salt water immersion test or a combined cyclic corrosion test.
  • a high-strength cold-rolled steel sheet having excellent corrosion resistance after coating is not obtained only by decreasing the Si concentration on the steel sheet surface after hot-rolling or decreasing the amount of the Si-containing linear oxide.
  • SiO 2 is insoluble in hydrochloric acid and cannot be removed even when the concentration of iron ions is controlled to 0.5% to 18%.
  • Patent Literature 4 discloses a technique for improving the chemical convertibility by removing a Si-containing oxide concentrated on the steel sheet surface through an annealing process or the like by pickling and furthermore providing a S-based compound to the surface to improve the reactivity with a chemical conversion treatment liquid.
  • Patent Literature 5 discloses a technique in which a P-based compound is provided instead of the S-based compound in Patent Literature 4.
  • Patent Literature 6 discloses the following technique for improving the reactivity with a chemical conversion treatment liquid to improve the chemical convertibility.
  • pickling is performed using an oxidizing acid to remove SiO 2 .
  • pickling is performed using a non-oxidizing acid to remove an Fe-based oxide formed during the pickling at the first stage.
  • the temperature of a chemical conversion treatment liquid has been decreased to reduce the amount of industrial waste (suppress the generation of sludge) and to reduce the operating cost.
  • the reactivity of the chemical conversion treatment liquid with a steel sheet has been considerably decreased compared with previous chemical conversion conditions.
  • the decrease in the temperature of the chemical conversion treatment liquid does not pose a problem for plain steel sheets, which have been conventionally used and contain only a small amount of alloy, by improving a surface control technique before the chemical conversion treatment, for example.
  • the reactivity with the chemical conversion treatment liquid is considerably decreased because of the influence of a Si-containing oxide formed in a surface layer of the steel sheet in the annealing process.
  • Patent Literature 4 and Patent Literature 5 are effective for conventional plain steel sheets, but do not provide a sufficient improvement effect on the decrease in the temperature of the chemical conversion treatment liquid for the high-strength cold-rolled steel sheet containing a large amount of Si. It has been found that, by applying the technique disclosed in Patent Literature 6 to the above techniques, the decrease in the temperature of the chemical conversion treatment liquid can be overcome even in the high-strength cold-rolled steel sheet containing a large amount of Si. In the technique disclosed in Patent Literature 6, however, when the Fe concentration is low, the pickling rate is low and thus the ability to remove a Si-containing oxide is insufficient. Furthermore, when the Fe concentration is high, an iron-based oxide is unfavorably formed, which degrades the chemical convertibility and also the corrosion resistance after coating.
  • the present invention provides a method for producing a cold-rolled steel sheet as defined in the appended claims. According to the production method of the present invention, a cold-rolled steel sheet having excellent chemical convertibility and high corrosion resistance after coating can be easily and stably produced through a typical cold-rolling process and pickling process by simply adjusting the pickling conditions.
  • a cold-rolled steel sheet can be provided which has excellent chemical convertibility even when 0.5% to 3.0% of Si is contained or even when the temperature of a chemical conversion treatment liquid is decreased and which has high corrosion resistance after coating even in a severe corrosive environment such as a hot salt water immersion test or a combined cyclic corrosion test. Accordingly, in the present invention, the chemical convertibility and the corrosion resistance after coating of a high-strength cold-rolled steel sheet having a tensile strength TS of 590 MPa or more and containing a large amount of Si can be considerably improved.
  • the cold-rolled steel sheet according to the present invention can be suitably used for, for example, high-strength components of automotive bodies.
  • a non-oxidizing gas or a reducing gas is normally used as an atmosphere gas, and the dew point is also strictly controlled. Therefore, in typical cold-rolled steel sheets containing only a small amount of alloy, the oxidation of the steel sheet surface is suppressed. In steel sheets containing 0.5% or more of Si or Mn, however, even when the components of the atmosphere gas and the dew point during annealing are strictly controlled, Si, Mn, or the like, which is more easily oxidized than Fe, is oxidized.
  • silicon oxide (SiO 2 ) or a Si-containing oxide such as a Si-Mn composite oxide is formed on the steel sheet surface.
  • the composition of such an oxide varies in accordance with the composition of the steel sheet, the annealing atmosphere, or the like, but often varies in accordance with mixed conditions of the composition of the steel sheet and the annealing atmosphere in general.
  • the Si-containing oxide is formed not only on the steel sheet surface, but also in a steel substrate, which degrades the etching properties of the steel sheet surface in a chemical conversion treatment (zinc phosphate treatment) performed as an underlayer treatment for electrodeposition painting and thus adversely affects the steady formation of a chemical conversion coating.
  • the temperature of the chemical conversion treatment liquid has been decreased in order to reduce the amount of sludge generated during the chemical conversion treatment and reduce the operating cost.
  • the chemical conversion treatment is performed under conditions in which the reactivity of the chemical conversion treatment liquid with the steel sheet is considerably low.
  • Such a change in chemical conversion conditions does not pose a problem for plain steel sheets, which have been conventionally used and contain only a small amount of alloy, by improving a surface control technique, for example.
  • the change in the chemical conversion conditions that is, the decrease in the temperature of the chemical conversion treatment liquid has quite a large influence. Therefore, in cold-rolled steel sheets containing a large amount of Si, the reactivity with the chemical conversion treatment liquid needs to be improved by activating the surface of the steel sheet itself in order to overcome the degradation of chemical conversion conditions.
  • the inventors have studied a method for improving the chemical convertibility of the steel sheet to overcome the degradation of chemical conversion conditions described above. As a result, they have found that it is effective to pickle the surface of a cold-rolled steel sheet subjected to continuous annealing using a strong acid such as nitric acid as a pickling solution to remove a Si-containing oxide layer formed in a surface layer of the steel sheet through continuous annealing or the like after cold-rolling.
  • the Si-containing oxide refers to SiO 2 or a Si-Mn composite oxide formed along grain boundaries on the steel sheet surface or in the steel sheet during slab heating or during annealing after hot-rolling or cold-rolling.
  • the thickness of a layer in which such a Si-containing oxide is present varies depending on the composition of the steel sheet and the annealing conditions (temperature, time, and atmosphere), and is normally about 1 ⁇ m from the steel sheet surface.
  • the phrase "to remove a Si-containing oxide layer" in the present invention refers to the removal of a Si-containing oxide layer by performing pickling until peaks of Si and O do not appear when the steel sheet surface is analyzed by GDS (glow discharge spectroscopy) in the depth direction.
  • the reason for which a strong acid such as nitric acid is used as the pickling solution is as follows.
  • a Si-Mn composite oxide easily dissolves in an acid, but SiO 2 does not easily dissolve in an acid. Therefore, to remove SiO 2 , the Si-containing oxide on the steel sheet surface needs to be removed together with the steel substrate.
  • the chemical convertibility is considerably improved by pickling a steel sheet with a strong acid such as nitric acid after continuous annealing to remove a Si-containing oxide layer present on the steel sheet surface, but the chemical convertibility is sometimes not sufficient.
  • the cause thereof has been further studied. Consequently, the following has been additionally found. That is, the Si-based oxide layer is removed by performing pickling with a strong acid such as nitric acid, but Fe eluted from the steel sheet surface as a result of the pickling forms an iron-based oxide, which is different from the Si-based oxide layer. This iron-based oxide is precipitated on the steel sheet surface so as to cover the steel sheet surface, resulting in the degradation of the chemical convertibility.
  • the concentration of iron ions in the present invention refers to the total concentration of Fe(II) ions and Fe(III) ions because, in the acid liquid containing nitric acid, which has a strong oxidation power, the eluted Fe(II) ions relatively quickly change to Fe(III) ions by the nitric acid.
  • the inventors have also found that when the coverage of the iron-based oxide generated on the steel sheet surface is controlled to 40% or less by pickling and the maximum thickness of the iron-based oxide is controlled to 150 nm or less, the chemical convertibility is further improved and the corrosion resistance is also further improved. They have also found that the maximum thickness of the iron-based oxide is effectively controlled to 150 nm or less by appropriately setting pickling conditions (concentration, temperature, and time) and non-oxidative pickling conditions (acid concentration, temperature, and time).
  • the iron-based oxide in the present invention refers to an oxide mainly containing iron at an atomic concentration ratio of 30% or more among elements other than oxygen constituting the oxide. This iron-based oxide is present with an uneven thickness on the steel sheet surface and is different from a natural oxide film present in the form of a layer with a uniform thickness of several nanometers.
  • the iron-based oxide generated on the surface of the cold-rolled steel sheet is found to be amorphous from the observation with a transmission electron microscope (TEM) and the analysis result of a diffraction pattern obtained by electron diffraction analysis.
  • TEM transmission electron microscope
  • a steel sheet obtained by heating a steel material (slab) containing Si in an amount of 0.5% to 3.0% and performing hot-rolling, cold-rolling, and continuous annealing is subjected to first pickling using an acid liquid 1) or an acid liquid 2) below and then subjected to second pickling using an acid liquid made of a non-oxidizing acid.
  • Fe eluted from the steel sheet surface by pickling forms an iron-based oxide, and this iron-based oxide is precipitated on the steel sheet surface so as to cover the steel sheet surface. Consequently, the chemical convertibility is sometimes degraded.
  • the amount of the iron-based oxide generated on the steel sheet surface is preferably suppressed. For the above reasons, the following pickling conditions are specified.
  • the concentration of the nitric acid is 50 g/L or less, a long time is required for pickling, which increases the facility length and thus increases the facility cost. If the concentration of the nitric acid is more than 200 g/L, the eluted iron is oxidized to generate an iron-based oxide. This iron-based oxide is precipitated on the steel sheet surface, which adversely affects the chemical convertibility and the corrosion resistance after coating. If R1 or R2 is more than 0.25 or the concentration of iron ions (total of Fe(II) and Fe(III)) is less than 3 g/L, a desired pickling rate is not achieved, and thus the Si-containing oxide cannot be efficiently removed.
  • the maximum thickness of the iron-based oxide can be controlled to 150 nm or less by appropriately setting the pickling conditions (concentration, temperature, and time).
  • the pickling conditions concentration, temperature, and time.
  • the maximum thickness of the iron-based oxide is controlled to 150 nm or less. Consequently, the chemical convertibility is further improved, and the corrosion resistance is also further improved.
  • the first pickling with a strong acid is not sufficient to stably control the surface coverage of the iron-based oxide generated on the steel sheet surface to 40% or less.
  • second pickling is performed in order to decrease, with certainty, the amount of the iron-based oxide generated on the steel sheet surface as a result of the first pickling. That is, pickling is performed using an acid liquid made of a non-oxidizing acid to dissolve and remove the iron-based oxide.
  • the second pickling is preferably performed at a temperature of the acid liquid of 20°C to 70°C for 1 to 30 seconds.
  • the temperature of the pickling solution is 20°C or higher and the treatment time is 1 second or more, the iron-based oxide left on the steel sheet surface is sufficiently removed.
  • the temperature of the pickling solution is 70°C or lower and the treatment time is 30 seconds or less, the steel sheet surface is not excessively dissolved and another surface oxide film is not formed.
  • the maximum thickness of the iron-based oxide present on the steel sheet surface after the pickling is preferably decreased to 150 nm or less with certainty.
  • the concentration of the acid liquid made of a non-oxidizing acid is preferably increased to an appropriate value.
  • the concentration of the hydrochloric acid is preferably 3 to 50 g/L.
  • sulfuric acid is used, the concentration of the sulfuric acid is preferably 8 to 150 g/L.
  • the first pickling and the second pickling are performed. Subsequently, an ordinary process such as temper rolling is performed to obtain a product sheet (cold-rolled steel sheet).
  • the Si content is preferably 0.5% to 3.0%.
  • Si has a large effect (solid-solution strengthening ability) of increasing the strength of steel without considerably impairing the workability. Therefore, Si is an element effective for increasing the strength of steel, but is also an element that adversely affects the chemical convertibility and the corrosion resistance after coating. For the above reason, the Si content is preferably 0.5% or more. If the Si content is more than 3.0%, the hot rollability and the cold rollability are considerably degraded, which may adversely affect the productivity or degrade the ductility of the steel sheet itself. Accordingly, when Si is added, the Si content is preferably 0.5% to 3.0% and more preferably 0.8% to 2.5%.
  • Components other than Si are allowable as long as the contents of the components are within the ranges of typical cold-rolled steel sheets.
  • the suitable composition except for Si is preferably as follows.
  • C is an element effective for increasing the strength of steel and also an element effective for generating retained austenite having a TRIP (transformation induced plasticity) effect, bainite, and martensite.
  • TRIP transformation induced plasticity
  • bainite bainite
  • martensite martensite.
  • the C content is 0.01% or more, the above effects are produced.
  • the C content is 0.30% or less, the weldability does not degrade. Accordingly, the C content is preferably 0.01% to 0.30% and more preferably 0.10% to 0.20%.
  • Mn is an element that increases the strength of steel through solid-solution strengthening, improves the hardenability, and facilitates the generation of retained austenite, bainite, and martensite.
  • the Mn content is 1.0% or more, such effects are produced.
  • the Mn content is 7.5% or less, the above effects are produced without increasing the cost. Accordingly, the Mn content is preferably 1.0% to 7.5% and more preferably 2.0% to 5.0%.
  • the P content is preferably 0.005% or more.
  • P is an element that degrades the spot weldability, no problem is posed when the P content is 0.05% or less. Accordingly, the P content is preferably 0.05% or less and more preferably 0.02% or less.
  • S is an impurity element that unavoidably mixes and a harmful component that precipitates in steel in the form of MnS to degrade the stretch flangeability of the steel sheet.
  • the S content is preferably 0.01% or less and more preferably 0.005% or less.
  • the Al content is preferably 0.01% or more.
  • the Al content is preferably 0.01% to 0.06% and more preferably 0.02% to 0.06%.
  • the balance other than the above components is Fe and unavoidable impurities.
  • the addition of other components is not necessarily denied as long as the advantageous effects of the present invention are not impaired.
  • the cold-rolled steel sheet according to the present invention has a steel sheet surface from which the Si-containing oxide layer, such as SiO 2 and a Si-Mn composite oxide, formed in the surface layer of the steel sheet during annealing has been removed.
  • the Si-containing oxide layer such as SiO 2 and a Si-Mn composite oxide
  • the surface coverage of the iron-based oxide present on the steel sheet surface needs to be decreased to 40% or less. This is because if the surface coverage is more than 40%, the dissolution reaction of iron in the chemical conversion treatment is inhibited, which suppresses the growth of conversion crystals of zinc phosphate or the like.
  • a coverage of 40% or less is insufficient for cold-rolled steel sheets used for parts, such as chassis parts of vehicles that severely corrode, required to have very high corrosion resistance after coating. Therefore, the surface coverage needs to be further decreased to 35% or less.
  • the surface coverage is preferably 35% or less.
  • the surface coverage of the iron-based oxide is determined by the following method.
  • a steel sheet surface subjected to pickling is observed for about five fields at an acceleration voltage of 2 kV at a working distance of 3.0 mm with about 1000-fold magnification using an ultra-low-voltage scanning electron microscope (ULV-SEM) that can detect information regarding an outermost surface layer.
  • UUV-SEM ultra-low-voltage scanning electron microscope
  • Spectroscopic analysis is performed using an energy-dispersive X-ray diffractometer (EDX) to obtain a backscattered electron image.
  • the backscattered electron image is processed using image analysis software such as Image J. Specifically, the backscattered electron image is converted into a binary representation to measure the area fraction of a black portion. By averaging the measured values in the fields, the surface coverage of the iron-based oxide can be obtained.
  • UUV-SEM ultra-low-voltage scanning electron microscope
  • EDX energy-dispersive X-ray diffractometer
  • a steel slab shown in Table 1 is subjected to hot-rolling, cold-rolling, and continuous annealing under the conditions shown in Table 2 to obtain a cold-rolled steel sheet having a sheet thickness of 1.8 mm.
  • the cold-rolled steel sheet after the continuous annealing is pickled under the conditions shown in Table 3, washed with water, dried, and then temper-rolled at an elongation percentage of 0.7% to obtain two cold-rolled steel sheets No. a and No. b containing different amounts of iron-based oxides on the steel sheet surfaces.
  • a is defined as a standard sample containing a large amount of iron-based oxide
  • the cold-rolled steel sheet No. b is defined as a standard sample containing a small amount of iron-based oxide.
  • Fig. 1 illustrates photographs of the backscattered electron images of the steel sheets No. a and No. b.
  • Fig. 2 illustrates a histogram showing the number of pixels plotted against gray values of the photographs of the backscattered electron images of the steel sheets No. a and No. b.
  • the gray value (Y point) corresponding to an intersection point (X point) of the histogram No. a and the histogram No. b in Fig. 2 is defined as a threshold.
  • the maximum thickness of the iron-based oxide is determined as follows.
  • the coating layer is found to be formed of an iron-based oxide.
  • the distance between the line A that indicates a steel sheet substrate and the line B that indicates the thickest portion of the iron-based oxide layer in the cross-sectional photograph of Fig. 3 is measured for all the ten replicas. The largest distance is defined as the maximum thickness of the iron-based oxide. Note that the size and number of replicas, the measurement conditions with a TEM, and the like are merely examples, and may be obviously changed appropriately.
  • the thus-obtained cold-rolled steel sheet has excellent chemical convertibility and high corrosion resistance after coating evaluated by a hot salt water immersion test or a combined cyclic corrosion test, and therefore can be suitably used for automotive components.
  • the hot-rolled steel sheet was pickled to remove scales and then cold-rolled to obtain a cold-rolled steel sheet having a sheet thickness of 1.8 mm.
  • the cold-rolled steel sheet was subjected to continuous annealing in which the steel sheet was heated to a soaking temperature of 750°C to 780°C and held for 40 to 50 seconds, then cooled from the soaking temperature to a cooling stop temperature of 350°C to 400°C at 20 to 30°C/s, and held in the cooling stop temperature range for 100 to 120 seconds.
  • the steel sheet surface was pickled under the conditions shown in Table 4-1 and Table 4-2, washed with water, dried, and then temper-rolled at an elongation percentage of 0.7% to obtain cold-rolled steel sheets Nos. 2 to 80 in Table 4-1 and Table 4-2.
  • a test specimen was collected from each of the cold-rolled steel sheets.
  • the steel sheet surface was observed for five fields at an acceleration voltage of 2 kV at a working distance of 3.0 mm with 1000-fold magnification using an ultra-low-voltage scanning electron microscope (ULV-SEM, manufactured by SEISS, ULTRA 55).
  • Spectroscopic analysis was performed using an energy-dispersive X-ray diffractometer (EDX, manufactured by Thermo Fisher, NSS312E) to obtain a backscattered electron image.
  • EDX energy-dispersive X-ray diffractometer
  • the backscattered electron image was processed using image analysis software (Image J).
  • the gray value (Y point) corresponding to an intersection point (X point) of the histograms of the standard samples No. a and No. b described above was defined as a threshold.
  • the backscattered electron image was converted into a binary representation to measure the area fraction of a black portion. The average of the measured values in the five
  • test specimen was collected from each of the cold-rolled steel sheets.
  • the test specimen was subjected to a chemical conversion treatment and a coating treatment under the conditions below and then subjected to three corrosion tests of a hot salt water immersion test, a salt spray test, and a combined cyclic corrosion test.
  • the corrosion resistance after coating was evaluated.
  • the depth profiles of O, Si, Mn, and Fe were measured by GDS for the surface of the test specimen collected from each of the cold-rolled steel sheets.
  • Steels A to O having compositions shown in Table 5 were refined through typical refining processes such as a converter process and degassing and continuously cast to obtain steel slabs.
  • Each of the steel slabs was hot-rolled under the hot-rolling conditions shown in Table 6 to obtain a hot-rolled steel sheet having a sheet thickness of 3 to 4 mm.
  • the hot-rolled steel sheet was pickled to remove scales on the steel sheet surface and then cold-rolled to obtain a cold-rolled steel sheet having a sheet thickness of 1.8 mm.
  • the cold-rolled steel sheet was subjected to continuous annealing and pickling under the conditions shown in Tables 6 and 7, then washed with water, dried, and temper-rolled at an elongation percentage of 0.7% to obtain each of cold-rolled steel sheets Nos. 81 to 111.
  • test specimen was collected from each of the thus-obtained cold-rolled steel sheets.
  • the surface coverage of the iron-based oxide on the steel sheet surface after pickling was measured in the same manner as in Example 1. Then, the test specimen was subjected to a tensile test and a test for corrosion resistance after coating described below. Furthermore, the depth profiles of O, Si, Mn, and Fe on the surface of the test specimen collected from each of the cold-rolled steel sheets were measured by GDS.
  • Example 1 A test specimen collected from each of the cold-rolled steel sheets was subjected to a chemical conversion treatment and electrodeposition painting under the same conditions as in Example 1. The test specimen was subjected to three corrosion tests of a hot salt water immersion test, a salt spray test (SST), and a combined cyclic corrosion test (CCT) in the same manner as in Example 1. Thus, the corrosion resistance after coating was evaluated.
  • SST salt spray test
  • CCT combined cyclic corrosion test
  • Table 7 shows the results of the tests (the tensile strength TS is shown in Table 6).
  • the high-strength cold-rolled steel sheets of Invention Examples that contained 0.5% or more of Si and pickled under the conditions of the present invention to decrease the surface coverage of the iron-based oxide on the steel sheet surface to 40% or less had not only excellent chemical convertibility and high corrosion resistance after coating, but also high strength with a tensile strength TS of 590 MPa or more.
  • the depth profiles of O, Si, Mn, and Fe were measured by GDS. It was confirmed that peaks of Si and O did not appear for all the steel sheets pickled under the conditions of the present invention, and thus the Si-containing oxide layer was sufficiently removed.
  • the slab was reheated to a temperature of 1150°C to 1170°C, then hot-rolled at a finishing temperature of 850°C to 880°C, and coiled at a temperature of 500°C to 550°C to obtain a hot-rolled steel sheet having a sheet thickness of 3 to 4 mm.
  • the hot-rolled steel sheet was pickled to remove scales and then cold-rolled to obtain a cold-rolled steel sheet having a sheet thickness of 1.8 mm.
  • the cold-rolled steel sheet was subjected to continuous annealing in which the steel sheet was heated to a soaking temperature of 750°C to 780°C and held for 40 to 50 seconds, then cooled from the soaking temperature to a cooling stop temperature of 350°C to 400°C at 20 to 30°C/s, and held in the cooling stop temperature range for 100 to 120 seconds. Subsequently, the steel sheet surface was pickled under the conditions shown in Table 8, washed with water, dried, and then temper-rolled at an elongation percentage of 0.7% to obtain cold-rolled steel sheets Nos. 112 to 149 in Table 8.
  • a test specimen was collected from each of the cold-rolled steel sheets.
  • the surface coverage and maximum thickness of the iron-based oxide generated on the steel sheet surface as a result of the pickling were measured by the above-described methods.
  • the test specimen collected from each of the cold-rolled steel sheets was subjected to a chemical conversion treatment so that the chemical conversion coating had a coating weight of 1.7 to 3.0 g/m 2 .
  • the chemical conversion treatment was performed using a degreasing agent FC-E2011, a surface controlling agent PL-X, and a chemical conversion treatment agent Palbond PB-L3065 manufactured by Nihon Parkerizing Co., Ltd. under two conditions below which are standard conditions and comparative conditions in which the temperature of the chemical conversion treatment liquid was decreased.
  • the temperature of the chemical conversion treatment liquid in the standard conditions was decreased to 33°C.
  • Electrodeposition painting was performed on the surface of the test specimen subjected to the above chemical conversion treatment using an electrodeposition paint V-50 manufactured by NIPPONPAINT Co., Ltd. so that a layer having a thickness of 25 ⁇ m was formed.
  • the test specimen was subjected to the three corrosion tests below under more strict conditions than those of Example 1.
  • the test specimen was then immersed in a 5 mass% NaCl solution (60°C) for 480 hours, washed with water, and dried.
  • a tape peel-off test was performed by attaching an adhesive tape to a cut mark portion and then peeling off the adhesive tape. The maximum total width of peeling on both left and right sides of the cut mark portion was measured. When the maximum total width of peeling is 5.0 mm or less, the corrosion resistance in the hot salt water immersion test is evaluated to be good.
  • the test specimen was then subjected to a salt spray test for 1400 hours using a 5 mass% aqueous NaCl solution in conformity with a neutral salt spray test specified in JIS Z2371:2000. Subsequently, a tape peel-off test was performed on a crosscut mark portion. The maximum total width of peeling on both left and right sides of the cut mark portion was measured. When the maximum total width of peeling is 4.0 mm or less, the corrosion resistance in the salt spray test is evaluated to be good.
  • the surface of the test specimen (n 1) subjected to the chemical conversion treatment and the electrodeposition painting was cut with a cutter to form a crosscut mark having a length of 45 mm.
  • the test specimen was subjected to a corrosion test in which 150 cycles each including salt spraying (5 mass% aqueous NaCl solution: 35°C, relative humidity: 98%) ⁇ 2 hours ⁇ drying (60°C, relative humidity: 30%) ⁇ 2 hours ⁇ wetting (50°C, relative humidity: 95%) x 2 hours were repeatedly performed.
  • the test specimen was washed with water and dried. Subsequently, a tape peel-off test was performed on a cut mark portion. The maximum total width of peeling on both left and right sides of the cut mark portion was measured. When the maximum total width of peeling is 6.0 mm or less, the corrosion resistance in the combined cyclic corrosion test is evaluated to be good.
  • the steel sheets of Invention Examples had very high corrosion resistance after coating.
  • the depth profiles of O, Si, Mn, and Fe were measured by GDS. It was confirmed that peaks of Si and O did not appear for all the steel sheets pickled under the conditions of the present invention, and thus the Si-containing oxide layer was sufficiently removed.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • General Chemical & Material Sciences (AREA)
  • Cleaning And De-Greasing Of Metallic Materials By Chemical Methods (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
EP15759246.0A 2014-03-04 2015-02-19 Cold-rolled steel sheet, manufacturing method therefor, and car part Active EP3115482B1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2014041089 2014-03-04
PCT/JP2015/000777 WO2015133077A1 (ja) 2014-03-04 2015-02-19 冷延鋼板およびその製造方法、ならびに自動車部材

Publications (3)

Publication Number Publication Date
EP3115482A1 EP3115482A1 (en) 2017-01-11
EP3115482A4 EP3115482A4 (en) 2017-05-10
EP3115482B1 true EP3115482B1 (en) 2022-01-26

Family

ID=54054897

Family Applications (1)

Application Number Title Priority Date Filing Date
EP15759246.0A Active EP3115482B1 (en) 2014-03-04 2015-02-19 Cold-rolled steel sheet, manufacturing method therefor, and car part

Country Status (5)

Country Link
EP (1) EP3115482B1 (es)
JP (1) JP6108028B2 (es)
CN (1) CN106062253B (es)
MX (1) MX2016011278A (es)
WO (1) WO2015133077A1 (es)

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN114318341B (zh) * 2021-12-16 2023-09-05 东风汽车集团股份有限公司 一种铝合金金相腐蚀方法及其金相腐蚀剂

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0328386A (ja) * 1989-06-23 1991-02-06 Daido Steel Co Ltd 金属の酸洗処理方法
JP3021164B2 (ja) * 1992-02-14 2000-03-15 川崎製鉄株式会社 表面光沢の優れるオーステナイト系ステンレス鋼の製造方法
JP3059376B2 (ja) * 1996-03-22 2000-07-04 川崎製鉄株式会社 光沢性および耐食性に優れるオーステナイト系ステンレス鋼板およびその製造方法

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5729211B2 (ja) * 2010-08-31 2015-06-03 Ｊｆｅスチール株式会社 冷延鋼板の製造方法、冷延鋼板および自動車部材
US20150013716A1 (en) * 2012-01-18 2015-01-15 Jfe Steel Corporation Method for prevention of yellowing on surface of steel sheet after pickling
JP2013173976A (ja) * 2012-02-24 2013-09-05 Jfe Steel Corp 冷延鋼板の製造方法およびその製造設備
JP6137089B2 (ja) * 2014-09-02 2017-05-31 Ｊｆｅスチール株式会社 冷延鋼板の製造方法および冷延鋼板の製造設備

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0328386A (ja) * 1989-06-23 1991-02-06 Daido Steel Co Ltd 金属の酸洗処理方法
JP3021164B2 (ja) * 1992-02-14 2000-03-15 川崎製鉄株式会社 表面光沢の優れるオーステナイト系ステンレス鋼の製造方法
JP3059376B2 (ja) * 1996-03-22 2000-07-04 川崎製鉄株式会社 光沢性および耐食性に優れるオーステナイト系ステンレス鋼板およびその製造方法

Also Published As

Publication number Publication date
MX2016011278A (es) 2016-11-25
JP6108028B2 (ja) 2017-04-05
WO2015133077A1 (ja) 2015-09-11
JPWO2015133077A1 (ja) 2017-04-06
EP3115482A1 (en) 2017-01-11
CN106062253A (zh) 2016-10-26
CN106062253B (zh) 2019-10-18
EP3115482A4 (en) 2017-05-10

Similar Documents

Publication Publication Date Title
EP2612957B1 (en) Method for producing cold-rolled steel sheet as well as cold-rolled steel sheet and members for automobile
EP3190211B1 (en) Cold-rolled steel sheet, method for producing cold-rolled steel sheet, automobile member, and equipment for producing cold-rolled steel sheet
EP2612956B1 (en) Method of producing cold-rolled steel sheet as well as cold-rolled steel sheet and members for automobile
EP3399064B1 (en) High-strength cold-rolled steel sheet
EP3409807B1 (en) High-yield ratio high-strength galvanized steel sheet, and method for producing same
EP2801634B1 (en) Hot-dip galvannealed steel sheet
EP3418417B1 (en) High-strength cold-rolled steel sheet
JP2010053371A (ja) 高強度冷延鋼板の製造方法
EP2821515A1 (en) Si-containing high strength cold rolled steel sheet, production method therefor, and vehicle member
JP5835545B2 (ja) Ｓｉ含有熱延鋼板の製造方法
WO2019021695A1 (ja) 高強度冷延鋼板及びその製造方法
EP3321394B1 (en) Process and equipment for producing cold-rolled steel strip
JP5835547B2 (ja) Ｓｉ含有冷延鋼板の製造方法
JP6160655B2 (ja) 熱延鋼板及びその製造方法
EP3115482B1 (en) Cold-rolled steel sheet, manufacturing method therefor, and car part
EP3072982A1 (en) High-strength steel sheet and method for manufacturing same
JP5682366B2 (ja) Ｓｉ含有冷延鋼板の製造方法
JP5835548B2 (ja) Ｓｉ含有冷延鋼板の製造方法

Legal Events

Date Code Title Description
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE

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

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE

17P Request for examination filed

Effective date: 20161004

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

AX Request for extension of the european patent

Extension state: BA ME

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 38/06 20060101ALI20170329BHEP

Ipc: C23G 1/08 20060101AFI20170329BHEP

Ipc: C22C 38/00 20060101ALI20170329BHEP

Ipc: C21D 9/46 20060101ALI20170329BHEP

A4 Supplementary search report drawn up and despatched

Effective date: 20170406

DAX Request for extension of the european patent (deleted)
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: 20190226

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: EXAMINATION IS IN PROGRESS

REG Reference to a national code

Ref country code: DE

Ref legal event code: R079

Ref document number: 602015076655

Country of ref document: DE

Free format text: PREVIOUS MAIN CLASS: C23G0001080000

Ipc: C22C0038020000

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

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 38/06 20060101ALI20210602BHEP

Ipc: C21D 9/46 20060101ALI20210602BHEP

Ipc: C22C 38/04 20060101ALI20210602BHEP

Ipc: C23G 1/08 20060101ALI20210602BHEP

Ipc: C23G 1/00 20060101ALI20210602BHEP

Ipc: C21D 8/04 20060101ALI20210602BHEP

Ipc: C22C 38/02 20060101AFI20210602BHEP

INTG Intention to grant announced

Effective date: 20210628

GRAJ Information related to disapproval of communication of intention to grant by the applicant or resumption of examination proceedings by the epo deleted

Free format text: ORIGINAL CODE: EPIDOSDIGR1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: EXAMINATION IS IN PROGRESS

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

INTC Intention to grant announced (deleted)
INTG Intention to grant announced

Effective date: 20210929

RAP3 Party data changed (applicant data changed or rights of an application transferred)

Owner name: JFE STEEL CORPORATION

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: AT

Ref legal event code: REF

Ref document number: 1465359

Country of ref document: AT

Kind code of ref document: T

Effective date: 20220215

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: 602015076655

Country of ref document: DE

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG9D

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20220126

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 1465359

Country of ref document: AT

Kind code of ref document: T

Effective date: 20220126

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: 20220126

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 FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220126

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: 20220126

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: 20220526

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: 20220426

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: 20220126

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: 20220126

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: 20220126

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: 20220426

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: 20220126

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: 20220126

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: 20220427

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: 20220126

Ref country code: AT

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: 20220126

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

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: 20220526

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20220228

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602015076655

Country of ref document: DE

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

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: 20220126

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: 20220126

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: 20220126

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: 20220126

Ref country code: LU

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

Effective date: 20220219

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: 20220126

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: 20220126

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: 20220126

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: 20220126

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: 20221027

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: 20220228

Ref country code: IE

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

Effective date: 20220219

Ref country code: CH

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

Effective date: 20220228

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

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: 20220126

Ref country code: BE

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

Effective date: 20220228

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

Ref country code: IT

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: 20220126

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: 20150219

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: 20220126

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: 20220126

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

Ref country code: DE

Payment date: 20231228

Year of fee payment: 10

Ref country code: GB

Payment date: 20240109

Year of fee payment: 10

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

Ref country code: FR

Payment date: 20240103

Year of fee payment: 10