EP3553197B1 - Fil d'acier à haute résistance présentant une excellente résistance à la corrosion et son procédé de fabrication - Google Patents

Fil d'acier à haute résistance présentant une excellente résistance à la corrosion et son procédé de fabrication Download PDF

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Publication number
EP3553197B1
EP3553197B1 EP17878243.9A EP17878243A EP3553197B1 EP 3553197 B1 EP3553197 B1 EP 3553197B1 EP 17878243 A EP17878243 A EP 17878243A EP 3553197 B1 EP3553197 B1 EP 3553197B1
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EP
European Patent Office
Prior art keywords
steel wire
corrosion resistance
wire rod
wire
high strength
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Application number
EP17878243.9A
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German (de)
English (en)
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EP3553197A4 (fr
EP3553197A1 (fr
Inventor
Choong-Yeol Lee
Yong-Sik Park
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Posco Holdings Inc
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Posco Co Ltd
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Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C21D2211/002—Bainite

Definitions

  • the present invention relates to a high strength steel wire, and more particularly, to a high strength steel wire having excellent corrosion resistance and a method for manufacturing the same.
  • An armor cable is a reinforcing material supporting the load on a flexible pipe transporting crude oil at sea, and requires high strength, as well as corrosion resistance in a corrosive environment.
  • a method for obtaining required physical properties in the armor cable may be as follows.
  • First is a method of increasing the strength of material itself by adding a large amount of elements that increase the strength of steel.
  • a representative example of strength increasing elements of steel is carbon. As the carbon content increases, the fraction of cementite, a hard phase, increases in a wire rod, and the lamellar spacing of a pearlite structure becomes significantly small, thereby improving the strength of a material.
  • carbon is effective for improving strength, but inhibits corrosion resistance. Therefore, there is a limit to selecting an appropriate content according to a use environment.
  • Second is a method of drastically improving strength by drawing out a wire rod and imparting work hardening thereto.
  • the drawing material is obtained by drawing and heat treating a rolled wire rod to be processed to form a final wire.
  • the lamellar spacing becomes significantly small, the work hardening coefficient increases, and dislocations accumulate, thereby imparting work hardening.
  • strength of a tire cord material may be improved by increasing drawing strain on the tire cord material.
  • the drawing strain of the material is closely related to ductility of the material, if there is no disconnection in a workpiece itself during a drawing process and the process thereof is facilitated, the material may be advantageous to improve strength.
  • KR 2016 0063553 A discloses a steel wire comprising by weight%, 0.07 to 0.15% of carbon (C), 2.7 to 3.5% of manganese (Mn), 0.10 or less of silicon (Si), 0% to 0.8% of chromium (Cr), 0.01 to 0.02% of titanium (Ti), 0.001 to 0.003% of boron (B), 0.05% or less of Nitrogen (N), 0.015% or less of Sulphur (S) and a remainder of iron (Fe) and unavoidable impurities.
  • the microstructure of the steel wire is a mixture including bainite.
  • KR 2016 0063565 A also discloses a steel wire comprising by weight%, 0.07 to 0.15% of carbon (C), 2.7 to 3.5% of manganese (Mn), 0.50 to 1.50% of silicon (Si), 0% to 0.8% of chromium (Cr), 0.01 to 0.02% of titanium (Ti), 0.001 to 0.003% of boron (B), 0.05% or less of Nitrogen (N), 0.015% or less of Sulphur (S) and a remainder of iron (Fe) and unavoidable impurities.
  • the microstructure of the steel wire is a mixture including bainite.
  • KR 20160075957 A also discloses a high strength, high corrosion resistance steel wire for a flexible pipe for transporting crude oil at sea and a method of manufacturing the same.
  • the present invention is to provide a steel wire having high strength as well as high corrosion resistance even with the omission of a heat treatment, and a method for manufacturing the same.
  • a high strength steel wire having excellent corrosion resistance includes, by weight%, 0.07 to 0.15% of carbon (C), 2.7 to 3.5% of manganese (Mn), 0.10 to 0.50% of silicon (Si), 0% to 0.8% of chromium (Cr), 0.01 to 0.02% of titanium (Ti), 0.001 to 0.003% of boron (B), 0.005% or less of Nitrogen (N), 0.015% or less of Sulphur (S) and a remainder of iron (Fe) and other unavoidable impurities, wherein the microstructure of the steel wire consists of a bainite phase.
  • a method of manufacturing a high strength steel wire having excellent corrosion resistance includes producing a wire rod including, by weight%, 0.07 to 0.15% of carbon (C), 2.7 to 3.5% of manganese (Mn), 0.10 to 0.50% of silicon (Si), 0% to 0.8% of chromium (Cr), 0.01 to 0.02% of titanium (Ti), 0.001 to 0.003% of boron (B), 0.005 or less of Nitrogen (N), 0.015% or less of Sulphur (S) and a remainder of iron (Fe) and unavoidable impurities; cold-drawing the wire rod at a total reduction ratio of 40 to 80% to produce a cold drawn wire rod; and cold-rolling the cold drawn wire rod at a total reduction ratio of 50 to 90% to produce a cold rolled material, wherein the producing of the wire rod comprises preparing a billet; heating the billet at a temperature of 1000 to 1100°C; finishing wire-rolling the heated billet at a temperature of 950
  • a steel wire having high strength, even with the omission of an LP heat treatment process, may be provided, and a steel wire according to an embodiment of the present disclosure exhibits an effect of securing excellent corrosion resistance.
  • a steel wire according to an embodiment of the present disclosure may be advantageously applicable to usage of requiring high strength and high corrosion resistance.
  • the inventors have conducted in-depth research to provide a steel wire that may be suitably used in environments requiring high corrosion resistance as well as high strength. As a result, it has been found that a steel wire having a microstructure advantageous for simultaneously securing both high strength and high corrosion resistance may be provided by optimizing an alloy composition and manufacturing conditions of steel, and thus the present disclosure has been obtained.
  • a high strength steel wire having excellent corrosion resistance includes, by weight%, 0.07 to 0.15% of carbon (C), 2.7 to 3.5% of manganese (Mn), 0.10 to 0.50% of silicon (Si), 0% to 0.8% of chromium (Cr), 0.01 to 0.02% of titanium (Ti), 0.001 to 0.003% of boron (B) 0.005% or less of Nitrogen (N), 0.015% or less of Sulphur (S) and a remainder of iron (Fe) and unavoidable impurities.
  • Carbon (C) is an element favorable for improving the strength of a steel wire. If the content of C is less than 0.07%, the strength is lowered. On the other hand, if the content of C exceeds 0.15%, the strength is improved, while ductility is decreased. In detail, corrosion resistance characteristics of the steel wire tend to decrease as the content of C increases.
  • the content of C is controlled to be 0.07 to 0.15% in terms of ensuring strength and corrosion resistance of the steel wire.
  • the content of C may be 0.09 to 0.13%.
  • Manganese (Mn) is an element to secure an intended microstructure as well as improving quenching properties of a steel wire. If the content of Mn is less than 2.7%, it may be difficult to secure quenching properties, and thus, there is a problem in which a required microstructure and strength may not be obtained. On the other hand, if the content of Mn exceeds 3.5%, there is a problem in which ductility is significantly lowered.
  • the content of Mn is controlled to be 2.7 to 3.5%, and, in more detail, 2.8 to 3.3%.
  • Silicon (Si) is an element favorable for a deoxidation effect, and Si may be added in an amount of 0.10% or more to obtain a sufficient deoxidation effect. If the content of Si is less than 0.10%, a deoxidation effect is insufficient and there is a possibility that inclusions will increase, which leads to a high possibility that ductility and corrosion resistance will be degraded. On the other hand, if the content of Si exceeds 0.50%, drawability and plate rolling properties are deteriorated.
  • the content of Si is controlled to be 0.10 to 0.50%, and, in more detail, 0.15 to 0.40%.
  • Chromium (Cr) is an element favorable for securing a bainite phase as the microstructure of a steel wire by securing quenching properties, and is also an element for strength improvement.
  • Cr may be further included for the above-mentioned effect, but if the content exceeds 0.8%, there is a fear that a martensite phase may be formed as a microstructure, to deteriorate drawability.
  • the content of Cr is controlled to be 0.8% or less when Cr is added, and even in a case in which Cr is not added, since a required microstructure and strength may be secured, 0% is included.
  • Titanium (Ti) is a most reactive element with nitrogen (N), and forms nitrides in the steel.
  • N nitrogen
  • TiN is a most reactive element with nitrogen (N)
  • B boron
  • Ti is added in an amount of 0.01% or more, but when the content exceeds 0.02%, a coarse nitride is formed to deteriorate mechanical properties.
  • the Ti content is controlled to be 0.01 to 0.02%, and in more detail, to be 0.012 to 0.07%.
  • Boron (B) is an element which is advantageous for improving hardenability of steel, and provides an effect of diffusing into an austenite grain boundary system to suppress formation of ferrite during cooling and increase quenching properties.
  • B may be added in an amount of 0.001% or more. However, if the content exceeds 0.003%, not only the above effect is saturated but also boron-based nitride precipitates, deteriorating grain boundary strength and lowering hot workability.
  • the content of B is controlled to be 0.001 to 0.003%.
  • an upper limit of the nitrogen (N) forming the TiN is limited to 0. 005%, such that boron (B) in steel may be maintained in a solid solution state, instead of precipitates (ex., BN), to sufficiently exhibit an effect of improving hardenability.
  • sulfur (S) forms low melting sulfides to deteriorate hot rolling properties and deteriorate drawing processability
  • an upper limit of S is limited to 0.015%.
  • the remainder is iron (Fe).
  • impurities which are not intended may be inevitably incorporated from a raw material or a surrounding environment, which cannot be excluded. These impurities are known to those skilled in the manufacturing field, and thus, are not specifically mentioned in this specification.
  • a steel wire according to an embodiment of the present disclosure satisfying the alloy composition described above includes a bainite single phase as a microstructure.
  • a uniform bainite phase with a microstructure is formed, thereby providing a steel wire having high strength and high corrosion resistance, and simultaneously, providing a technical significance in that an existing LP heat treatment process may be omitted.
  • the steel wire according to an embodiment of the present disclosure having a bainite phase as a microstructure, has a yield strength of 1100 MPa or more and a tensile strength of 1200 MPa or more.
  • the steel wire according to an embodiment has not only high strength but also excellent corrosion resistance in which sulfuric acid corrosion loss is 800g/mm 2 ⁇ h or lower.
  • a steel wire according to an embodiment in the present disclosure may be produced by a process of manufacturing a wire rod satisfying the above-described alloy composition, and then, of drawing the wire rod.
  • wire rod may be manufactured through a variety of wire rod manufacturing techniques known in the art, in detail, the wire rod may be manufactured through a series of processes to be described below.
  • a billet satisfying the above-mentioned alloy composition is manufactured, and may then be subjected to a heating process of homogenizing the billet.
  • a microstructure of the billet may be formed as an austenite single phase through the heating process.
  • the heating is performed in a temperature range of 1000 to 1100°C. If the heating temperature is less than 1000°C, it may be difficult to secure a temperature region in subsequent wire rolling. If the heating temperature exceeds 1100°C, austenite grains are formed coarsely and a target level of strength may be difficult to secure.
  • the billet heated as described above is subjected to wire rolling, and then, is cooled to be produced as a wire rod.
  • finishing hot rolling is performed in a temperature range of 950 to 1100°C. If a temperature during the finishing hot rolling is less than 950°C, there is a problem in which roll life is reduced due to an increase in a rolling load. On the other hand, if the temperature exceeds 1100°C, the grain size becomes coarse, and thus, ductility may be reduced. Further, in this case, decarburization may occur excessively, thereby deteriorating drawability.
  • a wire rod having a bainite phase is manufactured by cooling at a cooling rate of 1 to 3°C/s. If the cooling rate is less than 1°C/s, there is a fear that a structure such as pearlite or the like, other than the bainite phase, may be formed as a microstructure, while if the cooling rate exceeds 3°C/s, there is a fear that a martensite phase may be formed.
  • a steel wire is manufactured by drawing the wire rod manufactured as described above.
  • descriptions of an LP heat treatment generally performed before the wire rod is drawn will be omitted.
  • the wire rod having a uniform bainite phase is subjected to a drawing process, homogeneity and a relatively high work-hardening ratio may be secured without performing a separate LP heat treatment.
  • the wire rod may be directly cold-drawn without a LP heat treatment process, and in this case, a cold drawn wire rod is manufactured by performing cold drawing on the wire rod at a reduction ratio of 40 to 80% in total.
  • the reduction ratio is less than 40% in cold drawing, since the amount of drawing processing is insufficient, sufficient strength may not be secured. On the other hand, if the reduction ratio exceeds 80%, cracks may occur.
  • the cold drawn wire rod as described above may have a yield strength of 1000 MPa or more and a tensile strength of 1100 MPa or more.
  • the cold drawn wire rod is cold rolled, and in this case, a cold rolled material is produced by cold rolling at a total reduction ratio of 50 to 90%.
  • the cold rolling is to obtain a steel wire having a plate-like shape. If the reduction ratio in this case is less than 50%, a processing amount is insufficient and sufficient strength may not be ensured. On the other hand, if the reduction ratio exceeds 90%, cracks may occur.
  • the cold-rolled material as described above may have a yield strength of 1100 MPa or more and a tensile strength of 1200 MPa or more.
  • a billet having an alloy composition shown in the following Table 1 was prepared, and then, the billet was heated at 1000 to 1100°C and then hot-rolled at 1000°C to produce a wire rod. Thereafter, the wire rod was cooled to 500°C at a cooling rate of 1 to 3°C/s, followed by air-cooling to room temperature.
  • Inventive Steels 1 to 6 which satisfy an alloy composition proposed in the present disclosure, were cold rolled at a total reduction ratio of 50 to 90%, after performing drawing at a total reduction ratio of 40 to 80%, thereby producing a steel wire.
  • Comparative Steels 1 to 4 were subjected to an LP heat treatment and then subjected to a drawing process (a total reduction ratio of 40 to 80%) and cold rolling (a total reduction ratio of 50 to 90%).
  • Inventive Steels 1 to 6 having a bainite phase as a microstructure a work hardening rate is relatively high, and thus, required high strength may be obtained through a drawing process and cold rolling without performing an LP heat treatment, as compared with Comparative Steels 1 to 4 having a pearlite phase.
  • Inventive Steels 1 to 6 exhibited a corrosion loss of 550g/mm 2 ⁇ h or lower, which indicates that a corrosion rate was reduced by about 50% under the same conditions as Comparative Steels 1 to 4.
  • the corrosion resistance may be improved by removing a ferrite phase which adversely affects corrosion resistance characteristics of a steel wire and forming a bainite phase.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)

Claims (6)

  1. Fil d'acier à haute résistance ayant une excellente résistance à la corrosion, comprenant :
    en % en poids, 0,07 à 0,15 % de carbone (C), 2,7 à 3,5 % de manganèse (Mn), 0,10 à 0,50 % de silicium (Si), 0 % à 0,8 % de chrome (Cr), 0,01 à 0,02 % de titane (Ti), 0,001 à 0,003 % de bore (B), 0,005 % ou moins d'azote (N), 0,015 % ou moins de soufre (S) et un reste de fer (Fe) et des impuretés inévitables,
    la microstructure du fil d'acier étant constituée d'une phase bainite.
  2. Fil d'acier à haute résistance ayant une excellente résistance à la corrosion selon la revendication 1, dans lequel le fil d'acier a une perte par corrosion d'acide sulfurique de 800 g/mm2•h ou moins dans une solution d'acide sulfurique à 5 %.
  3. Fil d'acier à haute résistance ayant une excellente résistance à la corrosion selon la revendication 1, dans lequel le fil d'acier a une limite d'élasticité de 1 100 MPa ou plus et une résistance à la traction de 1 200 MPa ou plus.
  4. Procédé de fabrication d'un fil d'acier à haute résistance ayant une excellente résistance à la corrosion, le procédé comprenant :
    la production d'un fil machine comportant, en % en poids, 0,07 à 0,15 % de carbone (C), 2,7 à 3,5 % de manganèse (Mn), 0,10 à 0,50 % de silicium (Si), 0 % à 0,8 % de chrome (Cr), 0,01 à 0,02 % de titane (Ti), 0,001 à 0,003 % de bore (B), 0,005 % ou moins d'azote (N), 0,015 % ou moins de soufre (S) et un reste de fer (Fe) et des impuretés inévitables ;
    l'étirage à froid du fil machine à un rapport de réduction total de 40 à 80 % pour produire un fil machine étiré à froid ; et
    le laminage à froid du fil machine étiré à froid à un rapport de réduction total de 50 à 90 % pour produire un matériau laminé à froid, dans lequel la production du fil machine comprend la préparation d'une billette ; le chauffage de la billette à une température de 1 000 à 1 100 °C ; la finition du laminage de fil de la billette chauffée à une température de 950 à 1 100 ° C pour produire un fil machine ; et le refroidissement du fil machine à une vitesse de refroidissement de 1 à 3 °C/s.
  5. Procédé de fabrication d'un fil d'acier à haute résistance ayant une excellente résistance à la corrosion selon la revendication 4, dans lequel le fil machine étiré à froid a une limite d'élasticité de 1 000 MPa ou plus et une résistance à la traction de 1 100 MPa ou plus.
  6. Procédé de fabrication d'un fil d'acier à haute résistance ayant une excellente résistance à la corrosion selon la revendication 4, dans lequel le matériau laminé à froid a une limite d'élasticité de 1 100 MPa ou plus et une résistance à la traction de 1 200 MPa ou plus.
EP17878243.9A 2016-12-08 2017-11-29 Fil d'acier à haute résistance présentant une excellente résistance à la corrosion et son procédé de fabrication Active EP3553197B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
KR1020160166820A KR101917436B1 (ko) 2016-12-08 2016-12-08 내식성이 우수한 고강도 강선 및 이의 제조방법
PCT/KR2017/013821 WO2018105944A1 (fr) 2016-12-08 2017-11-29 Fil d'acier à haute résistance présentant une excellente résistance à la corrosion et son procédé de fabrication

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EP3553197A4 EP3553197A4 (fr) 2019-10-16
EP3553197A1 EP3553197A1 (fr) 2019-10-16
EP3553197B1 true EP3553197B1 (fr) 2020-09-30

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EP (1) EP3553197B1 (fr)
KR (1) KR101917436B1 (fr)
CN (1) CN110036130B (fr)
WO (1) WO2018105944A1 (fr)

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CN110036130B (zh) 2022-07-05
KR101917436B1 (ko) 2019-01-24
EP3553197A4 (fr) 2019-10-16
WO2018105944A1 (fr) 2018-06-14
EP3553197A1 (fr) 2019-10-16
KR20180065669A (ko) 2018-06-18
CN110036130A (zh) 2019-07-19

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