EP3828293B1 - Verfahren zur herstellung eines korrosionsbeständigen matrizenstahls - Google Patents

Verfahren zur herstellung eines korrosionsbeständigen matrizenstahls Download PDF

Info

Publication number
EP3828293B1
EP3828293B1 EP19840865.0A EP19840865A EP3828293B1 EP 3828293 B1 EP3828293 B1 EP 3828293B1 EP 19840865 A EP19840865 A EP 19840865A EP 3828293 B1 EP3828293 B1 EP 3828293B1
Authority
EP
European Patent Office
Prior art keywords
cooling
steel
holding
parts
forging
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
EP19840865.0A
Other languages
English (en)
French (fr)
Other versions
EP3828293A4 (de
EP3828293A1 (de
Inventor
Xu LUO
Junhong Li
Xujiang LIU
Qiang XIAO
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.)
Pangang Group Panzhihua Iron and Steel Research Institute Co Ltd
Original Assignee
Pangang Group Panzhihua Iron and Steel Research Institute Co Ltd
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 Pangang Group Panzhihua Iron and Steel Research Institute Co Ltd filed Critical Pangang Group Panzhihua Iron and Steel Research Institute Co Ltd
Publication of EP3828293A1 publication Critical patent/EP3828293A1/de
Publication of EP3828293A4 publication Critical patent/EP3828293A4/de
Application granted granted Critical
Publication of EP3828293B1 publication Critical patent/EP3828293B1/de
Active 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D7/00—Casting ingots, e.g. from ferrous metals
    • B22D7/005—Casting ingots, e.g. from ferrous metals from non-ferrous metals
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • C21D1/60—Aqueous agents
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • C21D1/613—Gases; Liquefied or solidified normally gaseous material
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/62—Quenching devices
    • C21D1/667—Quenching devices for spray quenching
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
    • C22B9/00—General processes of refining or remelting of metals; Apparatus for electroslag or arc remelting of metals
    • C22B9/16—Remelting metals
    • C22B9/18—Electroslag remelting
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium

Definitions

  • the present invention relates to corrosion resistant mirror die steel and a manufacturing method therefor, and belongs to the technical field of die steel products.
  • the die molding is a common practice for electric appliance parts, electromechanical industrial parts, rubber products, ceramic products and plastic products; so, the quality, efficiency and development ability of the products are largely determined by the die.
  • die failure occurs frequently in shape change and dimensional overrun, due to some complex factors such as high temperature, pressure and stress for a long time.
  • Basic failure modes are manifested as surface wear and corrosion, fracture, deformation and accidental damage of the die. Therefore, the die steel should present high wear resistance, corrosion resistance, strength, hardness and other properties. With the most productive and largest proportion in the die steel, plastic die steel has developed rapidly in recent years, which makes a higher demand for product quality.
  • Corrosion resistant plastic die steel has medium-high carbon content and high chromium content, and belongs to a higher grade of plastic die steel. It reveals good corrosion resistance against chlorine, fluorine and other gases, and presents good strength, hardness and wear resistance.
  • common steel grades are 2Crl3, 3Crl3, 4Crl3, 9Crl8, 9Crl8Mo and 1Crl7Ni2; whereas, overseas steel grades are represented by Krupp's GS-083 series; of which 4Crl3 is a typical medium carbon high chromium martensitic corrosion resistant steel with good machining property, which can obtain high strength and wear resistance, good polishing property and excellent corrosion resistance after heat treatment (quenching and tempering).
  • CN103060698A discloses a preparation process of corrosion resistant die steel, wherein the die steel comprises the following compositions in percentage by weight: 1.0-1.2% of C, 16-19% of Cr, 1.3-1.8% of Co, 0.2-0.6% of Mn, 0.2-0.7% of Si, 0.9-1.4% of Mo, 0.05-0.2% of V, 0.05 -0.4% of Ti, 0.05-0.4% of rare earth, and the balance of iron.
  • the preparation method is as follows: treating with Ti and rare earth while melting in an electric furnace; preparing 100-300 kg of ingot, electroslag remelting, and rolling to obtain flat steel with rolling deformation of 50-70%; then heating the flat steel to 650-760 °C, holding for 5-6 h, furnace cooling to 280-320 °C, holding for 3-5 h, then heating to 650-690 °C, holding for 32 h, cooling to 400 °C at 40 °C/h, and then cooling to 120 °C at 18 °C/h; carrying out heat treatment on the flat steel obtained above, heating to 1,000 °C, holding for 1-2 h, oil cooling to not more than 100 °C, reheating to the temperature range of 680 °C-710 °C, holding for 3 h, and then water cooling; after tempering, heating the head of flat steel to 320-400 °C, holding for 4-5 h, then spray cooling, keeping the tail of flat steel at 900-1,020 °C, holding for
  • the above preparation process requires the addition of many alloying elements and rare earth elements La and Ce to ensure high hardness and toughness of die steel.
  • rare earth elements can neutralize the impurities such as oxygen and sulfur in the steel resulting in violent reactions, so as to purify the steel and significantly improve the overall performance of steel.
  • the process causes a great waste of precious resources and a significant increase in production costs.
  • the ingot prepared by this method has small weight, limiting its scope of promotion and application.
  • the purpose of the present invention is to provide a manufacturing method for a corrosion resistant mirror die steel, aiming at solving the problem of high production cost in the prior art, resulting from the addition of rare earth elements and a large number of alloying elements to improve the overall performance of the die steel.
  • the present invention provides a manufacturing method of corrosion resistant mirror die steel as defined in claim 1 and comprising the following steps: smelting into molten steel, casting into billets, pre-forging annealing, forging, post-forging annealing, and heat treating; wherein,
  • the quenching comprises the following steps: discharging, air cooling for 2-3 min, spray cooling for 3-5 min, water cooling to the surface temperature of 690-710 °C, air cooling for 3-5 min, proceeding to water cooling to the surface temperature of 390-410 °C, air cooling for 3-5 min, proceeding to water cooling to the surface temperature of 190-210 °C, and removing from the heat treatment tank for air cooling.
  • the spray cooling pressure is 5-8 MPa; the water cooling pressure is 7-16 MPa; the air cooling speed is 2-4 m/s.
  • the casting comprises the step of obtaining steel ingots by die casting, wherein the die casting adopt bottom pouring with inert gas protection at the casting nozzle.
  • the inert gas is argon.
  • the slag system used for the electroslag remelting comprises CaF 2 , CaO, Al 2 O 3 , MgO and SiO 2 .
  • the slag system comprises the following components in parts by weight: 50 parts of CaF 2 , 30 parts of CaO, 10 parts of Al 2 O 3 , 5 parts of MgO and 5 parts of SiO 2 .
  • the heating temperature is not less than 1,200 °C, and the holding time is 12-15 h in the pre-forging annealing step.
  • the heating temperature is 1230-1250 °C in the forging step, and the billets are forged into the specifications with thickness of 300-600 mm, width of 800-1350 mm, length of being more than 3000mm, and total rolling deformation of 60-80%.
  • the post-forging annealing step comprises the following sub-steps: heating the forged module to 600-650 °C, holding for 4-8 h, furnace cooling to 280-350 °C, holding for 2-6 h, heating to 650-700 °C, holding for 25-35h, cooling to 390-410 °C at 30-60 °C/h, and cooling to 140-160 °C at 15-20 °C/h.
  • the present invention provides corrosion resistant mirror die steel obtained according to the manufacturing method.
  • novel corrosion resistant mirror die steel of optimized Changzhi steel 4Cr13 is developed by adopting a vanadium-titanium micro-alloyed composition route, and the die steel mainly has the following advantages: 1, high hardness, almost HRC35-50; 2, small hardness fluctuation range, ⁇ 1.5HRC; 3, high corrosion resistance, the surface of the specimen is bright as before after the specimen is soaked in 50% high concentration nitric acid at 50 °C for 120 h and in 15% acetic acid for 48 h; additionally, the surface of the specimen has not lost its metallic luster and no pitting corrosion is observed after soaking in hydrochloric acid medium at room temperature for 48 h; 4, high toughness, the impact value can reach 31J at room temperature; and 5, large module die steel can be obtained (thickness: 300-600mm, width: 800-1350mm, length>3000mm).
  • the raw materials and equipment used in specific embodiments of the present invention are all well-known products, which can be purchased in the market.
  • the molten steel obtained by smelting in the present invention has the following chemical components in percentage by weight: 0.35%-0.45% of C, 12%-15% of Cr, Co ⁇ 0.05%, 0.4%-0.7% of Mn, 0.35%-0.55% of Si, 0.08%-0.20% of Mo, 0.10%-0.30% of Ni, 0.08%-0.30% of W, 0.10%-0.30% of V, 0.01-0.05% of Ti, P ⁇ 0.020%, S ⁇ 0.012%, and the balance of Fe.
  • the Cr content is controlled to be not less than 12%, so as to ensure good corrosion resistance of the die steel.
  • Mo forms M 6 C-type carbide in steel, which precipitates to increase the solid solubility of Cr and improve wear resistance; on the other hand, the addition of Mo can cause dispersion hardening after tempering, which is conducive to improving the secondary hardness and thermal stability of steel, increasing the tempering brittleness temperature, and avoiding the occurrence of tempering brittleness.
  • Role of Ni the addition of a small amount of Ni can improve the toughness of steel, the thermal fatigue performance of modules and the hardenability.
  • Role of V 1, vanadium can improve the thermal strength, creep resistance and high-temperature durability of steel; 2, vanadium can improve the stability of steel in high-temperature and high-pressure hydrogen, so that the stability of steel to hydrogen can be more than 600 °C at high pressure; 3, in pearlite low-alloy steel, vanadium can prevent the graphitization of molybdenum steel at high temperature; and 4, through the precipitation in the final ferrite structure, VN precipitates are formed in a dispersed and finely distributed manner to improve the strength, toughness and fatigue resistance.
  • Role of Ti the addition of trace Ti forms Ti (CN) precipitates, which play a role in refining the grain during the heating process of the slab; whereas fine and diffusely distributed TiC precipitates in the final ferrite organization play a role in strengthening precipitation, and also improve the welding performance of the finished products.
  • CN trace Ti forms Ti
  • the present invention achieves the effect of improving the comprehensive mechanical properties of the die steel, especially the corrosion resistance and wear resistance of the steel, mainly by controlling the content of Cr, Mo, Ni, V, Ti and other elements, thereby avoiding the use of rare earth metals, reducing the total addition amount of alloy elements and significantly reducing the production cost.
  • impurity elements S and P have a detrimental effect on the toughness of the die steel.
  • the dynamic polarization of S, P and other impurity elements toward the grain boundary will damage the high-temperature plasticity and toughness of dies, resulting in their high-temperature embrittlement cracking.
  • Relevant studies have shown that the reduction of S and P content helps to improve the cold and hot fatigue properties of steel.
  • the present invention is able to control the P content below 0.020% and the S content below 0.012% through the refining process by avoiding the use of rare earth metals and reducing the total addition of alloying elements and the introduction of impurities such as S and P in general, thereby reducing or even eliminating the harm of trace impurity elements, improving the quality of die steel, and providing them with excellent corrosion resistance, wear resistance, hardness, toughness and other properties.
  • the manufacturing method of corrosion resistant mirror die steel of the present invention comprises a heat treating step, which is the key to ensure the comprehensive mechanical properties of the die steel.
  • the specific process comprises the following steps: heating to 1,120 °C-1,200 °C, holding for 12-20 h, quenching, and tempering at 500-590 °C for 5-20 h.
  • the quenching + high-temperature tempering treatment of steel by using this method can fully strengthen micro-alloy and control uniform precipitation, eliminate white spots, improve the transverse properties of the die, refine grains, and achieve uniform structure, so as to meet the requirements of mirror polishing of die steel and ensure its corrosion resistance, wear resistance and other properties.
  • Another advantage of the above heat treatment process lies in tempering treatment of large modules (thickness: 300-600 mm, width: 800-1,350 mm, length>3000mm).
  • the heat treatment process for large modules of corrosion resistant and wear-resistant mirror plastic die steel (hardness range: HRC35-50, hardness fluctuation ⁇ 3HRC) has not yet been reported.
  • the production process of the die steel of the present invention is as follows: primary smelting in electric furnace -> vacuum treatment outside the refining furnace (LF+VD furnace refining) ⁇ molten steel die casting ⁇ electroslag remelting ⁇ large module heating -> forging processing (thickness: 300-600 mm, width: 800-1350 mm, length >3000mm) ⁇ finished module annealing ⁇ heat treatment (quenching + tempering) ⁇ packaging and warehousing.
  • the molten steel obtained by smelting has the following chemical components in percentage by weight: 0.35%-0.45% of C, 12%-15% of Cr, Co ⁇ 0.05%, 0.4%-0.7% of Mn, 0.35%-0.55% of Si, 0.08%-0.20% of Mo, 0.10%-0.30% of Ni, 0.08%-0.30% of W, 0.10%-0.30% of V, 0.01-0.05% of Ti, P ⁇ 0.020%, S ⁇ 0.012%, and the balance of Fe.
  • Die casting based on bottom pouring, casting in the presence of argon to avoid oxidation at the casting nozzle, and weak blowing argon for being not less than 15 min before VD furnace tapping.
  • Casting temperature 1,530-1,540 °C; air in the ingot die is discharged by blowing argon in the ingot die before casting steel to prevent nitrogen in air from entering the molten steel, resulting in nitrogen increase.
  • Electroslag remelting the method of electroslag smelting is used to control the quality of steelmaking considering that the steel structure should be uniform and the hard spots like internal oxide inclusions should be as little as possible.
  • the specific process is as follows: one tip of the consumable electrode is inserted into the molten slag that is contained in the copper water-cooled crystallizer.
  • the consumable electrode, slag bath, metal melt pool, ingots, bottom water tank are formed into a circuit through a short-networked conductors and transformers.
  • the slag bath emits Joule heat to gradually melt the consumable electrode tip, and the molten metal converges into liquid droplets, which pass through the slag bath and fall into the crystallizer, forming a metal melt pool, where it is rapidly solidified to form ingot by water cooling.
  • steel and slag are in full contact and non-metallic inclusions in steel are absorbed by the slag. Harmful elements in the steel (sulfur, lead, antimony, bismuth and tin) are removed relatively effectively by means of the steel-slag reaction and high temperature gasification.
  • the slag system is a five-element slag system, which is based on CaF 2 and mixed with proper oxides such as CaO, Al 2 O 3 , MgO and SiO 2 .
  • the ratio of the five element slag system is 50% of CaF 2 , 30% of CaO, 10% of Al 2 O 3 , 5% of MgO, 5% of SiO 2 , which is well adaptative to the special steel electroslag remelting, and has high resistance and melting speed.
  • the heating temperature should be not less than 1,200 °C and the holding time is 12-15 h.
  • Forging a) at the forging heating temperature of 1,230-1,250 °C, forging large module die steel ingots into the required size with thickness of 300-600 mm, width of 800-1,350mm, length of being more than 3000mm and rolling deformation of 60-80%; and placing the forged large module for holding for 4-8 h, and furnace cooling to 280-350 °C and holding for 2-6 h; and b) reheating the ingots obtained in step a to 650-700 °C, holding for 25-35 h, cooling to 400 °C at 30-60 °C/h, and then cooling to 150 °C at 15-20 °C/h.
  • Heat treatment a) heating the large module die steel obtained in steps 1), 2) and 3) to 1,120 °C-1,200 °C, and holding for 12-20 h; quenching: discharging, air cooling for 2-3 min, spray cooling for 3-5 min, water cooling to the surface temperature of 700 °C, air cooling for 3-5 min, proceeding to water cooling to 400 °C, air cooling for 3-5 min, proceeding to water cooling to 200 °C, and removing from the heat treatment tank for air cooling; wherein the spray cooling pressure is 5-8 MPa, the air cooling speed is 2-4 m/s, and the water cooling pressure is 7-16 MPa; and (b) tempering process: the tempering temperature is 500-590 °C, and tempering time is 5-20 h.
  • the hardness values are HRC47.5, HRC46.5 and HRC46, with a hardness fluctuation range not more than 1. 5HRC, and the impact value is 31J at room temperature (20°C).
  • the surface of the specimen is bright as before and the quality thereof remains the same after the specimen is soaked in 50% high concentration nitric acid at 50 °C for 120 h and in 15% acetic acid for 48 h; additionally, the surface of the specimen has not lost its metallic luster and no pitting corrosion is observed after soaking in hydrochloric acid medium at room temperature for 48 h.

Landscapes

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

Claims (1)

  1. Herstellungsverfahren von korrosionsbeständigem Spiegel-Matrizenstahl, gekennzeichnet durch Umfassen der folgenden Schritte: Schmelzen in eine Stahlschmelze, Gießen in Barren, Glühen vor dem Schmieden, Schmieden, Glühen nach dem Schmieden, und Wärmebehandlung; wobei
    die Stahlschmelze aus den folgenden chemischen Komponenten in Gewichtsprozent besteht: 0,35 % bis 0,45 % C, 12 % bis 15 % Cr, Co ≤ 0,05 %, 0,4 % bis 0,7 % Mn, 0,35 % bis 0,55 % Si, 0,08 % bis 0,20 % Mo, 0,10 % bis 0,30 % Ni, 0,08 % bis 0,30 % W, 0,10 % bis 0,30 % V, 0,01 % bis 0,05 % Ti, P ≤ 0,020 %, S ≤ 0,012 % und dem Rest Fe;
    die Wärmebehandlung die folgenden Schritte umfasst: Erwärmen auf 1120-1200 °C, Halten über 12-20 h, Abschrecken, und Tempern bei 500-590 °C über 5-20 h, wobei das Abschrecken die folgenden Schritte umfasst: Ausbringen, Luftkühlung über 2-3 min, Sprühkühlung über 3-5 min, Wasserkühlung auf die Oberflächentemperatur von 690-710 °C, Luftkühlung über 3-5 min, Übergehen zur Wasserkühlung auf die Oberflächentemperatur von 390-410 °C, Luftkühlung über 3-5 min, Übergehen zur Wasserkühlung auf die Oberflächentemperatur von 190-210 °C, und Entfernen aus dem Wärmebehandlungsbehälter zur Luftkühlung, und der Druck der Sprühkühlung 5-8 MPa beträgt; der Druck der Wasserkühlung 7-16 MPa beträgt; die Geschwindigkeit der Luftkühlung 2-4 m/s beträgt;
    das Gießen den Schritt des Erhaltens von Stahlblöcken durch Druckgießen umfasst, wobei das Druckgießen steigendes Gießen mit Argongasschutz an der Gießdüse anwendet;
    Elektroschlackeumschmelzen an den Barren durchgeführt wird und das für das Elektroschlackeumschmelzen verwendete Schlackesystem CaF2, CaO, Al2O3, MgO und SiO2 umfasst, wobei das Schlackesystem die folgenden Komponenten in Gewichtsteilen umfasst: 50 Teile CaF2, 30 Teile CaO, 10 Teile Al2O3, 5 Teile MgO und 5 Teile SiO2;
    in dem Schritt des Glühens vor dem Schmieden die Erwärmungstemperatur nicht weniger als 1200 °C beträgt, und die Haltezeit 12-15 h beträgt;
    in dem Schritt des Schmiedens die Erwärmungstemperatur 1230-1250 °C beträgt, und die Barren in Spezifikationen mit einer Dicke von 300-600 mm, einer Breite von 800-1350 mm, einer Länge, die mehr als 3000 mm beträgt, und einer Gesamtverformung durch Walzen von 60-80 % geschmiedet werden; und
    der Schritt des Glühens nach dem Schmieden die folgenden Teilschritte umfasst:
    Erwärmen des geschmiedeten Moduls auf 600-650 °C, Halten über 4-8 h, Ofenkühlung auf 280-350 °C, Halten über 2-6 h, Erwärmen auf 650-700 °C, Halten über 25-35 h, Kühlen auf 390-410 °C bei 30-60 °C/h, und Kühlen auf 140-160 °C bei 15-20 °C/h.
EP19840865.0A 2018-07-26 2019-07-24 Verfahren zur herstellung eines korrosionsbeständigen matrizenstahls Active EP3828293B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN201810833317.1A CN108866444B (zh) 2018-07-26 2018-07-26 耐腐蚀镜面模具钢及其制备方法
PCT/CN2019/097543 WO2020020243A1 (zh) 2018-07-26 2019-07-24 耐腐蚀镜面模具钢及其制备方法

Publications (3)

Publication Number Publication Date
EP3828293A1 EP3828293A1 (de) 2021-06-02
EP3828293A4 EP3828293A4 (de) 2021-12-22
EP3828293B1 true EP3828293B1 (de) 2025-02-12

Family

ID=64305191

Family Applications (1)

Application Number Title Priority Date Filing Date
EP19840865.0A Active EP3828293B1 (de) 2018-07-26 2019-07-24 Verfahren zur herstellung eines korrosionsbeständigen matrizenstahls

Country Status (5)

Country Link
EP (1) EP3828293B1 (de)
KR (1) KR102562391B1 (de)
CN (1) CN108866444B (de)
UA (1) UA127856C2 (de)
WO (1) WO2020020243A1 (de)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2853835C1 (ru) * 2025-06-09 2025-12-26 федеральное государственное бюджетное образовательное учреждение высшего образования "Санкт-Петербургский горный университет императрицы Екатерины II" Способ термической обработки стальных изделий

Families Citing this family (20)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108866444B (zh) * 2018-07-26 2021-01-26 攀钢集团攀枝花钢铁研究院有限公司 耐腐蚀镜面模具钢及其制备方法
CN112853201A (zh) * 2019-11-28 2021-05-28 武汉昆伦特钢装备科技开发有限公司 一种超高强高硬耐磨抗冲击耐蚀的合金钢及制造工艺
CN113061801A (zh) * 2021-02-08 2021-07-02 中航上大高温合金材料股份有限公司 一种耐蚀镜面模具钢及制造方法
CN113481357B (zh) * 2021-06-30 2022-06-21 江苏省沙钢钢铁研究院有限公司 塑料模具钢板及其生产方法
CN114540703B (zh) * 2022-01-26 2022-09-27 江苏宏晟模具钢材料科技有限公司 一种高韧性、高抛光性、耐腐蚀的塑胶模具钢及其制备方法
CN114836689B (zh) * 2022-04-25 2023-04-07 宁国东方碾磨材料股份有限公司 一种高铬耐磨钢球及其制备方法
CN114875334B (zh) * 2022-05-31 2022-10-25 宝武集团鄂城钢铁有限公司 一种预硬型镜面塑料模具钢及其冶炼方法
CN115109986B (zh) * 2022-07-11 2023-10-10 中国铁建重工集团股份有限公司 一种大尺寸电渣重熔高锰钢锻坯及其制造方法
CN115821147B (zh) * 2022-12-06 2024-10-18 四川六合特种金属材料股份有限公司 一种改善镜面模具钢纯净度及组织均匀性的方法
CN115852261B (zh) * 2022-12-26 2024-07-26 河南中原特钢装备制造有限公司 一种截面硬度均匀的镜面塑料模具钢及其制造方法
CN116219123A (zh) * 2023-01-30 2023-06-06 东北特殊钢集团股份有限公司 一种马氏体-铁素体型耐蚀塑料模具扁钢的调质工艺
CN116397177B (zh) * 2023-02-23 2025-05-30 江苏宏晟模具钢材料科技有限公司 一种高韧性、高均匀性、高纯净、大尺寸压铸用热作模具钢及其制备方法
CN116175099B (zh) * 2023-02-27 2024-10-22 鞍钢股份有限公司 一种耐腐蚀模具用特厚模块钢的生产方法
CN116555681A (zh) * 2023-04-17 2023-08-08 江阴兴澄特种钢铁有限公司 一种具有微观结构的耐腐蚀及抗酸性钢板及制造方法
CN116657034A (zh) * 2023-04-21 2023-08-29 成都先进金属材料产业技术研究院股份有限公司 一种耐腐蚀塑料模具钢及制备方法
CN116716542A (zh) * 2023-06-13 2023-09-08 四川六合特种金属材料股份有限公司 一种耐热耐蚀高强韧性塑料模具钢及其制备工艺
CN117051331A (zh) * 2023-08-18 2023-11-14 深圳市国科六点科技有限公司 一种适用于热锻模具的热作模具钢及制备工艺
CN117448658B (zh) * 2023-09-20 2026-01-23 成都先进金属材料产业技术研究院股份有限公司 一种热作模具钢微观组织均匀性调控方法
CN118480664A (zh) * 2024-05-22 2024-08-13 山西太钢不锈钢股份有限公司 一种耐蚀塑模钢ttrm圆钢的生产方法
CN119351695B (zh) * 2024-10-24 2026-01-13 大冶特殊钢有限公司 一种大型镜面塑料模具钢的热处理方法

Family Cites Families (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2002088450A (ja) * 2000-09-14 2002-03-27 Daido Steel Co Ltd 熱間工具鋼
CN100402690C (zh) * 2005-04-18 2008-07-16 宝钢集团上海五钢有限公司 4Cr16Mo 模具钢镜面大模块的制备生产方法
CN1876881A (zh) * 2005-06-02 2006-12-13 大同特殊钢株式会社 塑料成形模具用钢
CN101967608A (zh) * 2010-11-12 2011-02-09 上海大学 一种含氮耐蚀塑料模具钢及其制备工艺
JP2013132659A (ja) * 2011-12-27 2013-07-08 Mitsubishi Heavy Ind Ltd 金型部品の製造方法
CN103060698B (zh) 2012-10-23 2015-12-02 合肥康龄养生科技有限公司 一种耐腐蚀模具钢的制备工艺
JP2015045071A (ja) * 2013-08-29 2015-03-12 山陽特殊製鋼株式会社 鏡面性に優れた耐食性プラスチック成形金型用鋼
AT515157B1 (de) * 2013-11-21 2016-12-15 Böhler Edelstahl GmbH & Co KG Verfahren zur Herstellung von Kunststoffformen aus martensitischem Chromstahl und Kunststoffform
KR20160041869A (ko) * 2016-03-28 2016-04-18 두산중공업 주식회사 열전도도가 향상된 다이케스팅 및 핫스템핑용 자동차용 금형강 및 그 제조방법
CN106350643B (zh) * 2016-11-14 2018-11-16 成都先进金属材料产业技术研究院有限公司 一种大型模具钢的热处理方法
CN106636895A (zh) * 2016-11-30 2017-05-10 重庆材料研究院有限公司 特种轴承钢及其制造方法
CN108866444B (zh) * 2018-07-26 2021-01-26 攀钢集团攀枝花钢铁研究院有限公司 耐腐蚀镜面模具钢及其制备方法

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2853835C1 (ru) * 2025-06-09 2025-12-26 федеральное государственное бюджетное образовательное учреждение высшего образования "Санкт-Петербургский горный университет императрицы Екатерины II" Способ термической обработки стальных изделий

Also Published As

Publication number Publication date
EP3828293A4 (de) 2021-12-22
UA127856C2 (uk) 2024-01-24
CN108866444A (zh) 2018-11-23
EP3828293A1 (de) 2021-06-02
KR102562391B1 (ko) 2023-08-01
WO2020020243A1 (zh) 2020-01-30
CN108866444B (zh) 2021-01-26
KR20210053290A (ko) 2021-05-11

Similar Documents

Publication Publication Date Title
KR102562391B1 (ko) 내식성 미러 다이강 및 이의 제조 방법
CN101954547B (zh) 高硅超低碳不锈钢焊丝及其水平连铸连轧连拔制造方法
CN100402690C (zh) 4Cr16Mo 模具钢镜面大模块的制备生产方法
CN102443741B (zh) 用于球磨机的钢球的制造方法
CN101954548B (zh) 一种超低碳稀土不锈钢焊丝及其制造方法
CN105525226A (zh) 一种马氏体不锈钢盘条及其制造方法
CN112981233B (zh) 一种适于冷锻加工的低硅中碳齿轮钢及其制造方法
CN101565801A (zh) 一种高碳铬轴承钢及其制造方法
CN101173343A (zh) 一种高强度耐磨铸钢衬板及其制造方法
CN113215472B (zh) 铌钒微合金化高强细晶非调质冷镦钢方坯及其制造方法
CN115896634B (zh) 一种耐高温有色金属压铸成型模具钢材料及其制备方法
CN102653843A (zh) 一种渗碳轴承钢
CN116121629B (zh) 一种齿轮钢18CrNiMo7-6的制备方法
CN109609845A (zh) 一种500MPa级耐候钢及其生产方法
CN114807558A (zh) 一种矿山钻头用ex50v圆钢的生产方法
CN116790983A (zh) 一种优质低碳低硅焊接用热轧盘条及其制备方法
CN115125457A (zh) 一种连铸大圆坯生产的耐-50℃低温石化热交换器管板用钢及其制造方法
CN112981228A (zh) 一种良好冷锻性能的变速器传动齿轴用钢棒材及制造方法
CN102418044A (zh) 一种钢球用钢及制造该钢球的方法
CN116005062B (zh) 高强度高耐蚀奥氏体不锈钢冷轧卷板及其制备方法
CN115896624B (zh) 一种氮化钢31CrMoV9退火材及其生产方法
CN119910160B (zh) 一种复合铸造耐磨轧辊制备方法
CN115889457A (zh) 一种直接切削加工用非调质机械结构钢的生产方法
CN120485645A (zh) 一种低成本耐磨性良好的磨球用钢及其生产方法
CN119243045A (zh) 一种综合力学性能良好的热处理钢轨及其制备方法

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: 20210210

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

DAV Request for validation of the european patent (deleted)
DAX Request for extension of the european patent (deleted)
A4 Supplementary search report drawn up and despatched

Effective date: 20211123

RIC1 Information provided on ipc code assigned before grant

Ipc: C21D 9/00 20060101ALI20211117BHEP

Ipc: C22B 9/18 20060101ALI20211117BHEP

Ipc: C21D 8/00 20060101ALI20211117BHEP

Ipc: C21D 6/00 20060101ALI20211117BHEP

Ipc: C21D 1/25 20060101ALI20211117BHEP

Ipc: C21D 1/613 20060101ALI20211117BHEP

Ipc: B22D 7/00 20060101ALI20211117BHEP

Ipc: C21D 1/667 20060101ALI20211117BHEP

Ipc: C21D 1/60 20060101ALI20211117BHEP

Ipc: C22C 38/46 20060101ALI20211117BHEP

Ipc: C22C 38/44 20060101ALI20211117BHEP

Ipc: C22C 38/40 20060101ALI20211117BHEP

Ipc: C22C 38/04 20060101ALI20211117BHEP

Ipc: C22C 38/02 20060101ALI20211117BHEP

Ipc: C21D 1/56 20060101ALI20211117BHEP

Ipc: C21D 1/26 20060101ALI20211117BHEP

Ipc: C22C 38/50 20060101ALI20211117BHEP

Ipc: C21D 1/18 20060101AFI20211117BHEP

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: 20231129

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

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

Free format text: STATUS: GRANT OF PATENT IS INTENDED

INTG Intention to grant announced

Effective date: 20241018

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: DE

Ref legal event code: R096

Ref document number: 602019065898

Country of ref document: DE

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20250212

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

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: 20250512

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

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: 20250212

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: 20250212

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

Effective date: 20250212

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG9D

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: 20250612

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: 20250512

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: 20250212

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

Ref country code: HR

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

Effective date: 20250212

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

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: 20250212

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: 20250612

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: 20250212

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: 20250513

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 1766106

Country of ref document: AT

Kind code of ref document: T

Effective date: 20250212

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: 20250212

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: 20250212

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

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: 20250212

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: 20250212

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

Effective date: 20250212

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: 20250212

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: 20250212

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

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: 20250212

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

Ref country code: SK

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

Effective date: 20250212

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602019065898

Country of ref document: DE

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

REG Reference to a national code

Ref country code: CH

Ref legal event code: L10

Free format text: ST27 STATUS EVENT CODE: U-0-0-L10-L00 (AS PROVIDED BY THE NATIONAL OFFICE)

Effective date: 20251224

26N No opposition filed

Effective date: 20251113

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 602019065898

Country of ref document: DE

REG Reference to a national code

Ref country code: CH

Ref legal event code: H13

Free format text: ST27 STATUS EVENT CODE: U-0-0-H10-H13 (AS PROVIDED BY THE NATIONAL OFFICE)

Effective date: 20260224

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: 20250724

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

Effective date: 20250724

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20250731

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

Ref country code: GB

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

Effective date: 20250724

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: 20260203

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: 20250731

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

Ref country code: CH

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

Effective date: 20250731

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

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: 20250212

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: 20250724

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: 20250212

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

Ref country code: FR

Payment date: 20260617

Year of fee payment: 8

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

Effective date: 20250212