US20180258504A1 - Method of producing a tool steel - Google Patents

Method of producing a tool steel Download PDF

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US20180258504A1
US20180258504A1 US15/761,373 US201615761373A US2018258504A1 US 20180258504 A1 US20180258504 A1 US 20180258504A1 US 201615761373 A US201615761373 A US 201615761373A US 2018258504 A1 US2018258504 A1 US 2018258504A1
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weight
temperature
hot
steel
cooling
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Harald Leitner
Siegfried Gelder
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Voestalpine Boehler Edelstahl GmbH and Co KG
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Boehler Edelstahl GmbH and Co KG
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    • 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
    • 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
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/20—Isothermal quenching, e.g. bainitic hardening
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • 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
    • C22C38/06—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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/44—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
    • 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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/20—Recycling

Definitions

  • the invention relates to a method of producing a tool steel and in particular a hot-work tool steel.
  • tool steels describes steel materials used in particular for the working or reshaping of a multiplicity of materials. It includes amongst others cool-work tool steels, plastic mould steels, metal-ceramic steels and hot-work tool steels.
  • Hot-work tool steels generally describes tool steels which, in use, accept a constant temperature lying in excess of 200° C., while this constant temperature is overlaid by temperature peaks arising from the work cycle. Besides the general mechanical stresses which such steels undergo due to the relevant forming process, they are therefore subject to a further thermal stress. General requirements for hot-work tool steels therefore also include a good so-called fire crack resistance, a type of wear resulting from frequent temperature changes in the surface areas.
  • hot-work tool steels must have resistance to the occurrence of heat cracks, which is ensured by a core requirement of hot-work tool steels, namely so-called thermal toughness.
  • hot-work tool steels must also of course possess high strength, since they are generally subject to impact compression or tension under heat. Not least of importance are of course good wear properties under heat, in particular a low tendency to adhere relative to the materials to be processed, good resistance to erosion, also to high-temperature corrosion and oxidation, together with good dimensional stability, also in the hot state.
  • the properties of steel materials described are determined on the one hand by the chemical analysis of the steel material, but primarily the structure of the hot-work tool steel is critical, in particular for properties such as toughness and strength.
  • properties such as toughness and strength, but also thermal conductivity and other important properties may not be individually enhanced without possible negative effects on other desirable properties.
  • hot-work tool steels often require compromises, on the one hand in respect of their chemical analysis, but on the other hand also in terms of their structural formation.
  • Hot-work tool steels are known for example from CH 165893, in which a chemical analysis is disclosed, also on the other hand a suitable heat treatment for setting certain properties.
  • chromium-tungsten-nickel steels in which the nickel content may be partly or wholly replaced by cobalt, and in which tungsten, cobalt, nickel and chromium may be contained but are preferably chromium-free.
  • WO 2008/017341 A1 is a method of setting the thermal conductivity of a steel, tool steel, in particular hot-work tool steel and a steel article made from the latter.
  • the steel material according to this document should have much greater thermal conductivity than known tool steels but, with an essentially known steel analysis, gives no indication as to how this higher thermal conductivity may be obtained in practice.
  • a steel for hot-work tools involving on the one hand a chemical analysis for a hot-work tool steel and on the other hand a heat treatment with cooling down from a temperature in the range of 900° C. to 1200° C. expediently 1000° C. to 1100° C. and tempering treatment at a temperature in the range of 500° C. to 750° C., so that a hardness of 30 to 60 HRC is obtained.
  • a substantially martensitic structure should be set.
  • bainitic hardness should be less distortion, good dimensional stability, enhanced resistance to crack growth and the scope for generating residual compressive stress in the layer. It has however emerged that the critical disadvantage of bainitic hardening is the comparatively long holding time in the austempering bath.
  • the bainite transformation is a time-intensive process, with the process time depending on the material structure, the composition of the alloy, the temperatures of austenitizing and of the bainite transformation itself.
  • austempering here takes place in a three-stage process, in which firstly austenitizing takes place with, as far as possible, complete transformation of the ferrite into austenite. The part is then cooled down so rapidly to the austempering temperature that no ferrite or pearlite occurs. Finally, the austempering temperature is held constant and the transformation from austenite to bainite takes place gradually.
  • Thermodynamic and kinetic models are presented so that steels with an optimal bainitic microstructure may be developed; these are comprised of a mixture of bainitic ferrite, plastic-enriched residual austenite and some martensite. Using these models, a set of seven carbides-free bainitic steels with 0.3 weight-% carbon is proposed for production.
  • DE 600 300 867 T2 is an ingot steel for the production of injection moulds for plastic material or for the production of workpieces for metal processing, which should have a martensitic or martensitic-bainitic structure with a relatively high chromium content.
  • EP 2 662 460 A1 is a method for the production of steel, in particular as a casting mould or tool, with both a bainitic and also a martensitic phase, wherein the steel should undergo heat treatment including austenitizing followed by rapid cooling, in order to inhibit the formation of stable phases with a transformation temperature above that of the bainite, and to hold the temperature high and long enough to prevent the transformation from austenite to martensite, so that at least 60 percent of the transformation takes place below the martensite start temperature plus 200° C.
  • the martensite start temperature should be ⁇ 480° C.
  • the silicon content at 1.3 percent, should be relatively high, as with many steels which are to be austempered.
  • EP 1 956 100 A1 is a hot-work tool steel and a method for its processing, in which a hot-work tool steel of a given analysis is cooled down to room temperature after solution annealing and then reheated to a temperature above Ac1 and subsequently cooled down to room temperature once more, then subjected to heat treatment, with austenitizing carried out during the first heat treatment.
  • EP 2 006 398 A1 is a method for the production of a steel material in which a steel material is completely austenitised and then cooled down to the temperature of the pearlite nose of the corresponding steel alloy, where it is held until complete pearlite transformation.
  • EP 1 887 096 A1 is a hot-work tool steel which is intended to have a considerably higher thermal conductivity than known hot-work tool steels, for which purpose it has a special analysis, which is however practical for any hot-work tool steel
  • the problem of the invention is to create a method for the production of a hot-work tool steel which ensures bainite transformation in an economically feasible short length of time.
  • the problem is solved by a method with the features of claim 1 .
  • a further problem is to create a hot-work tool steel with which the method may be implemented.
  • the problem is solved by a method with the features of claim 7 .
  • the austempering according to the invention of the steel material is brought about by providing that, after austenitizing treatment of the steel, it is cooled down to s holding temperature and is held at this holding temperature until austempering is completed.
  • the steel material according to the invention makes it possible for the austempering holding time to lie in roughly the same time range as the austenitizing holding time, which means that austempering is made possible in a time which is absolutely economical.
  • the holding time depends in particular on material strength and material quantity respectively, i.e. in particular the time within which the necessary holding temperatures occur.
  • this austempering may be measured in a dilatometer and, for the respective steel material, the relevant period of time depending on material strength may be determined.
  • the reduction in temperature following austenitizing is also accompanied by shrinkage due to reduced thermal expansion wherein, immediately after the holding temperature has been reached a relative change in length occurs due to the formation of the bainite.
  • the possible bainite transformation is completed wherein, as explained above, a complete bainite transformation may be achieved with the steel material according to the invention in contrast to customary hot-work tool steels. Cooling down to room temperature then takes place, leading to further shrinkage, wherein however as compared with the material before bainite transformation, the material after bainite transformation does not return to the value before transformation, but remains somewhat above it.
  • FIG. 1 the measurement of the change in length over the temperature programme in a dilatometer test of a steel according to the invention
  • FIG. 2 a representation of the change in length relative to temperature during heating up and cooling down including the isothermal holding time
  • FIG. 3 the course of the change in length relative to temperature during heating up and cooling down after the isothermal transformation
  • FIG. 4 the micro-section of the completely austempered but not tempered steel material at an isothermal holding temperature of 330° C.
  • FIG. 5 the micro-section of a steel material according to the invention, which shows complete transformation, austempered at 360° C. and not tempered;
  • FIG. 6 the course of the relative change in length and temperature during a dilatometer test with a conventional hot-work tool steel
  • FIG. 7 the course of the relative change in length depending on the temperature during heating up and cooling down including an isothermal holding step, for a conventional hot-work tool steel
  • FIG. 8 the course of the relative change in length and temperature during the dilatometer test at a holding temperature of 340° C., for a conventional hot-work tool steel
  • FIG. 9 the course of the relative change in length depending on the temperature during heating up and cooling down including an isothermal holding at 340° C., for a conventional hot-work tool steel;
  • FIG. 10 the bainite content depending on holding temperature and holding time for a conventional hot-work tool steel, showing that a complete bainite transformation is not possible;
  • FIG. 11 hardness and notch-bend impact energy for a steel according to the invention which has undergone bainite transformation according to the invention, dependent on tempering temperature;
  • FIG. 12 temperature conductivity and thermal conductivity of a steel which has been heat-treated according to the invention and a steel which has not been austempered according to the invention;
  • FIG. 13 the residual austenite content depending on the cooling rate for a steel according to the invention which is not heat-treated according to the invention
  • FIG. 18 an example of a heat treatment curve.
  • the steel according to the invention for implementing the method according to the invention with the result of a complete bainitic structure (if not otherwise stated, all percentage details are weight-%) has the following composition:
  • the remainder is iron and impurities due to smelting.
  • Such a steel is smelted and alloyed in the usual manner for hot-work tool steels.
  • such a steel is firstly austenitized at a temperature which lies at least above the austenitizing temperature (Ac 3 ) and ensures a complete full austenitizing of the material or workpiece.
  • a certain holding time may be necessary, depending on the workpiece and its dimensions.
  • austenitizing which is conducted at heating rates of 300° C./h to 400° C./h
  • the alloying position determines the cooling rate. Irrespective of the cooling rate, the cooling must be carried out with sufficient speed that no bainite transformation takes place during cooling.
  • FIG. 18 An example of heat treatment is revealed by FIG. 18 , wherein the specimen has dimensions of 370 mm ⁇ 150 mm ⁇ 60 mm.
  • the broken line indicates the required furnace value or furnace temperature and the solid line shows the temperature development of the test specimen material. It can be seen that, during a first heating-up to 650° C., the material follows and with a holding time of four hours, the furnace required temperature is also reached by the charge actual value. There then follows a further heating stage, which includes a rise of approx. 200° C./h and lasts for around two hours. After around one and a half hours, the material here also reaches the required temperature value and is then heated at a heating rate of approx. 260° C./h to the austenitizing temperature of over 1100° C. This temperature is reached relatively quickly by the material.
  • the holding times for austempering lie substantially in the range of holding times for austenitizing, which was previously unachievable in any circumstances.
  • a further test specimen in the form of a notched-bar specimen measuring 55 mm ⁇ 10 mm ⁇ 10 mm is heated to austenitizing temperature, with the austenitizing set at 1090° C.
  • the test specimen is held at this temperature for 15 min. and then cooled down to 330° C.
  • the rate of cooling is around 40° C. per second.
  • test specimens are held isothermally for 17 min. and then cooled down to room temperature.
  • the resultant change in length of the dilatometer test specimen over the temperature range is shown in FIG. 1 .
  • the temperature rise on the one hand and the relative change in length on the other hand are shown as percentages, wherein it is evident that, after the rapid cooling down from the austenitizing temperature to 330° C., a relative extension takes place, which approaches a maximum which is held. With the subsequent cooling down there is an irreversible lengthening even at room temperature as compared with the very small extension after reaching the austempering temperature.
  • FIG. 1 The resultant change in length of the dilatometer test specimen over the temperature range is shown in FIG. 1 .
  • the temperature rise on the one hand and the relative change in length on the other hand are shown as percentages, wherein it is evident that, after the rapid cooling down from the austenitizing temperature to 330° C., a relative extension takes place, which approaches a maximum which is held. With the subsequent cooling down there is an irreversible lengthening even at room temperature as compared with the very small extension
  • the relative change in length is plotted as a percentage against temperature, wherein it may be seen that, on completion of cooling down from the austenitizing temperature to the austempering temperature with isothermal holding, a change in length results, so that a hysteresis loop occurs, in particular between heating up and cooling down.
  • FIG. 4 shows the micro-section of the dilatometer test specimen, with the Vickers hardness amounting to 494, while the Rockwell hardness (HRC) comes to 50.5. A complete transformation of the material into bainite may be seen from the micro-section. The residual austenite content is ⁇ 1% and is therefore insignificant for the material properties.
  • example 1 The material of example 1 is smelted and alloyed in a comparable manner and then subjected to comparable heat treatment, wherein however the cooling down from the austenitizing temperature of 1090° C. is to 360° C., with the cooling rate coinciding with that of example 1.
  • the micro-section made after cooling down to room temperature, is shown in FIG. 5 .
  • the residual austenite content is >1%, while Vickers hardness is 494 and Rockwell hardness (HRC) comes to 47.
  • HRC Rockwell hardness
  • FIG. 6 shows the pattern of the relative change in length and temperature during the dilatometer test.
  • the material according to example 3 is austenitized in the same manner at 1030° C., but cooled down to an isothermal holding temperature of 340° C.
  • the pattern of the relative change in length depending on temperature during heating and cooling down including the isothermal holding time is here shown in FIGS. 8 and 9 , while here too it is evident that, although a certain lengthening due to bainite formation does take place, the lengthening then reduces and in particular a closed hysteresis curve is not obtained.
  • notch-bend impact energy and hardness respectively corresponding to FIG. 11 may be observed.
  • the Rockwell hardness may be varied between 47 and 52, while in each case notch-bend impact energy lies between 8 joules at room temperature (i.e. in the untempered state) and 5 to 6 joules, indicating very even hardness and toughness.
  • the material according to the invention is subjected to a conventional heat treatment on the dilatometer, with the test specimen dimensions corresponding to those of the previous examples.
  • ⁇ in this case being the cooling parameter, which is usual in the heat treatment of tool steels. It indicates in hectoseconds the time needed for cooling down a steel from 800° C. to 500° C.
  • Hardness and residual austenite patterns for different ⁇ -values are evident from FIG. 13 wherein, with slow cooling, hardness as expected falls from around 550 Vickers hardness to 325 Vickers hardness, whereas residual austenite content increases with rising ⁇ -values.
  • the material according to the invention has a martensitic structure, with the structure pattern shown in FIG. 14 , similarly the relative change in length and temperature during cooling.
  • the material according to the invention discloses this potential only with the heat treatment according to the invention; a conventional heat treatment does not lead to the desired result.

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  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
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US15/761,373 2015-08-07 2016-08-03 Method of producing a tool steel Abandoned US20180258504A1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
DE102015113058.0 2015-08-07
DE102015113058.0A DE102015113058A1 (de) 2015-08-07 2015-08-07 Verfahren zum Herstellen eines Werkzeugstahles
PCT/EP2016/068495 WO2017025397A1 (de) 2015-08-07 2016-08-03 Verfahren zum herstellen eines werkzeugstahles

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US (1) US20180258504A1 (de)
EP (1) EP3332040B1 (de)
KR (1) KR20180032631A (de)
CN (1) CN107835861A (de)
CA (1) CA2989091A1 (de)
DE (1) DE102015113058A1 (de)
ES (1) ES2862927T3 (de)
SI (1) SI3332040T1 (de)
WO (1) WO2017025397A1 (de)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113897547A (zh) * 2021-10-08 2022-01-07 内蒙古北方重工业集团有限公司 Cr-Mo-V型中碳热作模具钢及其组织球化方法

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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AT144892B (de) 1931-11-24 1936-03-10 Rudolf Bellak Stahllegierungen, insbesondere für Warmarbeitswerkzeuge, und Werkzeuge oder Gegenstände, welche in hohem Maße Unempfindlichkeit gegen Temperaturschwankungen, Maßhaltigkeit, Warmzerreißfestigkeit und Zähigkeit aufweisen.
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JPH07179988A (ja) * 1993-12-24 1995-07-18 Aichi Steel Works Ltd 高温強度の優れた熱間工具鋼
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CA2989091A1 (en) 2017-02-16
SI3332040T1 (sl) 2021-07-30
WO2017025397A1 (de) 2017-02-16
DE102015113058A1 (de) 2017-02-09
EP3332040A1 (de) 2018-06-13
KR20180032631A (ko) 2018-03-30
EP3332040B1 (de) 2021-03-03

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