EP3347500A1 - Acier, produit plat en acier laminé à chaud à partir d'un tel acier et procédé de fabrication de cet acier - Google Patents

Acier, produit plat en acier laminé à chaud à partir d'un tel acier et procédé de fabrication de cet acier

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Publication number
EP3347500A1
EP3347500A1 EP15763888.3A EP15763888A EP3347500A1 EP 3347500 A1 EP3347500 A1 EP 3347500A1 EP 15763888 A EP15763888 A EP 15763888A EP 3347500 A1 EP3347500 A1 EP 3347500A1
Authority
EP
European Patent Office
Prior art keywords
steel
content
temperature
flat steel
hot
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP15763888.3A
Other languages
German (de)
English (en)
Other versions
EP3347500B1 (fr
Inventor
Wolfgang ARENDT
Ulrich BLÖTNER
Volker Brandenburg
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.)
ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
Original Assignee
ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
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Filing date
Publication date
Application filed by ThyssenKrupp Steel Europe AG, ThyssenKrupp AG filed Critical ThyssenKrupp Steel Europe AG
Publication of EP3347500A1 publication Critical patent/EP3347500A1/fr
Application granted granted Critical
Publication of EP3347500B1 publication Critical patent/EP3347500B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • 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
    • C21D9/22—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for drills; for milling cutters; for machine cutting tools
    • 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
    • C22C38/18—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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling

Definitions

  • the invention relates to a for the production of a graphite-free
  • hot rolled flat steel product suitable steel a hot rolled flat steel product with a graphite-free structure and a method for producing such a hot rolled flat steel product.
  • a particular stress profile results, for example, in agricultural or forestry knives in harvesting use of the fact that the knives, although in principle for example for cutting comparatively soft clippings, such as grass serve, during the cutting process but also on relatively hard parts, such as stones, roots and the like , can meet. If the material of the knife is hard and brittle, there is a risk of knife breakage.
  • straw chopper knives are between about 3 mm and 5 mm thick in practice. They can be both completely tempered as well as only locally edge zone tempered executed. Other knives are at least 1, 3 mm thick, other wear parts, such as. the components used in harrows reach thicknesses of up to 20 mm.
  • the high abrasive wear to which the components made of steels of the type in question are exposed results mainly from the shock and friction loads occurring in use.
  • the steel material has to be separated by different separation processes of the respective starting material forming each hot rolled flat steel product and in one
  • shaping process can be brought into the required form and also be honorable. It should also be suitable for further surface protective or hardness enhancing processes.
  • Impurities (in% by weight) Steel 1: 0.2 - 0.4% C, 0.3 - 0.8% Si, 1, 0 - 2.5% Mn, max. 0.02% P, max. 0.02% S, max. 0.05% AI, max. 2% Cu, 0.1 - 0.5% Cr, max. 2% Ni, 0.1 - 1% Mo, 0.001 - 0.01% B, 0.01 - 1% W, max. 0.05% N, steel 2: 0.35-0.55% C, 0.1-2.5% Si, 0.3-2.5% Mn, max. 0.05% P, max. 0.01% S, max. 0.08% AI, max. 0.5% Cu, 0.1-2.0% Cr, max. 3.0% Ni, max. 1, 0% Mo, max.
  • the invention has this object by a steel alloyed according to claim 1, a hot rolled according to claim 2
  • Carbon is present in the steel according to the invention in contents of 0.4 to 0.7 wt .-% and acts in these levels hardness and strength increasing.
  • the minimum content of 0.4% is required for a sufficient basic hardness.
  • the C content can be limited to 0.6 wt .-%, with optimum rollability of the steel can be ensured if the C content 0.55 wt. % does not exceed.
  • the positive effect of the presence of carbon in the steel according to the invention can be used with particular certainty if the minimum content of carbon is 0.47% by weight.
  • Silicon acts in the steel according to the invention to greatly increase the hardenability and is therefore present in amounts of 0.15-0.5% by weight in the steel according to the invention. At higher levels, it can cause the formation of bad
  • Sulfur acts as a steel accompanying element in the steel according to the invention unfavorable in several respects.
  • the S content should therefore be kept as low as possible. Proportions of not more than 0.0050% by weight of S prove to be favorable, the negative effects of the presence of S in the steel according to the invention being particularly reliably excluded by a limitation to a maximum of 0.0005% by weight.
  • Desulfurization additionally performed a calcium treatment.
  • CaSi is added, as a result of which Ca contents of 0.0005-0.004% by weight of Ca are present in the steel according to the invention.
  • the increase in Si content associated with CaSi addition must be taken into account in the Si content design.
  • the Ca content is limited to 0.0015 wt% in order to avoid the formation of inclusions, which could have a negative effect on the toughness, with particular certainty.
  • the P content of a steel according to the invention may be limited to at most 0.025% by weight. However, in order to be able to use the favorable influence of P, it may be expedient to provide a minimum content of P of 0.001% by weight in the steel according to the invention.
  • Chromium acts both in hardening and strengthening the steel of the invention and is a carbide former. With increasing Cr content, however, the hydrogen permeability is reduced. Below 0.3% by weight of Cr, however, the increase in hardenability and strength would be too low, whereas with Cr contents of more than 1.0% by weight, the hydrogen permeability would be reduced too much. Cr also prevents the early onset of graphite after longer anneals. Due to graphite accumulation, resulting from the hardening process
  • An inventive steel is therefore designed using this positive effect of Cr so that any formation of graphite in the structure is avoided.
  • a Cr content of up to 1 wt .-% is
  • chromium of at least 0.3% by weight prevents unwanted graphitization in steels with simultaneous contents of Ni, Si, Mn, S and Al.
  • the Cr content is to be set as an additional condition for its minimum value so that it corresponds to at least one fifth of the sum of the contents of Ni, Si, Mn, S and Al, which therefore applies:
  • Molybdenum may optionally be added to a steel according to the invention to improve its through-hardenability. If steel flat products with thicknesses of up to 15 mm are produced from steel according to the invention, contents of at least 0.006% by weight are sufficient for this purpose. For larger thicknesses, however, no more than 0.02% by weight should be alloyed, since otherwise there is again the risk of graphite formation in the microstructure.
  • nickel acts both to increase the hardenability and, in particular at low temperatures, to improve the toughness.
  • Minimum content of 0.04 wt .-% is required for this purpose. However, because at too high Ni contents, the graphite formation would be favored, an upper limit of the Ni content of 2 wt .-% is observed. It is particularly safe to use the positive effect of Ni while avoiding negative effects if the Ni content is limited to a maximum of 0.35% by weight.
  • the alloy should be adjusted so that binding of the boron with nitrogen to BN is prevented. So boron full its hardenability-increasing effect it must be dissolved in the steel, so it must not be bound with nitrogen.
  • the steel contains 0.005-0.1% by weight of titanium.
  • Ti forms nitrides, carbonitrides and carbosulfides and thus binds the unfavorable components with respect to the properties of the steel nitrogen and sulfur and at the same time contributes to increase the strength and hardness of the steel according to the invention.
  • the presence of Ti makes it possible to control the austenite grain growth.
  • the Ti content should be at least 0.005 wt .-% and at most 0.1 wt .-%, with Ti contents of up to 0.04 wt .-% proved to be particularly effective in relation to the effect of Ti used in the invention to have.
  • a minimum content of 0.01% by weight may be provided.
  • the respective Ti content "% Ti” can also be set according to the following condition (in% by weight):
  • niobium is provided only as an accompanying element attributable to the unavoidable impurities at levels in which it has no effect. Therefore, the Nb content is limited to at most 0.004 wt%.
  • Vanadium like titanium, is a carbonitride, nitride and carbide-forming agent
  • Nitrogen contributes, especially in the unbound state, to the fatigue strength of the steel according to the invention.
  • a minimum content of 0.0015% by weight is provided in the steel according to the invention.
  • too high a non-set nitrogen content would lead to premature aging and thus to a less favorable processing behavior of the steel according to the invention. Therefore, the N content of the steel is limited to at most 0.010 wt%. Negative effects of the presence of nitrogen can be reliably avoided by lowering the nitrogen content to a maximum of 0.0070% by weight, in particular a maximum of 0.0040% by weight.
  • nitrogen present in the steel according to the invention are sufficient to ensure, in the simultaneous presence of V, the formation of an amount of nitrides, carbides and mixed forms of these precipitates sufficient for the improvement of wear resistance.
  • a further positive effect of nitrogen in the steel according to the invention is that N stabilizes existing iron carbides and therefore hinders graphite formation in the microstructure. Also for this effect, a minimum content of 5 ppm N is to be kept in the steel according to the invention.
  • the hydrogen content in the hot strip shall be limited to not more than 1 ppm in order to prevent hydrogen fractures.
  • Non-metallic inclusions can become sites for hydrogen accumulation, thus reducing hydrogen permeability.
  • the oxygen content of the steel according to the invention is limited to a maximum of 0.0050% by weight, in particular a maximum of 0.0030% by weight.
  • the Al content of the steel according to the invention is limited to a maximum of 0.05% by weight.
  • Copper is also present in the steel according to the invention only as an accompanying element, which has no positive effect on the desired properties of the steel.
  • excessively high Cu contents should be avoided since, in combination with sulfur and iron, Cu forms low-melting compounds which can cause surface defects and edge cracks during hot rolling. Therefore, the Cu content of the steel of the present invention is limited to at most 0.1 wt%.
  • the danger of formation, in particular of edge cracks, can be ruled out particularly reliably if the Cu content of the steel according to the invention is limited to a maximum of 0.012% by weight.
  • the inventive alloy concept based on the inventive combination of Mn, Ti, B and V contents in combination with a higher C content and the additional addition of nickel proves to be successful in the production of hot-rolled steel flat products, in particular
  • Hot-rolled coil thus not only optimized mechanical properties were achieved, which led to a significantly increased fatigue strength, but also minimizes the susceptibility to corrosion.
  • the invention makes it possible to produce much more economically owing to the more resource-conserving, precisely dimensioned alloy of nickel and chromium.
  • An inventive flat steel product is characterized in that it consists of a steel according to the invention and in the uncured state has an at least 80% by volume perlitic, graphite-free structure.
  • the absence of graphite makes the steel particularly suitable for hardening and minimizes the risk of hydrogen build-up in the structure of the steel, which favors the formation of cracks and reduces the fatigue strength of the steel.
  • the flat steel product produced and assembled in accordance with the invention has mechanical properties and wear resistance which, in combination with optimized elongation properties, make it particularly suitable for use with impact loads such as occur anywhere where ground or rock movements or vegetation work with appropriate equipment be made. Examples include agriculture or forestry, but also mining, construction, there in particular civil engineering, and the like. That's how it turns out
  • Steel flat products according to the invention measured transversely to the rolling direction, have a yield strength ReH of 450-650 MPa and a tensile strength Rm of 750-950 MPa and have a uniform elongation Ag of 5-15% and an elongation A80 of 15-30%.
  • flat steel products according to the invention or components produced therefrom have a structure which consists of at least 99% by volume of martensite and the balance of retained austenite.
  • Corrosion susceptibility of a steel flat product made of steel according to the invention or of a component produced therefrom is responsible for a certain combination of precipitates and martensite structure as well as the avoidance of relevant holes in the microstructure.
  • the method according to the invention for producing a flat steel product according to the invention comprises at least the following working steps:
  • the precursor may be a slab, a thin slab or a cast strip
  • this heating can also be in a hold on the respective preheating, when the precursor passes in sufficiently warm state in this step;
  • Hot rolling end temperature is 780 - 880 ° C
  • the method of producing a steel according to the invention is designed to reliably produce flat steel products which are both hot-rolled uncured, i. After cooling in the coil, and after the completed during their treatment steps are free of graphite.
  • the steelmaking process includes a denitrification of the melt to values below 100 ppm N and a secondary metallurgical Ca treatment to achieve minimum S contents.
  • the casting of the molten steel composite according to the invention can be carried out in the strand for the production of slabs or as near-net-shape strip casting with subsequent hot rolling.
  • the respective precursor is hot rolled to a hot strip with a thickness of typically at least 1, 2 mm and a maximum of 20 mm, wherein in the processing of cast strip a minimum thickness of 4 mm should be maintained to avoid adverse effects of systemic occurring coarser inclusions.
  • the preheating temperature i. the temperature to which the slabs are heated before the rolling process, should not be less than 1150 ° C in order to achieve as complete as possible dissolution of the precipitates of the micro-alloying elements formed in the previous casting process.
  • the preheating temperature should not be higher than 1300 ° C in order to avoid the formation of coarse austenite at the beginning of the rolling process.
  • phase transformation takes place in the system Fe-C after a stable or else after the so-called metastable system. Final products are then the carbon compound Fe3C or the pure carbon in the form of graphite. In this process of phase transformation affect the
  • a particularly slow cooling ie with regard to the stable state diagram, must be particularly beneficial for graphite formation.
  • the invention takes this into account in the design of the temperature profile during hot strip production. Long residence times at higher temperatures can be directly or indirectly influenced by other mechanisms
  • Scaling of the strip contributes to slow down the cooling of the hot strip in the coil due to the adjacent turns due to lower heat energy dissipation.
  • the attenuation of the emission by the scale layer and, on the other hand, the low thermal conductivity through the air layer have an effect.
  • particularly thick scale layers break up easily and too
  • the temperature control at higher temperatures is also in the stage of pre-rolling for the later graphite formation formative.
  • steels with relatively high C contents as provided according to the invention, increase Hot rolling temperatures of less than 780 ° C, the rolling forces required for forming clearly. To avoid this, the
  • Hot rolling end temperature when hot rolling according to the invention at least 780 ° C. Above 880 ° C, however, a too coarse and thus arises
  • Hot rolling end temperature according to the invention be at most 880 ° C.
  • the hot strip obtained is placed on a
  • Coil temperature cooled which is 550 - 580 ° C. This cooling can in a conventional manner by means of a suitable medium with a
  • Cooling rate of typically 2 - 50 ° C / s are performed.
  • the coiler temperature is at least 550 ° C, to prevent significant amounts of bainite or martensite from forming in the hot strip instead of the desired perlite.
  • a reel temperature of more than 680 ° C however, a further Austenitkorn growth would be possible, which could adversely affect the toughness of the hot strip and could trigger cracks or fractures during later unwinding in the cooled state.
  • the lower limit of the coiler temperature can be raised to 600 ° C. If optimized toughness properties are to be reliably ensured, the maximum reel temperature can be limited to 650 C C.
  • the temperature-controlled in the above-described manner and to a solid coil, in which the turns of the hot strip are close to each other, wound hot strip is cooled in the coil to a target temperature which is at most 100 ° C in the coil core.
  • Cooling rate of this cooling is in the coil core 4.5 - 14.5 W
  • the target temperature in the core region of the coil should be achieved within 40-120 hours, cooling times of 40-60 hours having proven particularly favorable here.
  • the cooling in the area of the free edges and surfaces of the coil can be done faster. Quenching with cooling media of any kind should be avoided.
  • the coil weight in the case of cooling in air should in practice be at most 38 t. Otherwise there is a risk that graphite will form as a result of too slow a cooling down in the structure.
  • the carbides in the hood furnace can be used individually or in a stack with annealing times of 10 to 100 hours in the temperature range of 660-740 ° C., in particular at temperatures of more than one as 660 ° C to less than 740 ° C, by a suitable method, such as laser cutting or punching, blanks or blanks are divided, from which
  • each of the components to be hot or cold formed in a conventional manner is a conventional manner.
  • a hot rolled flat steel product according to the invention can be cold rolled in a conventional manner, without resulting in the formation of graphite, so that cold worked flat steel products or components can be hardened easily from the flat steel product according to the invention and in the cured state optimum wear resistance and also for the here provided Use have optimal mechanical properties.
  • the hot rolled flat steel product according to the invention can be cold rolled in a conventional manner, without resulting in the formation of graphite, so that cold worked flat steel products or components can be hardened easily from the flat steel product according to the invention and in the cured state optimum wear resistance and also for the here provided Use have optimal mechanical properties.
  • steel flat products according to the invention or the components formed therefrom are subjected to a hardening process in which i) they reach an austenitizing temperature of 830-950 ° C.
  • the austenitizing temperature in step i) should not fall below 830 ° C and the holding time in step j) 3 min to achieve a sufficiently coarse Austenitkorn. This way, due to the
  • Transformation inertia of large austenites avoids the conversion of austenite into softer phase fractions such as ferrite or bainite and promotes the transformation into martensite, so that after hardening in each case
  • Flat steel product or component is present at least 99% of martensite existing structure.
  • the austenitizing temperature should not exceed 950 ° C and the holding time 60 minutes in order to avoid irreversible structural damage due to overheating.
  • the flat steel product or the molded component thereof are quenched in a conventional manner, for example by means of water or oil cooling with a cooling rate of 40 - 250 ° C / s.
  • the cooling rate is at least 40 ° C / s to ensure complete conversion of austenite to martensite.
  • the cooling rate is simultaneously limited to 250 ° C / s to
  • the flat steel product or the component produced therefrom are held for a period of 0.2-2 hours at a tempering temperature of 150-350 ° C., in particular 150-300 ° C., in order to improve the toughness. Subsequently, the respective flat steel product or the component formed therefrom can be cooled in air to room temperature.
  • compositions were melted and shed to slabs.
  • Slabs made of the steels S1, S2, S3, S5 and S6 have been heated to a preheating temperature T1 and then hot rolled starting from a hot rolling start temperature T2 and a hot rolling end temperature T3 to hot strips W1-W8 having a thickness of 2 to 6 mm in a conventional manner.
  • the hot strips were cooled to a coiling temperature T4 at a cooling rate CR1 and wound at this coiler temperature T4 into each coil where the turns were close together.
  • the hot strips W1 - W8 have been cooled over a cooling time t1 in the coil to a target temperature of 100 ° C, wherein the cooling in the core region of the coil was carried out with a cooling rate CR2. After cooling in the coil, the cooling to room temperature in air.
  • Perlite P the ferrite F, the sum of the bainite and martensite B + M, the graphite G and the residual austenite RA have been determined.
  • the hot-rolled samples W1 - W5, W7, W8 additionally each undergo a hardening process, in which they are first subjected to a hardening process
  • Austenitizing temperature T6 is heated, held there over a austenitizing t2 and after the austenitizing t2 with a
  • Cooling rate CR3 have been quenched.
  • Tempering treatment completed in which they have been heated to a tempering temperature T7 and held there for a tempering time t3. After the tempering time t3 has ended, the samples W1-W5, W7, W8 were cooled to room temperature in air.
  • the martensite fraction M For the microstructures of the samples H1 - H5, H7, H8 thus hardened and tempered, the martensite fraction M, the graphite content G and the residual austenite content RA have been determined.
  • the impact strength test according to DIN EN ISO 148-1, January 2011 edition, at 25 ° C on an ISO-V standard specimen, the notched impact strength KBZ and according to DIN ISO 17081, June 2014 edition, the hydrogen diffusion coefficient k has been determined.
  • the hot strip sample W5 already contains the unhardened structure
  • the existing hot-rolled sample W5 which is not according to the invention has the alloy selected in such a way that graphite is formed in the microstructure and accordingly there is the danger of the formation of holes in the steel.
  • Hot strip sample W4 has higher ferrite levels after hot rolling than sample W1. As a result, the cured sample H4 produced from this hot strip sample W4 does not meet the requirement of the present invention
  • the reason for the comparatively high ferrite content is the low Ni content.
  • the hardened steel S1 sample H1 not only has a higher toughness, but also has a particularly favorable fatigue strength, which is a measure of the life of components made from this steel, which is used for example in agricultural equipment become.
  • the hardened samples H7 and H3 not according to the invention achieve fatigue strengths Pü of only a maximum of 183 MPa determined according to DIN 50100, whereas the sample H1 according to the invention with 245 MPa has a significantly better fatigue strength Pü in combination with optimum toughness.
  • the sample H8 not according to the invention has a high hardness, but no good notched impact strength.
  • sample H7 according to the invention achieved only Pü values of less than 190 MPa.
  • the non-inventive, consisting of the non-inventive steel S4 sample H6 was intended for case hardening and therefore has not undergo the curing process according to the invention.
  • the hydrogen diffusion coefficient determined for this sample H6 for comparison was
  • H4 W4 S2 860 30 42 230 1 100 0 0 407 n.a. n / A. n / A.
  • H7 W7 S5 860 30 42 230 1 100 0 0 545 183 4 n.a.

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

Abstract

L'invention concerne un acier, un produit plat en acier fabriqué à partir de cet acier et un procédé pour la fabrication de tels produits plats en acier, qui permettent de fabriquer des produits présentant une combinaison optimisée de ténacité et de résistance à la fatigue en vue de leur utilisation dans le domaine de l'agriculture, de la foresterie ou des applications comparables. L'acier selon l'invention est constitué par (en % en poids) C : 0,4 - 0,7 %, Si : 0,15 - 0,5 %, Mn : 0,8 - 2,0 %, Cr : 0,3 - 1,0 %, la teneur en Cr, %Cr, répondant à chaque fois à la condition suivante : %Cr ≥ (%Ni + %Si + %Mn + %S + %Al)/5, dans laquelle %Ni représente la teneur en Ni, %Si la teneur en Si, %Mn la teneur en Mn, %S la teneur en S et %Al la teneur en Al de l'acier, N : 0,0015 - 0,0100 %, Ni : 0,04 - 2 %, Ti : 0,005 - 0,1 %, V : 0,0080 - 0,1 %, B : 0,0005 - 0,0040 %, Ca : 0,0005 - 0,004 %, P : ≤ 0,03 %, S : ≤ 0,005 %, Al : < 0,05 %, Cu : < 0,1 %, Nb : < 0,004 %, H : < 0,0001 %, O : < 0,005 % ainsi qu'éventuellement Mo : 0,006 - 0,02 %, le reste étant constitué de fer et d'impuretés inévitables. Pour la fabrication d'un produit plat en acier, selon l'invention, une masse fondue d'acier alliée de cette manière est coulée pour obtenir un produit semi-fini, qui est chauffé à une température de préchauffage de 1150 à 1300°C et laminé à chaud à une température de départ de 900 à 1150 °C et à une température finale de 780 à 880 °C. La bande chaude obtenue est refroidie à une vitesse de 2 - 50°C/s à 550 - 680°C et ensuite enroulée en une bobine solide, qui est refroidie à une vitesse de 4,5 - 14,5°C/h dans le noyau de la bobine jusqu'à ≤ 100°C et ensuite refroidie à l'air statique jusqu'à la température ambiante.
EP15763888.3A 2015-09-11 2015-09-11 Acier, produit plat laminé à chaud, et procédé de fabrication de ce prouduit Active EP3347500B1 (fr)

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PCT/EP2015/070880 WO2017041862A1 (fr) 2015-09-11 2015-09-11 Acier, produit plat en acier laminé à chaud à partir d'un tel acier et procédé de fabrication de cet acier

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EP3347500A1 true EP3347500A1 (fr) 2018-07-18
EP3347500B1 EP3347500B1 (fr) 2020-05-20

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DE102018122901A1 (de) 2018-09-18 2020-03-19 Voestalpine Stahl Gmbh Verfahren zur Herstellung ultrahochfester Stahlbleche und Stahlblech hierfür
EP3719147A1 (fr) * 2019-04-01 2020-10-07 ThyssenKrupp Steel Europe AG Produit en acier plat laminé à chaud et son procédé de fabrication
DE102020206298A1 (de) * 2020-05-19 2021-11-25 Thyssenkrupp Steel Europe Ag Stahlflachprodukt und Verfahren zu dessen Herstellung

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JP2000328182A (ja) * 1999-05-13 2000-11-28 Sanyo Special Steel Co Ltd 熱間加工性に優れる機械構造用快削鋼

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