EP2746409A1 - Procédé de traitement à chaud d'un produit en manganèse-acier et produit en manganèse-acier doté d'un alliage spécial - Google Patents

Procédé de traitement à chaud d'un produit en manganèse-acier et produit en manganèse-acier doté d'un alliage spécial Download PDF

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Publication number
EP2746409A1
EP2746409A1 EP12198817.4A EP12198817A EP2746409A1 EP 2746409 A1 EP2746409 A1 EP 2746409A1 EP 12198817 A EP12198817 A EP 12198817A EP 2746409 A1 EP2746409 A1 EP 2746409A1
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Prior art keywords
steel product
content
range
weight
cooling
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Ceased
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EP12198817.4A
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German (de)
English (en)
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Erfindernennung liegt noch nicht vor Die
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Voestalpine Stahl GmbH
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Voestalpine Stahl GmbH
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Priority to EP12198817.4A priority Critical patent/EP2746409A1/fr
Priority to US14/653,694 priority patent/US10450622B2/en
Priority to JP2015548288A priority patent/JP6719903B2/ja
Priority to CN201380072929.9A priority patent/CN104995317B/zh
Priority to PCT/EP2013/003898 priority patent/WO2014095082A1/fr
Priority to KR1020157019365A priority patent/KR102169850B1/ko
Priority to EP13830148.6A priority patent/EP2935635B1/fr
Publication of EP2746409A1 publication Critical patent/EP2746409A1/fr
Ceased legal-status Critical Current

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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
    • C21D6/005—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
    • 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
    • C21D1/185—Hardening; Quenching with or without subsequent tempering from an intercritical temperature
    • 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
    • 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
    • C22C38/02—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
    • 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
    • C21D1/78—Combined heat-treatments not provided for above

Definitions

  • the present invention relates to a method of heat treating a manganese steel product, also referred to herein as a mid-manganese steel product. It is also a special alloy of a manganese steel product that can be heat treated by a special process.
  • steel products may include ferrite, pearlite, retained austenite, tempered martensite, martensite and bainite microstructures .
  • the properties of steel alloys depend, among other things, on the proportions of different phases, microstructures and their structural arrangement in microscopic observation.
  • Simple forms of advanced, high-strength steels of the 1st generation have, for example, a 2-phase composition of ferrites and martensites. Such steels are also referred to as biphasic steels. Ferrite (also called ⁇ -Fe or ⁇ -Fe depending on the constellation) forms a relatively soft matrix and martensite typically forms inclusions in this matrix.
  • Second generation steels such as TWIP steel, have mainly an austenitic microstructure and a high manganese content greater than 15% by weight.
  • TWIP stands for TWinning Induced Plasticity steel.
  • Each of these steels has different properties. Depending on the specific requirement profile, different steels are used, for example, in the automotive industry.
  • the carbon content (C) in such steels is typically in the range between 0.2 and 1.2 wt%. These are usually mild steels.
  • An austenite structure (also called gamma, ⁇ mixed crystal or ⁇ -Fe) is a mixed crystal that can form in a steel product.
  • the austenite structure has a bcc crystal structure, has a high heat resistance and offers good corrosion properties.
  • austenite formers which increase the austenite range, or volume fraction. These include nickel (Ni), chromium (Co) and manganese (Mn).
  • martensitic transformation Due to the formation of martensite and precipitates, undesirable cracking may occur during hot rolling of such steel products.
  • reconverted austenite also called “reverted austenite” or “Rev. austenite”
  • This form of austenite can be produced by a Miller and Grange 2-stage heat treatment. This process is also known as ART heat treatment.
  • ART stands for "Austenite Reverted Transformation”. There is a back transformation of martensite to back-converted austenite during ART heat treatment.
  • Ferrite is a metallurgical name for another mixed crystal, in whose lattice carbon is dissolved interstitially (ie in intermediate positions of the lattice).
  • a purely ferritic structure has a low strength, but a high ductility. By adding carbon, the strength can be improved, at the expense of ductility. That related to Fig. 1 described cast iron is an example of such a material.
  • ferrite formers which increase the ferrite range or volume fraction. These include chromium (Cr), molybdenum (Mo), vanadium (V), aluminum (Al), titanium (Ti), phosphorus (P) and silicon (Si).
  • Fig. 1 is a classic, highly schematic diagram of cast iron (a high carbon iron-carbon alloy> 2.06 wt%) shown.
  • two exemplary cooling curves are plotted as a function of the temperature T [° C] and the time t [min].
  • the perlite area is in Fig. 1 marked with 4 and the bainit range with 5.
  • M S denotes the martensite start temperature.
  • the corresponding line is in Fig. 1 denoted by the reference numeral 3.
  • the martensite start temperature M S is dependent on the alloy composition.
  • Perlite is a microstructure in which ⁇ -ferrite and cementite lamellae (cementite is iron carbide, Fe 3 C) are present.
  • Bainite also called bainitic iron
  • Bainite is not a phase in the true sense, but a microstructure that forms in steel in a certain temperature range. Bainite is mainly made from austenite.
  • martensite is formed at temperatures below line 3 in such a cast iron product.
  • a martensite is a fine-needle, very hard and brittle structure.
  • quenching of austenite occurs at such high cooling rates that there is no time for the carbon content in the steel to diffuse out of the lattice.
  • Curve 1 in Fig. 1 shows the quenching with a high cooling rate, which leads to the formation of martensitic structure.
  • Curve 2 in Fig. 1 shows a so-called bainite temperature treatment.
  • austenite When held at a temperature above M s , austenite can transform to bainite by avoiding conversion to the perlite step.
  • the steel products of the invention should have a tensile strength greater than 700 MPa.
  • the tensile strength should even be greater than 1200 MPa.
  • the steel products of the invention should simultaneously have better drawability and better bendability than the first generation steel products.
  • a steel product preferably a cold-rolled steel product, having an ultrafine multiphase structure with corresponding formability is provided by a combination of process and alloy concept.
  • Particularly preferred embodiments have an ultrafine multiphase bainitic structure which has a correspondingly good formability.
  • the alloy of the steel products of the invention has an average manganese content, which means that the manganese content is in the range of 3.5% by weight ⁇ Mn ⁇ 10% by weight, and preferably in the range of 3.5% by weight ⁇ Mn ⁇ 4 , 9% by weight.
  • the steel products of the invention form a heterogeneous system or a heterogeneous structure.
  • the steel products of the invention preferably have, according to the invention, a bainitic microstructure at least proportionally.
  • the proportion of the bainitic microstructure may be up to 20% by weight of the steel product.
  • the steel products of the invention preferably comprise at least a proportion of microstructures or areas of bainitic microstructure and martensite according to the invention.
  • the carbon content according to the invention is generally rather low. That is, the carbon content is in the range 0.1 wt.% ⁇ C ⁇ 0.14 wt.%.
  • the steels alloyed according to the invention are so-called mild, hypoeutectic steels.
  • Such alloys result in steel products having the desired properties if subjected to a two-stage thermal treatment with the process steps of claim 1.
  • This special form of two-stage temperature treatment has a significant influence on the formation of a multi-phase structure of the steel product.
  • the microstructure or the microstructure of the steel product is specifically influenced by a special two-stage temperature treatment.
  • the two-stage temperature treatment during cooling comprises an intermediate holding phase at a temperature which is in the range between 370 ° C and 400 ° C.
  • the intermediate holding phase has a maximum duration of 5 minutes. Holding at a temperature above M s , austenite can at least partially convert to bainite by avoiding conversion to the pearlite stage.
  • the alloy of the steel products comprises Al and Si components.
  • bainitizing i. the formation of bainitic microstructures. That the reduction of the Al and Si contents, as the invention provides, leads to a promotion of bainitic transformation. This is done by moving the Bainitsche area in the transformation diagram.
  • the Cr content is set to a maximum of 0.4% by weight.
  • the relationship between the carbon content and the manganese content By determining the relationship between the carbon content and the manganese content, stabilization of the austenite phase can be achieved according to the invention. Therefore, in preferred Embodiments of the relationship between the carbon content and the manganese content are set as follows: 0.01 ⁇ C (weight%) / Mn (weight%) ⁇ 0.04. The composition gives particularly excellent properties 0.02 ⁇ C (% by weight) / Mn (% by weight) ⁇ 0.04.
  • the relationship between the silicon content, the aluminum content and the chromium content is set as follows: 0.3 wt% ⁇ Si + Al + Cr ⁇ 1.2 wt%.
  • the invention can be applied to both hot and cold rolled steels and corresponding flat steel products.
  • the invention is used to provide cold rolled steel products in the form of cold rolled flat products (e.g., coils).
  • the tensile strength of the steel product is significantly greater than 700 MPa and can reach 1200 MPa and more.
  • the steel product which according to preferred embodiments of the invention comprises a structure with bainite, that it has significantly better bending properties and also a better HET value (HET stands for "hole expansion test”).
  • the invention relates to multi-phase medium-manganese steel products comprising martensite, ferrite and retained austenite regions or phases, and optionally also bainite microstructures. That the steel products of the invention are characterized by a special microstructure constellation which, depending on the embodiment, is also referred to as multiphase microstructure or, if bainite is present, as multiphase bainitic microstructure. In particular, this is about cold-rolled steel products.
  • steel (intermediate) products are sometimes referred to when it comes to emphasizing that it is not about the finished steel product but about a preliminary or intermediate product in a multi-stage production process.
  • the starting point for such production processes is usually a melt.
  • the alloy composition of the melt is given, since on this side of the manufacturing process, it is possible to influence the alloy composition relatively precisely (eg by attacking constituents, such as silicon).
  • the alloy composition of the steel product usually deviates only insignificantly from the alloy composition of the melt.
  • phase is defined here inter alia by its composition of proportions of the components, enthalpy content and volume. Different phases are separated in the steel product by phase boundaries.
  • the “components” or “constituents” of the phases may be either chemical elements (such as Mn, Ni, Al, Fe, C, etc.) or neutral, molecular aggregates (such as FeSi, Fe 3 C, SiO 2 , etc.). ) or charged, molecular aggregates (such as Fe 2+ , Fe 3+ , etc.).
  • compositions of the alloy or the steel product comprise, in addition to the explicitly listed materials or materials as the basic material iron (Fe) and so-called unavoidable impurities, which always occur in the molten bath and also show up in the resulting steel product. All% by weight must always be added to 100% by weight.
  • the mild to medium manganese steel products of the invention all have a manganese content of between 3.5 and 10 wt%, with the stated limits being within the range.
  • Such steel products have a medium manganese content.
  • Very particularly advantageous are medium-manganese steel products whose manganese content is between 3.5 and 4.9% by weight, whereby here too the stated limits belong to the range to this.
  • a bainite microstructure is a type of interstitial structure which typically forms at temperatures intermediate to those for perlite or martensite formation, as with reference to FIGS. 6A to 6D will be explained in more detail.
  • the conversion to a bainite microstructure usually competes with the transformation into a pearlite structure.
  • the bainite microstructure occurs according to the invention usually in a kind of conglomerate together with ferrite.
  • the invention relies on a combination of alloy composition (the melt) and process steps for heat treating the steel intermediate to achieve bainite microstructure levels in the overall structure of the steel product.
  • both the information in terms of alloy composition and the method steps of the invention are used together, as this gives the best results.
  • the consideration of the statements in terms of alloy composition also already gives remarkable results, for example with regard to the non-formability (for example in cold rolling).
  • the aluminum content Al is preferably in all embodiments of the invention in the range 0.0005 ⁇ Al ⁇ 1 wt.% And in particular in the range 0.0005 ⁇ Al ⁇ 0.0015.
  • the silicon content Si, aluminum content Al and chromium content Cr 0.3% by weight ⁇ Si + Al + Cr ⁇ 1.2% by weight.
  • all embodiments of the invention comprise a chromium content Cr which is less than 0.4% by weight.
  • all embodiments of the invention comprise a silicon content Si which is between 0.25 and 0.7% by weight.
  • the silicon content is in the range 0.3 ⁇ Si ⁇ 0.6.
  • the alloy of the steel products preferably comprises silicon components Si and aluminum components Al in all embodiments.
  • the bainitization can be enhanced. That is, the reduction of the silicon content Si and aluminum content Al, as the invention provides, leads to a promotion of the bainitic transformation. This happens because the bainitsche area 50 in the transformation diagram (see FIGS. 6A to 6D ) is moved.
  • Fig. 6A is a continuous ZTU diagram for a first alloy according to the invention shown (melt called MF232), which has been subjected to various treatment steps.
  • Table 2 shows the concrete alloy composition of melt MF232 and other exemplary melts of the invention.
  • a ZTU diagram is a material-dependent time-temperature conversion diagram. That is, a ZTU diagram shows the rate of conversion as a function of time for a continuously decreasing temperature. Overall, in this diagram and in the diagrams of the Figures 6B . 6C and 6D each shown eight curves. The alloys whose curves are shown in these ZTU diagrams all have the compositions shown in Table 2.
  • M f is the martensite finish temperature, which in English is called "martensite finish temperature”.
  • the martensite finish temperature M f is the temperature at which the conversion to martensite is completed thermodynamically. Also shown are the temperature thresholds Ac 3 and Ac 1 (see also Fig. 4A and 4B ). The range between Ac 3 and Ac 1 is referred to as ⁇ + ⁇ phase region .
  • the bainite region 50 is shifted in the diagram.
  • FIGS. 6A to 6D In each case a block arrow is shown approx. in the middle of the diagram following on the left. This block arrow is intended to schematically indicate that by reducing the silicon components Si and aluminum components Al (in comparison to the prior art), the bainite region 50 is displaced to the left. Typically, during rapid cooling (eg, with water), essentially only martensite is formed. By moving the bainite region 50 to the left, bainite microstructures are formed in the steel product even with relatively rapid cooling.
  • the two-stage annealing process is preferably carried out for all alloy compositions in such a way that, above all during the first annealing process (step S4.1 in FIG Fig. 4A or 4B and Fig. 3 ) the cooling curve A1 of the steel (between) products is such that the region of bainite formation 50 is traversed.
  • all embodiments of the alloy composition additionally comprise a nitrogen content N ranging between 0.004 wt.% And 0.006 wt.%, which corresponds to 40 ppm to 60 ppm.
  • an intermediate annealing step (eg with T ⁇ 650 ° C and 10 to 24 hours duration) can be inserted (not in FIG Fig. 3 shown).
  • the pre-annealing step may be carried out in a nitrogen atmosphere.
  • Fig. 4A 1 is a schematic representation of an exemplary temperature-time diagram for a first 2-stage temperature treatment of a steel (inter) product of the invention.
  • a previously known 2-stage method according to Arlazarov et al. shown in order to better show significant differences.
  • the heating E1 during the first annealing process and / or the heating E2 during the second annealing process is preferably carried out at a heating rate which is between 4 Kelvin / second and 50 Kelvin / second. Above all, good results are achieved in the range between 5 Kelvin / second and 15 Kelvin / second.
  • the temperature of the steel (between) product is maintained substantially constant.
  • holding H2 in all embodiments lasts between 3 and 5 hours, and preferably between 3.5 and 4.5 hours. That The following statement applies: 3 h ⁇ ⁇ 2 ⁇ 5 h, or 3.5 h ⁇ ⁇ 2 ⁇ 4.5 h.
  • a retention time of ⁇ 2 ⁇ 4h at a second holding temperature of T2 ⁇ 650 ° C has proven particularly useful.
  • the cooling of the steel (intermediate) product in all embodiments is carried out in the first annealing process and / or in the second annealing process at a cooling rate which is between 25 Kelvin / second and 200 Kelvin / second.
  • the cooling rate in all embodiments is between 40 Kelvin / second and 150 Kelvin / second.
  • the curves A1 * in Fig. 4A and in Fig. 4B each show a cooling process that begins with a high cooling rate of about 150 Kelvin / second and then decreases its cooling rate in the direction of 40 Kelvin / second. Therefore, the curves A1 * have no straight line but a curved waveform.
  • the curves A1 in Fig. 4A and 4B each show a linear cooling process, which runs with a high cooling rate of about 150 Kelvin / second.
  • Cooling may be linear (e.g., 150 Kelvin / second) or along a curved curve (e.g., along curve A1 *) in the first annealing process and / or second annealing process.
  • the cooling can be carried out in the second annealing process as in Fig. 4B shown.
  • the cooling consists here of three steps.
  • a rapid (eg linear) cooling takes place from T2 to a holding temperature T3, which lies in the range between 370 ° C and 400 ° C.
  • this holding temperature T3 is about 380 ° C.
  • the holding temperature T3 is preferably selected in all embodiments so that it is above the temperature M S.
  • the desired bainite microstructures are also formed (depending on the alloy composition and process procedure) if the alloy according to the invention is predetermined and the first annealing process according to the invention is carried out.
  • Fig. 4A is shown by the curve e1, h1, a1 and e2, h2, a2, the temperature during the first hold h1 is significantly lower than during the inventive first hold H1.
  • the first hold period ⁇ 1 is significantly longer.
  • martensite phases but no bainite microstructures are formed.
  • the temperature is slightly higher during the second holding h2 than during the second holding H2 according to the invention.
  • the second holding period ⁇ 2 is significantly longer.
  • T 670 ° C and 1h ⁇ 2 ⁇ 30 h.
  • EBSD Electrode BackScattered Diffraction
  • Fig. 5 Fig. 12 shows a schematic diagram of the distribution function Fx (x) of the grain diameter of the bcc- ⁇ phase of a specific steel product of the invention.
  • bcc stands for "body centered cubic".
  • the special steel product whose distribution function Fx (x) of the grain diameter in Fig. 5 is shown, has the following inventive alloy composition (in Table 1, the setpoints of the melt are given): Table 1: [Wt.%] Fe C Si Mn al Sample 231 rest 0.140 0,550 4,000 0.0005
  • the Fig. 5 Based on the distribution function Fx (x) the Fig. 5 It can be seen that the majority of the grains of the alloy structure has a grain size between 0 and about 3 microns. Since the EBSD investigations used have a lower resolution limit at about 0.1 ⁇ m, the average distribution of the particle size of the bcc- ⁇ phase can be limited to the range from about 0.1 ⁇ m to about 3 ⁇ m. Further EBSD investigations have shown that the distribution of the grain size of the fcc- ⁇ phase can be limited to the range from about 0.25 ⁇ m to about 0.75 ⁇ m.
  • Fig. 2 shows a common scale that allows classification of steel products on the diameter of the grain size.
  • the steel product (sample 231) of the invention is thus in the range of ultrafine grains (if the average distribution). This classification can also be applied to the other alloy compositions of the invention. Therefore, there is also talk here of an ultrafine multiphase structure and of an ultrafine multiphase bainitic structure, if detectable bainite microstructures are present.
  • the grains of the ferrite phases and the bainite microstructure are very fine. Particular preference is therefore given to alloys or steel products which have a combination of ferrite phases and bainite microstructures.
  • Table 2 shows the actual alloy composition in wt% of various samples of the invention.
  • Table 2 sample 230 231 232 233 Melt setpoint steel product Melt setpoint steel product Melt setpoint steel product Melt setpoint steel product Fe / Rest X X X X X X X C 0140 0142 0140 0140 0100 0098 0100 0105 Si 0550 0520 0550 0540 0350 0320 0350 0340 Mn 4000 4120 4000 4070 4900 4940 4900 4970 P 0 0.0050 0 0.0051 0 0.0054 0 0.0057 S 0 0.0083 0 0.0084 0 0.0070 0 0.0075 al 0.0005 0.0100 0.0005 0.0090 0.0005 0.0090 0.0005 0009 Cr 0 0016 0 0016 0 0016 0 0015 Ni 0 0011 0 0012 0 0012 0 0011 Not a word 0 0004 0 0005 0
  • Table 3 shows various characteristic sizes of steel products in the form of cold tapes with the actual alloy composition of Samples 231 and 233 of the invention after undergoing a two-stage annealing process Fig. 4A ).
  • R m is the tensile strength in MPa
  • a total is the elongation at break in% (the elongation at break is proportional to the ductility)
  • R mx A total is the product of tensile strength and elongation at break in MPa%.
  • Table 3 shows the best results in terms of tensile strength with respect to the product of R mx A total .
  • Comparative tests with conventional single-stage annealing processes and conventional two-stage annealing processes show that the alloy composition and method of the invention are very good Values - particularly as the product of R x A total terms - can be achieved.
  • Table 3 [Wt.%] R m [MPa] A total [%] Rmx Atotal [MPa%] structure Total grain size [ ⁇ m] Sample 231 773 32 25030 approx.

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EP12198817.4A 2012-12-21 2012-12-21 Procédé de traitement à chaud d'un produit en manganèse-acier et produit en manganèse-acier doté d'un alliage spécial Ceased EP2746409A1 (fr)

Priority Applications (7)

Application Number Priority Date Filing Date Title
EP12198817.4A EP2746409A1 (fr) 2012-12-21 2012-12-21 Procédé de traitement à chaud d'un produit en manganèse-acier et produit en manganèse-acier doté d'un alliage spécial
US14/653,694 US10450622B2 (en) 2012-12-21 2013-12-20 Method for heat-treating a manganese steel product and manganese steel product
JP2015548288A JP6719903B2 (ja) 2012-12-21 2013-12-20 マンガン鋼材の熱処理方法およびマンガン鋼材
CN201380072929.9A CN104995317B (zh) 2012-12-21 2013-12-20 对锰钢产品进行热处理的方法和锰钢产品
PCT/EP2013/003898 WO2014095082A1 (fr) 2012-12-21 2013-12-20 Procédé de traitement thermique d'un produit en acier au manganèse et produit en acier au manganèse
KR1020157019365A KR102169850B1 (ko) 2012-12-21 2013-12-20 망간강 제품의 열처리 방법 및 망간강 제품
EP13830148.6A EP2935635B1 (fr) 2012-12-21 2013-12-20 Procédé de traitement thermique d'un produit en acier au manganèse et produit en acier au manganèse

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EP12198817.4A EP2746409A1 (fr) 2012-12-21 2012-12-21 Procédé de traitement à chaud d'un produit en manganèse-acier et produit en manganèse-acier doté d'un alliage spécial

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EP13830148.6A Active EP2935635B1 (fr) 2012-12-21 2013-12-20 Procédé de traitement thermique d'un produit en acier au manganèse et produit en acier au manganèse

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US (1) US10450622B2 (fr)
EP (2) EP2746409A1 (fr)
JP (1) JP6719903B2 (fr)
KR (1) KR102169850B1 (fr)
CN (1) CN104995317B (fr)
WO (1) WO2014095082A1 (fr)

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EP3029162A1 (fr) * 2014-12-01 2016-06-08 Voestalpine Stahl GmbH Procédé de traitement à chaud d'un produit en manganèse-acier et produit en manganèse-acier
WO2016087392A1 (fr) * 2014-12-01 2016-06-09 Voestalpine Stahl Gmbh Procédé de traitement thermique d'un produit en acier au manganèse et produit en acier au manganèse comprenant un alliage spécial
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CN104995317A (zh) 2015-10-21
US10450622B2 (en) 2019-10-22
US20160002746A1 (en) 2016-01-07
EP2935635A1 (fr) 2015-10-28
WO2014095082A1 (fr) 2014-06-26
EP2935635B1 (fr) 2022-09-28
KR102169850B1 (ko) 2020-10-27

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