EP3433386B1 - Procédé de traitement thermique d'un produit intermédiaire en acier au manganèse. - Google Patents

Procédé de traitement thermique d'un produit intermédiaire en acier au manganèse. Download PDF

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EP3433386B1
EP3433386B1 EP17709124.6A EP17709124A EP3433386B1 EP 3433386 B1 EP3433386 B1 EP 3433386B1 EP 17709124 A EP17709124 A EP 17709124A EP 3433386 B1 EP3433386 B1 EP 3433386B1
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Prior art keywords
temperature
treatment process
annealing
intermediate product
manganese
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EP3433386A1 (fr
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Friedrich FÜREDER-KITZMÜLLER
Reinhold Schneider
Daniel Krizan
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Voestalpine Stahl GmbH
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Voestalpine Stahl GmbH
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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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D6/005—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
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips 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
    • 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
    • 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

Definitions

  • the present invention relates to a method of heat treating a manganese steel intermediate. It is also about a specific alloy of a manganese steel intermediate, which is heat-treated in a special process in order to achieve a significantly reduced fatigue expansion.
  • composition or alloy as well as the heat treatment in the manufacturing process have a significant influence on the properties of steel products.
  • Mn manganese
  • medium-manganese steels which are also referred to as medium-manganese steels.
  • the manganese content in percent by weight (% by weight) is often in the range between 3 and 12.
  • a medium manganese steel has a high combination of tensile strength and elongation due to its structure. Typical applications in the automotive industry are complex safety-relevant deep-drawn components.
  • Fig. 1 A classic, highly schematic diagram is shown, in which the elongation at break A 80 (called total elongation) is plotted in percent above the tensile strength (called tensile strength) in MPa.
  • the tensile strength is abbreviated here with R m .
  • the diagram of the Fig. 1 provides an overview of the strength classes of steel materials currently used for the automotive industry. In general, the following statement applies: the higher the tensile strength R m of a steel alloy, the lower the elongation at break A 80 of this alloy. Put simply, it can be stated that the elongation at break A 80 decreases with increasing tensile strength R m and vice versa. An optimal compromise between the elongation at break A 80 and the tensile strength R m must therefore be found for each application.
  • Steel alloys with a high tensile strength R m of mostly more than 1000 MPa are used for steel barriers (e.g. for side impact protection), which are intended to prevent the penetration of vehicle parts in the event of an accident.
  • the new generation of high-strength AHSS (Advanced High-Strength Steels) steels is suitable here (reference number 2 in Fig. 1 ).
  • This category includes the TBF (Trip Bainitic Ferrite) steels and the Q&P (Quenching & Partitioning) steels.
  • These high-strength AHSS steels have, for example, a manganese content in the range between 1.2 and 3% by weight and a carbon content C which is between 0.05 and 0.25% by weight.
  • the range designated by the reference number 3 comprises medium-manganese steels with an Mn content between 3 and 12% by weight and with a carbon content ⁇ 1% by weight.
  • FIG. 2 An example tension curve 4 (also called stress-strain curve) is the Fig. 2 refer to.
  • the stress ⁇ in MPa
  • the tension curve 4 shows an intermediate maximum 5, which is referred to as the upper yield point (R eH ), followed by a plateau 6.
  • the plateau 6 merges into an increasing curve area.
  • the "length" of the plateau 6 is referred to as the elongation (A L ), as in Fig. 2 shown.
  • a steel product with such a pronounced yield strength can form undesirable strains on the surface of the components for the automotive industry. For this reason, the pronounced yield strength must typically be reduced by a re-rolling process.
  • the aftertreatment in a corresponding re-rolling mill (usually with a skin pass mill) is also referred to as skin pass.
  • the manganese steel intermediate products should preferably have no (measurable) fatigue strain.
  • a particularly suitable manganese steel alloy and an optimized method for the temperature treatment of a manganese steel intermediate product are provided.
  • the manganese-steel intermediate products which were produced from a melt of this manganese-steel alloy are subjected to a first temperature treatment process and a subsequent second temperature treatment process as part of a temperature treatment according to the invention.
  • the first temperature treatment process is a high temperature process in which the steel intermediate product is exposed to a first annealing temperature for a first holding period which is above a critical temperature limit (referred to as T KG ), which defines the critical temperature limit (T KG ) as follows is: T KG ⁇ (856 - SK ⁇ manganese content) degrees Celsius, and where S K is a slope value.
  • T KG critical temperature limit
  • the formula mentioned which serves as the definition of the critical temperature limit (T KG ), states that the critical temperature limit (T KG ) decreases with increasing manganese content in the manganese range mentioned.
  • the second temperature treatment process is an annealing process in which the steel intermediate product is exposed to a second annealing temperature T2, which is in any case lower than the first annealing temperature T1.
  • the first annealing temperature T1 preferably shows a dependency on the stated manganese range of the alloy, which is defined as follows: T1 T T KG .
  • the first holding period is preferably at least 10 seconds.
  • the first holding time is particularly preferably between 10 seconds and 7000 minutes in all embodiments.
  • the second annealing temperature T2 is preferably in the range between the temperatures A 1 and A 3 .
  • the second temperature treatment process including heating the steel intermediate, maintaining the second annealing temperature, and cooling the steel intermediate, takes less than 6000 minutes. This total time is preferably even less than 5000 minutes.
  • the invention makes it possible for the first time to provide intermediate steel products which have an elongation A L which is less than 3% and preferably less than 1%.
  • the process according to the invention can be used to produce intermediate steel products which have an average primary austenite grain size which is larger than 3 ⁇ m.
  • the alloy of the steel intermediate products of the invention preferably has an average manganese content, which means that the manganese content is in the range 3% by weight M Mn 12 12% by weight. In all embodiments, the manganese content is preferably in the range from 3.5% by weight M Mn 8 8.5% by weight.
  • the first temperature treatment process is carried out in a continuous belt system (annealing system).
  • annealing system This process is also known as continuous annealing.
  • hood annealing discontinuous heat treatment of the intermediate steel product.
  • the first temperature treatment of the invention can also be carried out by special temperature control during hot rolling. With this special temperature control, care is taken to ensure that the end temperature of the hot strip during hot rolling is in the range above the critical temperature limit T KG .
  • the second temperature treatment process is carried out in a discontinuously operating plant, the steel intermediate being exposed to the annealing process in this plant in a protective gas atmosphere.
  • This process is preferably carried out in a bell annealer.
  • the second temperature treatment process can also be carried out in a continuous strip system (annealing system) or in a hot-dip galvanizing system.
  • the steel intermediate of all embodiments can optionally be subjected to a skin pass process, this skin pass process primarily aimed at conditioning the surface of the steel intermediate product.
  • a more intensive skin pass is not necessary since the steel intermediate products of the invention have a low fatigue elongation.
  • the degree of skin passage can thus be reduced or avoided entirely.
  • steel intermediates can be produced which have an elongation at break which is less than 3% and which is preferably less than 1%.
  • intermediate steel products can be produced which have a tensile strength R m (also called minimum strength) which is greater than 490 MPa.
  • steel intermediate products can be produced which, owing to the reduced elastic expansion, have a (minimum) elongation at break (A 80 ) which is greater than 10%.
  • the invention can be used to e.g. To provide cold-rolled steel products in the form of cold-rolled flat materials (e.g. coils).
  • the invention can also be used to e.g. To manufacture thin sheets or wire and wire products.
  • the invention can also be used to provide hot-rolled steel products.
  • Quantities or proportions are mostly given in percent by weight (short% by weight), unless otherwise stated. If information is given on the composition of the alloy or steel product, then the composition includes iron (Fe) and so-called unavoidable in addition to the explicitly listed materials Contamination that always occurs in the weld pool and that is also evident in the resulting steel intermediate. All percentages by weight must therefore always be supplemented to 100 percent by weight and all percentages by volume must always be supplemented to 100 percent of the total volume.
  • the heat treatment of the intermediate steel product comprises a first temperature treatment process S.1 and a subsequent second temperature treatment process S.2. These two temperature treatment processes S.1 and S.2 are in Fig. 3 shown in two side-by-side temperature-time diagrams.
  • the first temperature treatment process S.1 is a high-temperature process in which the steel intermediate product is exposed to a first annealing temperature T1 for a first holding period ⁇ 1 (this step is also referred to as holding H1).
  • the annealing temperature T1 is above a critical temperature limit T KG during the holding H1.
  • the alloy composition of the respective type can be found in Table 1, only the essential alloy components being mentioned here. There are a number of exemplary embodiments that have been tested for each type. The corresponding examples are numbered 1 to 26 in the left column in Table 2.
  • Fig. 4 the following four samples are shown by the circle symbols mentioned: type 4, 18; Type1, 1; Type 3, 14 and Type 7, 24 (the designation Type 4, 18 stands for example for the alloy composition of Type 4, Example No. 18).
  • the absolute value 866 in degrees Celsius defines the point of intersection with the vertical axis and the value S K defines the slope. S K is therefore also referred to as the slope value.
  • the straight line 8 is parallel to the straight line 7.
  • the first annealing temperature T1 In the case of steel alloys of the manganese steel intermediate, as already defined, the first annealing temperature T1 must always be above the lower critical temperature limit T KG in order to ensure that a manganese steel intermediate is obtained in which the fatigue expansion occurs A L is less than 3%.
  • the second temperature treatment process S.2 also has an influence on the elongation.
  • the second annealing temperature T2 In order to maintain the grain size of the austenite grains in the structure, the second annealing temperature T2 must in any case be lower than the first annealing temperature T1. Since the first annealing temperature T1 is always above the lower critical temperature limit T KG , it can be concluded that the second annealing temperature T2 should preferably be below the lower critical temperature limit T KG .
  • the first annealing temperature T1 is above the temperature limit T KG and that the second annealing temperature T2 is in the range between A 1 and A 3 .
  • the second temperature treatment S.2 is also referred to as intercritical annealing.
  • the first holding period ⁇ 1 is preferably at least 10 seconds and preferably between 10 seconds and 6000 minutes.
  • the second holding period ⁇ 2 is at least 10 seconds in all embodiments. In Fig. 3 the two holding times ⁇ 1 and ⁇ 2 are only shown as examples. The time interval between the first temperature treatment process S.1 and the second temperature treatment process S.2 can be selected as required. The second temperature treatment process S.2 is typically carried out shortly after the first temperature treatment process S.1.
  • Embodiments are preferred in which the first temperature treatment process S.1, including heating E1 of the intermediate steel product, holding H1 of the first annealing temperature T1 and cooling Ab1 of the intermediate steel product, takes less than 7000 minutes.
  • Embodiments are preferred in which the second temperature treatment process S.2, including heating E2 of the steel intermediate, maintaining H2 of the second annealing temperature T2 and cooling Ab2 of the steel intermediate, takes less than 6000 minutes and preferably less than 5000 minutes.
  • the significant reduction in the elongation A L is independent of whether the first temperature treatment process S.1 and / or the second temperature treatment process S.2 in a continuous belt system (for example in a continuous system) or in a discontinuously operating system (for example in a bell annealer).
  • the invention can be applied both to cold strip intermediate products and to hot strip intermediate products. In both cases there is a significant reduction in the elongation A L.
  • Fig. 5 shows both the reduction in the elongation A L in percent and the dependence of the mean original austenite grain size (D UAK M ) in ⁇ m with increasing annealing temperature T1 for two exemplary samples of type 1 and type 2 (see also Table 1) as follows.
  • Fig. 5 derive from the fact that the critical temperature limit T KG1 ⁇ 820 ° C is for the examined alloy composition of type 1 (represented by curve 9), if one wants to achieve an elongation at break for this type composition 1 which is less than 3%.
  • Curve 10 shows the associated course of the mean original austenite grain boundary D UAK M 1 , as a function of temperature T1. For the Type 1 example, this results in a grain size of> 3 ⁇ m.
  • Fig. 5 derive from the fact that the critical temperature limit T KG2 is ⁇ 970 ° C for the examined alloy composition of type 2 (represented by curve 11), if one wants to achieve a fatigue strain which is less than 3% for this type 2 alloy composition.
  • Curve 12 shows the associated course of the mean original austenite grain boundary D UAK M , depending on the temperature T1. For the Type 2 example, this results in a grain size of> 8 ⁇ m.
  • the microalloying element niobium (Nb) has a noticeable influence, which is shown as a shift from T KG2 (compared to T KG1 ) to a higher critical temperature for A L ⁇ 3%.
  • Curves 10 and 12 in Fig. 5 show that the original austenite grain size increases with increasing temperature T1.
  • Fig. 5 the corresponding lower critical temperature limit T KG1 is shown as a dashed vertical line. It can be seen that the alloy compositions of type 1 have an average grain size which is> 3 ⁇ m from an annealing temperature T1> T KG1 .
  • the lower critical temperature limit T KG1 is in Fig. 4 identified by a small black triangle.
  • the microalloy leads to an increase in the critical temperature limit T KG .
  • the critical temperature limit T KG2 around is approx. 150 ° C higher than with Type 1 alloy compositions.
  • the corresponding effective lower critical temperature limit T * KG2 is shown as a dashed vertical line.
  • Fig. 6 shows a schematic diagram showing the stress ⁇ in MPa as a function of the elongation ⁇ in%.
  • the representation of the Fig. 6 is with the representation of the Fig. 2 to compare, being Fig. 6 shows only a small section.
  • Type 3 alloys in Table 1 four identical samples were compared here. Type 3 alloys also meet the requirements of the invention. All four samples were each subjected to a first temperature treatment process S.1 and a subsequent second temperature treatment process S.2. All process parameters were identical, except that in the first temperature treatment process S.1, the first annealing temperature T1 was varied as follows (see column 2 of the following Table 3): Table 3 alloy T1 [° C] T2 [° C] Curve Type 3 810 640 13.1 Type 3 850 640 13.2 Type 3 900 640 13.3 Type 3 950 640 13.4
  • the solid curve 13.1 Fig. 6 (Type 3, 14 of Table 2) shows a clearly visible pronounced yield point and has an elongation of A L ⁇ 2.6%.
  • Curve 13.2 represents another exemplary sample (type 3, 15 of table 2) of type 3, the yield strength here still being slightly pronounced.
  • Curve 13.4 represents another exemplary sample of type 3, with no pronounced yield point being visible here either. This is type 3, 17 of table 2.
  • the corresponding measurement values are in the range from approx. 700 to 1000 MPa and with an elongation at break A 80 in the range from approx. 20 to 40%.

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Claims (14)

  1. Procédé de traitement thermique d'un produit intermédiaire en acier au manganèse dont l'alliage comprend :
    ∘ une proportion de manganèse (Mn) dans la plage de manganèse (MnB) suivante 3 % en poids ≤ Mn ≤ 12 % en poids,
    ∘ une proportion d'un ou de plusieurs éléments d'alliage du groupe :
    silicium (Si), aluminium (Al), nickel (Ni), chrome (Cr), molybdène (Mo), phosphore (P), soufre (S), azote (N), cuivre (Cu), bore (B), tungstène (W), cobalt (Co),
    ∘ une proportion en carbone (C) optionnelle de moins de 1 % en poids,
    ∘ une proportion optionnelle d'un ou de plusieurs éléments de micro-alliage, la proportion totale des éléments de micro-alliage étant inférieure à 0,45 % en poids, et
    ∘ le reste présentant une proportion en fer (Fe) et des impuretés inévitables,
    le traitement thermique du produit intermédiaire en acier comprenant un premier processus de traitement thermique (S.1) et un deuxième processus de traitement thermique ultérieur (S.2), caractérisé en ce que
    - le premier processus de traitement thermique (S.1) est un procédé à haute température dans lequel le produit intermédiaire en acier est exposé pendant une première période de maintien (Δ1) à une première température de recuit (T1) qui est supérieure à une limite de température critique (TKG) qui est définie comme suit : TKG = (856 - SK * proportion de manganèse) degré Celsius, SK étant une valeur de pente, et cette valeur de pente étant égale à SK = 7,83 ± 10 %, de préférence SK = 7,83,
    - le deuxième processus de traitement thermique (S.2) est un procédé de recuit dans lequel le produit intermédiaire en acier est exposé à une deuxième température de recuit (T2) inférieure à la première température de recuit (T1).
  2. Procédé selon la revendication 1, caractérisé en ce que la première température de recuit (T1) dans la plage de manganèse mentionnée (MnB) présente une dépendance qui est définie comme suit : T1 ≈ (866-Sk * proportion de manganèse) degré Celsius.
  3. Procédé selon la revendication 1 ou 2, caractérisé en ce que la première période de maintien (Δ1) est d'au moins 10 secondes et est comprise de préférence entre 10 secondes et 6000 minutes.
  4. Procédé selon l'une des revendications 1 à 4, caractérisé en ce que la deuxième température de recuit (T2) se situe dans la plage entre les températures A1 et A3, A1 étant la température de départ de l'austénitisation et A3 étant la température de départ de l'austénitisation complète.
  5. Procédé selon la revendication 1, caractérisé en ce que la deuxième température de recuit (T2) est située dans la plage allant de 630 °C à 675 °C.
  6. Procédé selon l'une des revendications 1 à 5, caractérisé en ce que, dans le cadre du deuxième processus de traitement thermique (S.2), la deuxième température de recuit (T2) est maintenue pendant une deuxième période de maintien (Δ2) d'au moins 10 secondes.
  7. Procédé selon l'une des revendications 1 à 5, caractérisé en ce que le deuxième processus de traitement thermique (S.2), avec un processus de réchauffement (E2) du produit intermédiaire en acier, le maintien (H2) de la deuxième température de recuit (T2) et un processus de refroidissement (A2) du produit intermédiaire en acier, dure moins de 6000 minutes et de préférence moins de 5000 minutes.
  8. Procédé selon l'une des revendications 1 à 7, caractérisé en ce que la proportion du ou des plusieurs éléments d'alliage est située dans la plage suivante :
    - silicium (Si) ≤ 3 % en poids, et de préférence ≤ 2 % en poids,
    - aluminium (Al) ≤ 8 % en poids, et de préférence ≤ 6 % en poids,
    - nickel (Ni) ≤ 2 % en poids, et de préférence ≤ 1 % en poids,
    - chrome (Cr) ≤ 2 % en poids, et de préférence ≤ 0,5 % en poids,
    - molybdène (Mo) ≤ 0,5 % en poids, et de préférence ≤ 0,25 % en poids,
    - phosphore (P) ≤ 0,05 % en poids, et de préférence ≤ 0,025 % en poids,
    - soufre (S) ≤ 0,03 % en poids, et de préférence ≤ 0,01 % en poids,
    - azote (N) ≤ 0,05 % en poids, et de préférence ≤ 0,025 % en poids,
    - cuivre (Cu) ≤ 1 % en poids, et de préférence ≤ 0,5 % en poids,
    - bore (B) ≤ 0,005 % en poids, et de préférence ≤ 0,0035 % en poids,
    - tungstène (W) ≤ 1 % en poids, et de préférence ≤ 0,5 % en poids,
    - cobalt (Co) ≤ 2 % en poids, et de préférence ≤ 1 % en poids.
  9. Procédé selon l'une des revendications 1 à 7, caractérisé en ce que les éléments de micro-alliage sont des éléments du groupe : titane (Ti), niobium (Nb), vanadium (V).
  10. Procédé selon l'une des revendications 1 à 9, caractérisé en ce que le premier processus de traitement thermique (S.1) est un procédé qui est réalisé dans une installation à bande continue ou dans une installation fonctionnant en discontinu.
  11. Procédé selon l'une des revendications 1 à 10, caractérisé en ce que le deuxième processus de traitement thermique (S.2) est un procédé qui est réalisé dans une installation à bande continue ou dans une installation fonctionnant en discontinu, le produit intermédiaire en acier dans cette installation étant exposé au procédé de recuit dans une atmosphère inerte.
  12. Procédé selon la revendication 11, caractérisé en ce qu'on utilise une installation de recuit à cloche comme installation à fonctionnement discontinu.
  13. Procédé selon l'une des revendications 1 à 12, caractérisé en ce que le produit intermédiaire en acier, dans une étape en aval du deuxième processus de traitement thermique (S.2), est soumis à un procédé de dressage, ce procédé de dressage visant principalement à conditionner la surface du produit intermédiaire en acier.
  14. Procédé selon l'une des revendications 1 à 12, caractérisé en ce que le premier processus de traitement thermique (S.1) est réalisé pendant un procédé de laminage à chaud, ce procédé de laminage à chaud étant effectué avec une température de fin de laminage située dans la plage au-dessus de la limite de température critique (TKG).
EP17709124.6A 2016-03-23 2017-03-10 Procédé de traitement thermique d'un produit intermédiaire en acier au manganèse. Active EP3433386B1 (fr)

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Application Number Priority Date Filing Date Title
EP16162073.7A EP3222734A1 (fr) 2016-03-23 2016-03-23 Procede de traitement thermique d'un produit intermediaire en acier/manganese et produit intermediaire en acier traite thermiquement
PCT/EP2017/055714 WO2017162450A1 (fr) 2016-03-23 2017-03-10 Procédé de traitement thermique d'un produit intermédiaire en acier au manganèse et produit intermédiaire en acier-manganèse ayant subi un traitement thermique correspondant

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EP3433386A1 EP3433386A1 (fr) 2019-01-30
EP3433386B1 true EP3433386B1 (fr) 2020-06-17

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EP17709124.6A Active EP3433386B1 (fr) 2016-03-23 2017-03-10 Procédé de traitement thermique d'un produit intermédiaire en acier au manganèse.

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CN108034890A (zh) * 2017-12-13 2018-05-15 天津市宝月钢制品有限公司 低合金中锰耐磨钢热轧板及制备方法
EP3594368A1 (fr) * 2018-07-13 2020-01-15 voestalpine Stahl GmbH Produit intermédiaire d'acier milieu-manganèse-feuillard laminé à froid à teneur en carbone réduite et procédé de fourniture d'un tel produit intermédiaire d'acier

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JP2876968B2 (ja) * 1993-12-27 1999-03-31 日本鋼管株式会社 高延性を有する高強度鋼板およびその製造方法
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US10253389B2 (en) * 2014-03-31 2019-04-09 Jfe Steel Corporation High-yield-ratio, high-strength cold-rolled steel sheet and production method therefor
KR101677396B1 (ko) * 2015-11-02 2016-11-18 주식회사 포스코 성형성 및 구멍확장성이 우수한 초고강도 강판 및 이의 제조방법

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KR102246704B1 (ko) 2021-04-30
KR20180127435A (ko) 2018-11-28
EP3433386A1 (fr) 2019-01-30
JP6945545B2 (ja) 2021-10-06
EP3222734A1 (fr) 2017-09-27
CN108884507B (zh) 2020-06-16
ES2816065T3 (es) 2021-03-31
JP2019516857A (ja) 2019-06-20
WO2017162450A1 (fr) 2017-09-28
CN108884507A (zh) 2018-11-23
US20190071748A1 (en) 2019-03-07

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