EP3325678B1 - Acier léger deformable de construction présentant des propriétés mécaniques améliorées et procédé de fabrication de produit semi-fini à partir de cet acier - Google Patents

Acier léger deformable de construction présentant des propriétés mécaniques améliorées et procédé de fabrication de produit semi-fini à partir de cet acier Download PDF

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Publication number
EP3325678B1
EP3325678B1 EP16750113.9A EP16750113A EP3325678B1 EP 3325678 B1 EP3325678 B1 EP 3325678B1 EP 16750113 A EP16750113 A EP 16750113A EP 3325678 B1 EP3325678 B1 EP 3325678B1
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Prior art keywords
steel
max
strip
annealing
cold
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German (de)
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EP3325678A1 (fr
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Peter PALZER
Zacharias Georgeou
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Salzgitter Flachstahl GmbH
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Salzgitter Flachstahl GmbH
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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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties 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
    • C21D8/0221—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
    • 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
    • C21D8/0236—Cold 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
    • 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
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C22C38/06—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • 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
    • C21D8/0231—Warm 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
    • 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
    • C21D8/0273—Final recrystallisation annealing

Definitions

  • the invention relates to a formable lightweight structural steel with improved mechanical properties and a high resistance to delayed hydrogen-induced crack formation, according to claim 1. Furthermore, the invention relates to a method for producing semi-finished products from this steel.
  • semi-finished products are understood to mean hot or cold strip produced from this steel or an intermediate or end product produced therefrom, such as pipes, for example.
  • Known formable lightweight steel has, for example, the following alloy composition (in% by weight): C 0.04 to ⁇ 1.0, Al 0.05 to ⁇ 4.0, Si 0.05 to ⁇ 6.0, Mn 9, 0 to ⁇ 18.0, the remainder being iron including the usual accompanying steel elements
  • Cr, Cu, Ti, Zr, V and Nb can be added depending on the requirements.
  • This lightweight steel has a partially stabilized ⁇ mixed crystal structure with a defined stacking fault energy with a z. T. multiple TRIP effect, which enables the stress or strain-induced transformation of a face-centered ⁇ mixed crystal (austenite) into an ⁇ -martensite (hexagonal closest packing of spheres) and then with further deformation into a body-centered ⁇ -martensite and residual austenite.
  • TRIP Transformation Induced Plasticity
  • TWIP winning Induced Plasticity
  • an austenitic steel which is said to have excellent resistance to delayed crack formation.
  • the steel contains: 0.5 to 0.8 C, 10 to 17 Mn, at least 1.0 Al, at most 0.5 Si, at most 0.020 S, at most 0.050 P, 50 to 200 ppm N and 0.050 to 0.25 V.
  • a steel alloy for a high-strength cold-rolled steel sheet is known, which is also said to have an improved resistance to delayed cracking.
  • the steel contains: 0.05 to 0.3 C, 0.3 to 1.6 Si, 4.0 to 7.0 Mn, 0.5 to 2.0 Al, 0 .01 to 0.1 Cr, 0.02 to 0.1 Ni, 0.005 to 0.03 Ti, 5 to 30 ppm B, 0.01 to 0.03 Sb, and 0.008 or less S.
  • EP 2 128 293 A1 a lightweight steel with an improved elongation known, having in addition to iron and impurities in% by weight: 0.2 to 0.8 C, 2 to 10 Mn, 0.2 or less P, at most 0.015 S, 3.0 to 15 Al, at most 0.01 N and an Mn / Al ratio of 0.4 to 1.0.
  • EP 2 778 247 A1 discloses a steel sheet for hot forming with improved collision suitability, which in addition to iron and unavoidable impurities in wt .-% 0.01 to 0.5 C, 3 or less Si, 3 to 15 Mn, 0.0001 to 0.1 P, 0, 0001 to 0.03 S, 3 or less Al, and 0.03 or less N.
  • Cr, Mo, W, Ti, Nb, Zr, V, Cu, Ni, Sb, Sn or B can be added to the alloy.
  • the object of the invention is to provide a lightweight structural steel of the generic type which, while retaining very good mechanical properties (ductility, strength), does not have the effect of delayed crack formation or hydrogen embrittlement.
  • the product of tensile strength and elongation at break is advantageously used as a basis, which is a measure of the performance of the material.
  • the product or semi-finished product produced from the alloy according to the invention by forming which can be, for example, hot strip, cold strip, flexibly rolled hot or cold strip, a pipe or a body component, is therefore advantageously heat treated at 480 to 770 ° C for 1 minute to 48 hours, for example in a hood annealing with predominantly long annealing times or in a continuous annealing with predominantly short annealing times.
  • Such annealing can also take place before the final shaping into a finished product, for example on the cold strip, which is then further processed.
  • the time of annealing can therefore be flexibly adapted to the manufacturing process.
  • Annealing the end product in addition to annealing the semi-finished product can lead to a further improvement in the material properties.
  • the cast strip with a maximum thickness of 5 mm produced by means of a near-net-shape casting process it is particularly advantageous to cold-roll it to a uniform thickness or to flexibly cold-roll it to different thicknesses and then anneal the cold strip with the following parameters: Annealing temperature: 480 to 770 ° C Annealing time: 1 minute to 48 hours.
  • the annealing treatment is preferably carried out at temperatures of 670 to 770 ° C. for annealing times of 1 minute to 12 hours, since lower temperatures and longer annealing times lead to lower tensile strength and elongation at break.
  • continuous annealing is preferably used for short annealing times for hot strip, cold strip and flexibly rolled strip, and hood annealing is preferably used for long annealing times.
  • other annealing devices with the specified parameters such as a muffle furnace, can be used.
  • antimony also improves the behavior towards it Significantly improved hydrogen (delayed crack formation and hydrogen embrittlement).
  • the reason for the improvement in the material properties is that antimony hinders the diffusion of carbon and aluminum. Furthermore, antimony lowers the interfacial energy, which leads to a finer distribution of the carbides.
  • the reduced carbon diffusion thus delays the local accumulation of carbon at the grain boundaries and in the structure as well as, in connection with aluminum, the formation of kappa carbides or, in particular with V, Nb, Mo, Cr, W, Zr and Ti, the formation of larger local carbides. This improves the homogeneity of the material with the described positive effects on the mechanical properties and the resistance to delayed crack formation and hydrogen embrittlement.
  • the precipitation of finely divided carbides leads to a grain refinement in the structure, which is accompanied by an improvement in the behavior towards negative effects caused by hydrogen (delayed crack formation, hydrogen embrittlement) as well as an increase in strength and an improvement in toughness and elongation properties.
  • antimony according to the invention in low contents of up to a maximum of 0.3% by weight therefore significantly improves the behavior of the material with respect to influences caused by hydrogen.
  • antimony causes an undesirably strong precipitation of antimony at the grain boundaries and thereby reduces the toughness and elongation properties.
  • a content of at least 30 ppm is necessary for antimony to be effective.
  • antimony contents of more than 0.3% by weight make the material brittle and should therefore be avoided.
  • the optimum content of antimony is 0.1% by weight.
  • the small carbides (predominantly Cr, Mo, Ti, Nb, V, W, Zr and Kappa carbides), which are separated out much more finely than in the prior art, improve the degree of utilization of the corresponding alloying elements, which potentially allows a reduction in the amount added. Furthermore, due to the reduced carbon diffusion and the reduced grain growth due to the addition of antimony, the process window for the invention The resulting mechanical properties of the steel are less sensitive to process fluctuations (temperature, time).
  • An alloy according to claim 3, using optimized heat treatment parameters (see Tables 1 to 4), has a product of tensile strength and elongation at break of at least 20,000 MPa% and a tensile strength of at least 800 MPa.
  • the product of tensile strength and elongation at break is a measure of the performance of the material during forming.
  • An alloy according to one embodiment has a product of tensile strength and elongation at break of at least 30,000 MPa% and a tensile strength of at least 800 MPa.
  • An alloy according to a further embodiment has finely divided kappa carbide precipitates and a product of tensile strength and elongation at break of at least 30,000 MPa% and a yield strength of at least 700 MPa and a tensile strength of at least 800 MPa.
  • Table 1 shows the alloy compositions tested. The content of Sb and additions of Nb were varied while the chemical composition was otherwise approximately the same.

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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)

Claims (6)

  1. Acier de construction léger pouvant être mis en forme et présentant des propriétés mécaniques améliorées et une résistance élevée à la fissuration retardée induite par de l'hydrogène et à la fragilisation due à l'hydrogène, l'acier comprenant (en % en poids) les éléments suivants :
    C de 0,03 à ≤ 0,5, de manière particulière avantageuse de 0,1 à 0,35 Mn de 5 à 9
    Si de 0,1 à 3, de manière particulièrement avantageuse de 0,1 à 1
    Al de 0,1 à 4, de manière particulièrement avantageuse de 1 à 3,5
    Cr > 0,1 à 5, de manière particulièrement avantageuse de 0,5 à 4
    V de 0,005 à 1, de manière particulièrement avantageuse de 0,02 à 0,1
    P 0,1 maximum
    S 0,1 maximum
    N 0,03 maximum
    Sb de 0,005 à 0,3, de manière particulièrement avantageuse de 0,01 à 0,1
    et éventuellement un ou plusieurs des éléments de formation de carbure suivants dans la teneur spécifiée (en % en poids) :
    Mo de 0,05 à 2
    Ti de 0,01 à 2
    Nb de 0,005 à 1
    W de 0,005 à 1
    Zr de 0,001 à 0,3
    le reste étant du en fer, y compris des éléments habituels d'accompagnement de l'acier, avec addition supplémentaire facultative des éléments suivants en % en poids : Ni 5 maximum, Co 10 maximum, Ca 0,005 maximum, B 0,001 maximum et Cu de 0,05 à 2.
  2. Acier de construction léger selon la revendication 1, caractérisé en ce que le rapport Sb/C est inférieur ou égal à 1,5.
  3. Acier de construction léger selon la revendication 1 ou 2, caractérisé en ce que l'acier présente un produit de résistance à la traction et d'allongement à la rupture d'au moins 20000 MPa % et une résistance à la traction d'au moins 800 MPa.
  4. Procédé de production d'un acier selon les revendications 1 à 3, le procédé comprenant les étapes suivantes :
    - couler de l'acier selon le procédé de coulée continue, le procédé de coulée de brames minces ou d'un procédé de coulée de bandes horizontales ou verticales proches des dimensions finales,
    - laminer à chaud la brame coulée ou bande coulée d'une épaisseur supérieure à 5 mm à une épaisseur uniforme ou laminer à chaud de manière flexible à différentes épaisseurs,
    - éventuellement laminer à froid la bande laminée à chaud à une épaisseur uniforme ou une bande coulée de 5 mm d'épaisseur maximale produite au moyen de procédés de coulée proche des dimension finales à une épaisseur uniforme ou lamine à froid de manière flexible à différentes épaisseurs,
    - éventuellement recuire la bande chaude ou froide avec les paramètres suivants :
    température de recuit : 480 à 770 °C,
    durée de recuit : 1 minute à 48 heures.
  5. Procédé selon la revendication 4, caractérisé en ce que la bande coulée d'une épaisseur maximale de 5 mm produite au moyen d'un procédé de coulée proche des dimensions finales est laminée à froid à une épaisseur uniforme ou est laminée à froid de manière flexible à différentes épaisseurs puis la bande froide est recuite avec les paramètres suivants :
    température de recuit : 480 à 770 °C,
    temps de recuit : 1 minute à 48 heures.
  6. Procédé selon la revendication 4 ou 5, caractérisé en ce que, pour des alliages à Al > 1 % en poids, le recuit est de préférence réalisé à des températures de 670 à 770 °C avec des temps de recuit de 1 minute à 12 heures.
EP16750113.9A 2015-07-22 2016-07-20 Acier léger deformable de construction présentant des propriétés mécaniques améliorées et procédé de fabrication de produit semi-fini à partir de cet acier Active EP3325678B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102015111866.1A DE102015111866A1 (de) 2015-07-22 2015-07-22 Umformbarer Leichtbaustahl mit verbesserten mechanischen Eigenschaften und Verfahren zur Herstellung von Halbzeug aus diesem Stahl
PCT/EP2016/067347 WO2017013193A1 (fr) 2015-07-22 2016-07-20 Acier léger deformable de construction présentant des propriétés mécaniques améliorées et procédé de fabrication de produit semi-fini à partir de cet acier

Publications (2)

Publication Number Publication Date
EP3325678A1 EP3325678A1 (fr) 2018-05-30
EP3325678B1 true EP3325678B1 (fr) 2021-04-21

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Country Status (6)

Country Link
US (1) US20180216207A1 (fr)
EP (1) EP3325678B1 (fr)
KR (1) KR102096190B1 (fr)
DE (1) DE102015111866A1 (fr)
RU (1) RU2691436C1 (fr)
WO (1) WO2017013193A1 (fr)

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CN107841691B (zh) * 2017-10-25 2019-05-21 河北工业大学 一种750MPa级超高强度Fe-Mn-Al-C系轻质铸钢及其制备方法
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RU2721681C1 (ru) * 2019-12-23 2020-05-22 Федеральное Государственное Унитарное Предприятие "Центральный научно-исследовательский институт черной металлургии им. И.П. Бардина" (ФГУП "ЦНИИчермет им. И.П. Бардина") Способ производства холоднокатаного непрерывно отожженого листового проката из if-стали
CN111607740A (zh) * 2020-06-24 2020-09-01 安徽工业大学 高强度低密度钢的制备方法及高强度低密度钢
CN111593263A (zh) * 2020-06-24 2020-08-28 安徽工业大学 一种高强度低密度钢的制备方法及高强度低密度钢
CN114752867B (zh) * 2022-04-25 2022-10-11 燕山大学 一种高强韧轻质钢及其制备方法和应用

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US20180216207A1 (en) 2018-08-02
EP3325678A1 (fr) 2018-05-30
WO2017013193A1 (fr) 2017-01-26
KR102096190B1 (ko) 2020-04-02
RU2691436C1 (ru) 2019-06-13
DE102015111866A1 (de) 2017-01-26
KR20180033202A (ko) 2018-04-02

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