WO2017001303A1 - Bande d'acier galvanisé à chaud à haute résistance - Google Patents

Bande d'acier galvanisé à chaud à haute résistance Download PDF

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Publication number
WO2017001303A1
WO2017001303A1 PCT/EP2016/064704 EP2016064704W WO2017001303A1 WO 2017001303 A1 WO2017001303 A1 WO 2017001303A1 EP 2016064704 W EP2016064704 W EP 2016064704W WO 2017001303 A1 WO2017001303 A1 WO 2017001303A1
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WIPO (PCT)
Prior art keywords
strip
temperature
steel strip
hot dip
amount
Prior art date
Application number
PCT/EP2016/064704
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English (en)
Inventor
Joost Willem Hendrik VAN KREVEL
Cornelia IONESCU
Bernard Leo ENNIS
Original Assignee
Tata Steel Ijmuiden B.V.
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Tata Steel Ijmuiden B.V. filed Critical Tata Steel Ijmuiden B.V.
Priority to US15/580,776 priority Critical patent/US20180230570A1/en
Priority to CA2989710A priority patent/CA2989710A1/fr
Priority to MX2017016843A priority patent/MX2017016843A/es
Priority to CN201680032956.7A priority patent/CN107787375A/zh
Priority to BR112017023814A priority patent/BR112017023814A2/pt
Priority to JP2017567681A priority patent/JP2018524471A/ja
Priority to KR1020177034172A priority patent/KR20180025852A/ko
Priority to EP16733424.2A priority patent/EP3317431B1/fr
Priority to ES16733424T priority patent/ES2781781T3/es
Publication of WO2017001303A1 publication Critical patent/WO2017001303A1/fr
Priority to ZA2017/07294A priority patent/ZA201707294B/en

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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
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
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    • 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
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    • 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
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    • 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
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    • 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
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    • 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
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • 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
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    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals

Definitions

  • the invention relates to a high strength hot dip galvanised steel strip having improved formability, such as used in the automotive industry.
  • the invention also relates to a method for producing such steel strip.
  • Formability is not the only requirement for a TRIP assisted dual phase steel strip.
  • the alloying elements should be low in amount to make the cost of the steel as low as possible, and it should be as easy as possible to produce the steel strip at a broader width both in the hot rolling mill and in the cold rolling mill.
  • the steel strip should be easy to coat with a zinc based coating, the steel strip has to have high strength and a good weldability, and should also exhibit a good surface quality.
  • the balance being Fe and inevitable impurities.
  • the inventors have found that by a careful selection of the amounts of the main constituting elements of the steel, being carbon, manganese, silicon, aluminium, chromium and boron, a high strength hot dip galvanised steel strip can be produced that has the required formability, homogeneity, processability, strength and elongation, while at the same time providing a sufficient weldability, coatability and surface quality.
  • the inventors have especially found that it is advantageous to add boron to the composition of the steel.
  • the hot rolled steel can be cooled fast enough on the run-out table to get a coiling temperature that provides a suitable microstrueture for further processing.
  • the inventors due to the addition of boron, the inventors have found that the properties of the end product have a high degree of homogeneity.
  • the steel strip can be produced in a width that is commercially interesting.
  • TRIP assisted steel grades can be made by intercritically annealing of the cold rolled strip so that ferrite nucleation is not required.
  • adding boron improves the hardenability of the steel, resulting in the possibility to use less of the other alloying elements. This results in an improved dimensional window for the steel strip, meaning a higher width to thickness ratio while the mechanical properties of the steel over the width of the strip remain suitable.
  • the reason for the amounts of the main constituting elements is as follows.
  • C 0.10 - 0.21 mass %.
  • Carbon has to be present in an amount that is high enough to ensure hardenability and the formation of martensite at the cooling rates available in a conventional annealing/galvanising line. Martensite is required to deliver adequate strength. Free carbon also enables stabilisation of austenite which delivers improved work hardening potential and good formability for the resulting strength level. A lower limit of 0.10 mass % is needed for these reasons. A maximum level of 0.21 mass % has been found to be essential to ensure good weldability.
  • Mn 1.75 - 2.50 mass %.
  • Manganese is added to increase hardenability thus making the formation of hard phases like martensite or bainite easier within the cooling rate capability of a conventional continuous anneal ing/galvanising line.
  • Manganese also contributes to the solid solution strengthening which increases the tensile strength and strengthens the ferrite phase, and also helps to stabilise retained austenite.
  • Manganese lowers the transformation temperature range of the dual phase steel, thus lowering the required annealing temperature to levels that can be readily attained in a conventional continuous annealing/galvanising line.
  • a lower limit of 1.75 mass % is needed for the above reasons. This lower limit is possible in view of the addition of other elements, such as boron.
  • a maximum level of 2.50 mass % is imposed to ensure acceptable rolling forces in the hot mill and to ensure acceptable rolling forces in the cold mill by ensuring sufficient transformation of the dual phase steel to soft transformation products (ferrite and pearlite). This maximum level is also given in view o the stronger segregation during casting and the forming o a band of martensite in the strip at higher values.
  • the amount of manganese is between 1.9 and 2.3 mass %, more preferably between 2.0 and 2.2 mass % Si: 0.04 - 0.60 mass %. Silicon provides solid solution strengthening thus enabling the attainment of high strength, and the stabilisation of austenite via strengthening of the ferrite matrix.
  • Silicon very effectively retards the formation of carbides during overaging, thus keeping carbon in solution for stabilisation of austenite. For these reasons a lower limit o 0.04 mass % is needed. A maximum level of 0.60 mass % is imposed in view of the coatability of the steel strip, since high levels o silicon lead to unacceptable coating quality due to reduced adherence.
  • Al 0.20 - 1.40 mass %. Aluminium is added to liquid steel for the purpose of de- oxidation. In the right quantity it also provides an acceleration of the bainite transformation, thus enabling bainite formation within the time constraints imposed by the annealing section o a conventional continuous annealing/galvanising line. Aluminium also retards the formation of carbides thus keeping carbon in solution, thus causing partitioning to austenite during overaging, and promoting the stabilisation f austenite. A lower level of 0.20 mass % is required for the above reasons. A maximum level of 1.40 mass % is imposed for castability, since high aluminium contents lead to poisoning of the casting mould slag and consequently an increase in mould slag viscosity, leading to incorrect heat transfer and lubrication during casting.
  • Cr max 0.50 mass %. Chrome is added to increase hardenability. Chrome promotes formation of ferrite. A maximum level of 0.50 mass % is imposed to ensure that not too much martensite forms at the cost or retained austenite. It is also possible to add no chrome. Preferably, the amount of Cr is between 0.01 and 0.40 mass%, more preferably between 0.02 and 0.25 mass %.
  • Titanium is mainly added to strengthen the steel. A maximum level of 0.20 % is imposed to limit the cost of the steel. It is also possible to add no Ti.
  • Ca max 0.004 mass %.
  • the addition of calcium modifies the morphology of manganese sulphide inclusions. When calcium is added the inclusions get a globular rather than an elongated shape. Elongated inclusions, also called stringers, may act as planes of weakness along which lamellar tearing and delamination fracture can occur. The avoidance of stringers is beneficial for forming processes of steel sheets which entail the expansion of holes or the stretching of flanges and promotes isotropic forming behaviour.
  • Calcium treatment also prevents the formation of hard, angular, abrasive alumina inclusions in aluminium deoxidised steel types, forming instead calcium aluminate inclusions which are softer and globular at rolling temperatures, thereby improving the material's processing characteristics.
  • some inclusions occurring in molten steel have a tendency to block the nozzle, resulting in lost output and increased costs.
  • Calcium treatment reduces the propensity for blockage by promoting the formation of low melting point species which will not clog the caster nozzles. It is also possible to add no calcium when the sulphur content is very low.
  • the amount of Ca is between 0.0005 and 0.003 mass%.
  • P 0.001 - 0.025 mass%.
  • Phosphorus interferes with the formation of carbides, and therefore some phosphorus in the steel is advantageous.
  • phosphorus can make steel brittle upon welding, so the amount of phosphorus should be carefully controlled during steelmaking, especially in combination with other embrittling elements such as sulphur and nitrogen.
  • embrittling elements such as sulphur and nitrogen.
  • boron it is possible to have more phosphorus in the steel then usual.
  • the content of Nitrogen is limited to max 0.01 wt% as is typical for continuous casting plants. Usually, the amount of N is between 0.001 and 0.010 wt%.
  • the ranges for aluminium, boron, silicon, chromium and manganese are chosen such that a correct balance is found to deliver a transformation that is as homogeneous as possible on the run-out table and during coil cooling, to ensure a steel strip that can be cold rolled, and to provide a starting structure enabling rapid dissolution of carbon in the annealing line to promote hardenability and correct ferritie/bainitic transformation behaviour.
  • aluminium accelerates and chromium decelerates the bainitic transformation
  • the right balance between aluminium and chromium has to be present to produce the right quantity of bainite within the timescales permitted by a conventional hot dip galvanising line with a restricted overage section. In practice, this means that the content of aluminium should be higher than the content of chromium.
  • the amounts of Al and Si are chosen such that 0.60 % ⁇ Al + Si ⁇ 1.40 %
  • the amounts of Mn and Cr are chosen such that Mn + Cr > 2.00 %.
  • the amounts of Al and Si are chosen such that Si ⁇ Al.
  • Aluminium and silicon together should be maintained between 0.60 and 1.40 mass% to ensure suppression of carbides in the end product and stabilisation of a sufficient amount of austenite, with the correct composition, to provide a desirable extension of formability.
  • Manganese and chromium together should be above 2.00 mass% to ensure sufficient hardenability for formation of martensite and/or bainite and thus achievement of strength in a conventional continuous annealing line and hot dip galvanising line.
  • Mn aids to stabilise retained austenite.
  • Mn + Cr should be above 2.10 mass%, especially when the amount of Si is low.
  • Al should preferably be present in an amount equal to or higher then Si in view of a good zinc coatability.
  • element C is present in an amount of 0.13 - 0.18 %. In this range the hardenability of the steel is optimal while the weldability of the steel is enhanced, also by the presence of boron. More preferably element C is present in an amount of 0.14 0.17 %. This amount of C has been found to work well in practice.
  • element Si is present in an amount of 0.05 - 0.50 %, more preferably 0.05 - 0.40 %.
  • a amount of silicon lower then 0.50 % improves the coatability of the steel strip, even more so when the amount of silicon is below 0.40 %.
  • element Al is present in an amount of 0.30 - 1.20 %, preferably an amount of 0.40 - 1.00 %.
  • a raised lower level of aluminium has the same effect as a higher amount of silicon, but hardly increases the strength of the steel.
  • a lower upper limit of aluminium improves the castability of the steel.
  • the amount of element B is preferably between 0.001 1 and 0.0040 %, more preferably between 0.0013 and 0.0030 %. to provide the desired hardenability and hence bring sufficient strength.
  • the amount of Ti is preferably max 0.10 % so as to limit the cost of the steel and keep the dimensional window as large as possible. More preferably, the amount of Ti is between 0.005 and 0.05 %.
  • the hot dip galvanised steel strip has an ultimate tensile strength Rm above 750 MPa and/or a 0.2 % proof strength Rp of 430 - 700 MPa, preferably the difference between the middle and the edges of the steel strip being less then 75 MPa for both Rp and/or Rm, more preferably this difference being less then 60 MPa. These strength levels can be achieved with the composition according to the invention.
  • the hot dip galvanised steel strip has a microstructure, consisting of 20-50 volume % ferrite, 10-25 volume % retained austenite + martensite, of which 5-12% retained austenite, the remainder being tempered martensite, bainite and cementite.
  • a method for producing a high strength hot dip galvanised steel strip as defined above, wherein the cast steel is hot rolled to a thickness of 2.0 - 4.0 mm and coiled at a Coiling Temperature CT below Bs-20 °C temperature and above Ms+60 °C temperature, the strip is cold rolled with a reduction of 40 % or more, after which the strip is intercritically annealed at a temperature between Acl and Ac3 temperature, and the strip is overaged at a temperature below Bs temperature to form bainite and/or tempered martensite, after which the strip is hot dip galvanised.
  • the hot rolled coil has a microstructure consisting of 50 - 70 volume % ferrite, 20 - 50 volume % pearlite and/or bainite, and less then 10 % cementite.
  • the coil has the right properties for further processing, especially for the annealing step, and can be cold rolled in a wide dimensional window.
  • the hot dip galvanised strip is tension rolled with a reduction of 0.2 - 0.8 %. This percentage of tension rolling can provide the right mechanical properties to the strip, such as the right strength level, while the other properties remain inside the desired window.
  • a method for producing a high strength hot dip galvanised complex phase steel strip wherein the cast steel is hot rolled to a thickness of 2.0 - 4.0 mm and coiled at a Coiling Temperature CT below Bs-20 °C temperature and above Ms+60 °C temperature, the strip is cold rolled with a reduction o 40% or more, after which the strip is annealed at a temperature above Acl temperature plus 50° C, and the strip is overaged at a temperature below Bs temperature to form bainite and/or tempered martensite, after which the strip is hot dip galvanised.
  • This complex phase steel strip can be made due to the precise Coiling Temperature and the prescribed annealing and overaging temperatures.
  • this hot dip galvanised complex phase steel strip is tension rolled with a reduction o 0.4 - 2.0 %, preferably with a reduction of 0.4 - 1.2 %.
  • This percentage of tension rolling can provide the right mechanical properties to the strip, such as the right strength level, while the other properties remain inside the desired window.
  • Figure 1 shows measurement of the ultimate tensile strength Rm and 0.2% proof strength Rp after annealing.
  • compositions are defined in mill-wt%.
  • Bs and Ms values were calculated from [I J.
  • Casts number 1, 2, 3, 5 and 6 were hot rolled with a hot roll finishing temperature of
  • Table2 typical martensite + austenite distribution over different positions in the coil.
  • the material was hot and subsequently cold rolled to a typical gauge in the range 0.8-2.0 mm.
  • microstructure and phase fractions defined is provided in Figure 2.
  • microstructure over different sampling positions over the coil is provided in Table 2.
  • the microstructure is given for the head, middle and tail of a coil.
  • M indicates the middle of the strip, R the right hand side.
  • a Dual Phase steel strip was produced.
  • the hot roll finishing temperature was approximately 875 °C for all casts but for cast 4, as indicated above.
  • the coiling temperature was between 500-520 °C, well between Bs-20 °C and Ms + 60 °C.
  • the material was cold rolled and intercritically annealed at around 800 °C, and the overage temperature was 400 °C.
  • the strip was temper rolled with a reduction of around 0.3%.
  • Figure 2 shows typical microstructures ( ital etched) obtained at the middle of the hot rolled strip product, after coiling and cooling down. Used is the composition of cast 1.
  • the coiling temperature CT was 500 °C.
  • the right-hand picture shows the same material but after a coiling temperature of 550 °C.
  • the dark phase is perlite/bainite and the light phase is ferrite; black dots arc cementite.
  • perlite/bainite is present in 25-35%, ferrite 60-70% and cementite less than 10%.
  • perlite/bainite is present in 20-30%, ferrite 65-75% and cementite less than 10%.
  • Figure 3 shows the variation in Rm and Rp over the width of the strip.
  • Figure 3a shows this variation for a strip composition that is not according to the invention, having a composition of 0.15 C, 2.05 Mn, 0.2 Cr, 0.7 Al, 0.07 Si, 0.015 Nb and 0.004 N (in wt%).
  • the difference in Rm between middle and edge of the strip is approximately 100 MPa, the difference in Rp is approximately 50 MPa.
  • Figure 3b shows the variation in Rm and Rp for a strip with the composition of cast 1. This figure shows that it is possible to get a variation between the middle and the edge of the strip that is less than 20 MPa for both Rm and Rp.
  • Figure 3c shows in fact the same for a strip with the composition of cast 3. The strip shown in figures 3b and 3c has been manufactured in accordance with the method of the invention.
  • Figure 4 shows three different ways of graphically indicating the microstructures of the casts after using the method of the invention. These are the well known Picral, Nital and LePera representations. In the Picral graphs black represents bainite or tempered martensite. In the Nital graph the white spots indicate ferrite. In contrast, in the LePera graph white indicates (tempered) martensite + retained austenite. The differences between DP800 on the left-hand side and CP 800 on the right-hand side are clearly visible.

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  • Mechanical Engineering (AREA)
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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
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  • Crystallography & Structural Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
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  • Coating With Molten Metal (AREA)

Abstract

L'invention concerne une bande d'acier galvanisé à chaud à haute résistance comprenant, en pourcentage, les éléments suivants : de 0,10 à 0,21 % de C, de 1,75 à 2,50 % de Mn, de 0,04 à 0,60 % de Si, de 0,20 à 1,40 % d'Al, de 0,001 à 0,025 % de P, de 0,0005 à 0,0050 % de B, 0,50 % de Cr maximum, 0,20 % de Ti maximum, 0,004 % de Ca maximum, 0,015 % de N maximum, le reste étant constitué de Fe et d'impuretés inévitables.
PCT/EP2016/064704 2015-07-01 2016-06-24 Bande d'acier galvanisé à chaud à haute résistance WO2017001303A1 (fr)

Priority Applications (10)

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US15/580,776 US20180230570A1 (en) 2015-07-01 2016-06-24 High strength hot dip galvanised steel strip
CA2989710A CA2989710A1 (fr) 2015-07-01 2016-06-24 Bande d'acier galvanise a chaud a haute resistance
MX2017016843A MX2017016843A (es) 2015-07-01 2016-06-24 Banda de acero galvanizada por inmersion en caliente de alta resistencia.
CN201680032956.7A CN107787375A (zh) 2015-07-01 2016-06-24 高强度热镀锌钢带材
BR112017023814A BR112017023814A2 (pt) 2015-07-01 2016-06-24 tira de aço de alta resistência galvanizada por imersão a quente
JP2017567681A JP2018524471A (ja) 2015-07-01 2016-06-24 高強度溶融亜鉛めっき鋼帯
KR1020177034172A KR20180025852A (ko) 2015-07-01 2016-06-24 고강도 용융 침지 아연도금 강 스트립
EP16733424.2A EP3317431B1 (fr) 2015-07-01 2016-06-24 Bande d'acier galvanisé à chaud haute résistance
ES16733424T ES2781781T3 (es) 2015-07-01 2016-06-24 Fleje de acero galvanizado por inmersión en caliente de alta resistencia
ZA2017/07294A ZA201707294B (en) 2015-07-01 2017-10-26 High strength hot dip galvanized steel strip

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WO2020058330A1 (fr) * 2018-09-19 2020-03-26 Sms Group Gmbh Acier avancé à haute limite d'élasticité, bande en acier composée de cet acier ainsi que procédé pour la fabrication d'une bande en acier
WO2020221628A1 (fr) * 2019-04-30 2020-11-05 Tata Steel Ijmuiden B.V. Procédé de production d'une bande laminée sur mesure à recuit discontinu
WO2020245626A1 (fr) * 2019-06-03 2020-12-10 Arcelormittal Tôle d'acier laminée à froid et revêtue et son procédé de fabrication
DE102020110319A1 (de) 2020-04-15 2021-10-21 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines Stahlbandes mit einem Mehrphasengefüge und Stahlband hinzu

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BR112018011831B1 (pt) 2015-12-15 2022-11-29 Tata Steel Ijmuiden Bv Tira de aço galvanizada por imersão a quente de alta resistência e método de produção
WO2020245627A1 (fr) * 2019-06-03 2020-12-10 Arcelormittal Tôle d'acier laminée à froid et revêtue et son procédé de fabrication
CN113355604B (zh) * 2021-06-25 2022-05-24 攀钢集团攀枝花钢铁研究院有限公司 低成本700MPa级热镀锌复相钢板及其制备方法
CN117802400A (zh) * 2022-09-23 2024-04-02 宝山钢铁股份有限公司 一种低点焊裂纹敏感性的带镀层超高强钢及其制造方法

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WO2020058330A1 (fr) * 2018-09-19 2020-03-26 Sms Group Gmbh Acier avancé à haute limite d'élasticité, bande en acier composée de cet acier ainsi que procédé pour la fabrication d'une bande en acier
WO2020221628A1 (fr) * 2019-04-30 2020-11-05 Tata Steel Ijmuiden B.V. Procédé de production d'une bande laminée sur mesure à recuit discontinu
WO2020245626A1 (fr) * 2019-06-03 2020-12-10 Arcelormittal Tôle d'acier laminée à froid et revêtue et son procédé de fabrication
WO2020245668A1 (fr) * 2019-06-03 2020-12-10 Arcelormittal Tôle d'acier laminée à froid et revêtue et son procédé de fabrication
DE102020110319A1 (de) 2020-04-15 2021-10-21 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines Stahlbandes mit einem Mehrphasengefüge und Stahlband hinzu

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BR112017023814A2 (pt) 2018-07-31
CN107787375A (zh) 2018-03-09
JP2018524471A (ja) 2018-08-30
ZA201707294B (en) 2019-02-27
MX2017016843A (es) 2018-04-24

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