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WO2014198399A2 - Procédé de formage à chaud d'une bandelette, d'une feuille ou d'une ébauche revêtue de zinc ou d'un alliage de zinc - Google Patents

Procédé de formage à chaud d'une bandelette, d'une feuille ou d'une ébauche revêtue de zinc ou d'un alliage de zinc Download PDF

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Publication number
WO2014198399A2
WO2014198399A2 PCT/EP2014/001540 EP2014001540W WO2014198399A2 WO 2014198399 A2 WO2014198399 A2 WO 2014198399A2 EP 2014001540 W EP2014001540 W EP 2014001540W WO 2014198399 A2 WO2014198399 A2 WO 2014198399A2
Authority
WO
WIPO (PCT)
Prior art keywords
zinc
blank
thickness
formed product
coating
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/EP2014/001540
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English (en)
Other versions
WO2014198399A3 (fr
Inventor
Guido Cornelis Hensen
Willem Cornelis Verloop
Bastiaan Maarten NEELIS
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Tata Steel Ijmuiden BV
Original Assignee
Tata Steel Ijmuiden BV
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 BV filed Critical Tata Steel Ijmuiden BV
Publication of WO2014198399A2 publication Critical patent/WO2014198399A2/fr
Publication of WO2014198399A3 publication Critical patent/WO2014198399A3/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • 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
    • C21D1/62—Quenching devices
    • C21D1/673—Quenching devices for die quenching
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
    • C23C2/36—Elongated material
    • C23C2/40—Plates; Strips
    • C23C2/405—Plates of specific length
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/30—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer
    • C23C28/32—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one pure metallic layer
    • C23C28/321—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one pure metallic layer with at least one metal alloy layer
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/30—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer
    • C23C28/34—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one inorganic non-metallic material layer, e.g. metal carbide, nitride, boride, silicide layer and their mixtures, enamels, phosphates and sulphates
    • C23C28/345—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one inorganic non-metallic material layer, e.g. metal carbide, nitride, boride, silicide layer and their mixtures, enamels, phosphates and sulphates with at least one oxide layer
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
    • C21D7/04—Modifying the physical properties of iron or steel by deformation by cold working of the surface
    • C21D7/06—Modifying the physical properties of iron or steel by deformation by cold working of the surface by shot-peening or the like

Definitions

  • the invention relates to a method for hot forming a strip, sheet or blank coated with a zinc or zinc based alloy layer to form a hot formed product.
  • the method also relates to the hot formed product thus produced.
  • Hot forming a steel product is nowadays a much used method in the automotive industry.
  • hot formable steel is heated to a temperature above the Ac3 temperature and formed in a press, and thereafter quenched to provide a high tensile strength, while at the same time obtaining a sufficient high elongation.
  • aluminium alloy coated steel blanks are hot formed; usually an aluminium alloy containing silicon is used.
  • a method for hot forming a strip, sheet or blank coated with a zinc or zinc based alloy layer to form a hot formed product characterised in that:
  • a - the strip, sheet or blank has a thickness between 0.7 and 2.1 mm;
  • b - the zinc or zinc based alloy layer is a coating layer containing between 8 and 16 % iron;
  • the zinc or zinc based alloy layer has a coating thickness of between 6 and 13 ⁇ on each side of the strip, sheet or blank;
  • the blank is heated to a temperature between 850° C and 920° C, whereby a zinc-oxide layer is formed having a thickness of less then 50 g/m 2 on both sides of the blank;
  • the blank is hot formed in the hot forming press to obtain the hot formed product
  • the hot formed product is provided with an iron-zinc coating layer having a thickness between 10 and 30 ⁇ containing at least 65 % iron;
  • the hot formed product is quenched in the hot forming press to a temperature below 300° C using an average cooling rate higher than 40° C/sec to obtain a high tensile strength;
  • the zinc or zinc based alloy layer on each side of the strip, sheet or blank has a thickness variation of at most plus or minus 2.0 ⁇
  • a hot formed product having a high tensile strength, depending on the hot formable steel used, and having an elongation that is acceptable for automotive purposes.
  • the iron-zinc coating has a thickness such that a sufficient cathodic protection is obtained, and the hot formed product is weldable (with or without deployment of shot-blasting).
  • the time that is meant in feature f is the so-called “free on air” time, which in practice means the time between the opening of the furnace and the closing of the press.
  • the thickness variation of the zinc or zinc based layer on each side of the strip, sheet or blank should be limited, much more strict than regular NEN-EN standards, to provide a robust performance which is acceptable to the automotive manufacturers.
  • the minimum single spot coating thickness variation is limited to guarantee sufficient corrosion performance in each and every location of the strip.
  • the upper limit is less tight since more protection than required is less of a problem to the end user in case of cold forming. This can be seen in for example NEN-EN10336:2005 and NEN-10327:2005 where the lower limit is 2 to 3 pm below the average and the upper limit is commonly 5 pm above the average for galvannealed steel strip.
  • the inventors have found that the furnace time required to eliminate the presence of zinc-rich phases responsible for liquid metal embrittlement (LME) during hot forming is dependent on the maximum coating thickness on the strip.
  • the elimination of Zn-rich phases comes about by diffusion of iron from the steel substrate into the coating.
  • Experimental data illustrate that a difference in average coating thickness of approximately 1 pm between two materials requires 1.5 minutes extra furnace dwell time to ensure elimination of LME. For this reason the inventors round that it is required to limit the variation in coating thickness, especially the upper limit, to provide the end-user with a material that performs more robust in the hot forming process and does not need additional furnace dwell time to eliminate Zn-rich phases in locations with increased coating thickness.
  • coating thickness variation is brought about by tighter control of process parameters in the galvannealing line than is common for cold forming grades. Prior to tight control of line speed, air knife distance, wiping pressure and strip geometry the variations in coating thickness are larger than after these parameters have become part of the operators increased focus.
  • the zinc or zinc based alloy layer is a galvannealed coating layer.
  • the galvannealed coating layer has a good adhesion to the strip, sheet or blank substrate.
  • the zinc-oxide layer formed during the heating of the blank has a thickness between 10 and 50 g/m 2 .
  • This is the zinc-oxide layer that is formed on a zinc-coated blank during heating in a furnace for which no protective measures are taken, such as a protective atmosphere.
  • the zinc or zinc based alloy layer has a coating thickness of between 8 and 1 1 pm on each side of the strip, sheet or blank, and the hot formed product is provided with an iron-zinc coating layer having a thickness between 20 and 30 pm.
  • these thicknesses are suitable. A thinner coating will not provide enough corrosion protection, whereas a thicker coating is expensive without providing a better protection.
  • the strip, sheet or blank has a tensile strength between 450 and 650 MPa and the hot formed product has a tensile strength between 1300 and 1600 MPa.
  • a tensile strength before hot forming makes it possible to obtain a high tensile strength after hot forming, and such a tensile strength of the hot formed part is usually required by the automotive industry.
  • the zinc or zinc based alloy layer has a thickness variation at most plus or minus 1.5 pm, preferably a thickness variation of at most plus or minus 1.0 pm.
  • a further limitation of the thickness variation provides a product that has an even more robust performance.
  • the heating of step e) is performed during a heating time chosen such that the minimum total heating time depends on the thickness of the coating.
  • the heating time should be chosen such that no liquid iron zinc phases remain after the heating.
  • Tbiank is the temperature of the blank during heating in °C
  • Tfumace is the temperature inside the furnace in °C
  • t C oating is the thickness of the original coating in pm
  • A is a parameter dependent on the required microcrack depth and corrosion performance, wherein A is at most 5, preferably 4, more preferably 3 and most preferably 2.
  • the heating can thus be performed during a time that takes account of the thickness of the blank and the thickness of the coating.
  • the dependence of parameter A on the required microcrack depth means that to minimise the microcracks the parameter A has to be higher, but for cost efficiency and corrosion performance reasons the parameter A should be as low as possible.
  • the strip, sheet or blank has been made from steel having the following composition in weight %:
  • Mn 0.5 - 3.5, preferably 1.0 - 2.5
  • Si 0.1 - 0.8, preferably 0.1 - 0.4
  • Ti up to 0.2, preferably up to 0.1
  • Al up to 0.2, preferably up to 0.1
  • Nb up to 2, preferably up to 0.1
  • V up to 2, preferably up to 0.1
  • the hot formed product is airless shot-blasted using shot- blast having a hardness of at least 48 HRC and a diameter of at most 1.2 mm, whereby the zinc oxide layer is reduced to a thickness below 30 g/m 2 on both sides of the product.
  • Shot-blasting is a cost-effective way to reduce the thickness of the zinc oxide layer. It has been found that using shot-blast having a hardness of at least 48 HRC and a diameter of at most 1.2 mm provides a good surface quality.
  • a reduction of the zinc oxide layer is needed when the zinc oxide layer is thicker than 30 g/m 2 on each side of the product. It has been found that the thickness of the zinc oxide layer should we less so as to obtain a good spot weldability.
  • a hot formed product produced using the method as described above having a tensile strength between 1300 and 1600 MPa and a contact resistance as measured below 2 mOhm, preferably a contact resistance as measured below 1.5 mOhm, more preferably a contact resistance as measured below 1 mOhm.
  • the hot formed product has the tensile strength as commonly used by the automotive industry and has a contact resistance that is low enough to make the product weldable.
  • a contact resistance above 2 mOhm is likely to result in surface splashing during resistance spot welding and will reduce weld quality.
  • the product has an electrochemical potential as measured between the substrate and the coating of at least 50 mV, more preferably at least 100 mV, still more preferably at least 150 mV.
  • the product thus provides cathodic protection, which protection is better when the electrochemical potential between the substrate and the coating is higher.
  • the steel of the product has a minimum bending angle cti rnm of at least 40°, preferably at least 45°, more preferably at least 50°,
  • ai mm dm - t
  • a m is measured according to VDA 238-100 and t is the substrate thickness in mm.
  • the steel of the product has a minimum elongation A50 of
  • the iron-zinc coating layer has a hardness of at least 250 HV. Such a hardness provides scratch resistance for the hot formed product.
  • the iron-zinc coating layer is oiled after shot-blasting to prevent corrosion during transport.
  • Fig 1 shows the electrochemical potential of two different hot formed samples
  • Fig 2 shows the effect of strain during quenching of hot formed samples on the martensite fraction in the steel
  • Fig 3 shows the ZnO present after hot forming and shot-blasting in relation to contact resistance
  • Fig 4 shows heating curves of material with different gauges.
  • Fig 5 shows the microcrack performance and corrosion performance as a function of the furnace dwell time.
  • Fig 6 shows the distribution of the coating weight with and without improved thickness control.
  • Tests have been performed using hot formable steel. Two types of samples have been tested, of which the particulars are given in Table 1 and 2.
  • Table 1 shows that both sample types have been galvannealed. Two coating thicknesses have been used; the amount of Fe in the coating is the same for all samples.
  • Table 2 shows that material A has a composition that is different from material B. Material A and B also differ in the thickness of the substrate. Material A and B both have a thickness and a composition in accordance with the invention. The indicated single spot minimum and single spot maximum are the values as measured.
  • Table 3 shows the mechanical properties of material A both before and after hot forming according to the invention. Using process conditions A as elucidated below, a tensile strength of 1470 MPa and an A50 total elongation of 6.2 % is reached, starting from a material having a tensile strength of 531 MPa.
  • Process conditions A are used in which no stamping is performed, such that the blank placed in the tool remains flat. This test is used to determine the mechanical properties, as shown in Table 3.
  • Process conditions B are used in a tool for hot forming, wherein a top-hat part is produced, meaning a part having the shape of a top hat in cross section. Tests using process conditions B are used to determine whether microcracks are formed and to what extent.
  • ank Tf urn ace - 30°C) + (t coa ting - 9)/2 + A, as shown in table 5.
  • the table shows that where the time the blank is kept in the furnace is shorter because parameter A is chosen shorter, the relative microcrack depth is larger. This means that when relatively shallow microcracks are desired, the parameter A to be used will be higher, meaning that the furnace dwell time has to be longer. This results in a thicker zinc-oxide layer formed on the blank before it is pressed in the hot forming press.
  • Table 6 shows that the presence of Zn-rich ⁇ phases, as determined by low angle XRD from the surface of the material after heat treatment and quenching, leads to Liquid Metal Embrittlement (LME). With increasing furnace dwell time, the fraction of these phases is reduced and the susceptibility of the material to LME is eliminated.
  • LME Liquid Metal Embrittlement
  • Table 6 Effect of furnace dwell time on presence of Zn-rich ( ⁇ ) and other phases in the FeZn coating after heat treatment and the effect on LME when forming at high temperatures.
  • Table 7 shows the influence the furnace dwell time has on the zinc oxide on the formed part after heating, where material B is used.
  • the zinc oxide has an important influence on the contact resistance of the hot formed material, in all cases but one resulting in a contact resistance above 1 mOhm.
  • the contact resistance can be lowered using shot-blasting, as shown in table 7. The result is that the contact resistance in most cases can be lowered to a value below 1 mOhm. This means in practice that the shot-blasted hot formed parts can be spot-welded without problems.
  • Table 7 The effect of furnace dwell time on ZnO and contact resistance prior and after blasting
  • Table 8 shows the effect of the shot-blasting process on the contact resistance where material A is used and the furnace dwell time is the same for all samples.
  • the contact resistance is above 3 mOhm for all samples.
  • Each sample was subjected to a different shot-blasting test, with the conditions as shown in table 9.
  • Table 8 Effect of blasting process on contact resistance Table 8 shows that parameters used in the shot-bla tt se r a g onavecting operation have a ressance ae r
  • the data represents the electrochemical potential of the coating (left part of the graph) versus the electrochemical potential of the substrate (right part of the graph).
  • the data shows that the electrochemical potential difference between the coating and the substrate reduces for higher A values and since a large electrochemical potential difference between coating and substrate is preferred, these results illustrate that preferably short furnace dwell times are used.
  • Figure 2 shows the effect of strain during cooling (50°C/s) on the martensite fraction of heat treated 22MnB5 type steel (900 °C, 6 min). It illustrates that 22 nB5 steel is sensitive to strain induced ferrite formation even at higher cooling rates. Strain is present in deformed steel, also when hot formed in a hot forming press. This means that cooling after hot forming in the press should take place well above the critical quenching rate, normally regarded to be 27 °C/s, to result high amounts of martensite. It also shows that the deformation temperature should be high. This means a short transport time to take the heated blank from the furnace and placing it in the hot forming press.
  • Figure 3 shows the relationship between the residual zinc oxide and the contact resistance after both hot forming and shot-blasting according to ISO standard. It shows the importance of the removal of as much zinc oxide as possible to improve weldability.
  • Figure 4 shows that the heating curves of material with different thicknesses. Clearly, the heating behaviour depends on the material thickness.
  • Figure 5 shows schematically the effect of furnace dwell time parameter A on both microcrack depth and corrosion performance. An optimum for both does not exist at the same A-value so one has to choose based on the specific requirements for these material aspects. From the point of view of production rate and reduced costs, a low A value is generally preferred.
  • Figure 5 shows the microcrack performance and corrosion performance as a function of the furnace dwell time parameter A. It shows what is discussed in relation to the tables above.
  • Figure 6 shows the distribution of the coating weight over four coils.
  • Figure 6a shows the coating weight distribution over the width and the length of coils for hot forming having a thickness of 1.5 mm before an improved process control on coating layer thickness.
  • Figure 6b shows the coating weight distribution over the length and width of corresponding coils after the improved process control on coating layer thickness.
  • the two figures clearly show the improved control of the coating thickness using a tight control of line speed, air knife distance, wiping pressure and strip geometry.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Organic Chemistry (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Inorganic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Articles (AREA)
  • Coating With Molten Metal (AREA)
  • Electroplating Methods And Accessories (AREA)

Abstract

Cette invention concerne un procédé de formage à chaud d'une bandelette, d'une feuille ou d'une ébauche revêtue d'une couche de zinc ou d'alliage à base de zinc pour obtenir un produit formé à chaud. Selon l'invention, un certain nombre d'étapes spécifiques sont exécutées pour mettre en œuvre ce procédé dans certaines limites. Un produit formé à chaud obtenu par le procédé selon l'invention est en outre décrit.
PCT/EP2014/001540 2013-06-14 2014-06-06 Procédé de formage à chaud d'une bandelette, d'une feuille ou d'une ébauche revêtue de zinc ou d'un alliage de zinc Ceased WO2014198399A2 (fr)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
EP13003043.0 2013-06-14
EP13003043 2013-06-14
EP13004166.8 2013-08-23
EP13004166 2013-08-23

Publications (2)

Publication Number Publication Date
WO2014198399A2 true WO2014198399A2 (fr) 2014-12-18
WO2014198399A3 WO2014198399A3 (fr) 2015-02-26

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PCT/EP2014/001540 Ceased WO2014198399A2 (fr) 2013-06-14 2014-06-06 Procédé de formage à chaud d'une bandelette, d'une feuille ou d'une ébauche revêtue de zinc ou d'un alliage de zinc

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2024132139A1 (fr) * 2022-12-21 2024-06-27 Voestalpine Metal Forming Gmbh Procédé de production de pièces en acier trempé
WO2024166854A1 (fr) * 2023-02-07 2024-08-15 日本製鉄株式会社 Article façonné par estampage à chaud et procédé de fabrication associé

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE602004021802D1 (de) * 2003-04-23 2009-08-13 Sumitomo Metal Ind Heisspressgeformtes produkt und herstellungsverfahren dafür

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2024132139A1 (fr) * 2022-12-21 2024-06-27 Voestalpine Metal Forming Gmbh Procédé de production de pièces en acier trempé
WO2024166854A1 (fr) * 2023-02-07 2024-08-15 日本製鉄株式会社 Article façonné par estampage à chaud et procédé de fabrication associé

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Publication number Publication date
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