WO2020049833A1 - Plaque d'acier pour compression à chaud - Google Patents

Plaque d'acier pour compression à chaud Download PDF

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Publication number
WO2020049833A1
WO2020049833A1 PCT/JP2019/024473 JP2019024473W WO2020049833A1 WO 2020049833 A1 WO2020049833 A1 WO 2020049833A1 JP 2019024473 W JP2019024473 W JP 2019024473W WO 2020049833 A1 WO2020049833 A1 WO 2020049833A1
Authority
WO
WIPO (PCT)
Prior art keywords
steel sheet
plating layer
alloy plating
hot pressing
oxide
Prior art date
Application number
PCT/JP2019/024473
Other languages
English (en)
Japanese (ja)
Inventor
田中　稔
克利 ▲高▼島
安藤　聡
長滝　康伸
Original Assignee
Ｊｆｅスチール株式会社
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 Ｊｆｅスチール株式会社 filed Critical Ｊｆｅスチール株式会社
Priority to JP2019548339A priority Critical patent/JPWO2020049833A1/ja
Publication of WO2020049833A1 publication Critical patent/WO2020049833A1/fr

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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
    • C23C2/26—After-treatment
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/20—Deep-drawing
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C18/00—Alloys based on zinc
    • 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
    • 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
    • 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
    • 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
    • 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
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D5/00—Electroplating characterised by the process; Pretreatment or after-treatment of workpieces
    • C25D5/48—After-treatment of electroplated surfaces
    • 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

Definitions

  • the present invention relates to a steel sheet for hot pressing mainly used for a steel sheet for automobiles.
  • Patent Document 1 discloses a method for producing a hot pressed member free of liquid metal embrittlement cracking by setting the melting point of the plating layer of the steel sheet surface to 800 ° C. or higher.
  • Patent Document 2 discloses a steel sheet for hot pressing in which an oxide film mainly composed of ZnO is provided on the surface of a plating layer to prevent zinc evaporation during hot press heating.
  • a hot press member free from microcracks can be obtained by rapidly and intermediately cooling a steel sheet to 450 to 700 ° C. using an air jet or the like before hot pressing and then performing die cooling by pressing.
  • a method of making is disclosed.
  • a ZnO-based oxide film having irregularities is formed on the surface of the Zn plating layer.
  • the formation of ZnO on the surface of the plating layer means that the metal Zn, which should originally ensure the corrosion resistance of the steel sheet, decreases due to the sacrificial corrosion protection. Therefore, in order to ensure sacrificial corrosion protection equivalent to that of a non-heated material (a material that is not hot pressed), it is necessary to increase the thickness of the plating by taking into account the amount of metal Zn lost by oxidation during the heating process of the hot press. This leads to an increase in cost. Further, in a general continuous plating production line, there is a problem that the productivity is reduced because the line speed is limited due to thickening of plating.
  • the present invention has been made in view of such circumstances, and has an object to reduce the amount of metal Zn lost by oxidation during a heating process of a hot press, and to provide a steel sheet for hot press excellent in corrosion resistance. I do.
  • the present inventors formed various oxide layers on the surface of the Zn alloy plating layer by a wet process or a dry process, and investigated the corrosion resistance of the resulting hot pressed member after hot pressing.
  • an oxide layer that is more stable than ZnO that is, an oxide layer whose standard reaction Gibbs energy of the oxide at 900 ° C. is lower than ZnO
  • the amount of oxygen from the atmosphere supplied to the plating layer is reduced. It has been found that it functions as a so-called barrier layer, suppresses a decrease in the amount of metallic Zn due to Zn oxidation in the plating layer, and obtains excellent corrosion resistance.
  • the oxide layer is a metal oxide selected from one or more of Si, Mn, and Zr.
  • the Zn alloy plating layer includes a Zn—Al alloy plating layer, a Zn—Al—Mg alloy plating layer, a Zn—Al—Mg—Si alloy plating layer, a Zn—Fe alloy plating layer, and a Zn—Ni alloy plating layer.
  • the amount of metallic Zn lost by oxidation during the heating process of the hot press is reduced, and a steel sheet for hot press excellent in corrosion resistance can be obtained.
  • the unit of the content of each element of the steel component composition and the unit of the content of each element of the plating layer component composition are “% by mass”, and hereinafter, unless otherwise specified, simply “%”. Show.
  • the plating adhesion amount per one side is set to 120 g / m 2 or less.
  • it is 90 g / m ⁇ 2 > or less.
  • it is less than 10 g / m 2 , the effect of suppressing Fe scale formation at the time of hot press heating becomes insufficient, so that it is preferably 10 g / m 2 or more.
  • hot press members for automobiles are mainly applied to parts requiring corrosion resistance, such as underbody parts and skeletal members. Therefore, the plating layer needs to be a Zn alloy plating layer having a sacrificial anticorrosion action.
  • the composition is not particularly limited as long as the main component of the plating layer is Zn.
  • Layer a Zn—Fe alloy plating layer, or a Zn—Ni alloy plating layer.
  • the Zn alloy plating layer contains 10 to 25% by mass of Ni, and the remainder is a Zn—Ni alloy plating layer composed of Zn and unavoidable impurities.
  • the amount of Ni in the Zn alloy plating layer is controlled to 10 to 25% by mass, a ⁇ phase having a crystal structure of one of Ni 2 Zn 11 , NiZn 3 , and Ni 5 Zn 21 having a high melting point is formed. This is advantageous from the viewpoint of liquid metal embrittlement resistance as compared with other Zn alloy plating layers.
  • the surface of the Zn alloy plating layer has an oxide layer whose standard reaction Gibbs energy of oxide at 900 ° C. is lower than ZnO .
  • an oxide film mainly composed of ZnO is formed on the surface of the Zn plating layer.
  • a steel sheet is heated from room temperature to around 900 ° C. which is an austenite single phase region.
  • an oxide layer that is more stable than ZnO on the surface of the Zn alloy plating layer that is, an oxide layer whose standard reaction Gibbs energy of the oxide at 900 ° C. is lower than that of ZnO
  • It functions as a so-called barrier layer that suppresses the amount of oxygen from the atmosphere, and can suppress a decrease in the amount of metallic Zn due to Zn oxidation in the plating layer.
  • a reduction in the amount of metallic Zn due to Zn oxidation is suppressed, and a further sacrificial anticorrosion action is ensured.
  • oxygen in the oxide layer is supplied to Zn to be reduced and becomes a metal layer, so that a sufficient oxygen barrier effect cannot be obtained.
  • the standard reaction Gibbs energy can be calculated using the Ellingham diagram.
  • the oxide layer is preferably a metal oxide selected from one or more of Si, Mn, and Zr.
  • Each of the metal oxides listed here is an oxide layer whose free energy at 900 ° C. is lower than that of ZnO, and is more stable than ZnO in an air atmosphere at room temperature to 900 ° C.
  • the lower limit of the deposition of the oxide layer it is recognized corrosion resistance as compared with the case where there is no oxide layer in trace amounts, in the present invention, 0.1 g / m 2 or more.
  • an oxide layer having an excessive thickness causes an increase in cost, and therefore is preferably 30 g / m 2 or less. More preferably, it is 10 g / m 2 or less, still more preferably 5 g / m 2 or less.
  • the method for forming the oxide layer is not particularly limited.
  • the oxide layer can be formed using a dry process such as PVD (Physical Vapor Deposition), CVD (Chemical Vapor Deposition), or cold spray.
  • a hot-pressed member exceeding 1470 MPa class for example, as a base steel sheet of the plating layer, C: 0.20 to 0.35%, Si: 0.1 Containing 0.5 to 0.5%, Mn: 1.0 to 3.0%, P: 0.02% or less, and S: 0.01% or less, with the balance being Fe and unavoidable impurities.
  • a rolled steel plate or a hot rolled steel plate can be used. The reasons for limiting each component are described below.
  • C 0.20 to 0.35% C improves strength by forming martensite or the like as a steel structure. To obtain a strength exceeding the 1470 MPa class, 0.20% or more is required. On the other hand, if it exceeds 0.35%, the toughness of the spot-welded portion deteriorates. Therefore, the C content is preferably set to 0.20 to 0.35%.
  • Si 0.1-0.5% Si is an element effective for strengthening steel and obtaining a good material. For that purpose, 0.1% or more is required. On the other hand, when the content exceeds 0.5%, the ferrite is stabilized, so that the hardenability decreases. Therefore, the amount of Si is preferably set to 0.1 to 0.5%.
  • Mn 1.0 to 3.0%
  • Mn is an element effective for increasing the strength of steel. In order to ensure mechanical properties and strength, it is necessary to contain 1.0% or more. On the other hand, if it exceeds 3.0%, the surface concentration at the time of annealing increases, and it becomes difficult to secure plating adhesion. Therefore, the Mn content is preferably set to 1.0 to 3.0%.
  • the P content is preferably set to 0.02% or less.
  • S 0.01% or less S becomes an inclusion such as MnS, and causes deterioration of impact resistance and cracks along a metal flow of a welded portion. Therefore, it is desirable to reduce as much as possible, and it is preferable to make it 0.01% or less. In order to secure good stretch flangeability, the content is more preferably 0.005% or less.
  • Nb 0.05% or less
  • Ti 0.05% or less
  • B 0.0002 to 0.0050%
  • Cr 0.1 to 0.3%
  • Sb 0.003 to 0.030%
  • Nb 0.05% or less Nb is a component effective for strengthening steel. However, if it is contained excessively, shape freezing property decreases. Therefore, when Nb is contained, the content is set to 0.05% or less.
  • Ti 0.05% or less Ti is also effective in strengthening steel like Nb, but there is a problem that excessive inclusion of Ti lowers the shape freezing property. Therefore, when Ti is contained, the content is made 0.05% or less.
  • B 0.0002 to 0.0050% Since B has an effect of suppressing the formation and growth of ferrite from austenite grain boundaries, the addition of B is preferably 0.0002% or more. On the other hand, excessive addition of B greatly impairs moldability. Therefore, when B is contained, the content is made 0.0002 to 0.0050%.
  • Cr 0.1-0.3% Cr is useful for strengthening steel and improving hardenability. In order to exhibit such effects, addition of 0.1% or more is preferable. On the other hand, since the alloy cost is high, adding over 0.3% leads to a significant cost increase. Therefore, when Cr is contained, the content is set to 0.1 to 0.3%.
  • Sb 0.003 to 0.030% Sb also has the effect of suppressing the decarburization of the steel sheet surface layer during the hot pressing process. In order to exhibit such an effect, it is necessary to add 0.003% or more. On the other hand, when the amount of Sb exceeds 0.030%, the rolling load is increased, so that the productivity is reduced. Therefore, when Sb is contained, the content is made 0.003 to 0.030%.
  • the hot pressing step for producing a hot pressed member using the steel sheet for hot pressing of the present invention is not limited at all, and a known hot pressing step can be applied.
  • the steel sheet for hot pressing of the present invention is heated to a temperature range of from the Ac3 transformation point to 950 ° C., then hot pressed, and subsequently cooled using a mold or a coolant such as water.
  • a hot pressed member is manufactured.
  • the said heating temperature means the highest attainment temperature of a steel plate. Examples of the method for performing the heating include heating using an electric furnace or a gas furnace, flame heating, electric heating, high-frequency heating, induction heating, and the like.
  • the composition of the hot-dip plating bath was adjusted so that a desired composition was obtained, and the bath temperature was set to the melting point of each composition + 20 ° C. Further, the amount of adhesion was controlled by adjusting the wiping pressure.
  • the conditions of the electroplating treatment were such that the metal salt ratio in the bath and the current value were adjusted so as to obtain a desired composition, and the amount of deposition was controlled by changing the line speed.
  • the deposition conditions for PVD of the oxide layer were such that a desired metal or oxide target was used, and a desired amount of deposition was controlled by controlling the voltage, the oxygen partial pressure, and the processing time.
  • a test piece of 150 mmC ⁇ 300 mmL was sampled from the obtained steel sheet for hot pressing, heated to 900 ° C. for 4 minutes by an electric furnace, held at 900 ° C. for 1 minute, and then taken out of the electric furnace to remove a hat mold. Hot pressing was performed at 700 ° C. by a mold.
  • the shape of the part after molding is such that the length of the flat portion on the upper surface is 100 mm, the length of the flat portion on the side surface is 50 mm, and the length of the flat portion on the lower surface is 50 mm.
  • the bending R of the mold is 7R for both shoulders on the upper surface and both shoulders on the lower surface.
  • the hat-formed part obtained as described above was subjected to a corrosion test (SAE-J2334), and the corrosion resistance at the center of the flat side surface (area of 100 mmC ⁇ 30 mmL) after 60 cycles was evaluated and evaluated according to the following criteria. :: Average corrosion depth decreased by 100 ⁇ m or more compared to the case without the oxide layer. ⁇ : Average corrosion depth decreased from 0 ⁇ m to less than 100 ⁇ m compared to the case without the oxide layer. X: Average corrosion depth. However, if the evaluation was ⁇ , which is an increase compared with the case without the oxide layer, it was determined that the steel sheet for hot pressing had excellent corrosion resistance.
  • Table 1 shows the evaluation results.
  • the steel sheet for hot pressing of the present invention has excellent corrosion resistance.
  • the hot-pressed steel sheet having the Zn—Ni alloy plating layer evaluated in Example 1 was evaluated for LME resistance (LME: Liquid Metal Embrittlement, liquid metal embrittlement). Specifically, a sample for cross-sectional SEM observation is taken from the upper shoulder R of the hat-formed part obtained in Example 1, and penetrates into the base material in a visual field having a cross-sectional length of 5 mm outside the shoulder R by observation. The crack depth was measured at a total of 20 points at a pitch of 250 ⁇ m, and the LME resistance was evaluated based on the following criteria. :: No crack generation or average crack depth of less than 10 ⁇ m ⁇ : Average crack depth of 10 ⁇ m or more and less than 200 ⁇ m ⁇ : Average crack depth of 200 ⁇ m or more Excellent.
  • Table 2 shows the evaluation results of the LME resistance characteristics.
  • the Zn—Ni alloy plating layer may be a Zn—Ni alloy plating layer containing 10 to 25% by mass of Ni and the balance being Fe and unavoidable impurities. From this, it can be seen that, in addition to corrosion resistance, excellent LME resistance is provided.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Electrochemistry (AREA)
  • Other Surface Treatments For Metallic Materials (AREA)
  • Electroplating Methods And Accessories (AREA)
  • Coating With Molten Metal (AREA)
  • Heat Treatment Of Articles (AREA)
  • Shaping Metal By Deep-Drawing, Or The Like (AREA)

Abstract

L'invention a pour objet de fournir une plaque d'acier pour compression à chaud dont la masse de métal Zn perdue par oxydation lors du processus de chauffage d'une compression à chaud est réduite, et qui présente une excellente résistance à la corrosion. La plaque d'acier pour compression à chaud de l'invention possède à sa surface une couche de placage en alliage Zn telle que la masse de revêtement de placage pour une face est inférieure ou égale à １２０ｇ／ｍ２, et, à la surface de ladite couche de placage en alliage Zn, une couche d'oxyde présentant une énergie de Gibbs de réaction standard d'un oxyde à 900°C inférieure à celle d'un ZnO.
PCT/JP2019/024473 2018-09-07 2019-06-20 Plaque d'acier pour compression à chaud WO2020049833A1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
JP2019548339A JPWO2020049833A1 (ja) 2018-09-07 2019-06-20 熱間プレス用鋼板

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2018-167596 2018-09-07
JP2018167596 2018-09-07

Publications (1)

Publication Number Publication Date
WO2020049833A1 true WO2020049833A1 (fr) 2020-03-12

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Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2019/024473 WO2020049833A1 (fr) 2018-09-07 2019-06-20 Plaque d'acier pour compression à chaud

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JP (1) JPWO2020049833A1 (fr)
WO (1) WO2020049833A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPWO2022091480A1 (fr) * 2020-10-28 2022-05-05

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2004270029A (ja) * 2003-02-18 2004-09-30 Nippon Steel Corp 耐亜鉛揮発性に優れた亜鉛系めっき鋼板
JP2010090463A (ja) * 2008-10-10 2010-04-22 Jfe Steel Corp 熱間プレス成形用めっき鋼板およびその製造方法
JP2011032525A (ja) * 2009-07-31 2011-02-17 Jfe Steel Corp 表面処理鋼板およびその製造方法
US20120118437A1 (en) * 2010-11-17 2012-05-17 Jian Wang Zinc coated steel with inorganic overlay for hot forming
WO2012070482A1 (fr) * 2010-11-25 2012-05-31 Ｊｆｅスチール株式会社 Feuille d'acier pour pressage à chaud et procédé de fabrication d'un élément pressé à chaud à l'aide de la feuille d'acier pour pressage à chaud
WO2016159298A1 (fr) * 2015-03-31 2016-10-06 新日鐵住金株式会社 Tôle d'acier galvanisée à chaud au trempé

Family Cites Families (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2011101158A1 (fr) * 2010-02-19 2011-08-25 Tata Steel Nederland Technology Bv Bande, feuille ou ébauche adaptée au thermoformage et procédé de production associé
DE102014004649A1 (de) * 2014-03-29 2015-10-01 Daimler Ag Bauteil, insbesondere Strukturbauteil für einen Kraftwagen sowie Verfahren zum Herstellen eines Bauteils

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2004270029A (ja) * 2003-02-18 2004-09-30 Nippon Steel Corp 耐亜鉛揮発性に優れた亜鉛系めっき鋼板
JP2010090463A (ja) * 2008-10-10 2010-04-22 Jfe Steel Corp 熱間プレス成形用めっき鋼板およびその製造方法
JP2011032525A (ja) * 2009-07-31 2011-02-17 Jfe Steel Corp 表面処理鋼板およびその製造方法
US20120118437A1 (en) * 2010-11-17 2012-05-17 Jian Wang Zinc coated steel with inorganic overlay for hot forming
WO2012070482A1 (fr) * 2010-11-25 2012-05-31 Ｊｆｅスチール株式会社 Feuille d'acier pour pressage à chaud et procédé de fabrication d'un élément pressé à chaud à l'aide de la feuille d'acier pour pressage à chaud
WO2016159298A1 (fr) * 2015-03-31 2016-10-06 新日鐵住金株式会社 Tôle d'acier galvanisée à chaud au trempé

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPWO2022091480A1 (fr) * 2020-10-28 2022-05-05
WO2022091480A1 (fr) * 2020-10-28 2022-05-05 Ｊｆｅスチール株式会社 Élément pressé à chaud et tôle d'acier pour pressage à chaud, et procédé de fabrication pour élément pressé à chaud
JP7173368B2 (ja) 2020-10-28 2022-11-16 Ｊｆｅスチール株式会社 熱間プレス部材および熱間プレス用鋼板ならびに熱間プレス部材の製造方法

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