EP3135394B1 - Method for manufacturing hot press forming part - Google Patents

Method for manufacturing hot press forming part Download PDF

Info

Publication number
EP3135394B1
EP3135394B1 EP15783938.2A EP15783938A EP3135394B1 EP 3135394 B1 EP3135394 B1 EP 3135394B1 EP 15783938 A EP15783938 A EP 15783938A EP 3135394 B1 EP3135394 B1 EP 3135394B1
Authority
EP
European Patent Office
Prior art keywords
press forming
steel sheet
cooling
temperature
coated steel
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.)
Active
Application number
EP15783938.2A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP3135394A1 (en
EP3135394A4 (en
Inventor
Tatsuya Nakagaito
Yuichi Tokita
Toru Minote
Yoshikiyo Tamai
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.)
JFE Steel Corp
Original Assignee
JFE Steel Corp
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 Steel Corp filed Critical JFE Steel Corp
Publication of EP3135394A1 publication Critical patent/EP3135394A1/en
Publication of EP3135394A4 publication Critical patent/EP3135394A4/en
Application granted granted Critical
Publication of EP3135394B1 publication Critical patent/EP3135394B1/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • 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
    • B21D22/02—Stamping using rigid devices or tools
    • B21D22/022—Stamping using rigid devices or tools by heating the blank or stamping associated with heat 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
    • B21D22/208—Deep-drawing by heating the blank or deep-drawing associated with heat 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
    • 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
    • B21D24/00—Special deep-drawing arrangements in, or in connection with, presses
    • B21D24/04—Blank holders; Mounting means therefor
    • 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
    • B21D37/00—Tools as parts of machines covered by this subclass
    • B21D37/16—Heating or cooling
    • 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
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D3/00—Electroplating: Baths therefor
    • C25D3/02—Electroplating: Baths therefor from solutions
    • C25D3/56—Electroplating: Baths therefor from solutions of alloys
    • C25D3/565—Electroplating: Baths therefor from solutions of alloys containing more than 50% by weight of zinc

Definitions

  • This disclosure relates to a method of manufacturing a hot press forming part.
  • the disclosure particularly relates to a method for manufacturing a hot press forming part from a coated steel sheet wherein, while press forming the coated steel sheet heated beforehand into a predetermined shape, the steel sheet is simultaneously quenched to attain a predetermined strength (such that the tensile strength is at least 1180 MPa grade).
  • steel sheets used have higher strength, press formability is deteriorated, and forming the steel sheets into the desired part shape is more difficult.
  • the following technique is known to solve this problem: while hot press forming a blank sheet heated to high temperature into a desired shape using a tool of press forming, the steel sheet is quenched in the die by heat extraction, thus enhancing the hardness of the hot press formed part.
  • GB1490535A proposes a technique in which, when manufacturing a part of a predetermined shape by hot pressing a blank sheet (steel sheet) heated to an austenite single phase region of about 900 °C, the blank sheet is quenched in a tool of press forming simultaneously with the hot press forming, thus enhancing the strength of the part.
  • the technique proposed in PTL 1 has a problem in that, when heating the steel sheet to high temperature of about 900 °C before the pressing, oxide scale (iron oxide) forms on the surface of the steel sheet, and the oxide scale peels during the hot press forming and damages the die or the surface of the hot press formed part. Besides, the oxide scale remaining on the surface of the part causes poor appearance and lower coating adhesion. Accordingly, the oxide scale on the surface of the part is typically removed by a process such as pickling or shot blasting. Such a process, however, causes lower productivity.
  • oxide scale iron oxide
  • JP2001353548A proposes a technique in which a steel sheet coated with Zn or a zinc-based alloy is heated to 700 °C to 1200 °C and then hot press formed to obtain a hot press formed part having a Zn-Fe-based compound or a Zn-Fe-Al-based compound on its surface.
  • PTL 2 describes that the use of the steel sheet coated with Zn or a Zn-based alloy suppresses the oxidation of the surface of the steel sheet during heating before hot press forming, and also enables a hot press formed part having excellent corrosion resistance to be obtained.
  • the generation of oxide scale on the surface of the hot press formed part is suppressed to some extent.
  • Zn in the coating layer may cause liquid metal embrittlement cracking, resulting in cracks of about 100 ⁇ m in depth in the surface layer part of the hot press formed part.
  • Such cracks pose various problems such as a decrease in fatigue characteristics of the hot press formed part.
  • JP201391099A proposes a method in which a coated steel sheet obtained by providing a Zn-Fe-based coating layer on a surface of a steel sheet is heated to a temperature not less than Ac 1 transformation temperature of the steel sheet and not more than 950 °C and then cooled to a temperature not more than the freezing point of the coating layer, before starting the forming.
  • PTL 3 describes that liquid metal embrittlement cracking can be suppressed by starting the forming after the coated steel sheet is cooled to the temperature not more than the freezing point of the coating layer.
  • EP 2 602 359 A1 discloses a steel sheet for hot pressing from which a hot-pressed part excellent in perforation corrosion resistance is obtainable and a method of manufacturing a hot-pressed part using the steel sheet for hot pressing.
  • a steel sheet for hot pressing having, sequentially on a surface of a base steel sheet: a plating layer I containing 60% by mass or more of Ni and the remainder consisting of Zn and inevitable impurities, a coating mass thereof being 0.01 to 5 g/m2; and a plating layer II containing 10 to 25% by mass of Ni and the remainder consisting of Zn and inevitable impurities, a coating mass thereof being 10 to 90 g/m2.
  • the ⁇ -phase in the phase equilibrium diagram of Zn-Ni alloy has a fusing point of 860 °C or higher, which is very high as compared to that a normal Zn or Zn alloy coated layer, making it possible to suppress macro-cracks under normal press conditions.
  • minute cracking which is about 30 ⁇ m or less in depth from the interface between the coating layer and the steel toward the inside of the steel and in which Zn is not detected from its interface may also occur in the surface of the hot press formed part. Such minute cracking is called "micro-cracks".
  • Micro-cracks pass through the interface between the coating layer and the steel and reach the inside of the steel (steel sheet), adversely affecting the characteristics (fatigue characteristics, etc.) of the hot press formed part.
  • Macro-cracks also occur in, for example, a shoulder area of die R on the punch-contacting side which is subjected to only tensile strain while press forming of a hat-shaped section part (also referred to hereinafter as a "hat-shaped part").
  • hat-shaped section part also referred to hereinafter as a "hat-shaped part”
  • micro-cracks do not occur in such area, but on the die-contacting side of side wall portions, which are subjected to compression (due to bending) followed by tensile strain (due to bend restoration). It is thus estimated that macro-cracks and micro-cracks are produced by different mechanism.
  • PTL 3 may suppress the occurrence of macro-cracks in a coated steel sheet having a Zn-Fe-based coating layer formed thereon, but is not necessarily effective for suppressing the occurrence of micro-cracks, because it does not consider potential micro-cracks occurring in a coated steel sheet having a Zn-Ni coating layer formed thereon.
  • PTL 3 teaches that the coated steel sheet is press formed as a whole while being cooled to a temperature at or below the freezing point of the coating layer, without specifying the lowest temperature at which the press forming is started, leading to the problem of lower forming temperature resulting in higher strength of the steel sheet during press forming, and deteriorating the shape fixability (which is a characteristic that maintains the shape at press bottom dead center even after die release, because of little springback and the like).
  • micro-cracks minute cracking caused when hot press forming a Zn-based coated steel sheet.
  • press forming the Zn-based coated steel sheet at high temperature may induce minute cracking in the surface of the coated steel sheet, and such minute cracking also occurs in Zn-Ni coating.
  • the minute cracking has a depth of about 30 ⁇ m from the interface between the coating layer and the steel (steel sheet), and passes through the interface between the coating layer and the steel (steel sheet) and reaches the inside of the steel sheet.
  • micro-cracks are suppressed by performing hot press forming at low temperature. Further, the effect of significantly reducing the amount of coating attached to the tool of press forming, which would be quite large to cause problems with conventional coated steel sheets for hot press forming, was obtained by setting a low temperature for press forming as mentioned above.
  • FIG. 17 shows the forming conditions.
  • Most automotive press-formed parts are of so-called hat-like shape such as shown by "Final shape” in FIG. 17 , and are manufactured by a process such as draw forming ((a) in FIG. 17 ) in which press forming is performed by squeezing a steel sheet between a blank holder and a die to suppress wrinkle formation, or crush forming ((b) in FIG. 17 ) without using a blank holder.
  • draw forming ((a) in FIG. 17 ) in which press forming is performed by squeezing a steel sheet between a blank holder and a die to suppress wrinkle formation, or crush forming ((b) in FIG. 17 ) without using a blank holder.
  • draw forming ((a) in FIG. 17 ) in which press forming is performed by squeezing a steel sheet between a blank holder and a die to suppress wrinkle formation, or crush forming ((b) in FIG. 17 ) without using a blank
  • side wall portions are formed by those portions squeezed between the die and the blank holder prior to press forming.
  • the aforementioned angle change becomes small, because the portion of the steel sheet in contact with the punch shoulder portion at the time of press forming is not cooled during the cooling process in the die and the blank holder, and this portion is processed under high-temperature conditions. It is also believed that the side wall portions are reduced in shape accuracy since the temperature of the steel sheet during processing is decreased by cooling in the die and the blank holder. However, almost no deterioration of shape accuracy was observed over a holding time (within three seconds) when the temperature of the steel sheet is 400 °C or higher.
  • the reason may be that at a steel plate temperature of 400 °C or higher (over a holding time of 3 seconds or less), the metallographic structure during the press forming was still austenite, and the stress that had been introduced during the press forming was eased by martensitic transformation after the forming process, causing no deterioration of shape accuracy.
  • the holding time exceeds 3 seconds, the metallographic structure will have already been transformed to martensite at the time of press forming, and wall camber will be caused by the stress introduced during the press forming.
  • micro-cracks do not occur, and it is possible to manufacture a hot press forming part with sufficient strength and hardness as well as satisfactory shape fixability, without causing a significant increase in load of press forming.
  • the method for manufacturing a hot press forming part manufactures a hot press forming part by hot pressing, using a tool of press forming, a coated steel sheet that is obtained by forming a Zn-Ni coating layer on a surface of a steel sheet, the tool of press forming having a die, a blank holder, and a punch, the method comprising, as illustrated in FIG.
  • a coated steel sheet obtained by providing a Zn-Ni coating layer on a surface of the steel sheet is used as the blank material of a hot press formed part.
  • the provision of the Zn-Ni coating layer on the surface of the steel sheet ensures the corrosion resistance of the hot press formed part.
  • the method of forming the Zn-Ni coating layer on the surface of the steel sheet is not particularly limited, and may be any of the methods such as hot-dip galvanizing and electro-galvanizing.
  • the coating weight per side is preferably 10 g/m 2 or more and 90 g/m 2 or less.
  • the Ni content in the coating layer is preferably 9 mass% or more and 25 mass% or less.
  • a ⁇ phase having any of the crystal structures of Ni 2 Zn 11 , NiZn 3 , and Ni 5 Zn 21 is formed when the Ni content in the coating layer is 9 mass% or more and 25 mass% or less.
  • the ⁇ phase has a high fusing point, and thus is advantageous in preventing the coating layer from evaporating when heating the coated steel sheet before hot press forming.
  • the ⁇ phase is also advantageous in suppressing liquid metal embrittlement cracking during high-temperature hot press forming.
  • the coated steel sheet 1 is heated to a temperature range of Ac 3 transformation temperature to 1000 °C. If the heating temperature of the coated steel sheet 1 is below Ac 3 transformation temperature, a sufficient amount of austenite cannot be obtained during heating, leading to the presence of ferrite during press forming. As a result, sufficient strength and good shape fixability are difficult to achieve through hot press forming.
  • the heating temperature of the coated steel sheet 1 exceeds 1000 °C, on the other hand, the coating layer evaporates or excessive oxide generation occurs in the surface layer part, as a result of which the resistance to oxidation declines or the corrosion resistance of the hot press formed part declines. Therefore, the heating temperature is from Ac 3 transformation temperature to 1000 °C.
  • the heating temperature is from Ac 3 transformation temperature + 30 °C to 950 °C.
  • the method of heating the coated steel sheet 1 is not particularly limited, and may be any of the methods such as heating in an electric furnace, an induction heating furnace, and a direct current furnace.
  • the thickness of the steel sheet is preferably 0.8 mm to 4.0 mm from the perspective of guaranteeing the rigidity of the press formed part and ensuring the cooling rate during cooling in the tool of press forming. More preferably, the thickness is 1.0 mm 3.0 mm.
  • edges of the coated steel sheet thus heated are cooled, with the edges being squeezed between the die and the blank holder, to a temperature of 550 °C or lower and 400 °C or higher at a cooling rate of 100 °C/s or higher.
  • press forming is performed so that the press forming is started when the edges of the coated steel sheet reach a temperature of 550 °C or lower and 400 °C or higher.
  • the temperature at start of cooling, with the edges of the heated coated steel sheet 1 squeezed between the die and the blank holder is preferably 800 °C or lower from the perspective of preventing the risk of the Zn-Ni coating layer being adhered to the tool of press forming, and preferably 670 °C or higher from the perspective of guaranteeing the strength after hot press forming.
  • edges refer to those portions of the coated steel sheet that form, after subjection to the press forming, flange portions with at least the lower portions (on the flange side) of the side wall portions of a formed body.
  • a hat-shaped section part as illustrated in FIG. 14 such edges correspond to those portions that form, on the opposite sides of the coated steel sheet, flange portions with at least lower portions (on the flange side) of the side wall portions of a formed body; or when a cup-shaped part is formed, such edges correspond to those portions that form, on the entire circumference of the coated steel sheet, flange portions with at least lower portions (on the flange side) of the side wall portions of a formed body.
  • cooling in the tool of press forming using the die and the blank holder is adopted because, for example, when a hat-shaped section part is formed, the edges of the steel sheet that are squeezed between the die and the blank holder will be rapidly cooled, while other portions of the steel sheet that are in contact with the shoulder areas of the punch during the press forming will hardly be cooled, and thus can be press formed while being kept at high temperature.
  • the cooling rate for cooling in the tool of press forming is set to 100 °C/s or higher because, when a forming part is press formed into a hat-shaped part, for example, this cooling rate enables the side wall portions (portions squeezed by the tool of press forming) of the press formed body to have a martensite single phase structure, and thus allows for strengthening, without increasing cost, of the side wall portions.
  • FIG. 2 is a schematic diagram illustrating the relationship between metallographic structure, temperature, and cooling time. Graph (a) of FIG.
  • the present disclosure adopts the cooling step that enables rapid cooling of only edges of the coated steel sheet, with the edges squeezed between the die and the blank holder before the start of press forming, so that the side wall portions of the press formed body may have a martensite single phase structure, as shown by a curve indicated by a broken line in FIG. 3 .
  • the upper limit of the cooling rate for cooling in the tool of press forming is about 500 °C/s.
  • the edges are cooled to 550 °C or lower because, above 550 °C, cooling becomes insufficient, causing micro-cracks after subjection to the hot press forming.
  • the lower limit of the cooling temperature is 400 °C because, if the edges are cooled below 400 °C, the coated steel sheet 1 will be excessively cooled before subjection to the press forming, leading to deterioration in shape fixability.
  • cooling in the tool of press forming was controlled by the time for which the blank material was held by the die 3 and the blank holder 5 before the start of press forming.
  • the die is slidably moved at a constant high speed (12 spm [Shots Per Minute]).
  • a constant high speed (12 spm [Shots Per Minute]
  • coated steel sheet 1 was squeezed between die 3 and blank holder 5 and, as-is, slidably moved at a low speed (lower than 0.24 spm to 12 spm) before coming into contact with the punch, while in the subsequent press forming step after the coated steel sheet 1 coming into contact with the punch, the die was slidably moved at a high speed (12 spm) as is the case with the conventional press forming.
  • Cooling time was controlled by controlling the slidable movement speed. In the cooling step, when the slidable movement speed is from 0.24 spm to below 12 spm, the cooling time is from 0.16 s to less than 5.8 s.
  • FIG. 7 is a graph showing the results, where the vertical axis is temperature (°C) and the horizontal axis is time (s).
  • FIG. 8 is a graph representing a partial enlarged view of FIG. 7 , with emphasis on the horizontal axis, and focusing on an area enclosed by a broken line in FIG. 7 .
  • the change in temperature of the edge of the steel sheet caused by cooling in the tool of press forming is, as illustrated in FIG.
  • FIG. 9 shows SEM images of cross sections of steel sheet surface layers of side wall portions on the die side. It can be seen that no micro-cracks are observed where the cooling time in the tool of press forming is 0.60 s or more (where the press forming start temperature is 550 °C or lower). Under all conditions, Hv ⁇ 380, proving that quench hardenability does not deteriorate.
  • FIG. 10 is a graph illustrating the results of load of press forming, where the vertical axis is press load (kN) and the horizontal axis is press forming start temperature (°C).
  • the press forming start temperature refers to the temperature of the edges of the steel sheet that are squeezed between the die and the blank holder.
  • press load increases with decreasing press forming start temperature due to cooling in the tool of press forming prior to press forming.
  • load of press forming was as low as that of mild steel (270 D, cold draw forming), which poses no problem.
  • FIG. 11 is a graph illustrating the results of shape fixability, where the vertical axis is the amount of mouth opening deformation (mm) of the press forming part, and the horizontal axis is press forming start temperature (°C).
  • the amount of mouth opening deformation increases due to a decrease in the forming start temperature caused by the process of cooling in the tool of press forming prior to the press forming process, which shows a tendency such that shape fixability deteriorates accordingly.
  • the press forming start temperature is 400 °C or higher, almost no deterioration of shape fixability is observed.
  • the cooling step by cooling the edges of the heated coated steel sheet, with the edges squeezed between the die and the blank holder, to a temperature of 550 °C or lower to 400 °C or higher at a cooling rate of 100 °C/s or higher before the start of press forming, it becomes possible for the press forming part to have a sufficient strength, and it becomes possible to prevent the occurrence of micro-cracks, prevent an increase in the load of press forming, and achieve satisfactory shape fixability.
  • FIG. 12 illustrates an exemplary cooling method with blank holder 5.
  • the holding position of the blank holder 5 is set above the upper surface of the punch 7, the coated steel sheet 1 is squeezed between the die 3 and the blank holder 5, and then cooling is performed during the slidable movement of the die 3 until the coated steel sheet is brought into contact with the punch 7. At this time, the cooling time of the coated steel sheet 1 can be controlled by the slidable movement speed.
  • the slidable movement speed After starting press forming, it is preferable for the slidable movement speed to be fast in order to prevent reduction in productivity and press formability associated with the temperature drop of the coated steel sheet 1, and it is desirable to change the slidable movement speed before press forming and during press forming depending on needs.
  • the press forming start temperature at which the press forming is started is normally controlled by the cooling time.
  • the relation between the time of cooling in the tool of press forming and the decrease in blank temperature is measured beforehand, and based on this relation, the press forming start temperature is controlled. It is also possible to dispose temperature measuring elements such as a thermocouple on the surface of the tool of press forming to directly measure the temperature of the coated steel sheet 1 and control the press forming start temperature. Further, in order to suppress the rise in temperature of the tool of press forming during continuous press forming and reduce the variation in the cooling rate, it is also possible to perform cooling of the tool of press forming by disposing water cooling piping in the die 3 or the blank holder 5, or to use material with high thermal conductivity for the surface of the die 3 or the blank holder 5.
  • FIG. 12(b) it is also possible to squeeze the coated steel sheet 1 between the die 3 and the blank holder 5, and then stop the slidable movement for a certain period of time to cool the coated steel sheet 1, and then perform press forming.
  • pressing may be performed by setting the holding position of the blank holder 5 above the upper surface of the punch 7, squeezing the coated steel sheet 1 between the die 3 and the blank holder 5 and stopping for a certain period of time, and then performing slidable movement.
  • the stop time and the slidable movement time until the coated steel sheet 1 and the punch 7 are brought into contact added together is the cooling time of the coated steel sheet 1 before press forming.
  • FIG. 12(d) is an example of utilizing a pad 10.
  • the pad 10 can also be utilized in a similar way for the examples of FIG. 12(b) and FIG. 12(c) .
  • the press forming machine to be used is not particularly limited, when the slidable movement speed is changed in FIG. 12(a) , or when control is performed in which the slidable movement is temporarily stopped as in FIG. 12(B) and FIG. 12(c) , a servo-press machine needs to be used.
  • the press forming method is not particularly limited either. Possible methods include draw forming where forming is performed with the coated steel sheet 1 squeezed between the die 3 and the blank holder 5 as shown in FIG. 13(a) , or crush forming where the coated steel sheet 1 is squeezed between the die 3 and the blank holder 5 to be cooled and then forming is performed with the blank holder 5 once detached from the coated steel sheet 1 as shown in FIG. 13(b) . From the perspective of suppressing micro-cracks, crush forming in which the degree of processing the sidewall portion is small is preferable.
  • a formed body 1' after the press forming is quenched with the formed body 1' held at the press bottom dead center while being squeezed by the tool of press forming.
  • the slidable movement is stopped at the press bottom dead center after press forming.
  • the stop time i.e. the holding time at the press bottom dead center differs depending on the amount of heat extraction by the tool of press forming, it is preferably 3 seconds or more.
  • the upper limit is not particularly limited, it is preferably 20 seconds or less from the perspective of productivity.
  • % indicating the content of each component is “mass%", unless otherwise stated.
  • the C content is an element that improves the strength of steel.
  • the C content is preferably 0.15 % or more.
  • the C content exceeds 0.50 %, on the other hand, the weldability of the hot press formed part and the blanking workability of the raw material (steel sheet) decrease significantly. Accordingly, the C content is preferably 0.15 % or more and 0.50 % or less, and more preferably 0.20 % or more and 0.40 % or less.
  • Si 0.05 % or more and 2.00 % or less
  • the Si is an element that improves the strength of steel, as with C.
  • the Si content is preferably 0.05 % or more.
  • the Si content is preferably 0.05 % or more and 2.00 % or less, and more preferably 0.10 % or more and 1.50 % or less.
  • Mn 0.50 % or more and 3.00 % or less
  • Mn is an element that enhances the quench hardenability of steel, and is effective in suppressing the ferrite transformation of the steel sheet and improving quench hardenability in the cooling process after the hot press forming. Mn also has a function of decreasing the Ac 3 transformation temperature, and so is an element effective in lowering the heating temperature of the coated steel sheet 1 before the hot pressing. To achieve these effects, the Mn content is preferably 0.50 % or more. When the Mn content exceeds 3.00 %, on the other hand, Mn segregates and the uniformity of the characteristics of the steel sheet and hot press formed part declines. Accordingly, the Mn content is preferably 0.50 % or more and 3.00 % or less, and more preferably 0.75 % or more and 2.50 % or less.
  • the P content is preferably 0.10 % or less, and more preferably 0.01 % or less. Excessively reducing P, however, leads to longer refining time and higher cost, and accordingly, P content is preferably 0.003 % or more.
  • S is an element that forms a coarse sulfide by combining with Mn and causes a decrease in ductility of steel.
  • the S content is preferably reduced as much as possible, though up to 0.050 % is allowable. Accordingly, the S content is preferably 0.050 % or less, and more preferably 0.010 % or less. Excessively reducing S, however, leads to longer refining time and higher cost, and accordingly, S content is preferably 0.001 % or more.
  • the Al content exceeds 0.10 %, oxide inclusions in steel increase, and the ductility of steel declines. Accordingly, the Al content is preferably 0.10 % or less, and more preferably 0.07 % or less. Meanwhile, Al functions as a deoxidizer, and so the Al content is preferably 0.01 % or more to improve the cleanliness of steel.
  • the N content exceeds 0.010 %, nitrides such as AlN form in the steel sheet, which causes lower formability during hot pressing. Accordingly, the N content is preferably 0.010 % or less, and more preferably 0.005 % or less. Excessively reducing N, however, leads to longer refining time and higher cost, and accordingly, N content is preferably 0.001 % or more.
  • the steel sheet may further include the following elements when necessary. At least one type selected from the group consisting of Cr: 0.01 % or more and 0.50 % or less, V: 0.01 % or more and 0.50 % or less, Mo: 0.01 % or more and 0.50 % or less, and Ni: 0.01 % or more and 0.50 % or less Cr, V, Mo, and Ni are each an element effective in enhancing the quench hardenability of steel. This effect is achieved when the content is 0.01 % or more for each of the elements. When the content exceeds 0.50 % for each of Cr, V, Mo, and Ni, however, the effect saturates and the cost increases. Accordingly, in the case where at least one type of Cr, V, Mo, and Ni is included, the content is preferably 0.01 % or more and 0.50 % or less, and more preferably 0.10 % or more and 0.40 % or less.
  • Ti is effective for strengthening steel.
  • the strengthening effect of Ti is achieved when the content is 0.01 % or more. Ti within the specified range can be used to strengthen steel without any problem. When the Ti content exceeds 0.20 %, however, the effect saturates and the cost increases. Accordingly, in the case where Ti is included, the content is preferably 0.01 % or more and 0.20 % or less, and more preferably 0.01 % or more and 0.05 % or less.
  • Nb 0.01 % or more and 0.10 % or less
  • Nb is also effective for strengthening steel.
  • the strengthening effect of Nb is achieved when the content is 0.01 % or more. Nb within the specified range can be used to strengthen steel without any problem. When the Nb content exceeds 0.10 %, however, the effect saturates and the cost increases. Accordingly, in the case where Nb is included, the content is preferably 0.01 % or more and 0.10 % or less, and more preferably 0.01 % or more and 0.05 % or less.
  • B is an element that enhances the quench hardenability of steel, and is effective in suppressing the generation of ferrite from austenite grain boundaries and obtaining a quenched structure when cooling the steel sheet after the hot press forming. This effect is achieved when the B content is 0.0002 % or more. When the B content exceeds 0.0050 %, however, the effect saturates and the cost increases. Accordingly, in the case where B is included, the content is preferably 0.0002 % or more and 0.0050 % or less, and more preferably 0.0005 % or more and 0.0030 % or less.
  • the Sb has an effect of suppressing a decarburized layer generated in the surface layer part of the steel sheet from when a steel sheet is heated before the hot press forming to when the steel sheet is cooled by the process of hot press forming.
  • the Sb content is preferably 0.003 % or more.
  • the content is preferably 0.003 % or more and 0.030 % or less, and more preferably 0.005 % or more and 0.010 % or less.
  • the components (balance) other than the above components are Fe and inevitable impurities.
  • the manufacturing condition of the coated steel sheet 1 used as the raw material of the hot press formed part is not particularly limited.
  • the manufacturing condition of the steel sheet is not particularly limited.
  • a hot rolled steel sheet (pickled steel sheet) having a predetermined chemical composition or a cold rolled steel sheet obtained by subjecting the hot rolled sheet to cold rolling may be used as the steel sheet.
  • the condition when forming the Zn-Ni coating layer on the surface of the steel sheet to obtain the coated steel sheet 1 is not particularly limited.
  • the coated steel sheet 1 may be obtained by subjecting the hot rolled steel sheet (pickled steel sheet) to Zn-Ni coating treatment.
  • the coated steel sheet 1 may be obtained by subjecting the cold rolled steel sheet to Zn-Ni coating treatment after cold rolling.
  • the Zn-Ni coating layer may be formed by cleaning and pickling the steel sheet, and then subjecting the steel sheet to electroplating treatment with a current density of 10 A/dm 2 or more and 150 A/dm 2 or less in a plating bath having a pH of 1.0 or more and 3.0 or less and a bath temperature of 30 °C or more and 70 °C or less and containing: 100 g/L or more and 400 g/L or less nickel sulfate hexahydrate; and 10 g/L or more and 400 g/L or less zinc sulfate heptahydrate.
  • the cold rolled steel sheet may be subjected to annealing treatment before the cleaning and pickling.
  • the Ni content in the coating layer may be set to a desired Ni content (for example, 9 mass% or more and 25 mass% or less) by appropriately adjusting the concentration of the zinc sulfate heptahydrate or the current density within the above-mentioned range.
  • the coating weight of the Zn-Ni coating layer may be set to a desired coating weight (for example, 10 g/m 2 or more and 90 g/m 2 or less per side) by adjusting the current passage time.
  • the hot rolled steel sheet was then pickled and cold rolled with a rolling reduction of 50 %, to obtain a cold rolled steel sheet with a thickness of 1.6 mm.
  • the Ac 3 transformation temperature in Table 1 was calculated according to the following Formula (1) (see William C. Leslie, The Physical Metallurgy of Steels, translation supervised by Nariyasu Kouda, translated by Hiroshi Kumai and Tatsuhiko Noda, Maruzen Co., Ltd., 1985, p. 273 ).
  • the cold rolled steel sheet was passed through a continuous galvanizing line, heated to a temperature range of 800 °C or more and 900 °C or less at a heating rate of 10 °C/s, and held in the temperature range for 10 s or more and 120 s or less. After this, the cold rolled steel sheet was cooled to a temperature range of 460 °C or more and 500 °C or less at a cooling rate of 15 °C/s, and immersed into a galvanizing bath of 450 °C to form a Zn coating layer. The coating weight of the Zn coating layer was adjusted to a predetermined coating weight by the gas wiping method.
  • the cold rolled steel sheet was passed through a continuous galvanizing line, heated to a temperature range of 800 °C or more and 900 °C or less at a heating rate of 10 °C/s, and held in the temperature range for 10 s or more and 120 s or less. After this, the cold rolled steel sheet was cooled to a temperature range of 460 °C or more and 500 °C or less at a cooling rate of 15 °C/s, and immersed into a galvanizing bath of 450 °C to form a Zn coating layer. The coating weight of the Zn coating layer was adjusted to a predetermined coating weight by the gas wiping method.
  • the cold rolled steel sheet was heated to 500 °C to 550 °C in an alloying furnace and held for 5 s to 60 s, to form a Zn-Fe coating layer.
  • the Fe content in the coating layer was set to a predetermined content by changing the heating temperature in the alloying furnace or the holding time at the heating temperature within the above-mentioned range.
  • the cold rolled steel sheet was passed through a continuous annealing line, heated to a temperature range of 800 °C or more and 900 °C or less at a heating rate of 10 °C/s, and held in the temperature range for 10 s or more and 120 s or less. After this, the cold rolled steel sheet was cooled to a temperature range of 500 °C or less at a cooling rate of 15 °C/s.
  • the cold rolled steel sheet was then cleaned and pickled, and subjected to electroplating treatment of applying current for 10 s to 100 s with a current density of 30 A/dm 2 to 100 A/dm 2 in a plating bath having a pH of 1.3 and a bath temperature of 50 °C and containing: 200 g/L nickel sulfate hexahydrate; and 10 g/L to 300 g/L zinc sulfate heptahydrate, thus forming a Zn-Ni coating layer.
  • the Ni content in the coating layer was set to a predetermined content by appropriately adjusting the concentration of the zinc sulfate heptahydrate or the current density within the above-mentioned range.
  • the coating weight of the Zn-Ni coating layer was set to a predetermined coating weight by appropriately adjusting the current passage time in the above-mentioned range.
  • a blank sheet of 200 mm ⁇ 400 mm was punched from each coated steel sheet 1 obtained as described above, and heated in an electric furnace having an air atmosphere.
  • the blank sheet was set on a tool of press forming (material: SKD61), and then cooling and press forming was performed using the tool of press forming. After this, the blank sheet was quenched in the tool of press forming and released from the tool of press forming, thus manufacturing a press formed part with a hat-shaped cross section illustrated in FIG. 14 .
  • a tool of press forming with a shoulder area of punch R: 6 mm and a shoulder area of die R: 6 mm was used, and the press forming was performed with a punch-die clearance of 1.6 mm.
  • Cooling in the tool of press forming prior to press forming was performed by squeezing the blank sheet between the die 3 and the blank holder 5.
  • Press forming was performed by draw forming where forming is performed while applying a blank holder force of 98 kN, and crush forming where, after the cooling prior to press forming, the blank holder 5 is removed and forming is performed without the blank holder.
  • the relation between the time of cooling in the tool of press forming and the decrease in blank temperature was measured beforehand, and based on this relation, the press forming start temperature was obtained using time of cooling in the tool of press forming until press forming.
  • a sample was collected from the side wall portion of each obtained press formed part with a hat-shaped cross section, and the section of its surface was observed using a scanning electron microscope (SEM) with 1000 magnification for 10 fields per sample, to examine the presence or absence of micro-cracks (minute cracking in the surface of the sample, which passes through the interface between the coating layer and the steel sheet and reaches the inside of the steel sheet) and the average depth of micro-cracks.
  • the average depth of micro-cracks was calculated by averaging the micro-crack depths of any 20 micro-cracks.
  • the micro-crack depth mentioned here means the length (length h in FIG.
  • the hardness of the cross section of the sample was measured using a micro-Vickers hardness meter. A test was conducted with a test load of 9.8 N at 5 points in the center position in the thickness direction, and the average value thereof was used as the hardness of the samples. Here, the target hardness is 380 Hv or more.
  • a JIS No. 13 B tensile test piece was collected from the side wall portion of each obtained press formed part. A tensile test was conducted using the collected test piece according to JIS G 0567 (1998), to measure the tensile strength at room temperature (22 ⁇ 5 °C). The tensile test was conducted at a crosshead speed of 10 mm/min. These results are also shown in Table 2.
  • the type of coating layer Zn-Ni coating layer
  • cooling method cooling in tool of press forming
  • cooling rate appropriate range: 100 °C/s or more
  • press forming start temperature appropriate range: 400 °C to 550 °C
  • the type of coating layer is a Zn-Ni coating layer.
  • forming was performed without performing cooling in the tool of press forming.
  • the type of coating layer is a Zn-Ni coating layer.
  • the press forming start temperatures for each of comparative examples 2 to 4 were out of the appropriate range.
  • the press forming start temperature for comparative example 2 was 610 °C which is higher than the appropriate range, and the press forming start temperatures for comparative examples 3 and 4 were 350 °C and 230 °C which are lower than the appropriate range.
  • the amount of mouth opening deformation is 0 mm.
  • micro-cracks are generated. From these results, it can be seen that, when the press forming start temperature of the steel sheet is higher than 550 °C, micro-cracks are generated. In comparative examples 3 and 4, micro-cracks are not generated. However, the amount of mouth opening deformation is 8 mm to 10 mm. From these results, it can be seen that when the cooling time is too long and the forming start temperature of the steel sheet becomes lower than 400 °C, the strength of the steel sheet increases, and thus the shape fixability decreases.
  • the type of coating layer is a Zn-Ni coating layer.
  • the cooling method is gas cooling and the cooling rate is not 100 °C/s or more. Therefore, in comparative examples 5 and 6, the press forming start temperatures of the steel sheet are out of the appropriate range (over 550 °C), and micro-cracks are generated. Further, in comparative example 7, the press forming start temperature of the steel sheet was 530 °C which is within the appropriate range. However, the amount of mouth opening deformation was 3 mm, and shape fixability was decreased.
  • comparative examples 8 and 9 the cooling method (cooling in tool of press forming), cooling rate (167 °C/s, 170 °C/s), and press forming start temperature (530 °C to 540 °C) are appropriate.
  • the type of coating layer is different. Specifically, comparative example 8 is a coating layer of only Zn, and comparative example 9 is a coating layer of Zn-Fe, and therefore micro-cracks are generated in the samples after pressing.

Landscapes

  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Chemical & Material Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Materials Engineering (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Electrochemistry (AREA)
  • Shaping Metal By Deep-Drawing, Or The Like (AREA)
  • Heat Treatment Of Articles (AREA)
  • Electroplating Methods And Accessories (AREA)
EP15783938.2A 2014-04-23 2015-02-26 Method for manufacturing hot press forming part Active EP3135394B1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP2014088848 2014-04-23
JP2014179073A JP5825413B1 (ja) 2014-04-23 2014-09-03 熱間プレス成形品の製造方法
PCT/JP2015/056439 WO2015163016A1 (ja) 2014-04-23 2015-02-26 熱間プレス成形品の製造方法および熱間プレス成形品

Publications (3)

Publication Number Publication Date
EP3135394A1 EP3135394A1 (en) 2017-03-01
EP3135394A4 EP3135394A4 (en) 2017-04-26
EP3135394B1 true EP3135394B1 (en) 2018-01-31

Family

ID=54332187

Family Applications (1)

Application Number Title Priority Date Filing Date
EP15783938.2A Active EP3135394B1 (en) 2014-04-23 2015-02-26 Method for manufacturing hot press forming part

Country Status (7)

Country Link
US (1) US20170043386A1 (ja)
EP (1) EP3135394B1 (ja)
JP (1) JP5825413B1 (ja)
KR (1) KR101879307B1 (ja)
CN (1) CN106232254B (ja)
MX (1) MX2016013666A (ja)
WO (1) WO2015163016A1 (ja)

Families Citing this family (21)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2016027293A1 (ja) * 2014-08-22 2016-02-25 日新製鋼株式会社 Ｚｎ系めっき部品の加工方法
JP6152836B2 (ja) * 2014-09-25 2017-06-28 Ｊｆｅスチール株式会社 熱間プレス成形品の製造方法
JP6056826B2 (ja) * 2014-09-30 2017-01-11 Ｊｆｅスチール株式会社 熱間プレス成形品の製造方法
JP5910710B1 (ja) * 2014-12-02 2016-04-27 Ｊｆｅスチール株式会社 熱間プレス成形品の評価方法及び製造方法
GB201521443D0 (en) * 2015-12-04 2016-01-20 Impression Technologies Ltd Method for operating a press for metal sheet forming
TWI623361B (zh) * 2016-10-04 2018-05-11 Nippon Steel & Sumitomo Metal Corp Hot pressing method and hot pressing system
CN107413960A (zh) * 2017-07-31 2017-12-01 南京星乔威泰克汽车零部件有限公司 一种热成型模具的镶块及压料器和热成型模具
CN107460289A (zh) * 2017-08-08 2017-12-12 肥西县通力机械有限公司 一种提高热冲压零件强度的加工方法
WO2019104601A1 (zh) * 2017-11-30 2019-06-06 惠州市惠轩达汽车贸易有限公司 一种碳钢车框冲压成型工艺
CN112236243B (zh) * 2018-07-04 2023-04-04 日本制铁株式会社 热压成型品的制造方法、压制成型品、冲模模具及模具套件
US11633772B2 (en) * 2018-07-04 2023-04-25 Nippon Steel Corporation Hot press-formed item manufacturing method, press-formed item, die, and die set
CN109047429A (zh) * 2018-11-09 2018-12-21 浙江智造热成型科技有限公司 超高强度钢热压成形生产线
CN109570343B (zh) * 2018-11-16 2020-07-28 苏州普热斯勒先进成型技术有限公司 高强钢汽车覆盖件总成及其制造方法和装置
DE102019112547A1 (de) * 2019-05-14 2020-11-19 Felss Systems Gmbh Bearbeitungseinheit und Bearbeitungsmaschine zur Bearbeitung eines Werkstücks an einer Werkstückwand sowie Verfahren zur Herstellung einer Bearbeitungseinheit der genannten Art
CN114555453B (zh) * 2019-11-08 2024-06-14 自动工程有限公司 一种用于车辆框架的成形钣金部件和相应的生产方法
JP7239060B2 (ja) * 2020-03-23 2023-03-14 日本製鉄株式会社 ホットスタンプ成形体
CN115066516A (zh) * 2020-03-23 2022-09-16 日本制铁株式会社 热冲压成型体
US20230166314A1 (en) * 2020-04-20 2023-06-01 Nippon Steel Corporation Method for manufacturing hot-press-formed article, and hot-press-formed article
KR102240850B1 (ko) 2020-07-10 2021-04-16 주식회사 포스코 생산성, 용접성 및 성형성이 우수한 열간 프레스 성형 부재의 제조 방법
CN112222271B (zh) * 2020-09-24 2023-03-24 中国航发贵州黎阳航空动力有限公司 一种分流器外壳的热拉伸成形方法
KR20220069178A (ko) * 2020-11-19 2022-05-27 주식회사 엘지에너지솔루션 펀치와 다이를 이용한 펀치 핀 홀 검사 장치 및 이를 이용한 펀치 핀 홀 검사 방법

Family Cites Families (18)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2807447B1 (fr) 2000-04-07 2002-10-11 Usinor Procede de realisation d'une piece a tres hautes caracteristiques mecaniques, mise en forme par emboutissage, a partir d'une bande de tole d'acier laminee et notamment laminee a chaud et revetue
JP3896061B2 (ja) * 2002-10-07 2007-03-22 新日本製鐵株式会社 熱間成形加工後の硬化能に優れた鋼板およびその使用方法
JP4094473B2 (ja) * 2003-04-18 2008-06-04 新日本製鐵株式会社 高温成形後硬化能に優れた熱間成形加工用鋼板およびその使用方法
JP3816937B1 (ja) * 2005-03-31 2006-08-30 株式会社神戸製鋼所 熱間成形品用鋼板およびその製造方法並びに熱間成形品
US7650547B2 (en) 2007-02-28 2010-01-19 Verigy (Singapore) Pte. Ltd. Apparatus for locating a defect in a scan chain while testing digital logic
US7661282B2 (en) * 2008-03-21 2010-02-16 Gm Global Technology Operations, Inc. Hot forming process for metal alloy sheets
JP2009082992A (ja) * 2009-01-30 2009-04-23 Nippon Steel Corp 熱間成形方法
JP4825882B2 (ja) * 2009-02-03 2011-11-30 トヨタ自動車株式会社 高強度焼き入れ成形体及びその製造方法
JP2011101889A (ja) * 2009-11-10 2011-05-26 Sumitomo Metal Ind Ltd 熱間プレス成形部品およびその製造方法
JP5327106B2 (ja) * 2010-03-09 2013-10-30 Ｊｆｅスチール株式会社 プレス部材およびその製造方法
JP4883240B1 (ja) * 2010-08-04 2012-02-22 Ｊｆｅスチール株式会社 熱間プレス用鋼板およびそれを用いた熱間プレス部材の製造方法
CA2807332C (en) * 2010-08-23 2013-12-17 Nippon Steel & Sumitomo Metal Corporation Method of hot stamping galvanized steel sheet
CN103392014B (zh) * 2010-12-24 2016-01-27 沃斯特阿尔派因钢铁有限责任公司 生产具有不同硬度和/或延展性的区域的硬化的元件的方法
JP5817479B2 (ja) * 2011-03-10 2015-11-18 Ｊｆｅスチール株式会社 熱間プレス部材の製造方法
WO2013031984A1 (ja) 2011-09-01 2013-03-07 株式会社神戸製鋼所 熱間プレス成形品およびその製造方法
CN102527803A (zh) * 2011-12-28 2012-07-04 吉林大学 一种高强钢局部加热成形方法
JP6001883B2 (ja) * 2012-03-09 2016-10-05 株式会社神戸製鋼所 プレス成形品の製造方法およびプレス成形品
ES2578359T3 (es) * 2012-03-30 2016-07-26 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Método para fabricar un elemento de acero formado en una prensa caliente y el elemento de acero formado en la prensa caliente

Non-Patent Citations (1)

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

Also Published As

Publication number Publication date
KR20160130831A (ko) 2016-11-14
US20170043386A1 (en) 2017-02-16
EP3135394A1 (en) 2017-03-01
CN106232254A (zh) 2016-12-14
KR101879307B1 (ko) 2018-07-17
EP3135394A4 (en) 2017-04-26
WO2015163016A8 (ja) 2016-08-18
CN106232254B (zh) 2019-03-01
WO2015163016A1 (ja) 2015-10-29
MX2016013666A (es) 2017-01-23
JP5825413B1 (ja) 2015-12-02
JP2015213958A (ja) 2015-12-03

Similar Documents

Publication Publication Date Title
EP3135394B1 (en) Method for manufacturing hot press forming part
CN109982839B (zh) 用于热压印的热轧涂覆钢板、热压印涂覆钢部件以及用于制造其的方法
EP3040133B1 (en) Method of manufacturing hot press formed part, and hot press formed part
KR101949627B1 (ko) 고강도 강판 및 그 제조 방법
TWI656037B (zh) High strength steel plate
KR101624473B1 (ko) 고강도 용융 아연 도금 강판 및 그 제조 방법
EP3216886A1 (en) Hot-dip galvanized steel sheet
EP3216887A1 (en) Hot-dip galvanized steel sheet
EP3199257B1 (en) Method of manufacturing hot press-formed part, and hot press-formed part
EP3178956A1 (en) High-strength steel sheet and production method for same, and production method for high-strength galvanized steel sheet
KR20180043331A (ko) 열간 프레스용 아연도금 강판 및 열간 프레스 성형품의 제조 방법
EP3216891A1 (en) Hot-dip galvanized steel sheet
JP6326761B2 (ja) ホットスタンプ鋼材の製造方法、ホットスタンプ用鋼板の製造方法及びホットスタンプ用鋼板
EP3178953A1 (en) High-strength steel sheet and production method for same, and production method for high-strength galvanized steel sheet
JPWO2013121963A1 (ja) 鋼板、めっき鋼板、及びそれらの製造方法
KR20190073469A (ko) 고강도 강판 및 그 제조 방법
MX2015002530A (es) Lamina de acero.
US11332804B2 (en) High-strength cold-rolled steel sheet, high-strength coated steel sheet, and method for producing the same
JP5070865B2 (ja) 局部延性能に優れた熱延鋼板及びその製造方法
JP6411881B2 (ja) フェライト系ステンレス鋼およびその製造方法
RU2532689C2 (ru) Холоднокатаный стальной лист, обладающий превосходным качеством поверхности после штамповки, и способ его производства
JP5245948B2 (ja) 冷延鋼帯の製造方法
WO2024028642A1 (en) Steel sheet having excellent powdering properties after press-hardening and method for manufacturing the same
TWI464279B (zh) 高強度鋼板及其製造方法

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20160817

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

A4 Supplementary search report drawn up and despatched

Effective date: 20170329

RIC1 Information provided on ipc code assigned before grant

Ipc: B21D 22/20 20060101AFI20170323BHEP

Ipc: B21D 24/04 20060101ALI20170323BHEP

DAX Request for extension of the european patent (deleted)
GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

RIC1 Information provided on ipc code assigned before grant

Ipc: B21D 24/04 20060101ALI20170725BHEP

Ipc: B21D 22/20 20060101AFI20170725BHEP

INTG Intention to grant announced

Effective date: 20170825

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAJ Information related to disapproval of communication of intention to grant by the applicant or resumption of examination proceedings by the epo deleted

Free format text: ORIGINAL CODE: EPIDOSDIGR1

GRAL Information related to payment of fee for publishing/printing deleted

Free format text: ORIGINAL CODE: EPIDOSDIGR3

GRAR Information related to intention to grant a patent recorded

Free format text: ORIGINAL CODE: EPIDOSNIGR71

INTC Intention to grant announced (deleted)
GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

INTG Intention to grant announced

Effective date: 20171219

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 4

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 966875

Country of ref document: AT

Kind code of ref document: T

Effective date: 20180215

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602015007881

Country of ref document: DE

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20180131

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 966875

Country of ref document: AT

Kind code of ref document: T

Effective date: 20180131

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180430

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180501

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180430

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180531

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

Ref country code: SE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

Ref country code: AT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

Ref country code: RS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

Ref country code: IT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602015007881

Country of ref document: DE

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20180228

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180226

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180228

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180228

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

26N No opposition filed

Effective date: 20181102

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180226

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180228

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180226

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: GB

Payment date: 20200219

Year of fee payment: 6

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20150226

Ref country code: MK

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180131

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180131

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20210226

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210226

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20231229

Year of fee payment: 10

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20240103

Year of fee payment: 10