WO2012169640A1 - Article moulé par pressage à chaud, procédé pour produire celui-ci, et tôle d'acier mince pour moulage à la presse à chaud - Google Patents

Article moulé par pressage à chaud, procédé pour produire celui-ci, et tôle d'acier mince pour moulage à la presse à chaud Download PDF

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WO2012169640A1
WO2012169640A1 PCT/JP2012/064851 JP2012064851W WO2012169640A1 WO 2012169640 A1 WO2012169640 A1 WO 2012169640A1 JP 2012064851 W JP2012064851 W JP 2012064851W WO 2012169640 A1 WO2012169640 A1 WO 2012169640A1
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hot press
less
thin steel
steel sheet
formed product
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PCT/JP2012/064851
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English (en)
Japanese (ja)
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純也 内藤
村上　俊夫
池田　周之
圭介 沖田
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株式会社神戸製鋼所
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Priority to EP12797579.5A priority Critical patent/EP2719788B1/fr
Priority to CN201280027602.5A priority patent/CN103620075B/zh
Priority to ES12797579.5T priority patent/ES2603590T3/es
Priority to KR1020147000405A priority patent/KR20140027451A/ko
Priority to US14/114,715 priority patent/US20140065007A1/en
Publication of WO2012169640A1 publication Critical patent/WO2012169640A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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
    • B21D22/22—Deep-drawing with devices for holding the edge of the blanks
    • 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
    • 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
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to a hot press-formed product that requires strength, such as used for structural members of automobile parts, a manufacturing method thereof, and a thin steel plate for hot press forming, and in particular, a pre-heated steel plate (blank).
  • the present invention relates to a hot press-formed product that obtains a predetermined strength by performing heat treatment at the same time as forming the shape, and a method for producing such a hot press-formed product, and a thin steel sheet for hot press forming. Is.
  • the steel sheet is heated to a predetermined temperature (for example, a temperature at which it becomes an austenite phase) to reduce the strength (that is, to facilitate forming), and then at a lower temperature than the thin steel sheet (
  • a predetermined temperature for example, a temperature at which it becomes an austenite phase
  • a hot press molding method that secures the strength after molding by forming a mold with a room temperature mold and performing a quenching heat treatment (quenching) using the temperature difference between the two at the same time as giving the shape. It has been adopted.
  • Such a hot press forming method since the material is formed in a low strength state, a springback is reduced (good shape freezing property), and a material with good hardenability to which alloy elements such as Mn and B are added. By using it, the strength of 1500 MPa class is obtained by the tensile cooling.
  • a hot press forming method is called by various names such as a hot forming method, a hot stamping method, a hot stamp method, and a die quench method in addition to the hot press method.
  • FIG. 1 is a schematic explanatory view showing a mold configuration for carrying out the above hot press molding (hereinafter may be represented by “hot stamp”).
  • 3 is a blank holder
  • 4 is a steel plate (blank)
  • BHF is a crease pressing force
  • rp is a punch shoulder radius
  • rd is a die shoulder radius
  • CL is a punch / die clearance.
  • the punch 1 and the die 2 have passages 1a and 2a through which a cooling medium (for example, water) can pass, and the cooling medium is allowed to pass through the passages.
  • a cooling medium for example, water
  • a steel sheet for hot stamping As a steel sheet for hot stamping that is currently widely used, a steel sheet made of 22MnB5 steel is known. This steel sheet has a tensile strength of 1500 MPa and an elongation of about 6 to 8%, and is applied to an impact resistant member (a member that is not deformed as much as possible at the time of collision and does not break).
  • an impact resistant member a member that is not deformed as much as possible at the time of collision and does not break.
  • the development of increasing the C content and further increasing the strength (1500 MPa or higher, 1800 MPa class) based on 22MnB5 steel is also in progress.
  • Non-Patent Document 1 proposes a method of hot stamping 22MnB5 steel for hot stamping and a material that does not become high strength even if quenched with a mold and laser welding (tailored weld blank: TWB).
  • the tensile strength is 1500 MPa (elongation 6-8%) on the high strength side (impact resistant site side), and the tensile strength is 440 MPa (elongation 12%) on the low strength side (energy absorption site side).
  • techniques for creating different strengths in parts techniques such as Non-Patent Documents 2 to 4 have been proposed.
  • the tensile strength is 600 MPa or less and the elongation is about 12 to 18% on the energy absorption site side, but it is necessary to perform laser welding (tailored weld blank: TWB) in advance. As the number increases, the cost increases. Moreover, the energy absorption site
  • Non-Patent Document 3 is based on 22MnB5 steel, but due to the influence of boron addition, the robustness of the strength after quenching is poor with respect to the heating at the two-phase region temperature, and the strength control on the energy absorption site side is difficult. Further, only about 15% of elongation is obtained.
  • Non-Patent Document 4 is based on 22MnB5 steel, which is not rational in terms of controlling the 22MnB5 steel with good hardenability so as not to be quenched (mold cooling control).
  • the present invention has been made in view of the above circumstances, and an object of the present invention is to provide a hot press-molded product that can control the balance between strength and elongation within an appropriate range and has high ductility, and such hot press molding. It is an object of the present invention to provide a useful method for manufacturing a product and a thin steel sheet for hot press forming.
  • the hot press-formed product of the present invention that has achieved the above object is a hot press-formed product obtained by forming a thin steel plate by a hot press method, and the metal structure is martensite: 80 to 97 area%.
  • the remaining austenite is 3 to 20% by area, and the remaining structure is 5% by area or less.
  • the chemical component composition is not limited, but as a typical example, C: 0.15 to 0.35% (meaning mass%; hereinafter, the chemical component composition is the same).
  • Si 0.5 to 3%
  • Mn 0.5 to 2%
  • P 0.05% or less (not including 0%)
  • S 0.05% or less (not including 0%)
  • Al 0.01 to 0.1%
  • Cr 0.01 to 1%
  • B 0.0002 to 0.01%
  • N 0 .001% to 0.01% each, and the balance being iron and inevitable impurities.
  • the hot press-formed product of the present invention if necessary, as another element, (a) one or more selected from the group consisting of Cu, Ni and Mo: 1% or less in total (0% (B) V and / or Nb: It is also useful to contain a total of 0.1% or less (excluding 0%), etc., depending on the type of element contained, hot press The properties of the molded product are further improved.
  • the thin steel plate is heated to a temperature not lower than the Ac 3 transformation point and not higher than 1000 ° C., and then molded.
  • the molding may be terminated at a temperature equal to or lower than (Martensite transformation start temperature Ms point ⁇ 50 ° C.) while securing an average cooling rate of 20 ° C./second or more in the mold. .
  • the present invention also includes a thin steel plate for hot press forming for producing the above hot press formed product, and this thin steel plate has the chemical composition as described above.
  • the hot press forming method by appropriately controlling the conditions, it is possible to adjust the metal structure in the presence of an appropriate amount of retained austenite, compared with the case of using the conventional 22MnB5 steel.
  • a hot press-molded product having a higher ductility (residual ductility) inherent in the molded product can be realized, and the strength and elongation can be controlled by a combination with the heat treatment conditions and the structure (initial structure) of the steel sheet before forming.
  • the inventors of the present invention show a good ductility (elongation) while ensuring high strength after forming when a thin steel plate is heated to a predetermined temperature and then hot press-molded to produce a molded product. In order to realize hot press-formed products, we examined from various angles.
  • the heating temperature and the conditions at the time of forming are appropriately controlled, and 3 to 20 area% of retained austenite is included.
  • the present inventors completed the present invention by finding that a hot press-molded product excellent in strength-ductility balance can be realized by adjusting the structure as described above.
  • the reason for setting the range of each structure (basic structure) in the hot press-formed product of the present invention is as follows.
  • the area fraction of martensite needs to be 80 area% or more. However, when this fraction exceeds 97 area%, the fraction of retained austenite becomes insufficient and ductility (residual ductility) decreases.
  • a preferred lower limit of the martensite fraction is 83 area% or more (more preferably 85 area% or more), and a preferred upper limit is 95 area% or less (more preferably 93 area% or less).
  • Residual austenite has the effect of increasing the work hardening rate (transformation-induced plasticity) and improving the ductility of the molded product by transforming into martensite during plastic deformation.
  • the fraction of retained austenite needs to be 3 area% or more.
  • the ductility the higher the retained austenite fraction, the better.
  • the upper limit is about 20 area%.
  • the preferable lower limit of retained austenite is 5 area% or more (more preferably 7 area% or more), and the preferable upper limit is 17 area% or less (more preferably 15 area% or less, or 10 area% or less).
  • Remainder structure 5 area% or less
  • ferrite, pearlite, bainite, and the like may be included as the remaining structure.
  • these structures are softer than martensite and contribute less to the strength than other structures, and are preferably as small as possible.
  • up to 5 area% is acceptable.
  • the remaining structure is more preferably 3 area% or less, and still more preferably 0 area%.
  • a thin steel plate is used (the chemical composition is the same as that of the formed product), and when the thin steel plate is press-formed using a press mold, the thin steel plate is used. Is heated to a temperature not lower than the Ac 3 transformation point and not higher than 1000 ° C., and then molding is started. During the molding, while maintaining an average cooling rate of 20 ° C./second or higher in the mold (Martensite transformation start temperature Ms The molding may be completed at a temperature of point ⁇ 50 ° C. or lower.
  • the reasons for specifying each requirement in this method are as follows.
  • the heating temperature of the thin steel plate exceeds 1000 ° C.
  • the grain size of austenite increases during heating, the martensite transformation start temperature (Ms point) and the martensite transformation end temperature (Mf point) rise, and remain during quenching. Austenite cannot be secured and good moldability cannot be achieved.
  • a mixed structure of martensite and retained austenite can be obtained by cooling under such conditions.
  • the average cooling rate during molding is preferably 30 ° C./second or more (more preferably 40 ° C./second or more).
  • the molding completion temperature may be finished while cooling to room temperature at the above average cooling rate, but after cooling to (Ms point ⁇ 50 ° C.) or less (preferably to a temperature of Ms point ⁇ 50 ° C.), 200 You may make it cool to 2 degrees C or less (2 step cooling) with the average cooling rate of less than 20 degrees C / sec.
  • the average cooling rate during the second stage cooling is preferably 10 ° C./second or less (more preferably 5 ° C./second or less).
  • the average cooling rate during molding is controlled by means such as (a) controlling the temperature of the mold (cooling medium shown in FIG. 1), (b) controlling the thermal conductivity of the mold, and the like. Can be achieved.
  • the hot press molding method of the present invention not only the case of manufacturing a hot press molded product having a simple shape as shown in FIG. 1 (direct method) but also a molded product having a relatively complicated shape is manufactured. It can also be applied to the case. However, in the case of a complicated part shape, it may be difficult to create the final shape of the product by a single press molding. In such a case, a method of performing cold press forming in a pre-process of hot press forming (this method is called “indirect method”) can be employed. This method is a method in which a portion that is difficult to be molded is preliminarily molded to an approximate shape by cold working, and the other portions are hot press molded. If such a method is adopted, for example, when a part having three uneven portions (peaks) of a molded product is formed, the two parts are formed by cold press molding, and then the third part is formed. Will be hot pressed.
  • the present invention is made assuming a hot press-formed product made of a high-strength steel plate, and its steel type may be of a normal chemical composition as a high-strength steel plate, but C, Si, About Mn, P, S, Al, Cr, B, Ti, and N, it is good to adjust to an appropriate range. From such a viewpoint, the preferable ranges of these chemical components and the reasons for limiting the ranges are as follows.
  • C is an important element in controlling the strength of the martensite structure. If the C content is reduced, the strength is insufficient even with full martensite. If the C content is less than 0.15%, the strength of the martensite is insufficient, so the high strength of the hot press-formed product cannot be ensured. On the other hand, if the C content is excessive and exceeds 0.35%, the strength becomes too high and good ductility cannot be obtained.
  • the more preferable lower limit of the C content is 0.18% or more (more preferably 0.20% or more), and the more preferable upper limit is 0.30% or less (more preferably 0.27% or less, still more preferably 0). .25% or less).
  • Si exhibits the effect of forming retained austenite during quenching.
  • the solid solution strengthening also exerts the effect of increasing the strength without significantly degrading the ductility. If the Si content is less than 0.5%, a predetermined retained austenite amount cannot be secured, and good ductility cannot be obtained. On the other hand, if the Si content is excessive and exceeds 3%, the solid solution strengthening amount becomes too large, and the ductility is greatly deteriorated.
  • the more preferable lower limit of the Si content is 1.15% or more (more preferably 1.20% or more), and the more preferable upper limit is 2.7% or less (more preferably 2.5% or less).
  • Mn is an element that stabilizes austenite and contributes to an increase in retained austenite. Moreover, it is an element which improves hardenability, suppresses the formation of ferrite, pearlite and bainite during cooling after heating and contributes to securing retained austenite. In order to exhibit such an effect, it is preferable to contain 0.5% or more of Mn. When only the characteristics are considered, it is preferable that the Mn content is large, but it is preferable to make it 2% or less because the cost of alloy addition increases. Further, since the strength of austenite is significantly improved, the hot rolling load becomes large and the production of the steel sheet becomes difficult. Therefore, it is not preferable to contain more than 2% from the viewpoint of productivity. A more preferable lower limit of the Mn content is 0.7% or more (more preferably 0.9% or more), and a more preferable upper limit is 1.8% or less (more preferably 1.6% or less).
  • P 0.05% or less (excluding 0%)
  • P is an element inevitably contained in the steel, but it deteriorates ductility, so it is preferable to reduce P as much as possible.
  • extreme reduction leads to an increase in steelmaking cost, and since it is difficult to make it 0%, it is preferable to make it 0.05% or less (not including 0%).
  • a more preferable upper limit of the P content is 0.045% or less (more preferably 0.040% or less).
  • S 0.05% or less (excluding 0%)
  • S is an element inevitably contained in steel, and deteriorates ductility. Therefore, S is preferably reduced as much as possible.
  • extreme reduction leads to an increase in steelmaking cost, and since it is difficult to make it 0%, it is preferable to make it 0.05% or less (not including 0%).
  • a more preferable upper limit of the S content is 0.045% or less (more preferably 0.040% or less).
  • Al 0.01 to 0.1%
  • Al is useful as a deoxidizing element, and also fixes solid solution N present in steel as AlN, which is useful for improving ductility.
  • the Al content is preferably 0.01% or more.
  • a more preferable lower limit of the Al content is 0.013% or more (more preferably 0.015% or more), and a more preferable upper limit is 0.08% or less (more preferably 0.06% or less).
  • Cr 0.01 to 1% Since Cr has an action of suppressing ferrite transformation, pearlite transformation, and bainite transformation, it is an element that prevents formation of ferrite, pearlite, and bainite during cooling after heating and contributes to securing retained austenite. In order to exert such an effect, Cr is preferably contained in an amount of 0.01% or more, but even if it is contained in excess of 1%, the cost increases. A more preferable lower limit of the Cr content is 0.02% or more (more preferably 0.05% or more), and a more preferable upper limit is 0.8% or less (more preferably 0.5% or less).
  • B is an element that enhances hardenability and suppresses ferrite transformation, pearlite transformation, and bainite transformation, thus preventing formation of ferrite, pearlite, and bainite during cooling after heating and contributing to securing retained austenite. It is. In order to exert such effects, B is preferably contained in an amount of 0.0002% or more, but the effect is saturated even if it is contained in excess of 0.01%. A more preferable lower limit of the B content is 0.0003% or more (more preferably 0.0005% or more), and a more preferable upper limit is 0.008% or less (more preferably 0.005% or less).
  • Ti (N content) ⁇ 4 to 0.1%] Ti fixes N and allows B to be maintained in a solid solution state, thereby exhibiting an effect of improving hardenability. In order to exert such an effect, it is preferable to contain Ti at least four times the content of N. However, if the Ti content is excessive and exceeds 0.1%, a large amount of TiC is formed, The strength increases by precipitation strengthening, but the ductility deteriorates. A more preferable lower limit of the Ti content is 0.05% or more (more preferably 0.06% or more), and a more preferable upper limit is 0.09% or less (more preferably 0.08% or less).
  • N is an element that reduces the hardenability improving effect by fixing B as BN, and it is preferable to reduce it as much as possible.
  • the lower limit was set.
  • the upper limit was made 0.01%.
  • the upper limit with more preferable N content is 0.008% or less (more preferably 0.006% or less).
  • substantially iron means a trace component that does not inhibit the properties of the steel material of the present invention other than iron (for example, Mg, Ca, Sr, Ba, REM such as La, and Zr, Hf). , Ta, W, Mo and other carbide-forming elements) are acceptable, and inevitable impurities other than P and S (for example, O, H, etc.) can also be included.
  • the press-formed product of the present invention if necessary, (a) one or more selected from the group consisting of Cu, Ni and Mo: 1% or less in total (excluding 0%), (b) V and / Or Nb: It is also useful to contain a total of 0.1% or less (excluding 0%), etc., and the characteristics of the hot press-formed product are further improved depending on the type of element contained .
  • the preferable range when these elements are contained and the reason for limiting the range are as follows.
  • Cu, Ni and Mo 1% or less in total (excluding 0%)
  • Cu, Ni, and Mo suppress ferrite transformation, pearlite transformation, and bainite transformation, thus preventing formation of ferrite, pearlite, and bainite during cooling after heating, and effectively act to secure retained austenite.
  • the more preferable lower limit of the content of these elements is 0.05% or more (more preferably 0.06% or more) in total, and the more preferable upper limit is 0.9% or less (more preferably 0.8% or less) in total. ).
  • V and Nb 0.1% or less in total (excluding 0%)
  • V and Nb have the effect of forming fine carbides and making the structure fine by the pinning effect. In order to exhibit such an effect, it is preferable to contain 0.001% or more in total. However, if the content of these elements is excessive, coarse carbides are formed and the ductility is deteriorated by becoming the starting point of destruction, so the total content is preferably 0.1% or less.
  • the more preferable lower limit of the content of these elements is 0.005% or more (more preferably 0.008% or more) in total, and the more preferable upper limit is 0.08% or less (more preferably 0.06% or less) in total. ).
  • the hot press forming thin steel sheet of the present invention may be either a non-plated steel sheet or a plated steel sheet.
  • the type of plating may be any of general zinc-based plating and aluminum-based plating.
  • the plating method may be any one of hot dipping, electroplating, etc., and may be further subjected to alloying heat treatment after plating, or may be subjected to multilayer plating.
  • the press molding conditions heat treating temperature and cooling rate
  • properties such as strength and elongation of the molded product
  • high hotness residual ductility
  • a press-molded product can be obtained, it can be applied to parts that have been difficult to apply with conventional hot-pressed products (for example, energy absorbing members), which is extremely useful in expanding the range of application of hot-pressed products. It is.
  • the molded product obtained by the present invention has a larger residual ductility than a molded product whose structure is adjusted by performing normal annealing after cold press molding.
  • a steel material having the chemical composition shown in Table 1 below was vacuum-melted to obtain a slab for experiment, then hot rolled, and then cooled and wound up. Furthermore, it cold-rolled and made it the thin steel plate.
  • the Ac 3 transformation point and Ms point in Table 1 were obtained using the following formulas (1) and (2) (see, for example, “Leslie Steel Materials Science” Maruzen, (1985)). .
  • the obtained steel sheet was heated under the conditions shown in Table 2 below, and then subjected to forming / cooling treatment using a high-speed heat treatment test apparatus for steel (CAS series, ULVAC-RIKO) that can control the average cooling rate.
  • the steel plate size during forming and cooling was 190 mm ⁇ 70 mm (plate thickness: 1.4 mm).
  • the cooling rate 1 shown in Table 2 is the average cooling rate from the heating temperature to (Ms point ⁇ 50 ° C.) or less (molding end temperature), and the cooling rate 2 is the average cooling from the molding end temperature to 200 ° C. or less. Indicates the speed, respectively.
  • the steel plate was immersed in the molten zinc as needed, and galvanization was made to adhere to the steel plate surface (test No. 21).
  • Test No. Those of 1, 2, 6, 11, 12, 14 to 21 are examples that satisfy the requirements defined in the present invention, and it can be seen that parts having a good strength-ductility balance are obtained.
  • test no. 6 shows that a part having a very high strength and a good ductility is obtained.
  • test no. Samples 3 to 5, 7 to 10, and 13 are comparative examples that do not satisfy any of the requirements defined in the present invention, and any of the characteristics is deteriorated. That is, test no. In No. 3, the cooling rate after heating is slow, the martensite fraction is not secured (ferrite and bainitic ferrite are generated), and the strength is not secured. Test No. In No. 4, the heating temperature is lower than the Ac 3 transformation point, the martensite fraction is not secured, and the strength is not secured.
  • Test No. 7 and 8 are intended for conventional 22MnB5 equivalent steel (steel type C in Table 1). Although high strength is obtained, residual austenite is not secured and low elongation (EL) is achieved. It has only been obtained.
  • Test No. No. 9 is a steel that does not contain Ti and B (steel type D in Table 1), the martensite fraction is not secured, and the strength is not secured.
  • Test No. No. 10 is a steel using a steel with insufficient C content (steel type E in Table 1). Residual austenite is not ensured and only low elongation (EL) is obtained.
  • Test No. No. 13 is a steel that does not contain Cr (steel type H in Table 1), the martensite fraction is not secured, and the strength is not secured.
  • the present invention is a hot press-formed product obtained by forming a thin steel plate by a hot press forming method, wherein the metal structure includes martensite: 80 to 97 area%, residual austenite: 3 to 20 area%, and the remaining structure : By making the content 5% by area or less, it is possible to realize a hot press-formed product that can control the balance between strength and elongation within an appropriate range and has high ductility.

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Abstract

La présente invention concerne un article moulé par pressage à chaud comprenant une tôle d'acier mince formée par moulage à la presse à chaud. Par configuration de l'article moulé par pressage à chaud de sorte que la structure métallique comprenne de 80 à 97 % en aire de martensite, et de 3 à 20 % en aire d'austénite retenue, la structure résiduelle ne comprenant pas plus de 5 % en aire, l'équilibre entre la résistance et l'étirage peut être maintenu dans une plage appropriée, et une ductilité élevée peut être obtenue.
PCT/JP2012/064851 2011-06-10 2012-06-08 Article moulé par pressage à chaud, procédé pour produire celui-ci, et tôle d'acier mince pour moulage à la presse à chaud WO2012169640A1 (fr)

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EP12797579.5A EP2719788B1 (fr) 2011-06-10 2012-06-08 Article moulé par pressage à chaud, procédé pour produire celui-ci, et tôle d'acier mince pour moulage à la presse à chaud
CN201280027602.5A CN103620075B (zh) 2011-06-10 2012-06-08 热压成形品、其制造方法和热压成形用薄钢板
ES12797579.5T ES2603590T3 (es) 2011-06-10 2012-06-08 Artículo moldeado en prensa caliente, método para producir el mismo, y lámina fina de acero para el moldeado en prensa caliente
KR1020147000405A KR20140027451A (ko) 2011-06-10 2012-06-08 열간 프레스 성형품, 그 제조 방법 및 열간 프레스 성형용 박강판
US14/114,715 US20140065007A1 (en) 2011-06-10 2012-06-08 Hot press-formed product, process for producing same, and thin steel sheet for hot press forming

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JP2011208032 2011-09-22
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WO2015037061A1 (fr) * 2013-09-10 2015-03-19 株式会社神戸製鋼所 Tôle d'acier pour formage à chaud à la presse, article moulé à la presse et procédé de fabrication d'un article moulé à la presse
EP3045554A4 (fr) * 2013-09-10 2017-03-22 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Tôle d'acier pour formage à chaud à la presse, article moulé à la presse et procédé de fabrication d'un article moulé à la presse
WO2015037060A1 (fr) * 2013-09-10 2015-03-19 株式会社神戸製鋼所 Plaque d'acier pressée à chaud, article moulé à la presse, et procédé de fabrication d'article moulé à la presse
RU2628184C1 (ru) * 2013-09-10 2017-08-15 Кабусики Кайся Кобе Сейко Се (Кобе Стил,Лтд.) Горячештампованная толстолистовая сталь, формованное штамповкой изделие, и способ изготовления формованного штамповкой изделия
RU2625357C1 (ru) * 2013-09-10 2017-07-13 Кабусики Кайся Кобе Сейко Се (Кобе Стил, Лтд.) Горячештампованная толстолистовая сталь, формованное штампованием изделие и способ изготовления формованного штампованием изделия
EP3045553A4 (fr) * 2013-09-10 2017-03-22 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Plaque d'acier pressée à chaud, article moulé à la presse, et procédé de fabrication d'article moulé à la presse
WO2015041159A1 (fr) 2013-09-18 2015-03-26 新日鐵住金株式会社 Corps moulé par estampage à chaud et son procédé de production
CN105518173A (zh) * 2013-09-18 2016-04-20 新日铁住金株式会社 热冲压成型体以及其制造方法
EP3020845A4 (fr) * 2013-09-18 2017-04-05 Nippon Steel & Sumitomo Metal Corporation Corps moulé par estampage à chaud et son procédé de production
JPWO2015041159A1 (ja) * 2013-09-18 2017-03-02 新日鐵住金株式会社 ホットスタンプ成形体及びその製造方法
KR20160023855A (ko) 2013-09-18 2016-03-03 신닛테츠스미킨 카부시키카이샤 핫 스탬프 성형체 및 그 제조 방법
EP3020845A1 (fr) * 2013-09-18 2016-05-18 Nippon Steel & Sumitomo Metal Corporation Corps moulé par estampage à chaud et son procédé de production
US10301699B2 (en) 2013-09-18 2019-05-28 Nippon Steel & Sumitomo Metal Corporation Hot-stamped part and method of manufacturing the same
JPWO2016063467A1 (ja) * 2014-10-24 2017-04-27 Ｊｆｅスチール株式会社 高強度ホットプレス部材およびその製造方法
JP6004138B2 (ja) * 2014-10-24 2016-10-05 Ｊｆｅスチール株式会社 高強度ホットプレス部材およびその製造方法
WO2016063467A1 (fr) * 2014-10-24 2016-04-28 Ｊｆｅスチール株式会社 Élément de haute résistance formé à chaud à la presse et son procédé de fabrication
US10392677B2 (en) 2014-10-24 2019-08-27 Jfe Steel Corporation High-strength hot-pressed part and method for manufacturing the same
WO2022172993A1 (fr) * 2021-02-10 2022-08-18 日本製鉄株式会社 Corps moulé estampé à chaud

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KR20140027451A (ko) 2014-03-06
JP2013079441A (ja) 2013-05-02
EP2719788B1 (fr) 2016-11-02
EP2719788A4 (fr) 2015-10-21
JP5873393B2 (ja) 2016-03-01
EP2719788A1 (fr) 2014-04-16
CN103620075A (zh) 2014-03-05
US20140065007A1 (en) 2014-03-06
ES2603590T3 (es) 2017-02-28
CN103620075B (zh) 2016-02-17

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