WO2015037060A1 - Hot-pressing steel plate, press-molded article, and method for manufacturing press-molded article - Google Patents
Hot-pressing steel plate, press-molded article, and method for manufacturing press-molded article Download PDFInfo
- Publication number
- WO2015037060A1 WO2015037060A1 PCT/JP2013/074426 JP2013074426W WO2015037060A1 WO 2015037060 A1 WO2015037060 A1 WO 2015037060A1 JP 2013074426 W JP2013074426 W JP 2013074426W WO 2015037060 A1 WO2015037060 A1 WO 2015037060A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- press
- less
- area
- amount
- steel
- Prior art date
Links
Images
Classifications
-
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
-
- 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
-
- 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
- B21D22/28—Deep-drawing of cylindrical articles using consecutive dies
- B21D22/286—Deep-drawing of cylindrical articles using consecutive dies with lubricating or cooling means
-
- 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
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
- C21D1/20—Isothermal quenching, e.g. bainitic hardening
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
-
- 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
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
- C22C38/18—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
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
Definitions
- the present invention is used when manufacturing a structural part of an automobile, and is a hot-press steel sheet suitable for hot press forming, a press-formed product obtained from such a hot-press steel plate, and a press-formed product. It relates to a manufacturing method.
- a preheated steel plate blade
- the hot press steel plate is useful for application to a hot press forming method in which a heat treatment is performed simultaneously with shape formation to obtain a predetermined strength.
- a press-formed product, and a useful method for producing such a press-formed product is used when manufacturing a structural part of an automobile, and is a hot-press steel sheet suitable for hot press forming, a press-formed product obtained from such a hot-press steel plate, and a press-formed product.
- the steel sheet is heated to a predetermined temperature (for example, the temperature at which it becomes an austenite phase) to lower the strength, and then formed with a mold having a temperature lower than that of the steel sheet (for example, room temperature).
- a hot press molding method is used for manufacturing a part (press-molded product) that performs quenching heat treatment (quenching) using the temperature difference between the two to ensure strength after molding.
- 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 diagram showing a mold configuration for carrying out hot press molding as described above.
- 1 is a punch
- 2 is a die
- 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
- the steel plate (blank) 4 is subjected to the two-phase region temperature (Ac 1 transformation point to Ac 3 transformation point) or Ac 3 transformation. Molding is started in a state of being softened by heating to a single-phase temperature above the point. That is, in a state where the steel plate 4 in a high temperature state is sandwiched between the die 2 and the blank holder 3, the steel plate 4 is pushed into the hole of the die 2 (between 2 and 2 in FIG. 1) by the punch 1, and the outer diameter of the steel plate 4 is reduced. A shape corresponding to the outer shape of the punch 1 is formed while shrinking.
- a steel sheet for hot pressing that is widely used at present, 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 and does not break).
- an impact resistant member a member that is not deformed as much as possible and does not break.
- Patent Documents 1 to 4 As hot-press steel sheets exhibiting good elongation, for example, the techniques of Patent Documents 1 to 4 have been proposed. In these technologies, the basic strength class of each steel sheet is adjusted by setting the carbon content in the steel sheet to various ranges, and ferrite with high deformability is introduced, and the average of ferrite and martensite Elongation is improved by reducing the particle size. These techniques are effective for improving the elongation, but are still insufficient from the viewpoint of improving the elongation according to the strength of the steel sheet. For example, the tensile strength TS is 1470 MPa or more and the elongation EL is about 10.2% at the maximum, and further improvement is required.
- the part where deformation should be prevented is high strength (high strength side: impact resistant part side), and the part requiring energy absorption is low strength and high ductility (low strength side: energy absorbing part side).
- High strength side impact resistant part side
- low strength side energy absorbing part side
- Technology has been proposed.
- impact resistance is included in the parts of the B pillar and rear side member in consideration of compatibility (a function to protect the other party when a small car collides) in a side collision or a rear collision. In some cases, it has both functional parts of energy absorption.
- a tensile strength of 1500 MPa is achieved on the high strength side (impact resistant site side), but the maximum tensile strength is 700 MPa and the elongation EL is about 17% on the low strength side (energy absorption site side).
- the energy absorption site side In order to further improve the energy absorption characteristics, it is required to realize higher strength and higher ductility.
- Non-Patent Document 1 Although it is necessary to join automobile parts mainly by spot welding, it is known that the strength reduction in the welding heat affected zone (HAZ) is remarkable and the strength of the welded joint is reduced (softened) (for example, Non-Patent Document 1).
- the present invention has been made in view of the above circumstances, and its purpose is to facilitate molding and processing before hot pressing, and when a uniform characteristic is required in a molded product, it has high strength. If a region corresponding to an impact resistant region and an energy absorbing region is required in a single molded product, it is possible to obtain a press molded product that can achieve a high balance between elongation and elongation. Steel sheet for hot pressing that can achieve a high balance between high strength and elongation at a high level, and that is useful in obtaining a press-formed product with good softening prevention characteristics in HAZ, and a press-formed product that exhibits the above characteristics And providing a useful method for producing such a press-formed product.
- the steel sheet for hot pressing of the present invention that was able to achieve the above object, C: 0.15 to 0.5% (meaning mass%, hereinafter the same for chemical composition) Si: 0.2-3%, Mn: 0.5 to 3%, P: 0.05% or less (excluding 0%), S: 0.05% or less (excluding 0%), Al: 0.01 to 1%, B: 0.0002 to 0.01%, Ti: 3.4 [N] + 0.01% or more, 3.4 [N] + 0.1% or less (where [N] indicates the content (% by mass) of N), and N: 0.0010 ⁇ 0.01%, Each of which contains iron and inevitable impurities, Among the Ti-containing precipitates contained in the steel sheet, the average equivalent circle diameter of those having an equivalent circle diameter of 30 nm or less is 6 nm or less, and the relationship between the precipitated Ti amount in the steel and the total Ti amount in the following formula (1) And the metal structure is characterized in that the ferrite fraction is 30 area% or more.
- the “equivalent circle diameter” means the diameter when converted to a circle of the same area when focusing on the size (area) of the Ti-containing precipitate (eg, TiC) (the “average equivalent circle diameter” is its average Value).
- the hot press-forming steel sheet of the present invention it is also useful to contain at least one of the following (a) to (c) as other elements as required. Depending on the type of element contained as required, the properties of the press-formed product are further improved.
- C 0.01% or less (excluding 0%) of at least one selected from the group consisting of Mg, Ca and REM
- the method for producing a press-formed product of the present invention that has achieved the above-mentioned object includes the steel sheet for hot pressing of the present invention as described above having an Ac 1 transformation point of + 20 ° C. or higher and an Ac 3 transformation point of ⁇ 20 ° C. or lower. After heating to the above temperature, press forming of the steel sheet is started, and during the forming and after the forming is completed, a temperature lower by 100 ° C. than the bainite transformation start temperature Bs while ensuring an average cooling rate of 20 ° C./second or more in the mold. It is characterized by cooling to the following.
- the metal structure of the press-formed product is as follows: retained austenite: 3 to 20 area%, ferrite: 30 to 80 area%, bainitic ferrite: less than 30 area% (excluding 0 area%) Martensite: 31 area% or less (excluding 0 area%), and among the Ti-containing precipitates contained in the press-formed product, the average equivalent circle diameter of the equivalent circle diameter of 30 nm or less is 10 nm or less.
- the amount of precipitated Ti in the steel and the total amount of Ti satisfy the relationship of the following formula (1), and the balance between high strength and elongation can be achieved as a uniform characteristic at a high level in the molded product.
- Precipitated Ti amount (mass%)-3.4 [N] ⁇ 0.5 ⁇ [Total Ti amount (mass%)-3.4 [N]] (1) (In the formula (1), [N] indicates the content (% by mass) of N in the steel)
- another method for producing a press-formed product of the present invention that has achieved the above object is to use a steel sheet for hot pressing as described above, and divide the heating area of the steel sheet into at least two areas. region of Ac 3 transformation point or more, while heating to a temperature of 950 ° C. or less, the other one region Ac 1 transformation point + 20 ° C. or higher, then heated to Ac 3 transformation point -20 ° C. or less of the temperature, both Press molding is started for the region, and during molding and after completion of molding, the mold is cooled to a temperature below the martensite transformation start temperature Ms while ensuring an average cooling rate of 20 ° C./second or more in the mold. It is characterized by that.
- Another press-formed product of the present invention is a steel plate press-formed product having the chemical composition as described above, and the press-formed product has a metal structure of retained austenite: 3 to 20 area%, martensite: The first region is 80 area% or more, and the metal structure is retained austenite: 3 to 20 area%, ferrite: 30 to 80 area%, bainitic ferrite: less than 30 area% (excluding 0 area%) , Martensite: having a second region that is 31 area% or less (not including 0 area%), and among the Ti-containing precipitates contained in the steel of this second region, the equivalent circle diameter is The average equivalent circle diameter of those having a thickness of 30 nm or less is 10 nm or less, and the amount of precipitated Ti in the steel and the total amount of Ti satisfy the relationship of the following formula (1).
- the chemical component composition is strictly defined, the size of Ti-containing precipitates is controlled, the precipitation rate is controlled for Ti that does not form TiN, and the ferrite ratio for the metal structure. Since a steel sheet with adjusted thickness is used, the strength-elongation balance of the press-formed product can be raised to a high level by hot pressing this under predetermined conditions. In addition, when hot pressing is performed under different conditions in a plurality of regions, an impact resistant part and an energy absorbing part can be formed in a single molded product, and a high strength and elongation balance can be achieved at each part at a high level. The anti-softening property of is improved.
- the inventors of the present invention when heating a steel plate to a predetermined temperature and then producing a press-formed product by hot press forming, show good ductility (elongation) while ensuring high strength after press forming. In order to realize a hot-press steel sheet that can provide a simple press-formed product, studies were made from various angles.
- the chemical component composition of the steel sheet for hot pressing is strictly defined, the size of Ti-containing precipitates and the amount of precipitated Ti are controlled, the metal structure is made appropriate, and the steel sheet is subjected to predetermined conditions. It has been found that by performing hot press molding, a predetermined amount of retained austenite can be secured after press molding, and a press-molded product having increased inherent ductility (residual ductility) can be obtained, and the present invention has been completed.
- C corresponds to an impact resistant site and an energy absorbing site in a single molded product in order to achieve a high balance between high strength and elongation when uniform properties are required in a press molded product. It is an important element for securing retained austenite when a region is required, particularly in a low strength / high ductility region. Moreover, at the time of heating by hot press molding, C concentrates to austenite, so that residual austenite can be formed after quenching. Furthermore, it contributes to an increase in the amount of martensite and raises the strength. In order to exert these effects, the C content needs to be 0.15% or more.
- the target metal structure ferrite, bainitic ferrite, especially in low strength and high ductility parts
- the preferable lower limit of the C content is 0.17% or more (more preferably 0.20% or more), and the more preferable upper limit is 0.45% or less (more preferably 0.40% or less).
- Si (Si: 0.2-3%) Si exhibits the effect of forming retained austenite by suppressing martensite from tempering to form cementite and decomposition of untransformed austenite during cooling of mold quenching.
- the Si content needs to be 0.2% or more. Further, if the Si content is excessive and exceeds 3%, ferrite transformation is promoted during cooling after hot rolling, so that TiC in the ferrite formed at that time is easily formed coarsely. Therefore, the HAZ softening preventing property cannot be obtained.
- the preferable lower limit of the Si content is 0.5% or more (more preferably 1.0% or more), and the preferable upper limit is 2.5% or less (more preferably 2.0% or less).
- Mn is an element effective in enhancing hardenability and suppressing the formation of structures (ferrite, pearlite, bainite, etc.) other than martensite and retained austenite during cooling of mold hardening. Further, it is an element that stabilizes austenite and contributes to an increase in the amount of retained austenite. In order to exhibit such an effect, it is necessary to contain 0.5% or more of Mn. When only the characteristics are taken into consideration, it is preferable that the Mn content is high, but the upper limit is made 3% or less because the cost of alloy addition increases. The minimum with preferable Mn content is 0.7% or more (more preferably 1.0% or more), and a preferable upper limit is 2.5% or less (more preferably 2.0% or less).
- P 0.05% or less (excluding 0%)
- P is an element inevitably contained in the steel, but it deteriorates ductility, so P is preferably reduced as much as possible.
- the upper limit was made 0.05% or less (excluding 0%).
- the upper limit with preferable 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.
- the upper limit was made 0.05% or less (excluding 0%).
- the upper limit with preferable S content is 0.045% or less (more preferably 0.040% or less).
- Al 0.01-1%)
- 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 needs to be 0.01% or more.
- the preferable lower limit of the Al content is 0.02% or more (more preferably 0.03% or more), and the preferable upper limit is 0.8% or less (more preferably 0.6% or less).
- B has an action of suppressing ferrite transformation, pearlite transformation, and bainite transformation on the high-strength portion side, so that during the cooling after heating to the two-phase region temperature (Ac 1 transformation point to Ac 3 transformation point), It is an element that prevents the formation of pearlite and bainite and contributes to securing retained austenite.
- B In order to exert such an effect, B needs to be 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 preferable lower limit of the B content is 0.0003% or more (more preferably 0.0005% or more), and a preferable upper limit is 0.008% or less (more preferably 0.005% or less).
- Ti 3.4 [N] + 0.01% or more, 3.4 [N] + 0.1% or less: [N] is N content (mass%)
- 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 important to contain 0.01% or more than the stoichiometric ratio of Ti and N (3.4 times the N content). Further, Ti added excessively to N is present in a solid solution state in the hot stamping molded product, and the precipitated compound is dispersed finely, so that the solid solution is dissolved when the hot stamping molded product is welded.
- Strength reduction in HAZ can be suppressed by effects such as precipitation strengthening due to the formation of Ti as TiC and an increase delay of dislocation density due to the effect of preventing dislocation movement due to TiC.
- the Ti content becomes excessive and exceeds 3.4 [N] + 0.1%, the Ti-containing precipitates formed (for example, TiN) are coarsened and the ductility of the steel sheet is lowered.
- the more preferable lower limit of the Ti content is 3.4 [N] + 0.02% or more (more preferably 3.4 [N] + 0.05% or more), and the more preferable upper limit is 3.4 [N]. + 0.09% or less (more preferably 3.4 [N] + 0.08% or less).
- N (N: 0.001 to 0.01%) N is an element inevitably mixed in and is preferably reduced as much as possible. However, since there is a limit to reducing it in the actual process, 0.001% was set as the lower limit. Further, when the N content is excessive, the Ti-containing precipitates formed (for example, TiN) are coarsened, and the precipitates act as a starting point for fracture and reduce the ductility of the steel sheet. It was.
- the upper limit with more preferable N content is 0.008% or less (more preferably 0.006% or less).
- the basic chemical components in the steel sheet for hot pressing of the present invention are as described above, and the balance is iron and inevitable impurities (for example, O, H, etc.) other than P, S, and N.
- the steel sheet for hot pressing according to the present invention further contains at least one of the following (a) to (c) if necessary.
- the properties of the steel sheet for hot pressing ie, press-formed product
- the preferable range when these elements are contained and the reason for limiting the range are as follows.
- A 0.1% or less in total of one or more selected from the group consisting of V, Nb and Zr (excluding 0%)
- B 1% or less in total of at least one selected from the group consisting of Cu, Ni, Cr and Mo (not including 0%)
- C 0.01% or less (excluding 0%) of at least one selected from the group consisting of Mg, Ca and REM
- V, Nb, and Zr 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, when the content of these elements is excessive, coarse carbides are formed, and the ductility is deteriorated by becoming the starting point of fracture. For these reasons, the total content of these elements 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%) in total. The following).
- Cu, Ni, Cr and Mo 1% or less in total (excluding 0%)
- Cu, Ni, Cr, and Mo suppress ferrite transformation, pearlite transformation, and bainite transformation, and thus prevent 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 0.5% or less (more preferably 0.3% or less) in total. ).
- a total of one or more selected from the group consisting of Mg, Ca and REM (rare earth elements) is 0.01% or less (excluding 0%)) Since these elements refine the inclusions, they effectively work to improve ductility. In order to exhibit these effects, it is preferable to contain 0.0001% or more in total. Considering only the characteristics, it is preferable that the content is large, but since the effect is saturated, the total content is preferably 0.01% or less.
- the more preferable lower limit of the content of these elements is 0.0002% or more (more preferably 0.0005% or more) in total, and the more preferable upper limit is 0.005% or less (more preferably 0.003% or less) in total. ).
- the Ti-containing precipitates and the control of the formula (1) are for preventing the softening of the HAZ, and are essentially necessary control in the molded product, but the change of these values before and after hot press molding is small. Therefore, it is necessary to already control at the stage before forming (steel plate for hot pressing).
- a Ti-containing precipitate can be maintained in a solid solution state or a fine state during heating by hot pressing. It becomes like this.
- the amount of precipitated Ti in the press-formed product can be controlled to a predetermined amount or less, and joint characteristics can be improved by preventing softening in the HAZ.
- the average equivalent circle diameter of those having an equivalent circle diameter of 30 nm or less is 6 nm or less.
- the equivalent circle diameter of the target Ti-containing precipitate is defined as 30 nm or less, except for TiN, which is coarsely formed in the melting stage and does not affect the structure change or properties thereafter. This is because it is necessary to control the Ti-containing precipitates.
- the size (average equivalent circle diameter) of the Ti-containing precipitate is preferably 5 nm or less, and more preferably 3 nm or less.
- the Ti-containing precipitates that are the subject of the present invention include TiC and TiN as well as precipitates containing Ti such as TiVC, TiNbC, TiVCN, and TiNbCN.
- the average equivalent circle diameter of Ti-containing precipitates in a press-formed product is specified to be 10 nm or less, whereas it is specified to be 6 nm or less before forming (hot-press steel plate). .
- the reason is that Ti is present in a fine precipitate or a solid solution state in the steel plate, but when heating for about 15 minutes or more near 800 ° C., the Ti-containing precipitate is slightly coarsened. Rather than the molded product, the size of the precipitate is defined larger.
- the average equivalent circle diameter of the Ti-containing precipitate is required to be 10 nm or less, and in order to realize the precipitation state with a hot stamped product, It is necessary that the average equivalent circle diameter of fine precipitates of 30 ⁇ m or less is 6 nm or less at the stage, and most of Ti is present in a solid solution state.
- the amount of Ti present as precipitates other than TiN is the remaining amount of 0.1% after subtracting the Ti forming TiN out of the total Ti.
- the amount needs to be less than 5 times (that is, 0.5 ⁇ [total Ti amount (mass%) ⁇ 3.4 [N]]) (requirement (B) above).
- the amount of precipitated Ti (mass%)-3.4 [N] is preferably 0.4 ⁇ [total Ti amount (mass%)-3.4 [N]] or less, more preferably 0.3 ⁇ [ The total Ti amount (% by mass) is -3.4 [N] or less.
- the ferrite fraction in the hot-press steel sheet needs to be 30 area% or more (requirement (C) above).
- the ferrite fraction is preferably 50 area% or more, more preferably 70 area% or more.
- the balance of the metal structure is not particularly limited, and examples thereof include at least one of pearlite, bainite, martensite, and retained austenite.
- a slab obtained by melting a steel material having the above chemical composition is heated at a temperature of 1100 ° C. or higher (preferably 1150 ° C. or higher), Hot rolling is performed at 1300 ° C. or lower (preferably 1250 ° C. or lower), and the finish rolling temperature is 850 ° C. or higher (preferably 900 ° C. or higher), or 1050 ° C. or lower (preferably 1000 ° C. or lower). (Preferably 625 ° C. or less) is cooled (rapidly cooled) at an average cooling rate of 20 ° C./second or more (preferably 30 ° C./second or more), and 620 ° C.
- 580 ° C. is 10 ° C./second or less (preferably 5 ° C. After cooling at an average cooling rate of 10 ° C./second or higher, then 350 ° C. or higher (preferably 380 ° C. or higher), 450 ° C. or lower (preferably 4 0 °C should be as winding below).
- the steel sheet for hot pressing having the chemical composition, the metal structure and the Ti precipitation state as described above may be used for the production of the hot press as it is, and the reduction ratio after pickling: 60% or less (preferably 40% The following may be applied to the production of a hot press after cold rolling.
- the steel sheet for hot pressing of the present invention may have a microstructure when the hot-rolled material is heat-treated in a continuous annealing furnace or a continuous hot dip galvanizing line. In short, as long as the required characteristics such as the metal structure and the Ti precipitation state are satisfied, it is included in the steel sheet for hot pressing of the present invention.
- a steel sheet containing a predetermined amount of ferrite it is necessary to control the heating temperature within a predetermined range in order to partially transform the ferrite into austenite while partially retaining the ferrite.
- the heating temperature of the steel sheet is less than the Ac 1 transformation point + 20 ° C., a sufficient amount of austenite cannot be obtained during heating, and a predetermined amount of retained austenite cannot be secured in the final structure (structure of the molded product). If the heating temperature of the steel sheet exceeds the Ac 3 transformation point of ⁇ 20 ° C., the amount of transformation to austenite increases too much during heating, and a predetermined amount of ferrite cannot be secured in the final structure (structure of the molded product).
- the average cooling rate and the cooling end temperature during and after molding are appropriately controlled. There is a need. From such a viewpoint, the average cooling rate during molding must be 20 ° C./second or more, and the cooling end temperature must be 100 ° C. or lower than the bainite transformation start temperature Bs.
- the average cooling rate during molding is preferably 30 ° C./second or more (more preferably 40 ° C./second or more). By making the cooling end temperature 100 ° C.
- the austenite existing during heating is transformed into bainite or martensite while preventing the formation of a structure such as ferrite or pearlite.
- a predetermined amount of retained austenite is secured by allowing fine austenite to remain between bainite and martensite lath while securing martensite.
- the cooling end temperature is higher than the temperature lower by 100 ° C. than the bainite transformation start temperature Bs or the average cooling rate is less than 20 ° C./second, a structure such as ferrite or pearlite is formed, and a predetermined amount of retained austenite is secured. This is not possible, and the elongation (ductility) of the molded product is deteriorated.
- the cooling end temperature is not particularly limited as long as it is 100 ° C. or lower than Bs, and may be, for example, martensitic transformation start temperature Ms or lower.
- control of the average cooling rate is basically unnecessary when the temperature is lower than the bainite transformation start temperature Bs by 100 ° C. or less, for example, at an average cooling rate of 1 ° C./second or more and 100 ° C./second or less to room temperature. It may be cooled.
- Control of the average cooling rate during molding and after molding is completed by controlling (a) the temperature of the molding die (cooling medium shown in FIG. 1) and (b) controlling the thermal conductivity of the die. It can be achieved by such means.
- a press-molded product single region molded product manufactured by hot pressing as described above
- the metal structure is retained austenite: 3 to 20 area%, ferrite: 30 to 80 area%, bainitic ferrite: 30 Less than area% (excluding 0 area%), martensite: 31 area% or less (excluding 0 area%), and a high level and uniform balance between high strength and elongation in the molded product It can be achieved.
- the reason for setting the range of each requirement (basic structure) in such a hot press-formed product is as follows.
- 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 retained austenite fraction needs to be 3 area% or more.
- the higher the retained austenite fraction the better.
- the retained austenite that can be secured is limited, and 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).
- the ductility (elongation) of a press-formed product can be increased by making the main structure fine and highly ductile ferrite. From this point of view, the ferrite fraction is 30% by area or more. However, if this fraction exceeds 80 area%, the strength of the molded product cannot be ensured.
- a preferred lower limit of the ferrite fraction is 35 area% or more (more preferably 40 area% or more), and a preferred upper limit is 75 area% or less (more preferably 70 area% or less).
- Bainitic ferrite is an effective structure for improving the strength of a molded product, but it is a structure that is slightly poor in ductility. From such a viewpoint, the fraction of bainitic ferrite is less than 30 area%. A preferable upper limit of the fraction of bainitic ferrite is 25 area% or less (more preferably 20 area% or less).
- Martensite (an as-quenched martensite) is an effective structure for improving the strength of a molded product, but is a structure having poor ductility, and therefore, when present in a large amount, it deteriorates elongation. From such a viewpoint, the martensite fraction is 31 area% or less. A preferred upper limit of the martensite fraction is 25 area% or less (more preferably 20 area% or less).
- pearlite may be included as the remaining structure.
- these structures have a lower contribution to strength and ductility than other structures, and it is preferable not to basically contain them. (It may be 0 area%).
- the equivalent of the average circle having an equivalent circle diameter of 30 nm or less is 10 nm or less.
- the average equivalent circle diameter of the Ti-containing precipitate is preferably 8 nm or less, and more preferably 6 nm or less.
- the amount of Ti present as precipitates other than TiN is the remainder after subtracting Ti that forms TiN out of all Ti.
- the Ti content is less than 0.5 times that of Ti (that is, less than 0.5 ⁇ [total Ti amount (%) ⁇ 3.4 [N]]).
- the deposited Ti amount-3.4 [N] is preferably 0.4 ⁇ [total Ti amount (mass%) ⁇ 3.4 [N]] or less, more preferably 0.3 ⁇ [total Ti amount ( % By mass) -3.4 [N]] or less.
- the properties such as strength and elongation of the press-formed product can be controlled by appropriately adjusting the press forming conditions (heating temperature and cooling rate) and high ductility. (Residual ductility) press-molded products can be obtained, so it can be applied to parts that have been difficult to apply with conventional press-molded products (for example, energy absorbing members). Useful.
- the heating temperature and the conditions of each region at the time of molding are appropriately controlled.
- a press-formed product that exhibits a strength-ductility balance corresponding to each region hereinafter sometimes referred to as a multi-region molded product
- the heating region of the steel plate is divided into at least two regions, one of which is hereinafter referred to as the first region. Is heated to a temperature not lower than Ac 3 transformation point and not higher than 950 ° C., and the other region (hereinafter referred to as second region) is not lower than Ac 1 transformation point + 20 ° C. and temperature not higher than Ac 3 transformation point ⁇ 20 ° C. Then, press molding is started for both the first and second regions, and during molding and after completion of molding, both the first and second regions have a temperature of 20 ° C./second or more in the mold. What is necessary is just to cool to the temperature below the martensitic transformation start temperature Ms, ensuring an average cooling rate.
- the heating region of the steel sheet is divided into at least two regions (high-strength side region and low-strength side region), and the manufacturing conditions are controlled according to each region, whereby the strength-ductility balance corresponding to each region is obtained.
- a press-formed product exhibiting the above can be obtained.
- the second region corresponds to the low-strength side region
- the manufacturing conditions, structure, and characteristics in this region are basically the same as those of the single-region molded product described above.
- manufacturing conditions for forming the other first region corresponding to the high-strength side region
- the heating temperature of the steel sheet is preferably Ac 3 transformation point + 50 ° C. or higher and 930 ° C. or lower.
- the average cooling rate and the cooling end temperature during and after molding are appropriately controlled. There is a need. From this point of view, the average cooling rate during molding needs to be 20 ° C./second or more, and the cooling end temperature needs to be lower than the martensite transformation start temperature (Ms point).
- the average cooling rate during molding is preferably 30 ° C./second or more (more preferably 40 ° C./second or more).
- the cooling end temperature is specifically 400 ° C. or lower, preferably 300 ° C. or lower.
- the metal structure and precipitates are different between the first region and the second region.
- the metal structures are retained austenite: 3 to 20 area% (the effect of retained austenite is the same as described above), and martensite: 80 area% or more.
- the same metal structure and Ti state average equivalent circle diameter of Ti-containing precipitates, amount of precipitated Ti (mass%) -3.4 [N], etc.) as the single region molded product are satisfied. .
- the area fraction of martensite needs to be 80 area% or more.
- the fraction of martensite is preferably 85 area% or more (more preferably 90 area% or more).
- the remaining structure in the first region may partially include ferrite, pearlite, bainite, and the like.
- Example 1 Steel materials (steel Nos. 1-16, 18-32) having the chemical composition shown in Tables 1 and 2 below are vacuum-melted to form experimental slabs, followed by hot rolling to obtain steel plates, and then The process which cooled and simulated winding was performed (plate
- the winding simulation processing method after cooling to the winding temperature, the sample was placed in a furnace heated to the winding temperature, held for 30 minutes, and then cooled in the furnace. The steel sheet manufacturing conditions at this time are shown in Tables 3 and 4 below.
- Treatment (1) After cold-rolling a hot-rolled steel sheet (sheet thickness: 1.6 mm), simulating continuous annealing with a heat treatment simulator, heating to 800 ° C., holding for 90 seconds, and average cooling at 20 ° C./second Cooled to 500 ° C. at a rate and held for 300 seconds.
- the obtained steel plate (press forming steel plate) was analyzed for the precipitation state of Ti and the observation of the metal structure (fraction of each structure) in the following manner. Moreover, the tensile strength (TS) of each steel plate was measured by the method mentioned later. The results are shown in Table 5 below together with a calculated value of 0.5 ⁇ [total Ti amount (mass%) ⁇ 3.4 [N]] [displayed as 0.5 ⁇ [total Ti amount-3.4 [N]]]. , 6.
- the amount of precipitated Ti (mass%)-3.4 [N] (the amount of Ti present as a precipitate) was subjected to extraction residue analysis using a mesh having a mesh diameter of 0.1 ⁇ m (in the extraction process, Precipitates aggregate and fine precipitates can be measured), and the amount of precipitated Ti (mass%)-3.4 [N] (in Tables 5 and 6, indicated as precipitated Ti amount-3.4 [N]) is obtained. It was. When the Ti-containing precipitate partially contains V or Nb, the content of these precipitates was also measured.
- the Ti precipitation state was analyzed by the method described above.
- the martensite (as-quenched martensite) fraction was determined by X-ray diffraction from the area ratio of the martensite and retained austenite as it was quenched by repeller corrosion of the steel sheet.
- the martensite fraction was calculated by subtracting the residual austenite fraction.
- Tables 8 and 9 The observation results of the metal structure (Ti precipitation state, fraction of each structure, amount of precipitated Ti-3.4 [N]) are shown in Tables 8 and 9 below.
- Table 10 shows the mechanical properties (tensile strength TS, elongation EL, TS ⁇ EL, and hardness reduction amount ⁇ Hv) of the molded product.
- the value of the precipitated Ti amount-3.4 [N] in the formed product is slightly different from the value of the precipitated Ti amount-3.4 [N] in the press-formed steel sheet, but this is a measurement error.
- Steel No. Those of 3, 7 to 9, 12 to 14, 18, and 22 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, Steel No. No. 3 uses a steel sheet for press forming with a low Si content, and the retained austenite fraction in the press-formed product is not ensured and elongation is not achieved, so that the strength-elongation balance deteriorates. ing. Steel No. No. 7 has a low finish rolling temperature at the time of manufacturing the steel sheet, the Ti-containing precipitates in the press forming steel sheet become coarse, and does not satisfy the relationship of formula (1) at any stage of the press forming steel sheet or the press formed product. The anti-softening property is deteriorated.
- Steel No. No. 8 has a high cooling rate of 620 ° C. to 580 ° C. at the time of manufacturing the steel sheet, the ferrite transformation does not proceed sufficiently, the ferrite fraction in the press forming steel sheet cannot be secured, and the strength becomes high. It is expected that molding and processing before press molding will be difficult.
- Steel No. In No. 9 the coiling temperature at the time of manufacturing the steel sheet is high, and the Ti-containing precipitates in the steel sheet for press forming are coarsened. When press forming using such a steel sheet, the forming conditions are appropriate and the strength- Even if the ductility balance is good, the anti-softening property is deteriorated.
- Steel No. No. 14 has a high cooling end temperature during press molding, pearlite is generated, retained austenite cannot be secured, strength and elongation are lowered, and strength-elongation balance (TS ⁇ EL) is deteriorated.
- Steel No. No. 18 uses a steel sheet for press forming with an excessive C content, the ferrite fraction of the steel sheet cannot be secured, the ferrite fraction in the press-formed product cannot be secured, and only a low elongation EL is obtained. The strength-elongation balance (TS ⁇ EL) is also deteriorated.
- Example 2 Steel materials (steel Nos. 33 to 37) having the chemical composition shown in Table 11 below were melted in vacuum to form experimental slabs, followed by hot rolling, followed by cooling and winding (sheet thickness) : 3.0 mm). The steel plate production conditions at this time are shown in Table 12 below.
- each steel sheet (3.0mm t ⁇ 150mm ⁇ 200mm) was heated to a predetermined temperature in a heating furnace, performing a press-forming and cooling process in a mold of hat-shaped (FIG. 1), and a molded article .
- the steel sheet is placed in an infrared furnace, and the portion (the steel plate portion corresponding to the first region) to be strengthened is directly irradiated with infrared rays so that the portion can be heated at a high temperature.
- the steel plate portion corresponding to the region of (1) was covered with a cover so as to block a part of infrared rays so that it could be heated at a low temperature, thereby giving a heating temperature difference. Therefore, the molded product has regions having different strengths within a single part.
- Table 14 shows the press molding conditions (heating temperature, average cooling rate, rapid cooling end temperature in each region during press molding).
- Table 15 shows the observation results of metal structures (fraction of each structure) and the analysis results of the precipitation state of Ti.
- the mechanical properties (tensile strength TS, elongation EL, TS ⁇ EL, and hardness reduction amount ⁇ Hv) of the press-formed product are shown in Table 16 below.
- the tensile strength (TS) on the high strength side is 1470 MPa or higher
- the elongation (EL) satisfies 8% or higher
- the strength-elongation balance (TS ⁇ EL) is 14000 (MPa ⁇ %) or higher.
- Steel No. Nos. 33 to 36 are examples that satisfy the requirements defined in the present invention, and it can be seen that press-formed products having a good strength-ductility balance in each region are obtained.
- Steel No. In No. 37 the heating temperature at the time of press molding is low, the martensite fraction on the high strength side is insufficient, and the strength on the high strength side is reduced (the strength difference from the low strength side is Less than 300 MPa).
- the average equivalent circle diameter of those having an equivalent circle diameter of 30 nm or less is 6 nm or less, and the amount of precipitated Ti in the steel And the total Ti content satisfy a predetermined relationship, and the metal structure has a ferrite fraction of 30% by area or more, so that molding and processing can be easily performed before hot pressing, and in the molded product.
- a press-molded product that can achieve a high level of balance between strength and elongation can be obtained, and the area corresponding to the impact-resistant and energy-absorbing sites in a single molded product. Is required, it is possible to achieve a high level of balance between high strength and elongation according to each region, and hot press useful for obtaining a press-molded product with good softening prevention properties in HAZ. Steel sheet can be realized.
Abstract
Description
C :0.15~0.5%(質量%の意味。以下、化学成分組成について同じ。)、
Si:0.2~3%、
Mn:0.5~3%、
P :0.05%以下(0%を含まない)、
S :0.05%以下(0%を含まない)、
Al:0.01~1%、
B :0.0002~0.01%、
Ti:3.4[N]+0.01%以上、3.4[N]+0.1%以下(但し、[N]はNの含有量(質量%)を示す)、および
N:0.0010~0.01%、
を夫々含有し、残部が鉄および不可避不純物からなり、
鋼板中に含まれるTi含有析出物のうち、円相当直径が30nm以下のものの平均円相当直径が6nm以下であると共に、鋼中の析出Ti量と全Ti量とが下記(1)式の関係を満足し、且つ、金属組織が、フェライトの分率が30面積%以上であることを特徴とする。尚、「円相当直径」とは、Ti含有析出物(例えばTiC)の大きさ(面積)に着目したときに、同一面積の円に換算したときの直径(「平均円相当直径」はその平均値)である。
析出Ti量(質量%)-3.4[N]<0.5×[全Ti量(質量%)-3.4[N]] …(1)
((1)式中、[N]は鋼中のNの含有量(質量%)を示す) The steel sheet for hot pressing of the present invention that was able to achieve the above object,
C: 0.15 to 0.5% (meaning mass%, hereinafter the same for chemical composition)
Si: 0.2-3%,
Mn: 0.5 to 3%,
P: 0.05% or less (excluding 0%),
S: 0.05% or less (excluding 0%),
Al: 0.01 to 1%,
B: 0.0002 to 0.01%,
Ti: 3.4 [N] + 0.01% or more, 3.4 [N] + 0.1% or less (where [N] indicates the content (% by mass) of N), and N: 0.0010 ~ 0.01%,
Each of which contains iron and inevitable impurities,
Among the Ti-containing precipitates contained in the steel sheet, the average equivalent circle diameter of those having an equivalent circle diameter of 30 nm or less is 6 nm or less, and the relationship between the precipitated Ti amount in the steel and the total Ti amount in the following formula (1) And the metal structure is characterized in that the ferrite fraction is 30 area% or more. The “equivalent circle diameter” means the diameter when converted to a circle of the same area when focusing on the size (area) of the Ti-containing precipitate (eg, TiC) (the “average equivalent circle diameter” is its average Value).
Precipitated Ti amount (mass%)-3.4 [N] <0.5 × [Total Ti amount (mass%)-3.4 [N]] (1)
(In the formula (1), [N] indicates the content (% by mass) of N in the steel)
(a)V,NbおよびZrよりなる群から選択される1種以上を合計で0.1%以下(0%を含まない)
(b)Cu,Ni,CrおよびMoよりなる群から選択される1種以上を合計で1%以下(0%を含まない)
(c)Mg,CaおよびREMよりなる群から選択される1種以上を合計で0.01%以下(0%を含まない) In the hot press-forming steel sheet of the present invention, it is also useful to contain at least one of the following (a) to (c) as other elements as required. Depending on the type of element contained as required, the properties of the press-formed product are further improved.
(A) 0.1% or less in total of one or more selected from the group consisting of V, Nb and Zr (excluding 0%)
(B) 1% or less in total of at least one selected from the group consisting of Cu, Ni, Cr and Mo (not including 0%)
(C) 0.01% or less (excluding 0%) of at least one selected from the group consisting of Mg, Ca and REM
析出Ti量(質量%)-3.4[N]<0.5×[全Ti量(質量%)-3.4[N]] …(1)
((1)式中、[N]は鋼中のNの含有量(質量%)を示す) In the press-formed product of the present invention, the metal structure of the press-formed product is as follows: retained austenite: 3 to 20 area%, ferrite: 30 to 80 area%, bainitic ferrite: less than 30 area% (excluding 0 area%) Martensite: 31 area% or less (excluding 0 area%), and among the Ti-containing precipitates contained in the press-formed product, the average equivalent circle diameter of the equivalent circle diameter of 30 nm or less is 10 nm or less. The amount of precipitated Ti in the steel and the total amount of Ti satisfy the relationship of the following formula (1), and the balance between high strength and elongation can be achieved as a uniform characteristic at a high level in the molded product.
Precipitated Ti amount (mass%)-3.4 [N] <0.5 × [Total Ti amount (mass%)-3.4 [N]] (1)
(In the formula (1), [N] indicates the content (% by mass) of N in the steel)
析出Ti量(質量%)-3.4[N]<0.5×[全Ti量(質量%)-3.4[N]] …(1)
((1)式中、[N]は鋼中のNの含有量(質量%)を示す) Another press-formed product of the present invention is a steel plate press-formed product having the chemical composition as described above, and the press-formed product has a metal structure of retained austenite: 3 to 20 area%, martensite: The first region is 80 area% or more, and the metal structure is retained austenite: 3 to 20 area%, ferrite: 30 to 80 area%, bainitic ferrite: less than 30 area% (excluding 0 area%) , Martensite: having a second region that is 31 area% or less (not including 0 area%), and among the Ti-containing precipitates contained in the steel of this second region, the equivalent circle diameter is The average equivalent circle diameter of those having a thickness of 30 nm or less is 10 nm or less, and the amount of precipitated Ti in the steel and the total amount of Ti satisfy the relationship of the following formula (1). In such a press-molded product, a balance between high strength and elongation can be achieved at a high level according to each region, and there are regions corresponding to impact-resistant sites and energy-absorbing sites in a single molded product. The softening prevention property of the HAZ when spot welding is performed in the second region is good.
Precipitated Ti amount (mass%)-3.4 [N] <0.5 × [Total Ti amount (mass%)-3.4 [N]] (1)
(In the formula (1), [N] indicates the content (% by mass) of N in the steel)
Cは、プレス成形品内で均一な特性が要求される場合の高強度と伸びのバランスを高レベルで達成するために、或は単一成形品内に耐衝撃部位とエネルギー吸収部位に相当する領域が要求される場合の、特に低強度・高延性部位において残留オーステナイトを確保する上で重要な元素である。また熱間プレス成形での加熱時に、Cがオーステナイトに濃化することで、焼入れ後に残留オーステナイトを形成させることができる。更に、マルテンサイト量の増加にも寄与し、強度を上昇させる。これらの効果を発揮させるためには、C含有量は0.15%以上とする必要がある。 (C: 0.15-0.5%)
C corresponds to an impact resistant site and an energy absorbing site in a single molded product in order to achieve a high balance between high strength and elongation when uniform properties are required in a press molded product. It is an important element for securing retained austenite when a region is required, particularly in a low strength / high ductility region. Moreover, at the time of heating by hot press molding, C concentrates to austenite, so that residual austenite can be formed after quenching. Furthermore, it contributes to an increase in the amount of martensite and raises the strength. In order to exert these effects, the C content needs to be 0.15% or more.
Siは、金型焼入れの冷却中にマルテンサイトが焼戻されてセメンタイトが形成されたり、未変態のオーステナイトが分解されることを抑制することで、残留オーステナイトを形成させる効果を発揮する。こうした効果を発揮させるためには、Si含有量は0.2%以上とする必要がある。またSi含有量が過剰になって3%を超えると、熱間圧延後の冷却中にフェライト変態が促進されるようになるため、その際に形成されるフェライト中のTiCが粗大に形成されやすくなり、HAZ軟化防止特性が得られなくなる。Si含有量の好ましい下限は0.5%以上(より好ましくは1.0%以上)であり、好ましい上限は2.5%以下(より好ましくは2.0%以下)である。 (Si: 0.2-3%)
Si exhibits the effect of forming retained austenite by suppressing martensite from tempering to form cementite and decomposition of untransformed austenite during cooling of mold quenching. In order to exert such effects, the Si content needs to be 0.2% or more. Further, if the Si content is excessive and exceeds 3%, ferrite transformation is promoted during cooling after hot rolling, so that TiC in the ferrite formed at that time is easily formed coarsely. Therefore, the HAZ softening preventing property cannot be obtained. The preferable lower limit of the Si content is 0.5% or more (more preferably 1.0% or more), and the preferable upper limit is 2.5% or less (more preferably 2.0% or less).
Mnは、焼入れ性を高め、金型焼入れの冷却中のマルテンサイト、残留オーステナイト以外の組織(フェライト、パーライト、ベイナイト等)の形成を抑制するのに有効な元素である。また、オーステナイトを安定化させる元素であり、残留オーステナイト量の増加に寄与する元素である。こうした効果を発揮させるためには、Mnは0.5%以上含有させる必要がある。特性だけを考慮した場合は、Mn含有量は多い方が好ましいが、合金添加のコストが上昇することから、上限を3%以下とした。Mn含有量の好ましい下限は0.7%以上(より好ましくは1.0%以上)であり、好ましい上限は2.5%以下(より好ましくは2.0%以下)である。 (Mn: 0.5-3%)
Mn is an element effective in enhancing hardenability and suppressing the formation of structures (ferrite, pearlite, bainite, etc.) other than martensite and retained austenite during cooling of mold hardening. Further, it is an element that stabilizes austenite and contributes to an increase in the amount of retained austenite. In order to exhibit such an effect, it is necessary to contain 0.5% or more of Mn. When only the characteristics are taken into consideration, it is preferable that the Mn content is high, but the upper limit is made 3% or less because the cost of alloy addition increases. The minimum with preferable Mn content is 0.7% or more (more preferably 1.0% or more), and a preferable upper limit is 2.5% or less (more preferably 2.0% or less).
Pは、鋼中に不可避的に含まれる元素であるが、延性を劣化させるので、Pは極力低減することが好ましい。しかしながら、極端な低減は製鋼コストの増大を招き、0%とすることは製造上困難であるので、上限を0.05%以下(0%を含まない)とした。P含有量の好ましい上限は0.045%以下(より好ましくは0.040%以下)である。 (P: 0.05% or less (excluding 0%))
P is an element inevitably contained in the steel, but it deteriorates ductility, so P is preferably reduced as much as possible. However, extreme reduction leads to an increase in steelmaking cost, and it is difficult to make it 0%, so the upper limit was made 0.05% or less (excluding 0%). The upper limit with preferable P content is 0.045% or less (more preferably 0.040% or less).
SもPと同様に鋼中に不可避的に含まれる元素であり、延性を劣化させるので、Sは極力低減することが好ましい。しかしながら、極端な低減は製鋼コストの増大を招き、0%とすることは製造上困難であるので、上限を0.05%以下(0%を含まない)とした。S含有量の好ましい上限は0.045%以下(より好ましくは0.040%以下)である。 (S: 0.05% or less (excluding 0%))
Similarly to P, S is an element inevitably contained in steel, and deteriorates ductility. Therefore, S is preferably reduced as much as possible. However, extreme reduction leads to an increase in steelmaking cost, and it is difficult to make it 0%, so the upper limit was made 0.05% or less (excluding 0%). The upper limit with preferable S content is 0.045% or less (more preferably 0.040% or less).
Alは、脱酸元素として有用であると共に、鋼中に存在する固溶NをAlNとして固定し、延性の向上に有用である。こうした効果を有効に発揮させるためには、Al含有量は0.01%以上とする必要がある。しかしながら、Al含有量が過剰になって1%を超えると、Al2O3が過剰に生成し、延性を劣化させる。Al含有量の好ましい下限は0.02%以上(より好ましくは0.03%以上)であり、好ましい上限は0.8%以下(より好ましくは0.6%以下)である。 (Al: 0.01-1%)
Al is useful as a deoxidizing element, and also fixes solid solution N present in steel as AlN, which is useful for improving ductility. In order to exhibit such an effect effectively, the Al content needs to be 0.01% or more. However, when the Al content becomes excessive and exceeds 1%, Al 2 O 3 is excessively generated and ductility is deteriorated. The preferable lower limit of the Al content is 0.02% or more (more preferably 0.03% or more), and the preferable upper limit is 0.8% or less (more preferably 0.6% or less).
Bは、高強度部位側でフェライト変態、パーライト変態およびベイナイト変態を抑制する作用を有するため、(Ac1変態点~Ac3変態点)の二相域温度に加熱後の冷却中に、フェライト、パーライト、ベイナイトの形成を防止し、残留オーステナイトの確保に寄与する元素である。こうした効果を発揮させるためには、Bは0.0002%以上含有させる必要があるが、0.01%を超えて過剰に含有させても効果が飽和する。B含有量の好ましい下限は0.0003%以上(より好ましくは0.0005%以上)であり、好ましい上限は0.008%以下(より好ましくは0.005%以下)である。 (B: 0.0002 to 0.01%)
B has an action of suppressing ferrite transformation, pearlite transformation, and bainite transformation on the high-strength portion side, so that during the cooling after heating to the two-phase region temperature (Ac 1 transformation point to Ac 3 transformation point), It is an element that prevents the formation of pearlite and bainite and contributes to securing retained austenite. In order to exert such an effect, B needs to be 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 preferable lower limit of the B content is 0.0003% or more (more preferably 0.0005% or more), and a preferable upper limit is 0.008% or less (more preferably 0.005% or less).
Tiは、Nを固定し、Bを固溶状態で維持させることで焼入れ性の改善効果を発現させる。こうした効果を発揮させるためには、TiとNの化学量論比(Nの含有量の3.4倍)よりも0.01%以上多く含有させることが重要である。またNに対して過剰に添加されたTiをホットスタンプ成形品内に固溶状態で存在させ、且つ析出した化合物を微細に分散させておくことによって、ホットスタンプ成形品を溶接した際に固溶したTiがTiCとして形成されることによる析出強化や、TiCによる転位の移動防止効果による転位密度の増加遅延等の効果により、HAZにおける強度低下が抑制できる。但し、Ti含有量が過剰になって3.4[N]+0.1%よりも多くなると、形成されるTi含有析出物(例えばTiN)が粗大化され、鋼板の延性が低下する。Ti含有量のより好ましい下限は、3.4[N]+0.02%以上(更に好ましくは3.4[N]+0.05%以上)であり、より好ましい上限は、3.4[N]+0.09%以下(更に好ましくは3.4[N]+0.08%以下)である。 (Ti: 3.4 [N] + 0.01% or more, 3.4 [N] + 0.1% or less: [N] is N content (mass%))
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 important to contain 0.01% or more than the stoichiometric ratio of Ti and N (3.4 times the N content). Further, Ti added excessively to N is present in a solid solution state in the hot stamping molded product, and the precipitated compound is dispersed finely, so that the solid solution is dissolved when the hot stamping molded product is welded. Strength reduction in HAZ can be suppressed by effects such as precipitation strengthening due to the formation of Ti as TiC and an increase delay of dislocation density due to the effect of preventing dislocation movement due to TiC. However, when the Ti content becomes excessive and exceeds 3.4 [N] + 0.1%, the Ti-containing precipitates formed (for example, TiN) are coarsened and the ductility of the steel sheet is lowered. The more preferable lower limit of the Ti content is 3.4 [N] + 0.02% or more (more preferably 3.4 [N] + 0.05% or more), and the more preferable upper limit is 3.4 [N]. + 0.09% or less (more preferably 3.4 [N] + 0.08% or less).
Nは、不可避的に混入する元素であり、できるだけ低減することが好ましいが、実プロセスの中で低減するには限界があるため、0.001%を下限とした。また、N含有量が過剰になると、形成されるTi含有析出物(例えばTiN)が粗大化され、この析出物が破壊の起点として働き、鋼板の延性を低下させるため、上限を0.01%とした。N含有量のより好ましい上限は0.008%以下(更に好ましくは0.006%以下)である。 (N: 0.001 to 0.01%)
N is an element inevitably mixed in and is preferably reduced as much as possible. However, since there is a limit to reducing it in the actual process, 0.001% was set as the lower limit. Further, when the N content is excessive, the Ti-containing precipitates formed (for example, TiN) are coarsened, and the precipitates act as a starting point for fracture and reduce the ductility of the steel sheet. It was. The upper limit with more preferable N content is 0.008% or less (more preferably 0.006% or less).
(a)V,NbおよびZrよりなる群から選択される1種以上を合計で0.1%以下(0%を含まない)
(b)Cu,Ni,CrおよびMoよりなる群から選択される1種以上を合計で1%以下(0%を含まない)
(c)Mg,CaおよびREMよりなる群から選択される1種以上を合計で0.01%以下(0%を含まない) The basic chemical components in the steel sheet for hot pressing of the present invention are as described above, and the balance is iron and inevitable impurities (for example, O, H, etc.) other than P, S, and N. In addition, it is useful that the steel sheet for hot pressing according to the present invention further contains at least one of the following (a) to (c) if necessary. Depending on the type of element contained as necessary, the properties of the steel sheet for hot pressing (ie, press-formed product) are further improved. The preferable range when these elements are contained and the reason for limiting the range are as follows.
(A) 0.1% or less in total of one or more selected from the group consisting of V, Nb and Zr (excluding 0%)
(B) 1% or less in total of at least one selected from the group consisting of Cu, Ni, Cr and Mo (not including 0%)
(C) 0.01% or less (excluding 0%) of at least one selected from the group consisting of Mg, Ca and REM
V,NbおよびZrは、微細な炭化物を形成し、ピン止め効果により組織を微細にする効果がある。こうした効果を発揮させるためには、合計で0.001%以上含有させることが好ましい。しかしながら、これらの元素の含有量が過剰になると、粗大な炭化物が形成され、破壊の起点になることで逆に延性を劣化させる。こうしたことから、これらの元素は合計で0.1%以下とすることが好ましい。これらの元素の含有量のより好ましい下限は合計で0.005%以上(更に好ましくは0.008%以上)であり、より好ましい上限は合計で0.08%以下(更に好ましくは0.06%以下)である。 (A total of one or more selected from the group consisting of V, Nb and Zr is 0.1% or less (excluding 0%))
V, Nb, and Zr 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, when the content of these elements is excessive, coarse carbides are formed, and the ductility is deteriorated by becoming the starting point of fracture. For these reasons, the total content of these elements 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%) in total. The following).
Cu,Ni,CrおよびMoは、フェライト変態、パーライト変態およびベイナイト変態を抑制するため、加熱後の冷却中に、フェライト、パーライト、ベイナイトの形成を防止し、残留オーステナイトの確保に有効に作用する。こうした効果を発揮させるためには、合計で0.01%以上含有させることが好ましい。特性だけを考慮すると含有量は多い方が好ましいが、合金添加のコストが上昇することから、合計で1%以下とすることが好ましい。また、オーステナイトの強度を大幅に高める作用を有するため、熱間圧延の負荷が大きくなり、鋼板の製造が困難になるため、製造性の観点からも1%以下とすることが好ましい。これらの元素含有量のより好ましい下限は合計で0.05%以上(更に好ましくは0.06%以上)であり、より好ましい上限は合計で0.5%以下(更に好ましくは0.3%以下)である。 (One or more selected from the group consisting of Cu, Ni, Cr and Mo: 1% or less in total (excluding 0%))
Cu, Ni, Cr, and Mo suppress ferrite transformation, pearlite transformation, and bainite transformation, and thus prevent formation of ferrite, pearlite, and bainite during cooling after heating, and effectively act to secure retained austenite. In order to exhibit such an effect, it is preferable to contain 0.01% or more in total. Considering only the characteristics, it is preferable that the content is large. However, since the cost of alloy addition increases, the total content is preferably 1% or less. Moreover, since it has the effect | action which raises the intensity | strength of austenite significantly, since the load of hot rolling becomes large and manufacture of a steel plate becomes difficult, it is preferable to set it as 1% or less also from a viewpoint of productivity. 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 0.5% or less (more preferably 0.3% or less) in total. ).
これらの元素は、介在物を微細化するため、延性向上に有効に作用する。こうした効果を発揮させるためには、合計で0.0001%以上含有させることが好ましい。特性だけを考慮すると含有量は多い方が好ましいが、効果が飽和することから、合計で0.01%以下とすることが好ましい。これらの元素含有量のより好ましい下限は合計で0.0002%以上(更に好ましくは0.0005%以上)であり、より好ましい上限は合計で0.005%以下(更に好ましくは0.003%以下)である。 (A total of one or more selected from the group consisting of Mg, Ca and REM (rare earth elements) is 0.01% or less (excluding 0%))
Since these elements refine the inclusions, they effectively work to improve ductility. In order to exhibit these effects, it is preferable to contain 0.0001% or more in total. Considering only the characteristics, it is preferable that the content is large, but since the effect is saturated, the total content is preferably 0.01% or less. The more preferable lower limit of the content of these elements is 0.0002% or more (more preferably 0.0005% or more) in total, and the more preferable upper limit is 0.005% or less (more preferably 0.003% or less) in total. ).
プレス成形品の組織を適切に調整するためには、加熱温度は所定の範囲に制御する必要がある。この加熱温度を適切に制御することによって、その後の冷却過程で、所定量の残留オーステナイトを確保しつつ、マルテンサイトを主体とする組織に変態させ、最終的な熱間プレス成形品の領域内で所望の組織に作り込むことができる。この領域での鋼板加熱温度がAc3変態点未満であると、加熱時に十分な量のオーステナイトが得られず、最終組織(成形品の組織)で所定量の残留オーステナイトを確保できない。また、鋼板の加熱温度が950℃を超えると、加熱時にオーステナイトの粒径が大きくなり、マルテンサイト変態開始温度(Ms点)およびマルテンサイト変態終了温度(Mf点)が上昇し、焼入れ時に残留オーステナイトを確保できず、良好な成形性が達成されない。鋼板の加熱温度は、好ましくはAc3変態点+50℃以上であり、930℃以下である。 (Production conditions for the first region and the high-strength side region)
In order to appropriately adjust the structure of the press-formed product, it is necessary to control the heating temperature within a predetermined range. By appropriately controlling this heating temperature, in the subsequent cooling process, while maintaining a predetermined amount of retained austenite, it is transformed into a structure mainly composed of martensite, and within the region of the final hot press-formed product. It can be built into the desired tissue. If the steel sheet heating temperature in this region is less than the Ac 3 transformation point, a sufficient amount of austenite cannot be obtained during heating, and a predetermined amount of retained austenite cannot be secured in the final structure (structure of the molded product). If the heating temperature of the steel sheet exceeds 950 ° 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 residual austenite during quenching. Cannot be secured, and good moldability is not achieved. The heating temperature of the steel sheet is preferably Ac 3 transformation point + 50 ° C. or higher and 930 ° C. or lower.
下記表1、2に示した化学成分組成を有する鋼材(鋼No.1~16、18~32)を真空溶製し、実験用スラブとした後、熱間圧延を行って鋼板とし、その後に冷却して巻取りを模擬した処理を施した(板厚:1.6mmm若しくは3.0mm)。巻取り模擬処理方法は、巻取り温度まで冷却後、巻取り温度に加熱した炉に試料を入れ、30分保持した後炉冷した。このときの鋼板製造条件を下記表3、4に示す。尚、表1、2中のAc1変態点、Ac3変態点、Ms点およびBs点は、下記の(2)式~(5)式を用いて求めたものである(例えば、「レスリー鉄鋼材料学」丸善,(1985)参照)。また、表3の備考欄に示した処理(1)、(2)は、下記に示す各処理(圧延、冷却、合金化)を行ったものである。 [Example 1]
Steel materials (steel Nos. 1-16, 18-32) having the chemical composition shown in Tables 1 and 2 below are vacuum-melted to form experimental slabs, followed by hot rolling to obtain steel plates, and then The process which cooled and simulated winding was performed (plate | board thickness: 1.6 mm or 3.0 mm). In the winding simulation processing method, after cooling to the winding temperature, the sample was placed in a furnace heated to the winding temperature, held for 30 minutes, and then cooled in the furnace. The steel sheet manufacturing conditions at this time are shown in Tables 3 and 4 below. In Tables 1 and 2, the Ac 1 transformation point, Ac 3 transformation point, Ms point, and Bs point were determined using the following formulas (2) to (5) (for example, “Leslie Steel) Materials Science, Maruzen, (1985)). Further, the treatments (1) and (2) shown in the remarks column of Table 3 are obtained by performing the following treatments (rolling, cooling, and alloying).
Ac3変態点(℃)=910-203×[C]1/2+44.7×[Si]-30×[Mn]+700×[P]+400×[Al]+400×[Ti]+104×[V]-11×[Cr]+31.5×[Mo]-20×[Cu]-15.2×[Ni] …(3)
Ms点(℃)=550-361×[C]-39×[Mn]-10×[Cu]-17×[Ni]-20×[Cr]-5×[Mo]+30×[Al] …(4)
Bs点(℃)=830-270×[C]-90×[Mn]-37×[Ni]-70×[Cr]-83×[Mo] …(5)
但し、[C],[Si],[Mn],[P],[Al],[Ti],[V],[Cr],[Mo],[Cu]および[Ni]は、夫々C,Si,Mn,P,Al,Ti,V,Cr,Mo,CuおよびNiの含有量(質量%)を示す。また、上記(2)式~(5)式の各項に示された元素が含まれない場合は、その項がないものとして計算する。 Ac 1 transformation point (° C.) = 723 + 29.1 × [Si] −10.7 × [Mn] + 16.9 × [Cr] −16.9 [Ni] (2)
Ac 3 transformation point (° C.) = 910−203 × [C] 1/2 + 44.7 × [Si] −30 × [Mn] + 700 × [P] + 400 × [Al] + 400 × [Ti] + 104 × [V ] -11 × [Cr] + 31.5 × [Mo] −20 × [Cu] −15.2 × [Ni] (3)
Ms point (° C.) = 550−361 × [C] −39 × [Mn] −10 × [Cu] −17 × [Ni] −20 × [Cr] −5 × [Mo] + 30 × [Al] ( 4)
Bs point (° C.) = 830−270 × [C] −90 × [Mn] −37 × [Ni] −70 × [Cr] −83 × [Mo] (5)
However, [C], [Si], [Mn], [P], [Al], [Ti], [V], [Cr], [Mo], [Cu] and [Ni] are C, The contents (mass%) of Si, Mn, P, Al, Ti, V, Cr, Mo, Cu and Ni are shown. Further, when the element shown in each term of the above formulas (2) to (5) is not included, the calculation is made assuming that the term is not present.
処理(2):熱間圧延鋼板を冷間圧延後(板厚:1.6mm)、熱処理シミュレータで連続溶融亜鉛めっきラインを模擬するため860℃に加熱した後、30℃/秒の平均冷却速度で400℃まで冷却し、保持後、めっき浴への浸漬-合金化処理を模擬するために更に500℃×10秒保持後、20℃/秒の平均冷却速度で室温まで冷却した。 Treatment (1): After cold-rolling a hot-rolled steel sheet (sheet thickness: 1.6 mm), simulating continuous annealing with a heat treatment simulator, heating to 800 ° C., holding for 90 seconds, and average cooling at 20 ° C./second Cooled to 500 ° C. at a rate and held for 300 seconds.
Treatment (2): After cold rolling a hot-rolled steel sheet (sheet thickness: 1.6 mm), after heating to 860 ° C. to simulate a continuous hot-dip galvanizing line with a heat treatment simulator, an average cooling rate of 30 ° C./second The sample was cooled to 400 ° C., held, and then held at 500 ° C. for 10 seconds to simulate immersion-alloying treatment in a plating bath, and then cooled to room temperature at an average cooling rate of 20 ° C./second.
抽出レプリカサンプルを作製し、透過型電子顕微鏡(TEM)にてTi含有析出物の透過型電子顕微鏡像(倍率:10万倍)を撮影した。このとき、エネルギー分散型X線分光器(EDX)により析出物の組成分析をすることによって、Ti含有析出物(円相当直径で30nm以下のもの)を特定した。少なくとも100個以上のTi含有析出物の面積を画像解析により測定し、そこから円相当直径を求め、その平均値を析出物サイズ(Ti含有析出物の平均円相当直径)とした。また、析出Ti量(質量%)-3.4[N](析出物として存在するTi量)は、メッシュ径:0.1μmのメッシュを用いて抽出残渣分析を行い(抽出処理の際に、析出物が凝集して微細な析出物も測定できる)、析出Ti量(質量%)-3.4[N](表5、6では析出Ti量-3.4[N]と表示)を求めた。尚、Ti含有析出物がVやNbを一部含有している場合は、これらの析出物の含有量についても測定した。 (Analysis of Ti precipitation state of steel sheet)
An extraction replica sample was prepared, and a transmission electron microscope image (magnification: 100,000 times) of the Ti-containing precipitate was taken with a transmission electron microscope (TEM). At this time, Ti-containing precipitates (those with an equivalent circle diameter of 30 nm or less) were identified by analyzing the composition of the precipitates using an energy dispersive X-ray spectrometer (EDX). The area of at least 100 Ti-containing precipitates was measured by image analysis, the equivalent circle diameter was determined therefrom, and the average value was defined as the precipitate size (average equivalent circle diameter of the Ti-containing precipitate). Further, the amount of precipitated Ti (mass%)-3.4 [N] (the amount of Ti present as a precipitate) was subjected to extraction residue analysis using a mesh having a mesh diameter of 0.1 μm (in the extraction process, Precipitates aggregate and fine precipitates can be measured), and the amount of precipitated Ti (mass%)-3.4 [N] (in Tables 5 and 6, indicated as precipitated Ti amount-3.4 [N]) is obtained. It was. When the Ti-containing precipitate partially contains V or Nb, the content of these precipitates was also measured.
(1)鋼板中のフェライト、ベイニティッフェライト、パーライト、マルテンサイトの組織については、鋼板をナイタールで腐食し、SEM(倍率:1000倍または2000倍)観察により、フェライト、ベイニティッフェライト、パーライト、マルテンサイトを区別し、夫々の分率(面積率)を求めた。
(2)鋼板中の残留オーステナイト分率は、鋼板の1/4の厚さまで研削した後、化学研磨してからX線回折法によって測定した(例えば、ISJJ Int.Vol.33.(1933),No.7,P.776)。 (Observation of metal structure (fraction of each structure))
(1) Regarding the structure of ferrite, bainitic ferrite, pearlite, and martensite in the steel plate, the steel plate is corroded with nital, and the ferrite, bainitic ferrite, pearlite are observed by SEM (magnification: 1000 times or 2000 times) observation. The martensite was distinguished and the respective fractions (area ratios) were determined.
(2) The retained austenite fraction in the steel sheet was measured by X-ray diffraction after being ground to ¼ thickness of the steel sheet and then chemically polished (for example, ISJJ Int. Vol. 33. (1933), No. 7, P.776).
JIS5号試験片を用いて引張試験を行い、引張強度(TS)、伸び(EL)を測定した。このとき、引張試験の歪速度:10mm/秒とした。本発明では、引張強度(TS)が980MPa以上で伸び(EL)が16%以上を満足し、強度-伸びバランス(TS×EL)が16000(MPa・%)以上のときに合格と評価した。 (Measurement of tensile strength (TS) and elongation (total elongation EL))
A tensile test was performed using a JIS No. 5 test piece, and tensile strength (TS) and elongation (EL) were measured. At this time, the strain rate of the tensile test was set to 10 mm / second. In the present invention, when the tensile strength (TS) was 980 MPa or more and the elongation (EL) was 16% or more, and the strength-elongation balance (TS × EL) was 16000 (MPa ·%) or more, it was evaluated as passing.
(1)鋼板中のフェライト、ベイニティックフェライト、パーライトの組織については、鋼板をナイタールで腐食し、SEM(倍率:1000倍または2000倍)観察により、フェライト、ベイニティックフェライト、パーライトを区別し(フェライトと針状フェライトの区別も含む)、夫々の分率(面積率)を求めた。
(2)鋼板中の残留オーステナイト分率は、鋼板の1/4の厚さまで研削した後、化学研磨してからX線回折法によって測定した(例えば、ISJJ Int.Vol.33.(1933),No.7,P.776)。
(3)マルテンサイト(焼入れままマルテンサイト)分率については、鋼板をレペラ腐食し、白いコントラストを焼入れままマルテンサイトと残留オーステナイトの混合組織として面積率を測定し、そこからX線回折により求めた残留オーステナイト分率を差し引いて、マルテンサイト分率を計算した。 (Observation of metal structure (fraction of each structure))
(1) Regarding the structure of ferrite, bainitic ferrite and pearlite in the steel sheet, the steel sheet is corroded with nital, and ferrite, bainitic ferrite and pearlite are distinguished by SEM (magnification: 1000 times or 2000 times) observation. (Including the distinction between ferrite and acicular ferrite), each fraction (area ratio) was determined.
(2) The retained austenite fraction in the steel sheet was measured by X-ray diffraction after being ground to ¼ thickness of the steel sheet and then chemically polished (for example, ISJJ Int. Vol. 33. (1933), No. 7, P.776).
(3) The martensite (as-quenched martensite) fraction was determined by X-ray diffraction from the area ratio of the martensite and retained austenite as it was quenched by repeller corrosion of the steel sheet. The martensite fraction was calculated by subtracting the residual austenite fraction.
スポット溶接に準ずる熱履歴として、熱処理シミュレータで平均加熱速度50℃/秒で700℃に加熱後、平均冷却速度50℃/秒で冷却し、元の硬さ(ビッカース硬さ)に対する硬さ低下量(ΔHv)を測定した。硬さ低下量(ΔHv)が50Hv以下のときに、HAZでの軟化防止特性が良好であると判断した。 (Hardness reduction after heat treatment)
As a heat history equivalent to spot welding, after heating to 700 ° C at an average heating rate of 50 ° C / sec with a heat treatment simulator, cooling is performed at an average cooling rate of 50 ° C / sec to reduce the hardness against the original hardness (Vickers hardness) (ΔHv) was measured. When the hardness reduction amount (ΔHv) was 50 Hv or less, it was judged that the anti-softening property in HAZ was good.
下記表11に示した化学成分組成を有する鋼材(鋼No.33~37)を真空溶製し、実験用スラブとした後、熱間圧延を行い、その後に冷却して巻取った(板厚:3.0mm)。このときの鋼板製造条件を下記表12に示す。 [Example 2]
Steel materials (steel Nos. 33 to 37) having the chemical composition shown in Table 11 below were melted in vacuum to form experimental slabs, followed by hot rolling, followed by cooling and winding (sheet thickness) : 3.0 mm). The steel plate production conditions at this time are shown in Table 12 below.
2 ダイ
3 ブランクホルダー
4 鋼板(ブランク) 1
Claims (6)
- C :0.15~0.5%(質量%の意味。以下、化学成分組成について同じ。)、
Si:0.2~3%、
Mn:0.5~3%、
P :0.05%以下(0%を含まない)、
S :0.05%以下(0%を含まない)、
Al:0.01~1%、
B :0.0002~0.01%、
Ti:3.4[N]+0.01%以上、3.4[N]+0.1%以下[但し、[N]はNの含有量(質量%)を示す]、および
N:0.001~0.01%、
を夫々含有し、残部が鉄および不可避不純物からなり、
鋼板中に含まれるTi含有析出物のうち、円相当直径が30nm以下のものの平均円相当直径が6nm以下であると共に、鋼中の析出Ti量と全Ti量とが下記(1)式の関係を満足し、且つ、金属組織が、フェライトの分率が30面積%以上であることを特徴とする熱間プレス用鋼板。
析出Ti量(質量%)-3.4[N]<0.5×[全Ti量(質量%)-3.4[N]] …(1)
((1)式中、[N]は鋼中のNの含有量(質量%)を示す) C: 0.15 to 0.5% (meaning mass%, hereinafter the same for chemical composition)
Si: 0.2-3%,
Mn: 0.5 to 3%,
P: 0.05% or less (excluding 0%),
S: 0.05% or less (excluding 0%),
Al: 0.01 to 1%,
B: 0.0002 to 0.01%,
Ti: 3.4 [N] + 0.01% or more, 3.4 [N] + 0.1% or less [where [N] indicates the content (% by mass) of N], and N: 0.001 ~ 0.01%,
Each of which contains iron and inevitable impurities,
Among the Ti-containing precipitates contained in the steel sheet, the average equivalent circle diameter of those having an equivalent circle diameter of 30 nm or less is 6 nm or less, and the relationship between the precipitated Ti amount in the steel and the total Ti amount in the following formula (1) And the metal structure has a ferrite fraction of 30% by area or more.
Precipitated Ti amount (mass%)-3.4 [N] <0.5 × [Total Ti amount (mass%)-3.4 [N]] (1)
(In the formula (1), [N] indicates the content (% by mass) of N in the steel) - 更に他の元素として、下記(a)~(c)の少なくとも1つを含有するものである請求項1に記載の熱間プレス用鋼板。
(a)V,NbおよびZrよりなる群から選択される1種以上を合計で0.1%以下(0%を含まない)
(b)Cu,Ni,CrおよびMoよりなる群から選択される1種以上を合計で1%以下(0%を含まない)
(c)Mg,CaおよびREMよりなる群から選択される1種以上を合計で0.01%以下(0%を含まない) The steel sheet for hot pressing according to claim 1, further comprising at least one of the following (a) to (c) as another element.
(A) 0.1% or less in total of one or more selected from the group consisting of V, Nb and Zr (excluding 0%)
(B) 1% or less in total of at least one selected from the group consisting of Cu, Ni, Cr and Mo (not including 0%)
(C) 0.01% or less (excluding 0%) of at least one selected from the group consisting of Mg, Ca and REM - 請求項1または2に記載の熱間プレス用鋼板を、Ac1変態点+20℃以上、Ac3変態点-20℃以下の温度に加熱した後、前記鋼板のプレス成形を開始し、成形中および成形終了後は金型内で20℃/秒以上の平均冷却速度を確保しつつベイナイト変態開始温度Bsより100℃低い温度以下まで冷却することを特徴とするプレス成形品の製造方法。 The steel sheet for hot pressing according to claim 1 or 2 is heated to a temperature of Ac 1 transformation point + 20 ° C or higher and Ac 3 transformation point -20 ° C or lower, and then press forming of the steel sheet is started. A method for producing a press-molded product, characterized in that after molding is completed, cooling is performed to a temperature lower than 100 ° C. below the bainite transformation start temperature Bs while securing an average cooling rate of 20 ° C./second or more in the mold.
- 請求項1または2に記載の化学成分組成を有する鋼板のプレス成形品であって、前記プレス成形品中の金属組織が、残留オーステナイト:3~20面積%、フェライト:30~80面積%、ベイニティックフェライト:30面積%未満(0面積%を含まない)、マルテンサイト:31面積%以下(0面積%を含まない)であり、プレス成形品中に含まれるTi含有析出物のうち、円相当直径が30nm以下のものの平均円相当直径が10nm以下であると共に、鋼中の析出Ti量と全Ti量とが下記(1)式の関係を満足することを特徴とするプレス成形品。
析出Ti量(質量%)-3.4[N]<0.5×[全Ti量(質量%)-3.4[N]] …(1)
((1)式中、[N]は鋼中のNの含有量(質量%)を示す) 3. A press-formed product of a steel sheet having the chemical composition according to claim 1 or 2, wherein the metal structure in the press-formed product is a retained austenite: 3 to 20 area%, ferrite: 30 to 80 area%, bay Nitic ferrite: less than 30 area% (excluding 0 area%), martensite: 31 area% or less (not including 0 area%), and among the Ti-containing precipitates contained in the press-formed product, A press-formed product characterized in that the average equivalent-circle diameter of an equivalent diameter of 30 nm or less is 10 nm or less, and the amount of precipitated Ti in the steel and the total Ti amount satisfy the relationship of the following formula (1).
Precipitated Ti amount (mass%)-3.4 [N] <0.5 × [Total Ti amount (mass%)-3.4 [N]] (1)
(In the formula (1), [N] indicates the content (% by mass) of N in the steel) - 請求項1または2に記載の熱間プレス用鋼板を用い、鋼板の加熱領域を少なくとも2つの領域に分け、その一の領域をAc3変態点以上、950℃以下の温度に加熱すると共に、他の一の領域をAc1変態点+20℃以上、Ac3変態点-20℃以下の温度に加熱した後、両方の領域に対してプレス成形を開始し、成形中および成形終了後はいずれの領域でも金型内で20℃/秒以上の平均冷却速度を確保しつつマルテンサイト変態開始温度Ms以下の温度まで冷却することを特徴とするプレス成形品の製造方法。 The steel sheet for hot pressing according to claim 1 or 2 is used, the heating region of the steel plate is divided into at least two regions, and one region is heated to a temperature not lower than Ac 3 transformation point and not higher than 950 ° C. After heating one region to a temperature of Ac 1 transformation point + 20 ° C. or higher and Ac 3 transformation point −20 ° C. or lower, press molding was started for both regions, and either region during or after molding However, the method for producing a press-molded product is characterized by cooling to a temperature below the martensite transformation start temperature Ms while securing an average cooling rate of 20 ° C./second or more in the mold.
- 請求項1または2に記載の化学成分組成を有する鋼板のプレス成形品であって、前記プレス成形品は、金属組織が、残留オーステナイト:3~20面積%、マルテンサイト:80面積%以上である第1の領域と、金属組織が、残留オーステナイト:3~20面積%、フェライト:30~80面積%、ベイニティックフェライト:30面積%未満(0面積%を含まない)、マルテンサイト:31面積%以下(0面積%を含まない)である第2の領域を有しており、この第2の領域の鋼中に含まれるTi含有析出物のうち、円相当直径が30nm以下のものの平均円相当直径が10nm以下であると共に、鋼中の析出Ti量と全Ti量とが下記(1)式の関係を満足することを特徴とするプレス成形品。
析出Ti量(質量%)-3.4[N]<0.5×[全Ti量(質量%)-3.4[N]] …(1)
((1)式中、[N]は鋼中のNの含有量(質量%)を示す) 3. A press-formed product of a steel sheet having the chemical composition according to claim 1 or 2, wherein the press-formed product has a metal structure of residual austenite: 3 to 20 area%, martensite: 80 area% or more. The first region and the metal structure are retained austenite: 3 to 20 area%, ferrite: 30 to 80 area%, bainitic ferrite: less than 30 area% (excluding 0 area%), martensite: 31 area % Of the Ti-containing precipitates contained in the steel of the second region having an equivalent circle diameter of 30 nm or less. A press-formed product characterized in that the equivalent diameter is 10 nm or less, and the amount of precipitated Ti in the steel and the total amount of Ti satisfy the relationship of the following formula (1).
Precipitated Ti amount (mass%)-3.4 [N] <0.5 × [Total Ti amount (mass%)-3.4 [N]] (1)
(In the formula (1), [N] indicates the content (% by mass) of N in the steel)
Priority Applications (9)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US14/917,823 US20160222482A1 (en) | 2013-09-10 | 2013-09-10 | Hot-pressing steel plate, press-molded article, and method for manufacturing press-molded article |
KR1020167006201A KR101827187B1 (en) | 2013-09-10 | 2013-09-10 | Hot-pressing steel plate, press-molded article, and method for manufacturing press-molded article |
PCT/JP2013/074426 WO2015037060A1 (en) | 2013-09-10 | 2013-09-10 | Hot-pressing steel plate, press-molded article, and method for manufacturing press-molded article |
EP13893228.0A EP3045553A4 (en) | 2013-09-10 | 2013-09-10 | Hot-pressing steel plate, press-molded article, and method for manufacturing press-molded article |
CN201380079439.1A CN105518170A (en) | 2013-09-10 | 2013-09-10 | Hot-pressing steel plate, press-molded article, and method for manufacturing press-molded article |
MX2016003260A MX2016003260A (en) | 2013-09-10 | 2013-09-10 | Hot-pressing steel plate, press-molded article, and method for manufacturing press-molded article. |
CA3014626A CA3014626A1 (en) | 2013-09-10 | 2013-09-10 | Hot-pressing steel plate, press-molded article, and method for manufacturing press-molded article |
RU2016111914A RU2625357C1 (en) | 2013-09-10 | 2013-09-10 | Hot straight thick-gauge plate formed by pumping the product and method of manufacturing formed by stamping the product |
CA2923583A CA2923583A1 (en) | 2013-09-10 | 2013-09-10 | Hot-pressing steel plate, press-molded article, and method for manufacturing press-molded article |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
PCT/JP2013/074426 WO2015037060A1 (en) | 2013-09-10 | 2013-09-10 | Hot-pressing steel plate, press-molded article, and method for manufacturing press-molded article |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2015037060A1 true WO2015037060A1 (en) | 2015-03-19 |
Family
ID=52665202
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2013/074426 WO2015037060A1 (en) | 2013-09-10 | 2013-09-10 | Hot-pressing steel plate, press-molded article, and method for manufacturing press-molded article |
Country Status (8)
Country | Link |
---|---|
US (1) | US20160222482A1 (en) |
EP (1) | EP3045553A4 (en) |
KR (1) | KR101827187B1 (en) |
CN (1) | CN105518170A (en) |
CA (2) | CA2923583A1 (en) |
MX (1) | MX2016003260A (en) |
RU (1) | RU2625357C1 (en) |
WO (1) | WO2015037060A1 (en) |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN105929668A (en) * | 2016-04-25 | 2016-09-07 | 尊尚(深圳)穿金戴银技术股份有限公司 | Pure gold watchcase, manufacturing method thereof and dial plate comprising pure gold watchcase |
JP2019518609A (en) * | 2016-04-22 | 2019-07-04 | アペラム | Method of manufacturing martensitic stainless steel parts from sheet |
US11027781B2 (en) | 2016-07-13 | 2021-06-08 | Nippon Steel Corporation | Hot-stamping formed article, structural member using the same, and manufacturing method of hot-stamping formed article |
Families Citing this family (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
IN201617022707A (en) | 2014-01-06 | 2016-08-31 | Nippon Steel & Sumitomo Metal Corp | |
EP3093358B1 (en) | 2014-01-06 | 2019-08-14 | Nippon Steel Corporation | Steel and method of manufacturing the same |
US10650621B1 (en) | 2016-09-13 | 2020-05-12 | Iocurrents, Inc. | Interfacing with a vehicular controller area network |
PL3360981T3 (en) * | 2017-02-10 | 2020-12-14 | Outokumpu Oyj | Steel component manufactured by hot forming, method of manufacturing and use of the component |
KR101978072B1 (en) | 2017-06-27 | 2019-05-13 | 현대제철 주식회사 | Steel for taylor welded blank and method of manufacturing hot stampig component using the same |
WO2019004541A1 (en) * | 2017-06-27 | 2019-01-03 | 현대제철 주식회사 | Steel material for taylor welded blank and method for manufacturing hot-stamped part using same steel |
CN108220777A (en) * | 2018-01-19 | 2018-06-29 | 山东钢铁集团日照有限公司 | A kind of heat forming technology for realizing part high strength and ductility duplex structure |
CA3096907A1 (en) * | 2018-05-11 | 2019-11-14 | Magna International Inc. | Conduction pre-heating of sheet for hot forming |
KR101930287B1 (en) | 2018-05-25 | 2019-03-11 | 김정우 | Apparatus and method for manufacturing of mounting cover |
CN109047429A (en) * | 2018-11-09 | 2018-12-21 | 浙江智造热成型科技有限公司 | Unimach hot forming production line |
CN114058794B (en) * | 2021-10-27 | 2022-11-22 | 中国科学院金属研究所 | Warm pressing process for manufacturing pressed rigging |
Citations (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2006183139A (en) * | 2004-11-30 | 2006-07-13 | Jfe Steel Kk | Automobile member and its production method |
JP2009061473A (en) * | 2007-09-06 | 2009-03-26 | Sumitomo Metal Ind Ltd | Method for manufacturing high-strength component |
JP2010043323A (en) * | 2008-08-12 | 2010-02-25 | Sumitomo Metal Ind Ltd | Hot rolled steel sheet for hot press, method for producing the same, and method for producing hot pressed steel sheet member |
JP2010065292A (en) | 2008-09-12 | 2010-03-25 | Jfe Steel Corp | Hot press member having excellent ductility, steel sheet for the hot press member and method for producing the hot press member |
JP2010065293A (en) | 2008-09-12 | 2010-03-25 | Jfe Steel Corp | Hot press member having excellent ductility, steel sheet for the hot press member, and method for producing the hot press member |
JP2010065295A (en) | 2008-09-12 | 2010-03-25 | Jfe Steel Corp | Hot press member having excellent ductility, steel sheet for the hot press member, and method for producing the hot press member |
JP2010065294A (en) | 2008-09-12 | 2010-03-25 | Jfe Steel Corp | Hot press member having excellent ductility, steel sheet for the hot press member, and method for producing the hot press member |
WO2012169639A1 (en) * | 2011-06-10 | 2012-12-13 | 株式会社神戸製鋼所 | Hot press molded article, method for producing same, and thin steel sheet for hot press molding |
WO2012169640A1 (en) * | 2011-06-10 | 2012-12-13 | 株式会社神戸製鋼所 | Hot press molded article, method for producing same, and thin steel sheet for hot press molding |
JP2013185247A (en) * | 2012-03-09 | 2013-09-19 | Kobe Steel Ltd | Steel sheet for hot pressing, press-molded product and method for manufacturing the press-molded product |
Family Cites Families (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2003253380A (en) * | 2002-02-26 | 2003-09-10 | Jfe Steel Kk | High-strength steel superior in toughness of heat- affected zone by ultra-high heat input welding |
WO2007048883A1 (en) * | 2005-10-27 | 2007-05-03 | Usinor | Method of producing a part with very high mechanical properties from a rolled coated sheet |
KR101133870B1 (en) * | 2006-05-10 | 2012-04-06 | 수미도모 메탈 인더스트리즈, 리미티드 | Hot-pressed steel sheet member and process for production thereof |
EP3587104B1 (en) * | 2006-10-30 | 2022-03-30 | ArcelorMittal | Coated steel strips |
WO2012147963A1 (en) * | 2011-04-28 | 2012-11-01 | 株式会社神戸製鋼所 | Hot press molded article, fabrication method therefor, and thin steel plate for hot press molding |
JP5679452B2 (en) * | 2011-08-17 | 2015-03-04 | 株式会社神戸製鋼所 | High-strength hot-rolled steel sheet that combines formability and fatigue properties of the base metal and weld heat-affected zone |
JP5756774B2 (en) * | 2012-03-09 | 2015-07-29 | 株式会社神戸製鋼所 | Steel sheet for hot pressing, press-formed product, and method for producing press-formed product |
JP5756773B2 (en) * | 2012-03-09 | 2015-07-29 | 株式会社神戸製鋼所 | Steel sheet for hot pressing, press-formed product, and method for producing press-formed product |
JP6001884B2 (en) * | 2012-03-09 | 2016-10-05 | 株式会社神戸製鋼所 | Manufacturing method of press-molded product and press-molded product |
-
2013
- 2013-09-10 EP EP13893228.0A patent/EP3045553A4/en not_active Withdrawn
- 2013-09-10 MX MX2016003260A patent/MX2016003260A/en unknown
- 2013-09-10 RU RU2016111914A patent/RU2625357C1/en not_active IP Right Cessation
- 2013-09-10 KR KR1020167006201A patent/KR101827187B1/en active IP Right Grant
- 2013-09-10 CN CN201380079439.1A patent/CN105518170A/en active Pending
- 2013-09-10 US US14/917,823 patent/US20160222482A1/en not_active Abandoned
- 2013-09-10 WO PCT/JP2013/074426 patent/WO2015037060A1/en active Application Filing
- 2013-09-10 CA CA2923583A patent/CA2923583A1/en not_active Abandoned
- 2013-09-10 CA CA3014626A patent/CA3014626A1/en not_active Abandoned
Patent Citations (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2006183139A (en) * | 2004-11-30 | 2006-07-13 | Jfe Steel Kk | Automobile member and its production method |
JP2009061473A (en) * | 2007-09-06 | 2009-03-26 | Sumitomo Metal Ind Ltd | Method for manufacturing high-strength component |
JP2010043323A (en) * | 2008-08-12 | 2010-02-25 | Sumitomo Metal Ind Ltd | Hot rolled steel sheet for hot press, method for producing the same, and method for producing hot pressed steel sheet member |
JP2010065292A (en) | 2008-09-12 | 2010-03-25 | Jfe Steel Corp | Hot press member having excellent ductility, steel sheet for the hot press member and method for producing the hot press member |
JP2010065293A (en) | 2008-09-12 | 2010-03-25 | Jfe Steel Corp | Hot press member having excellent ductility, steel sheet for the hot press member, and method for producing the hot press member |
JP2010065295A (en) | 2008-09-12 | 2010-03-25 | Jfe Steel Corp | Hot press member having excellent ductility, steel sheet for the hot press member, and method for producing the hot press member |
JP2010065294A (en) | 2008-09-12 | 2010-03-25 | Jfe Steel Corp | Hot press member having excellent ductility, steel sheet for the hot press member, and method for producing the hot press member |
WO2012169639A1 (en) * | 2011-06-10 | 2012-12-13 | 株式会社神戸製鋼所 | Hot press molded article, method for producing same, and thin steel sheet for hot press molding |
WO2012169640A1 (en) * | 2011-06-10 | 2012-12-13 | 株式会社神戸製鋼所 | Hot press molded article, method for producing same, and thin steel sheet for hot press molding |
JP2013185247A (en) * | 2012-03-09 | 2013-09-19 | Kobe Steel Ltd | Steel sheet for hot pressing, press-molded product and method for manufacturing the press-molded product |
Non-Patent Citations (3)
Title |
---|
HIROSUE ET AL., NIPPON STEEL TECHNICAL REPORT, 2003, pages 15 - 20 |
ISJJ INT., vol. 33, no. 7, 1933, pages 776 |
See also references of EP3045553A4 * |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2019518609A (en) * | 2016-04-22 | 2019-07-04 | アペラム | Method of manufacturing martensitic stainless steel parts from sheet |
CN105929668A (en) * | 2016-04-25 | 2016-09-07 | 尊尚(深圳)穿金戴银技术股份有限公司 | Pure gold watchcase, manufacturing method thereof and dial plate comprising pure gold watchcase |
US11027781B2 (en) | 2016-07-13 | 2021-06-08 | Nippon Steel Corporation | Hot-stamping formed article, structural member using the same, and manufacturing method of hot-stamping formed article |
EP3485996B1 (en) * | 2016-07-13 | 2022-06-01 | Nippon Steel Corporation | Hot-stamping formed article, structural member using the same, and manufacturing method of hot-stamping formed article |
Also Published As
Publication number | Publication date |
---|---|
US20160222482A1 (en) | 2016-08-04 |
EP3045553A1 (en) | 2016-07-20 |
CA2923583A1 (en) | 2015-03-19 |
KR20160042968A (en) | 2016-04-20 |
KR101827187B1 (en) | 2018-02-07 |
RU2625357C1 (en) | 2017-07-13 |
CN105518170A (en) | 2016-04-20 |
EP3045553A4 (en) | 2017-03-22 |
CA3014626A1 (en) | 2015-03-19 |
MX2016003260A (en) | 2016-06-07 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP5756774B2 (en) | Steel sheet for hot pressing, press-formed product, and method for producing press-formed product | |
JP5756773B2 (en) | Steel sheet for hot pressing, press-formed product, and method for producing press-formed product | |
WO2015037060A1 (en) | Hot-pressing steel plate, press-molded article, and method for manufacturing press-molded article | |
JP6001883B2 (en) | Manufacturing method of press-molded product and press-molded product | |
WO2015037061A1 (en) | Hot-pressing steel plate, press-molded article, and method for manufacturing press-molded article | |
JP6001884B2 (en) | Manufacturing method of press-molded product and press-molded product | |
WO2015037059A1 (en) | Method for manufacturing press-molded article, and press-molded article | |
JP5894470B2 (en) | Steel sheet for hot pressing, press-formed product, and method for producing press-formed product | |
JP5894469B2 (en) | Steel sheet for hot pressing, press-formed product, and method for producing press-formed product | |
JP5802155B2 (en) | Manufacturing method of press-molded product and press-molded product | |
JP5869924B2 (en) | Manufacturing method of press-molded product and press-molded product |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 13893228 Country of ref document: EP Kind code of ref document: A1 |
|
ENP | Entry into the national phase |
Ref document number: 2923583 Country of ref document: CA |
|
ENP | Entry into the national phase |
Ref document number: 20167006201 Country of ref document: KR Kind code of ref document: A |
|
REEP | Request for entry into the european phase |
Ref document number: 2013893228 Country of ref document: EP |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2013893228 Country of ref document: EP |
|
WWE | Wipo information: entry into national phase |
Ref document number: 14917823 Country of ref document: US |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
WWE | Wipo information: entry into national phase |
Ref document number: MX/A/2016/003260 Country of ref document: MX |
|
REG | Reference to national code |
Ref country code: BR Ref legal event code: B01A Ref document number: 112016004928 Country of ref document: BR |
|
ENP | Entry into the national phase |
Ref document number: 2016111914 Country of ref document: RU Kind code of ref document: A |
|
NENP | Non-entry into the national phase |
Ref country code: JP |
|
ENP | Entry into the national phase |
Ref document number: 112016004928 Country of ref document: BR Kind code of ref document: A2 Effective date: 20160304 |