WO2015037059A1 - プレス成形品の製造方法およびプレス成形品 - Google Patents

プレス成形品の製造方法およびプレス成形品 Download PDF

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WO2015037059A1
WO2015037059A1 PCT/JP2013/074425 JP2013074425W WO2015037059A1 WO 2015037059 A1 WO2015037059 A1 WO 2015037059A1 JP 2013074425 W JP2013074425 W JP 2013074425W WO 2015037059 A1 WO2015037059 A1 WO 2015037059A1
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press
temperature
steel plate
amount
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PCT/JP2013/074425
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French (fr)
Japanese (ja)
Inventor
村上　俊夫
純也 内藤
圭介 沖田
池田　周之
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株式会社神戸製鋼所
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Priority to RU2016111916A priority Critical patent/RU2633416C1/ru
Priority to CA2923582A priority patent/CA2923582C/en
Priority to CN201380079440.4A priority patent/CN105518162B/zh
Priority to KR1020167006199A priority patent/KR101716624B1/ko
Priority to US14/917,845 priority patent/US20160222483A1/en
Priority to EP13893522.6A priority patent/EP3045550A4/en
Priority to PCT/JP2013/074425 priority patent/WO2015037059A1/ja
Priority to MX2016003258A priority patent/MX2016003258A/es
Publication of WO2015037059A1 publication Critical patent/WO2015037059A1/ja

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    • 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
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    • 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
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    • 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
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    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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    • 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
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    • 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
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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    • 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
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    • 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
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • 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

Definitions

  • the present invention relates to a press-formed product used when manufacturing a structural part of an automobile, and a method for manufacturing such a press-formed product.
  • a press-formed product used when manufacturing a structural part of an automobile
  • a method for manufacturing such a press-formed product In particular, when a preheated steel plate (blank) is formed into a predetermined shape, a press-molded product manufactured by applying a heat treatment to obtain a predetermined strength by applying heat treatment simultaneously with the shape formation, and such
  • the present invention relates to a useful method for producing a pressed 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 employed in the production of parts that performs quenching heat treatment (quenching) using the temperature difference between the two to ensure the 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, techniques such as 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 1270 MPa or more and the elongation EL is about 12.7% at the maximum, and further improvement is required.
  • Non-Patent Document 1 Non-Patent Document 1
  • the present invention has been made in view of the above circumstances, and its purpose is to obtain a press-molded product that can achieve a high balance between high strength and elongation, and has good softening prevention characteristics in HAZ. It is an object of the present invention to provide a method useful for obtaining a press-molded product and a press-molded product that exhibits the above characteristics.
  • the method for producing a press-formed product of the present invention that has achieved the above-mentioned object is as follows: 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)
  • the steel sheet for hot pressing that satisfies the above conditions is heated to
  • 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 steel sheet for hot pressing used in the production method of the present invention contains 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 metal structure is bainitic ferrite: 60 to 97 area%, martensite: 37 area% or less, retained austenite: 3 to 20 area%, and remaining structure: 5 area%.
  • the average equivalent circle diameter of those having an equivalent circle diameter of 30 nm or less is 10 nm or less, and satisfies the relationship of the formula (1), The balance between high strength and elongation can be achieved as a uniform characteristic at a high level in a press-formed product.
  • the chemical component composition is strictly defined, the size of Ti-containing precipitates is controlled, and for Ti that does not form TiN, a steel plate with a controlled precipitation rate is used.
  • a steel plate with a controlled precipitation rate is used.
  • 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 simple press-formed product, we examined it from various angles.
  • C is important in reducing the bainite transformation start temperature Bs to make the bainitic ferrite produced in the cooling process finer and increasing the dislocation density in the bainitic ferrite to improve the strength. It is an element. Also, by increasing the amount of fine retained austenite formed between the laths of bainitic ferrite, a high level of balance between strength and elongation can be secured. If the C content is less than 0.15%, the bainite transformation start temperature Bs increases, the bainitic ferrite becomes coarse and low dislocation density, and the strength of the hot press-formed product cannot be ensured. On the other hand, if the C content is excessive and exceeds 0.5%, the strength becomes too high and good ductility cannot be obtained.
  • the preferable lower limit of the C content is 0.18% or more (more preferably 0.20% or more), and the preferable upper limit is 0.45% or less (more preferably 0.40% or less).
  • Si exhibits the effect of forming retained austenite by suppressing the decomposition of residual austenite formed between the laths of bainitic ferrite during the quenching of mold quenching and the formation of cementite.
  • the Si content needs to be 0.2% or more. Further, if the Si content is excessive and exceeds 3%, ferrite tends to be formed, and it becomes difficult to make austenite single phase during heating, and the structure fraction other than bainitic ferrite and residual austenite in the steel sheet for hot pressing. Exceeds 5 area%.
  • 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 soft structures such as ferrite and pearlite during cooling of mold hardening. Further, by reducing the bainite transformation start temperature Bs, the bainitic ferrite generated in the cooling process is made finer, and the dislocation density in the bainitic ferrite is increased, which is important in improving the strength. It is an element. Furthermore, it is an element that stabilizes austenite and contributes to an increase in the amount of retained austenite. In order to exert these effects, it is necessary to contain Mn in an amount of 0.5% or more. Considering only the characteristics, it is preferable that the Mn content is large, but the alloy addition cost increases, so the content was made 3% or less. 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 it is preferable to reduce P as much as possible.
  • extreme reduction leads to an increase in steelmaking cost, and it is difficult to produce 0%, so 0.05% or less (excluding 0%) was set.
  • 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.
  • extreme reduction leads to an increase in steelmaking cost, and it is difficult to produce 0%, so 0.05% or less (excluding 0%) was set.
  • 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 minimum with preferable Al content is 0.02% or more (more preferably 0.03% or more), and a preferable upper limit is 0.8% or less (more preferably 0.6% or less).
  • B has the effect of suppressing ferrite transformation and pearlite transformation, and therefore prevents the formation of ferrite and pearlite during cooling after heating to the two-phase region temperature of (Ac 1 transformation point to Ac 3 transformation point) It is an element that contributes to securing 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 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 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 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 preferably reduced as much as possible in order to reduce the hardenability improvement effect by fixing B as BN.
  • 0.001% is set as the lower limit.
  • 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 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 used in the present invention are as described above, and the balance is iron and inevitable impurities other than P, S, N (for example, O, H, etc.).
  • the steel sheet for hot pressing used in the present invention contains at least one of the following (a) to (c) as other elements as required.
  • the properties of the 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, 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).
  • 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. ).
  • One or more selected from the group consisting of Mg, Ca, and REM is 0.01% or less in total (not including 0%)
  • these elements refine the inclusions, they effectively work to improve ductility.
  • 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 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 targeted in 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 nm or less at the stage is 6 nm or less, and most of Ti is present in a solid solution state.
  • the amount of Ti present as precipitates other than TiN is less than the remaining 0.5 times of the total Ti minus Ti forming TiN. (That is, less than 0.5 ⁇ [total Ti amount (%) ⁇ 3.4 [N]]) (requirement (B) above).
  • the amount of precipitated Ti-3.4 [N] is preferably 0.4 ⁇ [total Ti amount (%)-3.4 [N]] or less, more preferably 0.3 ⁇ [total Ti amount (% ) -3.4 [N]] or less.
  • a slab obtained by melting a steel material having the chemical composition as described above 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), the finish rolling temperature is 850 ° C. or higher (preferably 900 ° C. or higher), and 1000 ° C. or lower (preferably 950 ° C. or lower).
  • 450 ° C or lower is cooled (rapidly cooled) at an average cooling rate of 20 ° C / second or higher (preferably 30 ° C / second or higher), 200 ° C or higher (preferably 250 ° C or higher), 500 ° C or lower (preferably It may be wound at 450 ° C. or lower).
  • the steel sheet for hot pressing having the above chemical composition and Ti precipitation state may be used for the production of hot pressing as it is, and the reduction ratio after pickling: 10 to 80% (preferably 20 to 70%) ) May be used for manufacturing a hot press after cold rolling. Further, after heating the steel sheet for hot pressing or the cold rolled material thereof to 830 ° C. or higher (preferably 850 ° C. or higher, 900 ° C. or lower), the temperature reaches 500 ° C. or lower (preferably 450 ° C. or lower) at 20 ° C./second or higher ( After quenching at a cooling rate of preferably 30 ° C./second or higher), a heat treatment may be performed such that holding at 500 ° C.
  • the steel plate for hot pressing according to the present invention may be plated on the surface (base steel plate surface) containing one or more of Al, Zn, Mg, and Si.
  • the steel sheet for hot pressing as described above, after heating to a temperature of 900 ° C. or more and 1100 ° C. or less, press molding is started, and during molding and after the molding, an average of 20 ° C./second or more in the mold After cooling to a temperature 100 ° C. lower than the bainite transformation start temperature Bs (Bs ⁇ 100 ° C.) or lower and a martensite transformation start temperature Ms or higher while ensuring a cooling rate, the average cooling rate of less than 20 ° C./second is 200 ° C.
  • a press-formed product having a single characteristic can be formed into an optimum structure (structure mainly composed of bainitic ferrite) having a predetermined strength and high ductility.
  • the reasons for defining the requirements in this molding method are as follows.
  • the heating temperature of the steel sheet is lower than 900 ° C., sufficient austenite cannot be obtained during heating, and the martensite fraction becomes excessive in the final structure (structure of the molded product). Further, when the heating temperature of the steel sheet exceeds 1100 ° C., the grain size of austenite increases during heating, the martensite transformation start temperature Ms and the martensite end temperature Mf increase, and residual austenite cannot be secured during quenching, which is good. Formability is not achieved.
  • the heating temperature is preferably 950 ° C. or higher and 1050 ° C. or lower.
  • the heating time at this time is too long, the Ti-containing precipitates in the steel sheet are difficult to be refined, and even if the amount is small, the Ti-containing precipitates are formed and coarsened during the heating, thereby improving the weldability. Since it becomes small, the one where a heating time is short is preferable.
  • the preferable range of the heating time is 3600 seconds or less, more preferably 20 seconds or less.
  • the average during and after forming It is necessary to appropriately control the cooling rate and the cooling end temperature. 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 100 ° C. lower than the bainite transformation start temperature Bs or less than the martensite transformation start temperature Ms.
  • the average cooling rate during molding is preferably 30 ° C./second or more (more preferably 40 ° C./second or more). By setting the cooling end temperature to 100 ° C.
  • the austenite existing during heating is transformed into bainite while preventing the formation of a structure such as ferrite or pearlite, and the amount of bainitic ferrite.
  • a predetermined amount of retained austenite is secured by leaving fine austenite between the laths of bainitic ferrite.
  • Rapid cooling is stopped when the temperature is below 100 ° C. below the bainite transformation start temperature Bs and above the martensite transformation start temperature Ms, and then cooled to 200 ° C. or less at an average cooling rate of less than 20 ° C./second. Do. By adding such a cooling step, the bainitic ferrite transformation is promoted. If the average cooling rate at this time is 20 ° C./second or more, martensite is formed and the strength is increased, but good elongation cannot be obtained. The average cooling rate at this time is preferably 15 ° C./second or less, more preferably 10 ° C./second or less. The reason for cooling to 200 ° C. or less by this cooling is that carbon is distributed from bainitic ferrite to untransformed austenite to increase the amount of residual austenite remaining at room temperature.
  • the control of the average cooling rate during the press molding and after the molding is finished is (a) controlling the temperature of the molding die (cooling medium shown in FIG. 1), and (b) controlling the thermal conductivity of the die. This can be achieved by means such as
  • the metal structure is bainitic ferrite: 60 to 97 area%, martensite: 37 area% or less, retained austenite: 3 to 20 area%, and remaining structure: 5 area%.
  • the amount of carbon in the retained austenite becomes 0.50% or more, and the balance between high strength and elongation can be achieved as a high level and uniform characteristic in the molded product.
  • the reasons for setting the ranges of the requirements (basic structure and carbon content in retained austenite) in such a hot press-formed product are as follows.
  • the area fraction of bainitic ferrite needs to be 60 area% or more. However, when this fraction exceeds 97 area%, the fraction of retained austenite becomes insufficient and ductility (residual ductility) decreases.
  • the preferable lower limit of the bainitic ferrite fraction is 65 area% or more (more preferably 70 area% or more), and the preferable upper limit is 95 area% or less (more preferably 90 area% or less).
  • the area fraction of martensite needs to be 37 area% or less.
  • a preferred lower limit of the martensite fraction is 5 area% or more (more preferably 10 area% or more), and a preferred upper limit is 30 area% or less (more preferably 25 area% or less).
  • Residual austenite has the effect of increasing the work hardening rate (transformation-induced plasticity) and improving the ductility of the molded product by transforming into martensite during plastic deformation.
  • the 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).
  • ferrite, pearlite, and the like may be included as the remaining structure.
  • these structures have a lower contribution to strength and ductility than other structures, and it is preferable that they do not basically contain (0 area). % Is acceptable). However, up to 5 area% is acceptable.
  • the remaining structure is more preferably 4 area% or less, and still more preferably 3 area% or less.
  • the average equivalent circle diameter of the 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 0.5 times the remaining Ti after subtracting Ti forming TiN out of all Ti. (That is, less than 0.5 ⁇ [total Ti amount (%) ⁇ 3.4 [N]]).
  • Ti that is solid-dissolved during welding is finely precipitated in HAZ, or the existing fine Ti-containing precipitates suppress the recovery of dislocation, etc., thereby preventing softening in HAZ, Good weldability.
  • the amount of precipitated Ti-3.4 [N] is preferably 0.4 ⁇ [total Ti amount (%)-3.4 [N]] or less, more preferably 0.3 ⁇ [total Ti amount (% ) -3.4 [N]] or less.
  • the press molding conditions heatating temperature and cooling rate
  • properties such as strength and elongation of the molded product
  • high ductility residual ductility
  • a press-molded product can be obtained, it can be applied to parts that have been difficult to apply with conventional hot-pressed products (for example, energy absorbing members), which is extremely useful in expanding the range of application of hot-pressed products. It is.
  • Steel materials (steel Nos. 1-31) having the chemical composition shown in Table 1 below are vacuum-melted to make slabs for experiment, then hot rolled into steel plates, and then cooled and wound up Simulated treatment was performed (plate thickness: 3.0 mm).
  • 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 plate manufacturing conditions at this time are shown in Table 2 below.
  • the Ac 3 transformation point, Ms point, and Bs point in Table 1 were obtained using the following formulas (2) to (4) (for example, “Leslie Steel Material Science” Maruzen, (1985 )reference). Further, the treatments (1) and (2) shown in the remarks column of Table 2 are obtained by performing the following treatments (rolling, cooling, and alloying).
  • 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 sheet (press forming steel sheet) was analyzed for Ti precipitation (precipitation Ti amount-3.4 [N], average circle equivalent diameter of Ti-containing precipitates) in the following manner.
  • the results are shown in Table 3 below together with a calculated value of 0.5 ⁇ [total Ti amount-3.4 [N]].
  • Precipitation Ti amount-3.4 [N] (Ti amount present as precipitates) was subjected to extraction residue analysis using a mesh with a mesh diameter of 0.1 ⁇ m (the precipitates aggregated during the extraction process). Thus, fine precipitates can be measured), and the precipitated Ti amount-3.4 [N] was determined. When the Ti-containing precipitate partially contains V or Nb, the content of these precipitates was also measured.
  • the precipitation state of Ti was measured by the method described above.
  • TS tensile strength
  • EL elongation
  • TS ⁇ EL strength-elongation balance
  • Table 5 The observation results of the metal structure (fraction of each structure, Ti precipitation state, amount of precipitated Ti-3.4 [N]) are shown in Table 5 below.
  • Table 6 shows the mechanical properties (tensile strength TS, elongation ELTS ⁇ EL, and hardness reduction amount ⁇ Hv) of the press-formed product.
  • the value of the precipitated Ti amount-3.4 [N] in the press-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. Samples 3, 7, 11-14, 17, and 21 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 with a low Si content, the retained austenite fraction in the press-formed product is not secured, only low elongation EL is obtained, and the strength-elongation balance (TS ⁇ EL) is also obtained. It has deteriorated. Steel No. No. 7 has a low finish rolling temperature during the production of the steel sheet and does not satisfy the relationship of the formula (1), and the Ti-containing precipitate is coarsened and the strength-elongation balance (TS ⁇ EL) is lowered. At the same time, the softening prevention characteristics are deteriorated.
  • Steel No. No. 17 uses a steel sheet with an excessive C content, and the strength of the molded product is increased and only a low elongation EL is obtained.
  • Steel No. No. 21 uses a steel plate with an excessive Ti content, and the press-formed product does not satisfy the relationship of the formula (1), and the Ti-containing precipitate in the molded product becomes coarse. The softening prevention property is deteriorated.
  • 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
  • the steel sheet for hot pressing that satisfies the predetermined relationship between the total Ti content and the total Ti amount is heated to a temperature of 900 ° C. or higher and 1100 ° C. or lower, and then press forming is started. After cooling to a temperature not higher than 100 ° C.

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WO2019003445A1 (ja) 2017-06-30 2019-01-03 Ｊｆｅスチール株式会社 熱間プレス部材およびその製造方法ならびに熱間プレス用冷延鋼板
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