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WO2013089167A1 - Produit formé par compression à chaud, son procédé de production et installation de formage par compression - Google Patents

Produit formé par compression à chaud, son procédé de production et installation de formage par compression Download PDF

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Publication number
WO2013089167A1
WO2013089167A1 PCT/JP2012/082291 JP2012082291W WO2013089167A1 WO 2013089167 A1 WO2013089167 A1 WO 2013089167A1 JP 2012082291 W JP2012082291 W JP 2012082291W WO 2013089167 A1 WO2013089167 A1 WO 2013089167A1
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Prior art keywords
press
temperature
strength region
formed product
hot press
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PCT/JP2012/082291
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English (en)
Japanese (ja)
Inventor
圭介 沖田
純也 内藤
池田　周之
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株式会社神戸製鋼所
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Publication of WO2013089167A1 publication Critical patent/WO2013089167A1/fr

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    • 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
    • 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
    • C21D2221/00—Treating localised areas of an article

Definitions

  • the present invention relates to a hot press-formed product that requires strength as used for a structural member of an automobile part, a method for manufacturing the same, and a press-forming facility for manufacturing the press-formed product, and is particularly preheated.
  • the present invention relates to a hot press-formed product that obtains a predetermined strength by quenching at the same time as forming a steel sheet when it is formed into a predetermined shape, a manufacturing method of such a hot press-formed product, and a press forming facility therefor. is there.
  • the steel plate (work material) is heated to a predetermined temperature (for example, the temperature at which it becomes an austenite phase) to reduce the strength (that is, to facilitate forming), and then to the steel plate.
  • a predetermined temperature for example, the temperature at which it becomes an austenite phase
  • Hot press molding method that secures strength after molding by molding with a low temperature mold (for example, room temperature) compared to providing shape and quenching heat treatment (quenching) using the temperature difference between the two. Is used in parts manufacturing.
  • Such a hot press molding method since the molding is performed in a low strength state, the spring back is reduced (good shape freezing property), and a strength of 1500 MPa class is obtained as a tensile strength by rapid cooling.
  • a hot press forming method is called by various names such as a hot forming method, a hot stamping method, a hot stamp method, a die quench method, etc. in addition to a hot press method (for example, Patent Document 1).
  • FIG. 1 is a schematic explanatory view showing a mold configuration for carrying out the above hot press molding (hereinafter may be represented by “hot stamp”).
  • 3 is a blank holder
  • 4 is a steel plate (blank)
  • BHF is a crease pressing force
  • rp is a punch shoulder radius
  • rd is a die shoulder radius
  • CL is a punch / die clearance.
  • the punch 1 and the die 2 have passages 1a and 2a through which a cooling medium (for example, water) can pass, and the cooling medium is allowed to pass through the passages.
  • a cooling medium for example, water
  • a hot press forming facility provided with a press forming machine having a mold configuration as described above is disclosed in Non-Patent Document 1, for example.
  • a heating furnace for heating and softening a thin steel plate an apparatus for conveying the heated thin steel plate, a press forming machine for press-forming the thin steel plate, and trimming the formed product (laser) Etc., and a device for performing correction processing to obtain a final shape.
  • laser formed product
  • a method (direct method) is shown in which a hot press-formed product having a simple shape as shown in FIG. 1 is simultaneously formed and quenched in a mold from the stage of a steel plate.
  • the hot pressing method applied in (1) is not limited to the case of applying to such a construction method, but can also be applied to the case of manufacturing a molded product having a relatively complicated shape.
  • a method of performing cold press forming in a pre-process of hot press forming can be adopted (this method is called “indirect method”).
  • the indirect method is a method in which a portion that is difficult to be molded is preliminarily molded to an approximate shape by cold working, and the other portions are hot press molded. If this method is adopted, for example, when a part having three uneven portions (mountains) of a molded product is formed, the two parts are formed by cold press molding, and then the third part is formed. Will be hot-formed.
  • the conventional hot stamping method has a problem that the hardness is increased by quenching, so that drilling and trimming become difficult as the shear resistance increases (particularly when the direct method is adopted). Moreover, even if it can process, in addition to the influence of a tool breakage and tool wear, since a high residual stress arises in the cutting surface vicinity of a blank material, there exists a possibility of causing a delayed fracture. Therefore, for example, laser cutting is used when trimming, but application of laser cutting is expensive and causes high costs. For these reasons, there is a demand for a method that enables trimming by a mold (sometimes referred to as “die trimming”). Moreover, since rapid cooling (die quench) is performed in the mold, it is necessary to hold the mold at the bottom dead center for a certain period of time, and the low productivity also causes high costs.
  • a collision-resistant safety part in an automobile body structure needs to have both functions of an impact resistant part and an energy absorbing part.
  • the mainstream method has so far been laser-welded (Tailored Weld Blanks: TWB) of high strength high tensile strength and high strength high strength tensile strength steel and then cold-pressed. It was.
  • TWB Laser-welded
  • the material ductility decreases as the strength increases, so that it becomes difficult to exhibit the function as an energy absorbing portion where ductility is required.
  • material softening tends to occur in a heat affected zone (HAZ) formed during spot welding. When such a portion is subjected to an impact load, the breakage starting from the HAZ is also a cause of reducing the ductility of the component.
  • a technique in which the strength of a part of the hot stamped product is intentionally reduced that is, a technique in which different strength regions (high strength region and low strength region) are separately created in one part is also proposed.
  • Such technology is called tailored tempering or soft flange.
  • a technique for example, in Patent Document 3, a mold contacting with a low-strength region is recessed to reduce the contact area, or a heating means is provided to partially increase the mold temperature, or the mold material
  • a technique has been proposed in which a low-strength region is created by using a material having a low thermal conductivity and slowing the cooling rate.
  • a surface-treated steel sheet (Zn—Fe-based plated steel sheet) in which a Zn—Fe-based plated layer containing a predetermined amount of Fe is formed on the substrate surface is used.
  • Liquid liquid metal embrittlement
  • molten zinc enters the grain boundaries of the steel sheet subjected to tensile stress.
  • LME Metal Emblence
  • JP 2002-102980 A JP 2007-275937 A JP 2003-328031 A JP 2007-75834 A
  • the present invention has been made in view of the above circumstances, and its purpose is to perform hot press molding, which is excellent in productivity at the time of production, part ductility, and if necessary, hot press molded article having excellent corrosion resistance, It is another object of the present invention to provide a useful method for producing such a hot press-formed product and an equipment for producing such a hot press-formed product.
  • the present invention method which was able to achieve the above object, a hot press molded product having a high strength region and low intensity regions within a single component, when prepared using a press molding die, the steel sheet Ac 3 After heating to a temperature equal to or higher than the transformation point, prior to starting press molding, the high strength region is rapidly cooled.
  • the temperature of the steel sheet before press forming is 600 ° C. or lower in the high strength region, the martensite transformation start temperature Ms or higher, and 650 ° C. or higher in the low strength region.
  • the time from the start of rapid cooling to the start of press molding is preferably within 30 seconds.
  • the temperature of the molded product at the time of mold release after press molding is not more than the martensite transformation start temperature Ms + 100 ° C. in the high strength region, is not less than the martensite transformation end temperature Mf, and is in the low strength region (martensite transformation start temperature Ms + 100 ° C.) or higher.
  • the molded product may be allowed to cool after release, but (b) after molding, the high-strength region has an average cooling rate of 5 ° C./second or more and the martensite transformation end temperature. You may make it cool to the temperature below Mf.
  • the forming start temperature is equal to or lower than the freezing point of the plating layer according to the Fe content in the plating layer.
  • the temperature is The steel plate used in the present invention is not limited to a Zn—Fe-based plated steel plate, and a non-plated steel plate or an Al—Si-based plated steel plate may be used.
  • the present invention also includes a hot press-molded product obtained by the manufacturing method as described above. Moreover, as a press molding facility for producing such a hot press-formed product, a heating furnace and a press molding machine are provided, and a high strength region of a heated steel plate is provided between the heating furnace and the press molding machine. It is useful to provide a cooling part for partially quenching the water.
  • the steel plate is heated to a temperature equal to or higher than the Ac 3 transformation point. Later, prior to the start of press molding, the high-strength region was rapidly cooled, so a hot press-formed product with excellent ductility in the low-strength region and excellent part ductility can be produced with high productivity. .
  • the present inventors have studied from various angles in order to manufacture hot press-formed products having a high strength region and a low strength region in a single part with good productivity while ensuring the ductility of the part.
  • the steel plate is heated to a temperature equal to or higher than the Ac 3 transformation point, and then, before starting press forming, high strength It has been found that if the region is rapidly cooled, a hot press molded product having excellent ductility in a low strength region and excellent component ductility can be produced with high productivity, and the present invention has been completed.
  • the steel plate it is necessary to heat the steel plate to a temperature equal to or higher than the Ac 3 transformation point in order to exert the effect of the hot pressing method.
  • the heating temperature is less than the Ac 3 transformation point, an appropriate amount of austenite cannot be obtained during heating, and good moldability cannot be ensured.
  • the preferable lower limit of the heating temperature is not less than (Ac 3 transformation point + 50 ° C.) of the steel sheet.
  • the upper limit of the heating temperature of the steel sheet is preferably up to about 1000 ° C.
  • this heating temperature is higher than 1000 ° C.
  • the generation of oxide scale becomes significant (for example, 100 ⁇ m or more) during conveyance from the heating furnace to a press molding machine (see FIG. 5 below), and the thickness of the molded product (de There is a possibility that the thickness after scaling will be smaller than a predetermined value.
  • the upper limit with preferable heating temperature is 950 degrees C or less.
  • FIG. 2 The image of the heat pattern of the method of the present invention is schematically shown in FIG. 2 (CCT curve: Continuous Cooling Transformation diagram).
  • a high-strength region region desired to be a high-strength region: indicated by “region A” in the figure
  • a low-strength region region desired to be a low-strength region: “ In the region B "
  • press molding is simultaneously performed at a high temperature.
  • the die quench time at the bottom dead center of molding is shortened as much as possible.
  • the average cooling rate at the time of rapid cooling in the high strength region is preferably at least 27 ° C./second or more, more preferably 40 ° C./second or more.
  • the time from the rapid cooling start (region A) before press forming to the start of press forming is within 30 seconds (more preferably within 20 seconds), and the temperature of the steel plate before press forming is In the high-strength region (region A), the temperature is preferably 600 ° C. or lower and the martensitic transformation start temperature Ms or higher. This temperature corresponds to the rapid cooling end temperature in the high strength region.
  • the temperature in the low-strength region (region B) although the rapid cooling is not basically performed, the temperature of the steel sheet may decrease after heating and before press forming. In such a case, the low-strength region before press forming is assumed.
  • the temperature is preferably 650 ° C. or higher.
  • the die quench time (holding time at the molding bottom dead center) is preferably within 5 seconds (more preferably within 3 seconds).
  • the steel plate temperature (molded product temperature) at the time of mold release after press forming is (martensitic transformation start temperature Ms + 100 ° C.) or lower in the high strength region, martensitic transformation end temperature Mf or higher, and in the low strength region (martensitic transformation). It is preferable that the starting temperature is Ms + 100 ° C. or higher. By controlling in this way, higher strength can be achieved in the high strength region, and lower strength can be realized in the low strength region.
  • the steel plate temperature (molded product temperature) at the time of mold release after press forming is more preferably not higher than the martensite transformation start temperature Ms in the high strength region and not lower than (martensite transformation start temperature Ms + 180 ° C.) in the low strength region. .
  • the molded product may be allowed to cool after mold release.
  • the high-strength region has an average cooling rate of 5 ° C./second or more and a temperature equal to or lower than the martensite transformation end temperature Mf. You may make it cool (secondary cooling).
  • the average cooling rate of the secondary cooling is more preferably 10 ° C./second or more, and further preferably 20 ° C./second or more.
  • the high strength region is partially cooled before press molding, and the low strength region is basically formed without cooling before molding.
  • die trimming can be performed, and it is not necessary to use a laser cutting machine, so that low cost can be realized.
  • die trimming in a low-strength region is possible, there is an advantage that the risk of wear and damage of the mold can be reduced, and this also leads to low cost.
  • the low-strength region is die-trimmed, high residual stress is not generated in the vicinity of the cut surface, and the fear of delayed fracture is eliminated.
  • partial rapid cooling before press molding can shorten the die quench time, thereby improving productivity and reducing costs in this respect.
  • the material ductility of the low strength region is improved, so that the moldability of the entire molded product is improved.
  • material softening in the HAZ accompanying welding can be reduced, so the HAZ starting point is destroyed when subjected to an impact load.
  • the ductility of the molded product is improved.
  • LME in hot stamping is thought to occur when molten zinc penetrates into a place where tensile stress is applied in a Zn-based plated steel sheet being formed. That is, if press molding is performed below the freezing point of the Zn-based plating layer, LME does not occur. Therefore, as shown in FIG. 2, only the region A including the bending portion where tensile stress is generated during press forming is rapidly cooled before press forming, and the solidification temperature of the Zn-based plating layer (the freezing point corresponding to the Fe content). : Indicated by “Fp” in FIG.
  • low strength region is preferably formed at a temperature lower than the freezing point of the plating layer.
  • it is not significantly affected by press forming it is not always necessary to form at a temperature lower than the freezing point. What is necessary is just to start shaping
  • FIG. 3 is a Zn—Fe binary system state diagram.
  • the broken line portion in the figure indicates the boundary between the region including the liquid layer and the solid phase region (that is, corresponding to the freezing point: indicated by “Fp” in the drawing), and below this boundary is the solid phase region. Since the Zn-Fe-based plating layer has a different Fp temperature depending on the Fe content in the plating layer, the temperature of the galvanized layer before forming is equal to or less than Fp (corresponding to the freezing point) according to the Fe content. Cool down.
  • the press-forming is performed at a temperature below the freezing point of the plated layer according to the Fe content in the Zn—Fe-based plated layer. Since this is done, there is basically no LME problem. Therefore, even in a press-molded product manufactured by hot stamping, the sacrificial anticorrosive property of the Zn—Fe-based plated steel sheet can be exhibited, and application to the underbody becomes possible.
  • the steel type of the steel plate used in the method of the present invention may be a normal chemical component composition as a high-strength steel plate.
  • a steel plate having the chemical composition shown in Table 1 below can be cited.
  • the steel sheet has an Ac 3 transformation point of 832 ° C., a martensite transformation start temperature Ms: 411 ° C., and a martensite transformation end temperature Mf: 261 ° C.
  • the Ac 3 transformation point, Ms, and Mf of the steel sheet are values obtained using the following formulas (1) to (3) ( For example, “Heat Treatment” 41 (3), 164 to 169, 2001 Tetsuro Kunitake “Predicting Ac 1 , Ac 3 and Ms transformation points of steel by empirical formula”).
  • the Fe content in the Zn—Fe-based plating layer formed on the surface of the steel sheet is not particularly limited, and may be plated if it is 5% by mass or more (more preferably 13% by mass or more). Although it functions as a layer, if the Fe content is excessive, corrosion resistance, coating film adhesion, weldability, etc. are likely to deteriorate, so it is preferably 80% by mass or less (more preferably 20% by mass). Less than).
  • the Zn—Fe-based plating layer may contain alloy elements other than Fe (eg, Al, Mn, Ni, Cr, Co, Mg, Sn, Pb, etc.) up to about 3.3 mass%. These elements have little influence on the freezing point at the content level.
  • the Zn—Fe plating layer has some inevitable factors such as Be, B, Si, P, Ti, V, W, Mo, Sb, Cd, Nb, Cu, and Sr. Impurities can also be included.
  • the conventional hot press line generally has a configuration (equipment configuration) as shown in FIG. 4 (schematic explanatory diagram). That is, as shown in FIG. 4, after the coiled steel sheet 10 is cut out by a cutting machine 11 (Blanking), it is heated in a heating furnace 12, and then conveyed to the press molding machine 13 to perform press forming. A press-formed product 14 is obtained.
  • a cooling unit 15 is provided inside the heating furnace 12 in association with the heating furnace 12, and a part of the steel sheet is rapidly moved until the steel sheet 10 is moved from the heating furnace 12 to the press forming machine 13. Cooling.
  • the cooling unit 15 may be provided between the heating furnace 12 and the press molding machine 13 (see, for example, “cooling unit” or “cooling zone” in FIGS. 6 to 8). In the cooling performed by the cooling unit 15, for example, cooling can be performed by the following methods (1) to (4) (or in combination).
  • a means for bringing into contact with a metal as a refrigerant for example, a cooling means using a water-cooled roll
  • a gas cooling means is provided to cool the gas jet.
  • Provide mist cooling means for cooling for example, FIG. 8).
  • a dry ice shot means (cooled by causing the granule dry ice to collide with the blank material) is cooled.
  • the atmosphere can be controlled (for example, nitrogen or argon atmosphere) to prevent surface oxidation of the steel sheet. It is also possible to suppress surface oxidation by setting a relatively low temperature.
  • the cooling conditions differ depending on different regions (high strength region and low strength region) of the steel sheet, but the cooling means (1) to (4) described above are used only for the high strength region.
  • the cooling control corresponding to the steel plate region may be performed in the mold.
  • FIG. 6 is a schematic view showing a configuration example of the cooling unit, and shows a facility for cooling a heated thin steel plate by sandwiching it with a metal.
  • the heated thin steel sheet is transported from the heating furnace to a flat mold for cooling (dedicated cooling mold), and the thin steel sheet is rapidly cooled to a predetermined temperature by pressing with this mold (cooling by holding metal). .
  • the steel sheet may be conveyed to a mold having a predetermined shape (depress-only mold) and press-molded.
  • the shape of the cooling-only mold is preferably a flat surface on the steel plate contact surface side in order to cool the steel plate uniformly, but it is not necessarily flat for a temperature distribution or for some pre-forming. It is not necessary to have a step or curvature.
  • the steel plate is cooled to a predetermined temperature with a flat die (cooling-only die), and then sequentially pressed with a die having a predetermined shape.
  • a flat die cooling-only die
  • a die having a predetermined shape By molding, it is also possible to mold into a complicated shape (press die 1 and press die 2). Further, a step of imparting shape freezing property and a step of performing die trim piercing may be added.
  • partial cooling before press forming is not limited to sandwiching metal, but may be a method of rapid cooling by spraying mist (or air) as shown in FIG.
  • mist and air since the transition region between the cooling region and the non-cooling region becomes wide, in order to cool the target region (high-strength region) with high accuracy, it is preferable to perform cooling by sandwiching metal.
  • FIGS. 6 and 7 a transfer press molding machine that continuously performs cooling means and mold molding is assumed, but the press molding machine used in the present invention is not limited to such a configuration, As long as a sufficient conveyance speed can be ensured, a configuration in which the press molding machine provided with each mold is separated may be used. From the viewpoint of shortening the press time, it is preferable to use a mechanical press (called a mechanical press) with a mechanical driving force for the pressure generating mechanism, but hydraulic pressure is used for the pressure generating mechanism. It may be a hydraulic press (for example, a hydraulic press).
  • the present invention In producing a hot press-formed product having a high-strength region and a low-strength region in a single part using a press-molding die, the present invention, after heating the steel plate to a temperature equal to or higher than the Ac 3 transformation point, Prior to the start of press molding, the high-strength region is rapidly cooled to obtain a hot press-molded product having excellent productivity and part ductility at the time of manufacture, and excellent corrosion resistance if necessary.

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  • Chemical & Material Sciences (AREA)
  • Physics & Mathematics (AREA)
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  • Mechanical Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Shaping Metal By Deep-Drawing, Or The Like (AREA)

Abstract

　Lors de l'utilisation d'un moule de formage par compression pour produire un produit formé par compression à chaud présentant une zone à haute résistance et une faible résistance dans un composant unique, un produit formé par compression à chaud présentant une meilleure productivité et ductilité de composant lors du processus de production et présentant une meilleure résistance à la corrosion en cas de besoin est produit par chauffage d'une plaque d'acier pour le porter à une température supérieure ou égale au point de transformation Ac3, puis refroidissement rapide de la zone à haute résistance avant le début du processus de compression.
PCT/JP2012/082291 2011-12-13 2012-12-13 Produit formé par compression à chaud, son procédé de production et installation de formage par compression WO2013089167A1 (fr)

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JP2011-272649 2011-12-13
JP2011272649A JP5902939B2 (ja) 2011-12-13 2011-12-13 熱間プレス成形品の製造方法

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JP2014503360A (ja) * 2010-12-27 2014-02-13 ポスコ 異物性部品の製造方法
CN109821951A (zh) * 2018-12-06 2019-05-31 苏州普热斯勒先进成型技术有限公司 一种耐腐蚀热冲压零件的制备方法及装置
CN111344079A (zh) * 2017-08-02 2020-06-26 自动工程有限公司 用于涂层钢的压制方法以及钢的用途
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RU2787134C1 (ru) * 2019-10-14 2022-12-28 Аутотек Инжиниринг С.Л. Системы и способы прессования

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JP6381967B2 (ja) 2014-05-22 2018-08-29 住友重機械工業株式会社 成形装置及び成形方法
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JP2014503360A (ja) * 2010-12-27 2014-02-13 ポスコ 異物性部品の製造方法
CN111344079A (zh) * 2017-08-02 2020-06-26 自动工程有限公司 用于涂层钢的压制方法以及钢的用途
US20210362212A1 (en) * 2017-08-02 2021-11-25 Autotech Engineering S.L. Press methods for coated steels and uses of steels
US11633771B2 (en) * 2017-08-02 2023-04-25 Autotech Engineering S.L. Press methods for coated steels and uses of steels
CN109821951A (zh) * 2018-12-06 2019-05-31 苏州普热斯勒先进成型技术有限公司 一种耐腐蚀热冲压零件的制备方法及装置
WO2021074185A1 (fr) * 2019-10-14 2021-04-22 Autotech Engineering S.L. Systèmes de presse et procédés
CN114555256A (zh) * 2019-10-14 2022-05-27 昂登坦工程有限公司 压制系统和方法
RU2787134C1 (ru) * 2019-10-14 2022-12-28 Аутотек Инжиниринг С.Л. Системы и способы прессования
EP4219036A1 (fr) * 2019-10-14 2023-08-02 Autotech Engineering, S.L. Systèmes et procédés de presse
US11850648B2 (en) 2019-10-14 2023-12-26 Autotech Engineering S.L. Press systems and methods

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