CN103842528A - A method of forming parts from sheet steel - Google Patents
A method of forming parts from sheet steel Download PDFInfo
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- CN103842528A CN103842528A CN201280047038.3A CN201280047038A CN103842528A CN 103842528 A CN103842528 A CN 103842528A CN 201280047038 A CN201280047038 A CN 201280047038A CN 103842528 A CN103842528 A CN 103842528A
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- cooling
- steel disc
- arbitrary aforementioned
- cooling fluid
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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
- B21D22/02—Stamping using rigid devices or tools
- B21D22/022—Stamping using rigid devices or tools by heating the blank or stamping associated with heat treatment
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/62—Quenching devices
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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
- 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
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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
- C21D11/00—Process control or regulation for heat treatments
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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
- C21D9/0062—Heat-treating apparatus with a cooling or quenching zone
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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
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Mechanical Engineering (AREA)
- Crystallography & Structural Chemistry (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Articles (AREA)
- Shaping Metal By Deep-Drawing, Or The Like (AREA)
Abstract
A method is provided of forming a part from sheet steel. The method comprises the steps of (a) heating the sheet to a temperature at which austenitization occurs; and (b) forming the sheet between dies into the part, further cooling the formed sheet. There is an additional step between (a) and (b) of applying cooling means to the sheet.
Description
Technical field
The present invention relates to by metal forming parts.In embodiments, it relates to by tinsel as steel and Steel Alloy molded component.
Background technology
Use the technique of " hot stamping " rising as by steel disc shaping high-strength parts for example, for () automobile " body in white " (BiW) and the preferred version of chassis and suspension (C & S) parts.The development of boron steel makes this type of technique can be used for producing the crucial panel component of car safety, for example A-post, B-post, collision bumper, top luggage carrier, rocking arm luggage carrier and for the tunnel, ground of body in white and tubular part with for the distortion beam of C & S.In recent years, increase sharply to the demand of this type of superstrength steel part in the whole world.
Figure 1 illustrates a kind of typical boron steel hot stamping technique.It consists essentially of following steps:
(1) steel billet material is heated to above to its austenitizing temperature, such as 925 DEG C, and at this temperature all thermal treatment so that all metals are converted into austenite.In this state, described metal is soft and has high ductibility (being easily shaped);
(2) blank of described austenitizing is turned rapidly to punching press;
(3) use the shape that conventionally by water-cooled cold set of molds, described blank is configured as to element;
(4) parts of described shaping are kept for some time in described cold set of molds (for example 6-10 second, depend on geometrical shape, thickness of slab and pressure etc.) to quench, for example martensite of hard phase (for high strength components) of described material is formed; With
(5) when the temperature of described parts be down to enough low-level, such as 250 DEG C, open described mould, element is taken out.
This kind of technique is called as " hot stamping, cold die forming and quenching " technique sometimes.
Most of heat in described hot stamping technique in workpiece enters described mould.Rate of cooling is relevant with described tool surfaces temperature to a great extent.Under mass production environment, even if mould described in water-cooled is also difficult to keep described tool surfaces temperature enough low.High instrument surface temperature causes following problem:
For the conventional hot stamping technique by steel disc shaping complex component, sheet-like workpiece is transferred to the instrument in room temperature from stove as quickly as possible this, described sheet-like workpiece is out of shape simultaneously and quenches in described instrument.Described quenching rapid enough is to produce martensite microstructure in described steel, and this forms the basis of high-strength products.
(i) rate of cooling in die quenching may become too low, and this will cause less desirable soft form mutually (generation low-intensity part) in the situation that of steel; At light alloy, as aluminium alloy in the situation that, too low die quenching speed will cause less desirable grain boundary to be separated out, and it causes pressure corrosion cracking and low-intensity part;
(ii) the cold mould hold-time possibility long (because pass to and can, because of slack-off compared with hot mould, therefore need the long period to reach outlet temperature from the heat of described steel disc sheet) needing, this has reduced productivity (increasing the forming period time);
(iii) requirement of mold cools down is important fully, but manually provide cooling and (pass through special methods, adopt the cooling duct of forcing cooling fluid, Deng) increase tool operation cost, make effective ways be difficult to design and installation, and significantly improved tool operation and maintenance cost.
(iv) in the time of tool surfaces high temperature, tool wear and/or die surface distortion are accelerated, and have reduced life tools, and its cost increases the weight of the special cooling system of describing in (iii).
Therefore, generally speaking, in the time using this technique fast continuously to produce parts, contact the temperature rise that causes described instrument with workpiece from stove constant.As a result, quenching velocity reduces, and it may cause containing the not finished product of microstructure up to standard and produce.For fear of this result, can by reduce productivity or by use cooling system (as inside be loaded with the pipeline of refrigerant or to as described in spray refrigerant on instrument) maintain low tool temperature.Usually, be used in combination this two kinds of methods, to obtain the microstructure of expecting under the possible maximum productivity of the cooling strategy for providing.The defect of all these measures is to have increased cost.
Summary of the invention
Briefly, a kind of two stage method of cooling have been proposed to improve the productivity of high-strength sheet parts.In two stage method of cooling of described proposition, the steel disc of quick cooling heating between heating and shaping.It is contemplated that, described fast cooling be by some artificial means, instead of only by surrounding environment, leave standstill, air.For example, use high heat conductance transfer device, air jet stream or air/liquid spraying.In this mode, in the time that blank starts to be shaped, just can reduce the temperature of blank in mould.Therefore, in forming process (quenching again subsequently), described instrument absorbs less heat, and the rising of their temperature is lowered.Therefore, maintain low datum temperature and become easier, reduce costs and boost productivity.Selectable feature produces other beneficial effect.
According to a first aspect of the invention, provide a kind of method by steel disc molded component, described method comprises step:
(a) described steel disc is heated to the temperature that austenitizing occurs; With
(b) by described steel disc molded component between mould;
Wherein exist described steel disc application cooling way therefrom to extract the additional step of heat in step (a) with (b).
Described additional step can comprise that the described cooling way of application is with quick cooling described steel disc.
Compare common process, by the steel disc of the first fast cooling described heating described steel disc steel disc that is shaped between steel disc mould again, described steel disc can be shaped lower than conventional starting temperature in cold mould.This produces following effect: described steel disc can be cooling so that the hardest phase---martensite---formation fast enough in mould; Compare common process, described steel disc can arrive the applicable temperature discharging from described mould quickly, has accelerated production; Reduce the tool damage causing by improving surface temperature, extended life tools; Reduce instrument cooling structure as the demand of cooling tube, therefore reduced die cost.
Described additional step can comprise with cooling way as high heat conductance transfer device or by as described in apply for example refrigerant of cooling way on the steel disc of heating and extract heat.
Described refrigerant can be fluid.It can be gas, for example air.Described cooling fluid can be liquid, for example water.Described cooling fluid can comprise gas and liquid, as empty G&W.Described cooling fluid can pressurized fluid the form of stream led control.Described cooling fluid can injection stream form led control.The form that described cooling fluid can be sprayed is led control.Described cooling fluid can be used for cooling described mould.It can be used for clean described mould.It can be used for cooling and clean described mould.Described cooling fluid can be led control to described mould.It can be led control to described mould and be led subsequently the steel disc of control to described heating, and/or it can be led the steel disc of control to described mould and described heating simultaneously.
Described cooling way can be high heat conductance solid, as copper transfer handle or plate.
Can in the time that described blank is between described mould, apply described cooling way.
Also can by increase the transfer time of (for example, from stove to mould) between two steps realize (a) and (b) between cooling.
Described additional step can comprise leads the steel disc of control to described heating by described cooling fluid, so that described steel disc is cooling to avoid described steel disc to enter Bainite Phases of Some fast enough.Described additional step can comprise leads control to the steel disc of described heating by described cooling fluid, so that described steel disc is cooling to be on average greater than the speed of 25 DEG C/sec.Described additional step can comprise leads the steel disc of control to described heating by described cooling fluid.Can lead the described cooling fluid of control with regard to time length, temperature and/or flow, so that described steel disc is cooling to avoid described steel disc to enter Bainite Phases of Some fast enough.Can lead the described cooling fluid of control with regard to time length, temperature and/or flow, so that described steel disc is cooling to be on average greater than the speed of 25 DEG C/sec.
Described additional step can comprise leads the steel disc of control to heating by described cooling fluid, so that when cooling by this way, more than the temperature of described steel disc maintains the austenitizing temperature of described steel.Described additional step can comprise leads the steel disc of control to heating by described cooling fluid, so that described steel disc is cooled to 500 DEG C-600 DEG C.Can lead the described cooling fluid of control with regard to time length, temperature and/or flow, so that when cooling by this way, the temperature of described steel disc maintains the austenitizing state of described steel.Can lead the described cooling fluid of control with regard to time length, temperature and/or flow, so that described steel disc is cooled to 500 DEG C-600 DEG C.Unexpectedly, owing to keeping the described steel disc strain hardening of essentially identical while to increase in ductility, this has the effect that improves Alloy Forming ability.Described method can comprise and starts step (b) during in its austenite phase temperature when described steel disc.Described method also can comprise until described steel disc just carries out step (b) while reaching its martensitic phase temperature.
Step (a) can comprise some or all features of step in common process described herein.
Described method can be the method for shaping for the parts of automobile application.Described method can be the method for shaping for the panel component of automobile application.Described method can be the method being shaped for the load-supporting part of automobile application and the parts of applicable load-bearing; For example described method can be the following one or more method that is shaped: the post, collision bumper, Men Liang, top luggage carrier, rocking arm luggage carrier and the tunnel, ground that comprise A-post and B-post.Described method can be the method for shaping chassis and suspender; For example tube-like piece and distortion beam.
Described steel disc can be the alloy that comprises boron.
In another aspect of this invention, provide a kind of method by the material forming parts beyond steel.For example, described material can be aluminium alloy.It can be sheet form.It is contemplated that, the method described in first aspect can be used for aluminium alloy, the aluminium alloy of for example sheet form.In the method for this other side, step (a) can comprise the temperature that described thin slice is heated to the changes in crystal structure that is substantially equal to austenitizing generation.
Brief description of the drawings
Fig. 1 shows the schematic diagram of current hot stamping technique;
Fig. 2 shows the CCT chart of typical boron steel;
Fig. 3 shows the temperature collection of illustrative plates quenching in cold mould; With
Fig. 4 shows under the strain rate of 1.0s-1 the stress strain relationship of the boron steel of testing at the temperature of 500,600,700 and 800 DEG C.
Embodiment
As mentioned above, Fig. 1 shows a kind of existing method.Aspect very important in this existing method, be that, in the time that heat-punch member remains in cold mould, rate of cooling should be enough high, for example, be on average greater than 25 DEG C/sec (as shown in Figure 2), to form the hardest phase---the martensite of described material.By this way, can produce high strength components.Described rate of cooling is non-constant during cold die quenching, as shown in Figure 3.At first, the temperature contrast between described workpiece and described mould is high, can realize high rate of cooling.Be down to while approaching described tool surfaces temperature (it is because transfer of heat raises) when the temperature of described workpiece, rate of cooling significantly reduces.In continuous hot stamping technique, described tool surfaces temperature can be up to 150 DEG C.This causes the rate of cooling of workpiece in 500 DEG C of-250 DEG C of temperature ranges low.This is the sensitive range that metallographic changes, and low quench rates will cause more low intensive bainite instead of martensitic formation (see figure 2).Therefore, the low intensive parts that can be shaped.
The present embodiment provides a kind of method, and the heat that described method is passed to cold mould by workpiece compared with this type of existing method reduces, thereby has reduced tool temperature compared with the conventional method, and has solved above-mentioned existing methodical problem.This embodiment, in maintenance essential quench rates and productivity, has reduced the heat being absorbed by mould.
Generally, in the present embodiment, in the time that boron steel sheet forwards mould to from stove, its by the solid medium of high heat conductance or fluid as air jet stream or air/liquid spraying cooling fast, therefore its temperature reduction when it is placed on mould.Therefore, in forming process (quenching again subsequently), described instrument absorbs less heat, and the rising of their temperature is minimized.Therefore, maintain low datum temperature and become easier, reduce costs and boost productivity.
Described novel method comprises the following steps:
First, more than the sheet metal blank of boron steel is heated to its austenitizing temperature in stove.In the present embodiment, by blank heating to 925 DEG C.Then by all thermal treatment at this temperature of described blank, to ensure that described material changes into austenite phase completely.As common process, in this state, described metal is soft and has high ductibility (being easily shaped).
Next step is to forward the material blank of austenitizing under the pressure shape with the described parts that are shaped.During described transfer, or in other embodiments at described thermometal blank rotary after described mould but before the described mould of contact, by described blank is contacted to quick cooling described blank with the material with high heat conductance.This material, i.e. this cooling way, can adopt following one, multiple or whole form: copper handle, blow air, spray Air-Water spraying or other fluid/liquid refrigerant to described blank.In the present embodiment, Air-Water spraying is applicable to described blank.This can lead control to described blank by the mist of pressurized water by multiple nozzles and realize.By this way, described blank is cooled to the temperature of about 600 DEG C.According to the CCT chart of Fig. 2, adjust fast enough rate of cooling to keep austenitic structure.It is contemplated that, in the work-piece cools stage, also carry out cooling and clean described instrument with identical refrigerant.
The rest part of described method is identical with ordinary method described herein.Therefore, described method can be illustrated as the common process shown in Fig. 1, but in transfer process between described stove and described mould, exists extra cooling.
By the stresses typical-strain curve of the boron steel shown in Fig. 4, can find out in the time that temperature drops to 600 DEG C from 800 DEG C the not too large variation of the ductility of described alloy.But the strain hardening of described alloy causes intensity almost to double.This strain hardening characteristic significantly increases the crystallized ability of alloy, (, is out of shape more field strength higher by causing to be more uniformly out of shape, cause that other regions deform, then to become intensity higher in described other regions, etc.), therefore slow down the trend of localized necking.This is even more important in hot stamping, because conventionally there is high friction, and strain hardening characteristic can reduce frictional influence.Therefore, the in the situation that of the present embodiment, can be at molded component from the temperature of approximately 600 DEG C of beginnings in mould, instead of in conventional way 800 DEG C; The more element of complicated shape can be shaped.Should emphasize, not this effect can realize by simply described steel disc being heated to lower starting temperature, because it must first abundant austenitizing.
Boron steel CCT in Fig. 2 is pictorialization, if alloy be cooled fast to about 500-600 DEG C it will still be in austenitic state.If cooling too slow, can form more low intensive Bainite Phases of Some; But present method has been avoided this point.In the method, because described blank is transferred to cold mould and maintain the temperature of 450-500 DEG C during whole forming technology in this temperature range, therefore during all inversion of phasess all occur in described cold mould maintenance, and austenite is converted into martensite, generation high-strength parts completely.
In existing method, the temperature of described molded component discharges it once being down to about 250 DEG C from described mould.In this temperature, inversion of phases completes, and further cooling in air (there is no the constraint of instrument) do not observe thermal distortion significantly.In these existing methods, parts are from the about 800 DEG C cold die quenching times (being that described parts remain on the time described mould) that are cooled to about 250 DEG C (differing from 550 DEG C) to need, according to the thickness of described workpiece and shape and component shape, it it is approximately 5-15 second.Therefore, the heat of significant quantity has to directly be absorbed by described mould, makes to be difficult to cooling described mould.
In the present embodiment, described parts are in approximately 600-500 DEG C of shaping.Therefore, during cold die quenching, only need by the temperature of parts from then on scope be down to about 250 DEG C (differing from 250 DEG C) compared with 500 DEG C of low sides.Therefore only have only about half of caloric requirement to extract from described mould, therefore the cooling requirement of described instrument greatly reduces.Therefore described tool design can simpler and described instrument can be more cheap.The lower temperature of described tool surfaces significantly reduces the described cold mould hold-time, and also significantly increases the rate of cooling in the temperature range of 500 DEG C to 250 DEG C.The described hold-time can be down to about 2-8 second.Therefore, can significantly improve productivity.This is vital for for example competitive motor corporation.In addition, lower tool surfaces temperature has reduced tool wear, and therefore significant prolongation life tools, this is added advantage to reducing production costs.
Claims (16)
1. by a method for steel disc molded component, said method comprising the steps of:
(a) described steel disc is heated to the temperature that austenitizing occurs; With
(b) by described steel disc molded component between mould, then the steel disc of cooling described shaping;
Wherein there is the additional step to described steel disc application cooling way at (a) with (b).
2. method according to claim 1, before wherein said additional step occurs in the steel disc of described heating is placed between described mould.
3. method according to claim 1, wherein said additional step occurs in when the steel disc of described heating is placed between described mould.
4. according to the method described in arbitrary aforementioned claim, wherein said cooling way comprises that cooling fluid is as gas, for example air; And/or wherein said cooling fluid comprises liquid, for example water, described method comprises leads the steel disc of control to described heating by described cooling fluid.
5. according to the method described in arbitrary aforementioned claim, wherein said cooling fluid is led control with the form of pressurized fluid stream.
6. according to the method described in arbitrary aforementioned claim, wherein said cooling fluid is led control and/or is led control with the form of spraying with the form of injection stream.
7. according to the method described in arbitrary aforementioned claim, wherein said cooling fluid is led control by time length, temperature and/or the flow of controlling described cooling fluid.
8. according to the method described in arbitrary aforementioned claim, wherein said cooling way comprises cooling plate, for example cold copper coin.
9. according to the method described in arbitrary aforementioned claim, wherein said cooling by increasing the cooling realization of use natural air transfer time.
10. according to the method described in arbitrary aforementioned claim, wherein said additional step comprises leads the steel disc of control to described heating by described cooling fluid, so that described steel disc is cooling to avoid described steel disc to enter Bainite Phases of Some fast enough.
11. according to the method described in arbitrary aforementioned claim, and wherein said additional step comprises leads control to the steel disc of described heating by described cooling fluid, so that described steel disc is cooling to be on average greater than the speed of 25 DEG C/sec.
12. according to the method described in arbitrary aforementioned claim, and wherein said additional step comprises leads the steel disc of control to described heating by described cooling fluid, so that the temperature of described steel disc is kept above the austenitizing temperature of described steel.
13. according to the method described in arbitrary aforementioned claim, and wherein said additional step comprises leads the steel disc of control to described heating by described cooling fluid, so that described steel disc is cooled to 500 DEG C-600 DEG C.
14. according to the method described in arbitrary aforementioned claim, further comprising the steps of: in the mode defining in arbitrary aforementioned claim, cooling fluid is led to control with cooling described mould.
15. according to the method described in arbitrary aforementioned claim, further comprising the steps of: in the mode defining in arbitrary aforementioned claim, cooling fluid is led to control to clean described mould.
16. according to the method depending on described in the claim 15 of claim 14, wherein said cooling and clean in same step and carry out.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| GBGB1116668.3A GB201116668D0 (en) | 2011-09-27 | 2011-09-27 | A method of forming parts from sheet steel |
| GB1116668.3 | 2011-09-27 | ||
| PCT/GB2012/052399 WO2013045933A1 (en) | 2011-09-27 | 2012-09-27 | A method of forming parts from sheet steel |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN103842528A true CN103842528A (en) | 2014-06-04 |
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Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201280047038.3A Pending CN103842528A (en) | 2011-09-27 | 2012-09-27 | A method of forming parts from sheet steel |
Country Status (9)
| Country | Link |
|---|---|
| US (1) | US20140352388A1 (en) |
| EP (1) | EP2761039A1 (en) |
| JP (1) | JP2014531319A (en) |
| KR (1) | KR20140068230A (en) |
| CN (1) | CN103842528A (en) |
| CA (1) | CA2849867A1 (en) |
| GB (1) | GB201116668D0 (en) |
| MX (1) | MX2014003603A (en) |
| WO (1) | WO2013045933A1 (en) |
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| CN106795578A (en) * | 2014-10-02 | 2017-05-31 | 奥钢联钢铁有限责任公司 | For the method for cooling during rolling steel plate |
| CN108453175A (en) * | 2017-02-17 | 2018-08-28 | 明信产业株式会社 | Heat stamping and shaping method |
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| GB2527486A (en) | 2014-03-14 | 2015-12-30 | Imp Innovations Ltd | A method of forming complex parts from sheet metal alloy |
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| BR102016023753A2 (en) * | 2016-10-11 | 2018-05-02 | Aethra Sistemas Automotivos S/A | PROCESS FOR PRODUCTION OF HIGH MECHANICAL RESISTANCE PUMP PARTS THROUGH CONTROLLED ELECTRICAL HEATING |
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- 2012-09-27 US US14/347,531 patent/US20140352388A1/en not_active Abandoned
- 2012-09-27 KR KR1020147011107A patent/KR20140068230A/en not_active Application Discontinuation
- 2012-09-27 WO PCT/GB2012/052399 patent/WO2013045933A1/en active Application Filing
- 2012-09-27 JP JP2014531319A patent/JP2014531319A/en active Pending
- 2012-09-27 MX MX2014003603A patent/MX2014003603A/en unknown
- 2012-09-27 CN CN201280047038.3A patent/CN103842528A/en active Pending
- 2012-09-27 EP EP12770201.7A patent/EP2761039A1/en not_active Withdrawn
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN106795578A (en) * | 2014-10-02 | 2017-05-31 | 奥钢联钢铁有限责任公司 | For the method for cooling during rolling steel plate |
| CN108453175A (en) * | 2017-02-17 | 2018-08-28 | 明信产业株式会社 | Heat stamping and shaping method |
| CN108453175B (en) * | 2017-02-17 | 2020-02-28 | 明信汽车科技株式会社 | Hot stamping forming method |
Also Published As
| Publication number | Publication date |
|---|---|
| EP2761039A1 (en) | 2014-08-06 |
| WO2013045933A1 (en) | 2013-04-04 |
| US20140352388A1 (en) | 2014-12-04 |
| CA2849867A1 (en) | 2013-04-04 |
| KR20140068230A (en) | 2014-06-05 |
| MX2014003603A (en) | 2015-01-16 |
| GB201116668D0 (en) | 2011-11-09 |
| JP2014531319A (en) | 2014-11-27 |
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