CN106119688B - A kind of high intensity Q ＆ P steel part preparation methods of capability gradient distribution - Google Patents
A kind of high intensity Q ＆ P steel part preparation methods of capability gradient distribution Download PDFInfo
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- CN106119688B CN106119688B CN201610583875.8A CN201610583875A CN106119688B CN 106119688 B CN106119688 B CN 106119688B CN 201610583875 A CN201610583875 A CN 201610583875A CN 106119688 B CN106119688 B CN 106119688B
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 99
- 239000010959 steel Substances 0.000 title claims abstract description 99
- 238000009826 distribution Methods 0.000 title claims abstract description 21
- 238000002360 preparation method Methods 0.000 title claims abstract description 14
- 238000000034 method Methods 0.000 claims abstract description 40
- 238000001816 cooling Methods 0.000 claims abstract description 27
- 238000005192 partition Methods 0.000 claims abstract description 23
- 238000004080 punching Methods 0.000 claims abstract description 18
- 238000010791 quenching Methods 0.000 claims abstract description 16
- 230000000171 quenching effect Effects 0.000 claims abstract description 16
- 239000002826 coolant Substances 0.000 claims abstract description 6
- 238000009413 insulation Methods 0.000 claims abstract description 6
- 229910000734 martensite Inorganic materials 0.000 claims description 16
- 229910001566 austenite Inorganic materials 0.000 claims description 13
- 238000010438 heat treatment Methods 0.000 claims description 9
- 229910001339 C alloy Inorganic materials 0.000 claims description 6
- 238000012545 processing Methods 0.000 claims description 5
- 230000007704 transition Effects 0.000 claims description 4
- 239000012535 impurity Substances 0.000 claims description 3
- 238000002791 soaking Methods 0.000 claims description 3
- 239000000126 substance Substances 0.000 claims description 3
- 150000001875 compounds Chemical class 0.000 claims description 2
- 238000004519 manufacturing process Methods 0.000 abstract description 5
- 230000008901 benefit Effects 0.000 abstract description 3
- 230000000694 effects Effects 0.000 abstract description 3
- 238000000465 moulding Methods 0.000 abstract description 3
- 238000005516 engineering process Methods 0.000 description 15
- 230000008569 process Effects 0.000 description 10
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 4
- 229910052799 carbon Inorganic materials 0.000 description 4
- 230000009466 transformation Effects 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000011160 research Methods 0.000 description 2
- 238000007493 shaping process Methods 0.000 description 2
- 238000010792 warming Methods 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 229910000712 Boron steel Inorganic materials 0.000 description 1
- 229910000797 Ultra-high-strength steel Inorganic materials 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000036760 body temperature Effects 0.000 description 1
- 235000019628 coolness Nutrition 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000002224 dissection Methods 0.000 description 1
- 210000004209 hair Anatomy 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 238000005304 joining Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 238000012827 research and development Methods 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 238000004781 supercooling Methods 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- 238000011282 treatment Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Articles (AREA)
Abstract
The present invention provides a kind of high intensity Q＆P steel part preparation methods of capability gradient distribution.The inventive method：Stand-by steel part is heated to complete austenitizing, M is cooled to default cooldown rate after insulations‑MfBetween temperature, insulation；Stand-by steel part is heated again to MsThe partition temperature of the point above, stand-by steel part is completed using the mould with flat-temperature zone and cooling zone stamping, wherein, cooling zone is in punching course to the direct mould cold quenching of stand-by steel part, flat-temperature zone is to stand-by steel part constant temperature punching press and partition, then it is stripped, room temperature is quenched to stand-by steel part by cooling medium, finally gives the high intensity Q＆P steel parts of mechanical performance gradient distribution.There is the present invention industrialization easily to realize, the advantages of production efficiency is high, realize the mechanical performance gradient of high intensity Q＆P steel part different zones so that automobile improves the energy-absorbing effect of regional area on the premise of security is ensured, so as to improve the overall crashworthiness of drip molding.
Description
Technical field
The invention belongs to Q＆P steel part forming techniques field, and in particular to it is a kind of by two step method Q＆P steel will match somebody with somebody division technique and
The control technology that warm forming technique is synchronously carried out, so as to realize the high intensity Q＆P steel of different zones mechanical performance gradient distribution
Part preparation method.
Background technology
For automobile lightweight and the technical goal of security, in terms of automobile steel sheet, using ultrahigh-strength steel plates
Turn into the direction that automaker, iron and steel enterprise and major scientific research institutions make joint efforts, develop the first generation, the second generation in succession
And third generation automobile steel.The one kind of Q＆P steel as advanced third generation automobile steel, is 2003, researchers are in carbides-free
Made from the Technology for Heating Processing that martensite steel quenching+(carbon) partition is proposed on the Research foundation of bainitic steel, i.e., by steel by Ovshinsky
Body temperature is quenched into Ms~MfBetween a certain temperature, then in this temperature or higher than this temperature, make carbon from martensite to not
Spread and making it stable, last secondary quenching to room temperature, obtain by martensite and retained austenite group in the austenite of transformation
Into, the tissue with high intensity and preferable plasticity and toughness.So, in the Technology for Heating Processing, match somebody with somebody when primary quenching temperature is equal to
During point temperature, referred to as one-step method Q＆P techniques；When partition temperature is higher than primary quenching temperature, referred to as two-step method Q＆P techniques.When
Before, the manufacture method on Q＆P steel has been studied a lot, such as Xu Fang firm et al.《The Q＆P of TRIP800 steel and hot forming steel
Technical study》Point out 22MnB5 steel boards carrying out Q＆P PROCESS FOR TREATMENTs, it is proposed that the Q＆P techniques of a step and two step method, do not relate to
And hot forming, wherein, there occurs obvious tempering transition for tissue in two step method Q＆P techniques；Chang Ying et al. is proposed for 22MnB5
For steel, load when stamping is acted on to 22MnB5 steel martensite start temperatures MsThe influence of point is very sensitive, when sheet material quilt
It is heated to above MsWhen more than point temperature shaping, due to load effect be present, it will induce austenite and carried to martensitic traoformation
High MsPoint, shaping is difficult accurately to control its martensite start temperature and final temperature under the conditions of causing this, so as to influence Objective
The acquisition of energy, its optimal forming temperature is at 700 DEG C or so；Horse is peaceful et al. to be proposed according to CCT curve, and 22MnB5 needs to be not less than 30
DEG C/s cooldown rate just can guarantee that sufficiently martensitic phase transformation, obtain the martensite group that residual austenite content is no more than 5%
Structure is knitted, therefore, for boron steel, it is difficult the formation for avoiding other dephasigns to be formed during two step method partition；For
When the Q＆P techniques of 22MnB5 steel are combined with heat forming technology, control is in M mostlysPoint temperature below, such as China Patent Publication No.
For：CN103394573A《A kind of hot press-formed technique based on Q＆P one-step》Described in technology, be one by plate
Footwork MsDrop stamping is carried out below temperature, because press temperature is relatively low so that sheet forming poor fluidity, coefficient of friction is big, makes
It is serious into mould loss, do not realize the feature of capability gradient distribution yet；Duan Yanan et al. exists《A kind of high strength and ductility drop stamping into
The research and development of shape steel》Described in technology, be by adjusting its each transformation temperature equitemperature by the plate of special component
Value, shapes in temperature-fall period by the plate of austenitizing, then proceedes to cool to MsPoint occurs below dynamic carbon partition, should
Through the plate property gap very little under various process conditions in technology, close to unanimously；King deposits the Ovshinsky that space et al. proposes Q＆P techniques
After bodyization insulation, hot forming is carried out to steel plate in temperature-fall period, then carries out follow-up partition processing in heating furnace again, this adds
Carry except to MsPoint, outside then having an impact to the temperature control of partition process, because there is no the constraint of mould during partition, make
Obtain drip molding and cannot get accurate shape control, while steel part can not also realize that capability gradient is distributed.
During the use of auto parts and components, in order to simplify be welded wait Joining Technology, and raising parts military service
Performance, overall performance etc., researchers propose the steel part structure for developing capability gradient distribution；China Patent Publication No. is：
CN105463307A《A kind of Q＆P steel with gradient structure and preparation method thereof》Described in technology, be by increase ooze
Carbon technique realizes the feature of tissue gradient, but the process time is long, is unsuitable for large-scale mass production；High-strength steel gradient performance
Realization be currently mostly focused on hot formed quenching technical, or be by poor slab technique, such as China Patent Publication No.：
CN104668326A《A kind of hot stamping method of high strength steel parts capability gradientization distribution》Described in technology, be
Cooled down rapidly after drop stamping steel plate austenitizing is heated, be again heated to austenitizing region, carry out punching press, the technology has two
The situation of secondary heating austenitizing, is unfavorable for the raising of production efficiency, and secondary austenitizing is unfavorable for the group of crystal grain refinement
Acquisition is knitted, does not also meet Q＆P process characteristic；Or by utilizing the selective cooling technique of mould in quenching process, will be complete
The institutional framework of full austenite resolves into the different tissues such as martensite, pearlite, bainite, to realize the difference in performance,
Belong to the cold technique of full mould.To sum up, on how by designing new technology to realize capability gradient in two step method Q＆P technical process,
It is new through looking into, not yet there is relevant report.
The content of the invention
According to technical problem set forth above, and provide a kind of high intensity Q＆P steel part preparation methods of capability gradient distribution.
It is of the invention mainly to utilize the plate that will warm up austenitizing temperature to cool to M after being incubateds~MfBetween temperature and it is incubated, then
Plate is warming up to higher than M againsThe partition temperature of point, is struck out using the mould with flat-temperature zone and cooling zone to plate
After shape, cooling zone direct quenching；It is stripped after flat-temperature zone partition, then stand-by steel part is quenched by cooling medium, it is quenched
Cheng Zhong, unstable austenite are undergone phase transition, and stable austenite is remained in steel part, final to obtain mechanical performance gradient distribution
High intensity Q＆P steel parts.
The technological means that the present invention uses is as follows：
A kind of high intensity Q＆P steel part preparation methods of capability gradient distribution, it is characterised in that comprise the following steps：
S1, low-carbon alloy steel is made to stand-by steel part, the chemical component weight percentage of the low-carbon alloy steel is：C：0.1
~0.51%；Si：0~2.0%；Mn：0~6.0%；Cr：0~1.1%；Ni：0~3.0%；V：0~0.2%；Mo：0~
0.7%；Nb：0~0.05%；P≤0.015%；S≤0.005%；N≤0.006%；O≤30ppm；Surplus is Fe and can not
The impurity avoided；
S2, stand-by steel part is heated to complete austenitizing, 3~5 minutes is incubated, by the stand-by steel part of complete austenitizing
M is cooled to default cooldown rates-MfBetween temperature, 0-30s is incubated；
S3, stand-by steel part is heated again to MsThe partition temperature of the point above, utilizes the mould with flat-temperature zone and cooling zone
It is stamping to the completion of stand-by steel part, wherein, cooling zone is to stand-by steel part direct quenching in punching course, and flat-temperature zone is to stand-by
The punching press of steel part constant temperature and partition, are then stripped, are quenched to room temperature to stand-by steel part by cooling medium, finally give mechanical property
The high intensity Q＆P steel parts of gradient distribution.
Further, the default cooldown rate in the step S2 is not less than 5 DEG C/s.
Further, it is cooled to M in the step S2s-MfPrimary quenching temperature and soaking time between temperature are set
Put to control a martensite content to be no more than 30% for boundary.
Further, in the step S3, cooling zone quenches in punching course to stand-by steel part, obtains martensite
Microstructure；Flat-temperature zone carries out partition processing, insulation, 5~300s of pressurize in punching course to stand-by steel part, then is stripped, and leads to
Supercooling medium is quenched into room temperature to steel part, and some austenite is undergone phase transition in cooling procedure, and the final austenite that obtains contains
The compound microstructure of metastable austenite of the amount no less than 10% and martensite.
Further, the cooling zone of mould is the cooling mould with water channel or other cooling mediums in the step S3；
The flat-temperature zone of the mould can maintain the mould of constant temperature by heating element heater or other thermals source；After the flat-temperature zone demoulding of the mould
It can be cooled down by modes such as compressed gas or air coolings.
Compared with the prior art, the present invention has advantages below：
1st, mode of heating need not develop special heating furnace device in Q＆P techniques, industrialize and easily realize.
Although the 2, the present invention adds the cost of subregion mould, industrial production efficiency is high, does not influence current production
Flow.
3rd, the present invention is higher than MsThe partition process punching press of temperature, beneficial to the mobility of steel plate, reduce coefficient of friction, extend
Die life, improve formability.
4th, the parts that the present invention processes, the mechanical performance gradient of high intensity Q＆P steel part different zones is realized so that
Automobile improves the energy-absorbing effect of regional area on the premise of security is ensured, so as to improve the overall collision safety of drip molding
Property.
Brief description of the drawings
In order to illustrate more clearly about the embodiment of the present invention or technical scheme of the prior art, below will be to embodiment or existing
There is the required accompanying drawing used in technology description to be briefly described, it should be apparent that, drawings in the following description are this hairs
Some bright embodiments, for those of ordinary skill in the art, without having to pay creative labor, can be with
Other accompanying drawings are obtained according to these accompanying drawings.
Fig. 1 is the preparation method schematic flow sheet of the present invention.
Fig. 2 is the punching course schematic diagram of the present invention.
Fig. 3 is a kind of embodiment of the present invention, i.e., high-strength steel is U-shaped in the Q＆P techniques with capability gradient distribution
Mechanical property corresponding to part schematic diagram and each region, wherein, A is the position quenched again through constant temperature punching press/partition；B is directly to rush
Press the position of quenching.
Embodiment
To make the purpose, technical scheme and advantage of the embodiment of the present invention clearer, below in conjunction with the embodiment of the present invention
In accompanying drawing, the technical scheme in the embodiment of the present invention is clearly and completely described, it is clear that described embodiment is
Part of the embodiment of the present invention, rather than whole embodiments.Based on the embodiment in the present invention, those of ordinary skill in the art
The every other embodiment obtained under the premise of creative work is not made, belongs to the scope of protection of the invention.
A kind of high intensity Q＆P steel part preparation methods of capability gradient distribution, comprise the following steps (as shown in Figure 1)：
S1, low-carbon alloy steel is made to stand-by steel part, the chemical component weight percentage of the low-carbon alloy steel is：C：0.1
~0.51%；Si：0~2.0%；Mn：0~6.0%；Cr：0~1.1%；Ni：0~3.0%；V：0~0.2%；Mo：0~
0.7%；Nb：0~0.05%；P≤0.015%；S≤0.005%；N≤0.006%；O≤30ppm；Surplus is Fe and can not
The impurity avoided；
S2, stand-by steel part is heated to complete austenitizing, 3~5 minutes is incubated, by the stand-by steel part of complete austenitizing
M is cooled to the cooldown rate not less than 5 DEG C/ss-MfBetween temperature, 0-30s is incubated, its temperature is chosen with soaking time to control
Martensite content of system is preferred no more than 30%；
S3, stand-by steel part is heated again to MsThe partition temperature of the point above, utilizes the mould with flat-temperature zone and cooling zone
Stamping to the completion of stand-by steel part, as shown in Figure 2 wherein, cooling zone is in punching course to stand-by steel part direct quenching；It is permanent
Then warm area is stripped to stand-by steel part constant temperature punching press and partition, room temperature is quenched to stand-by steel part by cooling medium, final
To the high intensity Q＆P steel parts of mechanical performance gradient distribution.
The cooling zone of the mould is the cooling mould with water channel or other cooling mediums；The flat-temperature zone of the mould can
The mould of constant temperature is maintained by heating element heater or other thermals source；It can pass through compressed gas or sky after the flat-temperature zone demoulding of the mould
The mode such as cold is cooled down.
Embodiment
The steel alloy suitable for two step method Q＆P techniques is chosen, its composition of stand-by steel part is：C is 0.2%；Si is 1.0%；Mn
For 5.0%；Below 0.005%, remaining is Fe for P and S controls.
Stand-by steel part is heated to 850 DEG C, is incubated 5 minutes, complete, uniform austenitizing group is obtained to stand-by steel part
Knit.Then M is cooled to 10 DEG C/s cooldown rates~MfBetween temperature, 290 DEG C are chosen, is incubated 2s, now, the geneva of formation
Body content is no more than 30%；Then stand-by steel part is warming up to 500 DEG C.Plate is carried out using the mould with subregion to strike out steel
Part, a part of stand-by steel part is stamping in mould is cooled down and quenches in (B areas)；A part of stand-by steel part is at 500 DEG C of flat-temperature zones
Punching press and partition process are completed, is stripped after insulation, pressurize 30s, room temperature (A areas) is quenched to using air cooling mode.
As shown in figure 3, dissection steel part, the mechanical property such as table 1 of contrast different zones steel part：
Table 1U type parts have the mechanical property that capability gradient is distributed
| Mechanical property/subregion | A areas | B areas |
| Tensile strength/MPa | 865 | 1430 |
| Elongation percentage/% | 17 | 8 |
As can be seen from the table, A areas (being quenched again by constant temperature punching press/partition) and B areas (direct quenching after punching press) obtains
Obvious capability gradient, including tensile strength and elongation percentage all have a notable difference.
Finally it should be noted that：Various embodiments above is merely illustrative of the technical solution of the present invention, rather than its limitations；To the greatest extent
The present invention is described in detail with reference to foregoing embodiments for pipe, it will be understood by those within the art that：Its according to
The technical scheme described in foregoing embodiments can so be modified, either which part or all technical characteristic are entered
Row equivalent substitution；And these modifications or replacement, the essence of appropriate technical solution is departed from various embodiments of the present invention technology
The scope of scheme.
Claims (5)
1. a kind of high intensity Q＆P steel part preparation methods of capability gradient distribution, it is characterised in that comprise the following steps：
S1, low-carbon alloy steel is made to stand-by steel part, the chemical component weight percentage of the low-carbon alloy steel is：C：0.1~
0.51%；Si：0~2.0%；Mn：0~6.0%；Cr：0~1.1%；Ni：0~3.0%；V：0~0.2%；Mo：0~
0.7%；Nb：0~0.05%；P≤0.015%；S≤0.005%；N≤0.006%；O≤30ppm；Surplus is Fe and can not
The impurity avoided；
S2, stand-by steel part is heated to complete austenitizing, 3~5 minutes is incubated, by the stand-by steel part of complete austenitizing with pre-
If cooldown rate be cooled to Ms-MfPrimary quenching temperature between temperature, it is incubated 0-30s；
S3, stand-by steel part is heated again to MsThe partition temperature of the point above, using the mould with flat-temperature zone and cooling zone to stand-by
Steel part completion is stamping, wherein, cooling zone is to the direct mould cold quenching of stand-by steel part in punching course, and flat-temperature zone is to stand-by steel
The punching press of part constant temperature and partition, are then stripped, room temperature are quenched to stand-by steel part by cooling medium, finally give mechanical property ladder
Spend the high intensity Q＆P steel parts of distribution.
2. the high intensity Q＆P steel part preparation methods of capability gradient distribution according to claim 1, it is characterised in that described
Default cooldown rate in step S2 is not less than 5 DEG C/s.
3. the high intensity Q＆P steel part preparation methods of capability gradient distribution according to claim 1, it is characterised in that described
M is cooled in step S2s-MfThe setting of primary quenching temperature and soaking time between temperature is to control a martensite to contain
Amount is boundary no more than 30%.
4. the high intensity Q＆P steel part preparation methods of the capability gradient distribution according to Claims 2 or 3, it is characterised in that institute
State in step S3, cooling zone quenches in punching course to stand-by steel part, obtains martensitic microstructure；Flat-temperature zone is rushing
Partition processing, insulation, 5~300s of pressurize are carried out during pressure to stand-by steel part, then is stripped, steel part is quenched by cooling medium
To room temperature, some austenite is undergone phase transition in cooling procedure, the final Asia for obtaining residual austenite content and being no less than 10%
The compound microstructure of steady austenite and martensite.
5. the high intensity Q＆P steel part preparation methods of capability gradient distribution according to claim 4, it is characterised in that described
The cooling zone of mould is the cooling mould with water channel or other cooling mediums in step S3；The flat-temperature zone of the mould can pass through
Heating element heater or other thermals source maintain the mould of constant temperature；It can pass through compressed gas or air cooling side after the flat-temperature zone demoulding of the mould
Formula is cooled down.
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| CN113088821A (en) * | 2021-04-02 | 2021-07-09 | 河北工程大学 | Gradient grain structure high-strength and high-plasticity matching low alloy steel and preparation method thereof |
Citations (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102212742A (en) * | 2011-05-16 | 2011-10-12 | 马鸣图 | Hot-stamping automobile part with flexibly-distributed intensity and control method thereof |
| CN103215491A (en) * | 2013-02-01 | 2013-07-24 | 河北联合大学 | Method for preparing carbon-silicon-manganese-series Q&P steel through alloy element partitioning |
| CN103215516A (en) * | 2013-04-09 | 2013-07-24 | 宝山钢铁股份有限公司 | 700MPa high strength hot rolling Q&P steel and manufacturing method thereof |
| CN103394573A (en) * | 2013-08-02 | 2013-11-20 | 上海交通大学 | Hot stamping forming process based on Q&P one-step method |
| CN103409613A (en) * | 2013-08-30 | 2013-11-27 | 上海交通大学 | Method for realizing gradient property distribution of hot stamping workpiece |
| CN103521581A (en) * | 2013-10-23 | 2014-01-22 | 武汉理工大学 | Method and die for obtaining mechanical performance gradient hot stamping part |
| CN104195455A (en) * | 2014-08-19 | 2014-12-10 | 中国科学院金属研究所 | Hot stamping bake toughening steel based on carbon partitioning principle and processing method thereof |
| CN104588473A (en) * | 2014-11-28 | 2015-05-06 | 中国科学院金属研究所 | High-strength plastic product automobile part hot stamping and carbon partition integrated process |
| CN104630647A (en) * | 2015-02-02 | 2015-05-20 | 大连理工大学 | Preparation method of high-strength hot galvanizing Q&P steel |
| CN104668326A (en) * | 2015-03-05 | 2015-06-03 | 山东大王金泰集团有限公司 | Hot stamping method for performance gradient distribution of high-strength steel parts |
| CN104831020A (en) * | 2015-04-03 | 2015-08-12 | 燕山大学 | Method for stamping quenching molding in non-uniform temperature field |
-
2016
- 2016-07-22 CN CN201610583875.8A patent/CN106119688B/en not_active Expired - Fee Related
Patent Citations (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102212742A (en) * | 2011-05-16 | 2011-10-12 | 马鸣图 | Hot-stamping automobile part with flexibly-distributed intensity and control method thereof |
| CN103215491A (en) * | 2013-02-01 | 2013-07-24 | 河北联合大学 | Method for preparing carbon-silicon-manganese-series Q&P steel through alloy element partitioning |
| CN103215516A (en) * | 2013-04-09 | 2013-07-24 | 宝山钢铁股份有限公司 | 700MPa high strength hot rolling Q&P steel and manufacturing method thereof |
| CN103394573A (en) * | 2013-08-02 | 2013-11-20 | 上海交通大学 | Hot stamping forming process based on Q&P one-step method |
| CN103409613A (en) * | 2013-08-30 | 2013-11-27 | 上海交通大学 | Method for realizing gradient property distribution of hot stamping workpiece |
| CN103521581A (en) * | 2013-10-23 | 2014-01-22 | 武汉理工大学 | Method and die for obtaining mechanical performance gradient hot stamping part |
| CN104195455A (en) * | 2014-08-19 | 2014-12-10 | 中国科学院金属研究所 | Hot stamping bake toughening steel based on carbon partitioning principle and processing method thereof |
| CN104588473A (en) * | 2014-11-28 | 2015-05-06 | 中国科学院金属研究所 | High-strength plastic product automobile part hot stamping and carbon partition integrated process |
| CN104630647A (en) * | 2015-02-02 | 2015-05-20 | 大连理工大学 | Preparation method of high-strength hot galvanizing Q&P steel |
| CN104668326A (en) * | 2015-03-05 | 2015-06-03 | 山东大王金泰集团有限公司 | Hot stamping method for performance gradient distribution of high-strength steel parts |
| CN104831020A (en) * | 2015-04-03 | 2015-08-12 | 燕山大学 | Method for stamping quenching molding in non-uniform temperature field |
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