CN106119688A - A kind of high intensity Q ＆ P steel part preparation method of capability gradient distribution - Google Patents
A kind of high intensity Q ＆ P steel part preparation method of capability gradient distribution Download PDFInfo
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- CN106119688A CN106119688A CN201610583875.8A CN201610583875A CN106119688A CN 106119688 A CN106119688 A CN 106119688A CN 201610583875 A CN201610583875 A CN 201610583875A CN 106119688 A CN106119688 A CN 106119688A
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- 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
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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
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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- 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
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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Abstract
The present invention provides the high intensity Q&P steel part preparation method that a kind of capability gradient is distributed.The inventive method: stand-by steel part is heated to complete austenitizing, is cooled to M with default cooldown rate after insulations‑MfBetween temperature, insulation；Again heat stand-by steel part to MsThe partition temperature that point is above, the mould with flat-temperature zone and cooling zone is utilized to complete stamping to stand-by steel part, wherein, cooling zone is mould cold quenching direct to stand-by steel part in punching course, flat-temperature zone is to stand-by steel part constant temperature punching press partition, then the demoulding, is quenched to room temperature by cooling medium to stand-by steel part, finally gives the high intensity Q&P steel part of mechanical performance gradient distribution.The present invention has industrialization and easily realizes, the advantage that production efficiency is high, achieve the mechanical performance gradient of high intensity Q&P steel part zones of different so that automobile improves the energy-absorbing effect of regional area on the premise of ensureing safety, thus improves the crashworthiness that drip molding is overall.
Description
Technical field
The invention belongs to Q&P steel part forming technique field, be specifically related to a kind of by two step method Q&P steel by partition technique and
Warm forming technique synchronizes the control technology carried out, thus realizes the high intensity Q&P steel of zones of different mechanical performance gradient distribution
Part preparation method.
Background technology
For automobile lightweight and the technical goal of safety, in terms of automobile steel sheet, use ultrahigh-strength steel plates
Become the direction that automaker, iron and steel enterprise and Ge great scientific research institutions make joint efforts, in succession develop the first generation, the second filial generation
And third generation automobile steel.Q&P steel, as the one of advanced third generation automobile steel, is 2003, and researchers are at carbides-free
The Technology for Heating Processing of martensite steel quenching+(carbon) partition is proposed prepared on the Research foundation of bainitic steel, will 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
Spreading and making it stable in the austenite changed, last secondary quenching, to room temperature, obtains by martensite and retained austenite group
Become, there is high intensity and the tissue of preferable plasticity and toughness.So, in this Technology for Heating Processing, when primary quenching temperature is equal to joining
When dividing temperature, referred to as one-step method Q&P technique；When partition temperature is higher than primary quenching temperature, referred to as two-step method Q&P technique.When
Before, about Q&P steel manufacture method the most after deliberation a lot, such as Xu Fang is firm et al. " TRIP800 steel and the Q&P of hot forming steel
Technical study " point out 22MnB5 steel board is carried out Q&P PROCESS FOR TREATMENT, it is proposed that the Q&P technique of a step and two step method, do not relate to
And hot forming, wherein, in two step method Q&P technique, tissue there occurs obvious tempering transition；Chang Ying et al. is proposed for 22MnB5
For steel, load effect time stamping is to 22MnB5 steel martensite start temperature MsThe impact of point is very sensitive, when sheet material quilt
It is heated to above MsWhen more than some temperature shaping, owing to there is load effect, it will induction austenite carries to martensitic phase transformation
High MsPoint, shapes under the conditions of causing this and is difficult to accurately control its martensite start temperature and final temperature, thus affect targeted
The acquisition of energy, its optimal forming temperature is at about 700 DEG C；Horse is peaceful et al. proposes according to CCT curve, and 22MnB5 needs to be not less than 30
DEG C/the sufficiently martensitic phase transformation of cooldown rate guarantee of s, it is thus achieved that the residual austenite content martensite group less than 5%
Knit structure, therefore, for boron steel, during two step method partition, form the formation being difficult to avoid other dephasigns；For
The Q&P technique of 22MnB5 steel, when heat forming technology is combined, controls mostly at MsPoint temperature below, such as China Patent Publication No.
For: the technology described in CN103394573A " a kind of hot press-formed technique based on Q&P one-step ", is one by plate
Footwork MsCarrying out drop stamping below temperature, because press temperature is relatively low so that sheet forming poor fluidity, coefficient of friction is big, makes
Become mould loss serious, the most do not realize the feature of performance Gradient distribution；Duan Yanan et al. is at " a kind of high strength and ductility drop stamping one-tenth
The research and development of shape steel " described in technology, be by regulating its each transformation temperature equitemperature by the plate of special component
Value, the plate through austenitizing shapes in temperature-fall period, then proceedes to cool to MsPoint occurs below dynamic carbon partition, should
In technology, the plate property gap under various process conditions is the least, close to consistent；Wang Cunyu et al. proposes the Ovshinsky of Q&P technique
After bodyization insulation, steel plate carrying out in temperature-fall period hot forming, carry out follow-up partition the most again and process in heating furnace, this adds
Carry except to MsPoint, outside the temperature to partition process controls to have an impact then, because not having the constraint of mould during partition, makes
Obtaining drip molding and can not get the control of accurate shape, steel part also cannot realize performance Gradient distribution simultaneously.
During the use of auto parts and components, in order to simplify Joining Technology such as being welded, and improve the military service of parts
Performance, overall performance etc., researchers propose the steel part structure developing capability gradient distribution；China Patent Publication No. is:
Technology described in CN105463307A " a kind of Q&P steel with gradient structure and preparation method thereof ", is to be oozed by increase
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 by difference slab technique, such as China Patent Publication No. be:
Technology described in CN104668326A " hot stamping method of a kind of high strength steel parts capability gradientization distribution ", be
Cooling down rapidly after being heated by drop stamping steel plate austenitizing, be again heated to austenitizing region, carry out punching press, this technology exists two
The situation of secondary heating austenitizing, is unfavorable for the raising of production efficiency, and secondary austenitizing is unfavorable for the group that crystal grain refines
Knit acquisition, also do not meet the process characteristic of Q&P；Or by utilizing the selectivity cooling technique of mould in quenching process, by complete
The organizational structure of full austenite resolves into the different tissues such as martensite, pearlite, bainite, realizes the difference in performance,
Belong to the cold technique of full mould.To sum up, how to realize capability gradient by design new technology about in two step method Q&P technical process,
New through looking into, relevant report not yet occurs.
Summary of the invention
According to technical problem set forth above, and provide the high intensity Q&P steel part preparation method that a kind of capability gradient is distributed.
The present invention cools to M after mainly utilizing the plate insulation that will warm up austenitizing temperatures～MfBetween temperature and be incubated, then
Again plate is warmed up to higher than MsThe partition temperature of point, utilizes the mould with flat-temperature zone and cooling zone to strike out plate
After shape, cooling zone direct quenching；The demoulding after flat-temperature zone partition, then by cooling medium, stand-by steel part is quenched, quenched
Cheng Zhong, unstable austenite undergoes phase transition, and stable austenite remains in steel part, and the final mechanical performance gradient that obtains is distributed
High intensity Q&P steel part.
The technological means that the present invention uses is as follows:
The high intensity Q&P steel part preparation method of a kind of capability gradient distribution, it is characterised in that comprise the steps:
S1, low-carbon alloy steel being made stand-by steel part, the chemical component weight percentage ratio of this 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, is incubated 3～5 minutes, by the stand-by steel part of complete austenitizing
It is cooled to M with default cooldown rates-MfBetween temperature, it is incubated 0-30s；
S3, again heat stand-by steel part to MsThe partition temperature that point is above, utilizes the mould with flat-temperature zone and cooling zone
Completing stamping to 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
Steel part constant temperature punching press partition, the then demoulding, by cooling medium, stand-by steel part is quenched to room temperature, finally gives mechanical property
The high intensity Q&P steel part of Gradient distribution.
Further, the default cooldown rate in described step S2 is not less than 5 DEG C/s.
Further, described step S2 is cooled to Ms-MfSetting of primary quenching temperature between temperature and temperature retention time
Put to control martensite content less than 30% as boundary.
Further, in described step S3, stand-by steel part is quenched in punching course by cooling zone, it is thus achieved that martensite
Microstructure；Flat-temperature zone carries out partition process in punching course to stand-by steel part, insulation, pressurize 5～300s, then the demoulding, logical
Supercooling medium is quenched into room temperature to steel part, and in cooling procedure, some austenite undergoes phase transition, and the final austenite that obtains contains
Amount is no less than metastable austenite and the compound microstructure of martensite of 10%.
Further, in described step S3, the cooling zone of mould is the cooling mould with water channel or other cooling mediums；
The flat-temperature zone of described mould can maintain the mould of constant temperature by heating element heater or other thermals source；After the flat-temperature zone demoulding of described mould
Can be cooled down by the mode such as compressed gas or air cooling.
Compared with the prior art, the invention have the advantages that
1, in Q&P technique, mode of heating need not develop special heating furnace device, and industrialization easily realizes.
Although 2, the present invention adds the cost of subregion mould, but industrial production efficiency is high, does not affect current production
Flow process.
3, the present invention is higher than MsThe partition process punching press of temperature, the beneficially mobility of steel plate, reduce coefficient of friction, extend
Die life, improves formability.
4, the parts of present invention processing, it is achieved that the mechanical performance gradient of high intensity Q&P steel part zones of different so that
Automobile improves the energy-absorbing effect of regional area on the premise of ensureing safety, thus improves the collision safety that drip molding is overall
Property.
Accompanying drawing explanation
In order to be illustrated more clearly that the embodiment of the present invention or technical scheme of the prior art, below will be to embodiment or existing
In having technology to describe, the required accompanying drawing used is briefly described, it should be apparent that, the accompanying drawing in describing below is this
Some bright embodiments, for those of ordinary skill in the art, on the premise of not paying creative work, it is also possible to
Other accompanying drawing is 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 detailed description of the invention of the present invention, i.e. has high-strength steel in the Q&P technique of capability gradient distribution U-shaped
Mechanical property corresponding to part schematic diagram and each region, wherein, A is the position through constant temperature punching press/partition further quenching；B is directly punching
The position of pressure quenching.
Detailed description of the invention
For making the purpose of the embodiment of the present invention, technical scheme and advantage 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
The a part of 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 not making creative work premise, broadly falls into the scope of protection of the invention.
The high intensity Q&P steel part preparation method of a kind of capability gradient distribution, comprises the steps (as shown in Figure 1):
S1, low-carbon alloy steel being made stand-by steel part, the chemical component weight percentage ratio of this 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, is incubated 3～5 minutes, by the stand-by steel part of complete austenitizing
It is cooled to M being not less than the cooldown rate of 5 DEG C/ss-MfBetween temperature, being incubated 0-30s, its temperature is chosen with temperature retention time with control
Make a martensite content to be preferred less than 30%；
S3, again heat stand-by steel part to MsThe partition temperature that point is above, utilizes the mould with flat-temperature zone and cooling zone
Stand-by steel part is completed stamping, wherein, cooling zone in punching course to stand-by steel part direct quenching；Permanent
Warm area to stand-by steel part constant temperature punching press partition, the then demoulding, by cooling medium stand-by steel part is quenched to room temperature, final
High intensity Q&P steel part to mechanical performance gradient distribution.
The cooling zone of described mould is the cooling mould with water channel or other cooling mediums；The flat-temperature zone of described mould can
The mould of constant temperature is maintained by heating element heater or other thermals source；Compressed gas or sky can be passed through after the flat-temperature zone demoulding of described mould
The mode such as cold cools down.
Embodiment
Choosing the steel alloy being suitable to two step method Q&P technique, its composition of stand-by steel part is: C is 0.2%；Si is 1.0%；Mn
It is 5.0%；P and S controls below 0.005%, and remaining is Fe.
Stand-by steel part is heated to 850 DEG C, is incubated 5 minutes, obtain austenitizing group complete, uniform to stand-by steel part
Knit.Then M is cooled to the cooldown rate of 10 DEG C/ss～MfBetween temperature, choose 290 DEG C, be incubated 2s, now, the geneva of formation
Body burden is less than 30%；The most stand-by steel part is warmed up to 500 DEG C.Utilize the mould with subregion that plate is struck out steel
Part, a part of stand-by steel part is in cooling mould stamping and quench (B district)；A part of stand-by steel part is at 500 DEG C of flat-temperature zones
Complete punching press partition process, the demoulding after insulation, pressurize 30s, utilize air cooling mode to be quenched to room temperature (A district).
As it is shown on figure 3, dissection steel part, the mechanical property such as table 1 of contrast zones of different steel part:
Table 1U type part has the mechanical property of capability gradient distribution
| Mechanical property/subregion | A district | B district |
| Tensile strength/MPa | 865 | 1430 |
| Elongation percentage/% | 17 | 8 |
As can be seen from the table, A district (by constant temperature punching press/partition further quenching) and B district (direct quenching after punching press) obtains
Obvious capability gradient, all has notable difference including tensile strength and elongation percentage.
Last it is noted that various embodiments above is only in order to illustrate technical scheme, it is not intended to limit；To the greatest extent
The present invention has been described in detail by pipe with reference to foregoing embodiments, it will be understood by those within the art that: it depends on
So the technical scheme described in foregoing embodiments can be modified, or the most some or all of technical characteristic is entered
Row equivalent；And these amendments or replacement, do not make the essence of appropriate technical solution depart from various embodiments of the present invention technology
The scope of scheme.
Claims (5)
1. the high intensity Q&P steel part preparation method of a capability gradient distribution, it is characterised in that comprise the steps:
S1, low-carbon alloy steel being made stand-by steel part, the chemical component weight percentage ratio of this 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, is incubated 3～5 minutes, by the stand-by steel part of complete austenitizing with in advance
If cooldown rate be cooled to Ms-MfPrimary quenching temperature between temperature, is incubated 0-30s；
S3, again heat stand-by steel part to MsThe partition temperature that point is above, utilizes and has the mould of flat-temperature zone and cooling zone to stand-by
Steel part completes stamping, and wherein, cooling zone is mould cold quenching direct to stand-by steel part in punching course, and flat-temperature zone is to stand-by steel
Part constant temperature punching press partition, the then demoulding, by cooling medium, stand-by steel part is quenched to room temperature, finally gives mechanical property ladder
The high intensity Q&P steel part of degree distribution.
The high intensity Q&P steel part preparation method of capability gradient the most according to claim 1 distribution, it is characterised in that described
Default cooldown rate in step S2 is not less than 5 DEG C/s.
The high intensity Q&P steel part preparation method of capability gradient the most according to claim 1 distribution, it is characterised in that described
Step S2 is cooled to Ms-MfPrimary quenching temperature and the setting of temperature retention time between temperature contain to control a martensite
Amount is boundary less than 30%.
4. the high intensity Q&P steel part preparation method being distributed according to the capability gradient described in Claims 2 or 3, it is characterised in that institute
Stating in step S3, stand-by steel part is quenched in punching course by cooling zone, it is thus achieved that martensitic microstructure；Flat-temperature zone is in punching
During pressure, stand-by steel part is carried out partition process, insulation, pressurize 5～300s, then the demoulding, by cooling medium, steel part is quenched
To room temperature, in cooling procedure, some austenite undergoes phase transition, and the final residual austenite content that obtains is no less than the Asia of 10%
Steady austenite and the compound microstructure of martensite.
The high intensity Q&P steel part preparation method of capability gradient the most according to claim 4 distribution, it is characterised in that described
In step S3, the cooling zone of mould is the cooling mould with water channel or other cooling mediums；The flat-temperature zone of described mould can pass through
Heating element heater or other thermals source maintain the mould of constant temperature；Compressed gas or air cooling side can be passed through after the flat-temperature zone demoulding of described mould
Formula cools down.
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Cited By (9)
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| CN107326163A (en) * | 2017-06-12 | 2017-11-07 | 山东建筑大学 | A kind of method of Bainite Region isothermal+advanced high-strength steel of drop stamping deformation production |
| CN107520308A (en) * | 2017-08-25 | 2017-12-29 | 武汉理工大学 | A kind of high-strength steel servo medium temperature Sheet Metal Forming Technology |
| CN107557550A (en) * | 2017-08-22 | 2018-01-09 | 大连理工大学 | A kind of intensity adjustable high-strength steel automobile part preparation method |
| CN107828954A (en) * | 2017-10-26 | 2018-03-23 | 齐鲁工业大学 | Towards the pretreating process of high strength steel mechanical performance gradient distribution part |
| CN108060292A (en) * | 2018-01-19 | 2018-05-22 | 山东钢铁集团日照有限公司 | A kind of thermal quenching carbon partition warm working technique |
| CN108070791A (en) * | 2016-11-18 | 2018-05-25 | 北方工业大学 | High-strength anchor rod for mine reinforcement |
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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 |
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