CN104928456B - A kind of manufacture method for improving general chill ferritic lightweight steel ductility - Google Patents
A kind of manufacture method for improving general chill ferritic lightweight steel ductility Download PDFInfo
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Abstract
A kind of manufacture method for improving general chill ferritic lightweight steel ductility, it includes：Cold rolling preceding pretreatment, cold rolling and continuous annealing heat treatment are carried out to hot rolled plate, wherein, cold rolling preceding pretreatment includes cold rolling predeformation and recrystallization annealing.The present invention by hot rolled steel plate it is cold rolling it is preceding first pre-processed, to refine steel high temperature delta ferrite, steel plate structural homogenity after increase is annealed.The steel plate that the present invention is prepared significantly improves ductility and strength and ductility product on the basis of higher-strength is kept.
Description
Technical field
The invention belongs to ferrite lightweight rings domain, and in particular to a kind of system of the general chill ferritic lightweight steel ductility of raising
Make method.
Background technology
Traditional low-intensity rank steel are substituted using high-strength steel and advanced high-strength steel, the specific strength of automobile steel can be improved
(the ratio between intensity and density) and the thickness for reducing structural member, realizes vehicle structure lightweight.Improve the another of automobile steel specific strength
A kind of effective way is that the density of steel is reduced on the basis of the above-mentioned excellent mechanical property of high-strength steel is maintained.Therefore, develop low
Density, high-strength tenacity steel plate are precisely in order to tackle the active demand of further automobile lightweight.
Low density steel typically realizes the reduction of carbon steel density by adding more alloy element Al.At present, researcher
Exploitation is just directed to based on phase-change induced plastic (Transformation-induced plasticity, abbreviation TRIP) reinforcing
Mechanism and the ferrite low density steel rich in Al.The alloy content of this kind of ferritic steel with other low-density steel grades (such as ferrite-
Austenitic duplex steel and austenitic steel) alloy content compare it is low, thus it not only have low-density, high strength characteristics, together
When it also have good manufacturability.The microscopic structure of ferrite low density steel based on phase-change induced plastic mechanism it is main by
The metastable state of ferrite (including high temperature delta ferrite and the alpha ferrite through being mutually deformed into) and appropriate volume fraction is remaining difficult to understand
Family name's body is constituted.Metastable state retained austenite is induced progressive transitions for martensite under subsequent external deformation effect, to improve steel
The deformation processing hardening of plate, and then improve armor plate strength and improve ductility.
In the prior art, the main manufacturing processes flow of low-density and high-strength ferrite steel plate be followed successively by smelting and continuous casting,
Hot rolling, cold rolling and continuous annealing.High temperature ferrite (i.e. delta ferrite) is the main composition phase of ferrite lightweight steel.Molten steel solidification
After the completion of process, delta ferrite is retained all the time in subsequent thermal processing and heat treatment process, and it has following two characteristics：δ
Ferrite will not obtain structure refinement by solid-state phase changes；In actual production process, delta ferrite is not easy to by hot rolling, cold
Roll and occur fully dynamic and Static Recrystallization with continuous annealing process and refine.
In high Mn, the low-density ferrite steel plate of high Al content, although hot rolling and continuous annealing can make microcosmic group of delta ferrite
Hair-weaving life is replied and partial, re-crystallization, but strip delta ferrite still can largely exist in the matrix of steel, and these strips
Delta ferrite often has relatively low deformation plasticity.So, although annealed sheet steel matrix is dispersed with enough metastable state residual austenites
Body, but because the deformation plasticity of delta ferrite is poor, under external force the delta ferrite in annealed sheet steel mostly occur cleavage fracture
Failure mode, correspondingly, the integral extension of annealed sheet steel can also be reduced.In addition, the presence of a large amount of ribbon delta ferrites also can
Reduce the bending property of steel plate.
Therefore, make to be based on phase-change induced modeling to improve the deformation plasticity of delta ferrite in the urgent need to refinement delta ferrite tissue
The plasticity of the ferrite low density steel of property strengthening mechanism is significantly improved.
The content of the invention
It is an object of the invention to provide a kind of manufacture method for improving general chill ferritic lightweight steel ductility, keep compared with
On the basis of high intensity, the ductility and strength and ductility product (i.e. the product of intensity and ductility) of ferrite lightweight steel are significantly improved.
To reach above-mentioned purpose, the technical scheme is that：
A kind of manufacture method for improving general chill ferritic lightweight steel ductility, it comprises the following steps：
1) cold rolling predeformation
Cold rolling predeformation is carried out to hot rolled plate, deflection is 30~80%；The main chemical compositions weight percent of hot rolled plate
Than for：C：0.05~0.50%, Mn：0.25~12.0%, Al：3.0~7.0%, also contain：Si：0.01~1.5%, Ti：
0.005~0.6%, Nb：0.005~0.2%, V：0.005~0.5%, Cr：0.01~0.5%, Mo：0.01~0.5%, Ni：
0.05~2.0%, Cu：One or more of 0.05~1.0%, remaining is Fe and inevitable impurity；
2) recrystallization annealing
Using cover annealing, soaking temperature is 660~850 DEG C, and soaking time is 0.5~48h；
3) it is cold rolling
Cold rolling deflection is 30~90%；
4) continuous annealing is heat-treated
Cold-reduced sheet is heated to after 750~950 DEG C of soaking temperature to be incubated 30~600s, medium temperature is first cooled to, then it is cold
But to 200~500 DEG C of partition stabilization temperature, 0~600s is incubated, wherein, the rate of heat addition of cold-rolled steel sheet is 1~20 DEG C/s；
950 DEG C of 650 DEG C≤medium temperature ＜；The cooldown rate that steel plate after all heat-treated is cooled to medium temperature from soaking temperature is 1
~10 DEG C/s；Steel plate after all heat-treated from medium temperature be cooled to the cooldown rate of partition stabilization temperature for 1~150 DEG C/
S, and the cooldown rate is cooled to the cooldown rate of medium temperature not less than steel plate from soaking temperature.Partition stabilization processes knot
Shu Hou, by steel plate with 1~20 DEG C/s cooldown rate slow cooling to room temperature.
Further, step 1) in, hot rolled plate rolling：1000~1250 DEG C of heating-up temperature, soaking time is 0.5~3h, eventually
Temperature >=800 DEG C are rolled, hot rolled plate is batched at 300~750 DEG C；After cooling, pickling.
It is preferred that, step 1) in, the deflection of cold rolling predeformation is 40~60%.
It is preferred that, step 3) in, cold rolling deflection is 50~70%.
The microscopic structure of ferrite lightweight steel prepared by the present invention is mainly by the ferrite that fully recrystallizes and metastable
State retained austenite constitutes.
The reasons why design and manufacture technology of the present invention, is as follows：
(1) cold rolling preceding pretreating process
Cold rolling preceding pretreating process includes cold rolling predeformation and recrystallization annealing successively, and the purpose is to refine steel high temperature δ
Ferrite, steel plate structural homogenity after increase annealing.
Cold rolling predeformation is carried out to the hot rolled steel plate after pickling, deflection is 30~80%, preferably 40~60%.It is cold rolling pre-
Deformation stores deformation energy in steel matrix, is to be carried out during high temperature delta ferrite is organized in follow-up bell furnace recrystallization annealing
Recrystallization provides driving force.Increase the deflection of cold rolling predeformation, be favorably improved deformation energy storage and recrystallization driving force, so that
Increase the degree of refinement of deformation delta ferrite and improve the structural homogenity of annealed sheet steel.But if the deformation of cold rolling predeformation
Amount is excessive, because processing hardening causes the resistance of deformation of material very high.
Recrystallization annealing uses cover annealing, and cover annealing process, which is mainly, heats the coil of strip through cold rolling predeformation
It is incubated after to soaking temperature, this process is used for refining steel high temperature delta ferrite tissue and improves the structural homogenity of steel plate.
In addition, the delta ferrite refined can be the follow-up delta ferrite in continuous annealing heat treatment process of the steel plate through cold-rolling deformation
Further refinement more Recrystallization nucleation points are provided.The soaking temperature of cover annealing is 660~850 DEG C.When soaking temperature
Degree be less than 660 DEG C, delta ferrite tissue recrystallization carry out it is insufficient；When soaking temperature is higher than 850 DEG C, δ iron is plain after recrystallization
Body crystal grain can occur excessive coarsening.Soaking time can be adjusted by suitably changing soaking temperature, long soaking time influence
Production efficiency, therefore, the soaking time of present invention control cover annealing are no more than 48 hours.
Neutral or restitutive protection's atmosphere (such as N is used during recrystallization annealing2Gas or N2+H2Mixed gas), to prevent
Surface of steel plate is aoxidized and decarburization.After recrystallization annealing terminates, steel plate is cooled to room temperature.
(2) cold-rolling process
Cold-rolling deformation is carried out to the steel plate after recrystallization annealing to specific thickness, cold rolling reduction is 30~90%, preferably
50~70%.Increase cold rolling reduction, austenitic formation speed can be improved during follow-up continuous annealing and is promoted high
The further refinement of warm delta ferrite.But if cold rolling reduction is excessive, because processing hardening causes the resistance of deformation of material very
Height, preparing the cold-rolled steel sheet of specific thickness and good profile becomes abnormal difficult.
(3) continuous annealing process
Cold-rolled steel sheet is heat-treated using continuous annealing process, delta ferrite is occurred further recrystallization softening and acquisition
Appropriate metastable state retained austenite.Continuous annealing process of the present invention mainly includes equal thermal process and partition stabilization procedures, such as Fig. 1
It is shown.
Referring to Fig. 1, by cold-rolled steel sheet with rate of heat addition v0It is heated to being incubated t1 (soaking time) times after soaking temperature T1
Section.Soaking temperature T1 selection needs the recrystallization softening and austenite phase transformation that ensure deformation delta ferrite to occur simultaneously, therefore chooses
v0=1~20 DEG C/s；T1=750~950 DEG C；T1=30~600s.When soaking temperature T1 is less than 750 DEG C and soaking time t1 is small
In 30s, cold-rolled steel sheet matrix not yet fully occurs carbide in austenitizing, including matrix and is not yet completely dissolved generation Austria
Family name's body particle, and ribbon deformation delta ferrite can not fully be recrystallized and refined.
When soaking temperature T1 is higher than 950 DEG C and soaking time t1 is longer than after 600s, all heat-treated Austria in steel matrix tissue
The grain coarsening of family name's body and the reduction of austenite C content, both of which reduce stabilization of austenite in steel, so as to cause after annealing cooling
Residual austenite content is reduced in steel matrix, and retained austenite mechanical stability can also be reduced.Correspondingly, annealed sheet steel
Mechanical property deteriorate.
Referring to Fig. 1, by the steel plate after all heat-treated first with slow cooling speed v2Slow cooling to after medium temperature T2 immediately with rapid cooling
Speed v3It is cooled to after partition stabilization temperature T3 and is incubated t3 (partition the stabilizes the time) periods.Slow cooling speed v2With centre temperature
Degree T2 selection is mainly consideration：The austenite of all heat-treated formation is avoided to be cooled to the slow cooling of medium temperature by soaking temperature
Section, which decomposes generation carbide, easily operated control, makes annealing heat-treats smoothly be transitioned into rapid cooling section from soaking zone and maintain cold rolling
The plate shape of steel plate.The present invention chooses v2=1~10 DEG C/s, 950 DEG C of 650 DEG C≤T2 ＜；In rapid cooling section, v3=1~150 DEG C/s, and
And v3≥v2, equally it is to ensure that the austenite formed after all heat-treated is not decomposed in rapid cooling section experience different temperatures.
Partition stabilization processes section, partition stabilization temperature T3=200~500 DEG C；Partition stabilisation time t3=0~
600s.The present invention is using partition stabilization processes (i.e. austemper), further to improve stabilization of austenite.Partition
In stabilization procedures, partial austenitic can be converted into bainite ferrite, while carbide formation is suppressed, C atoms are from shellfish
Family name's body ferrite spreads to improve the C content and stability of retained austenite into remaining austenite.
Partition stabilization temperature T3 can cause austenite decomposition when being higher than 500 DEG C, so as to consume C and reduction in austenite
Stability of retained austenite；And partition stabilization temperature T3 temperature is less than 200 DEG C, then delay the generation of partition process.To avoid
Austenite is decomposed in long-time partition stabilization procedures, and is considered from effective and economy, chooses partition steady
Surely time t3 is changed no more than 600s.After partition stabilization processes terminate, steel plate is cooled to room temperature, v4=1 with cooldown rate v4
~20 DEG C/s.
(4) hot rolled plate rolling mill practice
1000~1250 DEG C of heating-up temperature in the hot rolled plate operation of rolling of the present invention, can be caused when heating-up temperature is more than 1250 DEG C
Strand burning, strand internal grain tissue is thick and reduces hot-working character, and superhigh temperature can cause blank surface decarburization
Seriously.When heating-up temperature is less than 1000 DEG C, strand is after high-pressure water descaling and breaking down, and finishing temperature is too low and causes the change of material
Shape drag is excessive, so that hot rolled steel plate not only free of surface defects but also with specific thickness can not be produced.
The present invention needs to control finishing temperature to complete the hot rolling to strand more than 800 DEG C.Finishing temperature is too low to be caused
Casting blank deformation drag is too high, it is difficult to thickness specification and the cold-rolled steel sheet without edge fault needed for producing；In addition, for this hair
For bright component system, finishing temperature is higher than 800 DEG C, contributes to hot rolling strip high temperature ferrite inside strand (to be also referred to as δ iron element
Body) occur Recovery and recrystallization.
The present invention batch hot rolled plate at 300~750 DEG C, if coiling temperature be higher than 750 DEG C, can cause κ carbide or
The excessive nodularization of cementite and roughening, are unfavorable for obtaining the retained austenite of uniform small stable after follow-up cold-rolled steel sheet annealing.Separately
Outside, coiling temperature is too high, easily causes flat volume, and head, middle part and the afterbody material microstructure inhomogeneities of hot rolled coil
Increase, so cause annealed steel volume header, in, afterbody microscopic structure and performance it is uneven.In addition, coiling temperature is at least 300 DEG C,
To suppress to form excessive martensitic structure in hot rolled steel plate, it is ensured that hot rolled steel plate has good cold-rolling deformation ability.
Compared with prior art, by optimizing manufacturing process, the elongation percentage and strength and ductility product of steel plate prepared by the present invention
Improve more than 20%.Manufacturing process of the present invention is applicable to manufacture all rich in Al and using ferrite as the general cold of main composition phase
TRIP steel plates, and suitable for producing the baseplate material with clad steel sheet, coating may be selected from Zn, Zn-Fe, Zn-Al, Zn-Mg,
One kind in Zn-Al-Mg, Al-Si and Al-Mg-Si.
Beneficial effects of the present invention：
1. the present invention by hot rolled steel plate it is cold rolling it is preceding pre-processed, it is cold rolling before pretreatment successively include cold rolling predeformation with
Recrystallization annealing, cold rolling preceding pretreating process substantially makes annealed sheet steel high temperature delta ferrite occur recrystallization and refine, strip group
Knit and significantly reduce, the structural homogenity of annealed sheet steel is improved.
2. the annealed sheet steel of the invention through cold rolling preceding pretreatment is while high intensity level is maintained, its ductility and strong modeling
Product is significantly improved.
3. the present invention can be completed on existing advanced high-strength steel production line, without doing larger adjustment, with pushing away well
Wide application prospect.
Brief description of the drawings
Fig. 1 is the process curve schematic diagram of the cold rolling rear continuous annealing process of the present invention.
Fig. 2 is the manufacturing process flow diagram of the embodiment of the present invention.
Fig. 3 is the representative microstructure photo of ferrite lightweight steel prepared by existing manufacturing process.
The representative microstructure photo for the ferrite lightweight steel that Fig. 4 is prepared for the present invention.
Embodiment
With reference to embodiment and accompanying drawing, the present invention will be further described.
Table 1 is the hot rolling, cold rolling preceding pretreatment and cold-rolling process parameter of the embodiment of the present invention, and table 2 is the embodiment of the present invention
Continuous annealing process parameter, table 3 is the mechanical property of the embodiment of the present invention and comparative example steel.
The manufacturing process of the embodiment of the present invention mainly includes：Smelt and continuous casting, hot rolling, cold rolling preceding pretreatment, cold rolling and company
Continuous annealing heat-treats.Pretreatment includes cold rolling predeformation and bell furnace recrystallization annealing, technological process such as Fig. 2 institutes successively before cold rolling
Show：
Comparative example 1：Before cold rolling without cold rolling preceding pretreatment (at i.e. cold rolling predeformation and bell furnace recrystallization annealing process
Reason), steel grade and other manufacturing process be the same as Examples 1.
Comparative example 2：Before cold rolling without cold rolling preceding pretreatment (at i.e. cold rolling predeformation and bell furnace recrystallization annealing process
Reason), steel grade and other manufacturing process be the same as Examples 2.
Comparative example 3：Before cold rolling without cold rolling preceding pretreatment (at i.e. cold rolling predeformation and bell furnace recrystallization annealing process
Reason), steel grade and other manufacturing process be the same as Examples 3.
Comparative example 4：Before cold rolling without cold rolling preceding pretreatment (at i.e. cold rolling predeformation and bell furnace recrystallization annealing process
Reason), steel grade and other manufacturing process be the same as Examples 4.
As shown in Table 3, embodiment 1 is compared with comparative example 1, and the elongation percentage of the annealed sheet steel of embodiment 1 improves 30.2%, by force
Modeling product improves 26.7%.Embodiment 2 is compared with comparative example 2, and the elongation percentage of the annealed sheet steel of embodiment 2 improves 28.9%, by force
Modeling product improves 24.1%.Embodiment 3 is compared with comparative example 3, and the elongation percentage of the annealed sheet steel of embodiment 3 improves 30.3%, by force
Modeling product improves 21.2%.Embodiment 4 is compared with comparative example 4, and the elongation percentage of the annealed sheet steel of embodiment 4 improves 27.5%, by force
Modeling product improves 21%.Therefore, the present invention by hot rolled steel plate in cold rolling advance cold rolling predeformation and bell furnace recrystallization annealing
Manufacturing process, it is ensured that ferrite lightweight steel is while high intensity level is maintained, and its ductility and strength and ductility product are significantly improved.
Fig. 3 is the representative microstructure photo of ferrite lightweight steel prepared by existing manufacturing process, and Fig. 4 is prepared for the present invention
Ferrite lightweight steel representative microstructure photo, δ represents high temperature delta ferrite in Fig. 3,4, and α+RA represent phase transformation alpha ferrite
With retained austenite RA mixture.
Referring to Fig. 3 and Fig. 4, the present invention, which implements cold rolling preceding pretreating process, substantially sends out annealed sheet steel high temperature delta ferrite
Life is recrystallized and refined, and streaky structure is significantly reduced, and the structural homogenity of annealed sheet steel is improved, and then is remarkably improved steel
Ductility.
Claims (4)
1. a kind of manufacture method for improving general chill ferritic lightweight steel ductility, it is characterised in that the ferrite lightweight steel
Microscopic structure is mainly made up of the ferrite fully recrystallized and metastable state retained austenite, the system of the ferrite lightweight steel
The method of making comprises the following steps：
1) cold rolling predeformation
Cold rolling predeformation is carried out to hot rolled plate, deflection is 30~80%；The main chemical compositions percentage by weight of hot rolled plate is：
C：0.05~0.50%, Mn：0.25~12.0%, Al：3.0~7.0%, also contain：Si：0.01~1.5%, Ti：0.005~
0.6%th, Nb：0.005~0.2%, V：0.005~0.5%, Cr：0.01~0.5%, Mo：0.01~0.5%, Ni：0.05~
2.0%th, Cu：One or more of 0.05~1.0%, remaining is Fe and inevitable impurity；
2) recrystallization annealing
Using cover annealing, soaking temperature is 660~850 DEG C, and soaking time is 0.5~48h；
3) it is cold rolling
Cold rolling deflection is 30~90%；
4) continuous annealing is heat-treated
Cold-reduced sheet is heated to after 750~950 DEG C of soaking temperature to be incubated 30~600s, medium temperature is first cooled to, is cooled to
200~500 DEG C of partition stabilization temperature, is incubated 0~600s, wherein, the rate of heat addition of cold-rolled steel sheet is 1~20 DEG C/s；650℃
950 DEG C of≤medium temperature ＜；The cooldown rate that steel plate after all heat-treated is cooled to medium temperature from soaking temperature is 1~10
℃/s；The cooldown rate that steel plate after all heat-treated is cooled to partition stabilization temperature from medium temperature is 1~150 DEG C/s, and
And the cooldown rate is cooled to the cooldown rate of medium temperature not less than steel plate from soaking temperature；Partition stabilization processes terminate
Afterwards, by steel plate with 1~20 DEG C/s cooldown rate slow cooling to room temperature.
2. the manufacture method according to claim 1 for improving general chill ferritic lightweight steel ductility, it is characterised in that step
1) in, hot rolled plate rolling：1000~1250 DEG C of heating-up temperature, soaking time is 0.5~3h, finishing temperature >=800 DEG C, 300
Hot rolled plate is batched at~750 DEG C；After cooling, pickling.
3. the manufacture method according to claim 1 for improving general chill ferritic lightweight steel ductility, it is characterised in that step
1) in, the deflection of cold rolling predeformation is 40~60%.
4. the manufacture method according to claim 1 for improving general chill ferritic lightweight steel ductility, it is characterised in that step
3) in, cold rolling deflection is 50~70%.
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| CN106086658B (en) * | 2016-06-20 | 2017-08-08 | 上海大学 | Carbon contains the low manganese lightweight steel of chromium and preparation method in a kind of high intensity |
| CN106011652B (en) * | 2016-06-28 | 2017-12-26 | 宝山钢铁股份有限公司 | A kind of excellent cold rolling low-density steel plate of phosphorus characteristic and its manufacture method |
| KR20190065671A (en) * | 2017-12-04 | 2019-06-12 | 현대자동차주식회사 | Ferric lightweight steel |
| CN111378908B (en) * | 2020-03-18 | 2021-10-01 | 云南昆钢耐磨材料科技股份有限公司 | Preparation method of alloy steel lining plate |
| CN112226701B (en) * | 2020-09-11 | 2021-12-31 | 北京科技大学 | High-aluminum-content fine-grain low-density full-high-temperature ferrite steel and preparation method thereof |
| CN116457480A (en) * | 2020-12-10 | 2023-07-18 | 安赛乐米塔尔公司 | Low-density cold-rolled and annealed steel sheet, method for producing same, and use of such steel for producing vehicle parts |
| CN114086080B (en) * | 2021-11-15 | 2022-11-18 | 华北理工大学 | Dual-phase-isomerism light high-strength steel and preparation method thereof |
| CN115125442B (en) * | 2022-06-16 | 2023-11-10 | 首钢集团有限公司 | Low-density high-strength steel with low crack rate and preparation method thereof |
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| CA2278841C (en) * | 1997-01-29 | 2007-05-01 | Nippon Steel Corporation | High strength steels having excellent formability and high impact energy absorption properties, and a method for producing the same |
| KR20120065464A (en) * | 2010-12-13 | 2012-06-21 | 주식회사 포스코 | Austenitic lightweight high strength hot rolled steel sheet having excellent yield-ratio and ductility and method for manufacturing the same |
| JP5699889B2 (en) * | 2011-09-30 | 2015-04-15 | 新日鐵住金株式会社 | Hot-dip galvanized steel sheet excellent in formability with a tensile strength of 980 MPa or more and its manufacturing method |
| CN102628140A (en) * | 2012-03-22 | 2012-08-08 | 内蒙古包钢钢联股份有限公司 | Extra-deep drawing IF steel and double cold rolling technology thereof |
| WO2013178887A1 (en) * | 2012-05-31 | 2013-12-05 | Arcelormittal Investigación Desarrollo Sl | Low-density hot- or cold-rolled steel, method for implementing same and use thereof |
| CN102912219A (en) * | 2012-10-23 | 2013-02-06 | 鞍钢股份有限公司 | High-strength plastic accumulation TRIP (Transformation-Induced Plasticity) steel plate and preparation method thereof |
| CN104109802B (en) * | 2014-08-04 | 2017-04-12 | 武汉钢铁(集团)公司 | Cold-rolled dual-phase steel with excellent broaching performance and production method |
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