CN106636905A - Method for improving deformation capability of medium manganese steel with TRIP (Transformation-Induced Plasticity) effect - Google Patents
Method for improving deformation capability of medium manganese steel with TRIP (Transformation-Induced Plasticity) effect Download PDFInfo
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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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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Abstract
The invention provides a method for improving the deformation capability of medium manganese steel with a TRIP (Transformation-Induced Plasticity) effect. The method is characterized by comprising the following steps: selecting a medium manganese steel plate to serve as a steel part for later use; stamping the medium manganese steel plate according to a preset initial shape by a mechanical stamping machine or a hydraulic machine; after the step S2, heating the initially-formed steel part at an average heating rate of 40 to 60 DEG C/s to a temperature range from Ac1 to Ac1+50 DEG C, preserving heat for 5 to 60 minutes, and cooling in the air to the room temperature; performing secondary stamping, flanging, punching and bending on the cooled steel part according to preset product requirements to finish a deformation process. In the method, a medium manganese steel phase change annealing process is used mainly, and the content of reduced metastable austenite is compensated, so that the subsequent deformation capability of the medium manganese steel is improved, the process adaptability of a medium manganese steel part is enhanced, the phenomena of cracks, failures and the like are avoided, and the quality of automobiles on the aspect of light weight and security is improved.
Description
Technical field
The invention belongs to high strength and ductility automobile steel technical field, more particularly to a kind of middle manganese of the raising with TRIP effects
The method of steel deformability.
Background technology
In recent years, in order to meet the technical need of automotive light weight technology and security, domestic and international experts and scholars have developed advanced
Third generation automobile steel, with high intensity, high-ductility, i.e. high strength and ductility (strength and ductility product can reach 30GPa%) mechanical property
Advantage, including Q＆P steel and medium managese steel.Wherein, medium managese steel metastable austenite content up to 20%-30%, even more high, to obtain
The performance objective of high strength and ductility.Medium managese steel plate metastable austenite is to be heated to more than Ac3 temperature austenitizing simultaneously by sheet material
Insulation, quenching form martensite or martensite-austenite heterogeneous structure；Carry out reverse transformation annealing, cooling technique again to obtain, most
The microstructure of soleplate material is made up of ultra-fine ferrite and metastable austenite.
There is obvious TRIP effects and there is good shaping in medium managese steel when shaping because of the presence of metastable austenite, room temperature
Property, meanwhile, metastable austenite is changed into martensite when also shaping because of room temperature so that phase transformation strengthening and processing hardening are obvious, causes
The reduction of subsequent deformation ability and ftracture, it is difficult to complete the operations such as secondary forming, flange or punching.From microcosmic angle point
Analysis, normally, the presence of metastable austenite in sheet material, partial austenitic can be transformed into martensite during Plastic Forming, and be carried
The effect of high-ductility, i.e. TRIP effects.However, this TRIP effects can play favourable one side when once-forming；But, connect
The secondary forming of generation, because obtaining obvious, a certain amount of martensite, phase transformation strengthening is occurred in that so that processing hardening
Phenomenon becomes apparent from than non-phase transformation steel, and formability of sheet material when secondary forming, or even cracking are reduced on the contrary.
The content of the invention
According to technical problem set forth above, and provide a kind of side for improving the medium managese steel deformability with TRIP effects
Method, to meet the process requirements of multi-pass deformation.When the medium managese steel with TRIP effects occurs punching press deformation, obtains initial shape
Shape, especially when metastable austenite content is in 20%-30%, when even more many, its metastable austenite is changed into martensite, causes
Sheet material matrix strength performance is elevated and reduces formability.The present invention is in medium managese steel plate through once-forming acquisition preliminary configuration
Afterwards, medium managese steel reverse transformation annealing process is reused, the metastable austenite content for having reduced part compensation is carried out into, in improvement
Manganese steel subsequent deformation ability, to avoid the occurrence of the phenomenons such as Cracking Failure.
The technological means that the present invention is adopted is as follows：
A kind of method for improving the medium managese steel deformability with TRIP effects, it is characterised in that comprise the steps：
S1, selection medium managese steel plate are stand-by steel part, and the chemical component weight percentage of the medium managese steel plate is：C：0.02～
0.50%；Mn：3.5～6.0%；N≤0.006%；O≤30ppm；P≤0.015%；S≤0.020%, balance of Fe and not
Evitable impurity；
S2, using mechanical stamping machine or hydraulic press, carry out according to default original shape centering manganese steel plate stamping；
S3, Jing after step S2, by the steel part of initial formation with 40 DEG C/s-60 DEG C/s of average heating rate, be heated to Ac1
(started temperature that pearlite changes to austenite during heating) within the temperature range of Ac1+50 DEG C, insulation 5min-60min after,
It is air cooled to room temperature；
S4, the steel part after cooling is carried out into two times punch, flange, punching, bending according to default product requirement, complete shape
Change process.
Further, in step S1, add percentage by weight as follows on the basis of the medium managese steel chemical composition
One or more element：Cr：0.2～3.0%；Ni：0.1～3.0%；V：0～0.2%；Mo：0～0.7%；Nb：0～
0.3%；Cu：0.5-2.0%；Al：0.01～2.5%；Si：0～2.0%；RE：0.002-0.005%.
Certain thickness medium managese steel is carried out preform by the present invention, original shape is configured to, now due to metastable austenite
TRIP effects, medium managese steel has good formability, however, metastable austenite drops because being changed into martensite in forming process
Low content, causes its follow-up deformability to reduce；Therefore, the medium managese steel part after preform is heated into Ac1 to Ac1+50 DEG C of temperature
Reverse transformation annealing is carried out between degree, 5min-60min is incubated, with the metastable austenite content of matrix after part compensation preform, will
Steel part is cooled to room temperature, then carry out punching press flange drilling the deformation process such as bending.
Compared with the prior art, the present invention is scientifically combined elastoplasticity Forming Theory with Technology for Heating Processing, with this area
Before the difference of disclosed technological means is：
(1) for automobile steel parts with complex shape, be generally first stamped into original shape, then again it is secondary into
Shape is net shape, and completes the operations such as flange, punching.For non-phase transformation steel or the unconspicuous steel plate of phase transition phenomena, i.e.,
Make it is once-forming bring processing hardening phenomenon, but not yet therefore, it can smoothly to causing to significantly affect during secondary forming
Complete repeatedly to form process procedure.
(2) for the more medium managese steel of metastable austenite content, original plate metastable austenite is obtained by
The austenitizing of sheet material is heated and is incubated, quenching obtains martensite or martensite-austenite heterogeneous structure；Move back through reverse transformation again
Fire, cooling technique, finally give ultra-fine grained ferrite and metastable austenite institutional framework；And medium managese steel plate is once-forming for initial
After shape, obvious martensite is had in its microstructure and is formed, microstructure now is by ferrite, martensite and remnants
Austenite composition, when martensite reaches certain content, correspondingly, also there is significantly change in mechanical property, to follow-up
Deformability also has a significant effect, and will be difficult to shape or complete the subsequent handlings such as flange according still further to existing forming technology, therefore, profit
With the TRIP effects of medium managese steel, the acquisition of sheet material original shape is completed；It is different metastable austenite approach to be obtained from original plate
It is that the medium managese steel part with shape is directly over into reverse transformation annealing, horse is reduced for austenite by martensite transfor mation
Family name's body content, makes up the partial austenitic that martensitic traoformation occurs because of shaping, improves the deformability of medium managese steel, completes follow-up
Process procedure.
To sum up, the invention provides a kind of meet multi-step forming process, middle manganese of the raising with TRIP effects
The preparation method of steel deformability, prepares with complex shape, high strength and ductility automobile medium managese steel part, improves medium managese steel part
Technological adaptability, meets automotive light weight technology and security requirement.
Description of the drawings
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
The accompanying drawing to be used needed for having technology description does simply to introduce, it should be apparent that, drawings in the following description are these
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 appearance of the secondary forming cracking phenomena of existing process medium managese steel, wherein, (a) medium managese steel completes the first operation
Punching press preform；B (), not over the stamping operation of second, main failure forms are crackle and wrinkle.
Fig. 2 is the firmness change being intercepted in Fig. 1 (a) in exemplar each position.
Fig. 3 is the medium managese steel parts after the present invention is repeatedly shaped, wherein, (1) is once-forming；(2) it is secondary forming
And the subsequently processing such as flange, punching.
Specific embodiment
To make purpose, technical scheme and the 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
The a part of embodiment of the present invention, rather than the embodiment of whole.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 method for improving the medium managese steel deformability with TRIP effects, it is characterised in that comprise the steps：
S1, selection medium managese steel plate are stand-by steel part, and the chemical component weight percentage of the medium managese steel plate is：C：0.02～
0.50%；Mn：3.5～6.0%；N≤0.006%；O≤30ppm；P≤0.015%；S≤0.020%, balance of Fe and not
Evitable impurity；One or more following element of percentage by weight is added on the basis of the medium managese steel chemical composition：
Cr：0.2～3.0%；Ni：0.1～3.0%；V：0～0.2%；Mo：0～0.7%；Nb：0～0.3%；Cu：0.5-2.0%；
Al：0.01～2.5%；Si：0～2.0%；RE：0.002-0.005%.
S2, using mechanical stamping machine or hydraulic press, carry out according to default original shape centering manganese steel plate stamping；
S3, Jing after step S2, by the steel part of initial formation with 40 DEG C/s-60 DEG C/s of average heating rate, be heated to Ac1 extremely
Within the temperature range of Ac1+50 DEG C, after insulation 5min-60min, room temperature is air cooled to；
S4, the steel part after cooling is carried out into two times punch, flange, punching, bending according to default product requirement, complete shape
Change process.
Embodiment 1
It is calculated as from the chemical composition weight percent (%) of medium managese steel：C：0.1, Mn：5.0, P：0.008, S：
0.002, N：0.003, O：20ppm, Cu：0.6, Al：0.03, Si：0.2；Remaining is Fe.Medium managese steel plate thickness is 2.0mm, original
21.3%, its Ac1 temperature is 630 DEG C to the metastable austenite content of sheet material, and Ac3 (austenitizing temperature) temperature is 780 DEG C.With
As a example by the rear traveller fixed-link plate of certain vehicle.
Preparation method comprises the steps：
Existing process：By product requirement, by Fig. 1 (a), medium managese steel have successfully completed the punching press preform of the first operation；
After once-forming, the medium managese steel part with original shape is carried out secondary forming, by Fig. 1 (b), it is found that medium managese steel part does not lead to
The stamping operation of second is crossed, main failure forms are crackle and wrinkle.
The generation of cracking phenomena when shaping for second in Fig. 1 (b), research is special through the exemplar performance of shaping for the first time
The impact to second shaping is levied, according to the intercepting that exemplar is carried out on the direction illustrated in Fig. 1 (a), after shaping from first time
20mm is spaced on exemplar and takes hardness HV of measurement cross section successively.Its distribution is as shown in Figure 2, it can be seen that shape for the first time
Afterwards, the firmness change of medium managese steel exemplar occurs in that larger fluctuation, and 30HV is differed between maxima and minima because hardness and
There is certain conversion relation in tensile strength, it may be said that its corresponding tensile strength gap is it is also obvious that occur in that significantly
Uneven distribution, formability is also correspondingly reduced, and the result of TRIP effects is that martensitic structure feature generally occurs,
That is, different from the original structure of sheet material, metastable austenite is transformed into martensitic structure when once-forming.Therefore, Fig. 1 (b)
In it is follow-up secondary forming, occur in that the phenomenon of Cracking Failure.
Method proposed by the present invention：Medium managese steel plate of the same race is carried out once stamping, acquisition original shape, by Fig. 3 (1)
Shown, now, Jing XRD tests deform larger region metastable austenite and are reduced to 7% or so, and most of metastable austenite occurs
Martensitic traoformation；Medium managese steel part with original shape is put into heating furnace, is heated with the heating rate of 50 DEG C/s,
Heating-up temperature is 650 DEG C, is incubated 10 minutes, and air cooling to room temperature is annealed by reverse transformation, is partial austenitic by martensite transfor mation
And reduce martensite content；Then, the steel part is transferred on secondary forming mould carries out stamping, flange, punching work
Sequence, obtains net shape, and by Fig. 3 (2), the not cracking phenomenon of steel part, through method proposed by the present invention, is obtained secondary
Shape complete steel part during shaping.
Finally it should be noted that：Various embodiments above only to illustrate technical scheme, rather than a limitation；To the greatest extent
Pipe has been described in detail with reference to foregoing embodiments to the present invention, it will be understood by those within the art that：Its according to
So the technical scheme described in foregoing embodiments can be modified, either which part or all technical characteristic are entered
Row equivalent；And these modifications or replacement, do not make the essence disengaging various embodiments of the present invention technology of appropriate technical solution
The scope of scheme.
Claims (2)
1. a kind of method that raising has the medium managese steel deformability of TRIP effects, it is characterised in that comprise the steps：
S1, selection medium managese steel plate are stand-by steel part, and the chemical component weight percentage of the medium managese steel plate is：C：0.02～
0.50%；Mn：3.5～6.0%；N≤0.006%；O≤30ppm；P≤0.015%；S≤0.020%, balance of Fe and not
Evitable impurity；
S2, using mechanical stamping machine or hydraulic press, carry out according to default original shape centering manganese steel plate stamping；
S3, Jing after step S2, by the steel part of initial formation with 40 DEG C/s-60 DEG C/s of average heating rate, be heated to Ac1 to Ac1+
Within the temperature range of 50 DEG C, after insulation 5min-60min, room temperature is air cooled to；
S4, the steel part after cooling is carried out into two times punch, flange, punching, bending according to default product requirement, complete deformation
Journey.
2. the method that raising according to claim 1 has the medium managese steel deformability of TRIP effects, it is characterised in that institute
In stating step S1, one or more following element of percentage by weight is added on the basis of the medium managese steel chemical composition：Cr：
0.2～3.0%；Ni：0.1～3.0%；V：0～0.2%；Mo：0～0.7%；Nb：0～0.3%；Cu：0.5-2.0%；Al：
0.01～2.5%；Si：0～2.0%；RE：0.002-0.005%.
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108060355A (en) * | 2017-11-23 | 2018-05-22 | 东北大学 | A kind of Steel material and preparation method thereof |
| CN108330402A (en) * | 2018-02-01 | 2018-07-27 | 武汉科技大学 | A kind of Nb-Mo alloys High-strength high-plasticity cold rolling medium managese steel and preparation method thereof |
| CN110129688A (en) * | 2019-06-12 | 2019-08-16 | 上海清河机械有限公司 | A kind of high-voltage-resistant anti-corrosion steel and its preparation method and application |
| CN110524349A (en) * | 2019-08-24 | 2019-12-03 | 张家港海运金属冷挤压有限公司 | A kind of special processing unit (plant) and method of double end abnormity orifice |
| CN115772629A (en) * | 2022-10-25 | 2023-03-10 | 常州大学 | Industrial superplastic medium manganese steel and preparation method thereof |
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| CN103103438A (en) * | 2013-03-07 | 2013-05-15 | 北京科技大学 | High-strength and high-plasticity medium manganese cold-roll steel sheet and manufacturing method thereof |
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| CN108060355A (en) * | 2017-11-23 | 2018-05-22 | 东北大学 | A kind of Steel material and preparation method thereof |
| CN108060355B (en) * | 2017-11-23 | 2019-12-27 | 东北大学 | Steel material and preparation method thereof |
| CN108330402A (en) * | 2018-02-01 | 2018-07-27 | 武汉科技大学 | A kind of Nb-Mo alloys High-strength high-plasticity cold rolling medium managese steel and preparation method thereof |
| CN110129688A (en) * | 2019-06-12 | 2019-08-16 | 上海清河机械有限公司 | A kind of high-voltage-resistant anti-corrosion steel and its preparation method and application |
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| CN115772629A (en) * | 2022-10-25 | 2023-03-10 | 常州大学 | Industrial superplastic medium manganese steel and preparation method thereof |
| CN115772629B (en) * | 2022-10-25 | 2024-04-30 | 常州大学 | Superplastic medium manganese steel for industrialization and preparation method thereof |
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