CN106086653B - It is a kind of to realize capability gradient, the warm forming medium managese steel part preparation method of equal thickness - Google Patents
It is a kind of to realize capability gradient, the warm forming medium managese steel part preparation method of equal thickness Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 109
- 239000010959 steel Substances 0.000 title claims abstract description 109
- 238000002360 preparation method Methods 0.000 title claims abstract description 16
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 26
- 238000001816 cooling Methods 0.000 claims abstract description 15
- 238000000034 method Methods 0.000 claims abstract description 15
- 230000009466 transformation Effects 0.000 claims abstract description 13
- 238000009826 distribution Methods 0.000 claims abstract description 12
- 230000008569 process Effects 0.000 claims abstract description 6
- 229910000734 martensite Inorganic materials 0.000 claims description 17
- 238000010438 heat treatment Methods 0.000 claims description 15
- 229910001563 bainite Inorganic materials 0.000 claims description 12
- 239000011159 matrix material Substances 0.000 claims description 8
- 229910000859 α-Fe Inorganic materials 0.000 claims description 8
- 238000002791 soaking Methods 0.000 claims description 7
- 239000000126 substance Substances 0.000 claims description 7
- 239000007789 gas Substances 0.000 claims description 6
- 230000006698 induction Effects 0.000 claims description 6
- 238000009413 insulation Methods 0.000 claims description 6
- 239000000112 cooling gas Substances 0.000 claims description 5
- 230000009467 reduction Effects 0.000 claims description 5
- 239000012535 impurity Substances 0.000 claims description 4
- 239000000203 mixture Substances 0.000 claims description 3
- 238000010791 quenching Methods 0.000 claims description 3
- 230000000171 quenching effect Effects 0.000 claims description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 3
- 238000005516 engineering process Methods 0.000 description 8
- 238000004519 manufacturing process Methods 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 3
- 230000033228 biological regulation Effects 0.000 description 2
- 230000002265 prevention Effects 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 238000007493 shaping process Methods 0.000 description 2
- 229910000712 Boron steel Inorganic materials 0.000 description 1
- 229910000794 TRIP steel Inorganic materials 0.000 description 1
- 229910000937 TWIP steel Inorganic materials 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 239000004744 fabric Substances 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 210000004209 hair Anatomy 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 230000005855 radiation Effects 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 238000011426 transformation method Methods 0.000 description 1
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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
-
- 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
- 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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- 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
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
-
- 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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
-
- 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
- C21D2211/001—Austenite
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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
- C21D2211/002—Bainite
-
- 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
- C21D2211/005—Ferrite
-
- 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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- Crystallography & Structural Chemistry (AREA)
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Abstract
Present invention offer is a kind of to realize capability gradient, the warm forming medium managese steel part preparation method of equal thickness, comprises the following steps：It is stand-by steel plate to choose medium managese steel plate；Stand-by steel plate is heated to complete austenitizing；It is transported in diel and carries out stamping, is quenched to room temperature and obtains warm forming steel part；Steel part after cooling is partly or wholly heated using gradient-heated mode, realize the heat time graded of steel part diverse location, complete steel part after reverse transformation process and be cooled to room temperature, obtaining has capability gradient distribution, high intensity, high-ductility, the medium managese steel part of equal thickness.The medium managese steel part that the present invention is obtained is heterogeneous structure structure, superhigh intensity had not only been realized on same steel part but also the capability gradient distribution of high-ductility is obtained, and the Gradient Features of performance are further realized because of the graded of austenite content in high plastic zone, the demand of lightweight and security is met, with extensive dissemination.
Description
Technical field
The invention belongs to automobile steel part forming technique field, more particularly to a kind of realize capability gradient, the temperature of equal thickness
Hot forming medium managese steel part preparation method, is suitable for the thin medium managese steel plate that thickness specification is 0.6mm-2mm, obtaining has capability gradient
Distribution, with martensite or bainite structure or metastable austenite and the part of ferrite matrix institutional framework.
Background technology
The developing direction of automobile is lightweight, reduction fuel consumption, reduces discharge and improve security, so as to accounting for automobile
The automobile steel of weight 70% or so it is also proposed higher requirement, drive the development of automobile steel.In automobile steel making, IF steel,
DP steel, TRIP steel and martensite steel etc. are referred to as first generation automobile steel；TWIP steel and full austenite steel are referred to as second generation automobile steel.
American scholar (performance and cost) between the first generation and second generation automobile steel proposes third generation automobile steel, i.e. novel steam
Automobile-used steel.Q＆P steel and medium managese steel are as third generation automobile steel, because of its preferable mechanical property, have been obtained for major steel mill and
The production and application of automaker.Medium managese steel has ultra-fine metastable austenite and ferrite matrix institutional framework, its Ovshinsky
Being formed by the basis of the martensite of quenching formation or bainite structure for body, new austenite is formed by subsequent annealing
With solute element in the enrichment of austenite, the austenite component of ambient-temp-stable is finally given, this technique is referred to as austenite reverse transformation
Method.Currently, the reverse transformation technique on medium managese steel is concentrated mainly in the manufacturing process of sheet material, and for warm deep drawing shaping zero
In part manufacture, austenite anti-phase political reform how is introduced, to carry out regulation and control design to its performance, there is not yet report.
Technical elements are realized in preparation and the various performances of sheet material on automobile medium managese steel plate, and such as Chinese patent discloses
Number it is：CN101638749B《A kind of automobile steel with low cost and high strength ductility balance and preparation method thereof》Described technology, its is original
Sheet material has ultra-fine institutional framework, very high strength and ductility product and relatively low production cost.But how to be configured to automobile on sheet material
Part and its required various performance requirements are not referred to but.Warm forming medium managese steel result in superelevation tensile strength >=
1000MPa, it might even be possible to reach more than 1400MPa, while the performance characteristic of elongation percentage >=10%.So, how in a temperature
Capability gradient is realized on hot forming medium managese steel part, it is difficult the high intensity, high-plastic surmounted its subregion is possessed hot forming boron steel
Property mechanical property, subregion possess is realized on the gradient performance feature of elongation percentage >=30%, Same Part capability gradient point
Cloth is current urgent problem to be solved.
The content of the invention
According to technical problem set forth above, and provide and a kind of realize capability gradient, the warm forming medium managese steel of equal thickness
Part preparation method.Invention introduces the austenite reverse transformation feature of medium managese steel, by warm forming technique and austenite reverse transformation
Technique is combined, so as to obtain the medium managese steel part of the high intensity being distributed with capability gradient, high-ductility, equal thickness.
The technological means that the present invention is used is as follows：
It is a kind of to realize capability gradient, the warm forming medium managese steel part preparation method of equal thickness, it is characterised in that including as follows
Step：
S1, selection medium managese steel plate are stand-by steel plate, and the chemical component weight percentage of the medium managese steel plate is：C：0.01-
0.50%；Mn：4.0-6.0%；P≤0.015%；S≤0.02%, remainder is Fe and inevitable impurity；
S2, stand-by steel plate is heated to complete austenitizing, heating-up temperature is between 750 DEG C -950 DEG C, 1-10 points of insulation
Clock；It is transported in diel, in MsMore than temperature carry out stamping, be quenched to room temperature and obtain warm forming steel part, according to
The difference of quenching rate, forms martensitic structure structure or bainite structure structure；
S3, the steel part after cooling partly or wholly heated using gradient-heated mode, realize steel part diverse location
Heat time graded, heating-up temperature is between 100 DEG C~Ac1 of below Ac1, soaking time -600 minutes 5 minutes, complete
Steel part is cooled to room temperature after reverse transformation process, and obtaining has capability gradient distribution, high intensity, high-ductility, the medium managese steel of equal thickness
Part.
Further, in the step S1, percentage by weight is added on the basis of the chemical composition of the medium managese steel plate
Following one or more elements：Cr：0.2-3.0%；Si：0.3-2.3%；B：0.0005-0.005%；Nb：0.02-
0.10%；[N]：0.002-0.25%；Ti：0.05-0.25%；V：0.02-0.25%；Al：0.015-0.060%；Re：
0.002-0.005%.
Further, in the step S2 stand-by steel plate in martensitic traoformation MsAfter point temperatures above is stamping, pass through
Air cooling, oil cooling or water cooling are quenched into room temperature, final to obtain martensite or bainite structure structure.
Further, in the step S3, the steel part after cooling is partly or wholly heated using induction coil, control
The Gradient Features of heat time, complete reverse transformation process；Non-heated region is utilized with circulating cooling gas or compressed gas
Pre-cooler reduces steel part temperature.
Further, the Gradient Features of the heat time are to set induction coil different heating and thermal insulation time, heating
After stopping, the pre-cooler reduction steel part temperature with circulating cooling gas or compressed gas is utilized together with non-heated region.
Further, the medium managese steel part obtained in the step S3 is heterogeneous structure structure, with martensite or bainite
Institutional framework and metastable austenite and ferrite matrix institutional framework, wherein metastable austenite content reach 5%-40% it
Between graded.I.e. non-heated region is martensitic structure structure or bainite structure structure, and heating region is metastable Ovshinsky
Body and ferrite matrix institutional framework.
Further, the medium managese steel part obtained in the step S3 has intensity region：Tensile strength >=1000MPa and prolong
Stretch rate >=10%；High plastic zone：The capability gradient distribution of tensile strength >=600MPa and elongation percentage >=30%.
More existing forming technology technology is compared, and invention introduces the austenite reverse transformation feature of medium managese steel, will be warmed into
Shape technique is combined with austenite reverse transformation technique.When setting 750 DEG C -950 DEG C of austenitizing temperature and being incubated 1-10 minutes, remove
Based on outside warm forming technology characteristics, it is also contemplated that in reverse transformation technique austenitizing heating process need more fully, tissue
Regulation and control are more scientific, the gradient formation of metastable austenite and stability during in favor of follow-up reverse transformation.The different anti-phase by setting
Become technological parameter, realize the formation of metastable austenite and ferrite matrix, and realize the graded of metastable austenite content,
So as to further realize the graded of performance in the tissue regions, while the martensite or bainite group that are obtained with warm forming
Structural region matching is knitted, the high intensity being distributed with capability gradient, high-ductility, the medium managese steel part of equal thickness is obtained.
The present invention is to make use of warm forming technique to reduce steel part resilience feature, can form martensite or bainite
Institutional framework, combines the tissue modulation technology of third generation automobile medium managese steel again, forms metastable austenite and ferrite matrix tissue
Structure, and austenite content can form gradient distribution, and superhigh intensity had not only been realized on same steel part but also the performance of high-ductility is obtained
Gradient is distributed, and the Gradient Features of performance are further realized because of the graded of austenite content in high plastic zone, is met
Lightweight and the demand of security, with extensive dissemination.
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 accompanying drawing used required in technology description to do simply to introduce, 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 process chart of the invention.
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
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 the premise of creative work is not made, belongs to the scope of protection of the invention.
As shown in figure 1, a kind of realize capability gradient, the warm forming medium managese steel part preparation method of equal thickness, including it is as follows
Step：
S1, selection medium managese steel plate are stand-by steel plate, and the chemical component weight percentage of the medium managese steel plate is：C：0.01-
0.50%；Mn：4.0-6.0%；P≤0.015%；S≤0.02%, remainder is Fe and inevitable impurity；The step S1
In, the following one or more elements of percentage by weight are added on the basis of the chemical composition of the medium managese steel plate：Cr：0.2-
3.0%；Si：0.3-2.3%；B：0.0005-0.005%；Nb：0.02-0.10%；[N]：0.002-0.25%；Ti：0.05-
0.25%；V：0.02-0.25%；Al：0.015-0.060%；Re：0.002-0.005%.
S2, stand-by steel plate is heated to complete austenitizing, heating-up temperature is between 750 DEG C -950 DEG C, 1-10 points of insulation
Clock；It is transported in diel, in MsMore than temperature carry out stamping, be quenched to room temperature and obtain warm forming steel part；It is described
Stand-by steel plate is in martensitic traoformation M in step S2sAfter point temperatures above is stamping, it is quenched into by air cooling, oil cooling or water cooling
Room temperature, it is final to obtain martensite or bainite structure structure.
S3, the steel part after cooling partly or wholly heated using induction coil using gradient-heated mode, controlled
The Gradient Features of heat time, that is, set the induction coil different heating and thermal insulation time, when realizing the heating of steel part diverse location
Between graded, heating-up temperature is between 100 DEG C~Ac1 of below Ac1, soaking time -600 minutes 5 minutes, complete reverse transformation mistake
Cheng Hou, stops heating, and the pre-cooler reduction steel with circulating cooling gas or compressed gas is utilized together with non-heated region
Part temperature, obtaining has capability gradient distribution, high intensity, high-ductility, the medium managese steel part of equal thickness.
Obtained medium managese steel part is heterogeneous structure structure, with martensite or bainite structure structure and metastable Ovshinsky
Body and ferrite matrix institutional framework, wherein metastable austenite content reach the graded between 5%-40%.Medium managese steel part
With intensity region：Tensile strength >=1000MPa and elongation percentage >=10%；High plastic zone：Tensile strength >=600MPa and extension
The capability gradient distribution of rate >=30%.
Embodiment 1
Choosing medium managese steel part chemical component weight percentage is：C：0.1%；Mn：4.6%；Nb：0.05%；Ti：
0.05%；P：0.013%；S：0.01%, remainder is Fe and inevitable impurity.
By taking certain vehicle collision prevention girders as an example, by thickness for needed for 1.6mm stand-by steel plate is cut into steel part size, by stand-by steel
Part is heated to 850 DEG C, is incubated 5 minutes；It is transported in diel and carries out stamping, is measured after shaping using infrared radiation thermometer
Steel part mean temperature is at 450 DEG C or so, and stand-by steel part is air-cooled to room temperature.Steel part is divided into three regions, 1. and 2. region is to add
Thermal region, carries out sensing heating, heating-up temperature is at 670 DEG C (this temperature is between 100 DEG C~Ac1 of below Ac1), and heating region is 1.
Soaking time is 5 minutes, and 2. soaking time is 1 hour to heating region.3. remaining region, passes through the cooling of compressed gas for region
Processing, it is to avoid 3. temperature is too high and occur structural transformation in region.Stand-by steel part is cooled to after above-mentioned successive heating and thermal insulation processing
Room temperature.
Three regions after stamping from steel part are separately sampled, and load-deformation curve is obtained by uniaxial tensile test,
And then mechanical property is obtained, as shown in table 1, the austenite volume content for heating 1. area (soaking time 5 minutes) is 10.2%, its
Mechanical property：Tensile strength 720MPa, elongation percentage 18%, i.e. strength and ductility product are 13GPa% or so；Heating 2. area, (soaking time 1 is small
When) austenite volume content be 30%, its mechanical property：Tensile strength 706MPa, elongation percentage 42%, i.e. strength and ductility product are
30GPa% or so, non-heated region (3. area) has martensitic structure structure, its mechanical property：Tensile strength is 1510MPa,
Elongation percentage 11.4%, i.e. strength and ductility product are 17GPa% or so.It is achieved thereby that the distribution of same equal thickness steel part capability gradient, high-strength
Degree and high-ductility have concurrently.
The mechanical property of certain the vehicle collision prevention girders capability gradient distribution of table 1
| Subregion performance | Tensile strength (MPa) | Elongation percentage (%) | Strength and ductility product (GPa%) |
| 1. area | 720 | 18 | 13 |
| 2. area | 706 | 42 | 30 |
| 3. area | 1510 | 11.4 | 17 |
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, or 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 (7)
1. a kind of realize capability gradient, the warm forming medium managese steel part preparation method of equal thickness, it is characterised in that including following step
Suddenly：
S1, selection medium managese steel plate are stand-by steel plate, and the chemical component weight percentage of the medium managese steel plate is：C：0.01-
0.50%；Mn：4.0-6.0%；P≤0.015%；S≤0.02%, remainder is Fe and inevitable impurity；
S2, stand-by steel plate is heated to complete austenitizing, heating-up temperature is incubated 1-10 minutes between 750 DEG C -950 DEG C；Turn
Transport in diel, in MsMore than temperature carry out stamping, be quenched to room temperature and obtain warm forming steel part；
S3, the steel part after cooling partly or wholly heated using gradient-heated mode, realize steel part diverse location plus
Hot time gradient change, heating-up temperature is between 100 DEG C~Ac1 of below Ac1, soaking time -600 minutes 5 minutes, completes anti-phase
Steel part is cooled to room temperature after change process, and obtaining has capability gradient distribution, high intensity, high-ductility, the medium managese steel part of equal thickness.
2. according to claim 1 realize capability gradient, the warm forming medium managese steel part preparation method of equal thickness, its feature
Be, in the step S1, added on the basis of the chemical composition of the medium managese steel plate the following one kind of percentage by weight or
Multiple element：Cr：0.2-3.0%；Si：0.3-2.3%；B：0.0005-0.005%；Nb：0.02-0.10%；[N]：0.002-
0.25%；Ti：0.05-0.25%；V：0.02-0.25%；Al：0.015-0.060%；Re：0.002-0.005%.
3. according to claim 1 realize capability gradient, the warm forming medium managese steel part preparation method of equal thickness, its feature
It is, stand-by steel plate is in martensitic traoformation M in the step S2sAfter point temperatures above is stamping, pass through air cooling, oil cooling or water
Cold quenching is final to obtain martensite or bainite structure structure to room temperature.
4. according to claim 1 realize capability gradient, the warm forming medium managese steel part preparation method of equal thickness, its feature
It is, in the step S3, the steel part after cooling is partly or wholly heated using induction coil, controls the ladder of heat time
Feature is spent, reverse transformation process is completed；Non-heated region utilizes the pre-cooler reduction with circulating cooling gas or compressed gas
Steel part temperature.
5. according to claim 4 realize capability gradient, the warm forming medium managese steel part preparation method of equal thickness, its feature
It is, the Gradient Features of the heat time are to set the induction coil different heating and thermal insulation time, after heating stops, and are added with non-
Thermal region utilizes the pre-cooler reduction steel part temperature with circulating cooling gas or compressed gas together.
6. capability gradient, the warm forming medium managese steel part preparation method of equal thickness are realized according to claim 3 or 4, its
Be characterised by, the medium managese steel part obtained in the step S3 is heterogeneous structure structure, with martensite or bainite structure structure,
And metastable austenite and ferrite matrix institutional framework, wherein metastable austenite content reaches that gradient between 5%-40% becomes
Change.
7. according to claim 6 realize capability gradient, the warm forming medium managese steel part preparation method of equal thickness, its feature
It is, the medium managese steel part obtained in the step S3 has intensity region：Tensile strength >=1000MPa and elongation percentage >=10%；
High plastic zone：The capability gradient distribution of tensile strength >=600MPa and elongation percentage >=30%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201610668465.3A CN106086653B (en) | 2016-08-15 | 2016-08-15 | It is a kind of to realize capability gradient, the warm forming medium managese steel part preparation method of equal thickness |
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| CN109762965B (en) * | 2019-02-01 | 2024-04-16 | 哈尔滨工业大学（威海） | Continuous online preparation method of Mn-B steel structural part with super high toughness |
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