CN106868398B - 1300MPa grades of ultra-fine grained ferrites/low temperature bainite dual-phase steel and preparation method thereof - Google Patents
1300MPa grades of ultra-fine grained ferrites/low temperature bainite dual-phase steel and preparation method thereof Download PDFInfo
- Publication number
- CN106868398B CN106868398B CN201611130256.XA CN201611130256A CN106868398B CN 106868398 B CN106868398 B CN 106868398B CN 201611130256 A CN201611130256 A CN 201611130256A CN 106868398 B CN106868398 B CN 106868398B
- Authority
- CN
- China
- Prior art keywords
- temperature
- ultra
- steel
- fine grained
- slab
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—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
-
- 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
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
- C21D1/20—Isothermal quenching, e.g. bainitic hardening
-
- 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
- C21D1/26—Methods of annealing
-
- 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
-
- 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
- C21D8/0226—Hot rolling
-
- 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
- C21D8/0231—Warm rolling
-
- 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
- C21D8/0236—Cold rolling
-
- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
-
- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- 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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- 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
- C22C38/40—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
-
- 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
- C22C38/40—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
-
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The invention discloses a kind of 1300MPa grades of ultra-fine grained ferrite/low temperature bainite dual-phase steels and preparation method thereof, belong to steel material engineering field.The chemical component of the dual phase steel is by weight percentage：C 0.28 ~ 0.32, Si 1.7 ~ 2.1, Mn 1.5 ~ 1.7, Cr1.1 ~ 1.4, Ni 0.8 ~ 1.2, W 0.6 ~ 0.8, P≤0.02, S≤0.02, remaining is Fe and the impurity that can not must be avoided；Its metallographic structure is ultra-fine grained ferrite and low temperature bainite, and wherein the crystallite dimension of ultra-fine grained ferrite is 0.5 ~ 2 μm, volume content is 20 ~ 35%.The siliceous low-alloy steel quenched martensite tissue of middle carbon is heated toA c1Following temperature comes out of the stove after heat preservation and carries out rolling deformation, is then heated to " α+γ " two-phase section partial saturation, places into progress Isothermal Bainite transformation in the salt bath furnace of the martensite starting point of a little higher than two-phase section austenite of temperature, is air-cooled to room temperature.
Description
Technical field
The invention belongs to steel material engineering field, it is related to a kind of dual phase steel and preparation method thereof, it is especially a kind of
1300MPa grades of ultra-fine grained ferrites/low temperature bainite dual-phase steel and preparation method thereof.
Background technique
Conventional ferrite/martensite dual-phase steel yield tensile ratio is lower, and initial manufacture hardening rate is high and plasticity and toughness are good.But by
Strength difference is larger between ferrite and martensite, and micro-crack is extended readily along ferrite/martensite phase interface to be expanded, to lead
It causes reaming performance bad, often cracks in reaming overturning process.And ferrite/bainite dual phase steel is then more preferable with toughness
Bainite there is flange more better than ferrite/martensite dual phase steel and reaming performance instead of martensite, and preferably
Tensile property and impact flexibility are more suitable for manufacturing complex-shaped auto parts and components（Such as wheel, chassis, suspension）, engineering machine
Tool components and anti-large-strain pipeline.
Currently, ferrite/bainite dual phase steel mainly uses low-carbon low-alloy steel（Including microalloying and non-microalloying
's）It being prepared by the method for controlled rolling and controlled cooling, preparation method discloses in multinomial patent, such as application No. is
200910169738.X Chinese patent disclose a kind of high tensile strength hot rolled ferrite bainite dual phase steel and its manufacturer
Method, the tensile strength is between 514 ~ 535MPa, and yield tensile ratio is 0.63 or more, but in tensile strength or relatively low, toughness
Not enough.In order to obtain the ferrite/bainite dual phase steel with more excellent comprehensive mechanical property, researcher is respectively to its iron
Ferritic and bainite structure conduct in-depth research and improve.Ferritic structure is refined first, makes ferrite crystal grain
Size is refined to micron order (1 ~ 4 μm), i.e. ultra-fine ferrite tissue, and ultra-fine ferrite makes dual phase steel because of its higher intensity
Performance improves；Secondly bainite structure is also being continuously improved, and carbide-free Bainite, low temperature bainite etc. have excellent obdurability
Bainite structure be also gradually applied in dual phase steel, the dual phase steel that ultra-fine ferrite and high tough bainite combine, which becomes, works as
The emphasis and hot spot of modern scientific research scholar research.
Summary of the invention
The technical problem to be solved in the present invention provides that a kind of simple process, preparation efficiency are high, be easy to accurately control, quality is steady
Middle carbon is contained silicon low-alloy by qualitative high 1300MPa grade ultra-fine grained ferrite/low temperature bainite dual-phase steel and preparation method thereof
Steel quenched martensite tissue is heated toA c1Following temperature comes out of the stove after heat preservation and carries out warm-rolling or cold-rolling deformation, be then heated to " α+
γ " two-phase section partial saturation, place into the salt bath furnace of the martensite starting point of a little higher than two-phase section austenite of temperature into
The transformation of row Isothermal Bainite, is air-cooled to room temperature, obtains ultra-fine grained ferrite/low temperature bainite duplex structure.Its simple process, shape
At dual phase steel have superhigh intensity and good plasticity.
In order to solve the above technical problems, the technical solution adopted by the present invention is that：
A kind of 1300MPa grades of ultra-fine grained ferrite/low temperature bainite dual-phase steel, chemical component are by weight percentage：C
0.28~0.32、Si 1.7~2.1、Mn 1.5~1.7、Cr1.1~1.4、Ni 0.8~1.2、W 0.6~0.8、P≤0.02、S≤
0.02, remaining is Fe and the impurity that can not must be avoided；Its metallographic structure is ultra-fine grained ferrite and low temperature bainite, wherein ultra-fine
The crystallite dimension of grained ferrite is 0.5 ~ 2 μm, volume content is 20 ~ 35%, and the slat dimension of low temperature bainite is 75 ~ 300 nm.
The 1300MPa grades of ultra-fine grained ferrite/low temperature bainite dual-phase steel tensile strength is not less than 1300 MPa, Qu Qiang
Than being 0.50 ~ 0.65, elongation percentage is not less than 12%.
The present invention also provides the preparation sides of two kinds of above-mentioned 1300MPa grades of ultra-fine grained ferrite/low temperature bainite dual-phase steels
Method, one of method include the following steps：
A, it makes steel：Ingredient proportion, melting are calculated according to the design requirement of steel and pour into steel ingot；
B, annealing, hot rolling：By the ingot annealing, hot rolling, it is air-cooled to room temperature after hot rolling, obtains hot rolling slab；
C, it quenches：The hot rolling slab is heated to 800 ~ 1000 DEG C, 20 ~ 40min of heat preservation, is then put into oil rapidly and quenches
Fire is cooled to room temperature, and obtains quenching slab；
D, warm-rolling：The quenching slab is kept the temperature into 1h under the conditions of 450 ~ 550 DEG C, obtains the slab of secondary troostite tissue,
Then the slab of secondary troostite tissue is become at 500 ~ 600 DEG C through the rolling that 5 ~ 7 passages, progress overall reduction are 30 ~ 50%
Shape is air-cooled to room temperature, obtains warm-rolling plate；
E, it is heat-treated：By the warm-rolling plate under the conditions of 760 ~ 780 DEG C, 3 ~ 5h is kept the temperature, is then put into 260 ~ 320 rapidly
DEG C salt bath furnace in 1.5 ~ 10 h of isothermal, then come out of the stove and be air-cooled to room temperature.
Another method, includes the following steps：
A, it makes steel：Ingredient proportion, melting are calculated according to the design requirement of steel and pour into steel ingot；
B, Heating Steel Ingots carry out Homogenization Treatments to 1200 ~ 1250 DEG C of 3 ~ 5 h of heat preservation；Then 1180 DEG C of open rollings are air-cooled to,
Finishing temperature is not less than 880 DEG C, by 5 ~ 6 passes, is finally rolled into the hot rolling slab of 18 ~ 20 mm thickness, hot rolling slab is empty
It is cooled to room temperature；
C, quenching and tempering：850 ~ 950 DEG C of heat preservations 20 ~ 40 will be reheated to by the hot rolling slab of step B processing
After min, it is put into oil quenching rapidly and is cooled to room temperature, is then placed in 480 ~ 520 DEG C of stove and keeps the temperature 1 h, come out of the stove and be air-cooled to
The slab of secondary troostite tissue is made in room temperature；
D, cold rolling：The multi-pass cold-rolling deformation that slab after tempering is carried out to overall reduction 40% obtains the cold of 12 mm thickness
Rolling sheets；
E, it is heat-treated：Cold rolled sheet is put into the stove that temperature is 760 ~ 780 DEG C, after keeping the temperature 3 ~ 5h, is put into temperature rapidly
Degree keeps 1.5 ~ 10 h for constant temperature in 260 ~ 320 DEG C of salt bath furnace, then comes out of the stove and is air-cooled to room temperature, obtains ultra-fine grained ferrite/low
Warm bainite dual-phase steel plate.
Low temperature bainite is the film-form retained austenite by very thin ferrite bainite and therebetween of beginning of this century exploitation
The tissue of composition is that the high-carbon alloy steel of siliceous 1.5% or more weight percent is low in the progress of a little higher than martensite starting point temperature
What warm Isothermal Bainite changed.Since transition temperature is low, therefore obtained lath of bainite thinner thickness, it has been even up to several
Ten nanometers；Again since element silicon is to the inhibiting effect of Carbide Precipitation in isothermal transformation, therefore formed between lath of bainite
Retained austenite and carbides-free is precipitated.So also known as the tissue is carbides-free nanostructure bainite.Superfine small plate
Bainite leads to high intensity, the transformation induced plasticity effect of the retained austenite of film-form can further improve plasticity and toughness,
It reduces yield tensile ratio and improves formability.So, the hard phase of traditional dual phase steel is replaced with low temperature bainite, then soft phase ferrite is brilliant
Grain is refined, and fine grain ferrite/low temperature bainite dual-phase steel can be obtained, this will be such that two-phase Steel Properties further increase.
The physical metallurgy principle of above-mentioned technical proposal is：Martensite is heated toA c1Following temperature heat preservation obtains tempering and bends
Family name's body tissue is heated to the heat preservation of " α+γ " two-phase section after rolling deformation, and ferrite recrystallization occurs and forms part Ovshinsky
Body.Since secondary troostite maintains the thinning microstructure form of quenched martensite, heating recrystallization be will form after rolling deformation
Tiny ferrite equi-axed crystal, obtains ultra-fine grained ferrite；At the same time, heating temperature is more thanA c1（A c1Be it is described " α+
The minimum temperature of γ " two-phase section）Austenite transformation then occurs, since heating temperature is in two-phase section, Austenite Grain Growth by
Larger limitation, therefore form fine grain austenite.In this way, will form " ultra-fine grained ferrite+fine grain in two-phase section heating and thermal insulation process
Austenite " tissue then carries out low temperature in salt bath furnace（The martensite starting point of this little higher than fine grain austenite）Constant temperature process
In, bainite transformation occurs for fine grain austenite, and ultra-fine grained ferrite does not change substantially.Since higher silicone content inhibits
Carbide is precipitated in Isothermal Bainite transition process, so to be changed into the distributed thin-film shape between lath of bainite remaining for austenite
The carbide-free Bainite tissue of austenite, i.e. Low Temperature Bainitic Microstructure.So, it is cooled to after room temperature and has just obtained Ultra-fine Grained iron
Ferritic/low temperature bainite dual-phase steel.
The beneficial effect generated by adopting the above technical scheme is：（1）Ultra-fine grained ferrite of the invention/low temperature bainite
The tissue of dual phase steel has obtained fine, and tensile strength is not less than 1300MPa, even as high as 1500MPa, yield tensile ratio 0.48
~ 0.63, elongation percentage is not less than 12%, has high intensity, high-ductility, low yield strength ratio and high strength and ductility, and comprehensive mechanical property is good,
It can be used for manufacturing the demanding energy-absorbing anti-collision component of formability；（2）Preparation process flow of the invention is simple and easy, is easy control
System, is advantageously implemented industrialized production, it is only necessary to the i.e. controllable product quality of the temperature of accurate control heat treatment, preparation efficiency
It is high.
Detailed description of the invention
Fig. 1 is the stereoscan photograph of dual phase steel microstructure prepared by embodiment 1；
Fig. 2 is the stress strain curve of two-phase steel curved beam prepared by embodiment 1；
Fig. 3 is the stereoscan photograph of dual phase steel microstructure prepared by embodiment 2；
Fig. 4 is the stereoscan photograph of dual phase steel microstructure prepared by embodiment 5；
Fig. 5 is the stress strain curve of two-phase steel curved beam prepared by embodiment 5 ~ 7；
Fig. 6 is the stress strain curve of two-phase steel curved beam prepared by embodiment 8 ~ 10.
Specific embodiment
Embodiment 1
It A, is C 0.3, Si 1.9, Mn 1.6, Cr 1.3, Ni 1.0, W 0.7, P 0.01, S according to mass percent
0.01, remaining is Fe and the proportion of impurity that can not must be avoided, calculate melting in ingredient proportion, in a vacuum frequency electric induction furnace,
And pour into the cylindrical steel ingot of 170 mm diameters.
B, annealing, hot rolling：By Heating Steel Ingots to 1220 DEG C of 4 h Homogenization Treatments of heat preservation, comes out of the stove and is air-cooled to 1180 DEG C of open rollings,
Finishing temperature is 880 DEG C, by 6 passes, is finally rolled into the hot rolling slab of 20 mm thickness, is air-cooled to room temperature after rolling.
Above-mentioned steps A and melting in step C and annealing, hot rolling are conventional steps.
C, it quenches：The hot rolling slab is heated to 900 DEG C, heat preservation 30min, oil quenching is then put into rapidly and is cooled to
Room temperature obtains quenching slab.
D, warm-rolling：The quenching slab is put into 500 DEG C of stove and keeps the temperature 1h, carries out overall reduction after coming out of the stove immediately
40% multi- pass rolling deformation, obtains the warm-rolling plate of 12mm thickness.
E, it is heat-treated：The warm-rolling plate is put into the stove that temperature is 760 DEG C, keeps the temperature 5h, be then put into 260 rapidly
DEG C salt bath furnace in 10 h of isothermal, then come out of the stove and be air-cooled to room temperature.
Electronic Speculum is scanned to plate obtained by the present embodiment（SEM）Analysis, microstructure photo is referring to Fig. 1, from figure
In it can be seen that：The present embodiment is prepared for ultra-fine grained ferrite and bainite dual-phase steel, wherein the crystal grain ruler of ultra-fine grained ferrite
Very little is 0.5 ~ 2 μm, and volume content is about 30%.
By the board making sample of the present embodiment, tension test is carried out according to GB/T228.1-2010 standard, stress-is answered
Varied curve referring to fig. 2, measures the tensile strength of sample（）For 1383MPa, yield strength（）For 775 MPa, elongation percentage（）Be 14%, calculate yield tensile ratio be 0.56, strength and ductility product be 19362 MPa%.Referring specifically to the data of table 1.
The microstructure and mechanical property of dual phase steel in 1 embodiment 1-4 of table
The above results show：Ultra-fine grained ferrite/low temperature bainite dual-phase steel has been made in the present embodiment, with high-strength
Degree, high-ductility, low yield strength ratio and high strength and ductility, comprehensive mechanical property are good.It is anti-to can be used for manufacturing the demanding energy-absorbing of formability
Hit component.
Embodiment 2
The warm-rolling plate obtained according to embodiment 1 is put into the stove that temperature is 760 DEG C, after keeping the temperature 5 h, is put into rapidly
10 h of isothermal in the salt bath furnace that temperature is 290 DEG C, then comes out of the stove and is air-cooled to room temperature.Its SEM photograph is surveyed referring to Fig. 3, mechanical property
Test result is as shown in table 1.
Embodiment 3
It A, is C 0.28, Si 1.7, Mn 1.7, Cr 1.1, Ni 1.2, W 0.6, P 0.01, S according to mass percent
0.01, remaining is Fe and the proportion of impurity that can not must be avoided, calculate melting in ingredient proportion, in a vacuum frequency electric induction furnace,
And pour into the cylindrical steel ingot of 170 mm diameters.
B, annealing, hot rolling：By Heating Steel Ingots to 1200 DEG C of 5 h Homogenization Treatments of heat preservation, comes out of the stove and is air-cooled to 1180 DEG C of open rollings,
Finishing temperature is 880 DEG C, by 7 passes, is finally rolled into the hot rolling slab of 20 mm thickness, is air-cooled to room temperature after rolling.
C, it quenches：The hot rolling slab is heated to 850 DEG C, heat preservation 60min, oil quenching is then put into rapidly and is cooled to
Room temperature obtains quenching slab.
D, warm-rolling：The quenching slab is put into 480 DEG C of stove and keeps the temperature 1h, carries out overall reduction after coming out of the stove immediately
35% multi- pass rolling deformation, obtains the warm-rolling plate of 13mm thickness；
E, it is heat-treated：By the warm-rolling plate under the conditions of 780 DEG C, 3h is kept the temperature, is then put into 290 DEG C of salt bath furnace rapidly
Middle isothermal 3h, then come out of the stove and be air-cooled to room temperature.
Electronic Speculum is scanned to plate obtained by the present embodiment（SEM）Analysis and tension test, as a result referring to table 1.
The above results show：Ultra-fine grained ferrite/low temperature bainite dual-phase steel has been made in the present embodiment, with high-strength
Degree, high-ductility, low yield strength ratio and high strength and ductility, comprehensive mechanical property are good.
Embodiment 4
It A, is C 0.32, Si 2.1, Mn 1.5, Cr 1.4, Ni 0.8, W 0.8, P 0.01, S according to mass percent
0.01, remaining is Fe and the proportion of impurity that can not must be avoided, calculate melting in ingredient proportion, in a vacuum frequency electric induction furnace,
And pour into the cylindrical steel ingot of 170 mm diameters.
B, annealing, hot rolling：By Heating Steel Ingots to 1250 DEG C of 2 h Homogenization Treatments of heat preservation, comes out of the stove and is air-cooled to 1180 DEG C of open rollings,
Finishing temperature is 880 DEG C, by 7 passes, is finally rolled into the hot rolling slab of 20 mm thickness, is air-cooled to room temperature after rolling.
C, it quenches：The hot rolling slab is heated to 950 DEG C, heat preservation 20min, oil quenching is then put into rapidly and is cooled to
Room temperature obtains quenching slab.
D, warm-rolling：The quenching slab is kept the temperature into 1h under the conditions of 550 DEG C, carries out the more of overall reduction 50% immediately after
Passes obtain the warm-rolling plate of 10mm thickness；
E, it is heat-treated：Warm-rolling plate is put into the stove that temperature is 780 DEG C, after keeping the temperature 3 h, being put into temperature rapidly is
1.5 h of isothermal, then comes out of the stove and is air-cooled to room temperature in 320 DEG C of salt bath furnace.
Electronic Speculum is scanned to plate obtained by the present embodiment（SEM）Analysis and tension test, as a result referring to table 1.
The above results show：Ultra-fine grained ferrite/low temperature bainite dual-phase steel has been made in the present embodiment, with high-strength
Degree, high-ductility, low yield strength ratio and high strength and ductility, comprehensive mechanical property are good.
Embodiment 5
It A, is C 0.3, Si 1.9, Mn 1.6, Cr 1.3, Ni 1.0, W 0.7, P 0.01, S according to mass percent
0.01, remaining is Fe and the proportion of impurity that can not must be avoided, calculate melting in ingredient proportion, in a vacuum frequency electric induction furnace,
And pour into the cylindrical steel ingot of 170 mm diameters；
B, Heating Steel Ingots come out of the stove to 1220 DEG C of 4 h Homogenization Treatments of heat preservation and are air-cooled to 1180 DEG C of open rollings, finishing temperature is
880 DEG C, by 6 passes, the first and second reduction in pass is respectively 40 and 30 mm, and rear four-pass drafts is 20 mm,
It is finally rolled into the hot rolling slab of 20 mm thickness, is air-cooled to room temperature after rolling；
C, after hot rolling slab being reheated to 900 DEG C of 30 min of heat preservation, it is put into oil quenching rapidly and is cooled to room temperature, so
It is put into 500 DEG C of stove afterwards and keeps the temperature 1 h, come out of the stove and be air-cooled to room temperature, the slab of secondary troostite tissue is made；
D, the multi-pass cold-rolling deformation that the slab after tempering is carried out to overall reduction 40%, obtains the cold-reduced sheet of 12 mm thickness
Material；
E, cold rolled sheet is put into the stove that temperature is 760 DEG C, after keeping the temperature 5 h, is put into the salt that temperature is 260 DEG C rapidly
10 h of isothermal, then comes out of the stove and is air-cooled to room temperature in liquid furnace, and ultra-fine grained ferrite/low temperature bainite dual-phase steel plate is made.Its is micro-
See the stereoscan photograph of tissue referring to fig. 4.As can be seen from the figure：The crystallite dimension of ultra-fine grained ferrite is 0.5 ~ 2 μm, body
Product content is about 35%.
By the board making sample of the present embodiment, tension test is carried out according to GB/T228.1-2010 standard, stress-is answered
Varied curve is referring to Fig. 5, as can be seen from the figure：After tensile load effect starts, stress-strain diagram initially enters flexible deformation
Stage, i.e., with the increase of strain, tensile stress also correspondingly linearly increases trend；With the increasing of tensile load action time
Long, curve is gradually transitions yielding stage, at this stage, does not occur apparent platform or zigzag in curve, therefore push away
The process of breaking is continuous surrender；Further extend load action time, curve enters the uniform plastic deformation stage, and curve rises simultaneously
Reach the tensile strength of material；Sample continues to generate uneven plastic deformation hereafter, generates constriction in regional area, reaches pole
After limit value, sample fracture.
According to the load-deformation curve of sample, the tensile strength of sample is measured（）, yield strength（）And elongation percentage
（）The results are shown in Table 2.
The sample tissue parameter and mechanical property prepared in 2 embodiment 5,7,8 and 10 of table
This example demonstrates that：Ultra-fine grained ferrite manufactured in the present embodiment/low temperature bainite dual-phase steel has high-intensitive, high
Plasticity, low yield strength ratio and high strength and ductility, comprehensive mechanical property is good, can be used for manufacturing the demanding energy-absorbing anti-collision structure of formability
Part.
Embodiment 6 ~ 7
Unlike the first embodiment, cold rolled sheet is put into the stove that temperature is 760 DEG C in step D, after keeping the temperature 5 h,
It is respectively 275 DEG C in temperature（Embodiment 6）With 290 DEG C（Embodiment 7）Salt bath furnace in 10 h of isothermal, then come out of the stove and be air-cooled to room
Temperature.Its stress strain curve and the result of test are referring to Fig. 5 and table 2.
Embodiment 8 ~ 10
Unlike the first embodiment, in 780 DEG C of furnaces, after keeping the temperature 3 h, then cold rolled sheet is put into temperature in step D is
It is put into 3 h of isothermal in the salt bath furnace that temperature is 290,305 and 320 DEG C rapidly respectively, then comes out of the stove and be air-cooled to room temperature.It stretches examination
Curve and result are tested respectively referring to Fig. 6 and table 2.
Claims (6)
1. a kind of 1300MPa grades of ultra-fine grained ferrite/low temperature bainite dual-phase steel, it is characterised in that its chemical component is by weight
Percentage is：C 0.28~0.32,Si 1.7~2.1,Mn 1.5~1.7,Cr1.1~1.4,Ni 0.8~1.2,W 0.6~0.8,P≤
0.02, S≤0.02, remaining is Fe and inevitable impurity；Its metallographic structure be ultra-fine grained ferrite and low temperature bainite,
The crystallite dimension of middle ultra-fine grained ferrite is 0.5 ~ 2 μm, volume content is 20 ~ 35%, the slat dimension of low temperature bainite is 75 ~
300 nm。
2. 1300MPa grades of ultra-fine grained ferrite/low temperature bainite dual-phase steel according to claim 1, it is characterised in that institute
Dual phase steel tensile strength is stated not less than 1300 MPa, yield tensile ratio is 0.50 ~ 0.65, and elongation percentage is not less than 12%.
3. a kind of preparation method of 1300MPa described in claim 1 grades of ultra-fine grained ferrites/low temperature bainite dual-phase steel,
It is characterized in that including the following steps：
A, it makes steel：Ingredient proportion, melting are calculated according to the design requirement of steel and pour into steel ingot；
B, annealing, hot rolling：By the ingot annealing, hot rolling, it is air-cooled to room temperature after hot rolling, obtains hot rolling slab；
C, it quenches：The hot rolling slab is heated to 800 ~ 1000 DEG C, 20 ~ 40min of heat preservation, it is cold to be then put into oil quenching rapidly
But to room temperature, quenching slab is obtained；
D, warm-rolling：The quenching slab is kept the temperature into 1h under the conditions of 450 ~ 550 DEG C, obtains the slab of secondary troostite tissue, then
The rolling deformation for being 30 ~ 50% through 5 ~ 7 passages, progress overall reduction at 500 ~ 600 DEG C by the slab of secondary troostite tissue, it is empty
It is cooled to room temperature, obtains warm-rolling plate；
E, it is heat-treated：By the warm-rolling plate under the conditions of 760 ~ 780 DEG C, 3 ~ 5h is kept the temperature, is then put into 260 ~ 320 DEG C rapidly
1.5 ~ 10 h of isothermal in salt bath furnace, then come out of the stove and be air-cooled to room temperature.
4. the preparation method of 1300MPa grades of ultra-fine grained ferrite/low temperature bainite dual-phase steel according to claim 3,
It is characterized in that in step B that ingot annealing condition is：It is heated to 1200 DEG C ~ 1250 DEG C 2 ~ 5h of heat preservation；The condition of hot rolling is：It will annealing
Steel ingot after heat preservation is air-cooled to 1150 ~ 1180 DEG C of open rollings, rolls 4 ~ 7 passages, and finishing temperature is not less than 880 DEG C, the stagnation pressure of hot rolling
Lower amount is 30 ~ 50%.
5. the preparation method of 1300MPa grades of ultra-fine grained ferrite/low temperature bainite dual-phase steel according to claim 3,
Be characterized in that hot rolled steel plate in step B with a thickness of 20mm, gained warm-rolling plate with a thickness of 10 ~ 14mm in step D.
6. a kind of preparation method of 1300MPa described in claim 1 grades of ultra-fine grained ferrites/low temperature bainite dual-phase steel,
It is characterized in that including the following steps：
A, it makes steel：Ingredient proportion, melting are calculated according to the design requirement of steel and pour into steel ingot；
B, Heating Steel Ingots carry out Homogenization Treatments to 1200 ~ 1250 DEG C of 3 ~ 5 h of heat preservation；Then 1180 DEG C of open rollings, finish to gauge are air-cooled to
Temperature is not less than 880 DEG C, by 5 ~ 6 passes, is finally rolled into the hot rolling slab of 18 ~ 20 mm thickness, hot rolling slab is air-cooled to
Room temperature；
C, quenching and tempering：By after the hot rolling slab that step B is handled is reheated to 850 ~ 950 DEG C of 20 ~ 40 min of heat preservation,
It is put into oil quenching rapidly to be cooled to room temperature, is then placed in 480 ~ 520 DEG C of stove and keeps the temperature 1 h, come out of the stove and be air-cooled to room temperature, make
Obtain the slab of secondary troostite tissue；
D, cold rolling：The multi-pass cold-rolling deformation that slab after tempering is carried out to overall reduction 40%, obtains the cold-reduced sheet of 12 mm thickness
Material；
E, it is heat-treated：Cold rolled sheet is put into the stove that temperature is 760 ~ 780 DEG C, after keeping the temperature 3 ~ 5h, being put into temperature rapidly is
Constant temperature keeps 1.5 ~ 10 h in 260 ~ 320 DEG C of salt bath furnace, then comes out of the stove and is air-cooled to room temperature, obtains ultra-fine grained ferrite/low temperature shellfish
Family name's body dual phase steel plate.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2015109127996 | 2015-12-11 | ||
| CN201510912799 | 2015-12-11 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN106868398A CN106868398A (en) | 2017-06-20 |
| CN106868398B true CN106868398B (en) | 2018-11-30 |
Family
ID=59163928
Family Applications (5)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201611129146.1A Active CN106868413B (en) | 2015-12-11 | 2016-12-09 | Ultra-fine grained ferrite/nanometer bainite two-phase medium carbon steel and preparation method thereof |
| CN201611130221.6A Active CN106868415B (en) | 2015-12-11 | 2016-12-09 | Superhigh intensity ultra-fine grained ferrite/nanometer bainite dual-phase steel and preparation method thereof |
| CN201611128627.0A Active CN106868281B (en) | 2015-12-11 | 2016-12-09 | A kind of ultra-fine grained ferrite/low temperature bainite dual-phase steel and preparation method thereof |
| CN201611130256.XA Active CN106868398B (en) | 2015-12-11 | 2016-12-09 | 1300MPa grades of ultra-fine grained ferrites/low temperature bainite dual-phase steel and preparation method thereof |
| CN201611129217.8A Active CN106868414B (en) | 2015-12-11 | 2016-12-09 | Ultra-fine grained ferrite/low temperature bainite two-phase mild steel and preparation method thereof |
Family Applications Before (3)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201611129146.1A Active CN106868413B (en) | 2015-12-11 | 2016-12-09 | Ultra-fine grained ferrite/nanometer bainite two-phase medium carbon steel and preparation method thereof |
| CN201611130221.6A Active CN106868415B (en) | 2015-12-11 | 2016-12-09 | Superhigh intensity ultra-fine grained ferrite/nanometer bainite dual-phase steel and preparation method thereof |
| CN201611128627.0A Active CN106868281B (en) | 2015-12-11 | 2016-12-09 | A kind of ultra-fine grained ferrite/low temperature bainite dual-phase steel and preparation method thereof |
Family Applications After (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201611129217.8A Active CN106868414B (en) | 2015-12-11 | 2016-12-09 | Ultra-fine grained ferrite/low temperature bainite two-phase mild steel and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (5) | CN106868413B (en) |
Families Citing this family (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110863084B (en) * | 2018-08-28 | 2021-08-03 | 南京理工大学 | Processing method for regulating ductility and toughness of dual-phase steel material through surface strong plastic deformation |
| CN111118397A (en) * | 2020-01-19 | 2020-05-08 | 攀钢集团攀枝花钢铁研究院有限公司 | 980 MPa-grade quenching distribution steel and preparation method thereof |
| CN111549286B (en) * | 2020-06-22 | 2021-10-15 | 中南大学 | Easily-welded ultrahigh-strength high-toughness steel and preparation method thereof |
| CN111676362B (en) * | 2020-06-27 | 2021-10-12 | 扬州大学 | Novel quenching-partitioning-isothermal quenching heat treatment method capable of obtaining Si-series ultrahigh-strength disc spring |
| CN111850413B (en) * | 2020-08-06 | 2021-09-21 | 中南大学 | Preparation method of easily-welded fatigue-resistant high-strength and high-toughness alloy steel |
| CN111893391A (en) * | 2020-08-12 | 2020-11-06 | 燕山大学 | Nano bainite hot work die steel and preparation method thereof |
| CN112210726B (en) * | 2020-09-29 | 2022-02-15 | 中国科学院金属研究所 | Ultrahigh-strength nanocrystalline 40Cr2NiMnW structural steel and preparation method thereof |
| CN112725698B (en) * | 2020-12-28 | 2021-12-07 | 郑州航空工业管理学院 | Multi-scale structure block material and preparation method and application thereof |
| CN114737122A (en) * | 2022-04-18 | 2022-07-12 | 燕山大学 | Cu-Ni series hot-work die steel with excellent comprehensive mechanical properties and preparation method thereof |
| CN115181903B (en) * | 2022-06-12 | 2023-04-28 | 北京理工大学 | High-strength high-toughness low-carbon low-alloy steel with bricked structure and preparation method thereof |
| CN115747612B (en) * | 2022-10-19 | 2024-02-09 | 成都先进金属材料产业技术研究院股份有限公司 | Complex-phase H13 hot working die steel and preparation method thereof |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101693981B (en) * | 2009-10-23 | 2011-04-06 | 燕山大学 | Preparation method of low-alloy high-carbon steel with high-strength and high ductility nano structure |
| CN102534369B (en) * | 2012-01-13 | 2013-05-01 | 北京科技大学 | Method for preparing N80 steel-grade expansion tubes for petroleum and natural gas exploitation |
| EP2834378B1 (en) * | 2012-04-04 | 2016-02-24 | Aktiebolaget SKF | Steel alloy |
| CN104109813B (en) * | 2014-07-03 | 2016-06-22 | 西南石油大学 | A kind of big expansion-ratio expansion pipe dual phase steel of high resistance to Produced Water In Oil-gas Fields, Ngi corrosion and preparation method thereof |
| CN104593664B (en) * | 2014-11-13 | 2017-01-25 | 东北大学 | Hot-rolled nanometer bainite steel, production method of hot-rolled nanometer bainite steel and manufacturing method of automotive frame |
-
2016
- 2016-12-09 CN CN201611129146.1A patent/CN106868413B/en active Active
- 2016-12-09 CN CN201611130221.6A patent/CN106868415B/en active Active
- 2016-12-09 CN CN201611128627.0A patent/CN106868281B/en active Active
- 2016-12-09 CN CN201611130256.XA patent/CN106868398B/en active Active
- 2016-12-09 CN CN201611129217.8A patent/CN106868414B/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| CN106868415A (en) | 2017-06-20 |
| CN106868413A (en) | 2017-06-20 |
| CN106868398A (en) | 2017-06-20 |
| CN106868413B (en) | 2018-11-30 |
| CN106868414A (en) | 2017-06-20 |
| CN106868281B (en) | 2018-07-17 |
| CN106868414B (en) | 2018-11-30 |
| CN106868281A (en) | 2017-06-20 |
| CN106868415B (en) | 2018-11-30 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN106868398B (en) | 1300MPa grades of ultra-fine grained ferrites/low temperature bainite dual-phase steel and preparation method thereof | |
| CN106811698B (en) | A kind of high strength steel plate and its manufacture method based on tissue precise controlling | |
| CN102080192B (en) | Low-yield ratio, high-plasticity, ultrafine-grain and high-strength steel and manufacturing method thereof | |
| CN108486494B (en) | The production method of vanadium micro-alloying 1300MPa grade high-strength hot rolled steel plate and cold-rolled biphase steel plate | |
| CN107794357A (en) | The method of super rapid heating technique productions superhigh intensity martensite cold-rolled steel sheet | |
| WO2014188966A1 (en) | Hot-rolled steel sheet and method for manufacturing same | |
| MXPA97008775A (en) | Process to produce steel pipe without seams of great strength having excellent resistance to the fissure by tensions by sulf | |
| US11401569B2 (en) | High-strength cold-rolled steel sheet and method for manufacturing same | |
| CN107012398B (en) | A kind of Nb-microalloying TRIP steel and preparation method thereof | |
| JP5640931B2 (en) | Medium carbon cold-rolled steel sheet excellent in workability and hardenability and its manufacturing method | |
| CN109898017A (en) | 1000MPa grades of cold-bending properties excellent cold-rolled biphase steel and production method | |
| JP2007291514A (en) | Hot-rolled steel sheet with small in-plane anisotropy after cold rolling and recrystallization annealing, cold-rolled steel sheet with small in-plane anisotropy and production method therefor | |
| JP2014189868A (en) | High strength steel sheet and manufacturing method therefor | |
| JP2016028172A (en) | Cold rolled steel sheet and production method therefor | |
| JP2002285278A (en) | High strength and high ductility steel sheet with hyperfine crystal grain structure obtainable by subjecting plain low carbon steel to low strain working and annealing and production method therefor | |
| CN107177783A (en) | A kind of Ultra-fine Grained martensite ferrite dual phase steel being distributed with bimodal ferrite crystal grain and its production technology | |
| JP5302840B2 (en) | High-strength cold-rolled steel sheet with an excellent balance between elongation and stretch flangeability | |
| CN106957995B (en) | Fine ferrite grain/low temperature bainite two-phase mild steel and preparation method thereof | |
| CN110100027A (en) | The steel plate and its manufacturing method of low yielding ratio with excellent low-temperature flexibility | |
| JP2012224884A (en) | High strength steel material having excellent strength, ductility and energy absorption power, and method for producing the same | |
| JP2022537538A (en) | Untempered wire rod with excellent wire drawability and impact toughness, and method for producing the same | |
| CN106319375A (en) | Punching alloy structural steel cold-rolled plate and preparation method thereof | |
| CN111440991B (en) | Hot rolled steel plate with yield strength of 800MPa and manufacturing method thereof | |
| JP6121292B2 (en) | High-strength steel sheet having high yield ratio and formability and manufacturing method thereof | |
| CN106591696A (en) | Hot-rolled multi-phase steel with excellent flangability and production method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |