CN107177783B - A kind of Ultra-fine Grained martensite ferrite dual phase steel and its production technology with the distribution of bimodal ferrite crystal grain - Google Patents
A kind of Ultra-fine Grained martensite ferrite dual phase steel and its production technology with the distribution of bimodal ferrite crystal grain Download PDFInfo
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- CN107177783B CN107177783B CN201710600110.5A CN201710600110A CN107177783B CN 107177783 B CN107177783 B CN 107177783B CN 201710600110 A CN201710600110 A CN 201710600110A CN 107177783 B CN107177783 B CN 107177783B
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- 229910000859 α-Fe Inorganic materials 0.000 title claims abstract description 64
- 229910000734 martensite Inorganic materials 0.000 title claims abstract description 42
- 229910000885 Dual-phase steel Inorganic materials 0.000 title claims abstract description 30
- 239000013078 crystal Substances 0.000 title claims abstract description 28
- 238000009826 distribution Methods 0.000 title claims abstract description 24
- 230000002902 bimodal effect Effects 0.000 title claims abstract description 15
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 15
- 238000000137 annealing Methods 0.000 claims abstract description 31
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 29
- 239000010959 steel Substances 0.000 claims abstract description 29
- 238000005096 rolling process Methods 0.000 claims abstract description 21
- 238000005098 hot rolling Methods 0.000 claims abstract description 12
- 238000005266 casting Methods 0.000 claims abstract description 9
- 238000000034 method Methods 0.000 claims abstract description 7
- 238000003723 Smelting Methods 0.000 claims abstract description 4
- 238000005242 forging Methods 0.000 claims abstract description 4
- 238000010792 warming Methods 0.000 claims abstract description 4
- 229910052804 chromium Inorganic materials 0.000 claims description 6
- 229910052748 manganese Inorganic materials 0.000 claims description 6
- 229910052750 molybdenum Inorganic materials 0.000 claims description 6
- 229910052758 niobium Inorganic materials 0.000 claims description 6
- 239000004615 ingredient Substances 0.000 claims description 2
- 229910001566 austenite Inorganic materials 0.000 abstract description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 9
- 230000009977 dual effect Effects 0.000 description 8
- 230000005540 biological transmission Effects 0.000 description 7
- 239000000203 mixture Substances 0.000 description 4
- 238000001816 cooling Methods 0.000 description 3
- 230000005611 electricity Effects 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 238000004321 preservation Methods 0.000 description 3
- 230000002708 enhancing effect Effects 0.000 description 2
- 150000001247 metal acetylides Chemical class 0.000 description 2
- 238000010899 nucleation Methods 0.000 description 2
- 230000006911 nucleation Effects 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- 241001417490 Sillaginidae Species 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 238000009825 accumulation Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 150000001722 carbon compounds Chemical class 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000003801 milling Methods 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing 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
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/28—Normalising
-
- 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
- C21D8/0247—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
- C22C38/06—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
- C22C38/18—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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- 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
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium 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
- C21D2211/005—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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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The invention discloses a kind of Ultra-fine Grained martensite ferrite dual phase steel with the distribution of bimodal ferrite crystal grain and its production technology to be heat-treated the steel billet after smelting, casting, forging, hot rolling obtain steel billet, including following process：Homogenizing annealing, normalizing, warm-rolling and continuous annealing；The continuous annealing includes three phases：(1) Ac is heated to the rate of 40 DEG C/s~80 DEG C/s1Temperature；(2) continue to be warming up to 740~800 DEG C with the rate of 1 DEG C/s~5 DEG C/s；(3) it quenches.The technique of the present invention makes austenite grain refine, and at the feature of bimodal Size Distribution, room temperature pulls down its uniform elongation and be greatly improved ferrite crystal grain, and yield tensile ratio is less than 0.5.
Description
Technical field
The invention belongs to metallurgical material technical field, more particularly to a kind of Ultra-fine Grained with the distribution of bimodal ferrite crystal grain
Martensite ferrite dual phase steel and its production technology.
Background technology
Martensite ferrite dual phase steel with its good intensity and plasticity matching, high initial manufacture hardening ratio, high touch
It hits energy absorption capability and becomes important automobile steel, and be widely used, but high strength dual phase steel is because of intensity
Raising makes plasticity decline, and cannot be satisfied the requirement of deep drawability, limits its application in terms of stamping parts.
Crystal grain thinning can also be such that its plasticity is improved with toughness while improving polycrystal intensity.People are ultra-fine
Brilliant concept is introduced into dual phase steel, and domestic and foreign scholars prepare ultra-fine crystal two-phase steel using different methods so far, brilliant
Particle size has reached 3 μm or less.Although ultra-fine crystal two-phase steel has preferable strong plasticity matching, it is thin due to crystal grain
Change, causes it to bend intensity and improve, yield tensile ratio increases.And its uniform elongation also reduces compared with before refinement.
In the past relatively low in order to solve Ultra-fine Grained Ferrite Steel work hardening rate, the problem for causing its uniform elongation low is adopted
Suitable relatively coarse crystal grain is introduced in ultrafine-grained (UFG) microstructure, that is, causes the grain structure of crystallite dimension bimodal distribution, it can
Elongation percentage is greatly improved in the case of loss of strength very little.As Chinese invention patent prospectus CNC1632138A is public
The process that 20CrMnTi steel obtains bimodal grain size distribution ultrafine-grained (UFG) microstructure is opened, former martensite forms Ultra-fine Grained group
It knits, and former ferrite forms more texture of coarse crystal, obtains the crystal grain group mainly by a diameter of 50~200nm and 1~2 μm
At bimodal grain size distribution tissue.Chinese invention patent prospectus CN101671772A discloses Ultra-fine Grained iron element
The preparation method of body and nano-carbide low-carbon steel plate, using martensite+ferrite dual phase tissue warm-rolling, horse in duplex structure
Family name's body is in the hard phase of island distribution, and ferrite is soft phase；Ferrite crystal grain average diameter is 0.7~1.2 μm, carbide particle
Average diameter is 65~86nm.Although since the presence of hard phase martensite, work hardening rate obtain in ultra-fine crystal two-phase steel
It improves, but its uniform elongation is still relatively low compared with coarse-grain dual phase steel.
It is those skilled in the art's mesh so how to improve the uniform elongation of Ultra-fine Grained martensite ferrite dual phase steel
The preceding technical issues that need to address.
Invention content
The object of the present invention is to provide a kind of production technology of Ultra-fine Grained martensite ferrite dual phase steel, obtained Ultra-fine Grained
Martensite ferrite dual phase steel has low yield tensile ratio and high uniform elongation.
In order to realize that the above goal of the invention, the present invention provide a kind of production work of Ultra-fine Grained martensite ferrite dual phase steel
Skill obtains steel billet through smelting, casting, forging, hot rolling, the steel billet is heat-treated, including following process：Homogenizing annealing
(Homogenizing annealing), normalizing (Normalized), warm-rolling (Warm rolled) and continuous annealing
(Continuous annealing)；
Homogenizing annealing and the purpose of normalizing are the banded structures eliminated in steel billet, and fine microstructures is made to homogenize.
Segregation occurs for the ferrite crystal grain refined after warm-rolling, carbide particle.For the subsequent continuous annealing stage
Provide original structure.
The continuous annealing includes three phases：
(1) Ac is heated to the rate of 40 DEG C/s~80 DEG C/s1Temperature；
(2) continue to be warming up to 740~800 DEG C with the rate of 1 DEG C/s~5 DEG C/s；
(3) it quenches.
In the continuous annealing stage, steel plate is heated to Ac with the rate of heat addition of 40~80 DEG C/s first1After temperature with 1~5 DEG C/
S is heated to annealing temperature.In rapid heat-up stage, since the rate of heat addition is very fast, partial, re-crystallization only occurs for ferrite, is reaching
Austenite transition temperature (Ac1) after, into the slow heat stage, austenite phase transformation occurs simultaneously with ferrite recrystallization, the two
It influences each other, the crystallite dimension of fining ferrite and austenite, and the ferrite recrystallized is grown up in this stage.In addition, by
So that distribution of carbides is uneven in tissue after warm-rolling, increase in the Enhancing Nucleation Density of high density carbides enrichment region, austenite,
Prevent ferritic growth.In low density carbon compound enrichment region, since austenite Enhancing Nucleation Density is relatively low, ferrite generation is tied again
Resistance that is brilliant and growing up reduces, and produces relatively coarse ferrite crystal grain.
Above-mentioned several stages cooperate, and achieve the purpose that fining ferrite martensite dual-phase steel crystal grain, and make iron element
Body crystal grain have bimodal distribution feature, obtained ferrito-martensite dual phase sheet steel band have higher uniform elongation and compared with
Low yield tensile ratio.
Preferably, the warm-rolling be at 450~600 DEG C, carry out warm-rolling after it is air-cooled.
Preferably, the normalizing is 30~60min of normalized treatment at 900~950 DEG C.
Preferably, the homogenizing annealing is 10~15h of homogenizing annealing at 1100~1200 DEG C.
Preferably, the finishing temperature of the hot rolling is 800~850 DEG C, air-cooled after hot rolling to arrive room temperature.
Preferably, the ingredient of the steel billet, by weight percentage, C 0.08%~0.15%, Mn 1.60%~
2.00%, Si 0.05%~0.10%, Al 0.35%~0.45%, Mo 0.15%~0.20%, Cr 0.35%~
0.40%, Nb 0.035%~0.04%, surplus Fe.
It is described it is a further object of the present invention to provide the Ultra-fine Grained martensite ferrite dual phase steel that above-mentioned production technology obtains
Feature of the Ultra-fine Grained martensite ferrite dual phase steel with the distribution of bimodal ferrite crystal grain, fine grain part ferrite grain size are
0.5~3 μm, coarse-grain part ferrite grain size is 3~8 μm.
Preferably, the crystal grain of the martensite is less than 3 μm.
Preferably, at room temperature, the tensile strength of the Ultra-fine Grained martensite ferrite dual phase steel is more than 900MPa, uniformly prolongs
It stretches rate and is more than 14%, yield tensile ratio is less than 0.5.Beneficial effects of the present invention：
The production technology of Ultra-fine Grained martensite ferrite dual phase steel provided by the invention makes austenite grain refine, iron
Ferritic crystal grain is at the feature of bimodal Size Distribution, its uniform elongation is greatly improved under room temperature tensile, and yield tensile ratio is small
In 0.5.
Description of the drawings
7 width of attached drawing of the present invention,
Fig. 1 is the temperature-time curve figure being heat-treated in Ultra-fine Grained martensite ferrite dual phase steel production technology of the present invention；
Fig. 2 is the scanning electricity of the martensite ferritic structure for the Ultra-fine Grained martensite ferrite dual phase steel that embodiment 1 produces
Mirror photo figure；
Fig. 3 is the transmission electricity of the martensite ferritic structure for the Ultra-fine Grained martensite ferrite dual phase steel that embodiment 1 produces
Sub- microscope photo figure；
Fig. 4 is the ferrite grain size distribution map that embodiment 1 produces Ultra-fine Grained martensite ferrite dual phase steel；
Fig. 5 is the stereoscan photograph figure of the martensite ferritic structure for the dual phase sheet steel band that embodiment 2 produces；
Fig. 6 is the transmission electron microscope photo figure of the martensite ferritic structure for the dual phase sheet steel band that embodiment 2 produces；
Fig. 7 is the ferritic ferrite grain size distribution map of martensite for the dual phase sheet steel band that embodiment 2 produces；
Fig. 8 is the scanning electricity of the ferritic martensite ferritic structure of martensite for the dual phase sheet steel band that embodiment 3 produces
Mirror photo figure；
Fig. 9 is the ferritic transmission electron microscope photo figure of martensite for the dual phase sheet steel band that embodiment 3 produces；
Figure 10 is the ferritic ferrite grain size distribution map of martensite for the dual phase sheet steel band that embodiment 3 produces.
Specific implementation mode
It is right with reference to the accompanying drawings and detailed description in order to make those skilled in the art more fully understand the present invention program
The present invention is further described in detail.
Fig. 1 is a kind of specific embodiment party of the production technology of Ultra-fine Grained martensite ferrite dual phase steel provided by the present invention
The steel billet is heat-treated by formula after smelting, casting, forging, hot rolling obtain steel billet, including following process：Homogenization is moved back
Fire, normalizing, warm-rolling and continuous annealing；Hot-rolled steel is carried out 1100~1200 DEG C, the homogenizing annealing of 10~15h by the first stage；
Second stage carries out 900~950 DEG C, the normalized treatment of 30~60min；Phase III, in 450~600 DEG C of temperature range
Warm-rolling is carried out, accumulation strain is ε=2.0~2.8, is rolled rear air-cooled to room temperature；Fourth stage, the sample after warm-rolling is in continuous annealing
It anneals in stove, continuous annealing is divided into 3 stages, quick bringing-up section (FHS), slow heat section (SHS) and quenching section (WQ).Its
In, the quick bringing-up section rate of heat addition is 40~80 DEG C/s, is heated to be warming up to the rate of heat addition of 1~5 DEG C/s after Ac1 temperature and move back
Fiery temperature (740~800 DEG C), is quenched into room temperature, to complete continuous annealing immediately.
In a specific embodiment, above-mentioned martensite ferrite dual phase steel production technology select steel billet be through
The induction furnace melting of 50kg forms, by weight percentage, chemical composition be C 0.08%~0.15%, Mn 1.60%~
2.00%, Si 0.05%~0.10%, Al 0.35%~0.45%, Mo 0.15%~0.20%, Cr 0.35%~
0.40%, Nb 0.035%~0.045%, surplus Fe.After ingot casting smelts casting, square billet is forged into for hot rolling.Hot rolling is whole
Roll temperature be 800~850 DEG C, roll it is rear it is air-cooled arrive room temperature, obtain the slab of 4.0~4.5mm thickness.
In a preferred embodiment, warm-rolling, the plate after warm-rolling are carried out to the strip after normalizing using four rod milling trains
Base thickness is 0.3~0.5mm.
Following non-limiting embodiments can make those skilled in the art be more fully understood the present invention, but not with
Any mode limits the present invention.
In the embodiment of the present invention：
1, microstructure observation is carried out to the sample after annealing using 600 scanning electron microscope of Quanta.It is long using mean intercept
The size of legally constituted authority meter crystallite dimension is spent, each sample about counts 1000 crystal grain to determine the size of crystallite dimension with theirs
Distribution.
2, the fine structure of microstructure is observed using TECNAIG220 transmission electron microscopes；It utilizes
II full-automatic phase transformation instrument of Fomastor-F measures Ac1Temperature.
3, rectangular section standard tensile specimen is made by GB/T228-2002, in CMT5105-SANS microcomputer controlled electronics ten thousand
Stretching experiment can be carried out in experimental machine.
Embodiment 1
Select ingot casting composition by weight percent be：C 0.11%, Mn 1.83%, Si 0.062%, Al 0.38%, Mo
0.17%, Cr 0.37%, Nb 0.04%, surplus Fe.Finishing temperature is 800 DEG C, and it is 4.3mm to roll back plate tape thickness.Hot rolling
Slab furnace cooling after 10h of annealing at 1100 DEG C, later in 900 DEG C of normalizing 30min, is reheated to 570 DEG C of heat preservation 10min to room temperature
Warm-rolling is carried out, air-cooled to arrive room temperature, obtained slab thickness is 0.35mm (ε=2.5)；Slab after warm-rolling is tried in continuous annealing
It tests on machine and anneals, it is 40 DEG C/s that first segment, which heats (FHS) rate, is heated to Ac1Temperature (655 DEG C), second segment heating
(SHS) rate is 2 DEG C/s, is quenched immediately after being heated to 750 DEG C.The ultra-fine crystal two-phase steel of the bimodal ferrite distribution finally obtained
Plank, it is 0.5~3 μm to measure fine grain part ferrite grain size with scanning electron microscope, coarse-grain ferrite grain size
It it is 3~6.5 μm, its tensile strength is 905MPa, uniform elongation 15.3%, yield tensile ratio 0.48 at room temperature.Scanning electron microscope
Tissue and transmission electron microscope macrograph are as shown in Figures 2 and 3, and ferrite grain size distribution is as shown in Figure 4.
Embodiment 2
Select ingot casting composition by weight percent be：C 0.10%, Mn 1.7%, Si 0.05%, Al 0.35%, Mo
0.16%, Cr 0.35%, Nb 0.037%, surplus Fe.Finishing temperature is 820 DEG C, and it is 4mm to roll back plate tape thickness.By hot rolling
Slab furnace cooling after 12h of annealing at 1150 DEG C, later in 930 DEG C of normalizing 30min, is reheated to 550 DEG C of heat preservation 10min to room temperature
Warm-rolling is carried out, air-cooled to arrive room temperature, obtained slab thickness is 0.4mm (ε=2.3)；Slab after warm-rolling is tried in continuous annealing
It tests on machine and anneals, it is 60 DEG C/s that first segment, which heats (FHS) rate, is heated to Ac1Temperature (663 DEG C), second segment heating
(SHS) rate is 3 DEG C/s, is quenched immediately after being heated to 760 DEG C.The ultra-fine crystal two-phase steel of the last bimodal ferrite distribution arrived
Plank, it is 0.5-3 μm to measure fine grain part ferrite grain size with scanning electron microscope, and coarse-grain ferrite grain size is
3-7.5 μm, its tensile strength is 911MPa, uniform elongation 14.8%, yield tensile ratio 0.47 at room temperature.Scanning electron microscope tissue
And transmission electron microscope macrograph is as shown in Figure 5 and Figure 6, ferrite grain size distribution is as shown in Figure 7.
Embodiment 3
Select ingot casting composition by weight percent be：C 0.08%, Mn 1.80%, Si 0.06%, Al 0.36%, Mo
0.16%, 0.38%Cr, 0.039%Nb, surplus Fe.Finishing temperature is 850 DEG C, and it is 4.2mm to roll back plate tape thickness.By hot rolling
Slab furnace cooling after 15h of annealing at 1180 DEG C, later in 950 DEG C of normalizing 20min, is reheated to 500 DEG C of heat preservation 10min to room temperature
Warm-rolling is carried out, air-cooled to arrive room temperature, obtained slab thickness is 0.45mm (ε=2.2)；Slab after warm-rolling is tried in continuous annealing
It tests on machine and anneals, it is 80 DEG C/s that first segment, which heats (FHS) rate, is heated to Ac1Temperature (678 DEG C), second segment heating
(SHS) rate is 4 DEG C/s, is quenched immediately after being heated to 770 DEG C.The ultra-fine crystal two-phase steel of the last bimodal ferrite distribution arrived
Plank is 0.5~3 μm with the fine grain part ferrite grain size that scanning electron microscope measures, coarse-grain ferrite crystal grain ruler
Very little is 3~7 μm, its tensile strength is 932MPa, uniform elongation 14.2%, yield tensile ratio 0.47 at room temperature.Scanning electron microscope
Tissue and transmission electron microscope macrograph are as shown in Figure 8 and Figure 9, and ferrite grain size distribution is as shown in Figure 10.
Claims (5)
1. a kind of production technology of Ultra-fine Grained martensite ferrite dual phase steel, steel billet is obtained through smelting, casting, forging, hot rolling,
It is characterized in that, the steel billet is heat-treated, including following process：Homogenizing annealing, normalizing, warm-rolling and continuous annealing；Institute
The continuous annealing stated includes three phases：
(1) Ac is heated to the rate of 40 DEG C/s~80 DEG C/s1Temperature；
(2) continue to be warming up to 740~800 DEG C with the rate of 1 DEG C/s~5 DEG C/s；
(3) it quenches；
The ingredient of the steel billet, by weight percentage, C 0.08%~0.15%, Mn 1.60%~2.00%, Si
0.05%~0.10%, Al 0.35%~0.45%, Mo 0.15%~0.20%, Cr 0.35%~0.40%, Nb
0.035%~0.045%, surplus Fe；
The homogenizing annealing is 10~15h of homogenizing annealing at 1100~1200 DEG C；
The normalizing is 30~60min of normalized treatment at 900~950 DEG C；
The warm-rolling be at 450~600 DEG C, carry out warm-rolling after it is air-cooled.
2. the production technology of Ultra-fine Grained martensite ferrite dual phase steel according to claim 1, which is characterized in that the heat
The finishing temperature rolled is 800~850 DEG C, air-cooled after hot rolling to arrive room temperature.
3. the Ultra-fine Grained martensite ferrite dual phase steel that production technology described in claims 1 or 2 obtains, which is characterized in that described
Feature of the Ultra-fine Grained martensite ferrite dual phase steel with the distribution of bimodal ferrite crystal grain, fine grain part ferrite grain size are
0.5~3 μm, coarse-grain part ferrite grain size is 3~8 μm.
4. Ultra-fine Grained martensite ferrite dual phase steel according to claim 3, which is characterized in that the crystal grain of the martensite
Size is less than 3 μm.
5. Ultra-fine Grained martensite ferrite dual phase steel according to claim 4, which is characterized in that at room temperature, described ultra-fine
The tensile strength of brilliant martensite ferrite dual phase steel is more than 900MPa, and uniform elongation is more than 14%, and yield tensile ratio is less than 0.5.
Priority Applications (1)
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| CN110527792B (en) * | 2019-08-26 | 2020-12-22 | 武汉科技大学 | Tempering method for reducing residual stress |
| CN112680652A (en) * | 2020-10-23 | 2021-04-20 | 莱芜钢铁集团银山型钢有限公司 | Cr-Mo low-alloy steel plate for pressure vessel and preparation method thereof |
| CN113151645B (en) * | 2021-04-14 | 2022-07-15 | 鞍钢集团北京研究院有限公司 | High-ductility maraging steel with excellent fatigue resistance and preparation method thereof |
| CN114085971B (en) * | 2021-11-16 | 2023-03-21 | 沈阳理工大学 | Process method for producing high-strength-ductility ferrite-martensite dual-phase steel by utilizing cross warm rolling continuous annealing |
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| CN102586688B (en) * | 2011-01-10 | 2016-03-30 | 宝山钢铁股份有限公司 | A kind of dual phase sheet steel and manufacture method thereof |
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