CN107177783A - A kind of Ultra-fine Grained martensite ferrite dual phase steel being distributed with bimodal ferrite crystal grain and its production technology - Google Patents
A kind of Ultra-fine Grained martensite ferrite dual phase steel being distributed with bimodal ferrite crystal grain and its production technology Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
- 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
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/28—Normalising
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0231—Warm rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- 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
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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
- C21D2211/008—Martensite
Abstract
The invention discloses a kind of Ultra-fine Grained martensite ferrite dual phase steel being distributed with bimodal ferrite crystal grain and its production technology, after obtaining steel billet through smelting, casting, forging, hot rolling, the steel billet is heat-treated, including following process：Homogenizing annealing, normalizing, warm-rolling and continuous annealing；Described continuous annealing includes three phases：(1) Ac is heated to 40 DEG C/s~80 DEG C/s speed1Temperature；(2) continue to be warming up to 740~800 DEG C with 1 DEG C/s~5 DEG C/s speed；(3) quench.The technique of the present invention refines austenite crystal, and ferrite crystal grain is into the feature of bimodal Size Distribution, and room temperature its uniform elongation of leaving behind is greatly improved, 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 being distributed with 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
Hit energy absorption capability and turn into important automobile steel, and be widely used, but high strength dual phase steel is because of intensity
Raising declines plasticity, it is impossible to meet 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 polycrystal intensity is improved.People are ultra-fine
Brilliant concept is incorporated into dual phase steel, and domestic and foreign scholars prepare ultra-fine crystal two-phase steel using different methods so far, and it is brilliant
Particle size has reached less than 3 μm.Although ultra-fine crystal two-phase steel has preferably strong plasticity matching, it is thin due to crystal grain
Change, cause it to bend intensity and improve, yield tensile ratio increase.And its uniform elongation is also reduced compared with before refinement.
It is in the past relatively low in order to solve Ultra-fine Grained Ferrite Steel work hardening rate, the problem of its uniform elongation is low is caused, is adopted
Appropriate relatively coarse crystal grain is introduced in ultrafine-grained (UFG) microstructure, that is, causes the grainiess of crystallite dimension bimodal distribution, can
So that 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, former martensite formation Ultra-fine Grained group are opened
Knit, and former ferrite formation more texture of coarse crystal, obtain the crystal grain group mainly by a diameter of 50~200nm and 1~2 μm
Into 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 the hard phase being distributed in island, and ferrite is soft phase；Ferrite crystal grain average diameter is 0.7~1.2 μm, carbide particle
Average diameter is 65~86nm.Although due to the presence of hard phase martensite in ultra-fine crystal two-phase steel, its work hardening rate is obtained
Improve, but its uniform elongation is still relatively low compared with coarse-grain dual phase steel.
So, the uniform elongation of Ultra-fine Grained martensite ferrite dual phase steel how is improved, is those skilled in the art's mesh
The preceding technical issues that need to address.
The content of the invention
It is an object of the invention 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 above goal of the invention, the present invention provides a kind of production work of Ultra-fine Grained martensite ferrite dual phase steel
Skill, through smelting, casting, forge, hot rolling obtains steel billet, and 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 to eliminate the banded structure in steel billet, homogenize fine microstructures.
Segregation occurs for the ferrite crystal grain refined after warm-rolling, carbide particle.For the follow-up continuous annealing stage
There is provided original structure.
Described continuous annealing includes three phases：
(1) Ac is heated to 40 DEG C/s~80 DEG C/s speed1Temperature；
(2) continue to be warming up to 740~800 DEG C with 1 DEG C/s~5 DEG C/s speed；
(3) quench.
In the continuous annealing stage, steel plate is first with 40~80 DEG C/s heating rate to Ac1After temperature with 1~5 DEG C/
S is heated to annealing temperature.In rapid heat-up stage, because 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, both
Influence each other, the crystallite dimension of fining ferrite and austenite, and the ferrite recrystallized is grown up in this stage.In addition, by
In causing that distribution of carbides is uneven in tissue after warm-rolling, in high density carbides enrichment region, the Enhancing Nucleation Density of austenite increases,
Prevent ferritic growth.In low density carbon compound enrichment region, because austenite Enhancing Nucleation Density is relatively low, ferrite occurs to tie again
Resistance that is brilliant and growing up reduces, and generates relatively coarse ferrite crystal grain.
Above-mentioned several stages cooperate, and reach the purpose of fining ferrite martensite dual-phase steel crystal grain, and cause iron element
Body crystal grain has the feature of bimodal distribution, obtained ferrito-martensite dual phase sheet steel band have higher uniform elongation and compared with
Low yield tensile ratio.
Preferably, described warm-rolling is, at 450~600 DEG C, to carry out air cooling after warm-rolling.
Preferably, described normalizing is in 900~950 DEG C, 30~60min of normalized treatment.
Preferably, described homogenizing annealing is in 1100~1200 DEG C, 10~15h of homogenizing annealing.
Preferably, the finishing temperature of the hot rolling is 800~850 DEG C, and air cooling is to room temperature after hot rolling.
Preferably, the composition 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 is 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 is obtained
Ultra-fine Grained martensite ferrite dual phase steel has the feature of bimodal ferrite crystal grain distribution, and fine grain part ferrite grain size is
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
Rate is stretched more than 14%, and yield tensile ratio is less than 0.5.Beneficial effects of the present invention：
The production technology for the Ultra-fine Grained martensite ferrite dual phase steel that the present invention is provided refines austenite crystal, iron
Ferritic crystal grain is into the feature of bimodal Size Distribution, and its uniform elongation is greatly improved under room temperature tensile, and yield tensile ratio is small
In 0.5.
Brief description of the drawings
The width of accompanying drawing 7 of the present invention,
Fig. 1 is the temperature-time curve figure that is 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 is produced
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 is produced
Sub- microphotograph 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 is produced；
Fig. 6 is the transmission electron microscope photo figure of the martensite ferritic structure for the dual phase sheet steel band that embodiment 2 is produced；
Fig. 7 is the ferritic ferrite grain size distribution map of martensite for the dual phase sheet steel band that embodiment 2 is produced；
Fig. 8 is the scanning electricity of the ferritic martensite ferritic structure of martensite for the dual phase sheet steel band that embodiment 3 is produced
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 is produced；
Figure 10 is the ferritic ferrite grain size distribution map of martensite for the dual phase sheet steel band that embodiment 3 is produced.
Embodiment
In order that those skilled in the art more fully understand the present invention program, it is right with reference to the accompanying drawings and detailed description
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
Formula, after obtaining steel billet through smelting, casting, forging, hot rolling, the steel billet is heat-treated, including following process：Homogenization is moved back
Fire, normalizing, warm-rolling and continuous annealing；First stage, hot-rolled steel is subjected to 1100~1200 DEG C, 10~15h homogenizing annealing；
Second stage, carries out 900~950 DEG C, 30~60min normalized treatment；Phase III, in 450~600 DEG C of temperature range
Warm-rolling is carried out, accumulation strain is ε=2.0~2.8, rolls rear air cooling to room temperature；Sample after fourth stage, warm-rolling is in continuous annealing
Annealed 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 1~5 DEG C/s rate of heat addition after Ac1 temperature and moves back
Fiery temperature (740~800 DEG C), is quenched into room temperature, to complete continuous annealing immediately.
In a kind of embodiment, the steel billet that the production technology of above-mentioned martensite ferrite dual phase steel is selected be through
50kg induction furnace melting is formed, by weight percentage, its 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 is Fe.Ingot casting is smelted after casting, and being forged into square billet is used for hot rolling.Hot rolling is whole
Temperature is rolled for 800~850 DEG C, is rolled rear air cooling to room temperature, is obtained the thick slabs of 4.0~4.5mm.
In a preferred embodiment, the plate after warm-rolling, warm-rolling is carried out to the strip after normalizing using four rod milling trains
Base thickness is 0.3~0.5mm.
Following non-limiting examples can make one of ordinary skill 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：
1st, microstructure observation is carried out to the sample after annealing using the ESEMs of Quanta 600.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.
2nd, the fine structure of microstructure is observed using TECNAIG220 transmission electron microscopes；Utilize
The full-automatic phase transformation instrument of Fomastor-F II determines Ac1Temperature.
3rd, square-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
It is from ingot casting composition by weight percent：C 0.11%, Mn 1.83%, Si 0.062%, Al 0.38%, Mo
0.17%, Cr 0.37%, Nb 0.04%, surplus is Fe.Finishing temperature is 800 DEG C, rolls back plate tape thickness for 4.3mm.Hot rolling
Slab stove after 1100 DEG C of 10h that anneal is as cold as room temperature, afterwards in 900 DEG C of normalizing 30min, is reheated to 570 DEG C of insulation 10min
Warm-rolling, air cooling to room temperature are carried out, obtained slab thickness is 0.35mm (ε=2.5)；Slab after warm-rolling is tried in continuous annealing
Test on machine and annealed, first paragraph heating (FHS) speed is 40 DEG C/s, is heated to Ac1Temperature (655 DEG C), second segment heating
(SHS) speed 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
Sheet material, it is 0.5~3 μm, coarse-grain ferrite grain size that fine grain part ferrite grain size is measured with SEM
For 3~6.5 μm, its tensile strength is 905MPa at room temperature, and uniform elongation is 15.3%, and yield tensile ratio is 0.48.ESEM
As shown in Figures 2 and 3, ferrite grain size distribution is as shown in Figure 4 for tissue and transmission electron microscope macrograph.
Embodiment 2
It is from ingot casting composition by weight percent：C 0.10%, Mn 1.7%, Si 0.05%, Al 0.35%, Mo
0.16%, Cr 0.35%, Nb 0.037%, surplus is Fe.Finishing temperature is 820 DEG C, rolls back plate tape thickness for 4mm.By hot rolling
Slab stove after 1150 DEG C of 12h that anneal is as cold as room temperature, afterwards in 930 DEG C of normalizing 30min, is reheated to 550 DEG C of insulation 10min
Warm-rolling, air cooling to room temperature are carried out, obtained slab thickness is 0.4mm (ε=2.3)；Slab after warm-rolling is tried in continuous annealing
Test on machine and annealed, first paragraph heating (FHS) speed is 60 DEG C/s, is heated to Ac1Temperature (663 DEG C), second segment heating
(SHS) speed 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 arrived distribution
Sheet material, it is 0.5-3 μm that fine grain part ferrite grain size is measured with SEM, and coarse-grain ferrite grain size is
3-7.5 μm, its tensile strength is 911MPa at room temperature, and uniform elongation is 14.8%, and yield tensile ratio is 0.47.ESEM 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
It is from ingot casting composition by weight percent：C 0.08%, Mn 1.80%, Si 0.06%, Al 0.36%, Mo
0.16%, 0.38%Cr, 0.039%Nb, surplus are Fe.Finishing temperature is 850 DEG C, rolls back plate tape thickness for 4.2mm.By hot rolling
Slab stove after 1180 DEG C of 15h that anneal is as cold as room temperature, afterwards in 950 DEG C of normalizing 20min, is reheated to 500 DEG C of insulation 10min
Warm-rolling, air cooling to room temperature are carried out, obtained slab thickness is 0.45mm (ε=2.2)；Slab after warm-rolling is tried in continuous annealing
Test on machine and annealed, first paragraph heating (FHS) speed is 80 DEG C/s, is heated to Ac1Temperature (678 DEG C), second segment heating
(SHS) speed 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 arrived distribution
Sheet material, the fine grain part ferrite grain size measured with SEM is 0.5~3 μm, coarse-grain ferrite crystal grain chi
Very little is 3~7 μm, and its tensile strength is 932MPa at room temperature, and uniform elongation is 14.2%, and yield tensile ratio is 0.47.ESEM
As shown in Figure 8 and Figure 9, ferrite grain size distribution is as shown in Figure 10 for tissue and transmission electron microscope macrograph.
Claims (9)
1. a kind of production technology of Ultra-fine Grained martensite ferrite dual phase steel, through smelting, casting, forge, hot rolling obtains steel billet, its
It is characterised by, the steel billet is heat-treated, including following process：Homogenizing annealing, normalizing, warm-rolling and continuous annealing；
Described continuous annealing includes three phases：
(1) Ac is heated to 40 DEG C/s~80 DEG C/s speed1Temperature；
(2) continue to be warming up to 740~800 DEG C with 1 DEG C/s~5 DEG C/s speed；
(3) quench.
2. the production technology of Ultra-fine Grained martensite ferrite dual phase steel according to claim 1, it is characterised in that described
Warm-rolling is, at 450~600 DEG C, to carry out air cooling after warm-rolling.
3. the production technology of Ultra-fine Grained martensite ferrite dual phase steel according to claim 1, it is characterised in that described
Normalizing is in 900~950 DEG C, 30~60min of normalized treatment.
4. the production technology of Ultra-fine Grained martensite ferrite dual phase steel according to claim 1, it is characterised in that described
Homogenizing annealing is in 1100~1200 DEG C, 10~15h of homogenizing annealing.
5. the production technology of Ultra-fine Grained martensite ferrite dual phase steel according to claim 1, it is characterised in that the heat
The finishing temperature rolled is 800~850 DEG C, and air cooling is to room temperature after hot rolling.
6. the production technology of Ultra-fine Grained martensite ferrite dual phase steel according to claim 1, it is characterised in that the steel
The composition of base, 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%, it is remaining
Measure as Fe.
7. the Ultra-fine Grained martensite ferrite dual phase steel that production technology described in claim 1-6 any one is obtained, its feature exists
In the Ultra-fine Grained martensite ferrite dual phase steel has the feature of bimodal ferrite crystal grain distribution, and fine grain part ferrite is brilliant
Particle size is 0.5~3 μm, and coarse-grain part ferrite grain size is 3~8 μm.
8. Ultra-fine Grained martensite ferrite dual phase steel according to claim 7, it is characterised in that the crystal grain of the martensite
Size is less than 3 μm.
9. Ultra-fine Grained martensite ferrite dual phase steel according to claim 8, it is characterised 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.
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| CN110527792A (en) * | 2019-08-26 | 2019-12-03 | 武汉科技大学 | Reduce the tempering method of residual stress |
| CN111363901A (en) * | 2018-12-26 | 2020-07-03 | 宝山钢铁股份有限公司 | Ferrite-martensite hot-rolled dual-phase steel with high surface quality and manufacturing method thereof |
| 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 |
| CN113151645A (en) * | 2021-04-14 | 2021-07-23 | 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 |
| CN114085971A (en) * | 2021-11-16 | 2022-02-25 | 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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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN111363901A (en) * | 2018-12-26 | 2020-07-03 | 宝山钢铁股份有限公司 | Ferrite-martensite hot-rolled dual-phase steel with high surface quality and manufacturing method thereof |
| CN111363901B (en) * | 2018-12-26 | 2022-06-24 | 宝山钢铁股份有限公司 | Ferrite-martensite hot-rolled dual-phase steel with high surface quality and manufacturing method thereof |
| CN110527792A (en) * | 2019-08-26 | 2019-12-03 | 武汉科技大学 | Reduce the tempering method of 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 |
| CN113151645A (en) * | 2021-04-14 | 2021-07-23 | 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 |
| CN114085971A (en) * | 2021-11-16 | 2022-02-25 | 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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