CN102618802A - Ultrafine grained dual-phase steel material and production method thereof - Google Patents
Ultrafine grained dual-phase steel material and production method thereof Download PDFInfo
- Publication number
- CN102618802A CN102618802A CN2012100729864A CN201210072986A CN102618802A CN 102618802 A CN102618802 A CN 102618802A CN 2012100729864 A CN2012100729864 A CN 2012100729864A CN 201210072986 A CN201210072986 A CN 201210072986A CN 102618802 A CN102618802 A CN 102618802A
- Authority
- CN
- China
- Prior art keywords
- steel
- steel material
- room temperature
- grain
- crystal particle
- 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.)
- Granted
Links
- 239000000463 material Substances 0.000 title claims abstract description 38
- 229910000885 Dual-phase steel Inorganic materials 0.000 title claims abstract description 21
- 238000004519 manufacturing process Methods 0.000 title abstract description 6
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 71
- 239000010959 steel Substances 0.000 claims abstract description 71
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 22
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 13
- 239000013078 crystal Substances 0.000 claims description 34
- 238000005097 cold rolling Methods 0.000 claims description 19
- 239000002245 particle Substances 0.000 claims description 17
- 239000000956 alloy Substances 0.000 claims description 16
- 239000000126 substance Substances 0.000 claims description 12
- 229910045601 alloy Inorganic materials 0.000 claims description 11
- 238000002360 preparation method Methods 0.000 claims description 11
- 238000009413 insulation Methods 0.000 claims description 10
- 239000000203 mixture Substances 0.000 claims description 10
- 230000009467 reduction Effects 0.000 claims description 10
- 238000005275 alloying Methods 0.000 claims description 9
- 238000005266 casting Methods 0.000 claims description 8
- 230000006698 induction Effects 0.000 claims description 8
- 238000003723 Smelting Methods 0.000 claims description 7
- 229910052799 carbon Inorganic materials 0.000 claims description 6
- 238000005098 hot rolling Methods 0.000 claims description 6
- 241001417490 Sillaginidae Species 0.000 claims description 5
- 238000003801 milling Methods 0.000 claims description 5
- 229910052750 molybdenum Inorganic materials 0.000 claims description 3
- 229910052720 vanadium Inorganic materials 0.000 claims description 3
- 229910052804 chromium Inorganic materials 0.000 claims description 2
- 239000002131 composite material Substances 0.000 claims description 2
- 229910052802 copper Inorganic materials 0.000 claims description 2
- 238000009826 distribution Methods 0.000 claims description 2
- 229910052748 manganese Inorganic materials 0.000 claims description 2
- 229910052759 nickel Inorganic materials 0.000 claims description 2
- 239000007769 metal material Substances 0.000 abstract description 3
- 238000004886 process control Methods 0.000 abstract 1
- 238000000034 method Methods 0.000 description 19
- 230000008569 process Effects 0.000 description 11
- 238000005096 rolling process Methods 0.000 description 10
- 239000007789 gas Substances 0.000 description 8
- 238000005516 engineering process Methods 0.000 description 7
- 238000012545 processing Methods 0.000 description 7
- 238000000137 annealing Methods 0.000 description 6
- 238000001816 cooling Methods 0.000 description 6
- 239000000843 powder Substances 0.000 description 6
- 238000001953 recrystallisation Methods 0.000 description 6
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 5
- 238000004458 analytical method Methods 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 239000000470 constituent Substances 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 239000013081 microcrystal Substances 0.000 description 3
- 238000002791 soaking Methods 0.000 description 3
- 229910001220 stainless steel Inorganic materials 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 239000010964 304L stainless steel Substances 0.000 description 2
- 241000446313 Lamella Species 0.000 description 2
- 101100400378 Mus musculus Marveld2 gene Proteins 0.000 description 2
- 230000005540 biological transmission Effects 0.000 description 2
- 238000010276 construction Methods 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 150000002739 metals Chemical class 0.000 description 2
- 238000001000 micrograph Methods 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 239000010935 stainless steel Substances 0.000 description 2
- 238000007669 thermal treatment Methods 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 208000035126 Facies Diseases 0.000 description 1
- 229910000742 Microalloyed steel Inorganic materials 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 238000004873 anchoring Methods 0.000 description 1
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000011261 inert gas Substances 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 239000002159 nanocrystal Substances 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 239000003208 petroleum Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 238000012958 reprocessing Methods 0.000 description 1
- 230000004044 response Effects 0.000 description 1
- 230000000630 rising effect Effects 0.000 description 1
- 239000013535 sea water Substances 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
Images
Landscapes
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention belongs to the technical field of metal materials, and particularly relates to ultrafine grained dual-phase steel material and a production method thereof. The ultrafine grained dual-phase steel material comprises, in weight percentage, 13.5-14.5% of Cr, 6.1-6.9% of Ni, 2.3-2.7% of Mn, 0.33-0.37% of Si, 0.60-0.90% of Cu, 0.10-0.03% of C, 0.021-0.025% of V, 0.60-0.90% of Mo, 0.02% of P, 0.04% of S and the balance of Fe. The microstructure of the ultrafine grained dual-phase steel material is formed by coaxial ultrafine grains distributed in random orientation, the diameter of each grain is 500-2000 nanometers, microstructure of each grain is formed by austenite and martensite, yield strength of the steel material at room temperature is 1100-1600MPa, tensile strength of the steel material is 1200-1850MPa, and elongation of the steel material is 10-20%. By reasonable component design and process control, the produced hot-rolled steel material has martensitic structure, submicron ultrafine grains and nano-scale twin-lamella structure, and the structures cooperate together so that the steel material has ultrahigh strength and certain plastic deformation.
Description
Technical field
The invention belongs to the metallic substance technical field, particularly a kind of superfine crystal particle dual phase steel material and preparation method thereof.
Background technology
Steel is the most a kind of material of purposes in all metals, in industrial circle widespread uses such as aviation, nuclear energy, naval vessel and petrochemical industry.The order of World Ship construction at present tonnage summation is 300,000,000 5,630 ten thousand tons; The Made in China shipyard accounts for world's hydromotive equipment and builds 69.4% of total amount; Korea S only accounts for 23%; Becoming the first in the world shipbuilding big country though China has gone beyond Korea S and Japan in quantity, is not first shipbuilding power, and this mainly is because receive the restriction of high-performance steel iron material.Seaplane carrier is compared the singularity that is had with steel with the large-sized civil shipping steel and is mainly comprised: anti-seawater corrosion; Anti-magnetic; High thermal resistance and very high intensity, toughness are arranged and good welding property or the like.In recent years; Developed countries such as the U.S., Japan and Russia develop in succession and progressively adopt the above superstrength hull of 400 MPa to substitute traditional HS hull steel with steel; Yet; The shipping steel of China's production at present still can not satisfy the demand of this industrial circle development fully, and along with the fast development of China's shipbuilding, the superstrength hull obviously increases with the demand of steel.The superstrength hull steel not only requires high intensity; Also require to have better low-temperature impact toughness; The production of superstrength hull steel mainly relies on higher alloying constituent both at home and abroad at present; The employing hardening and tempering process is produced, and in order to obtain good toughness, the content that adds Ni in the steel has generally all surpassed 11.5 wt. %; This makes this steel grade cost high always, and therefore developing the superstrength hull steel that performance is more excellent, cost is lower becomes extremely urgent problem in shipbuilding and the ocean platform building industry.
Dual phase steel be meant that soft steel or low-carbon micro steel-alloy obtain through critical zone thermal treatment or cooling controlling and rolling controlling process mainly by plow-steel that ferritic+a spot of martensite is formed; And have continuous surrender, characteristics such as yield tensile ratio is low, work hardening rate is higher and elongation is bigger and by people institute extensive concern; The production technique of dual phase steel mainly contains 2 kinds: heat treating process and hot direct rolling process; By contrast; Hot rolling method production dual phase steel operation is simple, cost is low, practice thrift the man-hour and the energy, be convenient to scale operation, becomes the prefered method of producing dual phase steel, along with the rising of finishing temperature; The tensile strength of dual phase steel can be elevated to 780MPa by 717MPa, and this mainly is to be raise by martensitic percentage composition in the tissue to cause.
Martensite is a kind ofly can make steel hardening, enhanced tissue; On practical applications; For strengthening material is usually directed to martensite strengthening mechanism; Simultaneously; In practical applications, adopt the crystal grain thinning method for strengthening material; This is a kind of intensity of utilizing a large amount of crystal boundary restrictions or anchoring dislocation motion to improve material; Can be described by famous Hall-Petch relation (
), people have observed most metal YIELD STRENGTH and the hardness value trend that reduces to show increase with grain-size from various metals and alloy, defer to the Hall-Petch relation well.
It has been generally acknowledged that nanocrystalline grain size range is d < 100 nm; Ultra-fine crystalline substance (Ultrafine grains; UFG) grain size range is 100 nm < d < 1 μ m; And being defined as of sub-micron grain (Submicron grains) tissue: the size of crystal grain on all directions is all less than 1 μ m, and (High angle grain boundary, ratio HAGB) is greater than 70% for high-angle boundary.Grain refining is known todayly can improve intensity, can improve the flexible main method again, and the grain structure of submicron can make material at room temperature have high intensity and toughness.Usually the grain refining of metallic substance mainly is through traditional viscous deformation processing and annealing process subsequently; Take place promptly that recrystallize and grain growth obtain; The grain-size of the material that this common process is prepared is about 10 μ m, and common coarse crystal steel (grain-size is about 100 μ m) tensile ys s at room temperature
yBe merely 90 MPa, ultra-fine grain micro-alloy steel (Fe-0.8C, grain-size is about 6 μ m) at room temperature stretches, its ys s
yBe about 310 MPa (Bramfitt B.L., Marder A.R., Metallurgical and Petroleum Engineers, 191-198,1973); The stainless ys of commercial use 304L is 370 MPa, tensile strength 900 MPa, and extensibility is 40% (Joshua A.L.; Martin C.M., Chester J.V.T., Effect of strain rate on stress-strain behavior of alloy 309 and 304L austenitic stainless steel; Metallurgical and Materials Transactions A; Vol. 37,147-161,2006); (Eastern steel, Spring House PA) pass through rolling deformation 15% to people such as Taiwan scientist Lee with the 304L stainless steel with commerce; Its ys rises to 370 MPa, and tensile strength 900 MPa, stretching elongation are 40% (Lee W.S.; Lin C.F., Comparative study of the impact response and microstructure of 304L stainless steel with and without pre-strain, Metallurgical and Materials Transactions A; Vol. 33; 2801-2810,2002), have a large amount of twins and martensite in its distortion back microtexture; Though this method makes prepared material reinforcement based on same deformation principle, the tensile strength and the ys of the material that obtains are all lower; People (Chen A.Y., Ruan H.H., Wang J., Chan H.L. such as Lu professor Jian of City University of Hong Kong; Wang Q., Li Q., Lu J., Acta Materialia; Vol.59 3697-3709,2011) adopt the making Nano surface technology, with the processing treatment of commercial 304 stainless steels (thickness is 1mm), make about 10 nm of its surface microstructure size; About 200 nm of crystal grain are located, its ys 1000 MPa, about 1050 MPa of tensile strength for about 50 microns in the distance surface; Though its plasticity is better, extensibility 30%, intensity is significantly improved; But adopt only several centimetres of treatable length of material of its process method institute, thickness is also less, still can't satisfy in the industry demand to steel strength and wear resisting property.
Summary of the invention
Steel tensile strength and the lower problem of ys to the prior art existence; The present invention provides a kind of superfine crystal particle dual phase steel material and preparation method thereof; Purpose is through reasonable component design and technology controlling and process, makes to have a large amount of martensitic stuctures and submicron-grade superfine crystal grain in the prepared HRS material, has the twin lamellae structure of nanoscale simultaneously; Several kinds of coordination effects make this steel when having superstrength and have certain plastic deformation ability.
For realizing above purpose, technical scheme of the present invention is:
A kind of superfine crystal particle dual phase steel material, its chemical constitution is by weight percentage: (13.5 ~ 14.5) % Cr, (6.1 ~ 6.9) % Ni, (2.3 ~ 2.7) % Mn; (0.33 ~ 0.37) % Si, (0.60 ~ 0.90) % Cu, (0.01 ~ 0.03) % C, (0.021 ~ 0.025) % V; (0.60 ~ 0.90) %Mo, < 0.02%, < 0.04%, surplus is the Fe element to S to P; Its microtexture is made up of the superfine crystal particle of orientation stochastic distribution, and the diameter of crystal grain is 500～2000nm, and its microtexture is by austenite and martensite two phase composites; Ys under its room temperature condition is 1100 ~ 1600MPa, and tensile strength is 1200 ~ 1850MPa, and unit elongation is 10 ~ 20%.
Wherein the crystal grain diameter of part martensitic stucture is merely tens nanometers, has the twin lamellae structure at the partial martensite organization internal, about tens nanometers of twin lamellae width.
A kind of superfine crystal particle dual phase steel preparation methods is carried out according to following steps:
By weight percentage, be that the base alloy composition is prepared burden with Fe-(13.5 ~ 14.5) Cr-(2.3 ~ 2.7) Mn-(6.1 ~ 6.9) Ni-(0.01 ~ 0.03) C, the compositing range of other trace alloying elements is: (0.023 ± 0.002) V; (0.075 ± 0.015) Mo smelts alloy material in vacuum induction furnace, in stove, feed rare gas element Ar as shielding gas; Smelting molten steel is cast into steel ingot, and is heated to 1150 ℃, after the abundant solution treatment of insulation 1h; The ingot casting cogging is become steel billet, carry out the hot rolling of two stages, the fs hot-rolled temperature is 1050～1150 ℃; Relative reduction is respectively 35%, and the subordinate phase hot-rolled temperature is 820～950 ℃, and relative reduction is 15%; Steel plate carries out chilling through the ultrafast cool equipment of milling train exit configuration after the finish to gauge, speed between 50～80 ℃/s, be cooled to 650 ℃ after water-cooled to room temperature; Adopt two-roller mill that steel plate is carried out cold-rolling treatment then, deformation range is 50%～75%, after the cold rolling completion this sheet material is placed in the resistance furnace in 450-650 ℃ of insulation 5 min; Water-cooled obtains superfine crystal particle dual phase steel steel plate to room temperature then.。
Compared with prior art, characteristics of the present invention and beneficial effect are:
1. the present invention calculates through stacking fault energy to be carried out to the branch design; Confirm with Fe-(13.5 ~ 14.5) Cr-(2.3 ~ 2.7) Mn-(6.1 ~ 6.9) Ni-(0.01 ~ 0.03) C to be the base alloy composition, the stacking fault energy theoretical value of the material of this alloying constituent is about 17 mJ/mol, and this stacking fault energy helps making institute's molten alloy that martensitic transformation takes place under suitable processing conditions and machinery is twin; Thereby form the martensitic stucture and the twins sub-structure of a large amount of nanoscales; Metal is strengthened, and simultaneously, the steel grade of this alloying constituent is similar with stainless steel; Make the corrosion resistance nature of prepared material stronger, can satisfy the needs that it uses at corrosive atmospheres such as oceans;
2. steel has phase transformation and twin effect among the present invention; In the reprocessing process, will produce the martensite lamella and the twins sub-structure of a large amount of nanometer scale, have the extremely strong big ability of absorption dislocation in this class formation, and make material have very high intensity and certain plastic deformation ability; And have with the stainless steel similar component and determined it to have superior wear and corrosion behavior; Therefore, the automotive industry of this high-intensity steel to developing rapidly, construction industry; Nuclear industry, the development of hi-techs such as new technical field such as shipbuilding has important value;
3. the present invention utilizes process for vacuum induction smelting and continuous rolling technology; And combination continuous annealing and fast cooling technology; Prepare through reasonable technology process and processing parameter and to have two-phase, i.e. the steel of austenite+martensitic stucture and superfine crystal particle structure, average grain size is 800 nm; Because its special heterogeneous microstructure and superfine crystal particle; Make it have very high room temperature tensile intensity, can reach 1850MPa, this intensity is far above the tensile strength with the steel sample of the suitable grain-size of traditional method preparation;
4. the present invention utilizes traditional process for vacuum induction smelting; In conjunction with continuous rolling, continuous annealing and fast cooling technology; Only need to improve processing condition; Control suitable thermal treatment and cooling parameter and can obtain this duplex structure adjustable ratio, the plow-steel material that median size and twin width distribute in the different scale scope.
Description of drawings
Fig. 1 is the electron scanning micrograph of the steel of the embodiment of the invention 1 preparation;
Fig. 2 is the microtexture shape appearance figure of the steel of the embodiment of the invention 3 preparations;
Fig. 3 is under the room temperature condition, and steel of the present invention is the engineering stress of unilateral stretching-engineering strain curve at room temperature;
Among Fig. 3: 1 represents the embodiment of the invention 1 resulting data, the 2 expression embodiment of the invention, 2 resulting data, the 3 expression embodiment of the invention, 3 resulting data.
Embodiment
The melting equipment of the embodiment of the invention is the 150kg vacuum induction melting furnace, has the protection of inert gas device;
Rolling equipment is the two unidirectional asynchronous rolling machines of roller of Φ 450 types;
Cooling apparatus is that cooling rate is the ultrafast cool equipment of multi-nozzle of (50～80) ℃/s;
Heat-preserving equipment is a SX2-12-10 molding box formula resistance furnace.
The alloy raw material that the embodiment of the invention adopts is the analytical pure level; Comprise analytical pure level Fe powder (Fe >=99.9%); Analytical pure level Cr powder (Cr >=99.9%); Analytical pure level Ni powder (Mn >=99.9%), the powder of analytical pure level Mn powder (Mn >=99.9%) and analytical pure level C powder (C >=99.9%) and analytical pure level trace alloying element V and Mo is the base alloy component with Fe-(13.5 ~ 14.5) Cr-(2.3 ~ 2.7) Mn-(6.1 ~ 6.9) Ni-(0.01 ~ 0.03) C.
Below in conjunction with accompanying drawing and embodiment the present invention is further described.
Embodiment 1
With Fe-(13.5 ~ 14.5) Cr-(2.3 ~ 2.7) Mn-(6.1 ~ 6.9) Ni-(0.01 ~ 0.03) C is that the base alloy composition is prepared burden, and the compositing range of other trace alloying elements is: (0.023 ± 0.002) V, and (0.075 ± 0.015) Mo smelts alloy material in vacuum induction furnace; In stove, feed rare gas element Ar as shielding gas, with the smelting molten steel ingot casting and be heated to 1150 ℃, insulation 1h, it is the square base of 100 mm * 100mm that the ingot casting cogging is become the cross section; The controlled rolling of two stages is adopted in hot rolling, and the fs hot-rolled temperature is 1050 ℃, is austenite recrystallization temperature, and the subordinate phase hot-rolled temperature is 820 ℃; Be austenite non-recrystallization temperature, two stage relative reduction is respectively 35% and 15%, is 8 mm through 6 passage thicknesss of slab; After the finish to gauge, the ultrafast cool equipment of configuration carries out chilling to steel plate through the milling train exit immediately, and speed is 50 ℃/s; Be cooled to 650 ℃, be incubated half a hour, water-cooled is to room temperature; It is cold rolling that the gained steel plate is carried out multi-pass, carries out anneal, 450 ℃ of annealing temperatures after each cold rolling; Soaking time 10 min descend a time cold rolling then, and cold rolling total reduction is 75%; After the cold rolling completion this sheet material is placed on 450 ℃ of insulation 5 min in the resistance furnace, water-cooled is to room temperature then, and the steel plate final thickness is 2 mm.
The tabular steel of preparing has two-phase, i.e. austenite+martensitic structure characteristic, and grain-size is 800 nm; Simultaneously, this material has the twin lamellae structure of nanoscale, and its mean sizes is 10 nm; And the great number of grains size is at the superfine crystal particle of nanometer scale, and this hot-rolled sheet steel is 1600MPa in the ys of room temperature, and tensile strength is 1850 MPa; Extensibility is 10%, and is as shown in Figure 3.
Chemical analysis results shows that the chemical composition content of preparation attitude micro-crystal plate steel sample is as shown in table 1:
The superfine crystal particle dual phase steel chemical constitution of table 1 embodiment 1
Sem facies analysis result shows that the average grain size of the steel plate materials of preparing is about 800 nm; Microtexture is made up of austenite+martensite two-phase, has a large amount of twin lamellae structures and nanocrystal bunch, and is as shown in Figure 1; Wherein light tone is represented martensitic stucture; As can be seen from the figure, there is its volume(tric)fraction of a large amount of martensitic phases about 57% in dark-coloured expression austenite structure in the microtexture; The crystal grain of submicron order, nanometer scale twin crystal (TBs) and ε-martensite lamella (ε).
With Fe-(13.5 ~ 14.5) Cr-(2.3 ~ 2.7) Mn-(6.1 ~ 6.9) Ni-(0.01 ~ 0.03) C is that the base alloy composition is prepared burden, and the compositing range of other trace alloying elements is: (0.023 ± 0.002) V, and (0.075 ± 0.015) Mo smelts alloy material in vacuum induction furnace; In stove, feed rare gas element Ar as shielding gas, with the smelting molten steel ingot casting and be heated to 1150 ℃, insulation 1h, it is the square base of 100 mm * 100mm that the ingot casting cogging is become the cross section; The controlled rolling of two stages is adopted in hot rolling, and the fs hot-rolled temperature is 1150 ℃, is austenite recrystallization temperature, and the subordinate phase hot-rolled temperature is 950 ℃; Be austenite non-recrystallization temperature, two stage relative reduction is respectively 35% and 15%, is 8 mm through 6 passage thicknesss of slab; After the finish to gauge, the ultrafast cool equipment of configuration carries out chilling to steel plate through the milling train exit immediately, and speed is 80 ℃/s; Be cooled to 650 ℃, be incubated half a hour, water-cooled is to room temperature; It is cold rolling that the gained steel plate is carried out multi-pass, carries out anneal, 450 ℃ of annealing temperatures after each cold rolling; Soaking time 10 min descend a time cold rolling then, and cold rolling total reduction is 50%; After the cold rolling completion this sheet material is placed on 550 ℃ of insulation 5 min in the resistance furnace, water-cooled is to room temperature then, and the steel plate final thickness is 2 mm.
Prepare superstrength, superfine crystal steel under these processing condition, scanning electron microscope image is as shown in Figure 2, and observation shows: have a large amount of martensitic phases in the microtexture; Its volume(tric)fraction is about 65%, has the crystal grain of submicron order, and its average grain size is about 900 nm; This superfine crystal steel is 1490 MPa in the ys of room temperature; Tensile strength is 1580 MPa, and extensibility is 16%, and is as shown in Figure 3; The crystal grain inside of this steel of transmission electron microscope observation has part twin lamellae structure, mean thickness 30 nm of twins sub-structure.
Chemical analysis results shows that the chemical composition content of preparation attitude micro-crystal plate steel sample is as shown in table 2:
The superfine crystal particle dual phase steel chemical constitution of table 2 embodiment 2
With Fe-(13.5 ~ 14.5) Cr-(2.3 ~ 2.7) Mn-(6.1 ~ 6.9) Ni-(0.01 ~ 0.03) C is that the base alloy composition is prepared burden, and the compositing range of other trace alloying elements is: (0.023 ± 0.002) V, and (0.075 ± 0.015) Mo smelts alloy material in vacuum induction furnace; In stove, feed rare gas element Ar as shielding gas, with the smelting molten steel ingot casting and be heated to 1150 ℃, insulation 1h, it is the square base of 100 mm * 100mm that the ingot casting cogging is become the cross section; The controlled rolling of two stages is adopted in hot rolling, and the fs hot-rolled temperature is 1100 ℃, is austenite recrystallization temperature, and the subordinate phase hot-rolled temperature is 900 ℃; Be austenite non-recrystallization temperature, two stage relative reduction is respectively 35% and 15%, is 8 mm through 6 passage thicknesss of slab; After the finish to gauge, the ultrafast cool equipment of configuration carries out chilling to steel plate through the milling train exit immediately, and speed is 80 ℃/s; Be cooled to 650 ℃, be incubated half a hour, water-cooled is to room temperature; It is cold rolling that the gained steel plate is carried out 2 passages, carries out anneal, 450 ℃ of annealing temperatures after each cold rolling; Soaking time 10 min descend a time cold rolling then, and cold rolling total reduction is 60%; After the cold rolling completion this sheet material is placed on 650 ℃ of insulation 5 min in the resistance furnace, water-cooled is to room temperature then, and the steel plate final thickness is 5 mm.
Can prepare the steel of high-tensile and high-ductility under these processing condition equally; Observation by light microscope shows that its average grain size is about 1 μ m, and this superfine crystal steel is 1100MPa in the ys of room temperature, and tensile strength is 1200 MPa; Extensibility is 20 %, and is as shown in Figure 3; The crystal grain inside of this steel of transmission electron microscope observation has part twin lamellae structure, mean thickness 50 nm of twins sub-structure.
Chemical analysis results shows that the chemical composition content of preparation attitude micro-crystal plate steel sample is as shown in table 3:
The superfine crystal particle dual phase steel chemical constitution of table 3 embodiment 3
Claims (2)
1. a superfine crystal particle dual phase steel material is characterized in that its chemical constitution is by weight percentage: (13.5 ~ 14.5) % Cr, (6.1 ~ 6.9) % Ni; (2.3 ~ 2.7) % Mn, (0.33 ~ 0.37) % Si, (0.60 ~ 0.90) % Cu; (0.01 ~ 0.03) % C, (0.021 ~ 0.025) % V, (0.60 ~ 0.90) %Mo; < 0.02%, < 0.04%, surplus is the Fe element to S to P; Its microtexture is made up of the superfine crystal particle of orientation stochastic distribution, and the diameter of crystal grain is 500～2000nm, and its microtexture is by austenite and martensite two phase composites; Ys under its room temperature condition is 1100 ~ 1600MPa, and tensile strength is 1200 ~ 1850MPa, and unit elongation is 10 ~ 20%.
2. a kind of superfine crystal particle dual phase steel preparation methods as claimed in claim 1 is characterized in that carrying out according to following steps:
By weight percentage, be that the base alloy composition is prepared burden with Fe-(13.5 ~ 14.5) Cr-(2.3 ~ 2.7) Mn-(6.1 ~ 6.9) Ni-(0.01 ~ 0.03) C, the compositing range of other trace alloying elements is: (0.023 ± 0.002) V; (0.075 ± 0.015) Mo smelts alloy material in vacuum induction furnace, in stove, feed rare gas element Ar as shielding gas; Smelting molten steel is cast into steel ingot, and is heated to 1150 ℃, after the abundant solution treatment of insulation 1h; The ingot casting cogging is become steel billet, carry out the hot rolling of two stages, the fs hot-rolled temperature is 1050～1150 ℃; Relative reduction is respectively 35%, and the subordinate phase hot-rolled temperature is 820～950 ℃, and relative reduction is 15%; Steel plate carries out chilling through the ultrafast cool equipment of milling train exit configuration after the finish to gauge, speed between 50～80 ℃/s, be cooled to 650 ℃ after water-cooled to room temperature; Adopt two-roller mill that steel plate is carried out cold-rolling treatment then, deformation range is 50%～75%, after the cold rolling completion this sheet material is placed in the resistance furnace in 450-650 ℃ of insulation 5 min; Water-cooled obtains superfine crystal particle dual phase steel steel plate to room temperature then.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN 201210072986 CN102618802B (en) | 2012-03-20 | 2012-03-20 | Ultrafine grained dual-phase steel material and production method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN 201210072986 CN102618802B (en) | 2012-03-20 | 2012-03-20 | Ultrafine grained dual-phase steel material and production method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN102618802A true CN102618802A (en) | 2012-08-01 |
| CN102618802B CN102618802B (en) | 2013-08-21 |
Family
ID=46559000
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN 201210072986 Expired - Fee Related CN102618802B (en) | 2012-03-20 | 2012-03-20 | Ultrafine grained dual-phase steel material and production method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN102618802B (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| RU2659542C2 (en) * | 2016-12-09 | 2018-07-02 | федеральное государственное бюджетное образовательное учреждение высшего образования "Уфимский государственный авиационный технический университет" | Super-strong high-manganese steel obtained by a combination of strengthening mechanisms |
| CN110423876A (en) * | 2019-08-02 | 2019-11-08 | 清华大学深圳研究生院 | A kind of method that can improve nuclear power plant reactor steel anti-radiation performance |
| CN112210728A (en) * | 2020-09-29 | 2021-01-12 | 中国科学院金属研究所 | Ultrahigh-strength nanocrystalline 3Cr9W2MoSi die steel and preparation method thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101331019A (en) * | 2005-10-24 | 2008-12-24 | 埃克森美孚上游研究公司 | High strength dual phase steel with low yield ratio, high toughness and superior weldability |
| CN102046827A (en) * | 2008-05-21 | 2011-05-04 | 安赛乐米塔尔研究与发展有限责任公司 | Method for manufacturing very high strength, cold-rolled, dual phase steel sheets, and sheets thus produced |
| WO2011062152A1 (en) * | 2009-11-18 | 2011-05-26 | 住友金属工業株式会社 | Austenite stainless steel sheet and method for producing same |
-
2012
- 2012-03-20 CN CN 201210072986 patent/CN102618802B/en not_active Expired - Fee Related
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101331019A (en) * | 2005-10-24 | 2008-12-24 | 埃克森美孚上游研究公司 | High strength dual phase steel with low yield ratio, high toughness and superior weldability |
| CN102046827A (en) * | 2008-05-21 | 2011-05-04 | 安赛乐米塔尔研究与发展有限责任公司 | Method for manufacturing very high strength, cold-rolled, dual phase steel sheets, and sheets thus produced |
| WO2011062152A1 (en) * | 2009-11-18 | 2011-05-26 | 住友金属工業株式会社 | Austenite stainless steel sheet and method for producing same |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| RU2659542C2 (en) * | 2016-12-09 | 2018-07-02 | федеральное государственное бюджетное образовательное учреждение высшего образования "Уфимский государственный авиационный технический университет" | Super-strong high-manganese steel obtained by a combination of strengthening mechanisms |
| CN110423876A (en) * | 2019-08-02 | 2019-11-08 | 清华大学深圳研究生院 | A kind of method that can improve nuclear power plant reactor steel anti-radiation performance |
| CN110423876B (en) * | 2019-08-02 | 2021-09-10 | 清华大学深圳研究生院 | Method for improving radiation resistance of steel for nuclear power plant reactor |
| CN112210728A (en) * | 2020-09-29 | 2021-01-12 | 中国科学院金属研究所 | Ultrahigh-strength nanocrystalline 3Cr9W2MoSi die steel and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN102618802B (en) | 2013-08-21 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN105463324B (en) | A kind of thick-specification high-tenacity pipe line steel and its manufacture method | |
| CN101481780B (en) | Easy-to-weld superfine austenite crystal steel with superhigh intensity and high tenacity and manufacturing method thereof | |
| CN104419878B (en) | Superhigh intensity cold rolling dual phase steel with weatherability and its manufacture method | |
| CN102080192B (en) | Low-yield ratio, high-plasticity, ultrafine-grain and high-strength steel and manufacturing method thereof | |
| CN102876999B (en) | Steel plate for hardening and tempering type low temperature pressure vessel and method for producing steel plate | |
| CN105492643A (en) | High-strength cold-rolled steel sheet and method for manufacturing same | |
| CN101429621B (en) | Nitrogen intensified high-carbon twin crystal inducement plastic steel material and its production technique | |
| CN108796363A (en) | The great surface quality for adapting to large deformation and punch process covers aluminum substrate steel and its production method | |
| CN101906519A (en) | Manufacture method of low yield ratio surface layer ultra fine grain low-carbon steel thick plate | |
| CN105695870A (en) | thick hot rolled sheet steel with 450MPa grade yield strength and manufacturing method thereof | |
| CN106435406B (en) | A kind of Millettia pachycarpa weather-resistant steel plate and its manufacturing method | |
| CN103774041A (en) | Thin-strip continuous casting economical high-strength binding strip with tensile strength more than or equal to 1100MPa and manufacturing method thereof | |
| CN111996461A (en) | X70 pipeline coiled plate for microalloyed resistance welded pipe and production method thereof | |
| CN100577846C (en) | Copper and nickel alloying twin crystal inducing plasticity steel material and preparation technique | |
| CN103757532A (en) | Thin strip continuous casting economic high-strength binding strip with tensile strength of at least 980 MPa and manufacturing method thereof | |
| CN102162063B (en) | Ferritic stainless steel medium plate and manufacturing method thereof | |
| CN102618802B (en) | Ultrafine grained dual-phase steel material and production method thereof | |
| CN102392179B (en) | Steel plate with ultrahigh strength and ultrahigh toughness, and preparation method thereof | |
| CN103757536A (en) | Thin strip continuous casting economic high-strength binding strip with tensile strength of at least 1100 MPa and manufacturing method thereof | |
| CN103436778B (en) | There is low-temperature flexibility flux-cored wire cold rolled strip and production method thereof | |
| CN102643969A (en) | Ultra-high strength plastic low alloy steel with nano structure and preparation method thereof | |
| CN105624567B (en) | A kind of ferrite steel plate of nano-level sphere cementite reinforcing and preparation method thereof | |
| CN103757531A (en) | Thin strip continuous casting economic high-strength binding strip with tensile strength of at least 1000 MPa and manufacturing method thereof | |
| CN111349870A (en) | Q345D steel plate and production method thereof | |
| JP2007231352A (en) | Precipitation hardening high strength steel sheet and its production method |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20130821 |
|
| CF01 | Termination of patent right due to non-payment of annual fee |