CN102618802B - Ultrafine grained dual-phase steel material and production method thereof - Google Patents
Ultrafine grained dual-phase steel material and production method thereof Download PDFInfo
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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 purposes the most a kind of material 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%, though having gone beyond Korea S and Japan in quantity, China becomes the first in the world shipbuilding big country, but be not first shipbuilding power, this mainly is because be subjected to the restriction of high-performance steel iron material.Seaplane carrier is compared the singularity that has 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 etc.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 high strength 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, 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, 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 refer to that soft steel or low-carbon micro steel-alloy obtain through critical zone thermal treatment or cooling controlling and rolling controlling process mainly by high-strength steel that ferrite+a spot of martensite is formed, to have continuous surrender, yield tensile ratio is low, work hardening rate is higher with characteristics such as elongation are 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, save man-hour and the energy, be convenient to scale operation, become the prefered method of producing dual phase steel, rising along with 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 of tissue that can make steel hardening, enhancing, on engineering is used, for strengthening material is usually directed to martensite strengthening mechanism, simultaneously, in using, engineering adopts 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 concerned by famous Hall-Petch (
) describe, people have observed the yield strength of most of metallic substance and hardness value with the trend that reduces to show increase of 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 sub-micron grain (Submicron grains) tissue is defined as: the size of crystal grain on all directions is all less than 1 μ m, (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 main method of toughness 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 by traditional viscous deformation processing and annealing process subsequently, take place namely that recrystallize and grain growth obtain, the grain-size of the material that this common process is prepared is about 10 μ m, and the yield strength s that common coarse crystal steel (grain-size is about 100 μ m) at room temperature stretches
yOnly be 90 MPa, ultra-fine grain micro-alloy steel (Fe-0.8C, grain-size is about 6 μ m) at room temperature stretches, its yield strength s
yBe about 310 MPa(Bramfitt B.L., Marder A.R., Metallurgical and Petroleum Engineers, 191-198,1973); Commercial is 370 MPa with the stainless yield strength of 304L, tensile strength 900 MPa, 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); People such as Taiwan scientist Lee are with commerce 304L stainless steel (Eastern steel, Spring House, PA) by rolling deformation 15%, its yield strength rises to 370 MPa, tensile strength 900 MPa, the stretching elongation is 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, tensile strength and the yield strength of the material that obtains are all lower; People (Chen A.Y. such as Lu professor Jian of City University of Hong Kong, Ruan H.H., Wang J., Chan H.L., 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 yield strength 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 adopts only several centimetres of its processing method treatable length of material, 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 yield strength at the prior art existence, the invention provides a kind of superfine crystal particle dual phase steel material and preparation method thereof, purpose is by reasonable component design and technology controlling and process, make and have a large amount of martensitic stuctures and submicron-grade superfine crystal grain in the prepared hot-rolled steel material, the twin lamellae structure that has nanoscale simultaneously, several 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, P＜0.02%, S＜0.04%, surplus is the Fe element, and its microtexture is made up of the superfine crystal particle of orientation stochastic distribution, and the diameter of crystal grain is 500～2000nm, its microtexture is by austenite and martensite two phase composites, yield strength 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 partial martensite tissue only is 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; alloy material is smelted in vacuum induction furnace; in stove, feed rare gas element Ar as shielding gas; smelting molten steel is cast into steel ingot; and be 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%; the subordinate phase hot-rolled temperature is 820～950 ℃; 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 is between 50～80 ℃/s; water-cooled is to room temperature after being cooled to 650 ℃; adopt two-roller mill that steel plate is carried out cold-rolling treatment then, deformation range is 50%～75%, after cold rolling the finishing 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 by stacking fault energy to carry out the composition design, determine 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, this stacking fault energy is conducive to make institute's molten alloy that martensitic transformation takes place under suitable processing conditions and machinery is twin, thereby form martensitic stucture and the twins sub-structure of a large amount of nanoscales, metal is strengthened, simultaneously, the steel grade of this alloying constituent is similar to 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 martensite lamella and the twins sub-structure of a large amount of nanometer scale, has the extremely strong big ability of absorption dislocation in this class formation, 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 in conjunction with continuous annealing and fast cooling technology, prepare by rational technological process and processing parameter and to have two-phase, it is 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 high-strength 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 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 drawings and Examples the present invention is further described.
Embodiment 1
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; alloy material is smelted 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; the fs hot-rolled temperature is 1050 ℃; be austenite recrystallization temperature; the subordinate phase hot-rolled temperature is 820 ℃; be austenite non-recrystallization temperature; two stage relative reduction is respectively 35% and 15%; be 8 mm through 6 passage thicknesss of slab; after the finish to gauge; steel plate carries out chilling through the ultrafast cool equipment of milling train exit configuration immediately; speed is 50 ℃/s; be cooled to 650 ℃; insulation half an hour, water-cooled is to room temperature, and it is cold rolling that the gained steel plate is carried out multi-pass; carry out anneal after each cold rolling; 450 ℃ of annealing temperatures, soaking time 10 min descend a time cold rolling then; cold rolling total reduction is 75%; after cold rolling the finishing 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, it is austenite+martensitic structure feature, grain-size is 800 nm, and simultaneously, this material has the twin lamellae structure of nanoscale, 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 yield strength of room temperature, and tensile strength is 1850 MPa, extensibility is 10%, as shown in Figure 3.
Chemical analysis results shows that the chemical composition content of preparation attitude micro-crystal plate of moderate thickness steel sample is as shown in table 1:
The superfine crystal particle dual phase steel chemical constitution of table 1 embodiment 1
Scanning electronic microscope 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, there are a large amount of twin lamellae structures and nanocrystal bunch, as shown in Figure 1, wherein light tone is represented martensitic stucture, dark-coloured expression austenite structure, as can be seen from the figure, there is its volume fraction of a large amount of martensitic phases about 57% in the microtexture, the crystal grain of submicron order, nanometer scale twin crystal (TBs) and ε-martensite lamella (ε).
Embodiment 2
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; alloy material is smelted 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; the fs hot-rolled temperature is 1150 ℃; be austenite recrystallization temperature; the subordinate phase hot-rolled temperature is 950 ℃; be austenite non-recrystallization temperature; two stage relative reduction is respectively 35% and 15%; be 8 mm through 6 passage thicknesss of slab; after the finish to gauge; steel plate carries out chilling through the ultrafast cool equipment of milling train exit configuration immediately; speed is 80 ℃/s; be cooled to 650 ℃; insulation half an hour, water-cooled is to room temperature, and it is cold rolling that the gained steel plate is carried out multi-pass; carry out anneal after each cold rolling; 450 ℃ of annealing temperatures, soaking time 10 min descend a time cold rolling then; cold rolling total reduction is 50%; after cold rolling the finishing 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 as shown in Figure 2, observation shows: have a large amount of martensitic phases in the microtexture, its volume 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 yield strength of room temperature, tensile strength is 1580 MPa, and extensibility is 16%, 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 of moderate thickness steel sample is as shown in table 2:
The superfine crystal particle dual phase steel chemical constitution of table 2 embodiment 2
Embodiment 3
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; alloy material is smelted 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; the fs hot-rolled temperature is 1100 ℃; be austenite recrystallization temperature; the subordinate phase hot-rolled temperature is 900 ℃; be austenite non-recrystallization temperature; two stage relative reduction is respectively 35% and 15%; be 8 mm through 6 passage thicknesss of slab; after the finish to gauge; steel plate carries out chilling through the ultrafast cool equipment of milling train exit configuration immediately; speed is 80 ℃/s; be cooled to 650 ℃; insulation half an hour, water-cooled is to room temperature, and it is cold rolling that the gained steel plate is carried out 2 passages; carry out anneal after each cold rolling; 450 ℃ of annealing temperatures, soaking time 10 min descend a time cold rolling then; cold rolling total reduction is 60%; after cold rolling the finishing 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 yield strength of room temperature, and tensile strength is 1200 MPa, extensibility is 20 %, 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 of moderate thickness 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. superfine crystal particle dual phase steel material, it 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, (0.060～0.090) %Mo, P＜0.02%, S＜0.04%, surplus is the Fe element, and its microtexture is made up of the superfine crystal particle of orientation stochastic distribution, and the diameter of crystal grain is 500～2000nm, its microtexture is by austenite and martensite two phase composites, yield strength 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; it 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; alloy material is smelted in vacuum induction furnace; in stove, feed rare gas element Ar as shielding gas; smelting molten steel is cast into steel ingot; and be 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 35%; the subordinate phase hot-rolled temperature is 820～950 ℃; 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 is between 50～80 ℃/s; water-cooled is to room temperature after being cooled to 650 ℃; adopt two-roller mill that steel plate is carried out cold-rolling treatment then; deformation range is 50%～75%; after cold rolling the finishing this sheet material is placed in the resistance furnace in 450-650 ℃ of insulation 5min; water-cooled obtains superfine crystal particle dual phase steel steel plate to room temperature then.
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| 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 |
| 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 |
| CN112210728B (en) * | 2020-09-29 | 2022-03-18 | 中国科学院金属研究所 | Ultrahigh-strength nanocrystalline 3Cr9W2MoSi die steel and preparation method thereof |
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| 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 |
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| 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 |
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