CN110042311A - A kind of preparation method of the high boron austenitic stainless steel thin plate of high-plasticity - Google Patents

A kind of preparation method of the high boron austenitic stainless steel thin plate of high-plasticity Download PDF

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CN110042311A
CN110042311A CN201910460658.3A CN201910460658A CN110042311A CN 110042311 A CN110042311 A CN 110042311A CN 201910460658 A CN201910460658 A CN 201910460658A CN 110042311 A CN110042311 A CN 110042311A
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stainless steel
plasticity
thin plate
austenitic stainless
high boron
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CN110042311B (en
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刘海涛
王昭杰
刘光军
李永旺
王国栋
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Northeastern University China
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
    • B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
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    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • C21D8/0215—Rapid solidification; Thin strip casting
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite

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Abstract

A kind of preparation method of the high boron austenitic stainless steel thin plate of high-plasticity, (1) is sequentially included the following steps: by set component smelting molten steel, ingredient 1.5~2.5% B by mass percentage, Ti 0.5~1.5%, C < 0.01%, Cr 16.0~19.0%, Ni 14.0~16.0%, Mn 1.0~2.0%, Si 0.2~2.0%, remaining is Fe；(2) pouring molten steel controls liquid steel temperature in tundish and meets 10 DEG C < T-T into tundish0<50℃；(3) it solidifies and exports between the roll gap that molten steel passes through conticaster through tundish, obtain Cast Strip；(4) a time hot rolling is carried out, acquisition hot rolled plate is batched in cooling；(5) smooth processing after making annealing treatment.Method of the invention finally obtains the high boron stainless sheet steel of high-plasticity；And production procedure is compact, manufacturing process is few, can significantly reduce production cost.

Description

A kind of preparation method of the high boron austenitic stainless steel thin plate of high-plasticity
Technical field
The invention belongs to metallurgical material technical field, in particular to a kind of high boron austenitic stainless steel thin plate of high-plasticity Preparation method.
Background technique
Now with the development of China's nuclear industry, core spentnuclear fuel increasing number that nuclear reactor is drawn off；Since spentnuclear fuel has There is strong radioactivity, seriously endangers ambient enviroment and human health, must be made using thermal neutron absorbing material in nuclear industry The transport of standby spentnuclear fuel and storage container；The Service Environment of spentnuclear fuel storage and transportation thermal neutron absorbing material is severe in nuclear power field, Therefore the requirement to its performance is also extremely harsh；For the thermal neutron absorbing material of spent fuel transport container, it had been on active service It may be subjected to higher temperature and biggish impact failure in journey, therefore require it that there should be excellent mechanical property；For storage The thermal neutron absorbing material of spentnuclear fuel is deposited, long period of soaking need to have in boracic aqueous solution and bear larger irradiation dose Ability and stronger corrosion resistance；High boron stainless steel is a kind of austenitic stainless steel of boracic, has superior absorbent thermal neutron And the gamma-ray function of shielding, and there are the characteristics such as high, the corrosion-resistant, Flouride-resistani acid phesphatase of intensity, relatively broadly applied to spentnuclear fuel The preparation of storage and transportation material is the indispensable critical function material in nuclear industry field.
Boron content in high boron stainless steel is generally higher than 0.1%, has good neutron absorption effect, and its thermal neutron Absorbability enhances with the increase of boron content；However, solid solubility of the boron element in austenite stainless steel matrix is very low, only It is 0.018~0.026%；When conventional die casting process prepares high boron stainless steel, excessive boron element can in solidification relatively crystal boundary, A large amount of coarse, (Cr, Fe) in net distribution is precipitated2The firmly crisp boride of B, isolates austenitic matrix, severe exacerbation high boron steel Mechanical property and corrosion resisting property；In subsequent thermal processing deformation process, high boron stainless steel work-piece is easy to happen side and splits；Net distribution Hard crisp boride precipitated phase lead to production board intensity with higher, but temperature-room type plasticity, toughness are poor, support during being on active service Resistance to deformation and the ability of destruction are poor；Therefore, the low plasticity and toughness problem of high-boron stainless steel plate limits it and stores and transports in spentnuclear fuel and holds The development in the nuclear industry such as device field.
Powder metallurgic method is to prepare the main method of high-boron stainless steel plate at present, and technique mainly uses argon gas to protect gas Mist legal system carries out sinter molding after taking high boron powder of stainless steel, carries out the process flow of the subsequent preparation such as hot/cold processing again later； But current powder metallurgic method generally uses hip treatment technique to be sintered, this will make entire process flow Period is longer, and preparation cost is more high, it is difficult to realize mass production.
In recent years, there is scholar to propose that titanium elements are added in high boron steel, utilize high temperature precipitated phase TiB2Heterogeneous forming core make For improving (Cr, Fe)2The size and distribution of B boride；Xi'an Communications University accords with pallid light et al. in paper (DOI:10.1016/ J.msea.2007.02.032 influence of the titanium elements to high boron steel tissue and performance is had studied in), discovery is containing 1.5~2.5%B After 0.2~0.5%Ti is added in high boron steel, high temperature precipitated phase TiB is organized2Having a size of 5~10 μm, continuously distributed is netted (Cr,Fe)2B boride portion fractures, still (Cr, Fe)2B boride does not obviously refine, and is mostly 15~25 μm；Mechanical property High boron steel room temperature elongation percentage increases to 1.82% by 1.04% after energy detection discovery addition titanium elements, does not significantly improve；In addition, Northeastern University Li Yongwang et al. has studied in paper (DOI:10.1007/s12598-019-01247-w) containing 2.1%B high boron The changing rule organized after 2.0%Ti is added in steel, finds TiB in tissue2Having a size of 5~15 μm, (Cr, Fe)2B boride point Cloth more disperse, still (Cr, Fe)2B boride size is still greater than 15 μm, and boride is also without obvious refinement；Analysis is former Cause is found in high boron steel conventional die castings technique, after titanium elements are added, the first precipitated phase TiB in molten steel2Since density is lower, Molten steel surface largely is floated on, (Cr, Fe) can not be used as2The heterogeneous forming core core of B boride；In addition, TiB in process of setting2Understood Degree is grown up, and final size reaches 5~15 μm, is had exceeded as (Cr, Fe)2The critical dimension of the heterogeneous forming core core of B boride；Cause This, TiB in the stainless structure of steel of high boron of conventional die castings technique preparation2(Cr, Fe)2B boride is more coarse, and thin plate modeling is tough Property is very poor.
Summary of the invention
The above problem existing for structure property feature and technology of preparing for existing high boron steel plate, the present invention provide one kind The preparation method of the high boron austenitic stainless steel thin plate of high-plasticity is obtained thin by improving technique in high boron stainless sheet steel Small, disperse boride particle, to improve the room-temperature mechanical property and neutron shield performance of high boron stainless sheet steel.
Method of the invention sequentially includes the following steps:
1, high boron stainless molten steel is smelted by set component, ingredient contains B 1.5~2.5%, Ti by mass percentage 0.5~1.5%, C < 0.01%, Cr 16.0~19.0%, Ni 14.0~16.0%, Mn 1.0~2.0%, Si 0.2~ 2.0%, remaining is Fe and inevitable impurity, and Nieq > (1.1Creq-7.0), wherein Nieq=%Ni+30 × %C+ 0.5 × %Mn, Creq=%Cr+1.5 × %Si；
2, for pouring molten steel into tundish, controlling liquid steel temperature in tundish is T, and meets 10 DEG C < T-T0<50℃；Its In, T0For TiB2Precipitation Temperature, calculation method T0=227.5 × %B+208.5 × %Ti+1088.3, unit are DEG C；
3, molten steel is flowed into through tundish and is made of the water cooling crystallization roll and side seal board of two reverse rotations of double-roller continuous casting machine Cavity in, form molten bath, molten steel solidifies and export between the roll gap of two crystallization rolls, obtains the casting with a thickness of 2.0~5.0mm Band；
4, Cast Strip hot rolling machine is subjected to a time hot rolling that reduction ratio is 20~50%, is cooled to after hot rolling and batches temperature Degree, then acquisition hot rolled plate is batched, wherein start rolling temperature when hot rolling is 1000~1150 DEG C, and finishing temperature is 850~950 DEG C；
5, will be made annealing treatment after hot rolled plate uncoiling, annealing temperature be 1000~1100 DEG C, soaking time be 5~ 60min after the flattened processing of annealed sheet, obtains the high boron austenitic stainless steel thin plate of high-plasticity.
In the above method, 0.1~2.0m/s of hot rolling rate.
In the above method, 600~700 DEG C of coiling temperature.
In the above method, 1.0~4.0mm of hot rolling plate thickness.
It in the above method, is carried out using cooling system when hot roller repairing, the average cooling rate of hot rolled plate is 10~20 ℃/s。
In the above method, the reduction ratio of smooth processing is 0.5~1.2%.
In the high boron austenitic stainless steel thin plate of above-mentioned high-plasticity, TiB2Be precipitated mainly is in submicron particles shape, ruler It is very little in 100~400nm；(Cr,Fe)2B boride is mainly in the spherical of micron-sized aspherical particle shape and submicron order, and grain Boride area accounting 80% or more of the diameter less than 1.5 μm, partial size are greater than 2.5 μm of boride area accounting≤5%.
600~750MPa of tensile strength of the high boron austenitic stainless steel thin plate of above-mentioned high-plasticity, room temperature elongation percentage 14.0~16.5%.
When the high boron austenitic stainless steel thin plate thickness >=2.5mm of above-mentioned high-plasticity, 270~300KJ/ of impact flexibility m2。
Compared with conventional die castings technique, present invention process setting rate is fast, effectively inhibits boron element in process of setting Segregation degree, significantly refinement TiB2Particle makes it be distributed more disperse, to (Cr, Fe)2The heterogeneous forming core effect of B boride is aobvious It writes；In addition, strict control pouring molten steel temperature in present invention process, so that liquid steel temperature (T) and TiB in tundish2Temperature is precipitated Spend (T0=227.5 × %B+208.5 × %Ti+1088.3) difference is accurately controlled in 10~50 DEG C, to solve TiB2Due to Density is low and the problem of floating on molten steel surface, while in turn ensuring TiB2It is precipitated in time in process of setting, as (Cr, Fe)2B The heterogeneous forming core core of boride, therefore the boride in the solidified structure of high boron stainless steel Cast Strip is mainly in small and dispersed particle Shape distribution, for average grain diameter less than 2.5 μm, matrix is uniform and stable austenite structure；Pass through the hot rolling after control continuous casting Temperature, hot rolling drafts, obtain that shape is smooth, the boundless high boron stainless steel hot-rolling plate split；After annealed processing and smooth processing, Finally obtain the high boron stainless sheet steel of high-plasticity；In addition, present invention process production procedure is compact, manufacturing process is few, it can Significantly reduce production cost.
Compared with existing high-boron stainless steel plate, high boron stainless sheet steel provided by the present invention is realized to boride Imperceptibility and dispersion completely controls: TiB in finished sheet2Being precipitated mainly is in submicron particles shape, and particle size exists Within the scope of 100-400nm；(Cr,Fe)2B boride is mainly in the spherical of micron-sized aspherical particle shape and submicron order, and Boride of the partial size less than 1.5 μm accounts for 80% or more, and boride of the partial size greater than 2.5 μm is not more than 5%；The boronation of small and dispersed Object can play the deterioration of the dispersion-strengthened action of second phase particles and the temperature-room type plasticity of production board and toughness.Finally The tensile strength of production board is 600~750MPa, and room temperature elongation percentage is 14.0~16.5%, moreover, for thickness >=2.5mm Thin plate, impact flexibility are 270~300KJ/m2。
In the present invention, to guarantee that the matrix of high boron stainless sheet steel is stable austenite structure, high boron is stainless The chemical component of steel should meet Nieq > 1.1Creq-7.0, wherein Nieq=%Ni+30 × %C+0.5 × %Mn, Creq =%Cr+1.5 × %Si, wherein Mn content, which should be controlled, should control in 1.0~2.0%, Si content 0.2~2.0%；To solve TiB2Due to density is low and the problem of float on molten steel surface, control 10 DEG C < T-T of molten steel temperature in tundish0<50℃；In order to further Boride in high boron stainless steel is refined, its more uniform, disperse of distribution is made, one that reduction ratio is 20~50% is carried out to Cast Strip Secondary hot rolling, to guarantee that the hot-workability start rolling temperature of thin plate should be controlled at 1000~1150 DEG C, finishing temperature should control 850~ 950 DEG C, roll 0.1~2.0m/s of rate；In order to guarantee smoothly batching for high boron stainless sheet steel, oiler temperature control is 600 ~700 DEG C；The residual stress in austenite structure in order to eliminate high boron stainless steel base, the high boron Thin Stainless Steel after batching Plate is made annealing treatment, and annealing temperature is 1000~1100 DEG C, and soaking time is 5~60min；In order to guarantee high boron Thin Stainless Steel Thin plate after annealing is carried out the smooth processing that reduction ratio is 0.5~1.2% by plate template.
Detailed description of the invention
Fig. 1 is the process signal that hot rolled plate is prepared in high boron stainless sheet steel of high-plasticity of the invention and preparation method thereof Figure；In figure, 1, ladle, 2, tundish, 3, dual-roller thin-band conticaster crystallization roll, 4, molten bath, 5, Cast Strip, 6, hot-rolling mill, 7, cooling System, 8, coiling machine；
Fig. 2 is TiB in the Cast Strip of the embodiment of the present invention 12It is precipitated and (Cr, Fe)2B boride shape appearance figure and Cr, Fe, Mn, Ni With Ti distribution diagram of element；
The microscopic appearance figure of the Cast Strip of Fig. 3 embodiment of the present invention 1 and the high boron austenitic stainless steel thin plate of high-plasticity；Its In, left figure is Cast Strip, and right figure is the high boron austenitic stainless steel thin plate of high-plasticity；
The Cast Strip of Fig. 4 comparative example 1 of the present invention and the microscopic appearance figure of production board；Wherein, left figure is Cast Strip, and right figure is finished product Plate；
The stress strain curve figure of the high boron austenitic stainless steel thin plate of the high-plasticity of Fig. 5 inventive embodiments 1；
The stress strain curve figure of the production board of Fig. 6 comparative example 1 of the present invention.
Specific embodiment
The process that the present invention prepares hot rolled plate is as shown in Figure 1.
TiB is observed in the embodiment of the present invention2It is Tecnai G that the equipment that pattern uses, which is precipitated,2F20 type transmission electron microscopy Mirror, the equipment that observation microscopic structure uses is JEOL JXA-8530F type electron probe；Room temperature tensile specimen size and its performance Measuring method is to be dependent on GB/T228-2002, and used equipment is Instron4206-006 tensile testing machine；Room temperature Charpy V mouthfuls of impact specimen sizes and its performance measurement method are to be dependent on GB-T229-2007, and used equipment is ZBC2452-B pendulum Hammer shock machine.
%Ni, %C, %Mn, %Cr and %Si of the invention is respectively the mass percent of Ni, C, Mn, Cr and Si.
Annealing is carried out in the embodiment of the present invention to be carried out under the conditions of argon atmosphere.
Below with reference to embodiment, the present invention is described in further detail, embodiments of the present invention are not limited thereto.
Embodiment 1
High boron stainless molten steel is smelted by set component, ingredient contains B 2.1%, Ti 1.3%, C by mass percentage 0.004%, Cr 17.1%, Ni 15.8%, Mn 1.0%, Si 0.9%, remaining is Fe and inevitable impurity, Nieq > (1.1Creq-7.0), wherein Nieq=15.8+30 × 0.004+0.5 × 1.0=17.5, Creq=17.1+1.5 × 0.9= 18.45；17.5 > 20.295-7；
Pouring molten steel controls in tundish T=1850 DEG C of liquid steel temperature into tundish, and meets 10 DEG C < T-T0<50 ℃；Wherein, T0For TiB2Precipitation Temperature, calculation method T0=227.5 × 2.1+208.5 × 1.3+1088.3=477.75+ 271.05+1088.3=1837.1 DEG C；
Molten steel is made of through tundish inflow the two water cooling crystallization rolls reversely rotated and side seal board of double-roller continuous casting machine In cavity, molten bath is formed, molten steel is solidified and exported between the roll gap of two crystallization rolls, obtains the Cast Strip with a thickness of 4.0mm；It is microcosmic Tissue is as shown in Fig. 3 left figure；TiB2It is precipitated and (Cr, Fe)2B boride pattern and Cr, Fe, Mn, Ni and Ti Elemental redistribution such as Fig. 2 It is shown；
Cast Strip hot rolling machine is subjected to a time hot rolling that reduction ratio is 45%, hot rolling rate 2.0m/s, start rolling temperature is 1050 DEG C, finishing temperature is 870 DEG C；It carries out being cooled to 700 DEG C of coiling temperature using cooling system after hot rolling, average cooling rate For 10 DEG C/s, then batch acquisition hot rolled plate；
It will be made annealing treatment after hot rolled plate uncoiling, annealing temperature is 1100 DEG C, soaking time 30min, annealed sheet Flattened processing, the reduction ratio of smooth processing are 0.8%, obtain the high boron austenitic stainless steel thin plate of high-plasticity, thickness 2.16mm；
The TiB of the high boron austenitic stainless steel thin plate of high-plasticity2Being precipitated mainly is in submicron particles shape, and size is 100 ~300nm；(Cr,Fe)2B boride is mainly in the spherical of micron-sized aspherical particle shape and submicron order, and partial size is less than 1.5 μm of boride area accounting 89.2%, partial size are greater than 2.5 μm of boride area accounting 2.0%；
The tensile strength 652MPa of the high boron austenitic stainless steel thin plate of high-plasticity, room temperature elongation percentage 16.1% impact tough Property 293KJ/m2, microstructure is as shown in Fig. 3 right figure；Stress strain curve is as shown in Figure 5.
Embodiment 2
With embodiment 1, difference is method:
(1) molten steel composition contains B 2.5%, Ti 0.7%, C 0.003%, Cr 16.9%, Ni by mass percentage 15.1%, Mn 1.7%, Si 0.8%, remaining is Fe and inevitable impurity, wherein Nieq=15.1+30 × 0.003+0.5 × 1.7=16.04, Creq=16.9+1.5 × 0.8=18.1；Nieq > (1.1Creq-7.0)；
(2) liquid steel temperature T=1823 DEG C is controlled in tundish, T0=227.5 × 2.5+208.5 × 0.7+1088.3= 568.75+145.95+1088.3=1803 DEG C；
(3) Cast Strip thickness 2.4mm；
(4) hot rolling reduction ratio 41%, hot rolling rate 1.8m/s, 1100 DEG C of start rolling temperature, 920 DEG C of finishing temperature；Batch temperature 650 DEG C of degree, average cooling rate are 15 DEG C/s；
(5) 1000 DEG C of annealing temperature, soaking time 45min, the reduction ratio 1.0% of smooth processing；
The thickness 1.4mm of the high boron austenitic stainless steel thin plate of high-plasticity；TiB2Being precipitated mainly is in submicron particles shape, Size is in 100~400nm；(Cr,Fe)2B boride is mainly in the spherical of micron-sized aspherical particle shape and submicron order, and Boride area accounting 85.6% of the partial size less than 1.5 μm, partial size are greater than 2.5 μm of boride area accounting 3.5%；
The tensile strength 670MPa of the high boron austenitic stainless steel thin plate of high-plasticity, room temperature elongation percentage 15.1% impact tough Property 281KJ/m2。
Embodiment 3
With embodiment 1, difference is method:
(1) molten steel composition contains B 1.9%, Ti 0.5%, C 0.006%, Cr 18.1%, Ni by mass percentage 16.0%, Mn 1.8%, Si 1.2%, remaining be Fe and inevitable impurity, wherein Nieq=16+30 × 0.006+0.5 × 1.8=17.08 Creq=18.1+1.5 × 1.2=19.9；Nieq > (1.1Creq-7.0)；
(2) liquid steel temperature T=1654 DEG C is controlled in tundish, wherein T0=227.5 × 1.9+208.5 × 0.5+1088.3 =432.25+104.25+1088.3=1624.8 DEG C；
(3) Cast Strip thickness 3.2mm；
(4) hot rolling reduction ratio 25%, hot rolling rate 0.5m/s, 1150 DEG C of start rolling temperature, 950 DEG C of finishing temperature；Batch temperature 650 DEG C of degree, average cooling rate are 15 DEG C/s；
(5) 11100 DEG C of annealing temperature, soaking time 15min, the reduction ratio 0.7% of smooth processing；
The thickness 2.3mm of the high boron austenitic stainless steel thin plate of high-plasticity；TiB2Being precipitated mainly is in submicron particles shape, Size is in 100~400nm；(Cr,Fe)2B boride is mainly in the spherical of micron-sized aspherical particle shape and submicron order, and Boride area accounting 81.2% of the partial size less than 1.5 μm, partial size are greater than 2.5 μm of boride area accounting 4.6%；
The tensile strength 732MPa of the high boron austenitic stainless steel thin plate of high-plasticity, room temperature elongation percentage 14.3% impact tough Property 278KJ/m2。
Embodiment 4
With embodiment 1, difference is method:
(1) molten steel composition contains B 2.4%, Ti 0.9%, C 0.007%, Cr 16.1%, Ni by mass percentage 14.8%, Mn 2.0%, Si 0.5%, remaining is Fe and inevitable impurity, wherein Nieq=14.8+30 × 0.007+0.5 × 2=16.01, Creq=16.1r+1.5 × 0.5=16.85；Nieq > (1.1Creq-7.0)；
(2) liquid steel temperature T=1835 DEG C is controlled in tundish, wherein T0=227.5 × 2.4+208.5 × 0.9+1088.3 =546+187.65+1088.3=1821.95 DEG C；
(3) Cast Strip thickness 2.8mm；
(4) hot rolling reduction ratio 20%, hot rolling rate 0.9m/s, 1000 DEG C of start rolling temperature, 850 DEG C of finishing temperature；Batch temperature 600 DEG C of degree, average cooling rate are 20 DEG C/s；
(5) 1080 DEG C of annealing temperature, soaking time 30min, the reduction ratio 1.2% of smooth processing；
The thickness 2.3mm of the high boron austenitic stainless steel thin plate of high-plasticity；TiB2Being precipitated mainly is in submicron particles shape, Size is in 100~400nm；(Cr,Fe)2B boride is mainly in the spherical of micron-sized aspherical particle shape and submicron order, and Boride area accounting 83.6% of the partial size less than 1.5 μm, partial size are greater than 2.5 μm of boride area accounting 4.1%；
The tensile strength 705MPa of the high boron austenitic stainless steel thin plate of high-plasticity, room temperature elongation percentage 14.8% impact tough Property 273KJ/m2。
Comparative example 1
With embodiment 1, difference is method:
Molten steel composition is Cr 17.2%, C 0.004%, Ni 15.6%, Mn 1.8%, B 2.5% by mass percentage, Si 0.8%, remaining is Fe and inevitable impurity element, and molten steel temperature in tundish is 1670 DEG C；
Due to being not added with Ti element, there are the boronations of net distribution in the solidified structure of obtained high boron stainless steel Cast Strip Object, the average grain diameter of boride are 8.3 μm；After hot rolling, annealing, boride of the partial size less than 1.5 μm only accounts for total amount 35.2%, partial size accounts for sum-rate greater than 2.5 μm of boride and reaches 61.1%, microstructure such as Fig. 4 of Cast Strip and production board It is shown；The room temperature elongation percentage of production board is only 7.9%, impact flexibility 153KJ/m2, production board stress strain curve is as shown in Figure 6.
Comparative example 2
With embodiment 2, difference is method:
60 × 60 × 80mm ingot casting is obtained using conventional die castings technique, since cooling velocity is slower, ingot casting occurs apparent Coagulation defect, and TiB in tissue2For rodlike distribution, having a size of 5-15 μm, (Cr, Fe)2B boride is distributed in lath-shaped, size It is much in 15 μm；
It is 50% cogging hot rolling that ingot casting hot rolling machine, which carries out overall reduction, then hot rolling rate 0.3m/s is carried out under stagnation pressure The six passage hot rollings that amount is 90%, hot rolling rate are 0.12m/s, are finally batched, are obtained with a thickness of 3.1mm at 685 DEG C High boron stainless steel hot-rolling coiled sheet；Since boride is coarse in ingot structure, severe edge fracture occurs for when high boron stainless steel hot-rolling；At It is in lath-shaped and rodlike that product board group, which knits middle boride mainly, and room temperature elongation percentage is only 5.7%, and impact flexibility is only 107KJ/ m2。
Comparative example 3
With embodiment 3, difference is method:
Liquid steel temperature T is 1500 DEG C in tundish, TiB2Precipitation Temperature T0It is 1624.8 DEG C, is unsatisfactory for 10 DEG C < T-T0<50 ℃.TiB in the tissue of Cast Strip2For graininess distribution, average grain diameter is about 400nm, and (Cr, Fe)2B boride is in rodlike and blocky Distribution, size is mostly between 5-10 μm；Since molten steel temperature in tundish is too low, lead to TiB2It is precipitated and floats in advance in tundish On molten steel surface, TiB is reduced2To (Cr, Fe)2The heterogeneous forming core of B boride acts on, therefore (Cr, Fe)2B boride is distributed more Scattered property is obviously deteriorated, and size becomes coarseer；After hot rolling annealing, the room temperature elongation percentage of production board is only 10.8%, Impact flexibility is only 203KJ/m2。
Comparative example 4
With embodiment 4, difference is method:
Cast Strip hot rolling machine carries out a time hot rolling that drafts is 12.2%, and hot rolling rate is 0.3m/s, then 690 DEG C when batched, obtain the high boron stainless steel hot-rolling coiled sheet with a thickness of 2.45mm；Since drafts is smaller, high boron stainless steel hot Roll that plate shape is smooth, boundless splits；30min is kept the temperature at 1100 DEG C to the high boron stainless steel after batching, finally obtained high boron is not Become rusty steel production board；Since its hot rolling drafts is smaller, boride fails sufficiently to be crushed, and boride of the partial size less than 1.5 μm is only The 58.2% of total amount is accounted for, the boride of center portion is mainly in rodlike and blocky；The room temperature elongation percentage of production board is only 10.8%, impact Toughness is only 203KJ/m2。

Claims (8)

1. a kind of preparation method of the high boron austenitic stainless steel thin plate of high-plasticity, it is characterised in that sequentially include the following steps:
(1) high boron stainless molten steel is smelted by set component, ingredient contains B 1.5~2.5% by mass percentage, Ti 0.5~ 1.5%, C < 0.01%, Cr 16.0~19.0%, Ni 14.0~16.0%, Mn 1.0~2.0%, Si 0.2~2.0%, Remaining is Fe and inevitable impurity, and Nieq > (1.1Creq-7.0), wherein Nieq=%Ni+30 × %C+0.5 × %Mn, Creq=%Cr+1.5 × %Si；
(2) for pouring molten steel into tundish, controlling liquid steel temperature in tundish is T, and meets 10 DEG C < T-T0<50℃；Wherein, T0 For TiB2Precipitation Temperature, calculation method T0=227.5 × %B+208.5 × %Ti+1088.3, unit are DEG C；
(3) molten steel flows into the sky being made of the water cooling crystallization roll and side seal board of two reverse rotations of double-roller continuous casting machine through tundish It is intracavitary, molten bath is formed, molten steel is solidified and exported between the roll gap of two crystallization rolls, obtains the Cast Strip with a thickness of 2.0~5.0mm；
(4) Cast Strip hot rolling machine is subjected to a time hot rolling that reduction ratio is 20~50%, coiling temperature is cooled to after hot rolling, then Acquisition hot rolled plate is batched, wherein start rolling temperature when hot rolling is 1000~1150 DEG C, and finishing temperature is 850~950 DEG C；
(5) it being made annealing treatment after hot rolled plate uncoiling, annealing temperature is 1000~1100 DEG C, and soaking time is 5~60min, After the flattened processing of annealed sheet, the high boron austenitic stainless steel thin plate of high-plasticity is obtained.
2. a kind of preparation method of the high boron austenitic stainless steel thin plate of high-plasticity according to claim 1, feature exist In step (4), 0.1~2.0m/s of hot rolling rate.
3. a kind of preparation method of the high boron austenitic stainless steel thin plate of high-plasticity according to claim 1, feature exist In step (4), 600~700 DEG C of coiling temperature.
4. a kind of preparation method of the high boron austenitic stainless steel thin plate of high-plasticity according to claim 1, feature exist It is carried out when hot roller repairing using cooling system, the average cooling rate of hot rolled plate is 10~20 DEG C/s.
5. a kind of preparation method of the high boron austenitic stainless steel thin plate of high-plasticity according to claim 1, feature exist In step (5), the reduction ratio of smooth processing is 0.5~1.2%.
6. a kind of preparation method of the high boron austenitic stainless steel thin plate of high-plasticity according to claim 1, feature exist In the high boron austenitic stainless steel thin plate of high-plasticity, TiB2Being precipitated mainly is in submicron particles shape, and size is 100 ~400nm；(Cr,Fe)2B boride is mainly in the spherical of micron-sized aspherical particle shape and submicron order, and partial size is less than 1.5 μm of 80% or more boride area accounting, partial size are greater than 2.5 μm of boride area accounting≤5%.
7. a kind of preparation method of the high boron austenitic stainless steel thin plate of high-plasticity according to claim 1, feature exist In 600~750MPa of tensile strength of the high boron austenitic stainless steel thin plate of high-plasticity, room temperature elongation percentage 14.0~ 16.5%.
8. a kind of preparation method of the high boron austenitic stainless steel thin plate of high-plasticity according to claim 1, feature exist When the described high-plasticity high boron austenitic stainless steel thin plate thickness >=2.5mm, 270~300KJ/m of impact flexibility2。
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