CN116411156A - High-strength and high-toughness lamellar duplex stainless steel and preparation method thereof - Google Patents
High-strength and high-toughness lamellar duplex stainless steel and preparation method thereof Download PDFInfo
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- 229910001039 duplex stainless steel Inorganic materials 0.000 title claims abstract description 68
- 238000002360 preparation method Methods 0.000 title claims abstract description 19
- 238000001816 cooling Methods 0.000 claims abstract description 39
- 238000000034 method Methods 0.000 claims abstract description 23
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 21
- 239000000956 alloy Substances 0.000 claims abstract description 21
- 229910001220 stainless steel Inorganic materials 0.000 claims abstract description 19
- 239000010935 stainless steel Substances 0.000 claims abstract description 18
- 238000004321 preservation Methods 0.000 claims abstract description 15
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 5
- 238000005097 cold rolling Methods 0.000 claims description 23
- 238000010438 heat treatment Methods 0.000 claims description 22
- 238000003825 pressing Methods 0.000 claims description 12
- 238000005242 forging Methods 0.000 claims description 10
- 239000002105 nanoparticle Substances 0.000 claims description 7
- 239000006104 solid solution Substances 0.000 claims description 7
- 230000009467 reduction Effects 0.000 claims description 6
- 238000004519 manufacturing process Methods 0.000 claims 1
- 229910000885 Dual-phase steel Inorganic materials 0.000 abstract description 31
- 230000032683 aging Effects 0.000 abstract description 7
- 238000005096 rolling process Methods 0.000 abstract description 4
- 238000013001 point bending Methods 0.000 abstract description 3
- 125000004122 cyclic group Chemical group 0.000 abstract description 2
- 238000002474 experimental method Methods 0.000 abstract description 2
- 239000002245 particle Substances 0.000 abstract description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 11
- 229910001566 austenite Inorganic materials 0.000 description 8
- 238000009826 distribution Methods 0.000 description 6
- 230000008569 process Effects 0.000 description 5
- 229910000831 Steel Inorganic materials 0.000 description 4
- 238000006073 displacement reaction Methods 0.000 description 4
- 238000000635 electron micrograph Methods 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 4
- 238000007670 refining Methods 0.000 description 4
- 239000010959 steel Substances 0.000 description 4
- 229910000797 Ultra-high-strength steel Inorganic materials 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- INZDTEICWPZYJM-UHFFFAOYSA-N 1-(chloromethyl)-4-[4-(chloromethyl)phenyl]benzene Chemical compound C1=CC(CCl)=CC=C1C1=CC=C(CCl)C=C1 INZDTEICWPZYJM-UHFFFAOYSA-N 0.000 description 2
- 230000002902 bimodal effect Effects 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 238000005457 optimization Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- 229910000943 NiAl Inorganic materials 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000011651 chromium Substances 0.000 description 1
- 238000005253 cladding Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
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- 230000006872 improvement Effects 0.000 description 1
- 230000016507 interphase Effects 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
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- 238000012986 modification Methods 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/28—Normalising
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/02—Hardening by precipitation
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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Abstract
The invention discloses a high-strength and high-toughness lamellar duplex stainless steel and a preparation method thereof, wherein the lamellar stainless steel in a two-phase region is heated to 1100-1200 ℃ for heat preservation and air cooling for 3h to room temperature, so that alpha phase and gamma phase with high stability are obtained; compared with the traditional method, the strength of the dual-phase steel prepared by the method is improved to about 1200MPa, and meanwhile, the plasticity is kept above 15%. Subsequently, the alloy was cold rolled by 50%, deformed by rolling, then subjected to solution treatment at 1150 ℃, rapidly cooled with water, cooled to room temperature, and then subjected to rolling aging. The strength of the dual-phase steel prepared by the method is improved approximately200MPa to 1300MPa. Meanwhile, the uniform elongation is basically kept unchanged (18%), and a three-point bending cyclic loading experiment shows that the fracture toughness of the nano-grade B2 particle reinforced lamellar dual-phase steel prepared by the method can reach 176MPa m 1/2 。
Description
Technical Field
The invention belongs to the field of metal materials, and relates to high-strength and high-toughness lamellar duplex stainless steel and a preparation method thereof.
Background
At present, ferrite/austenite duplex stainless steel has very wide application fields at home and abroad, such as submarine pipelines, cable-stayed bridges, nuclear power cladding tubes and the like. Through component improvement and process optimization, the duplex stainless steel can keep high hardness, strength and excellent plasticity and toughness, and meanwhile, the corrosion resistance is considered, so that the application range of the duplex stainless steel is greatly widened.
Chinese patent CN103305766B discloses a high-strength high-plasticity ferritic stainless steel and a preparation method thereof, and the high-strength high-plasticity medium-chromium ferrite stainless steel combined by microalloy precipitation strengthening and parent phase transformation strengthening is prepared through the preferential addition of V, N, nb, C, cu and the layer-by-layer optimization of the preparation process. However, the room temperature yield strength is lower and only 250-400 MPa, and can only be applied to places with low requirements on the material strength, so that the application prospect is greatly limited.
Chinese patent CN109790611a discloses an austenitic martensitic dual phase steel having a composition of 8-12 wt.% Mn, 0.3-0.6 wt.% C, 1-4 wt.% Al, 0.4-1 wt.% V and the balance Fe, comprising vanadium carbide precipitates having a size of 10-30 nm. Compared with the traditional dual-phase steel, the TWIP and TRIP effects in the drawing process can greatly improve the strength and the ductility of the dual-phase steel, in addition, the vanadium carbide precipitation can effectively improve the yield strength, but the fracture toughness is not further described and improved, and the 170 MPa-m is difficult to break through 1/2 。
Chinese patent CN113604753A discloses 2600MPa grade ultra-high strength steel which comprises 10-18 wt% of Ni, 4-16 wt% of Co, 3-9 wt% of Mo, 0.5-6 wt% of Al and the balance of Fe, and is mainly characterized in that the ultra-high strength steel is martensitic high strength steel which is uniform in structure, high in density, B2-NiAl and reinforced by nano Mo clusters together, has yield strength of more than 2250MPa and tensile strength of more than 2600MPa, has very wide application prospect on an aircraft landing gear, an engine shell and a high-precision transmission main bearing member, but has poor ductility, engineering strain of less than 0.1%, and limits the application of the ultra-high strength steel to a certain extent in scenes with higher plastic requirements.
Aiming at the problem that the existing ferrite austenite dual-phase steel has higher strength and lower toughness due to the restriction relation of the toughness, the application of the alloy is limited, so that the alloy is necessary to be designed to have higher strength and higher toughness.
Disclosure of Invention
The invention aims to overcome the defects of the existing ferrite austenite duplex steel in the limitation relation of toughness and the preparation method thereof, and provides high-toughness lamellar duplex stainless steel and the preparation method thereof.
The invention is realized by the following technical scheme:
a preparation method of high-strength and high-toughness lamellar duplex stainless steel comprises the following steps:
step 1, heating an as-cast FeNiCrAl alloy to 1100-1200 ℃ for heat preservation, and then performing hot forging and cooling to obtain the layered structure duplex stainless steel;
and 4, heating the duplex stainless steel obtained in the step 3 to 1150 ℃, preserving heat, and cooling to obtain the solid solution state lamellar structure duplex stainless steel.
and 6, heating the duplex stainless steel obtained in the step 5 to 600-700 ℃, preserving heat for a long time, and slowly cooling to obtain the aged lamellar structure duplex stainless steel.
Preferably, the heat preservation time in the step 1 is 3-5 h.
Preferably, the pressing amount of the hot forging in the step 1 is 50%.
Preferably, in step 2, the duplex stainless steel is heated to 750-800 ℃ for normalizing treatment.
Preferably, the cold rolling is performed in step 3 by a reduction of 50%.
Preferably, the heat preservation time in the step 4 is 10min, and the cooling mode is water cooling.
Preferably, the cold rolling in step 5 is performed at a reduction of 50%.
Preferably, the heat preservation time in the step 5 is 2-5 hours, and the cooling mode is air cooling.
A high strength and toughness lamellar duplex stainless steel, which comprises a micron-sized lath-shaped alpha primary phase, a gamma primary phase and a nano-sized spherical intragranular B2 phase.
Compared with the prior art, the invention has the following beneficial technical effects:
the preparation method of the high-strength and high-toughness lamellar duplex stainless steel provided by the invention comprises the steps of quenching the cold-rolled duplex steel at 1100-1200 ℃ and cold-rolling again, dissolving a large number of precipitated phases with larger sizes back into a matrix, thinning two photo layers, and introducing a large number of non-uniform nucleation sites such as dislocation, deformation bands and the like. Subsequently, the rolled sample is subjected to aging treatment at 600-700 ℃ to facilitate annihilation of dislocations and precipitation of a precipitate phase of smaller size. The preparation method has simple process flow, can obtain the dual-phase steel with the layered heterostructure by using a process convenient to operate, and the heterostructure can provide additional back stress reinforcement, layered cracking and other toughening modes for the dual-phase steel, so that the toughness is improved while the strength of the dual-phase steel is maintained. Compared with the traditional method, the strength of the dual-phase steel prepared by the method is kept at 1300MPa, and the fracture toughness K is kept at the same time JIc 175 MPa.m of austenitic ferrite dual-phase steel never reached 1/2 。
Drawings
FIG. 1 is an electron micrograph of the distribution of the morphology of the structure in the dual phase steel of step 1 of the present invention.
FIG. 2 is a tensile engineering stress-strain curve of the dual phase steel of step 1 of the present invention.
FIG. 3 is an electron micrograph of the distribution of the morphology of the structure in the dual phase steel of step 2 of the present invention.
FIG. 4 is a tensile engineering stress-strain curve of the dual phase steel of step 2 of the present invention.
FIG. 5 is an electron micrograph of the distribution of the morphology of the structure in the dual phase steel of step 4 of the present invention.
FIG. 6 is an electron micrograph of the distribution of the morphology of the structure in the dual phase steel of step 6 of the present invention.
FIG. 7 is a tensile engineering stress-strain curve of the dual phase steel of step 6 of the present invention.
FIG. 8 is a graph of toughness of an alloy three-point bend specimen for the dual phase steel of step 6 of the present invention;
wherein, figure a is a crack opening displacement diagram, and figure a is a crack propagation displacement diagram.
Detailed Description
The invention will now be described in further detail with reference to the accompanying drawings, which illustrate but do not limit the invention.
The preparation method of the high-strength plastic layered double-phase stainless steel comprises the following steps:
and step 1, heating the as-cast FeNiCrAl alloy to 1100-1200 ℃ for long-time heat preservation to obtain an alpha phase and a gamma phase with high stability, and then carrying out hot forging and slow cooling to obtain the double-phase stainless steel with the layered structure.
The heat preservation time is 3-5 h, the actual pressing amount of the hot forging treatment is 50%, the cooling mode after the hot forging deformation is air cooling to room temperature, and the room temperature is 20-30 ℃.
And 2, heating the duplex stainless steel obtained in the step 1 to 750-800 ℃, normalizing, and slowly cooling to obtain the duplex stainless steel with the lamellar structure and smaller grain size.
The cooling mode is air cooling to room temperature, and the room temperature is 20-30 ℃.
And 3, performing cold rolling treatment on the double-phase stainless steel with the layered structure obtained in the step 2, and further refining the thickness of the lath with the layered structure.
The cold rolling reduction was 50%.
And 4, heating the duplex stainless steel obtained in the step 3 to 1150 ℃, carrying out heat preservation for a short time, and rapidly cooling to obtain the solid solution state lamellar structure duplex stainless steel.
The short-time heat preservation is 10min, and the quick cooling mode is water cooling.
And 5, performing cold rolling treatment on the double-phase stainless steel with the layered structure obtained in the step 4, and further refining the thickness of the lath with the layered structure.
The cold rolling reduction is 40-60%.
And 6, heating the duplex stainless steel obtained in the step 5 to 600-700 ℃, preserving heat for a long time, and slowly cooling to obtain the aging state layered duplex stainless steel.
The long-time heat preservation is carried out for 2-5h, the cooling mode is air cooling to room temperature, and the room temperature is 20-30 ℃.
The high-strength plastic layered double-phase stainless steel prepared by the method comprises a micron-sized lath-shaped alpha primary phase, a gamma primary phase and a nano-sized spherical intragranular B2 phase. The metallographic structure is a ferrite austenitic lath with a layer thickness of 5 mu m, and the ferrite and austenitic matrix is strengthened by a large amount of spherical nano-scale B2 phases, and a large amount of dislocation is emitted as a dislocation source to improve the toughness of the layered double-phase stainless steel, so that the alloy has excellent comprehensive mechanical properties. The strength of the dual-phase steel is 1300MPa, and the fracture toughness K is high JIc 175 MPa.m of austenitic ferrite dual-phase steel never reached 1/2 。
Example 1
The preparation method of the high-strength plastic layered double-phase stainless steel comprises the following steps:
and step 1, heating the as-cast FeNiCrAl alloy to 1100 ℃ and preserving heat for 4 hours to obtain an alpha phase and a gamma phase with high stability, then performing hot forging with the pressing amount of 50%, and obtaining the laminated structure duplex stainless steel after air cooling.
The morphology of the alloy tissue obtained by the step is shown in figure 1, micron-sized lamellar alpha and gamma primary phases and submicron-sized spherical intragranular B2 phases are in bimodal distribution, and the alloy strength-plasticity curve processed by the process of the step is shown in figure 2, so that the alloy has better strength/plasticity combination, the tensile strength reaches 850MPa, and the uniform elongation reaches 13%.
And 2, heating the duplex stainless steel obtained in the step 1 to 800 ℃, normalizing, and air-cooling to obtain the duplex stainless steel with the layered structure and the austenite content.
The morphology of the alloy structure after normalizing treatment is shown in figure 3, the micro-scale lamellar alpha and gamma primary phases and the nano-scale spherical B2 phase are in bimodal distribution, the austenite content is improved, and the solid solution strengthening effect is improved. The alloy strength-plasticity curve is shown in fig. 4, shows excellent strength/plasticity combination, the tensile strength reaches 1200MPa, and the uniform elongation reaches 18%.
And 3, performing cold rolling treatment on the double-phase stainless steel with the layered structure, which is obtained in the step 2, with the pressing amount of 50%, and further refining the thickness of the strip with the layered structure.
And 4, heating the duplex stainless steel obtained in the step 3 to 1150 ℃, preserving heat for 10min, and water-cooling to obtain the solid solution state lamellar structure duplex stainless steel.
The morphology of the alloy structure obtained by the step is shown in figure 5, and micron-sized lamellar alpha and gamma primary phases and submicron-sized spherical intragranular B2 phases are uniformly distributed in a ferrite matrix.
And 5, performing cold rolling treatment with the pressing quantity of 50% on the double-phase stainless steel with the layered structure obtained in the step 4, and refining the thickness of the strip with the layered structure and the phase B2.
And 6, heating the duplex stainless steel obtained in the step 5 to 650 ℃, preserving heat for 2 hours, and air-cooling to room temperature to obtain the aging state nano particle reinforced lamellar duplex stainless steel.
The morphology of the precipitated phase in the alloy matrix phase is shown in figure 7, and the nano needle-shaped precipitated phase and the nano spherical precipitated phase are respectively formed in austenite and ferrite, so that the yield strength of the dual-phase steel is greatly improved. The toughness graph 8 of the alloy three-point bending sample of the dual-phase steel treated by the process is shown in a graph a, wherein the graph a is a crack opening displacement graph, and the graph a is a crack expansion displacement graph, so that the dual-phase steel can be seen to show extremely high strength/plasticity combination, the tensile strength reaches 1400MPa while the yield strength reaches 1250MPa, the average elongation reaches 18%, and the fracture toughness KJIc reaches 175 MPa.m1/2 which is never reached in the austenitic ferrite dual-phase steel, as shown in FIG. 8.
Example 2
The preparation method of the high-strength plastic layered double-phase stainless steel comprises the following steps:
and step 1, heating the as-cast FeNiCrAl alloy to 1200 ℃ and preserving heat for 3 hours to obtain an alpha phase and a gamma phase with high stability, then performing hot forging with the pressing amount of 50%, and obtaining the laminated structure duplex stainless steel after air cooling.
And 2, heating the duplex stainless steel obtained in the step 1 to 750 ℃, normalizing, and air cooling to obtain the duplex stainless steel with the layered structure and the austenite content.
And 3, performing cold rolling treatment on the layered structure duplex stainless steel obtained in the step 2, wherein the pressing amount of the cold rolling treatment is 50%.
And 4, heating the duplex stainless steel obtained in the step 3 to 1150 ℃, preserving heat for 10min, and water-cooling to obtain the solid solution state lamellar structure duplex stainless steel.
And 5, performing cold rolling treatment on the layered structure duplex stainless steel obtained in the step 4, wherein the pressing amount of the cold rolling treatment is 40%.
And 6, heating the duplex stainless steel obtained in the step 5 to 600 ℃, preserving heat for 5 hours, and air-cooling to room temperature to obtain the aging state nano-particle reinforced lamellar structure duplex stainless steel.
Example 3
The preparation method of the high-strength plastic layered double-phase stainless steel comprises the following steps:
and step 1, heating the as-cast FeNiCrAl alloy to 1150 ℃ and preserving heat for 5 hours to obtain an alpha phase and a gamma phase with high stability, then performing hot forging with the pressing amount of 50%, and obtaining the laminated structure duplex stainless steel after air cooling.
And 2, heating the duplex stainless steel obtained in the step 1 to 780 ℃, normalizing, and air-cooling to obtain the duplex stainless steel with the layered structure and the austenite content.
And 3, performing cold rolling treatment on the layered structure duplex stainless steel obtained in the step 2, wherein the pressing amount of the cold rolling treatment is 50%.
And 4, heating the duplex stainless steel obtained in the step 3 to 1150 ℃, preserving heat for 10min, and water-cooling to obtain the solid solution state lamellar structure duplex stainless steel.
And 5, performing cold rolling treatment on the layered structure duplex stainless steel obtained in the step 4, wherein the pressing amount of the cold rolling treatment is 60%.
And 6, heating the duplex stainless steel obtained in the step 5 to 700 ℃, preserving heat for 4 hours, and air-cooling to room temperature to obtain the aging state nano-particle reinforced lamellar structure duplex stainless steel.
The invention aims to overcome the defects of the existing dual-phase steel and the preparation method thereof, and provides a preparation method of high-strength plastic lamellar dual-phase stainless steel, wherein the lamellar stainless steel in a two-phase region is heated to 1100-1200, and is subjected to heat preservation and air cooling for 3h to room temperature, so that alpha phase and gamma phase with high stability are obtained; compared with the traditional method, the strength of the dual-phase steel prepared by the method is improved to about 1200MPa, and meanwhile, the plasticity is kept above 15%. Subsequently, the alloy was cold rolled by 50%, deformed by rolling, then subjected to solution treatment at 1150 ℃, rapidly cooled with water, cooled to room temperature, and then subjected to rolling aging. The strength of the dual-phase steel prepared by the method is improved by about 200MPa to 1300MPa. Meanwhile, the uniform elongation is basically kept unchanged (18%), and a three-point bending cyclic loading experiment shows that the fracture toughness of the nano-grade B2 particle reinforced lamellar dual-phase steel prepared by the method can reach 176MPa m 1/2 . The method can obtain the layered structure duplex stainless steel comprising a micron-sized lath-shaped alpha primary phase and a gamma primary phase, a micron-sized interphase Laves precipitated phase and a nano-sized needle-shaped spherical intragranular B2 phase, and greatly improves the yield strength and the strain hardening capacity of the alloy, so that the high-strength and high-elongation duplex steel is obtained. The preparation process of the dual-phase steel is easy to operate, short in flow and low in equipment requirement.
The above is only for illustrating the technical idea of the present invention, and the protection scope of the present invention is not limited by this, and any modification made on the basis of the technical scheme according to the technical idea of the present invention falls within the protection scope of the claims of the present invention.
Claims (9)
1. The preparation method of the high-strength and high-toughness lamellar duplex stainless steel is characterized by comprising the following steps of:
step 1, heating an as-cast FeNiCrAl alloy to 1100-1200 ℃ for heat preservation, and then performing hot forging and cooling to obtain the layered structure duplex stainless steel;
step 2, normalizing the duplex stainless steel obtained in the step 1;
step 3, cold rolling the laminated structure duplex stainless steel obtained in the step 2;
step 4, heating the duplex stainless steel obtained in the step 3 to 1150 ℃, preserving heat, and cooling to obtain solid solution state lamellar structure duplex stainless steel;
step 5, cold rolling the layer structure double-phase stainless steel obtained in the step 4;
and 6, heating the duplex stainless steel obtained in the step 5 to 600-700 ℃, preserving heat for a long time, and slowly cooling to obtain the aged lamellar structure duplex stainless steel.
2. The method for preparing the high-strength and high-toughness lamellar duplex stainless steel according to claim 1, wherein the heat preservation time in the step 1 is 3-5 h.
3. The method for preparing high-strength and high-toughness lamellar duplex stainless steel according to claim 1, wherein the pressing amount of hot forging in the step 1 is 50%.
4. The method for preparing the high-strength and high-toughness layered duplex stainless steel according to claim 1, wherein the duplex stainless steel is heated to 750-800 ℃ in the step 2 for normalizing treatment.
5. The method for producing a high strength and toughness layered duplex stainless steel according to claim 1, wherein the cold rolling reduction in step 3 is 50%.
6. The method for preparing the high-strength and high-toughness lamellar duplex stainless steel according to claim 1, wherein the heat preservation time in the step 4 is 10min, and the cooling mode is water cooling.
7. The method for preparing high-strength and high-toughness lamellar duplex stainless steel according to claim 1, wherein the cold rolling reduction in step 5 is 50%.
8. The method for preparing the high-strength and high-toughness layered double-phase stainless steel according to claim 1, wherein the heat preservation time in the step 5 is 2-5h, and the cooling mode is air cooling.
9. A high strength and toughness layered duplex stainless steel according to any one of claims 1-8, wherein said duplex stainless steel comprises a micron-sized lath-like alpha primary phase, a gamma primary phase, and a nano-sized globular intragranular B2 phase.
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