CN114082874A - Preparation method of austenite/ferrite/martensite multiphase isomeric steel material - Google Patents
Preparation method of austenite/ferrite/martensite multiphase isomeric steel material Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 74
- 239000010959 steel Substances 0.000 title claims abstract description 74
- 239000000463 material Substances 0.000 title claims abstract description 35
- 229910001566 austenite Inorganic materials 0.000 title claims abstract description 25
- 229910000734 martensite Inorganic materials 0.000 title claims abstract description 24
- 229910000859 α-Fe Inorganic materials 0.000 title claims abstract description 20
- 238000002360 preparation method Methods 0.000 title claims description 4
- 238000003466 welding Methods 0.000 claims abstract description 60
- 238000005242 forging Methods 0.000 claims abstract description 52
- 229910001209 Low-carbon steel Inorganic materials 0.000 claims abstract description 44
- 238000005096 rolling process Methods 0.000 claims abstract description 37
- 238000010438 heat treatment Methods 0.000 claims abstract description 35
- 238000000034 method Methods 0.000 claims abstract description 22
- 238000010791 quenching Methods 0.000 claims abstract description 20
- 230000000171 quenching effect Effects 0.000 claims abstract description 20
- 229910000576 Laminated steel Inorganic materials 0.000 claims abstract description 12
- 229910000963 austenitic stainless steel Inorganic materials 0.000 claims description 32
- 238000005520 cutting process Methods 0.000 claims description 18
- 238000000227 grinding Methods 0.000 claims description 13
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 claims description 10
- 230000008569 process Effects 0.000 claims description 8
- 238000001816 cooling Methods 0.000 claims description 6
- 238000005498 polishing Methods 0.000 claims description 6
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 5
- 238000013459 approach Methods 0.000 claims description 5
- 229910052799 carbon Inorganic materials 0.000 claims description 5
- 238000004140 cleaning Methods 0.000 claims description 5
- 239000003344 environmental pollutant Substances 0.000 claims description 5
- 231100000719 pollutant Toxicity 0.000 claims description 5
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 4
- 230000009471 action Effects 0.000 claims description 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims 2
- 239000007788 liquid Substances 0.000 claims 1
- 229910052757 nitrogen Inorganic materials 0.000 claims 1
- 238000004321 preservation Methods 0.000 claims 1
- 238000009763 wire-cut EDM Methods 0.000 claims 1
- 229910001220 stainless steel Inorganic materials 0.000 abstract description 6
- 239000010935 stainless steel Substances 0.000 abstract description 6
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 8
- 229910052742 iron Inorganic materials 0.000 description 4
- 238000009826 distribution Methods 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 241000446313 Lamella Species 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 230000001105 regulatory effect Effects 0.000 description 2
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- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 229910001339 C alloy Inorganic materials 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/002—Hybrid process, e.g. forging following casting
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23P—METAL-WORKING NOT OTHERWISE PROVIDED FOR; COMBINED OPERATIONS; UNIVERSAL MACHINE TOOLS
- B23P15/00—Making specific metal objects by operations not covered by a single other subclass or a group in this subclass
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips 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
- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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- C—CHEMISTRY; METALLURGY
- 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
- C21D2211/005—Ferrite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
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Abstract
The present specification provides a method for preparing an austenitic/ferritic/martensitic heterogeneous steel material, comprising: the method comprises five procedures of rotary friction welding, alternate rotary friction welding, high-temperature free forging, low-temperature rolling and multiphase heterogeneous heat treatment. The method is characterized in that: selecting low-carbon steel and austenitic steel bars, and alternately welding the two steel materials by using a rotary friction welding method; carrying out high-temperature free forging and quenching on the welded cylindrical laminated sample to obtain a cubic laminated steel block and adjusting the initial structure of the low-carbon steel layer; and then the structures of the low-carbon steel and the stainless steel are thinned through low-temperature rolling, and finally the multiphase isomeric steel material consisting of superfine austenite, ferrite and martensite is obtained through multiphase isomeric heat treatment.
Description
Technical Field
The invention relates to a method for preparing an austenite/ferrite/martensite multiphase isomeric steel material, which comprises the following steps: the method comprises five procedures of rotary friction welding, alternate rotary friction welding, high-temperature free forging, low-temperature rolling and multiphase heterogeneous heat treatment. Specifically, low-carbon steel and austenitic steel bars are selected, and two steel materials are subjected to alternate butt welding by a rotary friction welding method; carrying out high-temperature free forging and quenching on the welded cylindrical laminated steel bar to obtain a cubic laminated steel block and adjusting the initial structure of a low-carbon steel layer; and then the structures of the low-carbon steel and the stainless steel are thinned through low-temperature rolling, and finally the multiphase isomeric steel material consisting of superfine austenite, ferrite and martensite is obtained through multiphase isomeric heat treatment.
Technical Field
The steel material is used as the most common structural material and is widely applied to various fields of buildings, transportation, petrochemical industry and the like. The improvement of the strength of the steel material has important significance for the structure lightweight and the improvement of the structure safety performance. For steel materials, increasing the carbon content is the most effective and economical way to strengthen steel materials, but the strength, toughness and plasticity of most steels are contradictory. In order to obtain higher toughness and plasticity, a portion of the strength often has to be sacrificed. An increase in the carbon content would also have a corresponding number of disadvantages, for example a reduction in the weldability and the formability of the material. However, the strength of the low-carbon alloy steel commonly used in the industry at present is generally low, for example, the tensile strength of the commonly used Q235 steel is usually below 500MPa, and the requirement of higher strength grade is difficult to meet. Therefore, how to obtain the high-performance steel material in an effective way has important significance for popularizing the application of the steel material.
For steel materials, different microstructures can be obtained by adjusting the content of alloy elements, plastic deformation, heat treatment modes and the like, wherein austenite has a face-centered cubic structure and generally has lower yield strength and excellent uniform elongation; the ferrite has low carbon content, low strength and good elongation; martensite has a high dislocation density due to its fine internal size, and has a high strength but a low elongation. Research shows that when the steel material forms a heterogeneous structure with dual-phase/multi-phase composition, the material can obtain excellent comprehensive mechanical properties. The invention discloses a method for manufacturing 1180 MPa-grade ultrahigh-strength low-cost cold-rolled quenching distribution steel through retrieval, and specifically discloses a method for manufacturing 1180 MPa-grade ultrahigh-strength low-cost cold-rolled quenching distribution steel, which comprises the steps of performing two-stage controlled rolling on an ingot, performing multi-pass cold rolling, and finally performing two-stage heat treatment to obtain a steel plate with a mixed structure of ferrite, martensite and retained austenite. The technology has the characteristics that the grain size can be effectively refined, and excellent strength-plasticity matching is obtained. However, disadvantages of this approach are: (1) the heating rate and the cooling rate need to be frequently adjusted, and the temperature and time of distribution are strictly controlled, so that the production difficulty is increased; (2) the content of the retained austenite depends on the regulation of the heat treatment process, and the high content of austenite structure cannot be provided to improve the elongation. Further search revealed that He et al published an article entitled "Improving reduction by increasing fractionation of interfacial zone in low C steel/304SS coatings" on mater.sci.eng.a 726(2018) 288-. The technology has the characteristics that the process is simple, the martensite in the obtained three-layer material provides high strength, the austenite content is high, and the elongation is provided. However, the disadvantages of this technique are: (1) the interface is difficult to ensure to be well combined in the hot rolling process, and the final mechanical property is influenced; (2) it is difficult to prepare a multilayer structure.
Disclosure of Invention
The invention provides a method for preparing high-strength and high-toughness multiphase isomeric steel materials, which comprises the steps of firstly utilizing rotary friction welding to alternately weld low-carbon low-alloy steel and austenitic stainless steel rods to prepare a cylindrical laminated sample consisting of multiple layers of low-carbon steel and austenitic stainless steel; then, the shape of the cylindrical sample is changed into a cube through high-temperature free forging, the subsequent low-temperature rolling treatment is facilitated while the high-temperature homogenization is realized, and the microstructure of the low-carbon steel layer is adjusted by combining the critical quenching treatment after forging; then, the austenitic stainless steel layer is subjected to strain induced martensitic phase transformation through low-temperature rolling deformation, and the grain size of the low-carbon steel layer is refined; finally, by skillfully utilizing different responses of the deformed low-carbon steel and the deformed austenitic steel under heat treatment, the austenite lamella is reversely transformed to form fine equiaxed austenite grains, and meanwhile, the low-carbon steel lamella is transformed into a superfine ferrite-martensite dual-phase structure, so that the multiphase isomeric steel material consisting of superfine austenite, ferrite and martensite is obtained. Wherein, good-toughness austenite, ferrite and high-strength martensite are respectively used as soft/hard components of the heterogeneous material, and the multi-component coordinated deformation improves the comprehensive mechanical property of the material.
The technical scheme for realizing the purpose of the invention is as follows:
a preparation method of austenite/ferrite/martensite multiphase isomeric steel material mainly comprises the following steps:
step one, rotating friction welding: the method comprises the steps of selecting a low-carbon steel rod and an austenitic stainless steel rod with certain diameters and lengths, sequentially polishing the end faces to be welded of the steel rods by 600#, 1200# and 2000# abrasive paper, and cleaning the end faces by alcohol and acetone to remove pollutants such as an oxide film, oil stains and the like on the welded end faces. As shown in fig. 1, low carbon steel is fixed to the rotating end of the spin friction welder by a rotating chuck, and austenitic stainless steel is fixed to the moving end by a fixed chuck. In the welding process, the rotating end rotates at a certain rotating speed, the moving end is close to and contacted with the rotating end, friction heat generated by relative rotating motion of the steel bars at two ends is used as a heat source, metallurgical reaction occurs at the interface under the action of upsetting pressure, and metallurgical bonding is realized between the steel bars. The diameter of the two bars is 10-30mm, the length is 50-100mm, the rotating speed of the rotating end is 1200-2000rpm, the upsetting pressure is 50-300MPa, the upsetting time is 5-15s, and the upsetting amount is 1-10 mm.
Step two, alternate spin friction welding: removing burrs at a welding joint by using an angle grinder, polishing to be bright by using a grinding wheel, cutting off one side of austenitic stainless steel at a position 2-10mm away from a welding line by using electric spark wire cutting, enabling the rest austenitic steel rods to be used, fixing the low-carbon steel rod welded with the austenitic steel at a rotating end again, fixing another low-carbon steel rod with the same diameter at a moving end, repeating the steps of rotary friction welding and wire cutting for more than one time, and obtaining the cylindrical laminated sample with the low-carbon steel and the austenitic stainless steel distributed alternately. The number of layers of the laminated bar and the thickness of each layer can be flexibly regulated and controlled by adjusting the times of the alternate friction welding and the length of each section of the steel bar. The number of the laminated bar is 2-8, and the thickness of each layer is 2-10 mm.
Step three, high-temperature free forging: performing high-temperature free forging on the cylindrical laminated steel bar obtained by the alternate rotary friction welding, forging a cylindrical test sample into a cubic shape through multi-pass free forging as shown in figure 1, heating the laminated steel block to 1000-; after the forging is finished, cooling the sample to the temperature of 720-860 ℃, and then performing water quenching; the total thickness of the freely forged cubic laminated sample along the direction vertical to the lamina is 10-25mm, and the width of the final cubic steel block is larger than the total thickness for facilitating subsequent low-temperature rolling.
Fourthly, low-temperature rolling: and (3) rolling the multilayer steel obtained by high-temperature free forging and quenching at a low temperature of-196-400 ℃, wherein the rolling amount is 0.2-0.5mm each time, and the accumulated rolling amount is 50-95%.
Fifthly, heterogeneous heat treatment: and (3) carrying out heat treatment on the steel plate after low-temperature rolling at 700-860 ℃ for 1-60min, and then carrying out quenching treatment on the steel plate to obtain the multiphase isomeric steel material consisting of ultrafine austenite, ferrite and martensite.
Compared with the prior art, the invention has the following remarkable advantages:
1. preparing a multiphase isomeric steel material, wherein ferrite and high-content austenite provide plasticity and martensite provides strength;
2. the interface bonding of the dissimilar materials formed by friction welding is good;
3. the thickness and the total number of layers of each layer in the multiphase isomeric steel can be flexibly regulated and controlled.
Drawings
FIG. 1 is a schematic process flow diagram;
the test device comprises a test piece, a rotating friction welding machine chuck, a low-carbon steel bar, an austenitic stainless steel bar, a laminated cylinder sample, a forging machine upper grinding iron, a forging machine lower grinding iron, a cubic laminated steel block obtained by free forging, a rolling mill roller and a heat treatment furnace, wherein the test piece 1 is the rotating friction welding machine chuck, the 2 is the low-carbon steel bar, the 3 is the austenitic stainless steel bar, the 4 is the laminated cylinder sample, the 5 is the grinding iron on the forging machine, the 6 is the lower grinding iron, the 7 is the cubic laminated steel block obtained by free forging, the 8 is the rolling mill roller and the 9 is the heat treatment furnace;
FIG. 2 is a schematic view of the structure of a steel sheet before and after heat treatment;
wherein 10 is martensite in the low carbon steel layer, 11 is ferrite in the low carbon steel layer, and 12 is austenite in the stainless steel layer;
FIG. 3 is the scanning electron microscope photograph of the dual-phase structure of ultra-fine ferrite and martensite and the transmission electron microscope photograph of ultra-fine equiaxed austenite after the isomerization heat treatment.
Detailed description of the invention
The present invention will be further illustrated by the following examples
Example 1
1 304 austenitic stainless steel rods with the diameter of 20mm and the length of 50mm and 2Q 235 low-carbon steel rods are selected.
(1) Rotating friction welding: before welding, sequentially polishing the end faces to be welded of the steel bars by using 600#, 1200# and 2000# abrasive paper, and cleaning the end faces by using alcohol and acetone to remove pollutants such as an oxide film, oil stains and the like on the welded end faces; fixing an austenitic stainless steel bar at a rotating end of a welding machine through a rotating chuck, and fixing a low-carbon steel bar at a moving end through a fixing chuck; in the welding process, the rotating end rotates at the rotating speed of 1500rpm, the moving end approaches and contacts the rotating end, the upsetting pressure is 100MPa, the upsetting time is 10s, and the upsetting amount is 3 mm.
(2) Alternate rotary friction welding: removing burrs at the welding joint by using an angle grinder after welding is finished, and grinding to be bright by using a grinding wheel; and (3) cutting off one side of the austenitic stainless steel at a position 5mm away from a welding line by using spark wire cutting after taking down the sample, keeping the residual austenitic stainless steel rod for standby, fixing the low-carbon steel rod welded with the stainless steel at the rotating end of a welding machine, fixing the other low-carbon steel rod with the same diameter at the moving end, repeating the steps for 2 times to obtain a cylindrical sample consisting of 4 layers of low-carbon steel and austenitic stainless steel alternately, wherein the thickness of each layer is 5mm, the total height of the sample in the direction vertical to the thickness of the sheet layer is 20mm, and finally cutting off redundant round rods at two sides by using the spark wire cutting.
(3) High-temperature free forging: performing high-temperature free forging on the 4 layers of steel rods obtained by the alternate rotary friction welding, changing the cylindrical test sample into a cubic shape through multi-pass free forging, heating the laminated steel block to 1100 ℃ before each pass of forging, preserving the heat for 30min, keeping the forging temperature in the range of 900-1000 ℃, and putting the sample into a furnace again for heating after each pass of forging is finished; finally, cooling the sample to 760 ℃ after forging is finished, and then performing water quenching; the total height of the as-forged cubic steel block in the direction perpendicular to the sheet layers was 18 mm.
(4) And (3) low-temperature rolling: the multilayer steel material with the thickness of 18mm obtained by high-temperature free forging and quenching is rolled at room temperature, the rolling amount is 0.5mm each time, the sample is statically placed in the air for 30s after each time, the accumulated rolling amount is 90%, and the final plate thickness is 1.8 mm.
(5) Heterogeneous heat treatment: and (3) carrying out 760 ℃ heat treatment on the steel plate after low-temperature rolling for 10min, and then carrying out quenching treatment on the steel plate to obtain the multiphase isomeric steel material consisting of superfine austenite, ferrite and martensite.
Example 2
1 304 austenitic stainless steel rods with the diameter of 20mm and the length of 50mm and 2Q 235 low-carbon steel rods are selected.
(1) Rotating friction welding: before welding, sequentially polishing the end faces to be welded of the steel bars by using 600#, 1200# and 2000# abrasive paper, and cleaning the end faces by using alcohol and acetone to remove pollutants such as an oxide film, oil stains and the like on the welded end faces; fixing an austenitic stainless steel bar at a rotating end of a welding machine through a rotating chuck, and fixing a low-carbon steel bar at a moving end through a fixing chuck; in the welding process, the rotating end rotates at the rotating speed of 1500rpm, the moving end approaches and contacts the rotating end, the upsetting pressure is 100MPa, the upsetting time is 10s, and the upsetting amount is 3 mm.
(2) Alternate spin friction welding: removing burrs at the welding joint by using an angle grinder after welding is finished, and grinding to be bright by using a grinding wheel; and cutting off one side of the austenitic stainless steel at a position 5mm away from the welding line by using spark wire cutting after the sample is taken down, reserving the residual austenitic stainless steel rod for later use, fixing the low-carbon steel rod welded with the stainless steel at the rotating end of a welding machine, fixing the other low-carbon steel rod with the same diameter at the moving end, repeating the steps for 3 times to obtain a cylindrical sample consisting of 5 layers of low-carbon steel and austenitic stainless steel alternately, wherein the thickness of each layer is 5mm, the total height of the sample in the direction vertical to the thickness of the sheet layer is 25mm, and finally cutting off the redundant round rods at two sides by using the spark wire cutting.
(3) High-temperature free forging: performing high-temperature free forging on 5 layers of steel rods obtained by alternate rotary friction welding, changing a cylindrical test sample into a cubic shape through multi-pass free forging, heating the laminated steel block to 1100 ℃ before each-pass forging, preserving the heat for 30min, keeping the forging temperature range at 900-1000 ℃, and putting the sample into a furnace again for heating after each-pass forging is finished; after the last forging, cooling the sample to 760 ℃, and then performing water quenching; the total height of the as-forged cube in the direction perpendicular to the sheets was 20 mm.
(4) And (3) low-temperature rolling: the multilayer steel material with the thickness of 20mm obtained by high-temperature free forging and quenching is rolled at room temperature, the rolling amount is 0.5mm each time, the sample is statically placed in the air for 30s after each time, the accumulated rolling amount is 90%, and the final plate thickness is 2 mm.
(5) Heterogeneous heat treatment: and (3) carrying out 760 ℃ heat treatment on the steel plate after low-temperature rolling for 10min, and then carrying out quenching treatment on the steel plate to obtain the multiphase isomeric steel material consisting of superfine austenite, ferrite and martensite.
Example 3
1 piece of 316L austenitic stainless steel bar and 2 pieces of Q235 low-carbon steel bar with the diameter of 20mm and the length of 50mm are selected.
(1) Rotating friction welding: before welding, sequentially polishing the end faces to be welded of the steel bars by using 600#, 1200# and 2000# abrasive paper, and cleaning the end faces by using alcohol and acetone to remove pollutants such as an oxide film, oil stains and the like on the welded end faces; fixing an austenitic stainless steel bar at a rotating end of a welding machine through a rotating chuck, and fixing a low-carbon steel bar at a moving end through a fixing chuck; in the welding process, the rotating end rotates at the rotating speed of 1500rpm, the moving end approaches and contacts the rotating end, the upsetting pressure is 100MPa, the upsetting time is 10s, and the upsetting amount is 3 mm.
(2) Alternate spin friction welding: removing burrs at the welding joint by using an angle grinder after welding is finished, and grinding to be bright by using a grinding wheel; and cutting off one side of the austenitic stainless steel at a position 3mm away from a welding line by using spark wire cutting after the sample is taken down, reserving the residual austenitic stainless steel rod for later use, fixing the low-carbon steel rod welded with the stainless steel at the rotating end of a welding machine, fixing another low-carbon steel with the same diameter at the moving end, repeating the welding and wire cutting steps to obtain a cylindrical sample consisting of 3 layers of low-carbon steel and 2 layers of austenitic stainless steel alternately, wherein the thickness of each layer of austenitic stainless steel is 3mm, the thickness of each layer of low-carbon steel is 5mm, the total height of the sample in the direction vertical to the thickness of the sheet layer is 21mm, and finally cutting off redundant round rods at two sides by using the spark wire cutting.
(3) High-temperature free forging: performing high-temperature free forging on the 5-layer steel bar obtained by the alternate rotary friction welding, changing the cylindrical test sample into a cubic shape through multi-pass free forging, heating the laminated steel block to 1100 ℃ before each pass of forging, preserving the heat for 30min, keeping the forging temperature in the range of 900-1000 ℃, and putting the sample into a furnace again for heating after each pass of forging is finished; finally, cooling the sample to 760 ℃ after forging is finished, and then performing water quenching; the total height of the as-forged cube in the direction perpendicular to the sheets was 20 mm.
(4) And (3) low-temperature rolling: and (3) rolling the multilayer steel with the thickness of 20mm obtained by high-temperature free forging and quenching at room temperature, wherein the rolling amount is 0.2-0.5mm each time, standing the sample in the air for 30s after each pass is finished, the accumulated rolling amount is 90%, and the final plate thickness is 2 mm.
(5) Heterogeneous heat treatment: and (3) carrying out 750 ℃ heat treatment on the steel plate after low-temperature rolling, keeping the temperature for 15min, and then carrying out quenching treatment on the steel plate to obtain the multiphase isomeric steel material consisting of superfine austenite, ferrite and martensite.
Claims (5)
1. A preparation method of austenite/ferrite/martensite multiphase isomeric steel material mainly comprises the following steps:
step one, rotating friction welding: selecting a low-carbon steel bar and an austenitic stainless steel bar with certain diameters and lengths, polishing the end faces to be welded of the steel bars by using 600#, 1200# and 2000# abrasive paper in sequence before welding, and cleaning the end faces by using alcohol and acetone to remove pollutants such as an oxide film, oil stains and the like on the welded end faces; fixing a low-carbon steel bar at the rotating end of a rotary friction welding machine through a rotating chuck, and fixing an austenitic stainless steel bar at the moving end through a fixing chuck; the rotating end rotates at a certain rotating speed, the moving end approaches to and contacts the rotating end, friction heat generated by relative rotating motion of the steel bars at the two ends is used as a heat source, and metallurgical bonding is realized between the steel bars under the action of upsetting pressure; in the welding process, the rotating speed of the rotating end is 1200-2000rpm, the upsetting pressure is 50-300MPa, the upsetting time is 5-15s, and the upsetting amount is 1-10 mm.
Step two, alternate spin friction welding: removing burrs at the welding joint obtained in the first step by using an angle grinder, and grinding the burrs to be bright by using a grinding wheel; cutting off the austenitic stainless steel at the position 2-10mm away from the welding seam by using electrospark wire-electrode cutting, and keeping the residual austenitic steel bar for later use; fixing the low-carbon steel rod welded with the austenitic steel at the rotating end again, fixing another low-carbon steel rod with the same diameter at the moving end, and repeating the steps to obtain cylindrical laminated samples with the low-carbon steel and the austenitic stainless steel distributed alternately; the number of the laminated bar is 2-8, the thickness of each layer is 2-10mm, the total thickness along the direction vertical to the laminated sheet is 10-30mm, and redundant parts at two ends are cut off by wire cut electrical discharge machining.
Step three, high-temperature free forging: performing high-temperature free forging on a cylindrical laminated sample obtained by alternate rotary friction welding, forging the cylindrical sample into a cubic shape through multi-pass free forging, heating the laminated steel block to 1000-1200 ℃ before each pass of forging, preserving heat for 10-30min, keeping the forging temperature range at 900-1000 ℃, and putting the sample into a furnace again for heating and preserving heat after each pass of forging is finished; and finally, cooling the sample to 720-860 ℃ after the forging is finished, and then performing water quenching.
Fourthly, low-temperature rolling: and (3) rolling the multilayer steel obtained by high-temperature free forging and quenching at a low temperature of-196-400 ℃, wherein the rolling amount is 0.2-0.5mm each time, and the accumulated rolling amount is 50-95%.
Fifthly, heterogeneous heat treatment: and (3) carrying out heat treatment on the steel plate after low-temperature rolling at 700-860 ℃ for 1-60min, and then carrying out quenching treatment on the steel plate to obtain the multiphase isomeric steel material consisting of superfine austenite, ferrite and martensite.
2. Spin friction welding according to claim 1, characterized in that the low carbon steel and the austenitic stainless steel rods are 10-40mm in diameter and 50-100mm in length, the low carbon steel having a carbon content in the range (c ≦ 0.25 wt.%), and the austenitic stainless steel being a 3-series austenitic stainless steel.
3. The high temperature free forging as claimed in claim 1, wherein the cubic laminated steel block obtained by free forging has a total thickness of 10-25mm in a direction perpendicular to the sheet direction, and the width of the final cubic steel block is equal to or greater than the total thickness for facilitating subsequent low temperature rolling.
4. The cryogenic rolling of claim 1 wherein the sample is immersed in liquid nitrogen for 5-10min before rolling below 0 ℃; and (3) placing the sample into a muffle furnace for heating and heat preservation for 5-30min before rolling at the temperature higher than 25 ℃.
5. The heterogeneous heat treatment according to claim 1, characterized in that the austenitic steel layer obtained by the heat treatment has a proportion of austenite grains of not less than 90%, the low carbon steel layer has a martensite fraction of 30% to 80%, and the remainder is ferrite.
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