CN117327991A - High-strength and high-toughness low-density steel with multi-stage nanostructure strengthening effect and preparation method thereof - Google Patents
High-strength and high-toughness low-density steel with multi-stage nanostructure strengthening effect and preparation method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 112
- 239000010959 steel Substances 0.000 title claims abstract description 112
- 239000002086 nanomaterial Substances 0.000 title claims abstract description 36
- 238000005728 strengthening Methods 0.000 title claims abstract description 34
- 230000000694 effects Effects 0.000 title claims abstract description 32
- 238000002360 preparation method Methods 0.000 title abstract description 11
- 239000000956 alloy Substances 0.000 claims abstract description 49
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 45
- 230000001427 coherent effect Effects 0.000 claims abstract description 13
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 10
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 7
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 6
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 238000000137 annealing Methods 0.000 claims description 35
- 238000005096 rolling process Methods 0.000 claims description 28
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 24
- 238000005098 hot rolling Methods 0.000 claims description 22
- 238000000265 homogenisation Methods 0.000 claims description 17
- 238000000034 method Methods 0.000 claims description 16
- 238000003723 Smelting Methods 0.000 claims description 12
- 229910052786 argon Inorganic materials 0.000 claims description 12
- 230000001681 protective effect Effects 0.000 claims description 12
- 238000005097 cold rolling Methods 0.000 claims description 10
- 238000005266 casting Methods 0.000 claims description 9
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 8
- 229910052757 nitrogen Inorganic materials 0.000 claims description 5
- 238000004321 preservation Methods 0.000 claims description 5
- 229910052734 helium Inorganic materials 0.000 claims description 4
- 239000001307 helium Substances 0.000 claims description 4
- SWQJXJOGLNCZEY-UHFFFAOYSA-N helium atom Chemical compound [He] SWQJXJOGLNCZEY-UHFFFAOYSA-N 0.000 claims description 4
- 239000011261 inert gas Substances 0.000 claims description 4
- 238000004519 manufacturing process Methods 0.000 claims description 2
- 230000003014 reinforcing effect Effects 0.000 claims 1
- 239000000463 material Substances 0.000 abstract description 49
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 abstract description 20
- 229910052742 iron Inorganic materials 0.000 abstract description 6
- 230000002787 reinforcement Effects 0.000 abstract description 3
- 239000007769 metal material Substances 0.000 abstract description 2
- 150000001247 metal acetylides Chemical class 0.000 abstract 1
- 239000002994 raw material Substances 0.000 description 11
- 239000007789 gas Substances 0.000 description 9
- 230000000052 comparative effect Effects 0.000 description 6
- 239000002244 precipitate Substances 0.000 description 6
- 229910052720 vanadium Inorganic materials 0.000 description 5
- 235000013339 cereals Nutrition 0.000 description 4
- 230000006698 induction Effects 0.000 description 4
- 238000010791 quenching Methods 0.000 description 4
- 230000000171 quenching effect Effects 0.000 description 4
- 239000000126 substance Substances 0.000 description 4
- 238000005406 washing Methods 0.000 description 4
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 4
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 3
- 238000013459 approach Methods 0.000 description 3
- 230000005540 biological transmission Effects 0.000 description 3
- 238000013329 compounding Methods 0.000 description 3
- 229910052758 niobium Inorganic materials 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 238000004098 selected area electron diffraction Methods 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 239000010949 copper Substances 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000005086 pumping Methods 0.000 description 2
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910000861 Mg alloy Inorganic materials 0.000 description 1
- 240000007594 Oryza sativa Species 0.000 description 1
- 235000007164 Oryza sativa Nutrition 0.000 description 1
- 229910000794 TRIP steel Inorganic materials 0.000 description 1
- 229910000937 TWIP steel Inorganic materials 0.000 description 1
- 229910001069 Ti alloy Inorganic materials 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000013256 coordination polymer Substances 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 230000009977 dual effect Effects 0.000 description 1
- 238000010891 electric arc Methods 0.000 description 1
- 238000003912 environmental pollution Methods 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 229910052746 lanthanum Inorganic materials 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 235000009566 rice Nutrition 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 239000000725 suspension Substances 0.000 description 1
- 239000010936 titanium Substances 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
Classifications
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- 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
- 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
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
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- Crystallography & Structural Chemistry (AREA)
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Abstract
The invention discloses high-strength and high-toughness low-density steel with a multi-stage nanostructure strengthening effect and a preparation method thereof, and belongs to the technical field of metal materials. Comprises the following components in atom percent: 25 to 32 percent of Mn, 12 to 18 percent of Al, 3.0 to 7.0 percent of C, 0 to or less than or equal to Nb and 0.2 percent, 0 to or less than or equal to V and 0.8 percent, and the balance of Fe and unavoidable impurities. The invention forms a multi-level coherent structure containing sub-nano kappa phase, several nano kappa phases and dozens of nano MC carbides in the iron and steel material, and the alloy has extremely high strength and better toughness through the multi-level nano structure reinforcement, and the iron and steel material has lower density and cost and can meet the requirement of the iron and steel material with high specific strength.
Description
Technical Field
The invention belongs to the technical field of metal materials, and particularly relates to high-strength and high-toughness low-density steel with a multi-stage nanostructure strengthening effect and a preparation method thereof.
Background
Increasing the specific strength of structural materials is critical to improving energy efficiency, reducing environmental pollution, saving resources, and protecting the environment, and especially in the field of automobile manufacturing, light weight has become an unavoidable trend. Currently, the main methods for achieving the light weight of equipment include two approaches. The first method is to use structural materials with lower density, such as aluminum alloy, magnesium alloy, titanium alloy and the like, but the wide application of the structural materials in the field of structural materials is limited due to poor strength and toughness and high cost. The second approach is to use high strength structural materials to reduce overall weight by reducing the size of the structural components, such as CP steel, DP steel, TRIP steel, TWIP steel, martensitic steel, Q & P steel, and the like. However, with the increase of strength, the plasticity of the materials is obviously reduced, and the density is higher, so that the requirements of high-strength, high-toughness and low-density materials cannot be met. Therefore, the limitations of the two approaches can be effectively solved by adopting a low-density high-strength structural material.
FeMnAlC series low-density steel is a novel light-weight high-strength material and can be divided into three types according to microstructure: austenitic low density steel, duplex low density steel, and ferritic low density steel. Among them, the austenitic low-density steel has excellent comprehensive mechanical properties, and is a very promising next-generation high-strength and high-toughness low-density steel material. However, austenitic low-density steels are liable to form large-size kappa phase, DO3 phase, beta Mn phase and the like at grain boundaries, and the mechanical properties of the alloy are seriously affected, so that the existing low-density steels are difficult to have extremely high specific strength.
In the prior art, chinese patent publication No. CN115216703A proposes a high-strength low-density steel, which comprises the following components in percentage by mass: 25 to 30 percent of Mn, 11 to 12 percent of Al, 1.0 to 1.2 percent of C, and the balance of Fe and unavoidable impurities. The invention fully utilizes the work hardening and the dispersion strengthening of kappa-carbide to improve the strength (1900 MPa) of the low-density steel, but has lower plasticity (5 percent) and is difficult to meet the requirements of high-specific-strength high-toughness structural materials.
The Chinese patent with publication number of CN114752864A discloses ultra-high strength plastic low-density steel, which comprises the following components in percentage by mass: 30 to 34 percent of Mn, 11 to 11.9 percent of Al, 1.2 to 1.29 percent of C, 4 to 7 percent of Cr, 0.5 to 1.2 percent of Cu, 0.01 to 0.3 percent of Nb, 0.01 to 0.3 percent of V, 0.01 to 0.3 percent of Ti, 0.05 to 0.1 percent of La, 0.0001 to 0.005 percent of B, 0.05 to 0.1 percent of N, less than or equal to 0.012 percent of P, less than or equal to 0.003 percent of S and the balance of iron and unavoidable impurities, and the low-density ultrahigh-strength high-plasticity steel has good plasticity, but has lower specific strength, lower yield strength of less than 1.0GPa and tensile strength of less than 1.1GPa.
Wang Z, lu W, zhao H et Al, in a paper published by Science Advance, ultrastrong lightweight compositionally complex steels via dual-nanoprisation [ J ]. Science Advances,2020,6, reported a low density iron and steel material Fe-26Mn-16Al-5Ni-5C, which had two coherent precipitate phases, and after heat treatment at 900 ℃ for 3 minutes, excellent mechanical properties including tensile strength of 1.4GPa and elongation at break of 38% were obtained. However, the alloy contains nickel element with higher cost, which is unfavorable for reducing the cost of the alloy.
Disclosure of Invention
This section is intended to outline some aspects of embodiments of the invention and to briefly introduce some preferred embodiments. Some simplifications or omissions may be made in this section as well as in the description summary and in the title of the application, to avoid obscuring the purpose of this section, the description summary and the title of the invention, which should not be used to limit the scope of the invention.
The present invention has been made in view of the above and/or problems occurring in the prior art.
One of the purposes of the invention is to provide a high-strength and high-toughness low-density steel with a multi-stage nanostructure strengthening effect.
In order to solve the technical problems, the invention provides the following technical scheme: the high-strength and high-toughness low-density steel with the multi-stage nanostructure strengthening effect comprises the following components in percentage by atom: 25 to 32 percent of Mn, 12 to 18 percent of Al, 3.0 to 7.0 percent of C, 0 to or less than or equal to Nb and 0.2 percent, 0 to or less than or equal to V and 0.8 percent, and the balance of Fe and unavoidable impurities;
wherein, according to the atomic percentage, mn/Al is more than or equal to 1.0, (Mn+Al)/C is more than or equal to 30, (Nb+V) is less than or equal to 1.0 percent and V/Nb is more than or equal to 4.
As a preferable scheme of the high-strength and high-toughness low-density steel with the multi-stage nanostructure strengthening effect, the invention comprises the following steps: the high-strength and high-toughness low-density steel internally forms a multi-stage coherent structure containing sub-nano-scale kappa phase, nano-scale kappa phase and tens of nano-scale MC carbide.
As a preferable scheme of the high-strength and high-toughness low-density steel with the multi-stage nanostructure strengthening effect, the invention comprises the following steps: the alloy has the following characteristics:
(i) Yield strength is 800-2000 MPa;
(ii) Tensile strength is 1000-2248 MPa;
(iii) The elongation after fracture is 3-70%;
(iv) The specific strength is 150-330 MPa cm 3 g -1 。
It is another object of the present invention to provide a method for preparing high strength and toughness low density steel having a multi-stage nanostructure strengthening effect as described above, comprising,
the components are prepared according to the atomic ratio, and are smelted under the protection of vacuum or inert gas, cast into a casting blank, and the casting blank is subjected to hot rolling, homogenization, cold rolling and annealing treatment to obtain the high-strength and high-toughness low-density steel with the multi-stage nanostructure strengthening effect.
As a preferable scheme of the preparation method of the high-strength and high-toughness low-density steel with the multi-stage nanostructure strengthening effect, the invention comprises the following steps: the raw materials of each component of the alloy adopt pure elements or intermediate alloy, and the purity is more than or equal to 99.0 percent. The defects of damaging the comprehensive performance of the alloy due to the inclusion and the like introduced by lower purity of the raw materials are overcome.
As a preferable scheme of the preparation method of the high-strength and high-toughness low-density steel with the multi-stage nanostructure strengthening effect, the invention comprises the following steps: the smelting comprises adopting an induction furnace, an electric arc furnace or a suspension furnace for smelting, wherein the smelting temperature is 1450-2200 ℃, and the heat preservation time is more than 0.1 hour; the smelting is carried out by maintaining the vacuum degree in the furnace below 1 Pa or maintaining the inert gas pressure in the furnace below 100 MPa. The alloy is repeatedly smelted for not less than 1 time so as to ensure that the alloy components are uniformly smelted.
As a preferable scheme of the preparation method of the high-strength and high-toughness low-density steel with the multi-stage nanostructure strengthening effect, the invention comprises the following steps: the hot rolling adopts multi-pass hot rolling, the hot rolling temperature is 800-1250 ℃, the single-pass rolling reduction is less than or equal to 25%, and the total rolling reduction is 30-90%.
As a preferable scheme of the preparation method of the high-strength and high-toughness low-density steel with the multi-stage nanostructure strengthening effect, the invention comprises the following steps: homogenizing, wherein the homogenizing treatment temperature is 1100-1250 ℃, and the homogenizing time is more than 30min; the homogenization treatment is performed under vacuum or a protective atmosphere, wherein the protective atmosphere is selected from one of argon, nitrogen or helium.
As a preferable scheme of the preparation method of the high-strength and high-toughness low-density steel with the multi-stage nanostructure strengthening effect, the invention comprises the following steps: the cold rolling adopts multi-pass cold rolling, the pass rolling reduction is less than or equal to 25 percent, and the total rolling reduction is 40 to 90 percent.
As a preferable scheme of the preparation method of the high-strength and high-toughness low-density steel with the multi-stage nanostructure strengthening effect, the invention comprises the following steps: the annealing is one of the first annealing and/or the second annealing;
wherein the first annealing temperature is 900-1100 ℃, and the heat preservation time is 5-300 min; the second annealing temperature is 550-650 ℃, and the heat preservation time is not less than 5min.
As a preferable scheme of the preparation method of the high-strength and high-toughness low-density steel with the multi-stage nanostructure strengthening effect, the invention comprises the following steps: the annealing is performed under vacuum or a protective atmosphere, wherein the protective atmosphere is selected from one of argon, nitrogen or helium.
Compared with the prior art, the invention has the following beneficial effects:
the invention has reasonable Mn, al and C contents, strictly controls the ratio of Mn/Al, (Mn+Al)/C and V/Nb, simultaneously controls the total amount of Nb and V, can form a multi-level coherent structure containing sub-nanometer (kappa phase), nanometer (kappa phase) and tens of nanometer (MC carbide) in the iron and steel material, and has the advantages of simple structure, low cost and low costThe rice structure reinforcement can make the alloy have extremely high strength, simultaneously maintain better toughness, and the density and cost of the steel material are lower, and the specific strength can reach 150-330 MPa cm 3 g -1 Can meet the requirement of high specific strength steel materials.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings that are needed in the description of the embodiments will be briefly described below, it being obvious that the drawings in the following description are only some embodiments of the present invention, and that other drawings may be obtained according to these drawings without inventive effort for a person skilled in the art. Wherein:
FIG. 1 is a graph of the scanning electron backscatter morphology of the high strength and toughness low density steel material provided in example 1 of the present invention;
FIG. 2 is a selected area electron diffraction pattern of the high strength and toughness low density steel material provided in example 1 of the present invention;
FIG. 3 is an atomic resolution high angle annular dark field diagram of the high strength and toughness low density steel material provided in example 1 of the present invention;
FIG. 4 is a graph of the transmitted dark field of (010) κ diffraction spots of the high strength and toughness low density steel material provided by example 1 of the present invention;
FIG. 5 is a drawing showing the tensile properties of the high strength and toughness low density steel material provided in example 1 of the present invention;
FIG. 6 is a graph of the scanning electron backscatter morphology of the high strength and toughness low density steel material provided in example 2 of the present invention;
FIG. 7 is a graph showing the profile of the high angle annular dark field image and the corresponding area of the high strength and toughness low density steel material provided in example 2 of the present invention;
FIG. 8 is an atomic resolution high angle annular dark field diagram of the high strength and toughness low density steel material provided in example 2 of the present invention;
FIG. 9 is a selected area electron diffraction pattern of the high strength and toughness low density steel material provided in example 2 of the present invention;
FIG. 10 is a graph of the transmitted dark field of (010) κ diffraction spots of the high strength and toughness low density steel material provided by example 2 of the present invention;
FIG. 11 is a drawing showing the tensile properties of the high strength and toughness low density steel material provided in example 2 of the present invention;
FIG. 12 is a graph of the scanning electron backscatter morphology of the high strength and toughness low density steel material provided in example 3 of the present invention;
FIG. 13 is a selected area electron diffraction pattern of the high strength and toughness low density steel material provided in example 3 of the present invention;
FIG. 14 is a graph of the transmitted dark field of (010) κ diffraction spots of the high strength and toughness low density steel material provided by example 3 of the present invention;
FIG. 15 is a drawing showing the tensile properties of the high strength and toughness low density steel material provided in example 3 of the present invention;
FIG. 16 is a drawing showing the tensile properties of the high strength and toughness low density steel material provided in example 4 of the present invention;
FIG. 17 is a drawing showing the tensile properties of the high strength and toughness low density steel material provided in comparative example 1 of the present invention.
FIG. 18 is a drawing showing the tensile properties of the high strength and toughness low density steel material provided in comparative example 2 of the present invention.
Detailed Description
In order that the above-recited objects, features and advantages of the present invention will become more apparent, a more particular description of the invention will be rendered by reference to specific embodiments thereof which are illustrated in the appended drawings.
In the following description, numerous specific details are set forth in order to provide a thorough understanding of the present invention, but the present invention may be practiced in other ways other than those described herein, and persons skilled in the art will readily appreciate that the present invention is not limited to the specific embodiments disclosed below.
Further, reference herein to "one embodiment" or "an embodiment" means that a particular feature, structure, or characteristic can be included in at least one implementation of the invention. The appearances of the phrase "in one embodiment" in various places in the specification are not necessarily all referring to the same embodiment, nor are separate or alternative embodiments mutually exclusive of other embodiments.
Unless otherwise indicated, all starting materials used in the examples were commercially available.
Example 1
(1) According to chemical formula Fe 50 Mn 30 Al 15 C 5 Compounding (atomic percent), wherein the raw materials are blocks corresponding to pure elements, and the purity is more than 99.9%;
(2) The prepared raw materials are smelted by induction, high-purity argon is firstly introduced into a furnace for gas washing, then the low vacuum is pumped to below 5 Pa, and then the high vacuum is pumped to 5 multiplied by 10 -3 Under Pa, finally, introducing high-purity argon of 5MPa as protective gas, smelting at 1600 ℃, preserving heat for 30min, and pouring to obtain an ingot;
(3) Carrying out multi-pass hot rolling treatment on the alloy ingot, wherein the hot rolling temperature is 900 ℃, the single rolling reduction is 10%, and the total rolling reduction is 50%;
(4) The alloy block after hot rolling was subjected to high-temperature homogenization treatment under vacuum (vacuum degree 10) -2 Pa), the temperature is 1200 ℃, the homogenization treatment time is 2 hours, and then water quenching is carried out;
(5) Carrying out multi-pass room temperature rolling on the alloy block subjected to high-temperature homogenization, wherein the rolling quantity of a single pass is 10%, and the total rolling quantity is 70%;
(6) Annealing the cold-rolled alloy sheet in vacuum (vacuum degree 10) -2 Pa), wherein the first annealing temperature is 900 ℃, the annealing time is 30min, the second annealing temperature is 600 ℃, and the annealing time is 40min, so that the high-strength and high-toughness low-density steel is obtained.
The morphology of the high-strength and high-toughness low-density steel obtained above was observed as shown in fig. 1 to 5. FIG. 1 is an electron backscatter scan of a high strength and toughness low density steel material having a uniform grain size and no significant grain boundary precipitation phase. FIG. 2 is a diffraction photograph of a transmission selective area of a high strength and toughness low density steel, from which it can be seen that the high strength and toughness steel material is of a single phase austenitic structure and has a coherent kappa-carbide precipitate phase. FIG. 3 is an atomic resolution high angle annular dark field plot of a high strength and toughness low density steel showing a coherent kappa-carbide precipitate phase. FIG. 4 is a graph of the transmitted dark field of a high strength and toughness low density steel, where the alloy is found to have a significant amount of nano-scale coherent kappa-carbides.
And (5) carrying out mechanical property test on the obtained high-strength and high-toughness low-density steel. The steel stress-strain curve obtained in example 1 is shown in fig. 5. As can be seen from FIG. 5, the high strength and toughness low density steel with multi-stage nanostructure strengthening effect obtained in this example has a yield strength of about 1063MPa, a tensile strength of about 1241MPa, a elongation after break of about 20% and a density of 6.7g/cm 3 The specific strength is 185MPa cm 3 g -1 。
Example 2
(1) According to chemical formula Fe 49 Mn 30 Al 15 C 5 V 0.8 Nb 0.2 Compounding (atomic percent), wherein the raw materials are blocks corresponding to pure elements, and the purity is more than 99.9%;
(2) The prepared raw materials are smelted by induction, high-purity argon is firstly introduced into a furnace for gas washing, then the low vacuum is pumped to below 5 Pa, and then the high vacuum is pumped to 5 multiplied by 10 -3 And finally, introducing high-purity argon of 5 megapascals as protective gas, keeping the smelting temperature at 1700 ℃, preserving the temperature for 15min, and casting under vacuum condition to obtain an alloy ingot;
(3) Carrying out multi-pass hot rolling treatment on the smelted alloy ingot, wherein the hot rolling temperature is 1000 ℃, the single rolling reduction is 15%, and the total rolling reduction is 60%;
(4) The alloy block after hot rolling was subjected to high temperature homogenization treatment under vacuum (vacuum degree 10) -2 Pa), the temperature is 1200 ℃, the homogenization treatment time is 4 hours, and then water quenching is carried out;
(5) Carrying out multi-pass room temperature rolling on the alloy block subjected to high-temperature homogenization, wherein the rolling quantity of a single pass is 15%, and the total rolling quantity is 60%;
(6) Annealing the cold-rolled alloy sheet in vacuum (vacuum degree 10) -2 Pa), wherein the first annealing temperature is 900 ℃, the annealing time is 5min, the second annealing temperature is 600 ℃, and the annealing time is 20min, so that the high-strength and high-toughness low-density steel is obtained.
The morphology of the high strength and toughness low density steel obtained above was observed as shown in fig. 6 to 11. FIG. 6 is an electron backscatter scan of a high strength and toughness low density steel, from which it can be seen that the material contains partially unrecrystallized regions where the grains are fine. FIG. 7 is a high angle annular dark field image of a high strength and toughness low density steel with MC-carbide precipitates of less than 20nm in size evident from the image. FIG. 8 is a view of an atomic resolution high angle annular dark field of a high strength and toughness low density steel, from which MC-carbides and austenitic matrices are evident. FIG. 9 is a diffraction photograph of a transmission selective area of a high strength and toughness low density steel, from which it can be seen that the high strength and toughness steel material is of a single phase austenitic structure and has a coherent kappa-carbide precipitate phase. FIG. 10 is a graph of the transmitted dark field of high strength and toughness low density steel. It was found that the alloy also had a large amount of nanoscale coherent kappa-carbides.
And (5) carrying out mechanical property test on the obtained high-strength and high-toughness low-density steel. The steel stress-strain curve obtained in example 2 is shown in fig. 11. As can be seen from FIG. 11, the high strength and toughness low density steel with multi-stage nanostructure strengthening effect obtained in this example has a yield strength of about 1423MPa, a tensile strength of about 1580MPa, a elongation after break of about 33% and a density of 6.8g/cm 3 Specific strength of 232MPa cm 3 g -1 。
Example 3
(1) According to chemical formula Fe 50 Mn 30 Al 15 C 5 Compounding (atomic percent), wherein the raw materials are blocks corresponding to pure elements, and the purity is more than 99.9%;
(2) The prepared raw materials are smelted by induction, high-purity argon is firstly introduced into a furnace for gas washing, then the low vacuum is pumped to below 5 Pa, and then the high vacuum is pumped to 5 multiplied by 10 -3 Under Pa, finally introducing high-purity argon of 5MPa as protective gas, smelting at 1600 ℃, preserving heat for 10min, and casting Cheng Ge gold ingots;
(3) Carrying out multi-pass hot rolling treatment on the smelted alloy ingot, wherein the hot rolling temperature is 950 ℃, the single rolling reduction is 10%, and the total rolling reduction is 50%;
(4) The alloy block after hot rolling was subjected to high-temperature homogenization treatment under vacuum (vacuum degree 10) -2 Pa), the temperature is 1200 ℃, the homogenization treatment time is 3 hours, and then water quenching is carried out;
(5) Will be cooledThe rolled alloy sheet was annealed under vacuum (vacuum degree 10) -2 Pa), carrying out multi-pass room temperature cold rolling on the alloy block subjected to high temperature homogenization, wherein the single-pass rolling reduction is 20%, and the total rolling reduction is 70%;
(6) Annealing the cold-rolled alloy sheet in vacuum (vacuum degree 10) -2 Pa), wherein the first annealing temperature is 900 ℃, the annealing time is 3min, the second annealing temperature is 600 ℃, and the annealing time is 40min, so that the high-strength and high-toughness low-density steel is obtained.
The morphology of the high strength and toughness low density steel obtained above was observed as shown in fig. 12 to 15. FIG. 12 is an electron backscatter scan of a high strength and toughness low density steel, from which it can be seen that the material has a uniform grain size without significant grain boundary precipitation phases. FIG. 13 is a diffraction photograph of a transmission selective area of a high strength and toughness low density steel, from which it can be seen that the high strength and toughness steel material is of a single phase austenitic structure and has a coherent kappa-carbide precipitate phase. FIG. 14 is a graph of the transmitted dark field of high strength and toughness low density steel. It was found that the alloy also had a large amount of nanoscale coherent kappa-carbides.
And (5) carrying out mechanical property test on the obtained high-strength and high-toughness low-density steel. The steel stress-strain curve obtained in example 2 is shown in fig. 15. As can be seen from FIG. 15, the high strength and toughness low density steel with multi-stage nanostructure strengthening effect obtained in this example has a yield strength of about 1094MPa, a tensile strength of about 1324MPa, a elongation after break of about 53% and a density of 6.7g/cm 3 The specific strength is 198MPa cm 3 g -1 。
Example 4
(1) According to chemical formula Fe 49 Mn 30 Al 15 C 5 V 0.8 Nb 0.2 Preparing raw materials, wherein the raw materials are blocks corresponding to all pure elements, the purity is greater than 99.9%, and the purity of carbon is greater than 99.9% by adopting graphite;
(2) Smelting the prepared raw materials in a copper crucible by adopting an arc furnace, firstly introducing high-purity argon into the crucible for gas washing, then pumping low vacuum to below 5 Pa, and then pumping high vacuum to 5X 10 -3 Under Pa, finally introducing high-purity argon gas of 5MPa asThe protective gas is smelted at 1700 ℃, the temperature is kept for 15min, and the smelting is repeated for 5 times to obtain a smelted alloy ingot;
(3) Carrying out multi-pass hot rolling treatment on the alloy, wherein the hot rolling temperature is 900 ℃, the single rolling reduction is 10%, and the total rolling reduction is 50%;
(4) The alloy block after hot rolling was subjected to high-temperature homogenization treatment under vacuum (vacuum degree 10) -2 Pa), the temperature is 1200 ℃, the homogenization treatment time is 2 hours, and then water quenching is carried out;
(5) Carrying out multi-pass room temperature rolling on the alloy block subjected to high-temperature homogenization, wherein the rolling quantity of a single pass is 15%, and the total rolling quantity is 75%;
(6) The alloy sheet after cold rolling was annealed under vacuum (vacuum degree 10) -2 Pa), the annealing temperature is 600 ℃, the annealing time is 40min, and the high-strength and high-toughness metastable multicomponent alloy material with precipitation strengthening effect is obtained.
And (5) carrying out mechanical property test on the obtained high-strength and high-toughness metastable multicomponent alloy material. The stress-strain curves of the high strength and toughness metastable multicomponent alloy material obtained in example 4 are shown in fig. 16. As can be seen from FIG. 16, the high strength and toughness low density steel with multi-stage nanostructure strengthening effect obtained in this example has a yield strength of about 2165MPa, a tensile strength of about 2248MPa, a elongation after break of about 3.7% and a density of 6.8g/cm 3 Specific strength of 330MPa cm 3 g -1 。
Comparative example 1
According to Materials Letters [ citation Materials Letters: G.F.Zhang., H.Y.Shi., S.T.Wang., Y.H.Tang., X.Y.Zhang., Q.Jing., R.P.Liu., ultrahigh strength and high ductility lightweight steel achieved by dual nanoprecipitate strengthening and dynamic slip refinishent.materials Letters,2023.330:133366 ]]After casting Fe-25Mn-10Al-1.2C-0.4V (mass ratio), annealing is carried out after hot forging (1120-1145 ℃) and hot rolling (1050 ℃, 85%) and cold rolling (60%), the annealing comprises 2h at 1050 ℃ and 2h at 600 ℃, and the mechanical property test is carried out on the prepared low-density steel, as shown in figure 18, the yield strength is 1216MPa, the tensile strength is 1356MPa, and the elongation is 28%. Density of about 6.5g/cm 3 Specific strength of 208MPa cm 3 g -1 。
Comparative example 2
The highest strength low density steels described in Science Advances [ cited Science Advances: Z.W., L.W., Z.H., C.H., liebscher., J.He., D.Ponge., D.Raabe., and L.Z, ultrastrong lightweight compositionally complex steels via dual-nanoprediction.science Advances,2020.6:9543]，Fe 48 Mn 26 Al 16 C 5 Ni 5 The tensile strength after homogenization (1200 ℃,1 h), hot rolling (1100 ℃), cold rolling (60% of total rolling reduction), annealing (800 ℃,3 min) is 1700MPa, the elongation is 13% and the density is 6.5g/cm 3 The specific strength is 260MPa cm 3 g -1 The stress strain curve of the alloy material is shown in fig. 17.
As can be seen from comparing examples 1, 2, 3 and 4 with comparative example 1, the low density steels outside the range of the composition of the present invention have much lower properties than the low density steel materials of the present invention on the basis of the same or similar processing techniques. As is apparent from the comparison of examples 1, 2, 3 and 4 with comparative example 2, the optimal properties of the alloy of the present invention are improved by 548MPa over the tensile strength of the prior alloy, and the density of the alloy of the present invention is 6.7 to 6.8g/cm 3 The specific strength can reach 330MPa cm at the highest 3 g -1 . The invention does not contain noble elements Cr, ni and the like, and has lower comprehensive cost. The high-strength and high-toughness low-density steel has the advantage that the alloy has a multi-level nano structure from sub-nanometer to nanometer, and the multi-scale nano structure greatly improves the strength and toughness of the material.
In addition, the alloy casting blank is hot rolled, so that defects (such as micropores, microcracks and the like) generated in the alloy during smelting and casting can be effectively eliminated, and the comprehensive performance of the alloy is improved; the invention can control the multi-scale nano structure, grain size and the like of the alloy by adjusting the annealing process parameters, thereby adjusting the mechanical property and improving the strength of the alloy on the premise of ensuring the good plasticity of the alloy.
The invention has reasonable Mn, al and C contents, strictly controls the ratio of Mn/Al, (Mn+Al)/C and V/Nb, simultaneously controls the total amount of Nb and V, can form a multi-level coherent structure containing sub-nano (kappa' phase), nano (kappa phase) and tens of nano (MC carbide) in the steel material, can realize extremely high strength of the alloy through the multi-level nano structure reinforcement, simultaneously keeps better toughness, has lower density and cost, and can meet the requirement of the steel material with high specific strength.
It should be noted that the above embodiments are only for illustrating the technical solution of the present invention and not for limiting the same, and although the present invention has been described in detail with reference to the preferred embodiments, it should be understood by those skilled in the art that the technical solution of the present invention may be modified or substituted without departing from the spirit and scope of the technical solution of the present invention, which is intended to be covered in the scope of the claims of the present invention.
Claims (10)
1. A high-strength and high-toughness low-density steel with a multi-stage nanostructure strengthening effect is characterized in that: comprises the following components in atom percent: 25 to 32 percent of Mn, 12 to 18 percent of Al, 3.0 to 7.0 percent of C, 0 to or less than or equal to Nb and 0.2 percent, 0 to or less than or equal to V and 0.8 percent, and the balance of Fe and unavoidable impurities;
wherein, according to the atomic percentage, mn/Al is more than or equal to 1.0, (Mn+Al)/C is more than or equal to 30, (Nb+V) is less than or equal to 1.0 percent and V/Nb is more than or equal to 4.
2. The high strength and toughness low density steel having multi-stage nanostructured reinforcing effect according to claim 1, wherein: the high-strength and high-toughness low-density steel internally forms a multi-stage coherent structure containing sub-nano-scale kappa phase, nano-scale kappa phase and tens of nano-scale MC carbide.
3. The high strength and toughness low density steel having multi-stage nanostructure strengthening effect according to claim 1 or 2, characterized in that: the alloy has the following characteristics:
(i) Yield strength is 800-2000 MPa;
(ii) Tensile strength is 1000-2248 MPa;
(iii) The elongation after fracture is 3-70%;
(iv) The specific strength is 150-330 MPa cm 3 g -1 。
4. A method for producing a high strength and toughness low density steel having a multi-stage nanostructure strengthening effect as set forth in any one of claims 1 to 3, characterized in that: comprising the steps of (a) a step of,
the components are prepared according to the atomic ratio, and are smelted under the protection of vacuum or inert gas, cast into a casting blank, and the casting blank is subjected to hot rolling, homogenization, cold rolling and annealing treatment to obtain the high-strength and high-toughness low-density steel with the multi-stage nanostructure strengthening effect.
5. The method for preparing high-strength and high-toughness low-density steel with multi-stage nanostructure strengthening effect according to claim 4, wherein the method comprises the following steps: the smelting is carried out at 1450-2200 ℃ for more than 0.1 hour; the smelting is carried out by maintaining the vacuum degree in the furnace below 1 Pa or maintaining the inert gas pressure in the furnace below 100 MPa.
6. The method for preparing high-strength and high-toughness low-density steel with multi-stage nanostructure strengthening effect according to claim 4, wherein the method comprises the following steps: the hot rolling adopts multi-pass hot rolling, the hot rolling temperature is 800-1250 ℃, the single-pass rolling reduction is less than or equal to 25%, and the total rolling reduction is 30-90%.
7. The method for preparing high-strength and high-toughness low-density steel with multi-stage nanostructure strengthening effect according to claim 4, wherein the method comprises the following steps: homogenizing, wherein the homogenizing treatment temperature is 1100-1250 ℃, and the homogenizing time is more than 30min; the homogenization treatment is performed under vacuum or a protective atmosphere, wherein the protective atmosphere is selected from one of argon, nitrogen or helium.
8. The method for preparing high-strength and high-toughness low-density steel with multi-stage nanostructure strengthening effect according to claim 4, wherein the method comprises the following steps: the cold rolling adopts multi-pass cold rolling, the pass rolling reduction is less than or equal to 25 percent, and the total rolling reduction is 40 to 90 percent.
9. The method for preparing high-strength and high-toughness low-density steel with multi-stage nanostructure strengthening effect according to any one of claims 4 to 8, characterized in that: the annealing is one of the first annealing and/or the second annealing;
wherein the first annealing temperature is 900-1100 ℃, and the heat preservation time is 5-300 min; the second annealing temperature is 550-650 ℃, and the heat preservation time is not less than 5min.
10. The method for preparing high-strength and high-toughness low-density steel with multi-stage nanostructure strengthening effect according to claim 9, wherein the method comprises the following steps: the annealing is performed under vacuum or a protective atmosphere, wherein the protective atmosphere is selected from one of argon, nitrogen or helium.
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