CN114561517A - Low-density high-ductility steel and preparation method and application thereof - Google Patents

Low-density high-ductility steel and preparation method and application thereof Download PDF

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CN114561517A
CN114561517A CN202210436540.9A CN202210436540A CN114561517A CN 114561517 A CN114561517 A CN 114561517A CN 202210436540 A CN202210436540 A CN 202210436540A CN 114561517 A CN114561517 A CN 114561517A
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CN114561517B (en
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刘日平
王青峰
张新宇
罗宝健
谢东
田野
毛忆瑄
王锁涛
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Yanshan University
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    • 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
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    • 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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    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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Abstract

The invention provides low-density high-ductility and toughness steel and a preparation method and application thereof, belonging to the technical field of austenitic stainless steel. According to the invention, Nb and Ti are added compositely, precipitation of grain boundary carbides is inhibited by generating (Nb, Ti) (C, N), and lightweight elements of Al, C, Si and Mn and strengthening elements of Cr, Cu and N are reasonably prepared, so that the density of steel is effectively reduced, the test steel is ensured to have higher strength, and plasticity and toughness are taken into consideration, so that the steel has good comprehensive mechanical properties. Meanwhile, the Nb and Ti elements are added to improve the precipitation condition of grain boundary carbide and promote the matching of the strength and the ductility and the toughness of the low-density high-strength austenitic steel.

Description

Low-density high-ductility steel and preparation method and application thereof
Technical Field
The invention relates to the technical field of austenitic stainless steel, in particular to low-density high-ductility and toughness steel and a preparation method and application thereof.
Background
With the rapid development of social economy, steel materials are one of the most important structural materials, and the problem of ecological environment pollution caused by overhigh energy consumption is increasingly serious. The solution is that on one hand, clean energy is adopted to replace fuel power, and on the other hand, the fuel consumption and pollution are reduced by reducing the weight of the traffic carrying equipment, so that the light weight of the traffic carrying equipment and structural parts is an important measure for energy conservation and environmental protection. Therefore, the Fe-Mn-Al-C series low-density steel mainly reduces the steel density through light-weight elements such as Al and C, and has higher cost advantage compared with light metals such as aluminum, magnesium and titanium, alloy materials and composite materials thereof. When Al and C contents are excessively added, a kappa carbide precipitate phase is generated in the Fe-Mn-Al-C system low density steel. The alloy obviously improves the yield strength of steel when being dispersed and distributed, and has adverse effect on the plastic toughness of steel when being distributed in a crystal boundary.
The invention patent CN104711494B discloses a low-density high-plasticity NiAl reinforced ultrahigh-strength steel and a preparation method thereof, the alloy comprises the following chemical components by weight percent: 0.5-1.5% of C, 15-25% of Mn, 7-10% of Al, 5-15% of Ni, 0-5% of Cr, 0-0.2% of Nb, and the balance of Fe and other inevitable impurity elements. The low-density high-strength steel has the advantages that a large amount of Ni and Al are added to generate NiAl intermetallic compounds, the contribution of Al to density is reduced, so that the density is high, the NiAl phase has high magnetism, the NiAl phase and kappa carbide which are not controlled in precipitation form influence the impact toughness, the yield ratio is 0.89-0.95, the elongation is only 10% -20%, and the impact power is low.
The Chinese invention patent CN 112899579A discloses a corrosion-resistant high-strength light steel and a preparation method thereof, and the corrosion-resistant high-strength light steel comprises the following components by mass percent: 1.4-1.7% of C, 25-30% of Mn, 10-12% of Al, 3-5% of Cr, 0.05-0.1% of Nb, less than or equal to 0.03% of S, less than or equal to 0.03% of P, and the balance of Fe and inevitable impurities. Although the Al content is high and the density is low, the C, Al is too high, so that a delta phase and a brittle phase along with crystal kappa are easily formed, and the plasticity and the impact property are insufficient.
Therefore, the steel material integrating multiple performances such as light weight, high ductility and toughness, low magnetism and the like is obtained, and the application prospect is wide.
Disclosure of Invention
The invention aims to provide low-density high-ductility and toughness steel and a preparation method and application thereof, and solves the problem that the existing austenitic steel is difficult to give consideration to low density, high strength and low magnetic property.
In order to achieve the above object, the present invention provides the following technical solutions:
the invention provides low-density high-plasticity and toughness steel which comprises the following chemical components in percentage by mass: 29-33% of Mn, 10.70-11.30% of Al, 1.15-1.19% of C, 0.01-0.20% of Si, 4.00-5.90% of Cr, 0.50-1.20% of Cu, 0.01-0.30% of Nb, 0.01-0.30% of Ti, 0.05-0.10% of N, less than or equal to 0.012% of P, less than or equal to 0.003% of S, and the balance of Fe and inevitable impurities; meanwhile, the mass percentage of Mn, Al, C, Nb and Ti satisfies 0.0098Al +0.208(C- (Nb + Ti)/5) +0.0054Mn-0.6 < 0; and the mass percentage of Al and C satisfies 105Al +356C multiplied by C-700 > 800.
The invention provides a preparation method of low-density high-ductility steel, which comprises the following steps:
mixing the raw materials corresponding to the low-density high-ductility and toughness steel, and sequentially smelting and pouring to obtain an ingot;
carrying out temperature control rolling on the cast ingot to obtain a rolled piece;
and sequentially carrying out quenching treatment, solid solution treatment and low-temperature aging treatment on the rolled piece to obtain the low-density high-ductility and toughness steel.
Preferably, the casting temperature is 1380-1500 ℃; and after the casting, cooling the obtained casting at a cooling speed of 5-8 ℃/h.
Preferably, before the temperature-controlled rolling, the cast ingot is heated to 1150-1190 ℃ at a heating rate of 25-35 ℃/h and is kept warm for more than 4 h; the temperature-controlled rolling conditions comprise: the initial rolling temperature is 1120-1140 ℃, rolling is carried out by using pass reduction of 6-20 mm, and the final rolling temperature is more than or equal to 1000 ℃.
Preferably, the quenching treatment conditions include: the cooling speed is more than or equal to 25 ℃/s, the water inlet temperature is more than or equal to 980 ℃, and the final cooling temperature is less than or equal to 100 ℃.
Preferably, the temperature of the solution treatment is 940-1100 ℃, and the heat preservation time is 1-5 h; and after the solid solution treatment is finished, cooling the obtained solid solution piece to room temperature by water at the water cooling speed of 15-50 ℃/s.
Preferably, the temperature of the low-temperature aging treatment is 450-550 ℃, and the heat preservation time is 3-6 h.
Preferably, after obtaining the ingot, the method further comprises: heating the cast ingot to 1110-1150 ℃ at a heating rate of 20-25 ℃/h, and preserving heat; the heat preservation time is more than or equal to 10 hours, and forging forming is carried out; the forging forming comprises shaping, widening, drawing and shaping which are sequentially carried out; the final forging temperature is more than or equal to 970 ℃.
Preferably, in the forging forming process, when the temperature of the forge piece is reduced to 950 ℃, the forge piece is returned to the furnace and heated to 1110-1150 ℃, and heat preservation is carried out, wherein the heat preservation time is more than or equal to 1 h.
The invention provides application of the low-density high-ductility and toughness steel in the technical scheme or the low-density high-ductility and toughness steel prepared by the preparation method in the technical scheme in high-toughness or nonmagnetic traffic carrying equipment.
The invention provides a low-density high-ductility steel, which is characterized in that Nb and Ti elements are added compositely, precipitation of grain boundary carbides is inhibited by generating (Nb, Ti) (C, N), lightweight Al, C, Si and Mn elements and strengthening Cr, Cu and N elements are reasonably allocated, the density of the steel is effectively reduced, high strength of the test steel is ensured, ductility and toughness are considered, and the steel has good comprehensive mechanical properties. Meanwhile, the Nb and Ti elements are added to improve the precipitation condition of grain boundary carbide and promote the matching of the strength and the ductility and the toughness of the low-density high-strength austenitic steel. The density rho of the steel obtained by the invention is less than or equal to 6.55g/cm3Relative magnetic permeability murLess than or equal to 1.150, yield strength ReLNot less than 830MPa, tensile strength Rm980MPa or more and elongation A5≥40％，-40℃KV2≥60J。
The invention provides a preparation method of the low-density high-plasticity and toughness steel, which adopts ingot smelting, temperature-controlled rolling, on-line quenching, off-line solid solution and low-temperature aging treatment; can generate (Nb, Ti) (C, N) to inhibit precipitation of grain boundary carbide, and can adjust and control the processing technology to obtain the novel high-strength high-toughness low-magnetism light austenitic steel with uniform tissue.
Furthermore, after the low-density austenitic steel is subjected to ingot casting, forging forming, temperature-controlled rolling, direct quenching and off-line solid solution, the size and the form of austenite grains are improved, grain boundary kappa carbide precipitation is inhibited and the like through long-time low-temperature aging treatment, the comprehensive mechanical property is ensured, and the low-density austenitic steel is suitable for being applied to important fields such as military and civil structural steel with high requirements on fracture and has a good application prospect.
Drawings
FIG. 1 is an SEM image of impact fracture of a low-density high-ductility steel prepared in example 2;
fig. 2 is an SEM image of the low density high ductility and toughness steel prepared in example 5.
Detailed Description
The invention provides low-density high-plasticity and toughness steel which comprises the following chemical components in percentage by mass: 29-33% of Mn, 10.70-11.30% of Al, 1.15-1.19% of C, 0.01-0.20% of Si, 4.00-5.90% of Cr, 0.50-1.20% of Cu, 0.01-0.30% of Nb, 0.01-0.30% of Ti, 0.05-0.10% of N, less than or equal to 0.012% of P, less than or equal to 0.003% of S, and the balance of Fe and inevitable impurities; meanwhile, the mass percentage of Mn, Al, C, Nb and Ti satisfies 0.0098Al +0.208(C- (Nb + Ti)/5) +0.0054Mn-0.6 < 0; and the mass percentage of Al and C satisfies 105Al +356 CxC-700 > 800.
In the present invention, unless otherwise specified, all the starting materials required for the preparation are commercially available products well known to those skilled in the art.
The low-density high-ductility and toughness steel comprises 29-33% of Mn, preferably 30-32% of Mn, and further preferably 31% of Mn in percentage by mass. Mn is an austenite stabilizing element, and can enlarge an austenite phase region, reduce a ferrite phase region, and suppress a kappa brittle phase. Meanwhile, Mn plays a role in solid solution strengthening, and correspondingly improves the work hardening rate of the steel. The higher Mn content is beneficial to obtaining a single-phase austenite structure, thereby improving the plasticity and toughness of the steel. The Mn content of the steel is limited to 29-33%, the increase of the Mn content is avoided, the crystal grains of the steel are coarsened, the thermal conductivity is rapidly reduced, the coefficient of linear expansion is increased, large internal stress is formed during working heating or cooling, the cracking tendency is remarkably increased, and the hot workability is deteriorated.
The low-density high-ductility and toughness steel provided by the invention comprises 10.70-11.30% of Al by mass percentage, and preferably 10.9-11.2%. Al remarkably reduces the density of steel, and the density is reduced by 0.101g/cm per 1 percent of Al3The density rho is less than or equal to 6.5g/cm3More than 11.4 percent of Al is required to be added, and meanwhile, the corrosion resistance and the strength of the steel are obviously improved by the Al. The invention limits the Al content to 11.40-11.90%, avoids the reduction of austenite interval caused by excessive ferrite forming element Al content, and promotes the brittleness of delta and kappaAnd phase, ductility and toughness are reduced.
The low-density high-plasticity and toughness steel comprises, by mass, 1.15-1.19% of C, and preferably 1.16-1.18%. C is a very obvious austenite stabilizing and solid solution strengthening element, the content of C is improved, the structure of the austenite dual-phase steel can be regulated and controlled, and the strength is improved. The content of C is limited to 1.09-1.14%, and excessive C, Mn and Al are prevented from forming a brittle phase along with crystal kappa, so that the ductility and toughness of steel are not facilitated.
The low-density high-ductility and toughness steel comprises, by mass, 0.01-0.20% of Si, preferably 0.05-0.15%, and more preferably 0.1%. Si is an effective deoxidizing element and a solid solution strengthening element, improves the content of Si, can reduce oxide inclusions in steel, correspondingly lightens pitting corrosion, and simultaneously improves the strength. According to the invention, the Si content is limited to 0.70-1.00%, so that the solubility of excessive Si in austenite is prevented from being reduced, the quantity of delta phase and kappa carbide is increased, and the impact toughness is correspondingly reduced.
The low-density high-plasticity and toughness steel provided by the invention comprises, by mass, 4.00-5.90% of Cr4.00, preferably 4.5-5.8%, and further preferably 4.9-5.3%. Cr: during solution treatment, most Cr is dissolved into austenite, so that the stability of steel is improved, perimorphic kappa carbides are inhibited during cooling, and the ductility and toughness can be improved by increasing the Cr content. The invention limits the Cr content to 2.00-3.90%, and avoids excessive Cr from increasing the network carbide separated along the crystal, thereby reducing the impact toughness and the plastic toughness.
The low-density high-ductility and toughness steel provided by the invention comprises 0.50-1.20% of Cu by mass percentage, and preferably 0.6-1.1%. The Cu has the effect of improving the corrosion resistance similar to Ni, the content of the Cu is limited to 0.50-1.20%, excessive Cu and Al are prevented from forming a B2 phase of CuAl, and the ductility and toughness of the steel are reduced.
The low-density high-ductility and toughness steel provided by the invention comprises 0.01-0.30% of Nb by mass percentage, and preferably 0.2%. Nb is a strong carbide forming element, and is easy to form fine Nb (C, N) at high temperature, so that crystal grain boundaries can be effectively pinned to refine grains, and kappa carbide precipitation is inhibited, thereby being beneficial to improving the ductility and toughness. The content of Nb is limited to 0.01-0.30%, and the phenomenon that too much Nb increases network carbide precipitated along the crystal is avoided, and the impact toughness and the plastic toughness are reduced.
The low-density high-ductility and toughness steel provided by the invention comprises 0.01-0.30% of Ti by mass percentage, and preferably 0.2%. Ti has strong affinity with C, and strong carbide forming elements have refining and strengthening effects, and the over-high precipitation strengthening content reduces the diffusion rate of C in austenite and the content of C in austenite, so that the stability of the machine body is reduced. Therefore, the mass percentage content of Ti is set to be 0.01-0.30%.
The low-density high-ductility and toughness steel provided by the invention comprises 0.05-0.10% of N, preferably 0.06-0.09%, and more preferably 0.07% of N in percentage by mass. N is a gamma-forming element and manganese is not very effective for forming austenite, but the addition of manganese allows more nitrogen, which is a very strong austenite-forming element, to be dissolved into stainless steel. The effects of N element interstitial solid solution strengthening and austenite structure stabilizing are much larger than that of carbon, so that the strength of the steel is greatly improved, and good ductility and toughness are maintained. The mass percentage content of N is set to be 0.05-0.10%, and AlN inclusions generated by excessive N elements are avoided, so that the performance is not improved.
The low-density high-ductility steel provided by the invention comprises, by mass, not more than 0.012% of P, not more than 0.003% of S, and the balance of Fe and inevitable impurities. P is a harmful element in the steel, and the high carbon content of the steel reduces the solubility of P in austenite, easily separates out film-shaped phosphide along crystallization, causes workpiece hot cracking and reduces the ductility and toughness of the steel. Therefore, the content of P is controlled to be less than or equal to 0.012 percent in the invention. S is easy to form MnS inclusion, the hot brittleness is increased, and the ductility and toughness are reduced, and the content of S in the steel is controlled to be less than or equal to 0.003 percent.
The invention provides a preparation method of low-density high-ductility steel, which comprises the following steps:
mixing the raw materials corresponding to the low-density high-ductility steel, and sequentially smelting and pouring to obtain an ingot;
carrying out temperature control rolling on the cast ingot to obtain a rolled piece;
and sequentially carrying out quenching treatment, solid solution treatment and low-temperature aging treatment on the rolled piece to obtain the low-density high-ductility and toughness steel.
The method mixes the raw materials corresponding to the low-density high-plasticity and toughness steel, and sequentially performs smelting and pouring to obtain the ingot. The invention has no special limitation on the specific types of the raw materials, and the raw materials are selected according to the raw materials well known in the field; in the embodiment of the invention, the manganese metal (the purity is more than or equal to 95.0 percent), the aluminum beans (the content is more than or equal to 99.0 percent), the recarburizer (the C content is 98.5 to 99.0 percent) and the industrial pure iron (the purity is 99.99 percent) are concretely mentioned.
In the invention, the smelting is preferably carried out by adopting a vacuum induction furnace smelting method or an electric arc furnace-refining furnace-vacuum degassing furnace triple method smelting method, the refining time of the refining furnace is preferably more than or equal to 30min, and the vacuum degassing time of the vacuum degassing furnace is preferably 10-30 min.
The specific process of the smelting is not particularly limited in the invention, and the smelting can be carried out according to the process well known in the field. In the embodiment of the invention, the raw materials required by corresponding proportion are placed in a magnesia crucible of a vacuum induction melting furnace, and the vacuum degree in the furnace is reduced to (1.7-2) x 10-2Pa, more preferably (1.8 to 1.9). times.10-2Pa, after the high-purity iron is completely melted, filling high-purity argon as protective gas to (3-3.2) x 104Pa, more preferably 3.1X 104And Pa, stirring in the smelting process, and smelting to obtain molten steel.
In the invention, the casting temperature is preferably 1380-1500 ℃, more preferably 1420-1446 ℃, and further preferably 1430-1441 ℃; the invention preferably performs inert gas protection pouring at the same time of die casting. After the casting is finished, the casting is preferably kept stand for 1h, then the casting is cooled to room temperature, and the casting ingot is obtained after demolding; the cooling speed is preferably 5-8 ℃/h, and more preferably 6-7 ℃/h. The mold used for the casting is not particularly limited in the present invention, and any corresponding mold known in the art may be used.
After the ingot is obtained, the temperature-controlled rolling is directly carried out after dead heads of the ingot are cut off, or the temperature-controlled rolling is carried out after the ingot is forged and formed.
When the ingot is forged and formed and then is subjected to temperature-controlled rolling, the ingot is heated to 1110-1150 ℃ at a heating rate of 20-25 ℃/h, and then is forged and formed after heat preservation; the heat preservation time is preferably not less than 10 hours, and more preferably 14-16 hours; the invention keeps the temperature until the cast ingot is fully homogenized, and then carries out forging forming.
In the present invention, the forging preferably includes shaping, widening, drawing, and shaping in this order; the initial forging temperature is preferably 1080-1110 ℃; the final forging temperature is preferably not less than 970 ℃, and more preferably 976-983 ℃; in the forging forming process, when the temperature of the forge piece is reduced to 950-965 ℃, returning to the furnace and heating to 1110-1150 ℃, more preferably 1120-1140 ℃, and carrying out heat preservation until the forge piece is forged into a plate-shaped blank suitable for rolling, wherein the heat preservation time is more than or equal to 1 h. The judgment criteria for the slab material suitable for rolling are not particularly limited in the present invention, and the slab material may be judged according to a procedure well known in the art.
After the forging forming is finished, the obtained plate blank is preferably slowly cooled to room temperature, and the temperature-controlled rolling is carried out after a dead head of the obtained forging blank is cut off. The process of the present invention for the slow cooling to room temperature is not particularly limited, and may be performed according to a process known in the art.
In the present invention, the temperature controlled rolling process preferably comprises: heating to 1150-1190 ℃ at a heating rate of 25-35 ℃/h, preserving heat for more than 4h, discharging the test piece after the test piece is completely uniform, rolling, wherein the initial rolling temperature is preferably 1120-1140 ℃, rolling is performed at a pass reduction of 6-20 mm, and the final rolling temperature is preferably not less than 1000 ℃. In the invention, the heating speed is more preferably 29-33 ℃/h, and more preferably 30 ℃/h; the heating temperature is preferably 1160-1180 ℃, more preferably 1170 ℃, and the initial rolling temperature is preferably 1120-1130 ℃; the pass reduction is preferably 10-18 mm, more preferably 12-16 mm, and the final rolling temperature is preferably 1020-1044 ℃, more preferably 1030-1040 ℃.
After the rolled piece is obtained, the invention sequentially carries out quenching treatment, solid solution treatment and low-temperature aging treatment on the rolled piece to obtain the low-density high-plasticity and toughness steel.
In the present invention, the quenching treatment is preferably an on-line quenching treatment; the invention preferably sends the rolled piece directly into laminar flow water or a water tank for quenching treatment; the conditions of the quenching treatment preferably include: the cooling speed is more than or equal to 25 ℃/s, more preferably 26-30 ℃/s, the water inlet temperature is more than or equal to 980 ℃, preferably 984-992 ℃, more preferably 985-990 ℃, the final cooling temperature is less than or equal to 100 ℃, more preferably 44-68 ℃, and more preferably 50-53 ℃.
In the invention, the temperature of the solution treatment is preferably 940-1100 ℃, more preferably 1050-1000 ℃, and the heat preservation time is preferably 1-5 h, more preferably 2-4 h, and further preferably 2.5-3 h; after the solution treatment is finished, cooling the obtained solid solution piece to room temperature by water, wherein the water cooling speed is preferably 15-50 ℃/s, more preferably 23-42 ℃, and further preferably 25 ℃.
In the invention, the temperature of the low-temperature aging treatment is preferably 450-550 ℃, more preferably 480-500 ℃, and the heat preservation time is preferably 3-6 hours, more preferably 4-5 hours. After the low-temperature aging treatment is finished, the steel is preferably cooled to room temperature by air, and the low-density high-plasticity and toughness steel is obtained.
The invention provides application of the low-density high-ductility and toughness steel in the technical scheme or the low-density high-ductility and toughness steel prepared by the preparation method in the technical scheme in high-toughness or nonmagnetic traffic carrying equipment. The method of the present invention is not particularly limited, and the method may be applied according to a method known in the art.
The technical solution of the present invention will be clearly and completely described below with reference to the embodiments of the present invention. It is to be understood that the described embodiments are merely exemplary of the invention, and not restrictive of the full scope of the invention. All other embodiments, which can be obtained by a person skilled in the art without making any creative effort based on the embodiments in the present invention, belong to the protection scope of the present invention.
Examples 1 to 5
The method comprises the steps of selecting metal manganese (the purity is more than or equal to 95.0%), aluminum beans (the content is more than or equal to 99.0%), a carburant (the content of C is 98.5% -99.0%) and industrial pure iron (the purity is 99.99%) as raw materials, and batching and smelting test steel according to the components in the following table 1 to serve as examples 1-5.
In the component design of examples 1-5, to ensure the density index, the weight percentage values of Mn, Al and C all satisfy 8.15-0.101Al-0.41C-0.0085Mn < 6.61; for controlling kappa carbide, the weight percentage values of Al, C, V, Nb and Mn all satisfy 0.0098Al +0.208(C- (Nb + V)/5) +0.0054Mn-0.6 < 0.
TABLE 1 Components of examples 1-5 and comparative examples 1-3
Composition (A) Mn Al C Si Cr Cu Nb Ti N P S Fe
Example 1 30 10.9 1.18 0.1 4.5 0.1 0.2 0.3 0.07 0.010 0.002 Balance of
Example 2 29 11.2 1.15 0.05 4 1 0.1 0.1 0.06 0.007 0.002 Balance of
Example 3 32 10.7 1.17 0.1 4.9 0.6 0.2 0.3 0.06 0.012 0.001 Allowance of
Example 4 31 10.9 1.16 0.15 5.3 1.1 0.1 0.2 0.07 0.011 0.001 Balance of
Example 5 31 11 1.15 0.19 5.8 1.1 0.3 0.2 0.09 0.008 0.003 Allowance of
Comparative example 1 30 10 1 0.1 4 0.1 0.2 0.010 0.002 Allowance of
Comparative example 2 28 10 0.9 4 0.008 0.002 Balance of
Comparative example 3 32 8 1 0.15 3 0.2 0.1 0.07 0.010 0.001 Allowance of
Example 1
According to the components of the example 1 in the table 1, the raw materials required by the corresponding proportion are placed into a magnesia crucible of a vacuum induction melting furnace, and the vacuum degree in the furnace is reduced to 2 multiplied by 10-2Pa, filling high-purity argon as protective gas to 3 x 10 after completely melting high-purity iron4Pa, stirring in the smelting process, and smelting to obtain molten steel. Injecting the obtained molten steel into a cast iron mold, casting the molten steel at the casting temperature of 1420 ℃, performing inert gas protection casting while die casting, discharging the molten steel from the furnace for 1h after casting, cooling the molten steel to room temperature at the speed of 8 ℃/h, and demolding to obtain a steel ingot;
temperature control rolling: heating the steel ingot to 1180 ℃ at a heating rate of 33 ℃/h, preserving heat for 4h, and then carrying out multi-pass rolling deformation, wherein the initial rolling temperature of hot rolling is 1120 ℃, the pass reduction is 18mm, and the final rolling temperature of hot rolling is 1040 ℃;
directly feeding the rolled test piece into laminar flow water cooling, wherein the water feeding temperature is 990 ℃, the cooling speed is 26 ℃/s, and the temperature is reduced to 53 ℃ to obtain a hot-rolled low-density steel austenitic steel plate;
solid solution: keeping the temperature of the obtained low-density steel hot-rolled steel plate at 1100 ℃ for 2h, and then cooling the steel plate to room temperature at a cooling speed of 23 ℃/s to obtain solid-solution low-density austenitic steel;
the aging process comprises the following steps: and (3) keeping the temperature of the obtained low-density steel hot-rolled steel plate at 450 ℃ for 5h, and then cooling the steel plate to room temperature in air to obtain the low-density austenitic steel in a low-temperature aging state.
Example 2
According to the components of the example 2 in the table 1, the raw materials required by the corresponding proportion are placed into a magnesia crucible of a vacuum induction melting furnaceIn the middle, the vacuum degree in the furnace is reduced to 1.9 multiplied by 10-2Pa, filling high-purity argon as protective gas to 3.1 × 10 after completely melting high-purity iron4And Pa, stirring in the smelting process, and smelting to obtain molten steel. And injecting the obtained molten steel into a cast iron mold, pouring the molten steel at 1441 ℃, carrying out inert gas protection pouring while die casting, discharging the molten steel for 1h after pouring, cooling the molten steel to room temperature at 5 ℃/h, and demolding to obtain the low-density steel ingot.
Temperature control rolling: heating the obtained low-density steel forging stock to 1170 ℃ at the heating rate of 30 ℃/h, preserving heat for 4h, and then carrying out multi-pass rolling deformation, wherein the initial rolling temperature of hot rolling is 1130 ℃, the pass reduction is 16mm, and the final rolling temperature of hot rolling is 1020 ℃.
And directly feeding laminar water cooling after rolling, wherein the water feeding temperature is 980 ℃, the cooling speed is 25 ℃/s, and the cooling is carried out to 68 ℃ to obtain the hot-rolled low-density steel austenitic steel plate.
Solid solution process: and (3) keeping the temperature of the obtained low-density steel hot-rolled steel plate at 1050 ℃ for 4h, and then cooling the steel plate to room temperature by water at the speed of 25 ℃/s to obtain the solid-solution low-density austenitic steel.
The aging process comprises the following steps: and (3) keeping the temperature of the obtained low-density steel hot-rolled steel plate at 500 ℃ for 4h, and then cooling the steel plate to room temperature in air to obtain the low-density austenitic steel in a low-temperature aging state.
Example 3
According to the components of the example 3 in the table 1, the raw materials required by the corresponding proportion are placed into a magnesia crucible of a vacuum induction melting furnace, and the vacuum degree in the furnace is reduced to 1.8 multiplied by 10-2Pa, filling high-purity argon as protective gas to 3 x 10 after completely melting high-purity iron4And Pa, stirring in the smelting process, and smelting to obtain molten steel. And injecting the obtained molten steel into a cast iron mold, casting the molten steel at the casting temperature of 1430 ℃, carrying out inert gas protection casting while die casting, discharging the molten steel from the furnace for 1h after casting, cooling the molten steel to room temperature at the speed of 7 ℃/h, and demolding to obtain the low-density steel cast ingot.
Temperature control rolling: heating the obtained low-density steel forging stock to 1190 ℃ at the heating rate of 35 ℃/h, preserving heat for 4h, then carrying out multi-pass rolling deformation, wherein the initial rolling temperature of hot rolling is 1120 ℃, the pass reduction is 10mm, and the final rolling temperature of hot rolling is 1029 ℃.
And directly feeding the rolled steel into laminar flow water cooling, wherein the water feeding temperature is 985 ℃, the cooling speed is 30 ℃/s, and the steel is cooled to 44 ℃ to obtain the hot-rolled low-density steel austenitic steel plate.
Solid solution process: and (3) keeping the temperature of the obtained low-density steel hot-rolled steel plate at 1100 ℃ for 1h, and then cooling the steel plate to room temperature at the water cooling speed of 15 ℃/s to obtain the solid-solution low-density austenitic steel.
The aging process comprises the following steps: and (3) keeping the temperature of the obtained low-density steel hot-rolled steel plate at 550 ℃ for 3h, and then cooling the steel plate to room temperature in air to obtain the low-density austenitic steel in a low-temperature aging state.
Example 4
According to the components of the example 4 in the table 1, the raw materials required by the corresponding proportion are placed into a magnesia crucible of a vacuum induction melting furnace, and the vacuum degree in the furnace is reduced to 2 multiplied by 10-2Pa, filling high-purity argon as protective gas to 3.1 × 10 after completely melting high-purity iron4And Pa, stirring in the smelting process, and smelting to obtain molten steel. Injecting the obtained molten steel into a cast iron mold, pouring the molten steel at 1444 ℃, carrying out inert gas protection pouring while die casting, discharging the molten steel for 1h after pouring, cooling the molten steel to room temperature at 8 ℃/h, and demolding to obtain a low-density steel ingot;
forging and forming process: heating the obtained low-density steel ingot to 1150 ℃ at a heating rate of 22 ℃/h and preserving heat for 14h, forging and forming according to the procedures of shaping, widening, drawing and shaping, wherein the initial forging temperature is 1110 ℃, when the temperature of a forge piece is reduced to 965 ℃, returning to a furnace and heating to 1140 ℃, preserving heat for 1h and then discharging from the furnace for continuous forging, the final forging temperature is 983 ℃, and directly cooling to room temperature after forging to obtain a low-density steel forging blank;
temperature control rolling: heating the obtained low-density steel forging stock to 1160 ℃ at a heating rate of 25 ℃/h, preserving heat for 4h, then carrying out multi-pass rolling deformation, wherein the initial rolling temperature of hot rolling is 1130 ℃, the pass reduction is 6mm, and the final rolling temperature of hot rolling is 1044 ℃.
And directly feeding laminar water cooling after rolling, wherein the water feeding temperature is 992 ℃, the cooling speed is 26 ℃/s, and the temperature is cooled to 50 ℃ to obtain the hot-rolled low-density steel austenitic steel plate.
Solid solution: and (3) keeping the temperature of the obtained low-density steel hot-rolled steel plate at 940 ℃ for 5 hours, and then cooling the steel plate to room temperature by water at the water cooling speed of 50 ℃/s to obtain the solid-solution low-density austenitic steel.
Aging: and (3) keeping the temperature of the obtained low-density steel hot-rolled steel plate at 450 ℃ for 6h, and then cooling the steel plate to room temperature in air to obtain the low-density austenitic steel in a low-temperature aging state.
Example 5
According to the components of the example 5 in the table 1, the raw materials required by the corresponding proportion are placed into a magnesia crucible of a vacuum induction melting furnace, and the vacuum degree in the furnace is reduced to 1.7 multiplied by 10-2Pa, filling high-purity argon as protective gas to 3.2 multiplied by 10 after completely melting high-purity iron4And Pa, stirring in the smelting process, and smelting to obtain molten steel. And injecting the obtained molten steel into a cast iron mold, pouring the molten steel at 1446 ℃, carrying out inert gas protection pouring while die casting, discharging the molten steel for 1h after pouring, cooling the molten steel to room temperature at 6 ℃/h, and demolding to obtain the low-density steel ingot.
Forging and forming: heating the obtained low-density steel cast ingot to 1110 ℃ at a heating rate of 25 ℃/h, preserving heat for 16h, forging and forming according to the procedures of shaping, widening, drawing and shaping, wherein the initial forging temperature is 1080 ℃, when the temperature of a forge piece is reduced to 959 ℃, returning to a furnace, heating to 1120 ℃, preserving heat for 1h, discharging from the furnace, continuously forging, wherein the final forging temperature is 976 ℃, and directly cooling to room temperature after forging to obtain a low-density steel forging blank.
Temperature control rolling: heating the obtained low-density steel forging stock to 1150 ℃ at a heating rate of 29 ℃/h, preserving heat for 4h, and then carrying out multi-pass rolling deformation, wherein the initial rolling temperature of hot rolling is 1140 ℃, the pass reduction is 20mm, and the final rolling temperature of hot rolling is 1030 ℃.
And directly feeding the rolled steel into laminar flow water cooling, wherein the water feeding temperature is 984 ℃, the cooling speed is 27 ℃/s, and the steel is cooled to 60 ℃ to obtain the hot-rolled low-density steel austenitic steel plate.
Solid solution: and (3) keeping the temperature of the obtained low-density steel hot-rolled steel plate at 1000 ℃ for 2.5h, and then cooling the steel plate to room temperature by water, wherein the water cooling speed is required to be 42 ℃/s, so that the solid-solution low-density austenitic steel is obtained.
Aging: and (3) keeping the temperature of the obtained low-density steel hot-rolled steel plate at 480 ℃ for 4h, and then cooling the steel plate to room temperature in air to obtain the low-density austenitic steel in a low-temperature aging state.
Comparative example 1
According to the components of comparative example 1 in table 1, the raw materials required by corresponding proportion are placed into a magnesia crucible of a vacuum induction melting furnace, and the vacuum degree in the furnace is reduced to 2 multiplied by 10-2Pa, filling high-purity argon as protective gas to 3 x 10 after completely melting high-purity iron4And Pa, stirring in the smelting process, and smelting to obtain molten steel.
Injecting the obtained molten steel into a cast iron mold, wherein the casting temperature of the molten steel is 1483 ℃, performing inert gas protection casting while die casting, demolding after 1h after the casting is finished, and slowly cooling to room temperature at the cooling speed of 7 ℃/h to obtain a low-density steel ingot;
remelting the obtained low-density steel ingot, selecting an appropriate slag system for electroslag, setting the electroslag melting speed to be 9kg/min, adopting argon as protective gas in the melting process, and slowly cooling the electroslag ingot to room temperature at the cooling speed of 5 ℃/h after demoulding to obtain the low-density steel electroslag ingot;
slowly heating the obtained low-density electroslag ingot to 1150 ℃ at a heating rate of 36 ℃/h and preserving heat for 14h, wherein the initial forging temperature is 1100 ℃, the final forging temperature is 983 ℃, the temperature is raised to 1160 ℃ when the temperature is lower than the initial forging temperature, the heating time is 1.5h until the low-density electroslag ingot is forged into a plate-shaped blank suitable for rolling, and directly cooling the low-density electroslag ingot to room temperature after forging to obtain a low-density steel forging stock;
slowly heating the obtained low-density steel forging stock to 1160 ℃ at a heating rate of 42 ℃/h, preserving heat for 5h, then carrying out multi-pass rolling deformation, wherein the initial rolling temperature of hot rolling is 1120 ℃, the pass reduction of the rolling deformation is controlled to be 12 mm, the final rolling temperature of the hot rolling is 986 ℃, directly cooling to room temperature after rolling, the cooling speed is 27 ℃/s, and the final cooling temperature is 70 ℃, so as to obtain a hot-rolled low-density austenite steel plate;
keeping the temperature of the obtained low-density steel hot rolled steel plate at 1050 ℃ for 1h, and then cooling the steel plate to room temperature by water at the speed of 15 ℃/s to obtain solid-solution low-density austenitic steel;
comparative example 2
According to the components of comparative example 2 in table 1, the raw materials required by corresponding proportion are placed into a magnesia crucible of a vacuum induction melting furnace, and the vacuum degree in the furnace is reduced to 1.9 multiplied by 10-2Pa, filling high-purity argon as protective gas to 3 x 10 after completely melting high-purity iron4And Pa, stirring in the smelting process, and smelting to obtain molten steel.
Injecting the obtained molten steel into a cast iron mold, casting the molten steel at 1400 ℃, performing inert gas protection casting while die casting, demolding after 1h after casting is finished, and slowly cooling to room temperature at a cooling speed of 7 ℃/h to obtain a low-density steel ingot;
remelting the obtained low-density steel ingot, selecting an appropriate slag system for electroslag, setting the electroslag melting speed to be 6kg/min, adopting argon as protective gas in the melting process, and slowly cooling the electroslag ingot to room temperature at the cooling speed of 5 ℃/h after demoulding to obtain the low-density steel electroslag ingot;
slowly heating the obtained low-density electroslag ingot to 1140 ℃ at the heating rate of 39 ℃/h and preserving heat for 11h, wherein the initial forging temperature is 1100 ℃, the final forging temperature is 984 ℃, the temperature is raised to 1140 ℃ when the temperature is lower than the initial forging temperature, the heating time is 1.5h, the low-density electroslag ingot is forged into a plate-shaped blank suitable for rolling, and the low-density steel forging blank is obtained by directly cooling to room temperature after forging;
slowly heating the obtained low-density steel forging stock to 1170 ℃ at the heating rate of 43 ℃/h, preserving heat for 4h, then carrying out multi-pass rolling deformation, wherein the initial rolling temperature of hot rolling is 1130 ℃, the pass reduction of the rolling deformation is controlled to be 10mm, the final rolling temperature of the hot rolling is 982 ℃, directly cooling to room temperature after rolling, the cooling rate is 32 ℃/s, and the final cooling temperature is 77 ℃, so as to obtain a hot-rolled low-density austenitic steel plate;
keeping the temperature of the obtained low-density steel hot-rolled steel plate at 950 ℃ for 3h, and then cooling the steel plate to room temperature at the water cooling speed of 20 ℃/s to obtain solid-solution low-density austenitic steel;
comparative example 3
According to the components of the embodiment shown in the table 1, the raw materials required by the corresponding proportion are placed into a magnesia crucible of a vacuum induction melting furnace, and the vacuum degree in the furnace is reduced to 1.8 multiplied by 10-2Pa, filling high-purity argon as protective gas after completely melting high-purity ironVolume to 3X 104And Pa, stirring in the smelting process, and smelting to obtain molten steel.
Injecting the obtained molten steel into a cast iron mold, wherein the casting temperature of the molten steel is 1420 ℃, performing inert gas protection casting while die casting, demolding after 1h after casting is finished, and slowly cooling to room temperature at a cooling speed of 5 ℃/h to obtain a low-density steel ingot;
remelting the obtained low-density steel ingot, selecting an appropriate slag system for electroslag, setting the electroslag melting speed to be 9kg/min, adopting argon as protective gas in the melting process, and slowly cooling the electroslag ingot to room temperature at the cooling speed of 7 ℃/h after demoulding to obtain the low-density steel electroslag ingot;
slowly heating the obtained low-density electroslag ingot to 1140 ℃ at a heating rate of 37 ℃/h and preserving heat for 12h, wherein the initial forging temperature is 1100 ℃, the final forging temperature is 986 ℃, the temperature is raised to 1140 ℃ when the temperature is lower than the initial forging temperature, the heating time is not less than 1.5h until the low-density electroslag ingot is forged into a plate-shaped blank suitable for rolling, and directly cooling the low-density electroslag ingot to room temperature after forging to obtain a low-density steel forging stock;
slowly heating the obtained low-density steel forging stock to 1150 ℃ at a heating rate of 40 ℃/h, preserving heat for 5h, then carrying out multi-pass rolling deformation, wherein the initial rolling temperature of hot rolling is 1120 ℃, the pass reduction of the rolling deformation is controlled to be 17mm, the final rolling temperature of the hot rolling is 985 ℃, directly cooling to room temperature after rolling, the cooling rate is 30 ℃/s, and the final cooling temperature is 40 ℃ to obtain a hot-rolled low-density austenite steel plate;
and (3) keeping the temperature of the obtained low-density steel hot-rolled steel plate at 1100 ℃ for 2h, and then cooling the steel plate to room temperature at the water cooling speed of 20 ℃/s to obtain the solid-solution low-density austenitic steel.
Characterization and Performance testing
1) FIG. 1 is an SEM image of impact fracture of a low-density high-ductility and toughness steel prepared in example 2; as can be seen from FIG. 1, the steel material is composed of dense equiaxed dimples, and the shape can effectively prevent the initiation and the expansion of cracks, which shows that the fracture toughness of the material is better.
FIG. 2 is an SEM image of a low-density high-ductility steel prepared in example 5, and it can be seen from FIG. 2 that (Ti, Nb) (C, N) is uniformly and dispersedly distributed on a single-phase austenite matrix, and kappa carbides or other brittle phases along grains are not present on grain boundaries, so that the steel has the effects of fine grain strengthening and precipitation strengthening and has high ductility.
2) Standard tensile samples are respectively processed from the alloy plates prepared in examples 1-5 and comparative examples 1-3, and the obtained data related to the mechanical properties are shown in table 2; processing a standard impact sample from the alloy plate, and carrying out a low-temperature impact test at-40 ℃; taking a density test sample from the alloy plate by utilizing linear cutting, and measuring the density value by utilizing an Archimedes principle; wherein the tensile test standard is as in GBT 228.1-2010 part 1 of the tensile test of metal materials: room temperature test method. GBT 229-. GB/T3850-2015 Density determination method for dense sintered metal materials and hard alloys. GB/T3658 + 2008 'method for measuring alternating current magnetic property of soft magnetic material' determines magnetism.
TABLE 2 Performance data for Steel products prepared in examples 1-5 and comparative examples 1-3
Figure BDA0003613074210000141
The comprehensive analysis of the examples 1 to 5 and the comparative examples 1 to 3 can be carried out, and the comparative example 1 lacks an electroslag remelting process, the comparative example 2 lacks an electroslag remelting and forging process, the comparative example 3 has low Al content and other differences, so that the comparative example has the problems of larger grain size nonuniformity, more precipitated phases in grain boundaries, more inclusions in grains and the like, and the comprehensive mechanical property and the density of the steel product are inferior to those of the steel products prepared in the examples 1 to 5. In comparative example 2, the element C is low, a ferrite magnetic phase is generated, alloy elements such as Ti, Nb and the like are not added, and the ferrite morphology cannot be regulated by the low-magnetic phase (Nb, Ti) (C, N), so that the magnetism is improved. In comparative examples 2 and 3, the contents of Al and C light elements are low, and the material density is also higher.
The foregoing is only a preferred embodiment of the present invention, and it should be noted that, for those skilled in the art, various modifications and decorations can be made without departing from the principle of the present invention, and these modifications and decorations should also be regarded as the protection scope of the present invention.

Claims (10)

1. The low-density high-ductility steel is characterized by comprising the following chemical components in percentage by mass: 29-33% of Mn, 10.70-11.30% of Al, 1.15-1.19% of C, 0.01-0.20% of Si, 4.00-5.90% of Cr, 0.50-1.20% of Cu, 0.01-0.30% of Nb, 0.01-0.30% of Ti, 0.05-0.10% of N, less than or equal to 0.012% of P, less than or equal to 0.003% of S, and the balance of Fe and inevitable impurities; meanwhile, the mass percentage of Mn, Al, C, Nb and Ti satisfies 0.0098Al +0.208(C- (Nb + Ti)/5) +0.0054Mn-0.6 < 0; and the mass percentage of Al and C satisfies 105Al +356C multiplied by C-700 > 800.
2. The method for preparing the low-density high-ductility steel as set forth in claim 1, characterized by comprising the steps of:
mixing the raw materials corresponding to the low-density high-ductility steel, and sequentially smelting and pouring to obtain an ingot;
carrying out temperature control rolling on the cast ingot to obtain a rolled piece;
and sequentially carrying out quenching treatment, solid solution treatment and low-temperature aging treatment on the rolled piece to obtain the low-density high-ductility and toughness steel.
3. The preparation method according to claim 2, wherein the casting temperature is 1380-1500 ℃; and after the casting, cooling the obtained casting at a cooling speed of 5-8 ℃/h.
4. The preparation method according to claim 2, wherein before the temperature-controlled rolling, the ingot is heated to 1150-1190 ℃ at a heating rate of 25-35 ℃/h and is kept at the temperature for more than 4 h; the temperature-controlled rolling conditions comprise: the initial rolling temperature is 1120-1140 ℃, rolling is carried out by using pass reduction of 6-20 mm, and the final rolling temperature is more than or equal to 1000 ℃.
5. The production method according to claim 2, wherein the conditions of the quenching treatment include: the cooling speed is more than or equal to 25 ℃/s, the water inlet temperature is more than or equal to 980 ℃, and the final cooling temperature is less than or equal to 100 ℃.
6. The preparation method according to claim 2, wherein the temperature of the solution treatment is 940-1100 ℃, and the holding time is 1-5 h; and after the solid solution treatment is finished, cooling the obtained solid solution piece to room temperature by water at the water cooling speed of 15-50 ℃/s.
7. The preparation method according to claim 2, wherein the temperature of the low-temperature aging treatment is 450-550 ℃, and the holding time is 3-6 h.
8. The method of claim 2, wherein after obtaining the ingot, further comprising: heating the cast ingot to 1110-1150 ℃ at a heating rate of 20-25 ℃/h, and preserving heat; the heat preservation time is more than or equal to 10 hours, and forging forming is carried out; the forging forming comprises shaping, widening, drawing and shaping which are sequentially carried out; the final forging temperature is more than or equal to 970 ℃.
9. The preparation method of the forging material as claimed in claim 8, wherein in the forging forming process, when the temperature of the forging piece is reduced to 950 ℃, the forging is returned to 1110-1150 ℃ for heat preservation, and the heat preservation time is more than or equal to 1 h.
10. The application of the low-density high-ductility and toughness steel as defined in claim 1 or the low-density high-ductility and toughness steel prepared by the preparation method as defined in any one of claims 2 to 9 in high-toughness or nonmagnetic traffic and carrying equipment.
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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN115323278A (en) * 2022-06-29 2022-11-11 钢铁研究总院有限公司 Low-density steel with yield of 700MPa and heat treatment method thereof
CN116676533A (en) * 2023-06-07 2023-09-01 燕山大学 Fe-Mn-Al-C-Mo-Ni-Cu austenitic steel and preparation method thereof

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5376193A (en) * 1993-06-23 1994-12-27 The United States Of America As Represented By The Secretary Of Commerce Intermetallic titanium-aluminum-niobium-chromium alloys
CN112877606A (en) * 2021-01-12 2021-06-01 钢铁研究总院 Ultrahigh-strength full-austenite low-density steel and preparation method thereof
CN113088826A (en) * 2021-02-25 2021-07-09 钢铁研究总院 Microalloyed high-strength high-toughness low-density steel and preparation method thereof
CN113278896A (en) * 2021-01-12 2021-08-20 北京科技大学 Fe-Mn-Al-C series high-strength low-density steel and preparation method thereof
WO2022041819A1 (en) * 2020-08-25 2022-03-03 华为技术有限公司 Fe-mn-al-c lightweight steel and preparation method therefor, terminal, steel structure, and electronic device

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5376193A (en) * 1993-06-23 1994-12-27 The United States Of America As Represented By The Secretary Of Commerce Intermetallic titanium-aluminum-niobium-chromium alloys
WO2022041819A1 (en) * 2020-08-25 2022-03-03 华为技术有限公司 Fe-mn-al-c lightweight steel and preparation method therefor, terminal, steel structure, and electronic device
CN112877606A (en) * 2021-01-12 2021-06-01 钢铁研究总院 Ultrahigh-strength full-austenite low-density steel and preparation method thereof
CN113278896A (en) * 2021-01-12 2021-08-20 北京科技大学 Fe-Mn-Al-C series high-strength low-density steel and preparation method thereof
CN113088826A (en) * 2021-02-25 2021-07-09 钢铁研究总院 Microalloyed high-strength high-toughness low-density steel and preparation method thereof

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
丁培道等: "《高速工具钢废料回收与利用》", 31 March 1984 *
王浩伟等: "《材料加工原理 下册》", 31 May 2019 *

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN115323278A (en) * 2022-06-29 2022-11-11 钢铁研究总院有限公司 Low-density steel with yield of 700MPa and heat treatment method thereof
CN116676533A (en) * 2023-06-07 2023-09-01 燕山大学 Fe-Mn-Al-C-Mo-Ni-Cu austenitic steel and preparation method thereof

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