CN114774806A - High-strength and high-toughness light steel plate and preparation method and application thereof - Google Patents

High-strength and high-toughness light steel plate and preparation method and application thereof Download PDF

Info

Publication number
CN114774806A
CN114774806A CN202210436283.9A CN202210436283A CN114774806A CN 114774806 A CN114774806 A CN 114774806A CN 202210436283 A CN202210436283 A CN 202210436283A CN 114774806 A CN114774806 A CN 114774806A
Authority
CN
China
Prior art keywords
strength
steel plate
equal
toughness
light steel
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
CN202210436283.9A
Other languages
Chinese (zh)
Other versions
CN114774806B (en
Inventor
刘日平
王青峰
张新宇
胡文俊
王子童
田野
耿路路
谯明亮
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Yanshan University
Original Assignee
Yanshan University
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Yanshan University filed Critical Yanshan University
Priority to CN202210436283.9A priority Critical patent/CN114774806B/en
Publication of CN114774806A publication Critical patent/CN114774806A/en
Application granted granted Critical
Publication of CN114774806B publication Critical patent/CN114774806B/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • 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
    • C22C33/06—Making ferrous alloys by melting using master alloys
    • 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
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

The invention relates to the technical field of alloys, in particular to a high-strength and high-toughness light steel plate and a preparation method and application thereof. The invention provides a high-strength and high-toughness light steel plate which comprises the following elements in percentage by mass: mn 27-30%, Al 8.30 c9.20 percent of C, 0.93-1.02 percent of C, 0.05-0.25 percent of Cr, 0.07-0.10 percent of Cu, 0.01-0.10 percent of Nb, 0.05-0.15 percent of Ti, less than or equal to 0.10 percent of N, less than or equal to 0.06 percent of Ce, less than or equal to 0.008 percent of P, less than or equal to 0.002 percent of S, and the balance of iron and inevitable impurities; and the mass relation of Al and C is lambda1≤[C]≤λ2；λ1＝1.53‑0.07[Al]，λ2＝1.9‑0.1[Al]. The high-strength high-toughness light steel plate simultaneously meets the characteristics of high strength, high toughness and light weight.

Description

High-strength and high-toughness light steel plate and preparation method and application thereof
Technical Field
The invention relates to the technical field of alloy, in particular to a high-strength and high-toughness light steel plate and a preparation method and application thereof.
Background
With the continuous development of social economy, a series of environmental problems are brought by large energy consumption, and the solutions of the problems are to use clean energy to replace fuel power on one hand and to reduce fuel consumption and pollution by reducing the weight of the transportation equipment on the other hand, so that the lightweight transportation equipment becomes the future development direction. The light-weight element Al is added into the steel so as to reduce the density of the steel, and then elements such as Mn, C and the like for stabilizing austenite are added, so that the Fe-Mn-Al-C series high-strength high-toughness austenite-based light steel is obtained.
Compared with the existing high-strength light steel patent, the patent finds that the steel sheet mainly relates to a sheet for the automobile industry, the rolling process mainly comprises cold rolling and annealing, and the performance indexes mainly comprise high strength, high plasticity and less steel sheets with high strength and high impact toughness. For example, chinese patent publication No. CN109735691A provides a high-carbon, high-manganese, and low-density steel with a tensile strength of 1000MPa grade, and the rolling method is hot rolling, quenching, and then cold rolling, and the thickness of the obtained steel sheet is only 1 mm; the Chinese patent with publication number CN108486492A discloses a 1200 MPa-level high-strength high-plasticity low-density steel and a preparation method thereof, wherein the rolling process comprises the steps of hot rolling, solid solution and cold rolling, and the thickness of the obtained steel plate is only 0.5-1.5 mm; the alloy disclosed in the Chinese patent with the publication number of CN103484771A comprises, by mass, 0.04-0.10% of C, 0.5-4.0% of Al, 0.3-3.0% of Mn, 0.5-2.0% of Cu, 0.4-1.6% of Ni, 0.2-1.0% of Si, 0.04-0.10% of Nb, and the balance of Fe and inevitable impurities; two-stage rolling and tempering treatment after rolling are adopted, but the added Al and C contents are low, the density is high and heavy, and the light weight effect is insufficient.
In order to solve the problem of insufficient weight reduction, a large amount of Al is generally added to reduce the density and a large amount of C is added to improve the strength. When two elements are present in large amounts at the same time, brittle kappa carbides (Fe, Mn) are easily precipitated upon cooling3And AlC leads the low-temperature impact toughness of the steel plate to be poor. For example, the literature (Current state of Fe-Mn-Al-C low density steps Progress in Materials Science) suggests that Al > 7% and C > 0.7% and that intragranular kappa carbides occur during solution cooling. The literature (the material report on the research progress of the Liuchuquan Fe-Mn-Al-C series low-density steel) suggests that kappa carbide is precipitated in the grain boundary when the Al content is more than 5.5 percent and the C content is more than 0.7 percent.
Disclosure of Invention
The invention aims to provide a high-strength and high-toughness light steel plate, and a preparation method and application thereof.
In order to achieve the above object, the present invention provides the following technical solutions:
the invention provides a high-strength and high-toughness light steel plate which comprises the following elements in percentage by mass: 27-30% of Mn, 8.30-9.20% of Al, 0.93-1.02% of C, 0.05-0.25% of Cr, 0.07-0.10% of Cu, 0.01-0.10% of Nb, 0.05-0.15% of Ti, less than or equal to 0.10% of N, less than or equal to 0.06% of Ce, less than or equal to 0.008% of P, less than or equal to 0.002% of S, and the balance of Fe and inevitable impurities;
and the mass relation of Al and C is lambda1≤[C]≤λ2；λ1＝1.53-0.07[Al]，λ2＝1.9-0.1[Al]。
Preferably, the structure of the high-strength and high-toughness lightweight steel plate is austenite + delta ferrite + (Nb, Ti) C carbide, wherein the content of delta ferrite is less than or equal to 5 vol%;
the density of the high-strength and high-toughness light steel plate is less than or equal to 6.9g/cm3(ii) a The yield strength is 620-680MPa, the tensile strength is 900-970 MPa, the elongation is more than or equal to 45%, and the transverse impact energy at minus 40 ℃ is more than or equal to 120J.
The invention also provides a preparation method of the high-strength and high-toughness light steel plate, which comprises the following steps:
according to the element composition of the high-strength and high-toughness light steel plate, mixing the preparation raw materials, and then sequentially smelting and pouring to obtain an ingot;
and sequentially rolling and quenching the cast ingot for solid solution to obtain the high-strength high-toughness light steel plate.
Preferably, after the ingot is obtained, the method further comprises the step of carrying out electroslag remelting on the ingot;
the electroslag remelting is carried out in a protective atmosphere;
the electroslag remelting comprises ingot remelting and electroslag ingot cooling which are sequentially carried out; the melting speed of the ingot remelting is 7-11 kg/min, and the cooling speed of the electroslag ingot cooling is 8-12 ℃/h.
Preferably, forging forming is further included after the electroslag remelting;
the forging temperature is 1130-1170 ℃, and the finish forging temperature is not less than 930 ℃.
Preferably, the smelting method is vacuum induction electric furnace smelting or triple process smelting;
the triple method smelting is a triple method of an electric arc furnace, a refining furnace and a vacuum degassing furnace.
Preferably, the casting temperature is 1400-1450 ℃.
Preferably, the rolling process is as follows: raising the temperature to 1150-1190 ℃ at the heating rate of 35-45 ℃/h, keeping the temperature, discharging from a furnace for rolling, wherein the initial rolling temperature is 1120-1140 ℃, rolling is carried out with the pass reduction of 6-20 mm, and the final rolling temperature is more than or equal to 970 ℃.
Preferably, the cooling rate of quenching and solid solution is more than or equal to 15 ℃/s, the water inlet temperature is more than or equal to 950 ℃, and the final cooling temperature is less than or equal to 200 ℃.
The invention also provides the application of the high-strength and high-toughness light steel plate in the technical scheme or the application of the high-strength and high-toughness light steel plate prepared by the preparation method in the field of traffic and carrying equipment.
The invention provides a high-strength and high-toughness light steel plate which comprises the following elements in percentage by mass: 27-30% of Mn, 8.30-9.20% of Al, 0.93-1.02% of C, 0.05-0.25% of Cr, 0.07-0.10% of Cu, 0.01-0.10% of Nb, 0.05-0.15% of Ti, less than or equal to 0.10% of N, less than or equal to 0.06% of Ce, less than or equal to 0.008% of P, less than or equal to 0.002% of S, and the balance of iron and inevitable impurities; and the mass relation of Al and C is lambda1≤[C]≤λ2；λ1＝1.53-0.07[Al]，λ2＝1.9-0.1[Al]. The Al content of the high-strength and high-toughness light steel plate is necessary factors for lightening (reducing material density), Mn and C content for obtaining room-temperature austenite structure and Al and C content for obtaining high-strength ductility and toughness; the strength is lower when the C content is lower, but the kappa brittle phase is promoted to be separated out when the C content is too high, so that the welding performance is not facilitated; too high Al content promotes the formation of a large amount of δ ferrite in the steel to reduce impact properties, so appropriate Al, C contents are important and are satisfied by defining the Al, C contents: 1.53-0.07[ Al ]]≤C≤1.9-0.1[Al]Under the condition of (1), austenite can be used as a matrix, the precipitation of kappa carbide is extremely easy to promote under the condition of avoiding that Al and C are both high in the required component range, and meanwhile, the content of delta ferrite is ensured to be less than or equal to 5 percent, so that a structure with high strength and excellent impact is obtained. In order to further improve the strength and toughness, the high-strength and high-toughness light steel plate is particularly added with a proper amount of key elements such as Cr, Nb, Ti, Cu, N, Ce and the like, but the hot workability and even the impact resistance can be damaged by adding too many of the elements, so that the elements can play a good role in improving the strength and the toughness in the steel by controlling the contents of the elements within the range of the percentage.
Drawings
FIG. 1 is a metallographic structure diagram of a high-toughness light steel plate according to example 1;
FIG. 2 is a metallographic structure diagram of a steel sheet according to comparative example 2;
FIG. 3 is a metallographic structure drawing of a steel plate according to comparative example 3.
Detailed Description
The invention provides a high-strength and high-toughness light steel plate which comprises the following elements in percentage by mass: 27-30% of Mn, 8.30-9.20% of Al, 0.93-1.02% of C, 0.05-0.25% of Cr, 0.07-0.10% of Cu, 0.01-0.10% of Nb, 0.05-0.15% of Ti, less than or equal to 0.10% of N, less than or equal to 0.06% of Ce, less than or equal to 0.008% of P, less than or equal to 0.002% of S, and the balance of Fe and inevitable impurities;
and the mass relation of Al and C is lambda1≤[C]≤λ2；λ1＝1.53-0.07[Al]，λ2＝1.9-0.1[Al]。
According to the mass percentage, the high-strength and high-toughness light steel plate comprises 27-30% of Mn, more preferably 27.5-29.5%, and most preferably 28-29%.
In the present invention, the Mn element is an austenite stabilizing element, and can expand an austenite phase region and lower the Ms point. Meanwhile, Mn plays a role in solid solution strengthening, so that the work hardening rate of the steel is improved, and the toughness of the steel is improved. The addition of Mn element can also reduce the stacking fault energy, generate twin crystals in the deformation process and obviously improve the plasticity of the steel. However, when the Mn content is too high, beta-Mn is formed to seriously deteriorate the impact toughness of the steel, so that the toughness is not affected on the premise of ensuring stable austenite in the present invention, and the above problem can be avoided by controlling the Mn content within the above range.
According to the mass percentage, the high-strength and high-toughness light steel plate comprises 8.30-9.20% of Al, more preferably 8.5-9.0%, and most preferably 8.6-8.8%.
In the present invention, the addition of said Al element can reduce the density of the steel by 0.101g/cm per 1 wt% of Al added3. Al is a ferrite-forming element and reduces the austenite region, and if the content is too high, the formation of delta ferrite in the high-temperature range is promoted. Al is a main solid solution strengthening element, and in addition, the addition of the Al element can form nano-scale kappa carbide to improve the strength of the steel and reduce the toughness. Controlling the Al content within the above range can reduce the kappa carbide and control the delta ferrite content.
According to the mass percentage, the high-strength and high-toughness light steel plate comprises 0.93-1.02% of C, more preferably 0.95-1.0%, and most preferably 0.97-0.98%.
In the present invention, C is an austenite stabilizing element and can expand the austenite phase region. Plays a role in interstitial solid solution strengthening, and can form kappa carbide with Mn and Al in the light steel. Can form strong carbide with Nb, V and other elements in steel, pin grain boundary and refine austenite grains.
According to the mass percentage, the high-strength and high-toughness light steel plate comprises 0.05-0.25% of Cr, more preferably 0.08-0.21%, and most preferably 0.13-0.17%.
In the present invention, most of Cr is dissolved into austenite at the time of solution treatment to increase the solution strengthening effect, and Cr forms a precipitation phase having higher energy instead of Mn/Fe atoms in kappa carbide, thereby suppressing the formation of kappa carbide. However, too much Cr tends to increase the net Cr segregation along the crystal23C6Carbides, on the contrary, reduce impact toughness. By controlling Cr within the above-mentioned content range, the above-mentioned problems can be avoided.
According to the mass percentage, the high-strength and high-toughness light steel plate comprises 0.07-0.10% of Cu, and more preferably 0.08-0.09%.
In the present invention, Cu has an effect of improving austenite stability similar to Ni, but too much Cu forms a B2 phase of CuAl with Al to lower ductility and toughness of steel, so Cu is controlled to be within the above range.
According to the mass percentage, the high-strength and high-toughness light steel plate comprises 0.01-0.10% of Nb, more preferably 0.03-0.08%, and most preferably 0.05-0.06%.
In the invention, Nb is a strong carbide forming element, and is easy to form fine Nb (C, N) at high temperature, so that grain boundaries can be effectively pinned to refine grains, precipitation of kappa carbide is inhibited, and the plasticity and toughness are improved. However, too much Nb tends to increase the amount of network carbide precipitated along the crystal, and conversely lowers the impact toughness.
According to the mass percentage, the high-strength and high-toughness light steel plate comprises 0.05-0.15% of Ti, more preferably 0.06-0.12%, and most preferably 0.08-0.10%.
In the invention, Ti is a strong carbide forming element, and can easily form fine Ti (C, N) at high temperature, effectively pin grain boundaries to refine grains, and inhibit kappa carbide precipitation, thereby being beneficial to improving ductility and toughness. However, when the content of Ti is too high, a large amount of C atoms in the steel are consumed to lower the austenite stability, and grain boundary carbides are formed to lower the impact resistance.
According to the mass percentage, the high-strength and high-toughness light steel plate comprises N which is less than or equal to 0.10 percent.
In the present invention, N atoms are solid-dissolved in austenite to generate a strong solid-solution strengthening effect, thereby increasing the stability of austenite and advantageously obtaining a single-phase austenite structure at low temperature, but too much N is bonded with Al in steel to form AlN, which affects the low-temperature impact toughness of steel.
According to the mass percentage, the high-strength and high-toughness light steel plate comprises Ce which is less than or equal to 0.06 percent, and preferably less than or equal to 0.05 percent.
In the invention, long delta ferrite appears on the austenite matrix inevitably when Al is more than or equal to 9 percent, and the impact toughness is reduced by the delta ferrite, so that a small amount of rare earth Ce is added under a certain Al content, and the Ce can be used as a nucleation point to refine the long delta ferrite and improve the impact toughness. However, too high rare earth Ce causes a large amount of inclusions formed in the steel to degrade the properties of the steel.
According to the mass percentage, the high-strength and high-toughness light steel plate comprises P which is less than or equal to 0.008 percent, preferably P which is less than or equal to 0.005 percent.
In the present invention, P is a harmful element in the steel, and the high carbon content of the steel reduces the solubility of P in austenite, easily precipitates a film-like phosphide along the crystal, causes hot cracking of workpieces, and reduces the ductility and toughness of the steel. Therefore, the content of P is controlled within the above range.
According to the mass percentage, the high-strength and high-toughness light steel plate comprises S which is less than or equal to 0.002 percent.
In the present invention, since S tends to form MnS inclusions, increases hot brittleness, and decreases ductility and toughness, the S content is controlled to be within the above range.
In the invention, the mass relation between Al and C is lambda1≤[C]≤λ2；λ1＝1.53-0.07[Al]，λ2＝1.9-0.1[Al](ii) a According to the invention, the content of Al and C is optimized, the precipitation of a large amount of carbide and delta ferrite is avoided, the precipitation of kappa carbide is further inhibited by adding Cr, the (Nb, Ti) C can be formed by adding Nb and Ti in a proper amount, the growth of austenite grains can be prevented, the ductility and toughness are improved, the addition of N generates a higher solid solution strengthening effect, the delta ferrite can be refined by rare earth Ce, the influence of the formation of strip ferrite on the impact toughness is avoided, an austenite + delta ferrite structure is obtained, the content of the delta ferrite is less than or equal to 5%, the lower density is obtained, the higher strength is obtained, and the higher impact toughness is also obtained.
In the invention, the structure of the high-strength and high-toughness light steel plate is austenite + delta ferrite + (Nb, Ti) C carbide, wherein the content of delta ferrite is less than or equal to 5 percent;
the density of the high-strength and high-toughness light steel plate is less than or equal to 6.9g/cm3(ii) a The yield strength is 620-680MPa, the tensile strength is 900-970 MPa, the elongation is more than or equal to 45%, and the transverse impact energy at-40 ℃ is more than or equal to 120J.
The invention also provides a preparation method of the high-strength and high-toughness light steel plate, which comprises the following steps:
according to the element composition of the high-strength and high-toughness light steel plate, mixing the preparation raw materials, and then sequentially smelting and pouring to obtain an ingot;
and sequentially rolling and quenching the cast ingot for solid solution to obtain the high-strength high-toughness light steel plate.
In the present invention, all the starting materials for the preparation are commercially available products well known to those skilled in the art, unless otherwise specified.
According to the element composition of the high-strength, high-toughness and light steel plate, the preparation raw materials are mixed, and then smelting and pouring are sequentially carried out to obtain an ingot.
In the invention, the preparation raw materials preferably comprise electrolytic manganese, graphitized carbon powder, metallic niobium, metallic titanium, pure copper, ferrosilicon, metallic nickel, chromium nitride and pure aluminum.
In the invention, the mixing is preferably to add electrolytic manganese, graphitized carbon powder, metal niobium, metal titanium, pure copper, ferrosilicon, metal nickel and chromium nitride into a vacuum induction furnace, vacuumize to below 0.1Pa, electrify to melt the raw materials, and add pure aluminum in 3 batches after the raw materials are added into the furnace and melted.
In the invention, the smelting method is preferably vacuum induction furnace smelting or triple smelting; the triple method smelting is a triple method of an electric arc furnace, a refining furnace and a vacuum degassing furnace.
In the invention, the smelting process of the vacuum induction furnace is preferably to firstly vacuumize to 0.1Pa, then fill nitrogen in the whole process, and gradually increase the power to 300kW at the speed of 60 kW/h.
In the present invention, the process of the triplet method is preferably: after the preparation raw materials are completely melted in an electric arc furnace, refining and vacuum degassing are carried out in sequence; the refining time is preferably more than or equal to 30 min; the time of vacuum degassing is preferably 10-30 min.
In the invention, the casting temperature is preferably 1400-1450 ℃, more preferably 1410-1440 ℃, and most preferably 1420-1430 ℃.
After the casting is finished, demoulding is preferably carried out within 1h, and finally cooling is preferably carried out to room temperature at a cooling speed of 12-15 ℃/h.
After obtaining the cast ingot, the invention also comprises the step of carrying out electroslag remelting on the cast ingot; after the electroslag remelting, peeling and polishing the cast ingot; the electroslag remelting is carried out in a protective atmosphere; the electroslag remelting comprises remelting and solidification which are sequentially carried out; the remelting melting speed is 7-11 kg/min, and the solidification cooling speed is 8-12 ℃/h.
In the invention, the electroslag remelting mainly has the effects of improving the internal quality of the ingot, reducing segregation, inclusion, pores, microcracks and the like, obtaining an as-cast structure with a uniform structure and no defect, and avoiding cracking in the subsequent hot working process caused by defects in the as-cast structure.
After the electroslag remelting, the invention also preferably comprises forging forming; the forging temperature is preferably 1130-1170 ℃, and more preferably 1140-1160 ℃; the finish forging temperature is preferably not less than 930 deg.C, more preferably not less than 950 deg.C.
In the invention, the forging forming process is preferably to heat up to 1130-1170 ℃ at a heating rate of 30-40 ℃/h, then keep the temperature, and forge according to the procedures of shaping, widening, drawing and shaping; and when the temperature of the forge piece is reduced to 930 ℃, returning to the furnace and heating to 1130-1170 ℃, and keeping the temperature for more than or equal to 1 hour to obtain the plate-shaped blank.
After the forging forming is finished, the invention also preferably comprises a process of cooling to room temperature; the cooling process is not particularly limited in the present invention, and may be performed by a process known to those skilled in the art.
In the invention, the forging forming mainly has the effect of changing the shape of an as-cast ingot, the ingot is usually round, and particularly, the ingot cannot be directly rolled when the single weight of the ingot is large, and needs to be forged into a slab with a thin thickness, so that the later rolling is facilitated. In addition, the forging can further homogenize the structure, change the columnar crystal in the cast structure into uniform isometric crystal and reduce the anisotropy.
After obtaining the cast ingot, the cast ingot is sequentially rolled, quenched and solid-dissolved to obtain the high-strength and high-toughness light steel plate.
In the present invention, the rolling process is preferably: heating to 1150-1190 ℃ at the heating rate of 35-45 ℃/h, keeping the temperature, discharging from a furnace for rolling, wherein the initial rolling temperature is 1120-1140 ℃, rolling is carried out with the pass reduction of 6-20 mm, and the final rolling temperature is more than or equal to 970 ℃; more preferably, the temperature is increased to 1160-1180 ℃ at the heating rate of 38-42 ℃/h, the temperature is kept, the steel is discharged from a furnace for rolling, the initial rolling temperature is 1125-1135 ℃, the rolling is carried out at the pass reduction of 10-15 mm, and the final rolling temperature is 970 ℃.
In the invention, the rolling is used for rolling the cast ingot or the forged blank into a plate, and the temperature and heat preservation conditions are mainly controlled in the rolling process so as to roll in a proper temperature range of the steel and avoid edge cracking caused by insufficient plasticity.
In the invention, the cooling rate of the quenching solid solution is preferably more than or equal to 15 ℃/s, and more preferably more than or equal to 17 ℃/s; the water inlet temperature is preferably more than or equal to 950 ℃, and more preferably more than or equal to 980 ℃; the final cooling temperature is preferably 200 ℃ or lower, more preferably 100 ℃ or lower.
In the present invention, the quenching and solution treatment are preferably performed by directly feeding the rolled material obtained by rolling into a laminar flow water or a water tank.
In the invention, the quenching and solid solution functions mainly to obtain a single-phase austenite structure, avoid the occurrence of brittle carbides in steel and further avoid the situation that the mechanical property does not meet the requirement.
The invention also provides application of the high-strength and high-toughness light steel plate in the technical scheme or the application of the high-strength and high-toughness light steel plate prepared by the preparation method in the technical scheme in the field of traffic and carrying equipment. The method of the present invention is not particularly limited, and may be carried out by a method known to those skilled in the art.
The high strength and toughness lightweight steel sheet provided by the present invention, the manufacturing method and the application thereof will be described in detail with reference to the following examples, but they should not be construed as limiting the scope of the present invention.
Example 1
The composition of the high strength and toughness lightweight steel sheet is shown in table 1:
the preparation process comprises the following steps:
adding electrolytic manganese, graphitized carbon powder, metallic niobium, metallic titanium, pure copper, metallic cerium and chromium nitride into a vacuum induction furnace, vacuumizing to below 0.1Pa, electrifying to melt raw materials, adding pure aluminum in 3 batches after the raw materials are added into the furnace and melted, refining for 30min after all the raw materials are melted, fully stirring to fully homogenize molten steel, controlling the pouring temperature of the molten steel to 1430 ℃, pouring into a circular casting mold, standing in the furnace for 1h, breaking the air, demolding, and slowly cooling to room temperature at the cooling rate of 13 ℃/h to obtain an ingot;
heating the cast ingot to a rolling temperature at a heating rate of 38 ℃/s, preserving heat (specifically shown in table 3), rolling after the structure is completely uniform, wherein the initial rolling temperature and the final rolling temperature are shown in table 3, and the thickness of a rolled plate is shown in table 3; after the rolling is finished, quenching and solid solution are carried out immediately, the water inlet temperature is shown in table 3, the cooling rate of online quenching is 17 ℃/s, and the final cooling temperature is 85 ℃;
the metallographic structure of the high-toughness lightweight steel sheet is shown in fig. 1, and it is understood from fig. 1 that the structure of the high-toughness lightweight steel sheet is single-phase austenite.
Examples 2 to 3
The composition of the high strength and toughness lightweight steel sheet is shown in table 1:
the preparation process refers to example 1, and specific condition parameters are shown in table 3, wherein the difference is that after an ingot is obtained, the method further comprises the steps of peeling and polishing the ingot, and removing surface microcracks and oxide skin to be used as an electrode bar for electroslag remelting so as to prevent the electroslag ingot from generating defects; and remelting the cast ingot at the speed of 7Kg/min, solidifying, adopting argon gas for protection in the electroslag remelting process, demoulding, and cooling to room temperature at the speed of 10 ℃/h.
Examples 4 to 5
The composition of the high-strength and high-toughness lightweight steel plate is shown in table 1:
the preparation process refers to example 2, and specific condition parameters are shown in table 3, wherein the difference is that after electroslag remelting is completed, the obtained electroslag ingot is added into a heating furnace, and the temperature is raised to the heating temperature at 80 ℃/h for heat preservation (shown in table 2), so that the electroslag ingot is fully homogenized; forging according to the procedures of shaping, widening, drawing and shaping; when the temperature of the forge piece is reduced to 930 ℃, returning to the furnace and raising the temperature to the forging starting temperature, preserving the temperature for 1h, wherein the final forging temperature is shown in table 2, and the thickness of the obtained plate blank is shown in table 2;
comparative example 1
The steel sheet had the composition shown in table 1, the production process was as in example 1, and the specific condition parameters are shown in table 3.
Comparative examples 2 to 3
The steel plate has the composition shown in table 1, the preparation process refers to examples 4-5, and the specific condition parameters are shown in tables 2 and 3;
FIG. 2 is a metallographic structure of comparative example 2, FIG. 3 is a metallographic structure of comparative example 3, and it can be seen from FIG. 2 that austenite grain boundaries of the steel sheet are significantly thicker, that is, kappa carbides are precipitated at the grain boundaries; as can be seen from FIG. 3, the metallographic structure of the steel sheet is austenite + delta ferrite, and the content of delta ferrite is less than or equal to 5%;
TABLE 1 alloy compositions of steels described in examples 1 to 5 and comparative examples 1 to 3
Figure BDA0003612986730000101
TABLE 2 Condition parameters for forging forming in examples 4 to 5 and comparative examples 2 to 3
Figure BDA0003612986730000102
Figure BDA0003612986730000111
TABLE 3 Condition parameters for Rolling in the production Processes described in examples 1 to 5 and comparative examples 1 to 3
Figure BDA0003612986730000112
Test example
The steel plates in examples 1-5 and comparative examples 1-3 are tested for material density, tensile property, impact property at-40 ℃ and corrosion resistance by referring to GB/T228-:
TABLE 4 Performance parameters of Steel sheets according to examples 1 to 5 and comparative examples 1 to 3
Density/g/cm3 Rp0.2/MPa Rm/MPa -40℃KV2/J Elongation/percent
Example 1 6.80 640 958 247 61
Example 2 6.85 625 947 240 57
Example 3 6.84 653 909 225 57
Example 4 6.76 675 970 200 55
Example 5 6.82 668 968 231 47
Comparative example 1 6.81 712 972 57 36
Comparative example 2 6.72 721 981 72 32
Comparative example 3 6.86 701 973 80 34
As is clear from Table 4, the densities ρ ≦ 6.9g/cm in examples 1 to 53The structure is single austenite or austenite + delta ferrite, and the yield strength ReL: 620-680MPa tensile strength Rm: 900-970 MPa, elongation A5≥45％、-40℃KV2The impact energy is more than or equal to 120J, and the steel has the typical characteristics of high-strength and high-toughness light steel. The comparative example 1 satisfies the regulation formula, but the water inlet temperature after rolling is lower than the lower limit value of 950 ℃ required by the process, and the poor structure of austenite and perimorphic kappa carbide is formed due to the lower water inlet temperature, so that the low-temperature impact energy is remarkably reduced without the inventionTypical characteristics of steel. In comparative example 2, since the components do not satisfy the component regulation formula of the present invention, Al and C contents both reach the upper limit of the component range, the precipitation kinetics of κ carbide is significantly enhanced, and the impact energy is lower than the minimum value of 120J of the present invention even though the processes both satisfy the requirements, and does not have the typical characteristics of the steel of the present invention. The comparative example 3 does not satisfy the composition regulation formula, and the relationship between the contents of Al and C reaches the composition lower limit, so that more delta ferrite appears in the steel, the impact energy is also lower than 120J, and the typical characteristics of the steel of the invention are not met.
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 high-strength and high-toughness light steel plate is characterized by comprising the following elements in percentage by mass: 27-30% of Mn, 8.30-9.20% of Al, 0.93-1.02% of C, 0.05-0.25% of Cr, 0.07-0.10% of Cu, 0.01-0.10% of Nb, 0.05-0.15% of Ti, less than or equal to 0.10% of N, less than or equal to 0.06% of Ce, less than or equal to 0.008% of P, less than or equal to 0.002% of S, and the balance of iron and inevitable impurities;
and the mass relation of Al and C is lambda1≤[C]≤λ2；λ1＝1.53-0.07[Al]，λ2＝1.9-0.1[Al]。
2. The high strength and toughness light steel plate as recited in claim 1, wherein the structure of said high strength and toughness light steel plate is austenite + δ ferrite + (Nb, Ti) C carbide, wherein the δ ferrite content is less than or equal to 5 vol%;
the density of the high-strength and high-toughness light steel plate is less than or equal to 6.9g/cm3(ii) a The yield strength is 620-680MPa, the tensile strength is 900-970 MPa, the elongation is more than or equal to 45%, and the transverse impact energy at minus 40 ℃ is more than or equal to 120J.
3. The method for preparing the high-strength light steel plate as claimed in claim 1 or 2, is characterized by comprising the following steps:
according to the element composition of the high-strength and high-toughness light steel plate, mixing the preparation raw materials, and then sequentially smelting and pouring to obtain an ingot;
and sequentially rolling, quenching and solid dissolving the cast ingot to obtain the high-strength high-toughness light steel plate.
4. The method according to claim 3, wherein after obtaining the ingot, further comprising subjecting the ingot to electroslag remelting;
the electroslag remelting is carried out in a protective atmosphere;
the electroslag remelting comprises ingot remelting and electroslag ingot cooling which are sequentially carried out; the melting speed of ingot remelting is 7-11 kg/min, and the cooling speed of electroslag ingot cooling is 8-12 ℃/h.
5. The method according to claim 4, wherein the electroslag remelting is followed by forging to form;
the forging temperature is 1130-1170 ℃, and the finish forging temperature is not less than 930 ℃.
6. The preparation method according to any one of claims 3 to 5, wherein the smelting method is vacuum induction furnace smelting or triple smelting;
the triple smelting method is an electric arc furnace-refining furnace-vacuum degassing furnace triple method.
7. A method according to any one of claims 3 to 5, wherein the casting temperature is from 1400 to 1450 ℃.
8. The method according to any one of claims 3 to 5, wherein the rolling process comprises: raising the temperature to 1150-1190 ℃ at the heating rate of 35-45 ℃/h, keeping the temperature, discharging from a furnace for rolling, wherein the initial rolling temperature is 1120-1140 ℃, rolling is carried out with the pass reduction of 6-20 mm, and the final rolling temperature is more than or equal to 970 ℃.
9. The preparation method according to any one of claims 3 to 5, wherein the cooling rate of quenching solid solution is not less than 15 ℃/s, the water entry temperature is not less than 950 ℃, and the final cooling temperature is not more than 200 ℃.
10. The application of the high-strength and high-toughness light steel plate as defined in claim 1 or 2 or the high-strength and high-toughness light steel plate prepared by the preparation method as defined in any one of claims 3 to 9 in the field of traffic and carrying equipment.
CN202210436283.9A 2022-04-25 2022-04-25 High-strength and high-toughness light steel plate and preparation method and application thereof Active CN114774806B (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
CN202210436283.9A CN114774806B (en) 2022-04-25 2022-04-25 High-strength and high-toughness light steel plate and preparation method and application thereof

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN202210436283.9A CN114774806B (en) 2022-04-25 2022-04-25 High-strength and high-toughness light steel plate and preparation method and application thereof

Publications (2)

Publication Number Publication Date
CN114774806A true CN114774806A (en) 2022-07-22
CN114774806B CN114774806B (en) 2023-05-23

Family

ID=82433184

Family Applications (1)

Application Number Title Priority Date Filing Date
CN202210436283.9A Active CN114774806B (en) 2022-04-25 2022-04-25 High-strength and high-toughness light steel plate and preparation method and application thereof

Country Status (1)

Country Link
CN (1) CN114774806B (en)

Citations (24)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4944814A (en) * 1989-03-02 1990-07-31 Ipsco Enterprises, Inc. Aluminum-manganese-iron steel alloy
JP2006176843A (en) * 2004-12-22 2006-07-06 Nippon Steel Corp High-strength and low-density steel sheet superior in ductility and manufacturing method therefor
DE102008040689A1 (en) * 2008-07-24 2010-02-11 Zf Friedrichshafen Ag Ball pivots or ball bushings, useful in ball joints for automobiles, are of special silicon- and aluminum-containing high-manganese steels requiring no inductive hardening
CN106244927A (en) * 2016-09-30 2016-12-21 北京理工大学 A kind of low-density unimach and preparation method thereof
CN106435380A (en) * 2016-10-26 2017-02-22 昆明理工大学 Microalloyed high-aluminum high-ductility steel plate and manufacturing method thereof
CN107557679A (en) * 2016-06-30 2018-01-09 鞍钢股份有限公司 Light austenitic steel with good strong plasticity and production method thereof
CN108642403A (en) * 2018-05-28 2018-10-12 河北工业大学 A kind of 780MPa grade super strengths Fe-Mn-Al-C systems lightweight cast steel and preparation method thereof
CN110066904A (en) * 2019-04-29 2019-07-30 武钢集团昆明钢铁股份有限公司 A kind of high-intensity and high-tenacity lightweight tool steel and preparation method thereof
CN110218948A (en) * 2019-06-27 2019-09-10 重庆金康新能源汽车设计院有限公司 A kind of low-density high tenacity steel and preparation method thereof
CN110607480A (en) * 2019-08-02 2019-12-24 华北理工大学 Nb-containing high-strength high-toughness low-density steel for automobile and preparation method thereof
CN110819908A (en) * 2019-11-18 2020-02-21 燕山大学 High-strength low-density austenitic steel and preparation method thereof
CN110951946A (en) * 2019-12-26 2020-04-03 安徽工业大学 Heat treatment process of low-density steel and preparation method thereof
CN111235484A (en) * 2020-03-13 2020-06-05 燕山大学 High-strength high-hardness low-density steel and preparation method and application thereof
CN111270158A (en) * 2020-03-13 2020-06-12 燕山大学 Low-density corrosion-resistant steel and preparation method and application thereof
CN111349865A (en) * 2020-03-13 2020-06-30 燕山大学 Aluminum-containing high-strength low-density steel and preparation method and application thereof
WO2020169764A1 (en) * 2019-02-22 2020-08-27 Salzgitter Flachstahl Gmbh Steel product made of lightweight steel containing manganese and method for production thereof
CN111850419A (en) * 2020-07-31 2020-10-30 燕山大学 High-manganese austenitic steel and preparation method thereof
CN112030077A (en) * 2020-09-08 2020-12-04 燕山大学 Manganese-containing high-strength low-density steel and preparation method and application thereof
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
CN112899579A (en) * 2021-01-18 2021-06-04 北京科技大学 Corrosion-resistant high-strength light 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
CN113549844A (en) * 2021-06-30 2021-10-26 华北理工大学 Method for improving hydrogen-induced delayed fracture resistance of Fe-Mn-Al-C light steel
CN114107830A (en) * 2021-11-19 2022-03-01 钢铁研究总院 Low-density wear-resistant steel used in wide temperature range and preparation method thereof

Patent Citations (24)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4944814A (en) * 1989-03-02 1990-07-31 Ipsco Enterprises, Inc. Aluminum-manganese-iron steel alloy
JP2006176843A (en) * 2004-12-22 2006-07-06 Nippon Steel Corp High-strength and low-density steel sheet superior in ductility and manufacturing method therefor
DE102008040689A1 (en) * 2008-07-24 2010-02-11 Zf Friedrichshafen Ag Ball pivots or ball bushings, useful in ball joints for automobiles, are of special silicon- and aluminum-containing high-manganese steels requiring no inductive hardening
CN107557679A (en) * 2016-06-30 2018-01-09 鞍钢股份有限公司 Light austenitic steel with good strong plasticity and production method thereof
CN106244927A (en) * 2016-09-30 2016-12-21 北京理工大学 A kind of low-density unimach and preparation method thereof
CN106435380A (en) * 2016-10-26 2017-02-22 昆明理工大学 Microalloyed high-aluminum high-ductility steel plate and manufacturing method thereof
CN108642403A (en) * 2018-05-28 2018-10-12 河北工业大学 A kind of 780MPa grade super strengths Fe-Mn-Al-C systems lightweight cast steel and preparation method thereof
WO2020169764A1 (en) * 2019-02-22 2020-08-27 Salzgitter Flachstahl Gmbh Steel product made of lightweight steel containing manganese and method for production thereof
CN110066904A (en) * 2019-04-29 2019-07-30 武钢集团昆明钢铁股份有限公司 A kind of high-intensity and high-tenacity lightweight tool steel and preparation method thereof
CN110218948A (en) * 2019-06-27 2019-09-10 重庆金康新能源汽车设计院有限公司 A kind of low-density high tenacity steel and preparation method thereof
CN110607480A (en) * 2019-08-02 2019-12-24 华北理工大学 Nb-containing high-strength high-toughness low-density steel for automobile and preparation method thereof
CN110819908A (en) * 2019-11-18 2020-02-21 燕山大学 High-strength low-density austenitic steel and preparation method thereof
CN110951946A (en) * 2019-12-26 2020-04-03 安徽工业大学 Heat treatment process of low-density steel and preparation method thereof
CN111235484A (en) * 2020-03-13 2020-06-05 燕山大学 High-strength high-hardness low-density steel and preparation method and application thereof
CN111349865A (en) * 2020-03-13 2020-06-30 燕山大学 Aluminum-containing high-strength low-density steel and preparation method and application thereof
CN111270158A (en) * 2020-03-13 2020-06-12 燕山大学 Low-density corrosion-resistant steel and preparation method and application thereof
CN111850419A (en) * 2020-07-31 2020-10-30 燕山大学 High-manganese austenitic steel and preparation method thereof
CN112030077A (en) * 2020-09-08 2020-12-04 燕山大学 Manganese-containing high-strength low-density steel and preparation method and application thereof
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
CN112899579A (en) * 2021-01-18 2021-06-04 北京科技大学 Corrosion-resistant high-strength light 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
CN113549844A (en) * 2021-06-30 2021-10-26 华北理工大学 Method for improving hydrogen-induced delayed fracture resistance of Fe-Mn-Al-C light steel
CN114107830A (en) * 2021-11-19 2022-03-01 钢铁研究总院 Low-density wear-resistant steel used in wide temperature range and preparation method thereof

Also Published As

Publication number Publication date
CN114774806B (en) 2023-05-23

Similar Documents

Publication Publication Date Title
CN108220766B (en) Cr-V hot work die steel and preparation method thereof
CN109136653B (en) Nickel-based alloy for nuclear power equipment and manufacturing method of hot rolled plate of nickel-based alloy
WO2017206418A1 (en) Normalized-condition delivered 180-200 mm-thick eh36 steel plate and preparation method therefor
CN111500917A (en) High-strength and high-toughness medium-entropy high-temperature alloy and preparation method thereof
CN109112423B (en) Super-thick alloy steel plate with excellent low-temperature toughness and preparation method thereof
CN110230009B (en) Hot work die steel with good cutting performance and preparation method thereof
EP4198158A1 (en) Steel board for polar marine engineering and preparation method therefor
CN114807772B (en) Aging-strengthened high-strength high-toughness light steel and manufacturing method thereof
CN110951946B (en) Heat treatment process of low-density steel and preparation method thereof
CN114561517B (en) Low-density high-plasticity and toughness steel and preparation method and application thereof
CN115710654A (en) Copper-nickel-tin alloy and preparation method thereof
CN115948694B (en) High-performance austenitic stainless steel plate with diameter of less than 45mm and manufacturing method thereof
CN114752864B (en) Low-density ultrahigh-strength high-plasticity steel and preparation method and application thereof
CN116732452A (en) High-corrosion-resistance high-carbon austenitic stainless steel for nuclear power and manufacturing method thereof
CN114875318B (en) Dispersed delta phase strengthened low-density high-strength and high-toughness steel and manufacturing method thereof
CN114752866B (en) Corrosion-resistant low-temperature impact-resistant austenitic light steel and preparation method and application thereof
CN114774806B (en) High-strength and high-toughness light steel plate and preparation method and application thereof
CN112322987B (en) Ultrahigh-strength steel wire for electric arc additive manufacturing and preparation method
CN114892084B (en) High-strength austenitic light steel with high impact toughness and manufacturing method thereof
CN114752867B (en) High-strength and high-toughness lightweight steel and preparation method and application thereof
CN111363970B (en) Nickel-free LPG (liquefied Petroleum gas) steel plate for ship and manufacturing method thereof
CN115652210B (en) Austenitic stainless steel billet with ultralow carbide content and manufacturing method thereof
CN114807782B (en) Dispersion-strengthened ultrahigh-strength high-plasticity light steel and manufacturing method thereof
CN113151739B (en) 540 MPa-grade VL4-4MOD ship steel plate and manufacturing method thereof
EP4435133A1 (en) Hot-rolled steel for enameling having enameling and firing strengthening property, and manufacturing method therefor

Legal Events

Date Code Title Description
PB01 Publication
PB01 Publication
SE01 Entry into force of request for substantive examination
SE01 Entry into force of request for substantive examination
GR01 Patent grant
GR01 Patent grant